Development of macro-defect-free PBF-EB-processed Ti–6Al–4V alloys with superior plasticity using PREP-synthesized powder and machine learning-assisted process optimization

Development of macro-defect-free PBF-EB-processed Ti–6Al–4V alloys with superior plasticity using PREP-synthesized powder and machine learning-assisted process optimization

Yunwei GuiabKenta Aoyagib Akihiko Chibab
aDepartment of Materials Processing, Graduate School of Engineering, Tohoku University, 6-6 Aramaki Aza Aoba, Aoba-ku, Sendai, 980-8579, Japan
bInstitute for Materials Research, Tohoku University, 2-1-1 Katahira, Aoba-ku, Sendai, 980-8577, Japan

Received 14 October 2022, Revised 23 December 2022, Accepted 3 January 2023, Available online 5 January 2023.Show lessAdd to MendeleyShareCite

https://doi.org/10.1016/j.msea.2023.144595Get rights and content

Abstract

The elimination of internal macro-defects is a key issue in Ti–6Al–4V alloys fabricated via powder bed fusion using electron beams (PBF-EB), wherein internal macro-defects mainly originate from the virgin powder and inappropriate printing parameters. This study compares different types powders by combining support vector machine techniques to determine the most suitable powder for PBF-EB and to predict the processing window for the printing parameters without internal macro-defects. The results show that powders fabricated via plasma rotating electrode process have the best sphericity, flowability, and minimal porosity and are most suitable for printing. Surface roughness criterion was also applied to determine the quality of the even surfaces, and support vector machine was used to construct processing maps capable of predicting a wide range of four-dimensional printing parameters to obtain macro-defect-free samples, offering the possibility of subsequent development of Ti–6Al–4V alloys with excellent properties. The macro-defect-free samples exhibited good elongation, with the best overall mechanical properties being the ultimate tensile strength and elongation of 934.7 MPa and 24.3%, respectively. The elongation of the three macro-defect-free samples was much higher than that previously reported for additively manufactured Ti–6Al–4V alloys. The high elongation of the samples in this work is mainly attributed to the elimination of internal macro-defects.

Introduction

Additive manufacturing (AM) technologies can rapidly manufacture complex or custom parts, reducing process steps and saving manufacturing time [[1], [2], [3], [4]], and are widely used in the aerospace, automotive, and other precision industries [5,6]. Powder bed fusion using an electron beam (PBF-EB) is an additive manufacturing method that uses a high-energy electron beam to melt metal powders layer by layer to produce parts. In contrast to selective laser melting, PBF-EB involves the preparation of samples in a high vacuum environment, which effectively prevents the introduction of impurities such as O and N. It also involves a preheating process for the print substrate and powder, which reduces residual thermal stress on the sample and subsequent heat treatment processes [[2], [3], [4],7]. Due to these features and advantages, PBF-EB technology is a very important AM technology with great potential in metallic materials. Moreover, PBF-EB is the ideal AM technology for the manufacture of complex components made of many alloys, such as titanium alloys, nickel-based superalloys, aluminum alloys and stainless steels [[2], [3], [4],8].

Ti–6Al–4V alloy is one of the prevalent commercial titanium alloys possessing high specific strength, excellent mechanical properties, excellent corrosion resistance, and good biocompatibility [9,10]. It is widely used in applications requiring low density and excellent corrosion resistance, such as the aerospace industry and biomechanical applications [11,12]. The mechanical properties of PBF-EB-processed Ti–6Al–4V alloys are superior to those fabricated by casting or forging, because the rapid cooling rate in PBF-EB results in finer grains [[12], [13], [14], [15], [16], [17], [18]]. However, the PBF-EB-fabricated parts often include internal macro-defects, which compromises their mechanical properties [[19], [20], [21], [22]]. This study focused on the elimination of macro-defects, such as porosity, lack of fusion, incomplete penetration and unmelted powders, which distinguishes them from micro-defects such as vacancies, dislocations, grain boundaries and secondary phases, etc. Large-sized fusion defects cause a severe reduction in mechanical strength. Smaller defects, such as pores and cracks, lead to the initiation of fatigue cracking and rapidly accelerate the cracking process [23]. The issue of internal macro-defects must be addressed to expand the application of the PBF-EB technology. The main studies for controlling internal macro-defects are online monitoring of defects, remelting and hot isostatic pressing (HIP). The literatures [24,25] report the use of infrared imaging or other imaging techniques to identify defects, but the monitoring of smaller sized defects is still not adequate. And in some cases remelting does not reduce the internal macro-defects of the part, but instead causes coarsening of the macrostructure and volatilization of some metal elements [23]. The HIP treatment does not completely eliminate the internal macro-defects, the original defect location may still act as a point of origin of the crack, and the subsequent treatment will consume more time and economic costs [23]. Therefore, optimizing suitable printing parameters to avoid internal macro-defects in printed parts at source is of great industrial value and research significance, and is an urgent issue in PBF-EB related technology.

There are two causes of internal macro-defects in the AM process: gas pores trapped in the virgin powder and the inappropriate printing parameters [7,23]. Gui et al. [26] classify internal macro-defects during PBF-EB process according to their shape, such as spherical defects, elongated shape defects, flat shape defects and other irregular shape defects. Of these, spherical defects mainly originate from raw material powders. Other shape defects mainly originate from lack of fusion or unmelted powders caused by unsuitable printing parameters, etc. The PBF-EB process requires powders with good flowability, and spherical powders are typically chosen as raw materials. The prevalent techniques for the fabrication of pre-alloyed powders are gas atomization (GA), plasma atomization (PA), and the plasma rotating electrode process (PREP) [27,28]. These methods yield powders with different characteristics that affect the subsequent fabrication. The selection of a suitable powder for PBF-EB is particularly important to produce Ti–6Al–4V alloys without internal macro-defects. The need to optimize several printing parameters such as beam current, scan speed, line offset, and focus offset make it difficult to eliminate internal macro-defects that occur during printing [23]. Most of the studies [11,12,22,[29], [30], [31], [32], [33]] on the optimization of AM processes for Ti–6Al–4V alloys have focused on samples with a limited set of parameters (e.g., power–scan speed) and do not allow for the guidance and development of unknown process windows for macro-defect-free samples. In addition, process optimization remains a time-consuming problem, with the traditional ‘trial and error’ method demanding considerable time and economic costs. The development of a simple and efficient method to predict the processing window for alloys without internal macro-defects is a key issue. In recent years, machine learning techniques have increasingly been used in the field of additive manufacturing and materials development [[34], [35], [36], [37]]. Aoyagi et al. [38] recently proposed a novel and efficient method based on a support vector machine (SVM) to optimize the two-dimensional process parameters (current and scan speed) and obtain PBF-EB-processed CoCr alloys without internal macro-defects. The method is one of the potential approaches toward effective optimization of more than two process parameters and makes it possible for the machine learning techniques to accelerate the development of alloys without internal macro-defects.

Herein, we focus on the elimination of internal macro-defects, such as pores, lack of fusion, etc., caused by raw powders and printing parameters. The Ti–6Al–4V powders produced by three different methods were compared, and the powder with the best sphericity, flowability, and minimal porosity was selected as the feedstock for subsequent printing. The relationship between the surface roughness and internal macro-defects in the Ti–6Al–4V components was also investigated. The combination of SVM and surface roughness indices (Sdr) predicted a wider four-dimensional processing window for obtaining Ti–6Al–4V alloys without internal macro-defects. Finally, we investigated the tensile properties of Ti–6Al–4V alloys at room temperature with different printing parameters, as well as the corresponding microstructures and fracture types.

Section snippets

Starting materials

Three types of Ti–6Al–4V alloy powders, produced by GA, PA, and PREP, were compared. The particle size distribution of the powders was determined using a laser particle size analyzer (LS230, Beckman Coulter, USA), and the flowability was measured using a Hall flowmeter (JIS-Z2502, Tsutsui Scientific Instruments Co., Ltd., Japan), according to the ASTM B213 standard. The powder morphology and internal macro-defects were determined using scanning electron microscopy (SEM, JEOL JCM-6000) and X-ray 

Comparison of the characteristics of GA, PA, and PREP Ti–6Al–4V powders

The particle size distributions (PSDs) and flowability of the three types of Ti–6Al–4V alloy powders produced by GA, PA, and PREP are shown in Fig. 2. Although the average particle sizes are similar (89.4 μm for GA, 82.5 μm for PA, and 86.1μm for PREP), the particle size range is different for the three types of powder (6.2–174.8 μm for GA, 27.3–139.2 μm for PA, and 39.4–133.9 μm for PREP). The flowability of the GA, PA, and PREP powders was 30.25 ± 0.98, 26.54 ± 0.37, and 25.03 ± 0.22 (s/50

Conclusions

The characteristics of the three types of Ti–6Al–4V alloy powders produced via GA, PA, and PREP were compared. The PREP powder with the best sphericity, flowability, and low porosity was found to be the most favorable powder for subsequent printing of Ti–6Al–4V alloys without internal macro-defects. The quantitative criterion of Sdr <0.015 for even surfaces was also found to be applicable to Ti–6Al–4V alloys. The process maps of Ti–6Al–4V alloys include two regions, high beam current/scan speed 

Uncited references

[55]; [56]; [57]; [58]; [59]; [60]; [61]; [62]; [63]; [64]; [65].

CRediT authorship contribution statement

Yunwei Gui: Writing – original draft, Visualization, Validation, Investigation. Kenta Aoyagi: Writing – review & editing, Supervision, Resources, Methodology, Funding acquisition, Conceptualization. Akihiko Chiba: Supervision, Funding acquisition.

Declaration of competing interest

The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

Acknowledgments

This study was based on the results obtained from project JPNP19007, commissioned by the New Energy and Industrial Technology Development Organization (NEDO). This work was also supported by JSPS KAKENHI (Proposal No. 21K03801) and the Inter-University Cooperative Research Program (Proposal nos. 18G0418, 19G0411, and 20G0418) of the Cooperative Research and Development Center for Advanced Materials, Institute for Materials Research, Tohoku University. It was also supported by the Council for

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Fig. 2 Modeling of bubble point test apparatus (left) and computational grid (righ

Flow-3d를 이용한 표면장력 탱크용메시스크린모델링

Modeling of Mesh Screen for Use in Surface TensionTankUsing Flow-3d Software

Hyuntak Kim․ Sang Hyuk Lim․Hosung Yoon․Jeong-Bae Park*․Sejin Kwon

ABSTRACT

Mesh screen modeling and liquid propellant discharge simulation of surface tension tank wereperformed using commercial CFD software Flow-3d. 350 × 2600, 400 × 3000 and 510 × 3600 DTW mesh screen were modeled using macroscopic porous media model. Porosity, capillary pressure, and drag
coefficient were assigned for each mesh screen model, and bubble point simulations were performed. The
mesh screen model was validated with the experimental data. Based on the screen modeling, liquidpropellant discharge simulation from PMD tank was performed. NTO was assigned as the liquidpropellant, and void was set to flow into the tank inlet to achieve an initial volume flowrate of
liquid propellant in 3 × 10-3 g acceleration condition. The intial flow pressure drop through the meshscreen was approximately 270 Pa, and the pressure drop increased with time. Liquid propellant
discharge was sustained until the flow pressure drop reached approximately 630 Pa, which was near
the estimated bubble point value of the screen model.

초 록

상용 CFD 프로그램 Flow-3d를 활용하여, 표면 장력 탱크 적용을 위한 메시 스크린의 모델링 및 추진제 배출 해석을 수행하였다. Flow-3d 내 거시적 다공성 매체 모델을 사용하였으며, 350 × 2600, 400× 3000, 510 × 3600 DTW 메시 스크린에 대한 공극률, 모세관압, 항력계수를 스크린 모델에 대입 후, 기포점 측정 시뮬레이션을 수행하였다.

시뮬레이션 결과를 실험 데이터와 비교하였으며, 메시 스크린 모델링의 적절성을 검증하였다. 이를 기반으로 스크린 모델을 포함한 PMD 구조체에 대한 추진제 배출 해석을 수행하였다. 추진제는 액상의 NTO를 가정하였으며, 3 × 10-3 g 가속 조건에서 초기 유량을만족하도록 void를 유입시켰다. 메시 스크린을 통한 차압은 초기 약 270 Pa에서 시간에 따라 증가하였으며, 스크린 모델의 예상 기포점과 유사한 630 Pa에 이르기까지 액상 추진제 배출을 지속하였다.

Key Words

Surface Tension Tank(표면장력 탱크), Propellant Management Device(추진제 관리 장치),
Mesh Screen(메시 스크린), Porous Media Model(다공성 매체 모델), Bubble Point(기포점)

서론

    우주비행체를 미소 중력 조건 내에서 운용하 는 경우, 가압 기체가 액상의 추진제와 혼합되어 엔진으로 공급될 우려가 있으므로 이를 방지하 기 위한 탱크의 설계가 필요하다.

    다이어프램 (Diaphragm), 피스톤(Piston) 등 다양한 장치들 이 활용되고 있으며, 이 중 표면 장력 탱크는 내 부의 메시 스크린(Mesh screen), 베인(Vane) 등 의 구조체에서 추진제의 표면장력을 활용함으로 써 액상 추진제의 이송 및 배출을 유도하는 방 식이다.

    표면 장력 탱크는 구동부가 없는 구조로 신뢰성이 높고, 전 부분을 티타늄 등의 금속 재 질로 구성함으로써 부식성 추진제의 사용 조건 에서도 장기 운용이 가능한 장점이 있다. 위에서 언급한 메시 스크린(Mesh screen)은 수 십 마이크로미터 두께의 금속 와이어를 직조한 다공성 재질로 표면 장력 탱크의 핵심 구성 요소 중 하나이다.

    미세 공극 상 추진제의 표면장력에 의해 기체와 액체 간 계면을 일정 차압 내에서 유지시킬 수 있다. 이러한 성질로 인해 일정 조 건에서 가압 기체가 메시 스크린을 통과하지 못 하게 되고, 스크린을 탱크 유로에 설치함으로써 액상의 추진제 배출을 유도할 수 있다.

    메시 스크린이 가압 기체를 통과시키기 직전 의 기체-액체 계면에 형성되는 최대 차압을 기포 점 (Bubble point) 이라 칭하며, 메시 스크린의 주 요 성능 지표 중 하나이다. IPA, 물, LH2, LCH4 등 다양한 기준 유체 및 추진제, 다양한 메시 스 크린 사양에 대해 기포점 측정 관련 실험적 연 구가 이루어져 왔다 [1-3].

    위 메시 스크린을 포함하여 표면 장력 탱크 내 액상의 추진제 배출을 유도하는 구조물 일체 를 PMD(Propellant management device)라 칭하 며, 갤러리(Gallery), 베인(Vane), 스펀지(Sponge), 트랩(Trap) 등 여러 종류의 구조물에 대해 각종 형상 변수를 내포한다[4, 5].

    따라서 다양한 파라미터를 고려한 실험적 연구는 제약이 따를 수 있으며, 베인 등 상대적으로 작은 미소 중력 조건에서 개방형 유로를 활용하는 경우 지상 추진제 배출 실험이 불가능하다[6]. 그러므로 CFD를 통한 표면장력 탱크 추진제 배출 해석은 다양한 작동 조건 및 PMD 형상 변수에 따른 추진제 거동을 이해하고, 탱크를 설계하는 데 유용하게 활용될 수 있다.

    상기 추진제 배출 해석을 수행하기 위해서는 핵심 요소 중 하나인 메시 스크린에 대한 모델링이 필수적이다. Chato, McQuillen 등은 상용 CFD 프로그램인 Fluent를 통해, 갤러리 내 유동 시뮬레이션을 수행하였으며, 이 때 메시 스크린에 ‘porous jump’ 경계 조건을 적용함으로써 액상의 추진제가 스크린을 통과할 때 생기는 압력 강하를 모델링하였다[7, 8].

    그러나 앞서 언급한 메시 스크린의 기포점 특성을 모델링한 사례는 찾아보기 힘들다. 이는 스크린을 활용하는 표면 장력 탱크 내 액상 추진제 배출 현상을 해석적으로 구현하기 위해 반드시 필요한 부분이다. 본 연구에서는 자유표면 해석에 상대적으로 강점을 지닌 상용 CFD 프로그램 Flow-3d를 사용하여, 메시 스크린을 모델링하였다.

    거시적 다공성 매체 모델(Macroscopic porous mediamodel)을 활용하여 메시 스크린 모델 영역에 공극률(Porosity), 모세관압(Capillary pressure), 항력 계수(Drag coefficient)를 지정하고, 이를 기반으로 기포점 측정 시뮬레이션을 수행, 해석 결과와 실험 데이터 간 비교 및 검증을 수행하였다.

    이를 기반으로 메시 스크린 및 PMD구조체를 포함한 탱크의 추진제 배출 해석을 수행하고, 기포점 특성의 반영 여부를 확인하였다.

    Fig. 1 Real geometry-based mesh screen model (left)
and mesh screen model based on macroscopic
porous media model in Flow-3d (righ
    Fig. 1 Real geometry-based mesh screen model (left) and mesh screen model based on macroscopic porous media model in Flow-3d (righ
    Fig. 2 Modeling of bubble point test apparatus (left)
and computational grid (righ
    Fig. 2 Modeling of bubble point test apparatus (left) and computational grid (righ)
    Fig. 3 Modeling of sump in a tank (left) and lower part
of the sump structure (right)
    Fig. 3 Modeling of sump in a tank (left) and lower part of the sump structure (right)

    참 고 문 헌

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    2. Hartwig, J., Mann, J. A. Jr., Darr, S. R., “Parametric Analysis of the LiquidHydrogen and Nitrogen Bubble Point Pressure for Cryogenic Liquid AcquisitionDevices”, Cryogenics, Vol. 63, 2014, pp. 25-36
    3. Jurns, J. M., McQuillen, J. B.,BubblePoint Measurement with Liquid Methane of a Screen Capillary Liquid AcquisitionDevice”, NASA-TM-2009-215496, 2009
    4. Jaekle, D. E. Jr., “Propellant Management Device: Conceptual Design and Analysis: Galleries”, AIAA 29th Joint PropulsionConference, AIAA-97-2811, 1997
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    8. McQuillen, J. B., Chao, D. F., Hall, N. R., Motil, B. J., Zhang, N., CFD simulation of Flow in Capillary Flow Liquid Acquisition Device Channel”, World Academy of Science, Engineering and Technology, Vol. 6, 2012, pp. 640-646
    9. Hartwig, J., Chato, D., McQuillen, J.,  Screen Channel LAD Bubble Point Tests in Liquid Hydrogen”, International Journal of Hydrogen Energy, Vol. 39, No. 2, 2014, pp. 853-861
    10. Fischer, A., Gerstmann, J., “Flow Resistance of Metallic Screens in Liquid, Gaseous and Cryogenic Flow”, 5th European Conferencefor Aeronautics and Space Sciences, Munich, Germany, 2013
    11. Fries, N., Odic, K., Dreyer, M., Wickingof Perfectly Wetting Liquids into a MetallicMesh”, 2nd International Conference onPorous Media and its Applications inScience and Engineering, 2007
    12. Seo, M, K., Kim, D, H., Seo, C, W., Lee, S, Y., Jang, S, P., Koo, J., “Experimental Study of Pressure Drop in CompressibleFluid through Porous Media”, Transactionsof the Korean Society of Mechanical Engineers – B, Vol. 37, No. 8, pp. 759-765, 2013.
    13. Hartwig, J., Mann, J. A., “Bubble Point Pressures of Binary Methanol/Water Mixtures in Fine-Mesh Screens”, AlChEJournal, Vol. 60, No. 2, 2014, pp. 730-739
    Serife Yurdagul Kumcu−2−KSCE Journal of Civil Engineeringthe use of CFD for the assessment of a design, as well as screeningand optimizing of hydraulic structures and cofferdam layouts. Theyconclude that CFD has been successful in optimizing the finalconceptual configuration for the hydraulics design of the project,but recommend that physical modeling still be used as a finalconfirmation.This paper provides experimental studies performed on Kav akDam and analyses the stability of spillway design by usingFLOW-3D model. It compares the hydraulic model tests withFLOW-3D simulation results and gives information on howaccurately a commercially available Computational Fluid Dynamic(CFD) model can predict the spillway discharge capacity andpressure distribution along the spillway bottom surface. 2. Physical ModelA 1/50-scaled undistorted physical model of the Kavsak Damspillway and stilling basin was built and tested at the HydraulicModel Laboratory of State Hydraulic Works of Turkey (DSI).The model was constructed of plexiglas and was fabricated toconform to the distinctive shape of an ogee crest. The spillwayhas 45.8 m in width and 57 m long with a bottom slope of 125%.The length of the stilling basin is about 90 m. During model tests,flow velocities were measured with an ultrasonic flow meter.Pressures on the spillway were measured using a piezometerssçTable 1. Upstream and Downstream Operating Conditions of theKavsak DamRun Upstream reservoir elevation (m)Downstream tailwater elevation (m)1 306.55 168.002 311.35 174.503 314.00 178.904 316.50 182.55Fig. 1. (a) Original Project Design and Final Project Design after Experimental Investigations and Flow Measurement Sections at theApproach, (b) Top View Experimentally Modified Approach in the Laboratory, (c) Side View of the Experimentally Modified Approachin the Laboratory

    Investigation of flow over spillway modeling and comparison between experimental data and CFD analysis

    여수로 모델링 및 실험 데이터와 CFD 해석의 비교에 대한 조사

    DOI:10.1007/s12205-016-1257-z

    Authors:

    Serife Yurdagul Kumcu at Necmettin Erbakan Üniversitesi

    Serife Yurdagul Kumcu

    Abstract and Figures

    As a part of design process for hydro-electric generating stations, hydraulic engineers typically conduct some form of model testing. The desired outcome from the testing can vary considerably depending on the specific situation, but often characteristics such as velocity patterns, discharge rating curves, water surface profiles, and pressures at various locations are measured. Due to recent advances in computational power and numerical techniques, it is now also possible to obtain much of this information through numerical modeling. In this paper, hydraulic characteristics of Kavsak Dam and Hydroelectric Power Plant (HEPP), which are under construction and built for producing energy in Turkey, were investigated experimentally by physical model studies. The 1/50-scaled physical model was used in conducting experiments. Flow depth, discharge and pressure data were recorded for different flow conditions. Serious modification was made on the original project with the experimental study. In order to evaluate the capability of the computational fluid dynamics on modeling spillway flow a comparative study was made by using results obtained from physical modeling and Computational Fluid Dynamics (CFD) simulation. A commercially available CFD program, which solves the Reynolds-averaged Navier-Stokes (RANS) equations, was used to model the numerical model setup by defining cells where the flow is partially or completely restricted in the computational space. Discharge rating curves, velocity patterns and pressures were used to compare the results of the physical model and the numerical model. It was shown that there is reasonably good agreement between the physical and numerical models in flow characteristics.

    수력 발전소 설계 프로세스의 일부로 수력 엔지니어는 일반적으로 어떤 형태의 모델 테스트를 수행합니다. 테스트에서 원하는 결과는 특정 상황에 따라 상당히 다를 수 있지만 속도 패턴, 방전 등급 곡선, 수면 프로파일 및 다양한 위치에서의 압력과 같은 특성이 측정되는 경우가 많습니다. 최근 계산 능력과 수치 기법의 발전으로 인해 이제는 수치 모델링을 통해 이러한 정보의 대부분을 얻을 수도 있습니다.

    본 논문에서는 터키에서 에너지 생산을 위해 건설 중인 Kavsak 댐과 수력발전소(HEPP)의 수력학적 특성을 물리적 모델 연구를 통해 실험적으로 조사하였다. 1/50 스케일의 물리적 모델이 실험 수행에 사용되었습니다. 다양한 흐름 조건에 대해 흐름 깊이, 배출 및 압력 데이터가 기록되었습니다. 실험 연구를 통해 원래 프로젝트에 대대적인 수정이 이루어졌습니다.

    배수로 흐름 모델링에 대한 전산유체역학의 능력을 평가하기 위해 물리적 모델링과 전산유체역학(CFD) 시뮬레이션 결과를 이용하여 비교 연구를 수행하였습니다. RANS(Reynolds-averaged Navier-Stokes) 방정식을 푸는 상업적으로 이용 가능한 CFD 프로그램은 흐름이 계산 공간에서 부분적으로 또는 완전히 제한되는 셀을 정의하여 수치 모델 설정을 모델링하는 데 사용되었습니다.

    물리적 모델과 수치 모델의 결과를 비교하기 위해 배출 등급 곡선, 속도 패턴 및 압력을 사용했습니다. 유동 특성에서 물리적 모델과 수치 모델 간에 상당히 좋은 일치가 있는 것으로 나타났습니다.

    Serife Yurdagul Kumcu−2−KSCE Journal of Civil Engineeringthe use of CFD for the assessment of a design, as well as screeningand optimizing of hydraulic structures and cofferdam layouts. Theyconclude that CFD has been successful in optimizing the finalconceptual configuration for the hydraulics design of the project,but recommend that physical modeling still be used as a finalconfirmation.This paper provides experimental studies performed on Kav akDam and analyses the stability of spillway design by usingFLOW-3D model. It compares the hydraulic model tests withFLOW-3D simulation results and gives information on howaccurately a commercially available Computational Fluid Dynamic(CFD) model can predict the spillway discharge capacity andpressure distribution along the spillway bottom surface. 2. Physical ModelA 1/50-scaled undistorted physical model of the Kavsak Damspillway and stilling basin was built and tested at the HydraulicModel Laboratory of State Hydraulic Works of Turkey (DSI).The model was constructed of plexiglas and was fabricated toconform to the distinctive shape of an ogee crest. The spillwayhas 45.8 m in width and 57 m long with a bottom slope of 125%.The length of the stilling basin is about 90 m. During model tests,flow velocities were measured with an ultrasonic flow meter.Pressures on the spillway were measured using a piezometerssçTable 1. Upstream and Downstream Operating Conditions of theKavsak DamRun Upstream reservoir elevation (m)Downstream tailwater elevation (m)1 306.55 168.002 311.35 174.503 314.00 178.904 316.50 182.55Fig. 1. (a) Original Project Design and Final Project Design after Experimental Investigations and Flow Measurement Sections at theApproach, (b) Top View Experimentally Modified Approach in the Laboratory, (c) Side View of the Experimentally Modified Approachin the Laboratory
    Serife Yurdagul Kumcu−2−KSCE Journal of Civil Engineeringthe use of CFD for the assessment of a design, as well as screeningand optimizing of hydraulic structures and cofferdam layouts. Theyconclude that CFD has been successful in optimizing the finalconceptual configuration for the hydraulics design of the project,but recommend that physical modeling still be used as a finalconfirmation.This paper provides experimental studies performed on Kav akDam and analyses the stability of spillway design by usingFLOW-3D model. It compares the hydraulic model tests withFLOW-3D simulation results and gives information on howaccurately a commercially available Computational Fluid Dynamic(CFD) model can predict the spillway discharge capacity andpressure distribution along the spillway bottom surface. 2. Physical ModelA 1/50-scaled undistorted physical model of the Kavsak Damspillway and stilling basin was built and tested at the HydraulicModel Laboratory of State Hydraulic Works of Turkey (DSI).The model was constructed of plexiglas and was fabricated toconform to the distinctive shape of an ogee crest. The spillwayhas 45.8 m in width and 57 m long with a bottom slope of 125%.The length of the stilling basin is about 90 m. During model tests,flow velocities were measured with an ultrasonic flow meter.Pressures on the spillway were measured using a piezometerssçTable 1. Upstream and Downstream Operating Conditions of theKavsak DamRun Upstream reservoir elevation (m)Downstream tailwater elevation (m)1 306.55 168.002 311.35 174.503 314.00 178.904 316.50 182.55Fig. 1. (a) Original Project Design and Final Project Design after Experimental Investigations and Flow Measurement Sections at theApproach, (b) Top View Experimentally Modified Approach in the Laboratory, (c) Side View of the Experimentally Modified Approachin the Laboratory

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    Assessment of spillway modeling using computational fluid dynamics

    전산유체역학을 이용한 여수로 모델링 평가

    Authors: Paul G. Chanel and John C. Doering AUTHORS INFO & AFFILIATIONS

    Publication: Canadian Journal of Civil Engineering

    3 December 2008

    Abstract

    Throughout the design and planning period for future hydroelectric generating stations, hydraulic engineers are increasingly integrating computational fluid dynamics (CFD) into the process. As a result, hydraulic engineers are interested in the reliability of CFD software to provide accurate flow data for a wide range of structures, including a variety of different spillways. In the literature, CFD results have generally been in agreement with physical model experimental data. Despite past success, there has not been a comprehensive assessment that looks at the ability of CFD to model a range of different spillway configurations, including flows with various gate openings. In this article, Flow-3D is used to model the discharge over ogee-crested spillways. The numerical model results are compared with physical model studies for three case study evaluations. The comparison indicates that the accuracy of Flow-3D is related to the parameter P/Hd.

    미래의 수력 발전소를 위한 설계 및 계획 기간 동안 유압 엔지니어는 전산유체역학(CFD)을 프로세스에 점점 더 많이 통합하고 있습니다. 결과적으로 유압 엔지니어는 다양한 여수로를 포함하여 광범위한 구조에 대한 정확한 흐름 데이터를 제공하는 CFD 소프트웨어의 신뢰성에 관심을 갖고 있습니다. 문헌에서 CFD 결과는 일반적으로 물리적 모델 실험 데이터와 일치했습니다. 과거의 성공에도 불구하고 다양한 게이트 개구부가 있는 흐름을 포함하여 다양한 여수로 구성을 모델링하는 CFD의 기능을 살펴보는 포괄적인 평가는 없었습니다. 이 기사에서는 Flow-3D를 사용하여 ogee-crested 방수로의 배출을 모델링합니다. 세 가지 사례 연구 평가를 위해 수치 모델 결과를 물리적 모델 연구와 비교합니다. 비교는 Flow-3D의 정확도가 매개변수 P/Hd와 관련되어 있음을 나타냅니다.

    Résumé

    Les ingénieurs en hydraulique intègrent de plus en plus la dynamique des fluides numérique (« CFD ») dans le processus de conception et de planification des futures centrales. Ainsi, les ingénieurs en hydraulique s’intéressent à la fiabilité du logiciel de « CFD » afin de fournir des données précises sur le débit pour une large gamme de structures, incluant différents types d’évacuateurs. Les résultats de « CFD » dans la littérature ont été globalement sont généralement en accord avec les données expérimentales des essais physiques. Malgré les succès antérieurs, il n’y avait aucune évaluation complète de la capacité des « CFD » à modéliser une plage de configuration des évacuateurs, incluant les débits à diverses ouvertures de vannes. Dans le présent article, le logiciel Flow-3D est utilisé pour modéliser le débit par des évacuateurs en doucine. Les résultats du modèle de calcul sont comparés à ceux des essais physiques pour trois études de cas. La comparaison montre que la précision du logiciel Flow-3D est associée au paramètre P/Hd.

    Fig. 1. Averaged error trend.
    Fig. 1. Averaged error trend.

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    Fig. 1. (a) Dimensions of the casting with runners (unit: mm), (b) a melt flow simulation using Flow-3D software together with Reilly's model[44], predicted that a large amount of bifilms (denoted by the black particles) would be contained in the final casting. (c) A solidification simulation using Pro-cast software showed that no shrinkage defect was contained in the final casting.

    AZ91 합금 주물 내 연행 결함에 대한 캐리어 가스의 영향

    TianLiabJ.M.T.DaviesaXiangzhenZhuc
    aUniversity of Birmingham, Birmingham B15 2TT, United Kingdom
    bGrainger and Worrall Ltd, Bridgnorth WV15 5HP, United Kingdom
    cBrunel Centre for Advanced Solidification Technology, Brunel University London, Kingston Ln, London, Uxbridge UB8 3PH, United Kingdom

    Abstract

    An entrainment defect (also known as a double oxide film defect or bifilm) acts a void containing an entrapped gas when submerged into a light-alloy melt, thus reducing the quality and reproducibility of the final castings. Previous publications, carried out with Al-alloy castings, reported that this trapped gas could be subsequently consumed by the reaction with the surrounding melt, thus reducing the void volume and negative effect of entrainment defects. Compared with Al-alloys, the entrapped gas within Mg-alloy might be more efficiently consumed due to the relatively high reactivity of magnesium. However, research into the entrainment defects within Mg alloys has been significantly limited. In the present work, AZ91 alloy castings were produced under different carrier gas atmospheres (i.e., SF6/CO2, SF6/air). The evolution processes of the entrainment defects contained in AZ91 alloy were suggested according to the microstructure inspections and thermodynamic calculations. The defects formed in the different atmospheres have a similar sandwich-like structure, but their oxide films contained different combinations of compounds. The use of carrier gases, which were associated with different entrained-gas consumption rates, affected the reproducibility of AZ91 castings.

    연행 결함(이중 산화막 결함 또는 이중막이라고도 함)은 경합금 용융물에 잠길 때 갇힌 가스를 포함하는 공극으로 작용하여 최종 주물의 품질과 재현성을 저하시킵니다. Al-합금 주물을 사용하여 수행된 이전 간행물에서는 이 갇힌 가스가 주변 용융물과의 반응에 의해 후속적으로 소모되어 공극 부피와 연행 결함의 부정적인 영향을 줄일 수 있다고 보고했습니다. Al-합금에 비해 마그네슘의 상대적으로 높은 반응성으로 인해 Mg-합금 내에 포집된 가스가 더 효율적으로 소모될 수 있습니다. 그러나 Mg 합금 내 연행 결함에 대한 연구는 상당히 제한적이었습니다. 현재 작업에서 AZ91 합금 주물은 다양한 캐리어 가스 분위기(즉, SF6/CO2, SF6/공기)에서 생산되었습니다. AZ91 합금에 포함된 연행 결함의 진화 과정은 미세 조직 검사 및 열역학 계산에 따라 제안되었습니다. 서로 다른 분위기에서 형성된 결함은 유사한 샌드위치 구조를 갖지만 산화막에는 서로 다른 화합물 조합이 포함되어 있습니다. 다른 동반 가스 소비율과 관련된 운반 가스의 사용은 AZ91 주물의 재현성에 영향을 미쳤습니다.

    Keywords

    Magnesium alloy, Casting, Oxide film, Bifilm, Entrainment defect, Reproducibility

    1. Introduction

    As the lightest structural metal available on Earth, magnesium became one of the most attractive light metals over the last few decades. The magnesium industry has consequently experienced a rapid development in the last 20 years [1,2], indicating a large growth in demand for Mg alloys all over the world. Nowadays, the use of Mg alloys can be found in the fields of automobiles, aerospace, electronics and etc.[3,4]. It has been predicted that the global consumption of Mg metals will further increase in the future, especially in the automotive industry, as the energy efficiency requirement of both traditional and electric vehicles further push manufactures lightweight their design [3,5,6].

    The sustained growth in demand for Mg alloys motivated a wide interest in the improvement of the quality and mechanical properties of Mg-alloy castings. During a Mg-alloy casting process, surface turbulence of the melt can lead to the entrapment of a doubled-over surface film containing a small quantity of the surrounding atmosphere, thus forming an entrainment defect (also known as a double oxide film defect or bifilm) [7][8][9][10]. The random size, quantity, orientation, and placement of entrainment defects are widely accepted to be significant factors linked to the variation of casting properties [7]. In addition, Peng et al. [11] found that entrained oxides films in AZ91 alloy melt acted as filters to Al8Mn5 particles, trapping them as they settle. Mackie et al. [12] further suggested that entrained oxide films can act to trawl the intermetallic particles, causing them to cluster and form extremely large defects. The clustering of intermetallic compounds made the entrainment defects more detrimental for the casting properties.

    Most of the previous studies regarding entrainment defects were carried out on Al-alloys [7,[13][14][15][16][17][18], and a few potential methods have been suggested for diminishing their negative effect on the quality of Al-alloy castings. Nyahumwa et al.,[16] shows that the void volume within entrainment defects could be reduced by a hot isostatic pressing (HIP) process. Campbell [7] suggested the entrained gas within the defects could be consumed due to reaction with the surrounding melt, which was further verified by Raiszedeh and Griffiths [19].The effect of the entrained gas consumption on the mechanical properties of Al-alloy castings has been investigated by [8,9], suggesting that the consumption of the entrained gas promoted the improvement of the casting reproducibility.

    Compared with the investigation concerning the defects within Al-alloys, research into the entrainment defects within Mg-alloys has been significantly limited. The existence of entrainment defects has been demonstrated in Mg-alloy castings [20,21], but their behaviour, evolution, as well as entrained gas consumption are still not clear.

    In a Mg-alloy casting process, the melt is usually protected by a cover gas to avoid magnesium ignition. The cavities of sand or investment moulds are accordingly required to be flushed with the cover gas prior to the melt pouring [22]. Therefore, the entrained gas within Mg-alloy castings should contain the cover gas used in the casting process, rather than air only, which may complicate the structure and evolution of the corresponding entrainment defects.

    SF6 is a typical cover gas widely used for Mg-alloy casting processes [23][24][25]. Although this cover gas has been restricted to use in European Mg-alloy foundries, a commercial report has pointed out that this cover is still popular in global Mg-alloy industry, especially in the countries which dominated the global Mg-alloy production, such as China, Brazil, India, etc. [26]. In addition, a survey in academic publications also showed that this cover gas was widely used in recent Mg-alloy studies [27]. The protective mechanism of SF6 cover gas (i.e., the reaction between liquid Mg-alloy and SF6 cover gas) has been investigated by several previous researchers, but the formation process of the surface oxide film is still not clearly understood, and even some published results are conflicting with each other. In early 1970s, Fruehling [28] found that the surface film formed under SF6 was MgO mainly with traces of fluorides, and suggested that SF6 was absorbed in the Mg-alloy surface film. Couling [29] further noticed that the absorbed SF6 reacted with the Mg-alloy melt to form MgF2. In last 20 years, different structures of the Mg-alloy surface films have been reported, as detailed below.(1)

    Single-layered film. Cashion [30,31] used X-ray Photoelectron Spectroscopy (XPS) and Auger Spectroscopy (AES) to identify the surface film as MgO and MgF2. He also found that composition of the film was constant throughout the thickness and the whole experimental holding time. The film observed by Cashion had a single-layered structure created from a holding time from 10 min to 100 min.(2)

    Double-layered film. Aarstad et. al [32] reported a doubled-layered surface oxide film in 2003. They observed several well-distributed MgF2 particles attached to the preliminary MgO film and grew until they covered 25–50% of the total surface area. The inward diffusion of F through the outer MgO film was the driving force for the evolution process. This double-layered structure was also supported by Xiong’s group [25,33] and Shih et al. [34].(3)

    Triple-layered film. The triple-layered film and its evolution process were reported in 2002 by Pettersen [35]. Pettersen found that the initial surface film was a MgO phase and then gradually evolved to the stable MgF2 phase by the inward diffusion of F. In the final stage, the film has a triple-layered structure with a thin O-rich interlayer between the thick top and bottom MgF2 layers.(4)

    Oxide film consisted of discrete particles. Wang et al [36] stirred the Mg-alloy surface film into the melt under a SF6 cover gas, and then inspect the entrained surface film after the solidification. They found that the entrained surface films were not continues as the protective surface films reported by other researchers but composed of discrete particles. The young oxide film was composed of MgO nano-sized oxide particles, while the old oxide films consist of coarse particles (about 1  µm in average size) on one side that contained fluorides and nitrides.

    The oxide films of a Mg-alloy melt surface or an entrained gas are both formed due to the reaction between liquid Mg-alloy and the cover gas, thus the above-mentioned research regarding the Mg-alloy surface film gives valuable insights into the evolution of entrainment defects. The protective mechanism of SF6 cover gas (i.e., formation of a Mg-alloy surface film) therefore indicated a potential complicated evolution process of the corresponding entrainment defects.

    However, it should be noted that the formation of a surface film on a Mg-alloy melt is in a different situation to the consumption of an entrained gas that is submerged into the melt. For example, a sufficient amount of cover gas was supported during the surface film formation in the studies previously mentioned, which suppressed the depletion of the cover gas. In contrast, the amount of entrained gas within a Mg-alloy melt is finite, and the entrained gas may become fully depleted. Mirak [37] introduced 3.5%SF6/air bubbles into a pure Mg-alloy melt solidifying in a specially designed permanent mould. It was found that the gas bubbles were entirely consumed, and the corresponding oxide film was a mixture of MgO and MgF2. However, the nucleation sites (such as the MgF2 spots observed by Aarstad [32] and Xiong [25,33]) were not observed. Mirak also speculated that the MgF2 formed prior to MgO in the oxide film based on the composition analysis, which was opposite to the surface film formation process reported in previous literatures (i.e., MgO formed prior to MgF2). Mirak’s work indicated that the oxide-film formation of an entrained gas may be quite different from that of surface films, but he did not reveal the structure and evolution of the oxide films.

    In addition, the use of carrier gas in the cover gases also influenced the reaction between the cover gas and the liquid Mg-alloy. SF6/air required a higher content of SF6 than did a SF6/CO2 carrier gas [38], to avoid the ignition of molten magnesium, revealing different gas-consumption rates. Liang et.al [39] suggested that carbon was formed in the surface film when CO2 was used as a carrier gas, which was different from the films formed in SF6/air. An investigation into Mg combustion [40] reported a detection of Mg2C3 in the Mg-alloy sample after burning in CO2, which not only supported Liang’s results, but also indicated a potential formation of Mg carbides in double oxide film defects.

    The work reported here is an investigation into the behaviour and evolution of entrainment defects formed in AZ91 Mg-alloy castings, protected by different cover gases (i.e., SF6/air and SF6/CO2). These carrier gases have different protectability for liquid Mg alloy, which may be therefore associated with different consumption rates and evolution processes of the corresponding entrained gases. The effect of the entrained-gas consumption on the reproducibility of AZ91 castings was also studied.

    2. Experiment

    2.1. Melting and casting

    Three kilograms AZ91 alloy was melted in a mild steel crucible at 700 ± 5 °C. The composition of the AZ91 alloy has been shown in Table 1. Prior to heating, all oxide scale on the ingot surface was removed by machining. The cover gases used were 0.5%SF6/air or 0.5%SF6/CO2 (vol.%) at a flow rate of 6 L/min for different castings. The melt was degassed by argon with a flow rate of 0.3 L/min for 15 min [41,42], and then poured into sand moulds. Prior to pouring, the sand mould cavity was flushed with the cover gas for 20 min [22]. The residual melt (around 1 kg) was solidified in the crucible.

    Table 1. Composition (wt.%) of the AZ91 alloy used in this study.

    AlZnMnSiFeNiMg
    9.40.610.150.020.0050.0017Residual

    Fig. 1(a) shows the dimensions of the casting with runners. A top-filling system was deliberately used to generate entrainment defects in the final castings. Green and Campbell [7,43] suggested that a top-filling system caused more entrainment events (i.e., bifilms) during a casting process, compared with a bottom-filling system. A melt flow simulation (Flow-3D software) of this mould, using Reilly’s model [44] regarding the entrainment events, also predicted that a large amount of bifilms would be contained in the final casting (denoted by the black particles in Fig. 1b).

    Fig. 1. (a) Dimensions of the casting with runners (unit: mm), (b) a melt flow simulation using Flow-3D software together with Reilly's model[44], predicted that a large amount of bifilms (denoted by the black particles) would be contained in the final casting. (c) A solidification simulation using Pro-cast software showed that no shrinkage defect was contained in the final casting.

    Shrinkage defects also affect the mechanical properties and reproducibility of castings. Since this study focused on the effect of bifilms on the casting quality, the mould has been deliberately designed to avoid generating shrinkage defects. A solidification simulation using ProCAST software showed that no shrinkage defect would be contained in the final casting, as shown in Fig. 1c. The casting soundness has also been confirmed using a real time X-ray prior to the test bar machining.

    The sand moulds were made from resin-bonded silica sand, containing 1wt. % PEPSET 5230 resin and 1wt. % PEPSET 5112 catalyst. The sand also contained 2 wt.% Na2SiF6 to act as an inhibitor [45]. The pouring temperature was 700 ± 5 °C. After the solidification, a section of the runner bars was sent to the Sci-Lab Analytical Ltd for a H-content analysis (LECO analysis), and all the H-content measurements were carried out on the 5th day after the casting process. Each of the castings was machined into 40 test bars for a tensile strength test, using a Zwick 1484 tensile test machine with a clip extensometer. The fracture surfaces of the broken test bars were examined using Scanning Electron Microscope (SEM, Philips JEOL7000) with an accelerating voltage of 5–15 kV. The fractured test bars, residual Mg-alloy solidified in the crucible, and the casting runners were then sectioned, polished and also inspected using the same SEM. The cross-section of the oxide film found on the test-bar fracture surface was exposed by the Focused Ion Beam milling technique (FIB), using a CFEI Quanta 3D FEG FIB-SEM. The oxide film required to be analysed was coated with a platinum layer. Then, a gallium ion beam, accelerated to 30 kV, milled the material substrate surrounding the platinum coated area to expose the cross section of the oxide film. EDS analysis of the oxide film’s cross section was carried out using the FIB equipment at accelerating voltage of 30 kV.

    2.2. Oxidation cell

    As previously mentioned, several past researchers investigated the protective film formed on a Mg-alloy melt surface [38,39,[46][47][48][49][50][51][52]. During these experiments, the amount of cover gas used was sufficient, thus suppressing the depletion of fluorides in the cover gas. The experiment described in this section used a sealed oxidation cell, which limited the supply of cover gas, to study the evolution of the oxide films of entrainment defects. The cover gas contained in the oxidation cell was regarded as large-size “entrained bubble”.

    As shown in Fig. 2, the main body of the oxidation cell was a closed-end mild steel tube which had an inner length of 400 mm, and an inner diameter of 32 mm. A water-cooled copper tube was wrapped around the upper section of the cell. When the tube was heated, the cooling system created a temperature difference between the upper and lower sections, causing the interior gas to convect within the tube. The temperature was monitored by a type-K thermocouple located at the top of the crucible. Nie et al. [53] suggested that the SF6 cover gas would react with the steel wall of the holding furnace when they investigated the surface film of a Mg-alloy melt. To avoid this reaction, the interior surface of the steel oxidation cell (shown in Fig. 2) and the upper half section of the thermocouple were coated with boron nitride (the Mg-alloy was not in contact with boron nitride).

    Fig. 2. Schematic of the oxidation cell used to study the evolution of the oxide films of the entrainment defects (unit mm).

    During the experiment, a block of solid AZ91 alloy was placed in a magnesia crucible located at the bottom of the oxidation cell. The cell was heated to 100 °C in an electric resistance furnace under a gas flow rate of 1 L/min. The cell was held at this temperature for 20 min, to replace the original trapped atmosphere (i.e. air). Then, the oxidation cell was further heated to 700 °C, melting the AZ91 sample. The gas inlet and exit valves were then closed, creating a sealed environment for oxidation under a limited supply of cover gas. The oxidation cell was then held at 700 ± 10 °C for periods of time from 5 min to 30 min in 5-min intervals. At the end of each holding time, the cell was quenched in water. After cooling to room temperature, the oxidised sample was sectioned, polished, and subsequently examined by SEM.

    3. Results

    3.1. Structure and composition of the entrainment defects formed in SF6/air

    The structure and composition of the entrainment defect formed in the AZ91 castings under a cover gas of 0.5%SF6/air was observed by SEM and EDS. The results indicate that there exist two types of entrainment defects which are sketched in Fig. 3: (1) Type A defect whose oxide film has a traditional single-layered structure and (2) Type B defect, whose oxide film has two layers. The details of these defects were introduced in the following. Here it should be noticed that, as the entrainment defects are also known as biofilms or double oxide film, the oxide films of Type B defect were referred to as “multi-layered oxide film” or “multi-layered structure” in the present work to avoid a confusing description such as “the double-layered oxide film of a double oxide film defect”.

    Fig. 3. Schematic of the different types of entrainment defects found in AZ91 castings. (a) Type A defect with a single-layered oxide film and (b) Type B defect with two-layered oxide film.

    Fig. 4(a-b) shows a Type A defect having a compact single-layered oxide film with about 0.4 µm thickness. Oxygen, fluorine, magnesium and aluminium were detected in this film (Fig. 4c). It is speculated that oxide film is the mixture of fluoride and oxide of magnesium and aluminium. The detection of fluorine revealed that an entrained cover gas was contained in the formation of this defect. That is to say that the pores shown in Fig. 4(a) were not shrinkage defects or hydrogen porosity, but entrainment defects. The detection of aluminium was different with Xiong and Wang’s previous study [47,48], which showed that no aluminium was contained in their surface film of an AZ91 melt protected by a SF6 cover gas. Sulphur could not be clearly recognized in the element map, but there was a S-peak in the corresponding ESD spectrum.

    Fig. 4. (a) A Type A entrainment defect formed in SF6/air and having a single-layered oxide film, (b) the oxide film of this defect, (c) SEM-EDS element maps (using Philips JEOL7000) corresponding to the area highlighted in (b).

    Fig. 5(a-b) shows a Type B entrainment defect having a multi-layered oxide film. The compact outer layers of the oxide films were enriched with fluorine and oxygen (Fig. 5c), while their relatively porous inner layers were only enriched with oxygen (i.e., poor in fluorine) and partly grew together, thus forming a sandwich-like structure. Therefore, it is speculated that the outer layer is the mixture of fluoride and oxide, while the inner layer is mainly oxide. Sulphur could only be recognized in the EDX spectrum and could not be clearly identified in the element map, which might be due to the small S-content in the cover gas (i.e., 0.5% volume content of SF6 in the cover gas). In this oxide film, aluminium was contained in the outer layer of this oxide film but could not be clearly detected in the inner layer. Moreover, the distribution of Al seems to be uneven. It can be found that, in the right side of the defect, aluminium exists in the film but its concentration can not be identified to be higher than the matrix. However, there is a small area with much higher aluminium concentration in the left side of the defect. Such an uneven distribution of aluminium was also observed in other defects (shown in the following), and it is the result of the formation of some oxide particles in or under the film.

    Fig. 5. (a) A Type B entrainment defect formed in SF6/air and having a multi-layered oxide film, (b) the oxide films of this defect have grown together, (c) SEM-EDS element maps (using Philips JEOL7000) corresponding to the area shown in (b).

    Figs. 4 and 5 show cross sectional observations of the entrainment defects formed in the AZ91 alloy sample cast under a cover gas of SF6/air. It is not sufficient to characterize the entrainment defects only by the figures observed from the two-dimensional section. To have a further understanding, the surface of the entrainment defects (i.e. the oxide film) was further studied by observing the fracture surface of the test bars.

    Fig. 6(a) shows fracture surfaces of an AZ91 alloy tensile test bar produced in SF6/air. Symmetrical dark regions can be seen on both sides of the fracture surfaces. Fig. 6(b) shows boundaries between the dark and bright regions. The bright region consisted of jagged and broken features, while the surface of the dark region was relatively smooth and flat. In addition, the EDS results (Fig. 6c-d and Table 2) show that fluorine, oxygen, sulphur, and nitrogen were only detected in the dark regions, indicating that the dark regions were surface protective films entrained into the melt. Therefore, it could be suggested that the dark regions were an entrainment defect with consideration of their symmetrical nature. Similar defects on fracture surfaces of Al-alloy castings have been previously reported [7]Nitrides were only found in the oxide films on the test-bar fracture surfaces but never detected in the cross-sectional samples shown in Figs. 4 and 5. An underlying reason is that the nitrides contained in these samples may have hydrolysed during the sample polishing process [54].

    Fig. 6. (a) A pair of the fracture surfaces of a AZ91 alloy tensile test bar produced under a cover gas of SF6/air. The dimension of the fracture surface is 5 mm × 6 mm, (b) a section of the boundary between the dark and bright regions shown in (a), (c-d) EDS spectrum of the (c) bright regions and (d) dark regions, (e) schematic of an entrainment defect contained in a test bar.

    Table 2. EDS results (wt.%) corresponding to the regions shown in Fig. 6 (cover gas: SF6/air).

    Empty CellCOMgFAlZnSN
    Dark region in Fig. 6(b)3.481.3279.130.4713.630.570.080.73
    Bright region in Fig. 6(b)3.5884.4811.250.68

    In conjunction with the cross-sectional observation of the defects shown in Figs. 4 and 5, the structure of an entrainment defect contained in a tensile test bar was sketched as shown in Fig. 6(e). The defect contained an entrained gas enclosed by its oxide film, creating a void section inside the test bar. When the tensile force applied on the defect during the fracture process, the crack was initiated at the void section and propagated along the entrainment defect, since cracks would be propagated along the weakest path [55]. Therefore, when the test bar was finally fractured, the oxide films of entrainment defect appeared on both fracture surfaces of the test bar, as shown in Fig. 6(a).

    3.2. Structure and composition of the entrainment defects formed in SF6/CO2

    Similar to the entrainment defect formed in SF6/air, the defects formed under a cover gas of 0.5%SF6/CO2 also had two types of oxide films (i.e., single-layered and multi-layered types). Fig. 7(a) shows an example of the entrainment defects containing a multi-layered oxide film. A magnified observation to the defect (Fig. 7b) shows that the inner layers of the oxide films had grown together, presenting a sandwich-like structure, which was similar to the defects formed in an atmosphere of SF6/air (Fig. 5b). An EDS spectrum (Fig. 7c) revealed that the joint area (inner layer) of this sandwich-like structure mainly contained magnesium oxides. Peaks of fluorine, sulphur, and aluminium were recognized in this EDS spectrum, but their amount was relatively small. In contrast, the outer layers of the oxide films were compact and composed of a mixture of fluorides and oxides (Fig. 7d-e).

    Fig. 7. (a) An example of entrainment defects formed in SF6/CO2 and having a multi-layered oxide film, (b) magnified observation of the defect, showing the inner layer of the oxide films has grown together, (c) EDS spectrum of the point denoted in (b), (d) outer layer of the oxide film, (e) SEM-EDS element maps (using Philips JEOL7000) corresponding to the area shown in (d).

    Fig. 8(a) shows an entrainment defect on the fracture surfaces of an AZ91 alloy tensile test bar, which was produced in an atmosphere of 0.5%SF6/CO2. The corresponding EDS results (Table 3) showed that oxide film contained fluorides and oxides. Sulphur and nitrogen were not detected. Besides, a magnified observation (Fig. 8b) indicated spots on the oxide film surface. The diameter of the spots ranged from hundreds of nanometres to a few micron meters.

    Fig. 8. (a) A pair of the fracture surfaces of a AZ91 alloy tensile test bar, produced in an atmosphere of SF6/CO2. The dimension of the fracture surface is 5 mm × 6 mm, (b) surface appearance of the oxide films on the fracture surfaces, showing spots on the film surface.

    To further reveal the structure and composition of the oxide film clearly, the cross-section of the oxide film on a test-bar fracture surface was onsite exposed using the FIB technique (Fig. 9). As shown in Fig. 9a, a continuous oxide film was found between the platinum coating layer and the Mg-Al alloy substrate. Fig. 9 (b-c) shows a magnified observation to oxide films, indicating a multi-layered structure (denoted by the red box in Fig. 9c). The bottom layer was enriched with fluorine and oxygen and should be the mixture of fluoride and oxide, which was similar to the “outer layer” shown in Figs. 5 and 7, while the only-oxygen-enriched top layer was similar to the “inner layer” shown in Figs. 5 and 7.

    Fig. 9. (a) A cross-sectional observation of the oxide film on the fracture surface of the AZ91 casting produced in SF6/CO2, exposed by FIB, (b) a magnified observation of area highlighted in (a), and (c) SEM-EDS elements map of the area shown in (b), obtained by CFEI Quanta 3D FEG FIB-SEM.

    Except the continuous film, some individual particles were also observed in or below the continuous film, as shown in Fig. 9. An Al-enriched particle was detected in the left side of the oxide film shown in Fig. 9b and might be speculated to be spinel Mg2AlO4 because it also contains abundant magnesium and oxygen elements. The existing of such Mg2AlO4 particles is responsible for the high concentration of aluminium in small areas of the observed film and the uneven distribution of aluminium, as shown in Fig. 5(c). Here it should be emphasized that, although the other part of the bottom layer of the continuous oxide film contains less aluminium than this Al-enriched particle, the Fig. 9c indicated that the amount of aluminium in this bottom layer was still non-negligible, especially when comparing with the outer layer of the film. Below the right side of the oxide film shown in Fig. 9b, a particle was detected and speculated to be MgO because it is rich in Mg and O. According to Wang’s result [56], lots of discrete MgO particles can be formed on the surface of the Mg melt by the oxidation of Mg melt and Mg vapor. The MgO particles observed in our present work may be formed due to the same reasons. While, due to the differences in experimental conditions, less Mg melt can be vapored or react with O2, thus only a few of MgO particles formed in our work. An enrichment of carbon was also found in the film, revealing that CO2 was able to react with the melt, thus forming carbon or carbides. This carbon concentration was consistent with the relatively high carbon content of the oxide film shown in Table 3 (i.e., the dark region). In the area next to the oxide film.

    Table 3. EDS results (wt.%) corresponding to the regions shown in Fig. 8 (cover gas: SF6/ CO2).

    Empty CellCOMgFAlZnSN
    Dark region in Fig. 8(a)7.253.6469.823.827.030.86
    Bright region in Fig. 8(a)2.100.4482.8313.261.36

    This cross-sectional observation of the oxide film on a test bar fracture surface (Fig. 9) further verified the schematic of the entrainment defect shown in Fig. 6(e). The entrainment defects formed in different atmospheres of SF6/CO2 and SF6/air had similar structures, but their compositions were different.

    3.3. Evolution of the oxide films in the oxidation cell

    The results in Section 3.1 and 3.2 have shown the structures and compositions of entrainment defects formed in AZ91 castings under cover gases of SF6/air and SF6/CO2. Different stages of the oxidation reaction may lead to the different structures and compositions of entrainment defects. Although Campbell has conjectured that an entrained gas may react with the surrounding melt, it is rarely reported that the reaction occurring between the Mg-alloy melt and entrapped cover gas. Previous researchers normally focus on the reaction between a Mg-alloy melt and the cover gas in an open environment [38,39,[46][47][48][49][50][51][52], which was different from the situation of a cover gas trapped into the melt. To further understand the formation of the entrainment defect in an AZ91 alloy, the evolution process of oxide films of the entrainment defect was further studied using an oxidation cell.

    Fig. 10 (a and d) shows a surface film held for 5 min in the oxidation cell, protected by 0.5%SF6/air. There was only one single layer consisting of fluoride and oxide (MgF2 and MgO). In this surface film. Sulphur was detected in the EDS spectrum, but its amount was too small to be recognized in the element map. The structure and composition of this oxide film was similar to the single-layered films of entrainment defects shown in Fig. 4.

    Fig. 10. Oxide films formed in the oxidation cell under a cover gas of 0.5%SF6/air and held at 700 °C for (a) 5 min; (b) 10 min; (c) 30 min, and (d-f) the SEM-EDS element maps (using Philips JEOL7000) corresponding to the oxide film shown in (a-c) respectively, (d) 5 min; (e) 10 min; (f) 30 min. The red points in (c and f) are the location references, denoting the boundary of the F-enriched layer in different element maps.

    After a holding time of 10 min, a thin (O, S)-enriched top layer (around 700 nm) appeared upon the preliminary F-enriched film, forming a multi-layered structure, as shown in Fig. 10(b and e). The thickness of the (O, S)-enriched top layer increased with increased holding time. As shown in Fig. 10(c and f), the oxide film held for 30 min also had a multi-layered structure, but the thickness of its (O, S)-enriched top layer (around 2.5 µm) was higher than the that of the 10-min oxide film. The multi-layered oxide films shown in Fig. 10(b-c) presented a similar appearance to the films of the sandwich-like defect shown in Fig. 5.

    The different structures of the oxide films shown in Fig. 10 indicated that fluorides in the cover gas would be preferentially consumed due to the reaction with the AZ91 alloy melt. After the depletion of fluorides, the residual cover gas reacted further with the liquid AZ91 alloy, forming the top (O, S)-enriched layer in the oxide film. Therefore, the different structures and compositions of entrainment defects shown in Figs. 4 and 5 may be due to an ongoing oxidation reaction between melt and entrapped cover gas.

    This multi-layered structure has not been reported in previous publications concerning the protective surface film formed on a Mg-alloy melt [38,[46][47][48][49][50][51]. This may be due to the fact that previous researchers carried out their experiments with an un-limited amount of cover gas, creating a situation where the fluorides in the cover gas were not able to become depleted. Therefore, the oxide film of an entrainment defect had behaviour traits similar to the oxide films shown in Fig. 10, but different from the oxide films formed on the Mg-alloy melt surface reported in [38,[46][47][48][49][50][51].

    Similar with the oxide films held in SF6/air, the oxide films formed in SF6/CO2 also had different structures with different holding times in the oxidation cell. Fig. 11(a) shows an oxide film, held on an AZ91 melt surface under a cover gas of 0.5%SF6/CO2 for 5 min. This film had a single-layered structure consisting of MgF2. The existence of MgO could not be confirmed in this film. After the holding time of 30 min, the film had a multi-layered structure; the inner layer was of a compact and uniform appearance and composed of MgF2, while the outer layer is the mixture of MgF2 and MgO. Sulphur was not detected in this film, which was different from the surface film formed in 0.5%SF6/air. Therefore, fluorides in the cover gas of 0.5%SF6/CO2 were also preferentially consumed at an early stage of the film growth process. Compared with the film formed in SF6/air, the MgO in film formed in SF6/CO2 appeared later and sulphide did not appear within 30 min. It may mean that the formation and evolution of film in SF6/air is faster than SF6/CO2. CO2 may have subsequently reacted with the melt to form MgO, while sulphur-containing compounds accumulated in the cover gas and reacted to form sulphide in very late stage (may after 30 min in oxidation cell).

    Fig. 11. Oxide films formed in the oxidation cell under a cover gas of 0.5%SF6/CO2, and their SEM-EDS element maps (using Philips JEOL7000). They were held at 700 °C for (a) 5 min; (b) 30 min. The red points in (b) are the location references, denoting the boundary between the top and bottom layers in the oxide film.

    4. Discussion

    4.1. Evolution of entrainment defects formed in SF6/air

    HSC software from Outokumpu HSC Chemistry for Windows (http://www.hsc-chemistry.net/) was used to carry out thermodynamic calculations needed to explore the reactions which might occur between the trapped gases and liquid AZ91 alloy. The solutions to the calculations suggest which products are most likely to form in the reaction process between a small amount of cover gas (i.e., the amount within a trapped bubble) and the AZ91-alloy melt.

    In the trials, the pressure was set to 1 atm, and the temperature set to 700 °C. The amount of the cover gas was assumed to be 7 × 10−7 kg, with a volume of approximately 0.57 cm3 (3.14 × 10−8 kmol) for 0.5%SF6/air, and 0.35 cm3 (3.12 × 10−8 kmol) for 0.5%SF6/CO2. The amount of the AZ91 alloy melt in contact with the trapped gas was assumed to be sufficient to complete all reactions. The decomposition products of SF6 were SF5, SF4, SF3, SF2, F2, S(g), S2(g) and F(g) [57][58][59][60].

    Fig. 12 shows the equilibrium diagram of the thermodynamic calculation of the reaction between the AZ91 alloy and 0.5%SF6/air. In the diagram, the reactants and products with less than 10−15 kmol have not been shown, as this was 5 orders of magnitude less than the amount of SF6 present (≈ 1.57 × 10−10 kmol) and therefore would not affect the observed process in a practical way.

    Fig. 12. An equilibrium diagram for the reaction between 7e-7 kg 0.5%SF6/air and a sufficient amount of AZ91 alloy. The X axis is the amount of AZ91 alloy melt having reacted with the entrained gas, and the vertical Y-axis is the amount of the reactants and products.

    This reaction process could be divided into 3 stages.

    Stage 1: The formation of fluorides. the AZ91 melt preferentially reacted with SF6 and its decomposition products, producing MgF2, AlF3, and ZnF2. However, the amount of ZnF2 may have been too small to be detected practically (1.25 × 10−12 kmol of ZnF2 compared with 3 × 10−10 kmol of MgF2), which may be the reason why Zn was not detected in any the oxide films shown in Sections 3.13.3. Meanwhile, sulphur accumulated in the residual gas as SO2.

    Stage 2: The formation of oxides. After the liquid AZ91 alloy had depleted all the available fluorides in the entrapped gas, the amount of AlF3 and ZnF2 quickly reduced due to a reaction with Mg. O2(g) and SO2 reacted with the AZ91 melt, forming MgO, Al2O3, MgAl2O4, ZnO, ZnSO4 and MgSO4. However, the amount of ZnO and ZnSO4 would have been too small to be found practically by EDS (e.g. 9.5 × 10−12 kmol of ZnO,1.38 × 10−14 kmol of ZnSO4, in contrast to 4.68 × 10−10 kmol of MgF2, when the amount of AZ91 on the X-axis is 2.5 × 10−9 kmol). In the experimental cases, the concentration of F in the cover gas is very low, whole the concentration f O is much higher. Therefore, the stage 1 and 2, i.e, the formation of fluoride and oxide may happen simultaneously at the beginning of the reaction, resulting in the formation of a singer-layered mixture of fluoride and oxide, as shown in Figs. 4 and 10(a). While an inner layer consisted of oxides but fluorides could form after the complete depletion of F element in the cover gas.

    Stages 1- 2 theoretically verified the formation process of the multi-layered structure shown in Fig. 10.

    The amount of MgAl2O4 and Al2O3 in the oxide film was of a sufficient amount to be detected, which was consistent with the oxide films shown in Fig. 4. However, the existence of aluminium could not be recognized in the oxide films grown in the oxidation cell, as shown in Fig. 10. This absence of Al may be due to the following reactions between the surface film and AZ91 alloy melt:(1)

    Al2O3 + 3Mg + = 3MgO + 2Al, △G(700 °C) = -119.82 kJ/mol(2)

    Mg + MgAl2O4 = MgO + Al, △G(700 °C) =-106.34 kJ/molwhich could not be simulated by the HSC software since the thermodynamic calculation was carried out under an assumption that the reactants were in full contact with each other. However, in a practical process, the AZ91 melt and the cover gas would not be able to be in contact with each other completely, due to the existence of the protective surface film.

    Stage 3: The formation of Sulphide and nitride. After a holding time of 30 min, the gas-phase fluorides and oxides in the oxidation cell had become depleted, allowing the melt reaction with the residual gas, forming an additional sulphur-enriched layer upon the initial F-enriched or (F, O)-enriched surface film, thus resulting in the observed multi-layered structure shown in Fig. 10 (b and c). Besides, nitrogen reacted with the AZ91 melt until all reactions were completed. The oxide film shown in Fig. 6 may correspond to this reaction stage due to its nitride content. However, the results shows that the nitrides were not detected in the polished samples shown in Figs. 4 and 5, but only found on the test bar fracture surfaces. The nitrides may have hydrolysed during the sample preparation process, as follows [54]:(3)

    Mg3N2 + 6H2O =3Mg(OH)2 + 2NH3↑(4)

    AlN+ 3H2O =Al(OH)3 + NH3

    In addition, Schmidt et al. [61] found that Mg3N2 and AlN could react to form ternary nitrides (Mg3AlnNn+2, n= 1, 2, 3…). HSC software did not contain the database of ternary nitrides, and it could not be added into the calculation. The oxide films in this stage may also contain ternary nitrides.

    4.2. Evolution of entrainment defects formed in SF6/CO2

    Fig. 13 shows the results of the thermodynamic calculation between AZ91 alloy and 0.5%SF6/CO2. This reaction processes can also be divided into three stages.

    Fig. 13. An equilibrium diagram for the reaction between 7e-7 kg 0.5%SF6/CO2 and a sufficient amount of AZ91 alloy. The X axis denotes the amount of Mg alloy melt having reacted with the entrained gas, and the vertical Y-axis denotes the amounts of the reactants and products.

    Stage 1: The formation of fluorides. SF6 and its decomposition products were consumed by the AZ91 melt, forming MgF2, AlF3, and ZnF2. As in the reaction of AZ91 in 0.5%SF6/air, the amount of ZnF2 was too small to be detected practically (1.51 × 10−13 kmol of ZnF2 compared with 2.67 × 10−10 kmol of MgF2). Sulphur accumulated in the residual trapped gas as S2(g) and a portion of the S2(g) reacted with CO2, to form SO2 and CO. The products in this reaction stage were consistent with the film shown in Fig. 11(a), which had a single layer structure that contained fluorides only.

    Stage 2: The formation of oxides. AlF3 and ZnF2 reacted with the Mg in the AZ91 melt, forming MgF2, Al and Zn. The SO2 began to be consumed, producing oxides in the surface film and S2(g) in the cover gas. Meanwhile, the CO2 directly reacted with the AZ91 melt, forming CO, MgO, ZnO, and Al2O3. The oxide films shown in Figs. 9 and 11(b) may correspond to this reaction stage due to their oxygen-enriched layer and multi-layered structure.

    The CO in the cover gas could further react with the AZ91 melt, producing C. This carbon may further react with Mg to form Mg carbides, when the temperature reduced (during solidification period) [62]. This may be the reason for the high carbon content in the oxide film shown in Figs. 89. Liang et al. [39] also reported carbon-detection in an AZ91 alloy surface film protected by SO2/CO2. The produced Al2O3 may be further combined with MgO, forming MgAl2O4 [63]. As discussed in Section 4.1, the alumina and spinel can react with Mg, causing an absence of aluminium in the surface films, as shown in Fig. 11.

    Stage 3: The formation of Sulphide. the AZ91 melt began to consume S2(g) in the residual entrapped gas, forming ZnS and MgS. These reactions did not occur until the last stage of the reaction process, which could be the reason why the S-content in the defect shown Fig. 7(c) was small.

    In summary, thermodynamic calculations indicate that the AZ91 melt will react with the cover gas to form fluorides firstly, then oxides and sulphides in the last. The oxide film in the different reaction stages would have different structures and compositions.

    4.3. Effect of the carrier gases on consumption of the entrained gas and the reproducibility of AZ91 castings

    The evolution processes of entrainment defects, formed in SF6/air and SF6/CO2, have been suggested in Sections 4.1 and 4.2. The theoretical calculations were verified with respect to the corresponding oxide films found in practical samples. The atmosphere within an entrainment defect could be efficiently consumed due to the reaction with liquid Mg-alloy, in a scenario dissimilar to the Al-alloy system (i.e., nitrogen in an entrained air bubble would not efficiently react with Al-alloy melt [64,65], however, nitrogen would be more readily consumed in liquid Mg alloys, commonly referred to as “nitrogen burning” [66]).

    The reaction between the entrained gas and the surrounding liquid Mg-alloy converted the entrained gas into solid compounds (e.g. MgO) within the oxide film, thus reducing the void volume of the entrainment defect and hence probably causing a collapse of the defect (e.g., if an entrained gas of air was depleted by the surrounding liquid Mg-alloy, under an assumption that the melt temperature is 700 °C and the depth of liquid Mg-alloy is 10 cm, the total volume of the final solid products would be 0.044% of the initial volume taken by the entrapped air).

    The relationship between the void volume reduction of entrainment defects and the corresponding casting properties has been widely studied in Al-alloy castings. Nyahumwa and Campbell [16] reported that the Hot Isostatic Pressing (HIP) process caused the entrainment defects in Al-alloy castings to collapse and their oxide surfaces forced into contact. The fatigue lives of their castings were improved after HIP. Nyahumwa and Campbell [16] also suggested a potential bonding of the double oxide films that were in contact with each other, but there was no direct evidence to support this. This binding phenomenon was further investigated by Aryafar et.al.[8], who re-melted two Al-alloy bars with oxide skins in a steel tube and then carried out a tensile strength test on the solidified sample. They found that the oxide skins of the Al-alloy bars strongly bonded with each other and became even stronger with an extension of the melt holding time, indicating a potential “healing” phenomenon due to the consumption of the entrained gas within the double oxide film structure. In addition, Raidszadeh and Griffiths [9,19] successfully reduced the negative effect of entrainment defects on the reproducibility of Al-alloy castings, by extending the melt holding time before solidification, which allowed the entrained gas to have a longer time to react with the surrounding melt.

    With consideration of the previous work mentioned, the consumption of the entrained gas in Mg-alloy castings may diminish the negative effect of entrainment defects in the following two ways.

    (1) Bonding phenomenon of the double oxide films. The sandwich-like structure shown in Fig. 5 and 7 indicated a potential bonding of the double oxide film structure. However, more evidence is required to quantify the increase in strength due to the bonding of the oxide films.

    (2) Void volume reduction of entrainment defects. The positive effect of void-volume reduction on the quality of castings has been widely demonstrated by the HIP process [67]. As the evolution processes discussed in Section 4.14.2, the oxide films of entrainment defects can grow together due to an ongoing reaction between the entrained gas and surrounding AZ91 alloy melt. The volume of the final solid products was significant small compared with the entrained gas (i.e., 0.044% as previously mentioned).

    Therefore, the consumption rate of the entrained gas (i.e., the growth rate of oxide films) may be a critical parameter for improving the quality of AZ91 alloy castings. The oxide film growth rate in the oxidization cell was accordingly further investigated.

    Fig. 14 shows a comparison of the surface film growth rates in different cover gases (i.e., 0.5%SF6/air and 0.5%SF6/CO2). 15 random points on each sample were selected for film thickness measurements. The 95% confidence interval (95%CI) was computed under an assumption that the variation of the film thickness followed a Gaussian distribution. It can be seen that all the surface films formed in 0.5%SF6/air grew faster than those formed in 0.5%SF6/CO2. The different growth rates suggested that the entrained-gas consumption rate of 0.5%SF6/air was higher than that of 0.5%SF6/CO2, which was more beneficial for the consumption of the entrained gas.

    Fig. 14. A comparison of the AZ91 alloy oxide film growth rates in 0.5%SF6/air and 0.5%SF6/CO2

    It should be noted that, in the oxidation cell, the contact area of liquid AZ91 alloy and cover gas (i.e. the size of the crucible) was relatively small with consideration of the large volume of melt and gas. Consequently, the holding time for the oxide film growth within the oxidation cell was comparatively long (i.e., 5–30 min). However, the entrainment defects contained in a real casting are comparatively very small (i.e., a few microns size as shown in Figs. 36, and [7]), and the entrained gas is fully enclosed by the surrounding melt, creating a relatively large contact area. Hence the reaction time for cover gas and the AZ91 alloy melt may be comparatively short. In addition, the solidification time of real Mg-alloy sand castings can be a few minutes (e.g. Guo [68] reported that a Mg-alloy sand casting with 60 mm diameter required 4 min to be solidified). Therefore, it can be expected that an entrained gas trapped during an Mg-alloy melt pouring process will be readily consumed by the surrounding melt, especially for sand castings and large-size castings, where solidification times are long.

    Therefore, the different cover gases (0.5%SF6/air and 0.5%SF6/CO2) associated with different consumption rates of the entrained gases may affect the reproducibility of the final castings. To verify this assumption, the AZ91 castings produced in 0.5%SF6/air and 0.5%SF6/CO2 were machined into test bars for mechanical evaluation. A Weibull analysis was carried out using both linear least square (LLS) method and non-linear least square (non-LLS) method [69].

    Fig. 15(a-b) shows a traditional 2-p linearized Weibull plot of the UTS and elongation of the AZ91 alloy castings, obtained by the LLS method. The estimator used is P= (i-0.5)/N, which was suggested to cause the lowest bias among all the popular estimators [69,70]. The casting produced in SF6/air has an UTS Weibull moduli of 16.9, and an elongation Weibull moduli of 5.0. In contrast, the UTS and elongation Weibull modulus of the casting produced in SF6/CO2 are 7.7 and 2.7 respectively, suggesting that the reproducibility of the casting protected by SF6/CO2 were much lower than that produced in SF6/air.

    Fig. 15. The Weibull modulus of AZ91 castings produced in different atmospheres, estimated by (a-b) the linear least square method, (c-d) the non-linear least square method, where SSR is the sum of residual squares.

    In addition, the author’s previous publication [69] demonstrated a shortcoming of the linearized Weibull plots, which may cause a higher bias and incorrect R2 interruption of the Weibull estimation. A Non-LLS Weibull estimation was therefore carried out, as shown in Fig. 15 (c-d). The UTS Weibull modulus of the SF6/air casting was 20.8, while the casting produced under SF6/CO2 had a lower UTS Weibull modulus of 11.4, showing a clear difference in their reproducibility. In addition, the SF6/air elongation (El%) dataset also had a Weibull modulus (shape = 5.8) higher than the elongation dataset of SF6/CO2 (shape = 3.1). Therefore, both the LLS and Non-LLS estimations suggested that the SF6/air casting has a higher reproducibility than the SF6/CO2 casting. It supports the method that the use of air instead of CO2 contributes to a quicker consumption of the entrained gas, which may reduce the void volume within the defects. Therefore, the use of 0.5%SF6/air instead of 0.5%SF6/CO2 (which increased the consumption rate of the entrained gas) improved the reproducibility of the AZ91 castings.

    However, it should be noted that not all the Mg-alloy foundries followed the casting process used in present work. The Mg-alloy melt in present work was degassed, thus reducing the effect of hydrogen on the consumption of the entrained gas (i.e., hydrogen could diffuse into the entrained gas, potentially suppressing the depletion of the entrained gas [7,71,72]). In contrast, in Mg-alloy foundries, the Mg-alloy melt is not normally degassed, since it was widely believed that there is not a ‘gas problem’ when casting magnesium and hence no significant change in tensile properties [73]. Although studies have shown the negative effect of hydrogen on the mechanical properties of Mg-alloy castings [41,42,73], a degassing process is still not very popular in Mg-alloy foundries.

    Moreover, in present work, the sand mould cavity was flushed with the SF6 cover gas prior to pouring [22]. However, not all the Mg-alloy foundries flushed the mould cavity in this way. For example, the Stone Foundry Ltd (UK) used sulphur powder instead of the cover-gas flushing. The entrained gas within their castings may be SO2/air, rather than the protective gas.

    Therefore, although the results in present work have shown that using air instead of CO2 improved the reproducibility of the final casting, it still requires further investigations to confirm the effect of carrier gases with respect to different industrial Mg-alloy casting processes.

    7. Conclusion

    Entrainment defects formed in an AZ91 alloy were observed. Their oxide films had two types of structure: single-layered and multi-layered. The multi-layered oxide film can grow together forming a sandwich-like structure in the final casting.2.

    Both the experimental results and the theoretical thermodynamic calculations demonstrated that fluorides in the trapped gas were depleted prior to the consumption of sulphur. A three-stage evolution process of the double oxide film defects has been suggested. The oxide films contained different combinations of compounds, depending on the evolution stage. The defects formed in SF6/air had a similar structure to those formed in SF6/CO2, but the compositions of their oxide films were different. The oxide-film formation and evolution process of the entrainment defects were different from that of the Mg-alloy surface films previous reported (i.e., MgO formed prior to MgF2).3.

    The growth rate of the oxide film was demonstrated to be greater under SF6/air than SF6/CO2, contributing to a quicker consumption of the damaging entrapped gas. The reproducibility of an AZ91 alloy casting improved when using SF6/air instead of SF6/CO2.

    Acknowledgements

    The authors acknowledge funding from the EPSRC LiME grant EP/H026177/1, and the help from Dr W.D. Griffiths and Mr. Adrian Carden (University of Birmingham). The casting work was carried out in University of Birmingham.

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    Fig. 1. Schematic of lap welding for 6061/5182 aluminum alloys.

    알루미늄 합금 겹침 용접 중 용접 형성, 용융 흐름 및 입자 구조에 대한 사인파 발진 레이저 빔의 영향

    린 첸 가오 양 미시 옹 장 춘밍 왕
    Lin Chen , Gaoyang Mi , Xiong Zhang , Chunming Wang *
    중국 우한시 화중과학기술대학 재료공학부, 430074

    Effects of sinusoidal oscillating laser beam on weld formation, melt flow and grain structure during aluminum alloys lap welding

    Abstract

    A numerical model of 1.5 mm 6061/5182 aluminum alloys thin sheets lap joints under laser sinusoidal oscillation (sine) welding and laser welding (SLW) weld was developed to simulate temperature distribution and melt flow. Unlike the common energy distribution of SLW, the sinusoidal oscillation of laser beam greatly homogenized the energy distribution and reduced the energy peak. The energy peaks were located at both sides of the sine weld, resulting in the tooth-shaped sectional formation. This paper illustrated the effect of the temperature gradient (G) and solidification rate (R) on the solidification microstructure by simulation. Results indicated that the center of the sine weld had a wider area with low G/R, promoting the formation of a wider equiaxed grain zone, and the columnar grains were slenderer because of greater GR. The porosity-free and non-penetration welds were obtained by the laser sinusoidal oscillation. The reasons were that the molten pool volume was enlarged, the volume proportion of keyhole was reduced and the turbulence in the molten pool was gentled, which was observed by the high-speed imaging and simulation results of melt flow. The tensile test of both welds showed a tensile fracture form along the fusion line, and the tensile strength of sine weld was significantly better than that of the SLW weld. This was because that the wider equiaxed grain area reduced the tendency of cracks and the finer grain size close to the fracture location. Defect-free and excellent welds are of great significance to the new energy vehicles industry.

    온도 분포 및 용융 흐름을 시뮬레이션하기 위해 레이저 사인파 진동 (사인) 용접 및 레이저 용접 (SLW) 용접에서 1.5mm 6061/5182 알루미늄 합금 박판 랩 조인트 의 수치 모델이 개발되었습니다. SLW의 일반적인 에너지 분포와 달리 레이저 빔의 사인파 진동은 에너지 분포를 크게 균질화하고 에너지 피크를 줄였습니다. 에너지 피크는 사인 용접의 양쪽에 위치하여 톱니 모양의 단면이 형성되었습니다. 이 논문은 온도 구배(G)와 응고 속도 의 영향을 설명했습니다.(R) 시뮬레이션에 의한 응고 미세 구조. 결과는 사인 용접의 중심이 낮은 G/R로 더 넓은 영역을 가짐으로써 더 넓은 등축 결정립 영역의 형성을 촉진하고 더 큰 GR로 인해 주상 결정립 이 더 가늘다는 것을 나타냅니다. 다공성 및 비관통 용접은 레이저 사인파 진동에 의해 얻어졌습니다. 그 이유는 용융 풀의 부피가 확대되고 열쇠 구멍의 부피 비율이 감소하며 용융 풀의 난류가 완만해졌기 때문이며, 이는 용융 흐름의 고속 이미징 및 시뮬레이션 결과에서 관찰되었습니다. 두 용접부 의 인장시험 은 융착선을 따라 인장파괴형태를인장강도사인 용접의 경우 SLW 용접보다 훨씬 우수했습니다. 이는 등축 결정립 영역이 넓을수록 균열 경향이 감소하고 파단 위치에 근접한 입자 크기가 미세 하기 때문입니다. 결함이 없고 우수한 용접은 신에너지 자동차 산업에 매우 중요합니다.

    Fig. 1. Schematic of lap welding for 6061/5182 aluminum alloys.
    Fig. 1. Schematic of lap welding for 6061/5182 aluminum alloys.
    Fig. 2. Finite element mesh.
    Fig. 2. Finite element mesh.
    Fig. 3. Weld morphologies of cross-section and upper surface for the two welds: (a) sine pattern weld; (b) SLW weld.
    Fig. 3. Weld morphologies of cross-section and upper surface for the two welds: (a) sine pattern weld; (b) SLW weld.
    Fig. 4. Calculation of laser energy distribution: (a)-(c) sine pattern weld; (d)-(f) SLW weld.
    Fig. 4. Calculation of laser energy distribution: (a)-(c) sine pattern weld; (d)-(f) SLW weld.
    Fig. 5. The partially melted region of zone A.
    Fig. 5. The partially melted region of zone A.
    Fig. 6. The simulated profiles of melted region for the two welds: (a) SLW weld; (b) sine pattern weld.
    Fig. 6. The simulated profiles of melted region for the two welds: (a) SLW weld; (b) sine pattern weld.
    Fig. 7. The temperature field simulation results of cross section for sine pattern weld.
    Fig. 7. The temperature field simulation results of cross section for sine pattern weld.
    Fig. 8. Dynamic behavior of the molten pool at the same time interval of 0.004 s within one oscillating period: (a) SLW weld; (b) sine pattern weld.
    Fig. 8. Dynamic behavior of the molten pool at the same time interval of 0.004 s within one oscillating period: (a) SLW weld; (b) sine pattern weld.
    Fig. 9. The temperature field and flow field of the molten pool for the SLW weld: (a)~(f) t = 80 ms~100 ms.
    Fig. 9. The temperature field and flow field of the molten pool for the SLW weld: (a)~(f) t = 80 ms~100 ms.
    Fig. 10. The temperature field and flow field of the molten pool for the sine pattern weld: (a)~(f) t = 151 ms~171 ms.
    Fig. 10. The temperature field and flow field of the molten pool for the sine pattern weld: (a)~(f) t = 151 ms~171 ms.
    Fig. 11. The evolution of the molten pool volume and keyhole depth within one period.
    Fig. 11. The evolution of the molten pool volume and keyhole depth within one period.
    Fig. 12. The X-ray inspection results for the two welds: (a) SLW weld, (b) sine pattern weld.
    Fig. 12. The X-ray inspection results for the two welds: (a) SLW weld, (b) sine pattern weld.
    Fig. 13. Comparison of the solidification parameters for sine and SLW patterns: (a) the temperature field simulated results of the molten pool upper surfaces; (b) temperature gradient G and solidification rate R along the molten pool boundary isotherm from weld centerline to the fusion boundary; (c) G/R; (d) GR.
    Fig. 13. Comparison of the solidification parameters for sine and SLW patterns: (a) the temperature field simulated results of the molten pool upper surfaces; (b) temperature gradient G and solidification rate R along the molten pool boundary isotherm from weld centerline to the fusion boundary; (c) G/R; (d) GR.
    Fig. 14. The EBSD results of equiaxed grain zone in the weld center of: (a) sine pattern weld; (b) SLW weld; (c) grain size.
    Fig. 14. The EBSD results of equiaxed grain zone in the weld center of: (a) sine pattern weld; (b) SLW weld; (c) grain size.
    Fig. 15. (a) EBSD results of horizontal sections of SLW weld and sine pattern weld; (b) The columnar crystal widths of SLW weld and sine pattern weld.
    Fig. 15. (a) EBSD results of horizontal sections of SLW weld and sine pattern weld; (b) The columnar crystal widths of SLW weld and sine pattern weld.
    Fig. 16. (a) The tensile test results of the two welds; (b) Fracture location of SLW weld; (b) Fracture location of sine pattern weld.
    Fig. 16. (a) The tensile test results of the two welds; (b) Fracture location of SLW weld; (b) Fracture location of sine pattern weld.

    Keywords

    Laser welding, Sinusoidal oscillating, Energy distribution, Numerical simulation, Molten pool flow, Grain structure

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    Figure 3. Comparison of water surface profiles over porous media with 12 mm particle diameter in laboratory measurements (symbols) and numerical results (lines).

    다공층에 대한 돌발 댐 붕괴의 3차원 유동 수치해석 시뮬레이션

    A. Safarzadeh1*, P. Mohsenzadeh2, S. Abbasi3
    1 Professor of Civil Eng., Water Engineering and Mineral Waters Research Center, Univ. of Mohaghegh Ardabili,Ardabil, Iran
    2 M.Sc., Graduated of Civil-Hydraulic Structures Eng., Faculty of Eng., Univ. of Mohaghegh Ardabili, Ardabil, Iran
    3 M.Sc., Graduated of Civil -Hydraulic Structures Eng., Faculty of Eng., Univ. of Mohaghegh Ardabili, Ardabil, Iran Safarzadeh@uma.ac.ir

    Highlights

    유체 이동에 의해 생성된 RBF는 Ls-Dyna에서 Fluent, ICFD ALE 및 SPH 방법으로 시뮬레이션되었습니다.
    RBF의 과예측은 유체가 메인 도메인에서 고속으로 분리될 때 발생합니다.
    이 과잉 예측은 요소 크기, 시간 단계 크기 및 유체 모델에 따라 다릅니다.
    유체 성능을 검증하려면 최대 RBF보다 임펄스가 권장됩니다.

    Abstract

    Dam break is a very important problem due to its effects on economy, security, human casualties and environmental consequences. In this study, 3D flow due to dam break over the porous substrate is numerically simulated and the effect of porosity, permeability and thickness of the porous bed and the water depth in the porous substrate are investigated. Classic models of dam break over a rigid bed and water infiltration through porous media were studied and results of the numerical simulations are compared with existing laboratory data. Validation of the results is performed by comparing the water surface profiles and wave front position with dam break on rigid and porous bed. Results showed that, due to the effect of dynamic wave in the initial stage of dam break, a local peak occurs in the flood hydrograph. The presence of porous bed reduces the acceleration of the flood wave relative to the flow over the solid bed and it decreases with the increase of the permeability of the bed. By increasing the permeability of the bed, the slope of the ascending limb of the flood hydrograph and the peak discharge drops. Furthermore, if the depth and permeability of the bed is such that the intrusive flow reaches the rigid substrate under the porous bed, saturation of the porous bed, results in a sharp increase in the slope of the flood hydrograph. The maximum values of the peak discharge at the end of the channel with porous bed occurred in saturated porous bed conditions.

    댐 붕괴는 경제, 보안, 인명 피해 및 환경적 영향으로 인해 매우 중요한 문제입니다. 본 연구에서는 다공성 기재에 대한 댐 파괴로 인한 3차원 유동을 수치적으로 시뮬레이션하고 다공성 기재의 다공성, 투과도 및 다공성 층의 두께 및 수심의 영향을 조사합니다. 단단한 바닥에 대한 댐 파괴 및 다공성 매체를 통한 물 침투의 고전 모델을 연구하고 수치 시뮬레이션 결과를 기존 실험실 데이터와 비교합니다. 결과 검증은 강체 및 다공성 베드에서 댐 파단과 수면 프로파일 및 파면 위치를 비교하여 수행됩니다. 그 결과 댐파괴 초기의 동적파동의 영향으로 홍수수문곡선에서 국부첨두가 발생하는 것으로 나타났다. 다공성 베드의 존재는 고체 베드 위의 유동에 대한 홍수파의 가속을 감소시키고 베드의 투과성이 증가함에 따라 감소합니다. 베드의 투수성을 증가시켜 홍수 수문곡선의 오름차순 경사와 첨두방류량이 감소한다. 더욱이, 만약 층의 깊이와 투과성이 관입 유동이 다공성 층 아래의 단단한 기질에 도달하는 정도라면, 다공성 층의 포화는 홍수 수문곡선의 기울기의 급격한 증가를 초래합니다. 다공층이 있는 채널의 끝단에서 최대 방전 피크값은 포화 다공층 조건에서 발생하였다.

    Keywords

    Keywords: Dams Break, 3D modeling, Porous Bed, Permeability, Flood wave

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    Fig. 1 Multi-physics phenomena in the laser-material interaction zone

    COMPARISON BETWEEN GREEN AND
    INFRARED LASER IN LASER POWDER BED
    FUSION OF PURE COPPER THROUGH HIGH
    FIDELITY NUMERICAL MODELLING AT MESOSCALE

    316-L 스테인리스강의 레이저 분말 베드 융합 중 콜드 스패터 형성의 충실도 높은 수치 모델링

    W.E. ALPHONSO1*, M. BAYAT1 and J.H. HATTEL1
    *Corresponding author
    1Technical University of Denmark (DTU), 2800, Kgs, Lyngby, Denmark

    ABSTRACT

    L-PBF(Laser Powder Bed Fusion)는 금속 적층 제조(MAM) 기술로, 기존 제조 공정에 비해 부품 설계 자유도, 조립품 통합, 부품 맞춤화 및 낮은 툴링 비용과 같은 여러 이점을 산업에 제공합니다.

    전기 코일 및 열 관리 장치는 일반적으로 높은 전기 및 열 전도성 특성으로 인해 순수 구리로 제조됩니다. 따라서 순동의 L-PBF가 가능하다면 기하학적으로 최적화된 방열판과 자유형 전자코일을 제작할 수 있습니다.

    그러나 L-PBF로 조밀한 순동 부품을 생산하는 것은 적외선에 대한 낮은 광 흡수율과 높은 열전도율로 인해 어렵습니다. 기존의 L-PBF 시스템에서 조밀한 구리 부품을 생산하려면 적외선 레이저의 출력을 500W 이상으로 높이거나 구리의 광흡수율이 높은 녹색 레이저를 사용해야 합니다.

    적외선 레이저 출력을 높이면 후면 반사로 인해 레이저 시스템의 광학 구성 요소가 손상되고 렌즈의 열 광학 현상으로 인해 공정이 불안정해질 수 있습니다. 이 작업에서 FVM(Finite Volume Method)에 기반한 다중 물리학 중간 규모 수치 모델은 Flow-3D에서 개발되어 용융 풀 역학과 궁극적으로 부품 품질을 제어하는 ​​물리적 현상 상호 작용을 조사합니다.

    녹색 레이저 열원과 적외선 레이저 열원은 기판 위의 순수 구리 분말 베드에 단일 트랙 증착을 생성하기 위해 개별적으로 사용됩니다.

    용융 풀 역학에 대한 레이저 열원의 유사하지 않은 광학 흡수 특성의 영향이 탐구됩니다. 수치 모델을 검증하기 위해 단일 트랙이 구리 분말 베드에 증착되고 시뮬레이션된 용융 풀 모양과 크기가 비교되는 실험이 수행되었습니다.

    녹색 레이저는 광흡수율이 높아 전도 및 키홀 모드 용융이 가능하고 적외선 레이저는 흡수율이 낮아 키홀 모드 용융만 가능하다. 레이저 파장에 대한 용융 모드의 변화는 궁극적으로 기계적, 전기적 및 열적 특성에 영향을 미치는 열 구배 및 냉각 속도에 대한 결과를 가져옵니다.

    Laser Powder Bed Fusion (L-PBF) is a Metal Additive Manufacturing (MAM) technology which offers several advantages to industries such as part design freedom, consolidation of assemblies, part customization and low tooling cost over conventional manufacturing processes. Electric coils and thermal management devices are generally manufactured from pure copper due to its high electrical and thermal conductivity properties. Therefore, if L-PBF of pure copper is feasible, geometrically optimized heat sinks and free-form electromagnetic coils can be manufactured. However, producing dense pure copper parts by L-PBF is difficult due to low optical absorptivity to infrared radiation and high thermal conductivity. To produce dense copper parts in a conventional L-PBF system either the power of the infrared laser must be increased above 500W, or a green laser should be used for which copper has a high optical absorptivity. Increasing the infrared laser power can damage the optical components of the laser systems due to back reflections and create instabilities in the process due to thermal-optical phenomenon of the lenses. In this work, a multi-physics meso-scale numerical model based on Finite Volume Method (FVM) is developed in Flow-3D to investigate the physical phenomena interaction which governs the melt pool dynamics and ultimately the part quality. A green laser heat source and an infrared laser heat source are used individually to create single track deposition on pure copper powder bed above a substrate. The effect of the dissimilar optical absorptivity property of laser heat sources on the melt pool dynamics is explored. To validate the numerical model, experiments were conducted wherein single tracks are deposited on a copper powder bed and the simulated melt pool shape and size are compared. As the green laser has a high optical absorptivity, a conduction and keyhole mode melting is possible while for the infrared laser only keyhole mode melting is possible due to low absorptivity. The variation in melting modes with respect to the laser wavelength has an outcome on thermal gradient and cooling rates which ultimately affect the mechanical, electrical, and thermal properties.

    Keywords

    Pure Copper, Laser Powder Bed Fusion, Finite Volume Method, multi-physics

    Fig. 1 Multi-physics phenomena in the laser-material interaction zone
    Fig. 1 Multi-physics phenomena in the laser-material interaction zone
    Fig. 2 Framework for single laser track simulation model including powder bed and substrate (a) computational domain with boundaries (b) discretization of the domain with uniform quad mesh.
    Fig. 2 Framework for single laser track simulation model including powder bed and substrate (a) computational domain with boundaries (b) discretization of the domain with uniform quad mesh.
    Fig. 3 2D melt pool contours from the numerical model compared to experiments [16] for (a) VED = 65 J/mm3 at 7 mm from the beginning of the single track (b) VED = 103 J/mm3 at 3 mm from the beginning of the single track (c) VED = 103 J/mm3 at 7 mm from the beginning of the single track. In the 2D contour, the non-melted region is indicated in blue, and the melted region is indicated by red and green when the VED is 65 J/mm3 and 103 J/mm3 respectively.
    Fig. 3 2D melt pool contours from the numerical model compared to experiments [16] for (a) VED = 65 J/mm3 at 7 mm from the beginning of the single track (b) VED = 103 J/mm3 at 3 mm from the beginning of the single track (c) VED = 103 J/mm3 at 7 mm from the beginning of the single track. In the 2D contour, the non-melted region is indicated in blue, and the melted region is indicated by red and green when the VED is 65 J/mm3 and 103 J/mm3 respectively.
    Fig. 4 3D temperature contour plots of during single track L-PBF process at time1.8 µs when (a) VED = 65 J/mm3 (b) VED = 103 J/mm3 along with 2D melt pool contours at 5 mm from the laser initial position. In the 2D contour, the non-melted region is indicated in blue, and the melted region is indicated by red and green when the VED is 65 J/mm3 and 103 J/mm3 respectively.
    Fig. 4 3D temperature contour plots of during single track L-PBF process at time1.8 µs when (a) VED = 65 J/mm3 (b) VED = 103 J/mm3 along with 2D melt pool contours at 5 mm from the laser initial position. In the 2D contour, the non-melted region is indicated in blue, and the melted region is indicated by red and green when the VED is 65 J/mm3 and 103 J/mm3 respectively.

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    Fig. 1. Schematic figure showing the PREP with additional gas flowing on the end face of electrode.

    플라즈마 회전 전극 공정 중 분말 형성에 대한 공정 매개변수 및 냉각 가스의 영향

    Effects of process parameters and cooling gas on powder formation during the plasma rotating electrode process

    Yujie Cuia Yufan Zhaoa1 Haruko Numatab Kenta Yamanakaa Huakang Biana Kenta Aoyagia AkihikoChibaa
    aInstitute for Materials Research, Tohoku University, Sendai 980-8577, JapanbDepartment of Materials Processing, Graduate School of Engineering, Tohoku University, Sendai 980-8577, Japan

    Highlights

    •The limitation of increasing the rotational speed in decreasing powder size was clarified.

    •Cooling and disturbance effects varied with the gas flowing rate.

    •Inclined angle of the residual electrode end face affected powder formation.

    •Additional cooling gas flowing could be applied to control powder size.

    Abstract

    The plasma rotating electrode process (PREP) is rapidly becoming an important powder fabrication method in additive manufacturing. However, the low production rate of fine PREP powder limits the development of PREP. Herein, we investigated different factors affecting powder formation during PREP by combining experimental methods and numerical simulations. The limitation of increasing the rotation electrode speed in decreasing powder size is attributed to the increased probability of adjacent droplets recombining and the decreased tendency of granulation. The effects of additional Ar/He gas flowing on the rotational electrode on powder formation is determined through the cooling effect, the disturbance effect, and the inclined effect of the residual electrode end face simultaneously. A smaller-sized powder was obtained in the He atmosphere owing to the larger inclined angle of the residual electrode end face compared to the Ar atmosphere. Our research highlights the route for the fabrication of smaller-sized powders using PREP.

    플라즈마 회전 전극 공정(PREP)은 적층 제조 에서 중요한 분말 제조 방법으로 빠르게 자리잡고 있습니다. 그러나 미세한 PREP 분말의 낮은 생산율은 PREP의 개발을 제한합니다. 여기에서 우리는 실험 방법과 수치 시뮬레이션을 결합하여 PREP 동안 분말 형성에 영향을 미치는 다양한 요인을 조사했습니다. 분말 크기 감소에서 회전 전극 속도 증가의 한계는 인접한 액적 재결합 확률 증가 및 과립화 경향 감소에 기인합니다.. 회전 전극에 흐르는 추가 Ar/He 가스가 분말 형성에 미치는 영향은 냉각 효과, 외란 효과 및 잔류 전극 단면의 경사 효과를 통해 동시에 결정됩니다. He 분위기에서는 Ar 분위기에 비해 잔류 전극 단면의 경사각이 크기 때문에 더 작은 크기의 분말이 얻어졌다. 우리의 연구는 PREP를 사용하여 더 작은 크기의 분말을 제조하는 경로를 강조합니다.

    Keywords

    Plasma rotating electrode process

    Ti-6Al-4 V alloy, Rotating speed, Numerical simulation, Gas flowing, Powder size

    Introduction

    With the development of additive manufacturing, there has been a significant increase in high-quality powder production demand [1,2]. The initial powder characteristics are closely related to the uniform powder spreading [3,4], packing density [5], and layer thickness observed during additive manufacturing [6], thus determining the mechanical properties of the additive manufactured parts [7,8]. Gas atomization (GA) [9–11], centrifugal atomization (CA) [12–15], and the plasma rotating electrode process (PREP) are three important powder fabrication methods.

    Currently, GA is the dominant powder fabrication method used in additive manufacturing [16] for the fabrication of a wide range of alloys [11]. GA produces powders by impinging a liquid metal stream to droplets through a high-speed gas flow of nitrogen, argon, or helium. With relatively low energy consumption and a high fraction of fine powders, GA has become the most popular powder manufacturing technology for AM.

    The entrapped gas pores are generally formed in the powder after solidification during GA, in which the molten metal is impacted by a high-speed atomization gas jet. In addition, satellites are formed in GA powder when fine particles adhere to partially molten particles.

    The gas pores of GA powder result in porosity generation in the additive manufactured parts, which in turn deteriorates its mechanical properties because pores can become crack initiation sites [17]. In CA, a molten metal stream is poured directly onto an atomizer disc spinning at a high rotational speed. A thin film is formed on the surface of the disc, which breaks into small droplets due to the centrifugal force. Metal powder is obtained when these droplets solidify.

    Compared with GA powder, CA powder exhibits higher sphericity, lower impurity content, fewer satellites, and narrower particle size distribution [12]. However, very high speed is required to obtain fine powder by CA. In PREP, the molten metal, melted using the plasma arc, is ejected from the rotating rod through centrifugal force. Compared with GA powder, PREP-produced powders also have higher sphericity and fewer pores and satellites [18].

    For instance, PREP-fabricated Ti6Al-4 V alloy powder with a powder size below 150 μm exhibits lower porosity than gas-atomized powder [19], which decreases the porosity of additive manufactured parts. Furthermore, the process window during electron beam melting was broadened using PREP powder compared to GA powder in Inconel 718 alloy [20] owing to the higher sphericity of the PREP powder.

    In summary, PREP powder exhibits many advantages and is highly recommended for powder-based additive manufacturing and direct energy deposition-type additive manufacturing. However, the low production rate of fine PREP powder limits the widespread application of PREP powder in additive manufacturing.

    Although increasing the rotating speed is an effective method to decrease the powder size [21,22], the reduction in powder size becomes smaller with the increased rotating speed [23]. The occurrence of limiting effects has not been fully clarified yet.

    Moreover, the powder size can be decreased by increasing the rotating electrode diameter [24]. However, these methods are quite demanding for the PREP equipment. For instance, it is costly to revise the PREP equipment to meet the demand of further increasing the rotating speed or electrode diameter.

    Accordingly, more feasible methods should be developed to further decrease the PREP powder size. Another factor that influences powder formation is the melting rate [25]. It has been reported that increasing the melting rate decreases the powder size of Inconel 718 alloy [26].

    In contrast, the powder size of SUS316 alloy was decreased by decreasing the plasma current within certain ranges. This was ascribed to the formation of larger-sized droplets from fluid strips with increased thickness and spatial density at higher plasma currents [27]. The powder size of NiTi alloy also decreases at lower melting rates [28]. Consequently, altering the melting rate, varied with the plasma current, is expected to regulate the PREP powder size.

    Furthermore, gas flowing has a significant influence on powder formation [27,29–31]. On one hand, the disturbance effect of gas flowing promotes fluid granulation, which in turn contributes to the formation of smaller-sized powder [27]. On the other hand, the cooling effect of gas flowing facilitates the formation of large-sized powder due to increased viscosity and surface tension. However, there is a lack of systematic research on the effect of different gas flowing on powder formation during PREP.

    Herein, the authors systematically studied the effects of rotating speed, electrode diameter, plasma current, and gas flowing on the formation of Ti-6Al-4 V alloy powder during PREP as additive manufactured Ti-6Al-4 V alloy exhibits great application potential [32]. Numerical simulations were conducted to explain why increasing the rotating speed is not effective in decreasing powder size when the rotation speed reaches a certain level. In addition, the different factors incited by the Ar/He gas flowing on powder formation were clarified.

    Fig. 1. Schematic figure showing the PREP with additional gas flowing on the end face of electrode.
    Fig. 1. Schematic figure showing the PREP with additional gas flowing on the end face of electrode.

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    Gating System Design Based on Numerical Simulation and Production Experiment Verification of Aluminum Alloy Bracket Fabricated by Semi-solid Rheo-Die Casting Process

    Gating System Design Based on Numerical Simulation and Production Experiment Verification of Aluminum Alloy Bracket Fabricated by Semi-solid Rheo-Die Casting Process

    반고체 레오 다이 캐스팅 공정으로 제작된 알루미늄 합금 브래킷의 수치 시뮬레이션 및 생산 실험 검증을 기반으로 한 게이팅 시스템 설계

    International Journal of Metalcasting volume 16, pages878–893 (2022)Cite this article

    Abstract

    In this study a gating system including sprue, runner and overflows for semi-solid rheocasting of aluminum alloy was designed by means of numerical simulations with a commercial software. The effects of pouring temperature, mold temperature and injection speed on the filling process performance of semi-solid die casting were studied. Based on orthogonal test analysis, the optimal die casting process parameters were selected, which were metal pouring temperature 590 °C, mold temperature 260 °C and injection velocity 0.5 m/s. Semi-solid slurry preparation process of Swirled Enthalpy Equilibration Device (SEED) was used for die casting production experiment. Aluminum alloy semi-solid bracket components were successfully produced with the key die casting process parameters selected, which was consistent with the simulation result. The design of semi-solid gating system was further verified by observing and analyzing the microstructure of different zones of the casting. The characteristic parameters, particle size and shape factor of microstructure of the produced semi-solid casting showed that the semi-solid aluminum alloy components are of good quality.

    이 연구에서 알루미늄 합금의 반고체 레오캐스팅을 위한 스프루, 러너 및 오버플로를 포함하는 게이팅 시스템은 상용 소프트웨어를 사용한 수치 시뮬레이션을 통해 설계되었습니다. 주입 온도, 금형 온도 및 사출 속도가 반고체 다이캐스팅의 충전 공정 성능에 미치는 영향을 연구했습니다. 직교 테스트 분석을 기반으로 금속 주입 온도 590°C, 금형 온도 260°C 및 사출 속도 0.5m/s인 최적의 다이 캐스팅 공정 매개변수가 선택되었습니다. Swirled Enthalpy Equilibration Device(SEED)의 반고체 슬러리 제조 공정을 다이캐스팅 생산 실험에 사용하였다. 알루미늄 합금 반고체 브래킷 구성 요소는 시뮬레이션 결과와 일치하는 주요 다이 캐스팅 공정 매개변수를 선택하여 성공적으로 생산되었습니다. 반고체 게이팅 시스템의 설계는 주조의 다른 영역의 미세 구조를 관찰하고 분석하여 추가로 검증되었습니다. 생산된 반고체 주조물의 특성 매개변수, 입자 크기 및 미세 구조의 형상 계수는 반고체 알루미늄 합금 부품의 품질이 양호함을 보여주었습니다.

    Gating System Design Based on Numerical Simulation and Production Experiment Verification of Aluminum Alloy Bracket Fabricated by Semi-solid Rheo-Die Casting Process
    Gating System Design Based on Numerical Simulation and Production Experiment Verification of Aluminum Alloy Bracket Fabricated by Semi-solid Rheo-Die Casting Process

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    Keywords

    • semi-solid rheo-die casting
    • gating system
    • process parameters
    • numerical simulation
    • microstructure
    Fig. 2: Scheme of the LED photo-crosslinking and 3D-printing section of the microfluidic/3D-printing device. The droplet train is transferred from the chip microchannel into a microtubing in a straight section with nearly identical inner channel and inner microtubing diameter. Further downstream, the microtubing passes an LED-section for fast photo cross-linking to generate the microgels. This section is contained in an aluminum encasing to avoid premature crosslinking of polymer precursor in upstream channel sections by stray light. Subsequently, the microtubing is integrated into a 3D-printhead, where the microgels are jammed into a filament that is directly 3D-printed into the scaffold.

    On-Chip Fabrication and In-Flow 3D-Printing of Cell-Laden Microgel Constructs: From Chip to Scaffold Materials in One Integral Process

    세포가 함유된 마이크로겔의 온칩 제작 및 인-플로우 3D 프린팅
    구성:하나의 통합 프로세스에서 칩에서 스캐폴드 재료까지

    Vollmer, Gültekin Tamgüney, Aldo Boccacini
    Submitted date: 10/05/2021 • Posted date: 11/05/2021
    Licence: CC BY-NC-ND 4.0

    바이오프린팅은 세포가 실린 스캐폴드의 제조를 위한 유력한 기술로 발전했습니다. 바이오잉크는 바이오프린팅의 가장 중요한 구성요소입니다. 최근 마이크로겔은 세포 보호 및 세포 미세 환경 제어를 가능하게 하는 매우 유망한 바이오 잉크로 도입되었습니다. 그러나 이들의 미세유체 제작은 본질적으로 한계가 있는 것으로 보입니다.

    여기에서 우리는 안정적인 스캐폴드에 직접 유입되는 바이오프린팅과 함께 세포가 실린 마이크로겔의 미세유체 생산을 위한 미세유체 및 3D 인쇄의 직접 결합을 소개합니다. 방법론은 세포를 단분산 미세 방울로 연속 온칩 캡슐화하여 후속 유입 교차 연결을 통해 세포가 함유된 마이크로겔을 생성할 수 있으며, 이는 미세관을 종료한 후 자동으로 얇은 연속 마이크로겔 필라멘트로 끼이게 됩니다.

    3D 프린트 헤드로의 통합으로 독립형 3차원 스캐폴드에 필라멘트를 직접 유입 인쇄할 수 있습니다. 이 방법은 다양한 교차 연결 방법 및 세포주에 대해 설명됩니다. 이러한 발전으로 미세유체학은 더 이상 바이오 제조의 병목을 초래하는 현상이 아닙니다.

    Bioprinting has evolved into a thriving technology for the fabrication of cell-laden scaffolds. Bioinks are the most critical component for bioprinting. Recently, microgels have been introduced as a very promising bioink enabling cell protection and the control of the cellular microenvironment. However, their microfluidic fabrication inherently seemed to be a limitation. Here we introduce a direct coupling of microfluidics and 3D-printing for the microfluidic production of cell-laden microgels with direct in-flow bioprinting into stable scaffolds. The methodology enables the continuous on-chip encapsulation of cells into monodisperse microdroplets with subsequent in-flow cross-linking to produce cell-laden microgels, which after exiting a microtubing are automatically jammed into thin continuous microgel filaments. The integration into a 3D printhead allows direct in-flow printing of the filaments into free-standing three-dimensional scaffolds. The method is demonstrated for different cross-linking methods and cell lines. With this advancement, microfluidics is no longer a bottleneck for biofabrication.

    Fig. 1: Three-dimensional schematic view of the multilayer double 3D-focusing microfluidic channel system, (b) control of droplet diameter via the Capiilary number Ca, and accessible hydrodynamic regimes for droplet production: squeezing (c), dripping (d) and jetting (e). The scale bars are 200 µm.
    Fig. 1: Three-dimensional schematic view of the multilayer double 3D-focusing microfluidic channel system, (b) control of droplet diameter via the Capiilary number Ca, and accessible hydrodynamic regimes for droplet production: squeezing (c), dripping (d) and jetting (e). The scale bars are 200 µm.
    Fig. 2: Scheme of the LED photo-crosslinking and 3D-printing section of the microfluidic/3D-printing device. The droplet train is transferred from the chip microchannel into a microtubing in a straight section with nearly identical inner channel and inner microtubing diameter. Further downstream, the microtubing passes an LED-section for fast photo cross-linking to generate the microgels. This section is contained in an aluminum encasing to avoid premature crosslinking of polymer precursor in upstream channel sections by stray light. Subsequently, the microtubing is integrated into a 3D-printhead, where the microgels are jammed into a filament that is directly 3D-printed into the scaffold.
    Fig. 2: Scheme of the LED photo-crosslinking and 3D-printing section of the microfluidic/3D-printing device. The droplet train is transferred from the chip microchannel into a microtubing in a straight section with nearly identical inner channel and inner microtubing diameter. Further downstream, the microtubing passes an LED-section for fast photo cross-linking to generate the microgels. This section is contained in an aluminum encasing to avoid premature crosslinking of polymer precursor in upstream channel sections by stray light. Subsequently, the microtubing is integrated into a 3D-printhead, where the microgels are jammed into a filament that is directly 3D-printed into the scaffold.
    Fig. 3: a) Photograph of a standard meander-shaped layer fabricated by microgel filament deposition printing. The lines have a thickness of 300 µm. b) photograph of a cross-bar pattern obtained by on-top deposition of several microgel filaments. The average linewidth is 1 mm. c) photograph of a donut-shaped microgel construct. The microgels have been fluorescently labelled by FITC-dextran to demonstrate the intrinsic microporosity corresponding to the black non-fluorescent regions, d) light microscopy image of a construct edge showing that fused adhesive microgels form a continuous, three-dimensional selfsupporting scaffold with intrinsic micropores.
    Fig. 3: a) Photograph of a standard meander-shaped layer fabricated by microgel filament deposition printing. The lines have a thickness of 300 µm. b) photograph of a cross-bar pattern obtained by on-top deposition of several microgel filaments. The average linewidth is 1 mm. c) photograph of a donut-shaped microgel construct. The microgels have been fluorescently labelled by FITC-dextran to demonstrate the intrinsic microporosity corresponding to the black non-fluorescent regions, d) light microscopy image of a construct edge showing that fused adhesive microgels form a continuous, three-dimensional selfsupporting scaffold with intrinsic micropores.
    Fig. 4: a) Scheme of the perfusion chamber consisting of an upstream and downstream chamber, perfusion ports, and removable scaffolds to stabilize the microgel construct during 3D-printing, b) photograph of a microgel construct in the perfusion chamber directly after printing and removal of the scaffolds, c) confocal microscopy image of the permeation front of a fluorescent dye, where the high dye concentration in the micropores can be clearly seen, d) confocal microscopy image of YFP-labelled HEK-cells within a microgel construct.
    Fig. 4: a) Scheme of the perfusion chamber consisting of an upstream and downstream chamber, perfusion ports, and removable scaffolds to stabilize the microgel construct during 3D-printing, b) photograph of a microgel construct in the perfusion chamber directly after printing and removal of the scaffolds, c) confocal microscopy image of the permeation front of a fluorescent dye, where the high dye concentration in the micropores can be clearly seen, d) confocal microscopy image of YFP-labelled HEK-cells within a microgel construct.
    Fig. 5: a) Layer-by-layer printing of microgel construct with integrated perfusion channel. After printing of the first layer, a hollow perfusion channel is inserted. Subsequently, the second and third layers are printed. b) The construct is directly printed into a perfusion chamber. The perfusion chamber provides whole construct permeation via flows cin and cout, as well as independent flow through the perfusion channel via flows vin and vout. c) Photograph of a perfusion chamber containing the construct directly after printing. The flow of the fluorescein solution through the integrated PVA hollow channel is clearly visible.
    Fig. 5: a) Layer-by-layer printing of microgel construct with integrated perfusion channel. After printing of the first layer, a hollow perfusion channel is inserted. Subsequently, the second and third layers are printed. b) The construct is directly printed into a perfusion chamber. The perfusion chamber provides whole construct permeation via flows cin and cout, as well as independent flow through the perfusion channel via flows vin and vout. c) Photograph of a perfusion chamber containing the construct directly after printing. The flow of the fluorescein solution through the integrated PVA hollow channel is clearly visible.
    Fig. 6: a) Photograph of an alginate capsule fiber formed after exiting the microtube. b) Confocal fluorescence microscopy image of part of a 3D-printed alginate capsule construct. The fluorescence arises from encapsulated fluorescently labelled polystyrene microbeads to demonstrate the integrity and stability of the alginate capsules.
    Fig. 6: a) Photograph of an alginate capsule fiber formed after exiting the microtube. b) Confocal fluorescence microscopy image of part of a 3D-printed alginate capsule construct. The fluorescence arises from encapsulated fluorescently labelled polystyrene microbeads to demonstrate the integrity and stability of the alginate capsules.

    Keywords

    biomaterials, microgels, microfluidics, 3D printing, bioprinting

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    Figure 3.10: Snapshots of Temperature Profile for Single Track in Keyhole Regime (P = 250W and V = 0.5m/s) at the Preheating Temperature of 100 °C

    Multiscale Process Modeling of Residual Deformation and Defect Formation for Laser Powder Bed Fusion Additive Manufacturing

    Qian Chen, PhD
    University of Pittsburgh, 2021

    레이저 분말 베드 퓨전(L-PBF) 적층 제조(AM)는 우수한 기계적 특성으로 그물 모양에 가까운 복잡한 부품을 생산할 수 있습니다. 그러나 빌드 실패 및 다공성과 같은 결함으로 이어지는 원치 않는 잔류 응력 및 왜곡이 L-PBF의 광범위한 적용을 방해하고 있습니다.

    L-PBF의 잠재력을 최대한 실현하기 위해 잔류 변형, 용융 풀 및 다공성 형성을 예측하는 다중 규모 모델링 방법론이 개발되었습니다. L-PBF의 잔류 변형 및 응력을 부품 규모에서 예측하기 위해 고유 변형 ​​방법을 기반으로 하는 다중 규모 프로세스 모델링 프레임워크가 제안됩니다.

    고유한 변형 벡터는 마이크로 스케일에서 충실도가 높은 상세한 다층 프로세스 시뮬레이션에서 추출됩니다. 균일하지만 이방성인 변형은 잔류 왜곡 및 응력을 예측하기 위해 준 정적 평형 유한 요소 분석(FEA)에서 레이어별로 L-PBF 부품에 적용됩니다.

    부품 규모에서의 잔류 변형 및 응력 예측 외에도 분말 규모의 다중물리 모델링을 수행하여 공정 매개변수, 예열 온도 및 스패터링 입자에 의해 유도된 용융 풀 변동 및 결함 형성을 연구합니다. 이러한 요인과 관련된 용융 풀 역학 및 다공성 형성 메커니즘은 시뮬레이션 및 실험을 통해 밝혀졌습니다.

    제안된 부품 규모 잔류 응력 및 왜곡 모델을 기반으로 경로 계획 방법은 큰 잔류 변형 및 건물 파손을 방지하기 위해 주어진 형상에 대한 레이저 스캐닝 경로를 조정하기 위해 개발되었습니다.

    연속 및 아일랜드 스캐닝 전략을 위한 기울기 기반 경로 계획이 공식화되고 공식화된 컴플라이언스 및 스트레스 최소화 문제에 대한 전체 감도 분석이 수행됩니다. 이 제안된 경로 계획 방법의 타당성과 효율성은 AconityONE L-PBF 시스템을 사용하여 실험적으로 입증되었습니다.

    또한 기계 학습을 활용한 데이터 기반 프레임워크를 개발하여 L-PBF에 대한 부품 규모의 열 이력을 예측합니다. 본 연구에서는 실시간 열 이력 예측을 위해 CNN(Convolutional Neural Network)과 RNN(Recurrent Neural Network)을 포함하는 순차적 기계 학습 모델을 제안합니다.

    유한 요소 해석과 비교하여 100배의 예측 속도 향상이 달성되어 실제 제작 프로세스보다 빠른 예측이 가능하고 실시간 온도 프로파일을 사용할 수 있습니다.

    Laser powder bed fusion (L-PBF) additive manufacturing (AM) is capable of producing complex parts near net shape with good mechanical properties. However, undesired residual stress and distortion that lead to build failure and defects such as porosity are preventing broader applications of L-PBF. To realize the full potential of L-PBF, a multiscale modeling methodology is developed to predict residual deformation, melt pool, and porosity formation. To predict the residual deformation and stress in L-PBF at part-scale, a multiscale process modeling framework based on inherent strain method is proposed.

    Inherent strain vectors are extracted from detailed multi-layer process simulation with high fidelity at micro-scale. Uniform but anisotropic strains are then applied to L-PBF part in a layer-by-layer fashion in a quasi-static equilibrium finite element analysis (FEA) to predict residual distortion and stress. Besides residual distortion and stress prediction at part scale, multiphysics modeling at powder scale is performed to study the melt pool variation and defect formation induced by process parameters, preheating temperature and spattering particles. Melt pool dynamics and porosity formation mechanisms associated with these factors are revealed through simulation and experiments.

    Based on the proposed part-scale residual stress and distortion model, path planning method is developed to tailor the laser scanning path for a given geometry to prevent large residual deformation and building failures. Gradient based path planning for continuous and island scanning strategy is formulated and full sensitivity analysis for the formulated compliance- and stress-minimization problem is performed.

    The feasibility and effectiveness of this proposed path planning method is demonstrated experimentally using the AconityONE L-PBF system. In addition, a data-driven framework utilizing machine learning is developed to predict the thermal history at part-scale for L-PBF.

    In this work, a sequential machine learning model including convolutional neural network (CNN) and recurrent neural network (RNN), long shortterm memory unit, is proposed for real-time thermal history prediction. A 100x prediction speed improvement is achieved compared to the finite element analysis which makes the prediction faster than real fabrication process and real-time temperature profile available.

    Figure 1.1: Schematic Overview of Metal Laser Powder Bed Fusion Process [2]
    Figure 1.1: Schematic Overview of Metal Laser Powder Bed Fusion Process [2]
    Figure 1.2: Commercial Powder Bed Fusion Systems
    Figure 1.2: Commercial Powder Bed Fusion Systems
    Figure 1.3: Commercial Metal Components Fabricated by Powder Bed Fusion Additive Manufacturing: (a) GE Fuel Nozzle; (b) Stryker Hip Biomedical Implant.
    Figure 1.3: Commercial Metal Components Fabricated by Powder Bed Fusion Additive Manufacturing: (a) GE Fuel Nozzle; (b) Stryker Hip Biomedical Implant.
    Figure 2.1: Proposed Multiscale Process Simulation Framework
    Figure 2.1: Proposed Multiscale Process Simulation Framework
    Figure 2.2: (a) Experimental Setup for In-situ Thermocouple Measurement in the EOS M290 Build Chamber; (b) Themocouple Locations on the Bottom Side of the Substrate.
    Figure 2.2: (a) Experimental Setup for In-situ Thermocouple Measurement in the EOS M290 Build Chamber; (b) Themocouple Locations on the Bottom Side of the Substrate.
    Figure 2.3: (a) Finite Element Model for Single Layer Thermal Analysis; (b) Deposition Layer
    Figure 2.3: (a) Finite Element Model for Single Layer Thermal Analysis; (b) Deposition Layer
    Figure 2.4: Core-skin layer: (a) Surface Morphology; (b) Scanning Strategy; (c) Transient Temperature Distribution and Temperature History at (d) Point 1; (e) Point 2 and (f) Point 3
    Figure 2.4: Core-skin layer: (a) Surface Morphology; (b) Scanning Strategy; (c) Transient Temperature Distribution and Temperature History at (d) Point 1; (e) Point 2 and (f) Point 3
    Figure 2.5: (a) Scanning Orientation of Each Layer; (b) Finite Element Model for Micro-scale Representative Volume
    Figure 2.5: (a) Scanning Orientation of Each Layer; (b) Finite Element Model for Micro-scale Representative Volume
    Figure 2.6: Bottom Layer (a) Thermal History; (b) Plastic Strain and (c) Elastic Strain Evolution History
    Figure 2.6: Bottom Layer (a) Thermal History; (b) Plastic Strain and (c) Elastic Strain Evolution History
    Figure 2.7: Bottom Layer Inherent Strain under Default Process Parameters along Horizontal Scanning Path
    Figure 2.7: Bottom Layer Inherent Strain under Default Process Parameters along Horizontal Scanning Path
    Figure 2.8: Snapshots of the Element Activation Process
    Figure 2.8: Snapshots of the Element Activation Process
    Figure 2.9: Double Cantilever Beam Structure Built by the EOS M290 DMLM Process (a) Before and (b) After Cutting off; (c) Faro Laser ScanArm V3 for Distortion Measurement
    Figure 2.9: Double Cantilever Beam Structure Built by the EOS M290 DMLM Process (a) Before and (b) After Cutting off; (c) Faro Laser ScanArm V3 for Distortion Measurement
    Figure 2.10: Square Canonical Structure Built by the EOS M290 DMLM Process
    Figure 2.10: Square Canonical Structure Built by the EOS M290 DMLM Process
    Figure 2.11: Finite Element Mesh for the Square Canonical and Snapshots of Element Activation Process
    Figure 2.11: Finite Element Mesh for the Square Canonical and Snapshots of Element Activation Process
    Figure 2.12: Simulated Distortion Field for the Double Cantilever Beam before Cutting off the Supports: (a) Inherent Strain Method; (b) Simufact Additive 3.1
    Figure 2.12: Simulated Distortion Field for the Double Cantilever Beam before Cutting off the Supports: (a) Inherent Strain Method; (b) Simufact Additive 3.1
    Figure 3.10: Snapshots of Temperature Profile for Single Track in Keyhole Regime (P = 250W and V = 0.5m/s) at the Preheating Temperature of 100 °C
    Figure 3.10: Snapshots of Temperature Profile for Single Track in Keyhole Regime (P = 250W and V = 0.5m/s) at the Preheating Temperature of 100 °C
    s) at the Preheating Temperature of 500 °C
    s) at the Preheating Temperature of 500 °C
    Figure 3.15: Melt Pool Cross Section Comparison Between Simulation and Experiment for Single Track
    Figure 3.15: Melt Pool Cross Section Comparison Between Simulation and Experiment for Single Track

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    Figure 3 Simulation PTC pipes enhanced with copper foam and nanoparticles in FLOW-3D software.

    다공성 미디어 및 나노유체에 의해 강화된 수집기로 태양광 CCHP 시스템의 최적화

    Optimization of Solar CCHP Systems with Collector Enhanced by Porous Media and Nanofluid


    Navid Tonekaboni,1Mahdi Feizbahr,2 Nima Tonekaboni,1Guang-Jun Jiang,3,4 and Hong-Xia Chen3,4

    Abstract

    태양열 집열기의 낮은 효율은 CCHP(Solar Combined Cooling, Heating, and Power) 사이클의 문제점 중 하나로 언급될 수 있습니다. 태양계를 개선하기 위해 나노유체와 다공성 매체가 태양열 집열기에 사용됩니다.

    다공성 매질과 나노입자를 사용하는 장점 중 하나는 동일한 조건에서 더 많은 에너지를 흡수할 수 있다는 것입니다. 이 연구에서는 평균 일사량이 1b인 따뜻하고 건조한 지역의 600 m2 건물의 전기, 냉방 및 난방을 생성하기 위해 다공성 매질과 나노유체를 사용하여 태양열 냉난방 복합 발전(SCCHP) 시스템을 최적화했습니다.

    본 논문에서는 침전물이 형성되지 않는 lb = 820 w/m2(이란) 정도까지 다공성 물질에서 나노유체의 최적량을 계산하였다. 이 연구에서 태양열 집열기는 구리 다공성 매체(95% 다공성)와 CuO 및 Al2O3 나노 유체로 향상되었습니다.

    나노유체의 0.1%-0.6%가 작동 유체로 물에 추가되었습니다. 나노유체의 0.5%가 태양열 집열기 및 SCCHP 시스템에서 가장 높은 에너지 및 엑서지 효율 향상으로 이어지는 것으로 밝혀졌습니다.

    본 연구에서 포물선형 집열기(PTC)의 최대 에너지 및 엑서지 효율은 각각 74.19% 및 32.6%입니다. 그림 1은 태양 CCHP의 주기를 정확하게 설명하기 위한 그래픽 초록으로 언급될 수 있습니다.

    The low efficiency of solar collectors can be mentioned as one of the problems in solar combined cooling, heating, and power (CCHP) cycles. For improving solar systems, nanofluid and porous media are used in solar collectors. One of the advantages of using porous media and nanoparticles is to absorb more energy under the same conditions. In this research, a solar combined cooling, heating, and power (SCCHP) system has been optimized by porous media and nanofluid for generating electricity, cooling, and heating of a 600 m2 building in a warm and dry region with average solar radiation of Ib = 820 w/m2 in Iran. In this paper, the optimal amount of nanofluid in porous materials has been calculated to the extent that no sediment is formed. In this study, solar collectors were enhanced with copper porous media (95% porosity) and CuO and Al2O3 nanofluids. 0.1%–0.6% of the nanofluids were added to water as working fluids; it is found that 0.5% of the nanofluids lead to the highest energy and exergy efficiency enhancement in solar collectors and SCCHP systems. Maximum energy and exergy efficiency of parabolic thermal collector (PTC) riches in this study are 74.19% and 32.6%, respectively. Figure 1 can be mentioned as a graphical abstract for accurately describing the cycle of solar CCHP.

    1. Introduction

    Due to the increase in energy consumption, the use of clean energy is one of the important goals of human societies. In the last four decades, the use of cogeneration cycles has increased significantly due to high efficiency. Among clean energy, the use of solar energy has become more popular due to its greater availability [1]. Low efficiency of energy production, transmission, and distribution system makes a new system to generate simultaneously electricity, heating, and cooling as an essential solution to be widely used. The low efficiency of the electricity generation, transmission, and distribution system makes the CCHP system a basic solution to eliminate waste of energy. CCHP system consists of a prime mover (PM), a power generator, a heat recovery system (produce extra heating/cooling/power), and thermal energy storage (TES) [2]. Solar combined cooling, heating, and power (SCCHP) has been started three decades ago. SCCHP is a system that receives its propulsive force from solar energy; in this cycle, solar collectors play the role of propulsive for generating power in this system [3].

    Increasing the rate of energy consumption in the whole world because of the low efficiency of energy production, transmission, and distribution system causes a new cogeneration system to generate electricity, heating, and cooling energy as an essential solution to be widely used. Building energy utilization fundamentally includes power required for lighting, home electrical appliances, warming and cooling of building inside, and boiling water. Domestic usage contributes to an average of 35% of the world’s total energy consumption [4].

    Due to the availability of solar energy in all areas, solar collectors can be used to obtain the propulsive power required for the CCHP cycle. Solar energy is the main source of energy in renewable applications. For selecting a suitable area to use solar collectors, annual sunshine hours, the number of sunny days, minus temperature and frosty days, and the windy status of the region are essentially considered [5]. Iran, with an average of more than 300 sunny days, is one of the suitable countries to use solar energy. Due to the fact that most of the solar radiation is in the southern regions of Iran, also the concentration of cities is low in these areas, and transmission lines are far apart, one of the best options is to use CCHP cycles based on solar collectors [6]. One of the major problems of solar collectors is their low efficiency [7]. Low efficiency increases the area of collectors, which increases the initial cost of solar systems and of course increases the initial payback period. To increase the efficiency of solar collectors and improve their performance, porous materials and nanofluids are used to increase their workability.

    There are two ways to increase the efficiency of solar collectors and mechanical and fluid improvement. In the first method, using porous materials or helical filaments inside the collector pipes causes turbulence of the flow and increases heat transfer. In the second method, using nanofluids or salt and other materials increases the heat transfer of water. The use of porous materials has grown up immensely over the past twenty years. Porous materials, especially copper porous foam, are widely used in solar collectors. Due to the high contact surface area, porous media are appropriate candidates for solar collectors [8]. A number of researchers investigated Solar System performance in accordance with energy and exergy analyses. Zhai et al. [9] reviewed the performance of a small solar-powered system in which the energy efficiency was 44.7% and the electrical efficiency was 16.9%.

    Abbasi et al. [10] proposed an innovative multiobjective optimization to optimize the design of a cogeneration system. Results showed the CCHP system based on an internal diesel combustion engine was the applicable alternative at all regions with different climates. The diesel engine can supply the electrical requirement of 31.0% and heating demand of 3.8% for building.

    Jiang et al. [11] combined the experiment and simulation together to analyze the performance of a cogeneration system. Moreover, some research focused on CCHP systems using solar energy. It integrated sustainable and renewable technologies in the CCHP, like PV, Stirling engine, and parabolic trough collector (PTC) [21215].

    Wang et al. [16] optimized a cogeneration solar cooling system with a Rankine cycle and ejector to reach the maximum total system efficiency of 55.9%. Jing et al. analyzed a big-scale building with the SCCHP system and auxiliary heaters to produced electrical, cooling, and heating power. The maximum energy efficiency reported in their work is 46.6% [17]. Various optimization methods have been used to improve the cogeneration system, minimum system size, and performance, such as genetic algorithm [1819].

    Hirasawa et al. [20] investigated the effect of using porous media to reduce thermal waste in solar systems. They used the high-porosity metal foam on top of the flat plate solar collector and observed that thermal waste decreased by 7% due to natural heat transfer. Many researchers study the efficiency improvement of the solar collector by changing the collector’s shapes or working fluids. However, the most effective method is the use of nanofluids in the solar collector as working fluid [21]. In the experimental study done by Jouybari et al. [22], the efficiency enhancement up to 8.1% was achieved by adding nanofluid in a flat plate collector. In this research, by adding porous materials to the solar collector, collector efficiency increased up to 92% in a low flow regime. Subramani et al. [23] analyzed the thermal performance of the parabolic solar collector with Al2O3 nanofluid. They conducted their experiments with Reynolds number range 2401 to 7202 and mass flow rate 0.0083 to 0.05 kg/s. The maximum efficiency improvement in this experiment was 56% at 0.05 kg/s mass flow rate.

    Shojaeizadeh et al. [24] investigated the analysis of the second law of thermodynamic on the flat plate solar collector using Al2O3/water nanofluid. Their research showed that energy efficiency rose up to 1.9% and the exergy efficiency increased by a maximum of 0.72% compared to pure water. Tiwari et al. [25] researched on the thermal performance of solar flat plate collectors for working fluid water with different nanofluids. The result showed that using 1.5% (optimum) particle volume fraction of Al2O3 nanofluid as an absorbing medium causes the thermal efficiency to enhance up to 31.64%.

    The effect of porous media and nanofluids on solar collectors has already been investigated in the literature but the SCCHP system with a collector embedded by both porous media and nanofluid for enhancing the ratio of nanoparticle in nanofluid for preventing sedimentation was not discussed. In this research, the amount of energy and exergy of the solar CCHP cycles with parabolic solar collectors in both base and improved modes with a porous material (copper foam with 95% porosity) and nanofluid with different ratios of nanoparticles was calculated. In the first step, it is planned to design a CCHP system based on the required load, and, in the next step, it will analyze the energy and exergy of the system in a basic and optimize mode. In the optimize mode, enhanced solar collectors with porous material and nanofluid in different ratios (0.1%–0.7%) were used to optimize the ratio of nanofluids to prevent sedimentation.

    2. Cycle Description

    CCHP is one of the methods to enhance energy efficiency and reduce energy loss and costs. The SCCHP system used a solar collector as a prime mover of the cogeneration system and assisted the boiler to generate vapor for the turbine. Hot water flows from the expander to the absorption chiller in summer or to the radiator or fan coil in winter. Finally, before the hot water wants to flow back to the storage tank, it flows inside a heat exchanger for generating domestic hot water [26].

    For designing of solar cogeneration system and its analysis, it is necessary to calculate the electrical, heating (heating load is the load required for the production of warm water and space heating), and cooling load required for the case study considered in a residential building with an area of 600 m2 in the warm region of Iran (Zahedan). In Table 1, the average of the required loads is shown for the different months of a year (average of electrical, heating, and cooling load calculated with CARRIER software).Table 1 The average amount of electric charges, heating load, and cooling load used in the different months of the year in the city of Zahedan for a residential building with 600 m2.

    According to Table 1, the maximum magnitude of heating, cooling, and electrical loads is used to calculate the cogeneration system. The maximum electric load is 96 kW, the maximum amount of heating load is 62 kW, and the maximum cooling load is 118 kW. Since the calculated loads are average, all loads increased up to 10% for the confidence coefficient. With the obtained values, the solar collector area and other cogeneration system components are calculated. The cogeneration cycle is capable of producing 105 kW electric power, 140 kW cooling capacity, and 100 kW heating power.

    2.1. System Analysis Equations

    An analysis is done by considering the following assumptions:(1)The system operates under steady-state conditions(2)The system is designed for the warm region of Iran (Zahedan) with average solar radiation Ib = 820 w/m2(3)The pressure drops in heat exchangers, separators, storage tanks, and pipes are ignored(4)The pressure drop is negligible in all processes and no expectable chemical reactions occurred in the processes(5)Potential, kinetic, and chemical exergy are not considered due to their insignificance(6)Pumps have been discontinued due to insignificance throughout the process(7)All components are assumed adiabatic

    Schematic shape of the cogeneration cycle is shown in Figure 1 and all data are given in Table 2.

    Figure 1 Schematic shape of the cogeneration cycle.Table 2 Temperature and humidity of different points of system.

    Based on the first law of thermodynamic, energy analysis is based on the following steps.

    First of all, the estimated solar radiation energy on collector has been calculated:where α is the heat transfer enhancement coefficient based on porous materials added to the collector’s pipes. The coefficient α is increased by the porosity percentage, the type of porous material (in this case, copper with a porosity percentage of 95), and the flow of fluid to the collector equation.

    Collector efficiency is going to be calculated by the following equation [9]:

    Total energy received by the collector is given by [9]

    Also, the auxiliary boiler heat load is [2]

    Energy consumed from vapor to expander is calculated by [2]

    The power output form by the screw expander [9]:

    The efficiency of the expander is 80% in this case [11].

    In this step, cooling and heating loads were calculated and then, the required heating load to reach sanitary hot water will be calculated as follows:

    First step: calculating the cooling load with the following equation [9]:

    Second step: calculating heating loads [9]:

    Then, calculating the required loud for sanitary hot water will be [9]

    According to the above-mentioned equations, efficiency is [9]

    In the third step, calculated exergy analysis as follows.

    First, the received exergy collector from the sun is calculated [9]:

    In the previous equation, f is the constant of air dilution.

    The received exergy from the collector is [9]

    In the case of using natural gas in an auxiliary heater, the gas exergy is calculated from the following equation [12]:

    Delivering exergy from vapor to expander is calculated with the following equation [9]:

    In the fourth step, the exergy in cooling and heating is calculated by the following equation:

    Cooling exergy in summer is calculated [9]:

    Heating exergy in winter is calculated [9]:

    In the last step based on thermodynamic second law, exergy efficiency has been calculated from the following equation and the above-mentioned calculated loads [9]:

    3. Porous Media

    The porous medium that filled the test section is copper foam with a porosity of 95%. The foams are determined in Figure 2 and also detailed thermophysical parameters and dimensions are shown in Table 3.

    Figure 2 Copper foam with a porosity of 95%.Table 3 Thermophysical parameters and dimensions of copper foam.

    In solar collectors, copper porous materials are suitable for use at low temperatures and have an easier and faster manufacturing process than ceramic porous materials. Due to the high coefficient conductivity of copper, the use of copper metallic foam to increase heat transfer is certainly more efficient in solar collectors.

    Porous media and nanofluid in solar collector’s pipes were simulated in FLOW-3D software using the finite-difference method [27]. Nanoparticles Al2O3 and CUO are mostly used in solar collector enhancement. In this research, different concentrations of nanofluid are added to the parabolic solar collectors with porous materials (copper foam with porosity of 95%) to achieve maximum heat transfer in the porous materials before sedimentation. After analyzing PTC pipes with the nanofluid flow in FLOW-3D software, for energy and exergy efficiency analysis, Carrier software results were used as EES software input. Simulation PTC with porous media inside collector pipe and nanofluids sedimentation is shown in Figure 3.

    Figure 3 Simulation PTC pipes enhanced with copper foam and nanoparticles in FLOW-3D software.

    3.1. Nano Fluid

    In this research, copper and silver nanofluids (Al2O3, CuO) have been added with percentages of 0.1%–0.7% as the working fluids. The nanoparticle properties are given in Table 4. Also, system constant parameters are presented in Table 4, which are available as default input in the EES software.Table 4 Properties of the nanoparticles [9].

    System constant parameters for input in the software are shown in Table 5.Table 5 System constant parameters.

    The thermal properties of the nanofluid can be obtained from equations (18)–(21). The basic fluid properties are indicated by the index (bf) and the properties of the nanoparticle silver with the index (np).

    The density of the mixture is shown in the following equation [28]:where ρ is density and ϕ is the nanoparticles volume fraction.

    The specific heat capacity is calculated from the following equation [29]:

    The thermal conductivity of the nanofluid is calculated from the following equation [29]:

    The parameter β is the ratio of the nanolayer thickness to the original particle radius and, usually, this parameter is taken equal to 0.1 for the calculated thermal conductivity of the nanofluids.

    The mixture viscosity is calculated as follows [30]:

    In all equations, instead of water properties, working fluids with nanofluid are used. All of the above equations and parameters are entered in the EES software for calculating the energy and exergy of solar collectors and the SCCHP cycle. All calculation repeats for both nanofluids with different concentrations of nanofluid in the solar collector’s pipe.

    4. Results and Discussion

    In the present study, relations were written according to Wang et al. [16] and the system analysis was performed to ensure the correctness of the code. The energy and exergy charts are plotted based on the main values of the paper and are shown in Figures 4 and 5. The error rate in this simulation is 1.07%.

    Figure 4 Verification charts of energy analysis results.

    Figure 5 Verification charts of exergy analysis results.

    We may also investigate the application of machine learning paradigms [3141] and various hybrid, advanced optimization approaches that are enhanced in terms of exploration and intensification [4255], and intelligent model studies [5661] as well, for example, methods such as particle swarm optimizer (PSO) [6062], differential search (DS) [63], ant colony optimizer (ACO) [616465], Harris hawks optimizer (HHO) [66], grey wolf optimizer (GWO) [5367], differential evolution (DE) [6869], and other fusion and boosted systems [4146485054557071].

    At the first step, the collector is modified with porous copper foam material. 14 cases have been considered for the analysis of the SCCHP system (Table 6). It should be noted that the adding of porous media causes an additional pressure drop inside the collector [922263072]. All fourteen cases use copper foam with a porosity of 95 percent. To simulate the effect of porous materials and nanofluids, the first solar PTC pipes have been simulated in the FLOW-3D software and then porous media (copper foam with porosity of 95%) and fluid flow with nanoparticles (AL2O3 and CUO) are generated in the software. After analyzing PTC pipes in FLOW-3D software, for analyzing energy and exergy efficiency, software outputs were used as EES software input for optimization ratio of sedimentation and calculating energy and exergy analyses.Table 6 Collectors with different percentages of nanofluids and porous media.

    In this research, an enhanced solar collector with both porous media and Nanofluid is investigated. In the present study, 0.1–0.5% CuO and Al2O3 concentration were added to the collector fully filled by porous media to achieve maximum energy and exergy efficiencies of solar CCHP systems. All steps of the investigation are shown in Table 6.

    Energy and exergy analyses of parabolic solar collectors and SCCHP systems are shown in Figures 6 and 7.

    Figure 6 Energy and exergy efficiencies of the PTC with porous media and nanofluid.

    Figure 7 Energy and exergy efficiency of the SCCHP.

    Results show that the highest energy and exergy efficiencies are 74.19% and 32.6%, respectively, that is achieved in Step 12 (parabolic collectors with filled porous media and 0.5% Al2O3). In the second step, the maximum energy efficiency of SCCHP systems with fourteen steps of simulation are shown in Figure 7.

    In the second step, where 0.1, −0.6% of the nanofluids were added, it is found that 0.5% leads to the highest energy and exergy efficiency enhancement in solar collectors and SCCHP systems. Using concentrations more than 0.5% leads to sediment in the solar collector’s pipe and a decrease of porosity in the pipe [73]. According to Figure 7, maximum energy and exergy efficiencies of SCCHP are achieved in Step 12. In this step energy efficiency is 54.49% and exergy efficiency is 18.29%. In steps 13 and 14, with increasing concentration of CUO and Al2O3 nanofluid solution in porous materials, decreasing of energy and exergy efficiency of PTC and SCCHP system at the same time happened. This decrease in efficiency is due to the formation of sediment in the porous material. Calculations and simulations have shown that porous materials more than 0.5% nanofluids inside the collector pipe cause sediment and disturb the porosity of porous materials and pressure drop and reduce the coefficient of performance of the cogeneration system. Most experience showed that CUO and AL2O3 nanofluids with less than 0.6% percent solution are used in the investigation on the solar collectors at low temperatures and discharges [74]. One of the important points of this research is that the best ratio of nanofluids in the solar collector with a low temperature is 0.5% (AL2O3 and CUO); with this replacement, the cost of solar collectors and SCCHP cycle is reduced.

    5. Conclusion and Future Directions

    In the present study, ways for increasing the efficiency of solar collectors in order to enhance the efficiency of the SCCHP cycle are examined. The research is aimed at adding both porous materials and nanofluids for estimating the best ratio of nanofluid for enhanced solar collector and protecting sedimentation in porous media. By adding porous materials (copper foam with porosity of 95%) and 0.5% nanofluids together, high efficiency in solar parabolic collectors can be achieved. The novelty in this research is the addition of both nanofluids and porous materials and calculating the best ratio for preventing sedimentation and pressure drop in solar collector’s pipe. In this study, it was observed that, by adding 0.5% of AL2O3 nanofluid in working fluids, the energy efficiency of PTC rises to 74.19% and exergy efficiency is grown up to 32.6%. In SCCHP cycle, energy efficiency is 54.49% and exergy efficiency is 18.29%.

    In this research, parabolic solar collectors fully filled by porous media (copper foam with a porosity of 95) are investigated. In the next step, parabolic solar collectors in the SCCHP cycle were simultaneously filled by porous media and different percentages of Al2O3 and CuO nanofluid. At this step, values of 0.1% to 0.6% of each nanofluid were added to the working fluid, and the efficiency of the energy and exergy of the collectors and the SCCHP cycle were determined. In this case, nanofluid and the porous media were used together in the solar collector and maximum efficiency achieved. 0.5% of both nanofluids were used to achieve the biggest efficiency enhancement.

    In the present study, as expected, the highest efficiency is for the parabolic solar collector fully filled by porous material (copper foam with a porosity of 95%) and 0.5% Al2O3. Results of the present study are as follows:(1)The average enhancement of collectors’ efficiency using porous media and nanofluids is 28%.(2)Solutions with 0.1 to 0.5% of nanofluids (CuO and Al2O3) are used to prevent collectors from sediment occurrence in porous media.(3)Collector of solar cogeneration cycles that is enhanced by both porous media and nanofluid has higher efficiency, and the stability of output temperature is more as well.(4)By using 0.6% of the nanofluids in the enhanced parabolic solar collectors with copper porous materials, sedimentation occurs and makes a high-pressure drop in the solar collector’s pipe which causes decrease in energy efficiency.(5)Average enhancement of SCCHP cycle efficiency is enhanced by both porous media and nanofluid 13%.

    Nomenclature

    :Solar radiation
    a:Heat transfer augmentation coefficient
    A:Solar collector area
    Bf:Basic fluid
    :Specific heat capacity of the nanofluid
    F:Constant of air dilution
    :Thermal conductivity of the nanofluid
    :Thermal conductivity of the basic fluid
    :Viscosity of the nanofluid
    :Viscosity of the basic fluid
    :Collector efficiency
    :Collector energy receives
    :Auxiliary boiler heat
    :Expander energy
    :Gas energy
    :Screw expander work
    :Cooling load, in kilowatts
    :Heating load, in kilowatts
    :Solar radiation energy on collector, in Joule
    :Sanitary hot water load
    Np:Nanoparticle
    :Energy efficiency
    :Heat exchanger efficiency
    :Sun exergy
    :Collector exergy
    :Natural gas exergy
    :Expander exergy
    :Cooling exergy
    :Heating exergy
    :Exergy efficiency
    :Steam mass flow rate
    :Hot water mass flow rate
    :Specific heat capacity of water
    :Power output form by the screw expander
    Tam:Average ambient temperature
    :Density of the mixture.

    Greek symbols

    ρ:Density
    ϕ:Nanoparticles volume fraction
    β:Ratio of the nanolayer thickness.

    Abbreviations

    CCHP:Combined cooling, heating, and power
    EES:Engineering equation solver.

    Data Availability

    For this study, data were generated by CARRIER software for the average electrical, heating, and cooling load of a residential building with 600 m2 in the city of Zahedan, Iran.

    Conflicts of Interest

    The authors declare that they have no conflicts of interest.

    Acknowledgments

    This work was partially supported by the National Natural Science Foundation of China under Contract no. 71761030 and Natural Science Foundation of Inner Mongolia under Contract no. 2019LH07003.

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    Energy and exergy analysis of an enhanced solar CCHP system with a collector embedded by porous media and nano fluid

    Energy and exergy analysis of an enhanced solar CCHP system with a collector embedded by porous media and nano fluid

    Year 2021, Volume 7, Issue 6, 1489 – 1505, 02.09.2021

    N. TONEKABONI  H. SALARIAN  M. Eshagh NIMVARI  J. KHALEGHINIA https://doi.org/10.18186/thermal.990897

    Abstract

    The low efficiency of Collectors that absorb energy can be mentioned as one of the drawbacks in solar cogeneration cycles. In the present study, solar systems have been improved by adding porous media and Nanofluid to collectors. One advantage of using porous media and nanomaterials is to absorb more energy while the surface area is reduced. In this study, first, solar collectors are enhanced using 90% porosity copper in solar combined cooling, heating and power systems (SCCHP). Second, different percentages of CuO and Al2O3 nano-fluids are added to a flat plate and parabolic collectors to enhance thermal properties. Simulations are performed in different modes (simple parabolic collectors, simple flat plate collectors, improved flat plate collectors, parabolic collectors with porous media, and flat plate and parabolic collectors with different density of CuO and Al2O3 nanofluids). A case study is investigated for warm and dry regions with mean solar radiation Ib = 820 w / m2 in Iran. The maximum energy and exergy efficiencies are 60.12% and 18.84%, respectively, that is related to enhanced parabolic solar collectors with porous media and nanofluids. Adding porous media and nano-fluids increases an average 14.4% collector energy efficiency and 8.08% collector exergy efficiency.

    Keywords

    Exergy analysisSolar cogeneration systemPorous mediaNanofluid

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    Details

    Primary LanguageEnglish
    SubjectsEngineering
    Journal SectionArticles
    AuthorsN. TONEKABONI  This is me
    Islamic Azad University Nour Branch
    0000-0002-1563-4407
    IranH. SALARIAN  This is me (Primary Author)
    Islamic Azad University Nour Branch
    0000-0002-2161-0276
    IranM. Eshagh NIMVARI  This is me
    Amol University of Special Modern Technologies
    0000-0002-7401-315X
    IranJ. KHALEGHINIA  This is me
    Islamic Azad University Nour Branch
    0000-0001-5357-193X
    Iran
    Publication DateSeptember 2, 2021
    Application DateDecember 28, 2020
    Acceptance DateMay 9, 2020
    Published in IssueYear 2021, Volume 7, Issue 6
    Figure 2. (a) Scanning electron microscopy images of Ti6Al4V powder particles and (b) simulated powder bed using discrete element modelling

    Laser Powder Bed에서 Laser Drilling에 의한 Keyhole 형성 Ti6Al4V 생체 의학 합금의 융합: 메조스코픽 전산유체역학 시뮬레이션 대 경험적 검증을 사용한 수학적 모델링

    Keyhole Formation by Laser Drilling in Laser Powder Bed Fusion of Ti6Al4V Biomedical Alloy: Mesoscopic Computational Fluid Dynamics Simulation versus Mathematical Modelling Using Empirical Validation

    Asif Ur Rehman 1,2,3,*
    ,† , Muhammad Arif Mahmood 4,*
    ,† , Fatih Pitir 1
    , Metin Uymaz Salamci 2,3
    ,
    Andrei C. Popescu 4 and Ion N. Mihailescu 4

    Abstract

    LPBF(Laser Powder Bed fusion) 공정에서 작동 조건은 열 분포를 기반으로 레이저 유도 키홀 영역을 결정하는 데 필수적입니다. 얕은 구멍과 깊은 구멍으로 분류되는 이러한 영역은 LPBF 프로세스에서 확률과 결함 형성 강도를 제어합니다.

    LPBF 프로세스의 핵심 구멍을 연구하고 제어하기 위해 수학적 및 CFD(전산 유체 역학) 모델이 제공됩니다. CFD의 경우 이산 요소 모델링 기법을 사용한 유체 체적 방법이 사용되었으며, 분말 베드 보이드 및 표면에 의한 레이저 빔 흡수를 포함하여 수학적 모델이 개발되었습니다.

    동적 용융 풀 거동을 자세히 살펴봅니다. 실험적, CFD 시뮬레이션 및 분석적 컴퓨팅 결과 간에 정량적 비교가 수행되어 좋은 일치를 얻습니다.

    LPBF에서 레이저 조사 영역 주변의 온도는 높은 내열성과 분말 입자 사이의 공기로 인해 분말층 주변에 비해 급격히 상승하여 레이저 횡방향 열파의 이동이 느려집니다. LPBF에서 키홀은 에너지 밀도에 의해 제어되는 얕고 깊은 키홀 모드로 분류될 수 있습니다. 에너지 밀도를 높이면 얕은 키홀 구멍 모드가 깊은 키홀 구멍 모드로 바뀝니다.

    깊은 키홀 구멍의 에너지 밀도는 다중 반사와 키홀 구멍 내의 2차 반사 빔의 집중으로 인해 더 높아져 재료가 빠르게 기화됩니다.

    깊은 키홀 구멍 모드에서는 온도 분포가 높기 때문에 액체 재료가 기화 온도에 가까우므로 얕은 키홀 구멍보다 구멍이 형성될 확률이 훨씬 높습니다. 온도가 급격히 상승하면 재료 밀도가 급격히 떨어지므로 비열과 융해 잠열로 인해 유체 부피가 증가합니다.

    그 대가로 표면 장력을 낮추고 용융 풀 균일성에 영향을 미칩니다.

    In the laser powder bed fusion (LPBF) process, the operating conditions are essential in determining laser-induced keyhole regimes based on the thermal distribution. These regimes, classified into shallow and deep keyholes, control the probability and defects formation intensity in the LPBF process. To study and control the keyhole in the LPBF process, mathematical and computational fluid dynamics (CFD) models are presented. For CFD, the volume of fluid method with the discrete element modeling technique was used, while a mathematical model was developed by including the laser beam absorption by the powder bed voids and surface. The dynamic melt pool behavior is explored in detail. Quantitative comparisons are made among experimental, CFD simulation and analytical computing results leading to a good correspondence. In LPBF, the temperature around the laser irradiation zone rises rapidly compared to the surroundings in the powder layer due to the high thermal resistance and the air between the powder particles, resulting in a slow travel of laser transverse heat waves. In LPBF, the keyhole can be classified into shallow and deep keyhole mode, controlled by the energy density. Increasing the energy density, the shallow keyhole mode transforms into the deep keyhole mode. The energy density in a deep keyhole is higher due to the multiple reflections and concentrations of secondary reflected beams within the keyhole, causing the material to vaporize quickly. Due to an elevated temperature distribution in deep keyhole mode, the probability of pores forming is much higher than in a shallow keyhole as the liquid material is close to the vaporization temperature. When the temperature increases rapidly, the material density drops quickly, thus, raising the fluid volume due to the specific heat and fusion latent heat. In return, this lowers the surface tension and affects the melt pool uniformity.

    Keywords: laser powder bed fusion; computational fluid dynamics; analytical modelling; shallow
    and deep keyhole modes; experimental correlation

    Figure 1. Powder bed schematic with voids.
    Figure 1. Powder bed schematic with voids.
    Figure 2. (a) Scanning electron microscopy images of Ti6Al4V powder particles and (b) simulated powder bed using discrete element modelling
    Figure 2. (a) Scanning electron microscopy images of Ti6Al4V powder particles and (b) simulated powder bed using discrete element modelling
    Figure 3. Temperature field contour formation at various time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms.
    Figure 3. Temperature field contour formation at various time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms.
    Figure 4. Detailed view of shallow depth melt mode with temperature field at 0.695 ms
    Figure 4. Detailed view of shallow depth melt mode with temperature field at 0.695 ms
    Figure 5. Melt flow stream traces formation at various time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms
    Figure 5. Melt flow stream traces formation at various time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms
    Figure 6. Density evolution of the melt pool at various time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms.
    Figure 6. Density evolution of the melt pool at various time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms.
    Figure 7. Un-melted and melted regions at different time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms
    Figure 7. Un-melted and melted regions at different time intervals (a) 0.695 ms, (b) 0.795 ms, (c) 0.995 ms and (d) 1.3 ms
    Figure 8. Transformation from shallow depth melt flow to deep keyhole formation when laser power increased from (a) 170 W to (b) 200 W
    Figure 8. Transformation from shallow depth melt flow to deep keyhole formation when laser power increased from (a) 170 W to (b) 200 W
    Figure 9. Stream traces and laser beam multiple reflections in deep keyhole melt flow mode
    Figure 9. Stream traces and laser beam multiple reflections in deep keyhole melt flow mode
    Figure 10. A comparison between analytical and CFD simulation results for peak thermal distribution value in the deep keyhole formation
    Figure 10. A comparison between analytical and CFD simulation results for peak thermal distribution value in the deep keyhole formation
    Figure 11. A comparison among experiments [49], CFD and analytical simulations for deep keyhole top width and bottom width
    Figure 11. A comparison among experiments [49], CFD and analytical simulations for deep keyhole top width and bottom width

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    Figure 1- Schematic diagram of pooled stepped spillway conducted by Felder et al. (2012A): Notes: h step height (10 cm): w pool height (3.1 cm): l horizontal step length (20 cm): lw pool weir length (1.5 cm): d' is the water depth above the crest; y' is the distance normal to the crest invert

    Study of inception point, void fraction and pressure over pooled stepped spillways using Flow-3D

    Khosro Morovati , Afshin Eghbalzadeh 
    International Journal of Numerical Methods for Heat & Fluid Flow

    ISSN: 0961-5539

    Article publication date: 3 April 2018

    Abstract

    많은 계단식 배수로 지오메트리 설계 지침이 평평한 단계를 위해 개발되었지만 통합 단계를 설계하는 것이 더 효율적으로 작동하는 배수로에 대한 적절한 대안이 될 수 있습니다.

    이 논문은 POOL의 다른 높이에서 공기 연행과 보이드 비율의 시작점을 다루는 것을 목표로 합니다. 그 후, FLOW-3D 소프트웨어를 사용하여 POOL과 경사면의 높이를 다르게 하여 폭기된 지역과 폭기되지 않은 지역에서 압력 분포를 평가했습니다.

    얻어진 수치 결과와 실험 결과의 비교는 본 연구에 사용된 모든 방류에 대해 잘 일치했습니다. POOL 높이는 시작 지점 위치에 미미한 영향을 미쳤습니다. 공극률의 값은 높은 방류에 비해 낮은 방전에서 더 많은 영향을 받았습니다.

    여수로의 마루(통기되지 않은 지역)에서는 음압이 나타나지 않았으며 각 방류에서 마루를 따라 높이가 15cm인 수영장에서 최대 압력 값이 얻어졌습니다.

    모든 사면에서 웅덩이 및 평평한 계단형 여수로의 계단층 부근에서는 음압이 형성되지 않았습니다. 그러나 평단식 여수로에 비해 평단식 여수로의 수직면 부근에서 음압이 더 많이 형성되어 평단식 슈트에서 캐비테이션 현상이 발생할 확률이 증가하였습니다.

    Study of inception point, void fraction and pressure over pooled
    stWhile many stepped spillways geometry design guidelines were developed for flat steps, designing pooled steps might be an appropriate alternative to spillways working more efficiency. This paper aims to deal with the inception point of air-entrainment and void fraction in the different height of the pools. Following that, pressure distribution was evaluated in aerated and non-aerated regions under the effect of different heights of the pools and slopes through the use of the FLOW-3D software. Comparison of obtained numerical results with experimental ones was in good agreement for all discharges used in this study. Pools height had the insignificant effect on the inception point location. The value of void fraction was more affected in lower discharges in comparison with higher ones. Negative pressure was not seen over the crest of spillway (non-aerated region), and the maximum pressure values were obtained for pools with 15 cm height along the crest in each discharge. In all slopes, negative pressure was not formed near the step bed in the pooled and flat stepped spillways. However, negative pressure was formed in more area near the vertical face in the flat stepped spillway compared with the pooled stepped spillway which increases the probability of cavitation phenomenon in the flat stepped chute.

    Design/methodology/approach

    압력, 공극률 및 시작점을 평가하기 위해 POOL된 계단식 여수로가 사용되었습니다. 또한 POOL의 다른 높이가 사용되었습니다. 이 연구의 수치 시뮬레이션은 Flow-3D 소프트웨어를 통해 수행되었습니다. 얻어진 결과는 풀이 압력, 공극률 및 시작점을 포함한 2상 유동 특성에 영향을 미칠 수 있음을 나타냅니다.

    Findings

    마루 위에는 음압이 보이지 않았습니다. 압력 값은 사용된 모든 높이와 15cm 높이에서 얻은 최대 값에 대해 다릅니다. 또한, 풀링 스텝은 플랫 케이스에 비해 음압점 감소에 더 효과적인 역할을 하였습니다. 시작 지점 위치는 특히 9 및 15cm 높이에 대해 스키밍 흐름 영역과 비교하여 낮잠 및 전환 흐름 영역에서 더 많은 영향을 받았습니다.

    Keywords

    Citation

    Morovati, K. and Eghbalzadeh, A. (2018), “Study of inception point, void fraction and pressure over pooled stepped spillways using Flow-3D”, International Journal of Numerical Methods for Heat & Fluid Flow, Vol. 28 No. 4, pp. 982-998. https://doi.org/10.1108/HFF-03-2017-0112

    Figure 1- Schematic diagram of pooled stepped spillway conducted by Felder et al. (2012A): Notes: h  step height (10 cm): w pool height (3.1 cm): l horizontal step length (20 cm): lw pool weir length (1.5 cm):  d' is the water depth above the crest; y' is the distance normal to the crest invert
    Figure 1- Schematic diagram of pooled stepped spillway conducted by Felder et al. (2012A): Notes: h step height (10 cm): w pool height (3.1 cm): l horizontal step length (20 cm): lw pool weir length (1.5 cm): d’ is the water depth above the crest; y’ is the distance normal to the crest invert
    Figure 2- meshing domain and distribution of blocks
    Figure 2- meshing domain and distribution of blocks
    Figure 3- Comparison of numerical simulation with experimental data by Felder et al. (2012A);  mesh convergence analysis; pooled stepped spillway (slope: 26.6 0 )
    Figure 3- Comparison of numerical simulation with experimental data by Felder et al. (2012A); mesh convergence analysis; pooled stepped spillway (slope: 26.6 0 )
    Figure 4- Comparison of numerical simulation with experimental data by Felder et al. (2012A);  Flat stepped spillway (slope: 0 26 6. )
    Figure 4- Comparison of numerical simulation with experimental data by Felder et al. (2012A); Flat stepped spillway (slope: 0 26 6. )
    Figure 5-Comparison of numerical simulation with experimental data by Felder et al. (2012B); pooled  and flat stepped spillways (slope: 0 9.8 )
    Figure 5-Comparison of numerical simulation with experimental data by Felder et al. (2012B); pooled and flat stepped spillways (slope: 0 9.8 )
    Figure 6- TKE distribution on steps 8, 9 and 10 for four different mesh numbers: 261252 (model 1),  288941 (model 2), 323578 (model 3) and 343154 (model 4)
    Figure 6- TKE distribution on steps 8, 9 and 10 for four different mesh numbers: 261252 (model 1), 288941 (model 2), 323578 (model 3) and 343154 (model 4)
    Figure 7- Comparison of obtained Void fraction distribution on step 10 in numerical simulation with  experimental work conducted by Felder et al. (2012A); (slope 26.60 )
    Figure 7- Comparison of obtained Void fraction distribution on step 10 in numerical simulation with experimental work conducted by Felder et al. (2012A); (slope 26.60 )
    Figure 8- Results of inception point of air entrainment in different height of the pools: comparison with  empirical correlations (Eqs 8-9), experimental (Felder et al. (2012A)) and numerical data
    Figure 8- Results of inception point of air entrainment in different height of the pools: comparison with empirical correlations (Eqs 8-9), experimental (Felder et al. (2012A)) and numerical data
    Figure 9- Void fraction distribution for different pool heights on steps 10; slope 26.6 0
    Figure 9- Void fraction distribution for different pool heights on steps 10; slope 26.6 0
    Figure 10- Comparison of pressure distribution between numerical simulation and experimental work  conducted by Zhang and Chanson (2016); flat stepped spillway (slope: 0 45 )
    Figure 10- Comparison of pressure distribution between numerical simulation and experimental work conducted by Zhang and Chanson (2016); flat stepped spillway (slope: 0 45 )
    Figure 11- A comparison of the pressure distribution above the crest of the spillway; B comparison of the  free surface profile along the crest of the spillway.  Note: x' indicates the longitudinal distance from the starting point of the crest.
    Figure 11- A comparison of the pressure distribution above the crest of the spillway; B comparison of the free surface profile along the crest of the spillway. Note: x’ indicates the longitudinal distance from the starting point of the crest.
    Figure 12- pressure distribution along crest of spillway in different discharges; slope 26.6
    Figure 12- pressure distribution along crest of spillway in different discharges; slope 26.6
    Figure 13- Pressure distribution near the last step bed for different slopes and discharges: x'' indicatesthe  longitudinal distance from the intersection of the horizontal and vertical faces of step 10; y" is the distance from the intersection of the horizontal and vertical faces in the vertical direction
    Figure 13- Pressure distribution near the last step bed for different slopes and discharges: x” indicatesthe longitudinal distance from the intersection of the horizontal and vertical faces of step 10; y” is the distance from the intersection of the horizontal and vertical faces in the vertical direction
    Figure 14- Pressure distribution adjacent the vertical face of step 9 for different discharges and slopes
    Figure 14- Pressure distribution adjacent the vertical face of step 9 for different discharges and slopes
    Table1- Used discharges for assessments of mesh convergence analysis and hydraulic  characteristics
    Table1- Used discharges for assessments of mesh convergence analysis and hydraulic characteristics

    Conclusion

    본 연구에서는 자유표면을 모사하기 위해 VOF 방법과 k -ε (RNG) 난류 모델을 활용하여 FLOW-3D 소프트웨어를 사용하였고, 계단식 배수로의 유동을 모사하기 위한 목적으로 난류 특성을 모사하였다. 얻은 결과는 수치 모델이 시작점 위치, 보이드 비율 및 압력을 적절하게 시뮬레이션했음을 나타냅니다. 풀의 높이는 공기 유입 위치에 미미한 영향을 미치므로 얻은 결과는 이 문서에서 제시된 상관 관계와 잘 일치했습니다. 즉, 사용 가능한 상관 관계를 서로 다른 풀 높이에 사용할 수 있습니다. 공극률의 결과는 스텝 풀 근처의 나프 유동 영역에서 공극율 값이 다른 배출보다 더 큰 것으로 나타났다. 더욱이 고방출량 .0 113m3/s에서 수영장 높이를 변경해도 수영장 표면 근처의 공극률 값에는 영향을 미치지 않았습니다.

    낮잠 및 전환 체제의 압력 분포에 대한 0 및 3cm 높이의 수영장 효과는 많은 지점에서 대부분 유사했습니다. 더욱이 조사된 모든 높이에서 여수로의 마루를 따라 부압이 없었습니다. 여수로 끝단의 바닥 부근의 압력 결과는 평평하고 고인 경우 부압이 발생하지 않았음을 나타냅니다. 수직면 부근의 음압은 웅덩이에 비해 평평한 계단형 여수로의 깊이(w=0 cm)의 대부분에서 발생하였다. 또한 더 큰 사면에 대한 풀링 케이스에서 음압이 제거되었습니다. 평단식 여수로에서는 계단의 수직면에 인접한 더 넓은 지역에서 음압이 발생하였기 때문에 이 여수로에서는 고형단식여수로보다 캐비테이션 현상이 발생할 가능성이 더 큽니다.

    In this study, the FLOW-3D software was used through utilizing the VOF method and k −ε (RNG) turbulence model in order to simulate free surface, and turbulence characteristics for the purpose of simulating flow over pooled stepped spillway. The results obtained indicated that the numerical model properly simulated the inception point location, void fraction, and pressure. The height of the pools has the insignificant effect on the location of air entrainment, so that obtained results were in good agreement with the correlations presented in this paper. In other words, available correlations can be used for different pool heights. The results of void fraction showed that the void fraction values in nappe flow regime near the step pool were more than the other discharges. Furthermore in high discharge, 0.113m3/s, altering pool height had no effect on the value of void fraction near the pool surface.

    The effect of the pools with 0 and 3 cm heights over the pressure distribution in nappe and transition regimes was mostly similar in many points. Furthermore, in all examined heights there was no negative pressure along the crest of the spillway. The pressure results near the bed of the step at the end of the spillway indicated that negative pressure did not occur in the flat and pooled cases. Negative pressure near the vertical face occurred in the most part of the depth in the flat stepped spillway (w=0 cm) in comparison with the pooled case. Also, the negative pressure was eliminated in the pooled case for the larger slopes. Since negative pressure occurred in a larger area adjacent the vertical face of the steps in the flat stepped spillways, it is more likely that cavitation phenomenon occurs in this spillway rather than the pooled stepped spillways.

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    Figures-Effects of sinusoidal oscillating laser beam on weld formation, melt flow and grain structure during aluminum alloys lap welding

    알루미늄 합금 겹침 용접 중 용접 형성, 용융 흐름 및 입자 구조에 대한 사인파 발진 레이저 빔의 영향

    Effects of sinusoidal oscillating laser beam on weld formation, melt flow and grain structure during aluminum alloys lap welding

    Lin Chen, Gaoyang Mi, Xiong Zhang, Chunming Wang
    School of Materials Science and Engineering, Huazhong University of Science and Technology, Wuhan, 430074, China

    Abstract

    레이저 사인파 진동(사인) 용접 및 레이저 용접(SLW)에서 1.5mm 6061/5182 알루미늄 합금 박판 랩 조인트의 수치 모델이 온도 분포와 용융 흐름을 시뮬레이션하기 위해 개발되었습니다.

    SLW의 일반적인 에너지 분포와 달리 레이저 빔의 사인파 진동은 에너지 분포를 크게 균질화하고 에너지 피크를 줄였습니다. 에너지 피크는 사인 용접의 양쪽에 위치하여 톱니 모양의 단면이 형성되었습니다. 이 논문은 시뮬레이션을 통해 응고 미세구조에 대한 온도 구배(G)와 응고 속도(R)의 영향을 설명했습니다.

    결과는 사인 용접의 중심이 낮은 G/R로 더 넓은 영역을 가짐으로써 더 넓은 등축 결정립 영역의 형성을 촉진하고 더 큰 GR로 인해 주상 결정립이 더 가늘다는 것을 나타냅니다. 다공성 및 비관통 용접은 레이저 사인파 진동에 의해 얻어졌습니다.

    그 이유는 용융 풀의 부피가 확대되고 열쇠 구멍의 부피 비율이 감소하며 용융 풀의 난류가 완만해졌기 때문이며, 이는 용융 흐름의 고속 이미징 및 시뮬레이션 결과에서 관찰되었습니다. 두 용접부의 인장시험에서 융착선을 따라 인장파괴 형태를 보였고 사인 용접부의 인장강도가 SLW 용접부보다 유의하게 우수하였습니다.

    이는 등축 결정립 영역이 넓을수록 균열 경향이 감소하고 파단 위치에 근접한 입자 크기가 미세하기 때문입니다. 결함이 없고 우수한 용접은 신에너지 자동차 산업에 매우 중요합니다.

    A numerical model of 1.5 mm 6061/5182 aluminum alloys thin sheets lap joints under laser sinusoidal oscillation (sine) welding and laser welding (SLW) weld was developed to simulate temperature distribution and melt flow. Unlike the common energy distribution of SLW, the sinusoidal oscillation of laser beam greatly homogenized the energy distribution and reduced the energy peak. The energy peaks were located at both sides of the sine weld, resulting in the tooth-shaped sectional formation. This paper illustrated the effect of the temperature gradient (G) and solidification rate (R) on the solidification microstructure by simulation. Results indicated that the center of the sine weld had a wider area with low G/R, promoting the formation of a wider equiaxed grain zone, and the columnar grains were slenderer because of greater GR. The porosity-free and non-penetration welds were obtained by the laser sinusoidal oscillation. The reasons were that the molten pool volume was enlarged, the volume proportion of keyhole was reduced and the turbulence in the molten pool was gentled, which was observed by the high-speed imaging and simulation results of melt flow. The tensile test of both welds showed a tensile fracture form along the fusion line, and the tensile strength of sine weld was significantly better than that of the SLW weld. This was because that the wider equiaxed grain area reduced the tendency of cracks and the finer grain size close to the fracture location. Defect-free and excellent welds are of great significance to the new energy vehicles industry.

    Keywords

    Laser weldingSinusoidal oscillatingEnergy distributionNumerical simulationMolten pool flowGrain structure

    Figures-Effects of sinusoidal oscillating laser beam on weld formation, melt flow and grain structure during aluminum alloys lap welding
    Figures-Effects of sinusoidal oscillating laser beam on weld formation, melt flow and grain structure during aluminum alloys lap welding
    Figure 6. Evolution of melt pool in the overhang region (θ = 45°, P = 100 W, v = 1000 mm/s, the streamlines are shown by arrows).

    Experimental and numerical investigation of the origin of surface roughness in laser powder bed fused overhang regions

    레이저 파우더 베드 융합 오버행 영역에서 표면 거칠기의 원인에 대한 실험 및 수치 조사

    Shaochuan Feng,Amar M. Kamat,Soheil Sabooni &Yutao PeiPages S66-S84 | Received 18 Jan 2021, Accepted 25 Feb 2021, Published online: 10 Mar 2021

    ABSTRACT

    Surface roughness of laser powder bed fusion (L-PBF) printed overhang regions is a major contributor to deteriorated shape accuracy/surface quality. This study investigates the mechanisms behind the evolution of surface roughness (Ra) in overhang regions. The evolution of surface morphology is the result of a combination of border track contour, powder adhesion, warp deformation, and dross formation, which is strongly related to the overhang angle (θ). When 0° ≤ θ ≤ 15°, the overhang angle does not affect Ra significantly since only a small area of the melt pool boundaries contacts the powder bed resulting in slight powder adhesion. When 15° < θ ≤ 50°, powder adhesion is enhanced by the melt pool sinking and the increased contact area between the melt pool boundary and powder bed. When θ > 50°, large waviness of the overhang contour, adhesion of powder clusters, severe warp deformation and dross formation increase Ra sharply.

    레이저 파우더 베드 퓨전 (L-PBF) 프린팅 오버행 영역의 표면 거칠기는 형상 정확도 / 표면 품질 저하의 주요 원인입니다. 이 연구 는 오버행 영역에서 표면 거칠기 (Ra ) 의 진화 뒤에 있는 메커니즘을 조사합니다 . 표면 형태의 진화는 오버행 각도 ( θ ) 와 밀접한 관련이있는 경계 트랙 윤곽, 분말 접착, 뒤틀림 변형 및 드로스 형성의 조합의 결과입니다 . 0° ≤  θ  ≤ 15° 인 경우 , 용융풀 경계의 작은 영역 만 분말 베드와 접촉하여 약간의 분말 접착이 발생하기 때문에 오버행 각도가 R a에 큰 영향을 주지 않습니다 . 15° < θ 일 때  ≤ 50°, 용융 풀 싱킹 및 용융 풀 경계와 분말 베드 사이의 증가된 접촉 면적으로 분말 접착력이 향상됩니다. θ  > 50° 일 때 오버행 윤곽의 큰 파형, 분말 클러스터의 접착, 심한 휨 변형 및 드 로스 형성이 Ra 급격히 증가 합니다.

    KEYWORDS: Laser powder bed fusion (L-PBF), melt pool dynamics, overhang region, shape deviation, surface roughness

    1. Introduction

    레이저 분말 베드 융합 (L-PBF)은 첨단 적층 제조 (AM) 기술로, 집중된 레이저 빔을 사용하여 금속 분말을 선택적으로 융합하여 슬라이스 된 3D 컴퓨터 지원에 따라 층별로 3 차원 (3D) 금속 부품을 구축합니다. 설계 (CAD) 모델 (Chatham, Long 및 Williams 2019 ; Tan, Zhu 및 Zhou 2020 ). 재료가 인쇄 층 아래에 ​​존재하는지 여부에 따라 인쇄 영역은 각각 솔리드 영역 또는 돌출 영역으로 분류 될 수 있습니다. 따라서 오버행 영역은 고체 기판이 아니라 분말 베드 바로 위에 건설되는 특수 구조입니다 (Patterson, Messimer 및 Farrington 2017). 오버행 영역은지지 구조를 포함하거나 포함하지 않고 구축 할 수 있으며, 지지대가있는 돌출 영역의 L-PBF는 지지체가 더 낮은 밀도로 구축된다는 점을 제외 하고 (Wang and Chou 2018 ) 고체 기판의 공정과 유사합니다 (따라서 기계적 강도가 낮기 때문에 L-PBF 공정 후 기계적으로 쉽게 제거 할 수 있습니다. 따라서지지 구조로 인쇄 된 오버행 영역은 L-PBF 공정 후 지지물 제거, 연삭 및 연마와 같은 추가 후 처리 단계가 필요합니다.

    수평 내부 채널의 제작과 같은 일부 특정 경우에는 공정 후 지지대를 제거하기가 어려우므로 채널 상단 절반의 돌출부 영역을 지지대없이 건설해야합니다 (Hopkinson and Dickens 2000 ). 수평 내부 채널에 사용할 수없는지지 구조 외에도 내부 표면, 특히 등각 냉각 채널 (Feng, Kamat 및 Pei 2021 ) 에서 발생하는 복잡한 3D 채널 네트워크의 경우 표면 마감 프로세스를 구현하는 것도 어렵습니다 . 결과적으로 오버행 영역은 (i) 잔류 응력에 의한 변형, (ii) 계단 효과 (Kuo et al. 2020 ; Li et al. 2020 )로 인해 설계된 모양에서 벗어날 수 있습니다 .) 및 (iii) 원하지 않는 분말 소결로 인한 향상된 표면 거칠기; 여기서, 앞의 두 요소는 일반적으로 mm 길이 스케일에서 ‘매크로’편차로 분류되고 후자는 일반적으로 µm 길이 스케일에서 ‘마이크로’편차로 인식됩니다.

    열 응력에 의한 변형은 오버행 영역에서 발생하는 중요한 문제입니다 (Patterson, Messimer 및 Farrington 2017 ). 국부적 인 용융 / 냉각은 용융 풀 내부 및 주변에서 큰 온도 구배를 유도하여 응고 된 층에 집중적 인 열 응력을 유발합니다. 열 응력에 의한 뒤틀림은 고체 영역을 현저하게 변형하지 않습니다. 이러한 영역은 아래의 여러 레이어에 의해 제한되기 때문입니다. 반면에 오버행 영역은 구속되지 않고 공정 중 응력 완화로 인해 상당한 변형이 발생합니다 (Kamat 및 Pei 2019 ). 더욱이 용융 깊이는 레이어 두께보다 큽니다 (이전 레이어도 재용 해되어 빌드 된 레이어간에 충분한 결합을 보장하기 때문입니다 [Yadroitsev et al. 2013 ; Kamath et al.2014 ]),응고 된 두께가 설계된 두께보다 크기 때문에형태 편차 (예 : 드 로스 [Charles et al. 2020 ; Feng et al. 2020 ])가 발생합니다. 마이크로 스케일에서 인쇄 된 표면 (R a 및 S a ∼ 10 μm)은 기계적으로 가공 된 표면보다 거칠다 (Duval-Chaneac et al. 2018 ; Wen et al. 2018 ). 이 문제는고형화 된 용융 풀의 가장자리에 부착 된 용융되지 않은 분말의 결과로 표면 거칠기 (R a )가 일반적으로 약 20 μm인 오버행 영역에서 특히 심각합니다 (Mazur et al. 2016 ; Pakkanen et al. 2016 ).

    오버행 각도 ( θ , 빌드 방향과 관련하여 측정)는 오버행 영역의 뒤틀림 편향과 표면 거칠기에 영향을 미치는 중요한 매개 변수입니다 (Kamat and Pei 2019 ; Mingear et al. 2019 ). θ ∼ 45 ° 의 오버행 각도 는 일반적으로지지 구조없이 오버행 영역을 인쇄 할 수있는 임계 값으로 합의됩니다 (Pakkanen et al. 2016 ; Kadirgama et al. 2018 ). θ 일 때이 임계 값보다 크면 오버행 영역을 허용 가능한 표면 품질로 인쇄 할 수 없습니다. 오버행 각도 외에도 레이저 매개 변수 (레이저 에너지 밀도와 관련된)는 용융 풀의 모양 / 크기 및 용융 풀 역학에 영향을줌으로써 오버행 영역의 표면 거칠기에 영향을줍니다 (Wang et al. 2013 ; Mingear et al . 2019 ).

    용융 풀 역학은 고체 (Shrestha 및 Chou 2018 ) 및 오버행 (Le et al. 2020 ) 영역 모두에서 수행되는 L-PBF 공정을 포함한 레이저 재료 가공의 일반적인 물리적 현상입니다 . 용융 풀 모양, 크기 및 냉각 속도는 잔류 응력으로 인한 변형과 ​​표면 거칠기에 모두 영향을 미치므로 처리 매개 변수와 표면 형태 / 품질 사이의 다리 역할을하며 용융 풀을 이해하기 위해 수치 시뮬레이션을 사용하여 추가 조사를 수행 할 수 있습니다. 거동과 표면 거칠기에 미치는 영향. 현재까지 고체 영역의 L-PBF 동안 용융 풀 동작을 시뮬레이션하기 위해 여러 연구가 수행되었습니다. 유한 요소 방법 (FEM)과 같은 시뮬레이션 기술 (Roberts et al. 2009 ; Du et al.2019 ), 유한 차분 법 (FDM) (Wu et al. 2018 ), 전산 유체 역학 (CFD) (Lee and Zhang 2016 ), 임의의 Lagrangian-Eulerian 방법 (ALE) (Khairallah and Anderson 2014 )을 사용하여 증발 반동 압력 (Hu et al. 2018 ) 및 Marangoni 대류 (Zhang et al. 2018 ) 현상을포함하는 열 전달 (온도 장) 및 물질 전달 (용융 흐름) 프로세스. 또한 이산 요소법 (DEM)을 사용하여 무작위 분산 분말 베드를 생성했습니다 (Lee and Zhang 2016 ; Wu et al. 2018 ). 이 모델은 분말 규모의 L-PBF 공정을 시뮬레이션했습니다 (Khairallah et al. 2016) 메조 스케일 (Khairallah 및 Anderson 2014 ), 단일 트랙 (Leitz et al. 2017 )에서 다중 트랙 (Foroozmehr et al. 2016 ) 및 다중 레이어 (Huang, Khamesee 및 Toyserkani 2019 )로.

    그러나 결과적인 표면 거칠기를 결정하는 오버행 영역의 용융 풀 역학은 문헌에서 거의 관심을받지 못했습니다. 솔리드 영역의 L-PBF에 대한 기존 시뮬레이션 모델이 어느 정도 참조가 될 수 있지만 오버행 영역과 솔리드 영역 간의 용융 풀 역학에는 상당한 차이가 있습니다. 오버행 영역에서 용융 금속은 분말 입자 사이의 틈새로 아래로 흘러 용융 풀이 다공성 분말 베드가 제공하는 약한 지지체 아래로 가라 앉습니다. 이것은 중력과 표면 장력의 영향이 용융 풀의 결과적인 모양 / 크기를 결정하는 데 중요하며, 결과적으로 오버행 영역의 마이크로 스케일 형태의 진화에 중요합니다. 또한 분말 입자 사이의 공극, 열 조건 (예 : 에너지 흡수,2019 ; Karimi et al. 2020 ; 노래와 영 2020 ). 표면 거칠기는 (마이크로) 형상 편차를 증가시킬뿐만 아니라 주기적 하중 동안 미세 균열의 시작 지점 역할을함으로써 기계적 강도를 저하시킵니다 (Günther et al. 2018 ). 오버행 영역의 높은 표면 거칠기는 (마이크로) 정확도 / 품질에 대한 엄격한 요구 사항이있는 부품 제조에서 L-PBF의 적용을 제한합니다.

    본 연구는 실험 및 시뮬레이션 연구를 사용하여 오버행 영역 (지지물없이 제작)의 미세 형상 편차 형성 메커니즘과 표면 거칠기의 기원을 체계적이고 포괄적으로 조사합니다. 결합 된 DEM-CFD 시뮬레이션 모델은 경계 트랙 윤곽, 분말 접착 및 뒤틀림 변형의 효과를 고려하여 오버행 영역의 용융 풀 역학과 표면 형태의 형성 메커니즘을 나타 내기 위해 개발되었습니다. 표면 거칠기 R의 시뮬레이션 및 단일 요인 L-PBF 인쇄 실험을 사용하여 오버행 각도의 함수로 연구됩니다. 용융 풀의 침몰과 관련된 오버행 영역에서 분말 접착의 세 가지 메커니즘이 식별되고 자세히 설명됩니다. 마지막으로, 인쇄 된 오버행 영역에서 높은 표면 거칠기 문제를 완화 할 수 있는 잠재적 솔루션에 대해 간략하게 설명합니다.

    The shape and size of the L-PBF printed samples are illustrated in Figure 1
    The shape and size of the L-PBF printed samples are illustrated in Figure 1
    Figure 2. Borders in the overhang region depending on the overhang angle θ
    Figure 2. Borders in the overhang region depending on the overhang angle θ
    Figure 3. (a) Profile of the volumetric heat source, (b) the model geometry of single-track printing on a solid substrate (unit: µm), and (c) the comparison of melt pool dimensions obtained from the experiment (right half) and simulation (left half) for a calibrated optical penetration depth of 110 µm (laser power 200 W and scan speed 800 mm/s, solidified layer thickness 30 µm, powder size 10–45 µm).
    Figure 3. (a) Profile of the volumetric heat source, (b) the model geometry of single-track printing on a solid substrate (unit: µm), and (c) the comparison of melt pool dimensions obtained from the experiment (right half) and simulation (left half) for a calibrated optical penetration depth of 110 µm (laser power 200 W and scan speed 800 mm/s, solidified layer thickness 30 µm, powder size 10–45 µm).
    Figure 4. The model geometry of an overhang being L-PBF processed: (a) 3D view and (b) right view.
    Figure 4. The model geometry of an overhang being L-PBF processed: (a) 3D view and (b) right view.
    Figure 5. The cross-sectional contour of border tracks in a 45° overhang region.
    Figure 5. The cross-sectional contour of border tracks in a 45° overhang region.
    Figure 6. Evolution of melt pool in the overhang region (θ = 45°, P = 100 W, v = 1000 mm/s, the streamlines are shown by arrows).
    Figure 6. Evolution of melt pool in the overhang region (θ = 45°, P = 100 W, v = 1000 mm/s, the streamlines are shown by arrows).
    Figure 7. The overhang contour is contributed by (a) only outer borders when θ ≤ 60° (b) both inner borders and outer borders when θ > 60°.
    Figure 7. The overhang contour is contributed by (a) only outer borders when θ ≤ 60° (b) both inner borders and outer borders when θ > 60°.
    Figure 8. Schematic of powder adhesion on a 45° overhang region.
    Figure 8. Schematic of powder adhesion on a 45° overhang region.
    Figure 9. The L-PBF printed samples with various overhang angle (a) θ = 0° (cube), (b) θ = 30°, (c) θ = 45°, (d) θ = 55° and (e) θ = 60°.
    Figure 9. The L-PBF printed samples with various overhang angle (a) θ = 0° (cube), (b) θ = 30°, (c) θ = 45°, (d) θ = 55° and (e) θ = 60°.
    Figure 10. Two mechanisms of powder adhesion related to the overhang angle: (a) simulation-predicted, θ = 45°; (b) simulation-predicted, θ = 60°; (c, e) optical micrographs, θ = 45°; (d, f) optical micrographs, θ = 60°. (e) and (f) are partial enlargement of (c) and (d), respectively.
    Figure 10. Two mechanisms of powder adhesion related to the overhang angle: (a) simulation-predicted, θ = 45°; (b) simulation-predicted, θ = 60°; (c, e) optical micrographs, θ = 45°; (d, f) optical micrographs, θ = 60°. (e) and (f) are partial enlargement of (c) and (d), respectively.
    Figure 11. Simulation-predicted surface morphology in the overhang region at different overhang angle: (a) θ = 15°, (b) θ = 30°, (c) θ = 45°, (d) θ = 60° and (e) θ = 80° (Blue solid lines: simulation-predicted contour; red dashed lines: the planar profile of designed overhang region specified by the overhang angles).
    Figure 11. Simulation-predicted surface morphology in the overhang region at different overhang angle: (a) θ = 15°, (b) θ = 30°, (c) θ = 45°, (d) θ = 60° and (e) θ = 80° (Blue solid lines: simulation-predicted contour; red dashed lines: the planar profile of designed overhang region specified by the overhang angles).
    Figure 12. Effect of overhang angle on surface roughness Ra in overhang regions
    Figure 12. Effect of overhang angle on surface roughness Ra in overhang regions
    Figure 13. Surface morphology of L-PBF printed overhang regions with different overhang angle: (a) θ = 15°, (b) θ = 30°, (c) θ = 45° and (d) θ = 60° (overhang border parameters: P = 100 W, v = 1000 mm/s).
    Figure 13. Surface morphology of L-PBF printed overhang regions with different overhang angle: (a) θ = 15°, (b) θ = 30°, (c) θ = 45° and (d) θ = 60° (overhang border parameters: P = 100 W, v = 1000 mm/s).
    Figure 14. Effect of (a) laser power (scan speed = 1000 mm/s) and (b) scan speed (lase power = 100 W) on surface roughness Ra in overhang regions (θ = 45°, laser power and scan speed referred to overhang border parameters, and the other process parameters are listed in Table 2).
    Figure 14. Effect of (a) laser power (scan speed = 1000 mm/s) and (b) scan speed (lase power = 100 W) on surface roughness Ra in overhang regions (θ = 45°, laser power and scan speed referred to overhang border parameters, and the other process parameters are listed in Table 2).

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    Simulating Porosity Factors

    다공성 요인 시뮬레이션

    Simulating Porosity Factors

    https://www.foundrymag.com/issues-and-ideas/article/21926214/simulating-porosity-factors
    Pamela Waterman

    수치 모델링 도구는 일반적이지만 원인을 파악하기가 너무 어렵 기 때문에 코어 가스 블로우 결함을 거의 이해하지 못합니다. FLOW-3D 소프트웨어는 코어 가스 흐름을 모델링하여 더 나은 품질의 주조로 이어집니다.

    파운드리는 첫 번째 시험에서 주조 품질을 달성하기 위해 많은 선행 엔지니어링을 수행해야합니다. 최근 몇 년 동안 금속 흐름, 응고, 미세 구조 진화 및 잔류 응력 모델링을위한 수치 도구가 보편화되었습니다.

    그러나 아직 완전히 해결되지 않은 주조 결함 중 하나는 일반적인 코어 가스 블로우 결함입니다. 이 문제의 물리학은 금속, 코어 및 바인더 간의 복잡한 상호 작용을 포함하며 해결되기 전에 많은 주물을 스크랩 할 수 있습니다. 대부분의 경우, 문제는 더 높은 타설 온도를 사용하고 영향을받는 영역에 더 많은 벽 스톡을 추가함으로써 단순히 관리되지만 완전히 해결되지는 않습니다.

    그러나 부품 설계가 복잡할수록 제조 문제가 발생할 가능성이 커집니다. 내부 세부 사항이 필요한 주조 조각의 경우 화학적으로 결합 된 모래 코어를 “인쇄”하여 모양을 만들고 금형 내부에 배치해야 합니다. 코어는 부품의 궁극적 인 기능에 중요한 내부 모양을 형성하며 제조 공정의 각 단계는 설계에 제약을 가합니다. 다양한 요구 사항이 코어 송풍 공정, 취급, 조립 및 가스 배출에 적용됩니다. 코어 디자인의 기술은 코어를 가열하는 동안 모양을 유지할 수 있을 만큼 견고하게 만드는 것과 부품이 냉각되었을 때 모래를 제거 할 수 있을 만큼 접착력이 끊어지는 것 사이의 미세한 균형입니다.

    최적의 분해 설계

    계획된 코어 분해의 메커니즘은 고체에서 가스로의 열 변환이지만 금형 설계는 그 가스가 코어 프린트를 통해 빠져 나갈 수 있도록해야합니다. 그렇지 않으면 금속이 기포를 가두어 모공을 형성 할 수 있습니다. 기껏해야 다공성은 표면 가공으로 밝혀집니다. 최악의 경우 부품이 더 아래쪽에서 실패합니다.

    과거에 재료 및 주조 엔지니어가 코어 가스 기포로 인한 다공성 결함 문제를 발견하면 바인더 함량 감소, 코어 환기 증가, 코어 코팅 또는 베이킹과 같은 일련의 표준 문제 해결 작업을 수행했습니다. 미리 코어. 가스가 따라가는 경로를 볼 수 없었기 때문에 하나의 금형을 완료하는 데 종종 몇 주가 걸리는 긴 인출 공정이었습니다. 그리고 다른 부분에 문제가있을 때마다 반복해야했습니다.

    이 처리 타임 라인을 압축해야하는 시장 주도적 요구는 주조 시뮬레이션 소프트웨어의 개발을 촉발했습니다. 설계와 제조 모두에 유용한 컴퓨터 기반 모델링을 통해 엔지니어는 실제 부품 비용이나 낭비없이 다양한 접근 방식을 테스트 할 수 있습니다. 파운드리가 특히 환기 설계에 시뮬레이션을 적용 할 수 있도록 Flow Science 는 최근 FLOW-3D 주조 해석 기능에 코어 가스 모델링을 추가했습니다.

    흐름에 따라

    FLOW-3D는 유체가 공기, 물, 용융 금속 또는 가스인지 여부에 관계없이 광범위한 일시적인 유체 흐름 프로세스에 대한 통찰력을 제공하는 전산 유체 역학 (CFD) 소프트웨어 패키지입니다. 다른 CFD 패키지와 비교할 때 움직이는 유체 표면을 모델링하고 추적하는 방식으로 인해 특히 정확합니다.

    코어 가스 흐름에 CFD 방법을 적용하는 것은 어려운 일입니다. 수지 기반 바인더의 화학적 복잡성으로 인해 모래 코어 열 분해 후 가스가 흐르는 위치와 방식을 이해하는 것은 복잡한 과정입니다. 그러나 Flow Science는 여러 그룹과 협력하여 실험 데이터를 얻고 시뮬레이션 된 모델의 결과와 비교했습니다. 이 회사는 General Motors, Graham-White Manufacturing Co. 및 AlchemCast에서 코어 가스 유량 정보를 수집하여 알루미늄, 철 및 강철과 함께 사용되는 모래 수지 코어에 대한 실제 데이터를 얻었습니다.

    GM Powertrain의 주조 분석 엔지니어 인 David Goettsch 박사는 15 년 동안 금속 주조의 충진 및 응고 분석에 FLOW-3D를 사용해 왔습니다. 새로운 코어 가스 모델은 설계 단계에서 재킷 코어 벤팅을 최적화하는 데 매우 유용했습니다. 코어 프린트에 대한 다른 모든 요구 사항이있는 기존 코어 박스에 벤트 트랙을 구현하는 것은 매우 어렵습니다. “코어 가스 배출에 대한 사전 분석 작업을 통해 시작하는 동안 높은 불량률을 줄일 수 있습니다.”라고 그는 설명합니다. “아마도 프로세스 기회가 문제를 해결할 수 있습니다. 하지만 그 지점에 도달하려면 테스트 기간이 오래 걸릴 수 있습니다.”

    흐름 매개 변수 정의

    도에 따라 금속 헤드 압력이 동일한 값에 도달하기 전에 가스 압력이 최고조에 달하여 가스가 거품을 형성 할 수 있습니다. 게이트 설계의 약간의 변경은 주입 속도를 높이는 데 도움이 될 수 있으므로 금속 압력이 더 빨리 생성되고 가스를 먼저 밀어 낼 수 있지만 물리적 시행 착오 접근 방식은 시간이 걸립니다. 가상 모델을 사용하여 지오메트리를 변경하는 방법을 식별하는 것은 코어 가스 시뮬레이션 소프트웨어 개발의 주요 목표였습니다.

    Flow Science의 개발자는 바인더 분해 가스 공급원, 모래의 섬도, 무게 비율에 따른 바인더의 양, 작동 온도 및 코어의 물리적 투과성과 같은 프로세스 별 매개 변수와 흐름이면의 물리학을 결합했습니다. 이 모든 값은 샌드 쉘 바인더 및 폴리 우레탄 콜드 박스 바인더 (PUCB)의 산업 보정 샘플을 사용하여 검증되었습니다.

    FLOW-3D 분석은 일정한 조성의 이상 기체를 가정하고 전체 바인더 분해의 최악의 시나리오를 취합니다. 타설하는 동안 코어 내에서 조건이 변화함에 따라 소프트웨어는 가스 압력의 변화, 가스 유동장의 기하학적 구조, 결합제 열화 영역 발생 및 금속으로의 가스 분사 가능한 표면 위치를 계산합니다. 모든 데이터는 사후 처리에 사용할 수 있습니다. 사용자는 가스 흐름을 쉽게 시각화하고 확대하고 특정 값을 얻기 위해 포인트를 클릭 할 수 있습니다.

    이제 FLOW-3D v9.4에서 사용할 수있는 코어 가스 모델을 통해 Goettsch는 다양한 삽입 및 배출 위치를 시도하고 글로벌 진단을받을 수 있습니다. 가스 발생량, 가스 발생 위치, 금속 전면이 잡히기 전에 유출 된 가스량 확인 그것까지. “실제로 문제의 근본 원인을 확인할 수있을 때 매우 좋습니다.”라고 그는 말합니다. “이러한 시각화는 실제 현상이 무엇을하고 있는지에 대한 작은 창을 확보하는 데 유용합니다.”

    멀티 코어 문제 Graham-White Manufacturing의 또 다른 숙련 된 파운드리 엔지니어 인 Elizabeth Ryder는 가스 다공성이 항상 조사하기 어려웠다는 의견을 반영합니다. 그녀는“특히 다중 코어의 경우 어떤 코어가 문제의 원인인지 파악하기가 어려웠습니다. 전체 시스템을 다루려고했습니다.”

    1,700 개의 부품을 지속적으로 생산하고 있으며 그중 일부는 연간 10,000 개의 부품을 생산하는 Graham-White는 시뮬레이션을 통해 제조 프로세스를 개선하는 데 매우 만족했습니다. 얇은 벽 부품은 코어 대 금속 비율이 높고 가스가 많이 발생하는 특별한 문제입니다.

    Graham-White는 레이저 스캐닝으로 생성 된 회색 철 부품 (약 34 인치)의 3D 모델을 사용하여 평가를 위해 현재 벤팅 설계를 제공했습니다. 이 게이팅 디자인은 수평으로 분할 된 몰드에서 패턴 플레이트 당 4 개의 인상으로 구성되었으며 각 인상에는 각 코어에 대한 통풍구가 있습니다. 중앙 스프 루를 통해 2 초 이내에 각 금형을 채울 수 있습니다.

    FLOW-3D 소프트웨어를 사용한 시뮬레이션은 채움 률을 확인했지만 하나의 코어에 환기가 충분하지 않은 것으로 나타났습니다. Graham-White는 코어에 더 깊은 구멍을 뚫어 기존 통풍구를 통해 더 많은 가스를 전달하기 시작했습니다. 새로운 벤팅 설계로 접근 방식을 전환 한 후이 회사는 코어 블로우 스크랩이 약 30 % 감소했습니다.

    또한 Flow Science 분석을 기반으로 엔지니어링 그룹은 문제가 있는 코어에 대한 추가 변경 사항을 평가하여 각 부품에 대한 추가 환기를 통해 두 부분으로 나눕니다. Ryder는 FLOW-3D 결과가 설계 초점을 좁히는데 도움이 되었고, 어떤 코어 (멀티 코어 설계)가 범인인지, 심지어 코어의 어느 영역이 문제의 원인인지 즉시 제로화 할 수 있었습니다. “미리 컴퓨터에서 더 많은 일을 할수록 더 좋습니다.”라고 그녀는 말합니다. “모든 것은 시간 절약으로 귀결됩니다.”

    Where to go from here

    파운드리 스크랩을 줄이고 주조 시뮬레이션 소프트웨어의 도움으로 자신의 핵심 인쇄 디자인의 효율성을 향상시킬 수 있습니다. Flow Science의 FLOW-3D CFD 분석 패키지의 새로운 코어 가스 모델은 중요한 다공성 계수를 시뮬레이션하여 설계자가 첫 번째 주조 전에 다양한 벤팅 설계를 평가하는 데 도움이 되기 때문에 중요합니다. 추가 재료 및 충진 방향에 대한 코어 가스 모델을 검증하는 개발이 계속됩니다.

    Fluid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 3: (a,b) Magnet distance d = 0; (c,d) Magnet distance d = 1 mm.

    Numerical Analysis of Bead Magnetophoresis from Flowing Blood in a Continuous-Flow Microchannel: Implications to the Bead-Fluid Interactions

    Scientific Reports volume 9, Article number: 7265 (2019) Cite this article

    Abstract

    이 연구에서는 비드 운동과 유체 흐름에 미치는 영향에 대한 자세한 분석을 제공하기 위해 연속 흐름 마이크로 채널 내부의 비드 자기 영동에 대한 수치 흐름 중심 연구를 보고합니다.

    수치 모델은 Lagrangian 접근 방식을 포함하며 영구 자석에 의해 생성 된 자기장의 적용에 의해 혈액에서 비드 분리 및 유동 버퍼로의 수집을 예측합니다.

    다음 시나리오가 모델링됩니다. (i) 운동량이 유체에서 점 입자로 처리되는 비드로 전달되는 단방향 커플 링, (ii) 비드가 점 입자로 처리되고 운동량이 다음으로부터 전달되는 양방향 결합 비드를 유체로 또는 그 반대로, (iii) 유체 변위에서 비드 체적의 영향을 고려한 양방향 커플 링.

    결과는 세 가지 시나리오에서 비드 궤적에 약간의 차이가 있지만 특히 높은 자기력이 비드에 적용될 때 유동장에 상당한 변화가 있음을 나타냅니다.

    따라서 높은 자기력을 사용할 때 비드 운동과 유동장의 체적 효과를 고려한 정확한 전체 유동 중심 모델을 해결해야 합니다. 그럼에도 불구하고 비드가 중간 또는 낮은 자기력을 받을 때 계산적으로 저렴한 모델을 안전하게 사용하여 자기 영동을 모델링 할 수 있습니다.

    Sketch of the magnetophoresis process in the continuous-flow microdevice.
    Sketch of the magnetophoresis process in the continuous-flow microdevice.
    Schematic view of the microdevice showing the working conditions set in the simulations.
    Schematic view of the microdevice showing the working conditions set in the simulations.
    Bead trajectories for different magnetic field conditions, magnet placed at different distances “d” from the channel: (a) d = 0; (b) d = 1 mm; (c) d = 1.5 mm; (d) d = 2 mm
    Bead trajectories for different magnetic field conditions, magnet placed at different distances “d” from the channel: (a) d = 0; (b) d = 1 mm; (c) d = 1.5 mm; (d) d = 2 mm
    Separation efficacy as a function of the magnet distance. Comparison between one-way and two-way coupling.
    Separation efficacy as a function of the magnet distance. Comparison between one-way and two-way coupling.
    (a) Fluid velocity magnitude including velocity vectors and (b) blood volumetric fraction contours with magnet distance d = 0 mm for scenario 1 (t = 0.25 s).
    (a) Fluid velocity magnitude including velocity vectors and (b) blood volumetric fraction contours with magnet distance d = 0 mm for scenario 1 (t = 0.25 s).
    luid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 2: (a,b) Magnet distance d = 0 mm at t = 0.4 s; (c,d) Magnet distance d = 1 mm at t = 0.4 s.
    luid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 2: (a,b) Magnet distance d = 0 mm at t = 0.4 s; (c,d) Magnet distance d = 1 mm at t = 0.4 s.
    Fluid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 3: (a,b) Magnet distance d = 0; (c,d) Magnet distance d = 1 mm.
    Fluid velocity magnitude including velocity vectors and blood volumetric fraction contours for scenario 3: (a,b) Magnet distance d = 0; (c,d) Magnet distance d = 1 mm.
    Blood volumetric fraction contours. Scenario 1: (a) Magnet distance d = 0 and (b) Magnet distance d = 1 mm; Scenario 2: (c) Magnet distance d = 0 and (d) Magnet distance d = 1 mm; and Scenario 3: (e) Magnet distance d = 0 and (f) Magnet distance d = 1 mm.
    Blood volumetric fraction contours. Scenario 1: (a) Magnet distance d = 0 and (b) Magnet distance d = 1 mm; Scenario 2: (c) Magnet distance d = 0 and (d) Magnet distance d = 1 mm; and Scenario 3: (e) Magnet distance d = 0 and (f) Magnet distance d = 1 mm.

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    Author information

    1. Edward P. Furlani is deceased.

    Affiliations

    1. Department of Chemical and Biomolecular Engineering, ETSIIT, University of Cantabria, Avda. Los Castros s/n, 39005, Santander, SpainJenifer Gómez-Pastora, Eugenio Bringas & Inmaculada Ortiz
    2. Flow Science, Inc, Santa Fe, New Mexico, 87505, USAIoannis H. Karampelas
    3. Department of Chemical and Biological Engineering, University at Buffalo (SUNY), Buffalo, New York, 14260, USAEdward P. Furlani
    4. Department of Electrical Engineering, University at Buffalo (SUNY), Buffalo, New York, 14260, USAEdward P. Furlani
    Fig. 1. Schematic description of the laser welding process considered in this study.

    Analysis of molten pool dynamics in laser welding with beam oscillation and filler wire feeding

    Won-Ik Cho, Peer Woizeschke
    Bremer Institut für angewandte Strahltechnik GmbH, Klagenfurter Straße 5, Bremen 28359, Germany

    Received 30 July 2020, Revised 3 October 2020, Accepted 18 October 2020, Available online 1 November 2020.

    Abstract

    Molten pool flow and heat transfer in a laser welding process using beam oscillation and filler wire feeding were calculated using computational fluid dynamics (CFD). There are various indirect methods used to analyze the molten pool dynamics in fusion welding. In this work, based on the simulation results, the surface fluctuation was directly measured to enable a more intuitive analysis, and then the signal was analyzed using the Fourier transform and wavelet transform in terms of the beam oscillation frequency and buttonhole formation. The 1st frequency (2 x beam oscillation frequency, the so-called chopping frequency), 2nd frequency (4 x beam oscillation frequency), and beam oscillation frequency components were the main components found. The 1st and 2nd frequency components were caused by the effect of the chopping process and lumped line energy. The beam oscillation frequency component was related to rapid, unstable molten pool behavior. The wavelet transform effectively analyzed the rapid behaviors based on the change of the frequency components over time.

    Korea Abstract

    빔 진동 및 필러 와이어 공급을 사용하는 레이저 용접 공정에서 용융 풀 흐름 및 열 전달은 CFD (전산 유체 역학)를 사용하여 계산되었습니다. 용융 용접에서 용융 풀 역학을 분석하는 데 사용되는 다양한 간접 방법이 있습니다.

    본 연구에서는 시뮬레이션 결과를 바탕으로 보다 직관적 인 분석이 가능하도록 표면 변동을 직접 측정 한 후 빔 발진 주파수 및 버튼 홀 형성 측면에서 푸리에 변환 및 웨이블릿 변환을 사용하여 신호를 분석했습니다.

    1 차 주파수 (2 x 빔 발진 주파수, 이른바 초핑 주파수), 2 차 주파수 (4 x 빔 발진 주파수) 및 빔 발진 주파수 성분이 발견 된 주요 구성 요소였습니다. 1 차 및 2 차 주파수 성분은 쵸핑 공정과 집중 라인 에너지의 영향으로 인해 발생했습니다.

    빔 진동 주파수 성분은 빠르고 불안정한 용융 풀 동작과 관련이 있습니다. 웨이블릿 변환은 시간 경과에 따른 주파수 구성 요소의 변화를 기반으로 빠른 동작을 효과적으로 분석했습니다.

    1 . 소개

    융합 용접에서 용융 풀 역학은 용접 결함과 시각적 이음새 품질에 직접적인 영향을 미칩니다. 이러한 역학을 연구하기 위해 고속 카메라를 사용하는 직접 방법과 광학 또는 음향 신호를 사용하는 간접 방법과 같은 다양한 측정 방법을 사용하여 여러 실험 방법을 고려했습니다. 시간 도메인의 원래 신호는 특별히 주파수 도메인에서 변환 된 신호로 변환되어 용융 풀 동작에 영향을 미치는 주파수 성분을 분석합니다. Kotecki et al. (1972)는 고속 카메라를 사용하여 가스 텅스텐 아크 용접에서 용융 풀을 관찰했습니다. [1]. 그들은 120Hz 리플 DC 출력을 가진 용접 전원을 사용할 때 용융 풀 진동 주파수가 120Hz임을 보여주었습니다. 전원을 끈 후 진동 주파수는 용융 풀의 고유 주파수를 나타내는 용융 풀 크기와 관련이 있습니다. 진동은 응고 중에 용접 표면 스케일링을 생성했습니다. Zacksenhouse and Hardt (1983)는 레이저 섀도 잉 동작 측정 기술을 사용하여 가스 텅스텐 아크 용접에서 완전히 관통 된 용융 풀의 동작을 측정했습니다 [2] . 그들은 2.5mm 두께의 강판에서 6mm 풀 반경 (고정 용접)에 대해 용융 풀의 고유 주파수가 18.9Hz라는 것을 발견했습니다. Semak et al. (1995) 고속 카메라를 사용하여 레이저 스폿 용접에서 용융 풀 및 키홀 역학 조사 [3]. 그들은 깊이가 약 3mm이고 반경이 약 3mm 인 용융 풀에서 200Hz의 낮은 체적 진동 주파수를 관찰했습니다. 0.45mm Aendenroomer와 den Ouden (1998)은 강철의 펄스 가스 텅스텐 아크 용접에서 용융 풀 진동을보고했습니다 [4] . 그들은 침투 깊이에 따라 진동 모드 변화를 보였고 주파수는 50Hz에서 150Hz 사이에서 변화했습니다. 주파수는 완전히 침투 된 용융 풀에서 더 낮았습니다. Hermans와 den Ouden (1999)은 단락 가스 금속 아크 용접에서 용융 풀 진동을 분석했습니다. [5]. 그들은 용융 풀의 단락 주파수와 고유 주파수가 같을 때 부분적으로 침투 된 용융 풀의 경우 공정 안정성이 향상되었음을 보여주었습니다. Yudodibroto et al. (2004)는 가스 텅스텐 아크 용접에서 용융 풀 진동에 대한 필러 와이어의 영향을 조사했습니다 [6] . 그들은 금속 전달이 특히 부분적으로 침투 된 용융 풀에서 진동 거동을 방해한다는 것을 보여주었습니다. Geiger et al. (2009) 레이저 키홀 용접에서 발광 분석 [7]. 신호의 주파수 분석을 사용하여 용융 풀 (1.5kHz 미만)과 키홀 (약 3kHz)에 해당하는 진동 주파수 범위를 찾았습니다. Kägeler와 Schmidt (2010)는 레이저 용접에서 용융 풀 크기의 변화를 관찰하기 위해 고속 카메라를 사용했습니다 [8] . 그들은 용융 풀에서 지배적 인 저주파 진동 성분 (100Hz 미만)을 발견했습니다. Shi et al. (2015) 고속 카메라를 사용하여 펄스 가스 텅스텐 아크 용접에서 용융 풀 진동 주파수 분석 [9]. 그들은 용접 침투 깊이가 작을수록 용융 풀의 진동 빈도가 더 높다는 것을 보여주었습니다. 추출 된 진동 주파수는 완전 용입 용접의 경우 85Hz 미만 이었지만 부분 용입 용접의 경우 110Hz에서 125Hz 사이였습니다. Volpp와 Vollertsen (2016)은 레이저 키홀 역학을 분석하기 위해 광학 신호를 사용했습니다 [10] . 그들은 공간 레이저 강도 분포로 인해 0.8에서 154 kHz 사이의 고주파 범위에서 피크를 발견했습니다. 위에서 언급 한 실험적 접근법은 공정 조건, 측정 방법 및 측정 된 위치에 따라 수십 Hz에서 수십 kHz까지 광범위한 용융 풀 역학에 대한 결과를 보여 주었다는 점에 유의해야합니다.

    융합 용접에서 용융 풀 역학을 연구하기 위해 분석 접근 방식도 사용되었습니다. Zacksenhouse와 Hardt (1983)는 2.5mm 두께의 강판에서 대칭형 완전 관통 용융 풀의 고유 진동수를 계산했습니다 [2] . 매스 스프링 해석 모델을 사용하여 용융 풀 반경 6mm (고정 용접)에 대해 20.4Hz (실험에서 18.9Hz)의 고유 진동수와 3mm 풀 반경 (연속 용접)에 대해 40Hz의 고유 진동수를 예측했습니다. ). Postacioglu et al. (1989)는 원통형 용융 풀과 키홀을 가정하여 레이저 용접의 용융 풀에서 키홀 진동의 고유 진동수를 계산했습니다 .. 특정 열쇠 구멍 모양의 경우 약 900Hz의 기본 주파수가 계산되었습니다. Postacioglu et al. (1991)은 또한 레이저 용접에서 용접 속도를 고려하기 위해 타원형 용융 풀의 고유 진동수를 계산했습니다 [12] . 그들은 타원형 용융 풀의 모양이 고유 진동수에 영향을 미친다는 것을 보여주었습니다. 고유 진동수는 축의 길이 비율이 낮았으며, 즉 타원의 반장 축과 반 단축의 비율이 낮았습니다. Kroos et al. (1993)은 축 대칭 용융 풀과 키홀을 가정하여 레이저 키홀 용접의 동적 거동에 대한 이론적 모델을 개발했습니다 .. 키홀 폐쇄 시간은 0.1ms였으며 안정성 분석은 약 500Hz의 주파수에서 공진과 같은 진동을 예측했습니다. Maruo와 Hirata (1993)는 완전 관통 아크 용접에서 용융 풀을 모델링했습니다 [14] . 그들은 녹은 웅덩이가 정적 타원 모양을 가지고 있다고 가정했습니다. 그들은 고유 진동수와 진동 모드 사이의 관계를 조사하고 용융 풀 크기가 감소함에 따라 고유 진동수가 증가한다는 것을 보여주었습니다. Klein et al. (1994)는 원통형 키홀 모양을 사용하여 완전 침투 레이저 용접에서 키홀 진동을 연구했습니다 [15] . 그들은 점성 감쇠로 인해 키홀 진동이 낮은 kHz 범위로 제한된다는 것을 보여주었습니다. Klein et al. (1996)은 또한 레이저 출력의 작은 변동이 강한 키홀 진동으로 이어질 수 있음을 보여주었습니다[16] . 그들은 키홀 진동의 주요 공진 주파수 범위가 500 ~ 3500Hz라는 것을 발견했습니다. Andersen et al. (1997)은 고정 가스 텅스텐 아크 용접 [17] 에서 고정 된 원통형 모양을 가정하여 용융 풀의 고유 진동수를 예측 했으며 완전 용입 용접에서 용융 풀 폭이 증가함에 따라 감소하는 것으로 나타났습니다. 3.175mm 두께의 강판의 경우 주파수는 20Hz ~ 100Hz 범위였습니다. 위에 표시된 분석 방법은 일반적으로 단순한 용융 풀 모양을 가정하고 고유 진동수를 계산했습니다. 이것은 단순한 용융 풀 모양으로 고정 용접 공정을 분석하는 데 충분하지만 대부분의 용접 사례를 설명하는 과도 용접 공정에서 용융 풀 역학 분석에는 적합하지 않습니다.

    반면에 수치 접근 방식은 고온 및 강한 빛과 같은 실험적 제한없이 자세한 정보를 제공하기 때문에 용융 풀 역학을 분석하는 이점이 있습니다. 전산 유체 역학 (CFD)의 수치 시뮬레이션 기술이 발전함에 따라 용융 풀 역학 분석에 대한 많은 연구가 수행되었습니다. 실제 용융 표면 변화는 VOF (체적 부피) 방법을 사용하여 계산할 수 있습니다. Cho et al. (2010) CO 2 레이저-아크 하이브리드 용접 공정을 위한 수학적 모델 개발 [18], 구형 방울이 생성 된 금속 와이어의 용융 과정이 와이어 공급 속도와 일치한다고 가정합니다. 그들은 필러 와이어가 희석되는 용융 풀 동작을 보여주었습니다. Cho et al. (2012)는 높은 빔 품질과 높은 금속 흡수율로 인해 업계에서 널리 사용되는 디스크 레이저 키홀 용접으로 수학적 모델을 확장했습니다 [19] . 그들은 열쇠 구멍에서 레이저 광선 번들의 다중 반사를 고려하고 용융 풀에서 keyholing과 같은 빠른 표면 변화를 자세히보고했습니다. 최근 CFD 시뮬레이션은 험핑 (Otto et al., 2016 [20] ) 및 기공 (Lin et al., 2017 [21] )과 같은보다 구체적인 현상을 분석하는데도 사용되었습니다 .) 레이저 용접에서. 그러나 용융 풀 역학과 관련된 연구는 거의 수행되지 않았습니다. Ko et al. (2000)은 수치 시뮬레이션을 사용하여 가스 텅스텐 아크 용접 풀의 동적 거동을 조사했습니다 [22] . 그들은 완전히 침투 된 용융 풀이 부분적으로 침투 된 풀보다 낮은 주파수에서 진동한다는 것을 보여주었습니다. 진동은 수십 분의 1 초 내에 무시할 수있는 크기로 감쇠되었습니다. Geiger et al. (2009)는 또한 수치 시뮬레이션을 사용하여 레이저 용접에서 용융 풀 거동을 보여주었습니다 [7]. 그들은 계산 된 증발 속도를 주파수 분석에 사용하여 공정에서 나오는 빛의 실험 결과와 비교했습니다. 판금 레이저 용접에서 중요한 공간 빔 진동 및 추가 필러 재료가있는 공정에 대한 용융 풀 역학에 대한 연구도 불충분합니다. Hu et al. (2018)은 금속 전달 메커니즘을 밝히기 위해 전자빔 3D 프린팅에서 와이어 공급 모델링을 수행했습니다. 그들은 주로 열 입력에 의해 결정되는 액체 브리지 전이, 액적 전이 및 중간 전이의 세 가지 유형의 금속 전달 모드를 보여주었습니다 .. Meng et al. (2020)은 레이저 빔 용접에서 용융 풀에 필러 와이어에 의해 추가 된 추가 요소의 전자기 교반 효과를 모델링했습니다. 용가재의 연속적인 액체 브릿지 이동이 가정되었고, 그 결과 전자기 교반의 영향이 키홀 깊이에 미미한 반면 필러 와이어 혼합을 향상 시켰습니다 [24] . Cho et al. (2017) 용접 방향에 수직 인 1 차원 빔 진동과 용접 라인을 따라 공급되는 필러 와이어를 사용하여 레이저 용접을위한 시뮬레이션 모델 개발 [25]. 그들은 시뮬레이션을 사용하여 특정 용접 현상, 즉 용융 풀의 단추 구멍 형성을 보여주었습니다. Cho et al. (2018)은 다중 반사 수와 전력 흡수량의 푸리에 변환을 사용하여 주파수 영역에서 소위 쵸핑 주파수 (2 x 빔 발진 주파수) 성분을 발견했습니다 [26] . 그러나 그들은 용융 풀 역학을 분석하기 위해 간접 신호를 사용했습니다. 따라서보다 직관적 인 분석을 위해서는 표면의 변동을 직접 측정해야합니다.

    이 연구는 이전 연구에서 개발 된 레이저 용접 모델을 사용하여 3 차원 과도 CFD 시뮬레이션을 수행하여 빔 진동 및 필러 와이어 공급을 포함한 레이저 용접 공정에서 용융 풀 역학을 조사합니다. 용융 된 풀 표면의 시간적 변화는 시뮬레이션 결과에서 추출되었습니다. 추출 된 데이터는 주파수 영역뿐만 아니라 시간-주파수 영역에서도 분석되었습니다. 신호 처리를 통해 도출 된 결과는 특징적인 용융 풀 역학을 나타내며 빔 진동 주파수 및 단추 구멍 형성 측면에서 레이저 용접의 역학을 줄일 수있는 잠재력을 제공합니다.

    2 . 방법론

    그림 1도 1은 용접 방향에 수직 인 1 차원 빔 진동과 용접 라인을 따라 공급되는 필러 와이어를 사용하는 레이저 용접 프로세스의 개략적 설명을 보여줍니다. 1mm 두께의 알루미늄 합금 (AlSi1MgMn) 시트는 시트 표면에 초점을 맞춘 멀티 kW 파이버 레이저 (YLR-8000S, IPG Photonics, USA)를 사용하여 용접되었습니다. 시트는 에어 갭이있는 맞대기 이음으로 정렬되었습니다. 1 차원 스캐너 (ILV DC-Scanner, Ingenieurbüro für Lasertechnik + Verschleiss-Schutz (ILV), 독일)를 사용하여 레이저 빔의 1 차원 정현파 진동을 실현했습니다. 이 스캔 시스템에서 최대 진동 폭은 250Hz의 진동 주파수에서 1.4mm입니다. 오정렬에 대한 공차를 개선하기 위해 동일한 최대 너비 값이 사용되었습니다. 와이어 공급 시스템은 1을 공급했습니다. 2mm 직경의 알루미늄 합금 (AlSi5) 필러 와이어를 일정한 공급 속도로 에어 갭을 채 웁니다. 1mm 에어 갭의 경우 와이어 이송 속도는 용접 속도의 1.5 배 값으로 설정되었으며 참조 실험 조건은 문헌에서 얻었습니다 (Schultz, 2015 참조).[27] ).

    그림 1

    CFD 시뮬레이션은 레이저 용접에서 열 전달 및 용융 풀 동작을 계산하기 위해 수행되었습니다. 그림 2 는 CFD 시뮬레이션을위한 계산 영역을 보여줍니다. 실온에서 1.2mm 직경의 필러 와이어가 공급되고 레이저 빔이 진동했습니다. 1mm 두께의 공작물이 용접 속도로 왼쪽에서 오른쪽으로 이동했습니다. 0.1mm의 최소 메쉬 크기가 도메인에서 생성되었습니다. 침투 깊이가 더 깊은 이전 연구의 메쉬 테스트 결과는 0.2mm 이하의 메쉬 크기로 시뮬레이션 정확도가 확보 된 것으로 나타 났으므로 [28] 본 연구에서 사용 된 메쉬 크기가 적절할 수 있습니다. 도메인을 구성하는 세포의 수는 약 120 만 개였습니다. 1 번 테이블사용 된 레이저 용접 매개 변수를 보여줍니다. 용융 풀 역학 측면에서 다양한 진동 주파수와 에어 갭 크기가 고려되었으며 12 개의 용접 사례가 표 2 에 나와 있습니다. 표 3 은 시뮬레이션에 사용 된 알루미늄 합금과 순수 알루미늄 (Cho et al., 2018 [26] )의 표면 장력 계수를 제외하고 온도와 무관 한 열-물리적 재료 특성을 보여줍니다 . 여기서 표면 장력 계수는 액체 온도에서 온도와 표면 장력 계수 사이의 선형 관계를 가진 유일한 온도 의존적 ​​특성이었습니다.

    그림 2

    표 1 . . 레이저 용접 매개 변수.

    레이저 용접 매개 변수
    레이저 빔 파워3.0kW
    빔 허리 반경50µm *
    용접 속도6.0m / 분
    와이어 공급 속도9.0m / 분
    빔 진동 폭1.4mm
    빔 진동 주파수100Hz, 150Hz, 200Hz, 250Hz
    에어 갭 크기0.8mm, 0.9mm, 1.0mm, 1.1mm

    반경은 1.07μm의 파장, 4.2mm • mrad의 빔 품질, 시준 초점 거리 및 초점 렌즈 200mm, 광섬유 직경 100μm의 원형 빔을 가정하여 계산되었습니다.

    표 2 . 이 연구에서 고려한 용접 사례.

    에어 갭 크기 [mm]진동 주파수 [Hz]
    100150200250
    0.9사례 1엑스엑스엑스
    1.0사례 2사례 4사례 7사례 10
    1.1사례 3사례 5사례 8사례 11
    1.2엑스사례 6사례 912면

    표 3 . 시뮬레이션에 사용 된 열 물리적 재료 특성 (Cho et al., 2018 [26] ).

    특성상징
    밀도ρ2700kg / m3
    열 전도성케이1.7×102Wm K
    점도ν1.15×10−삼kg / ms
    표면 장력 계수 티엘*γ엘0.871 J / m2
    표면 장력 온도 구배 *−1.55×10−4J / m 2 K
    표면 장력 계수γγ엘−ㅏ(티−티엘)
    비열8.5×102J / kg K
    융합 잠열h에스엘3.36×105J / kg
    기화 잠열 *hV1.05×107J / kg
    Solidus 온도티에스847K
    Liquidus 온도티엘905K
    끓는점 *티비2743K

    순수한 알루미늄.

    시뮬레이션을 위해 단상 뉴턴 유체와 비압축성 층류가 가정되었습니다. 질량, 운동량 및 에너지 보존의 지배 방정식을 해결하여 계산 영역에서 속도, 압력 및 온도 분포를 얻었습니다. VOF 방법은 자유 표면 경계를 찾는 데 사용되었습니다. 스칼라 보존 방정식을 추가로 도입하여 용융 풀에서 충전재의 부피 분율을 계산했습니다. 시뮬레이션에 사용 된 레이저 용접의 수학적 모델은 다음과 같습니다. 레이저 빔은 가우스와 같은 전력 밀도 분포를 기반으로 697 개의 광선 에너지 번들로 나뉩니다. 광선 추적 방법을 사용하여 다중 반사를 고려했습니다. 재료에 대한 레이저 빔의 반사 (또는 흡수) 에너지는 프레 넬 반사 모델을 사용하여 계산되었습니다. 온도에 따른 흡수율의 변화를 고려 하였다. 혼합물의 흡수율은베이스 및 충전제 물질 분획의 가중 평균을 사용하여 계산되었습니다. 반동 압력과 부력도 고려되었습니다. 경계 조건으로 에너지와 압력의 균형은 VOF 방법으로 계산 된 자유 표면에서 고려되었습니다. 레이저 용접 모델과 지배 방정식은 FLOW-3D v.11.2 (2017), Flow Science, Inc.에서 유한 차분 방법과 유한 체적 방법을 사용하여 이산화되고 해결되었습니다. 경계 조건으로 에너지와 압력의 균형은 VOF 방법으로 계산 된 자유 표면에서 고려되었습니다. 레이저 용접 모델과 지배 방정식은 FLOW-3D v.11.2 (2017), Flow Science, Inc.에서 유한 차분 방법과 유한 체적 방법을 사용하여 이산화되고 해결되었습니다. 경계 조건으로 에너지와 압력의 균형은 VOF 방법으로 계산 된 자유 표면에서 고려되었습니다. 레이저 용접 모델과 지배 방정식은 FLOW-3D v.11.2 (2017), Flow Science, Inc.에서 유한 차분 방법과 유한 체적 방법을 사용하여 이산화되고 해결되었습니다.[29] . 계산에는 48GB RAM이 장착 된 Intel® Xeon® 프로세서 E5649로 구성된 워크 스테이션이 사용되었습니다. 계산 시스템을 사용하여 0.2 초 레이저 용접을 시뮬레이션하는 데 약 18 시간이 걸렸습니다. 지배 방정식 (Cho and Woizeschke, 2020 [30] ) 및 레이저 용접 모델 (Cho et al., 2018 [26] )에 대한 자세한 설명은 부록 A 에서 확인할 수 있습니다 .

    그림 3 은 용융 풀 변동의 직접 측정에 대한 개략적 설명을 보여줍니다. 용융 풀의 역학을 분석하기 위해 시뮬레이션 중에 용융 풀 표면의 시간적 변동 운동을 측정했습니다. 상단 및 하단 표면 모두에서 10kHz의 샘플링 주파수로 변동을 측정 한 반면, 측정 위치는 X 축의 레이저 빔 위치에서 2mm 떨어진 용접 중심선에있었습니다. 그림 4시간 신호를 분석하는 데 사용되는 푸리에 변환 및 웨이블릿 변환의 개략적 설명을 보여줍니다. 측정 된 시간 신호는 고속 푸리에 변환 (FFT) 방법을 사용하여 주파수 영역으로 변환되었습니다. 결과는 측정 기간 동안 평균화 된 주파수 성분의 크기를 보여줍니다. 웨이블릿 변환 방법은 시간-주파수 영역에서 국부적 인 특성을 찾는 데 사용되었습니다. 결과는 주파수 구성 요소의 크기뿐만 아니라 시간 변화도 보여줍니다.

    그림 3
    그림 4

    3 . 결과

    이 연구 에서는 표 2에 표시된 12 가지 용접 사례 를 시뮬레이션했습니다. 그림 5 는 3 차원 시뮬레이션 결과를 평면도 와 바닥면으로 보여줍니다. 결과는 용융 된 풀의 거동에 따라 분류 할 수 있습니다 : 단추 구멍 형성 없음 (녹색), 안정 또는 불안정 단추 구멍 있음 (파란색), 불안정한 단추 구멍으로 인한 구멍 결함 (빨간색). 일반적인 열쇠 구멍보다 훨씬 큰 직경을 가진 단추 구멍은 레이저 용접의 특정 진동 조건에서 나타날 수 있습니다 (Vollertsen, 2016 [31]). 진동 주파수가 증가함에 따라 용접 이음 부 코스 및 스케일링 측면에서 시각적 이음새 품질이 향상되었습니다. 고주파에서 스케일링은 무시할 수있을 정도 였고 코스는 균질했습니다. 언더컷 결함의 발생도 감소했습니다. 그러나 관통 결함 부족 (case 7, case 10)이 나타났다. 에어 갭은 단추 구멍 형성에 중요했습니다. 에어 갭 크기가 증가함에 따라 단추 구멍이 더 쉽게 형성되었지만 구멍 결함으로 더 쉽게 남아 있습니다. 안정적인 단추 구멍 형성은 고려 된 공극 조건의 좁은 영역에서만 나타납니다.

    그림 5

    그림 6 은 시뮬레이션과 실험에서 융합 영역의 모양을 보여줍니다. 버튼 홀이없는 경우 1, 불안정한 버튼 홀 형성이있는 경우 8, 안정적인 버튼 홀 형성이있는 경우 11의 3 가지 경우에 대해 시뮬레이션 결과와 실험 결과를 비교하여 유사성을 나타냈다. 본 연구에서 고려한 용접 조건의 경우 표면 품질 결과는 Fig. 5 와 같이 큰 차이를 보였으 나 단면 융착 영역 [26] 과 형상은 큰 차이를 보이지 않았다.

    그림 6

    무화과. 7 과 8 은 각각 100Hz와 250Hz의 진동 주파수에서 시뮬레이션 결과를 기반으로 분석 된 용융 풀 역학과 시뮬레이션 및 실험 결과를 보여줍니다. 이전 연구에서 볼 수 있듯이 레이저 빔의 진동 주파수는 단추 구멍 형성과 밀접한 관련이 있습니다 (Cho et al., 2018 [26] 참조 ). 그림 7 (a) 및 (b)는 각각 시뮬레이션 및 실험을 기반으로 한 진동 주파수 100Hz에서 대표적인 용융 풀 동작을 보여줍니다. 완전히 관통 된 키홀 및 버튼 홀 형성은 관찰되지 않았으며 응고 후 거친 비드 표면이 남았습니다. 그림 7(c)와 (d)는 각각 윗면과 바닥면의 표면 변동에 대한 시뮬레이션 결과를 기반으로 한 용융 풀 역학 분석을 보여줍니다. 샘플링 데이터는 상단 표면이 공작물의 상단 표면 위치에서 평균적으로 변동하는 반면 하단 표면은 공작물의 하단 표면 위치에서 평균적으로 변동하는 것으로 나타났습니다. 표면 변동의 푸리에 변환 및 웨이블릿 변환 결과는 명확한 1  주파수 (2 x 빔 발진 주파수, 이른바 초핑 주파수, Cho et al., 2018 [26] 참조 ) 및 2  주파수 (4 x 빔 발진)를 보여줍니다. 주파수) 두 표면의 구성 요소, 그러나 바닥 표면과 첫 번째에 대한 결과주파수 성분이 더 강합니다. 반면 그림 8 (a)와 (b)에서 보는 바와 같이 250Hz의 진동 주파수에서 시뮬레이션과 실험 결과는 안정된 버튼 홀 형성과 응고 후 매끄러운 비드 표면을 나타냈다. 그림 8 의 샘플링 신호의 진폭은 그림 7 의 진폭 보다 작으며 푸리에 변환 및 웨이블릿 변환의 결과에서 중요한 주파수 성분이 발견되지 않았습니다.

    Fi 7
    그림 8

    Fig. 9 는 진동 주파수 200Hz에서 시뮬레이션 결과를 바탕으로 분석 된 용융 풀 역학과 시뮬레이션 및 실험 결과를 보여준다. 이 주파수에서 Fig. 9 (a)와 (b) 에서 보는 바와 같이 , 시뮬레이션과 실험 모두에서 불안정한 buttonhole 거동이 관찰되었다. 바닥면에서 샘플링 데이터의 푸리에 변환 및 웨이블릿 변환의 결과 빔 발진 주파수 성분이 발견되었습니다.

    그림 9

    4 . 토론

    시뮬레이션 및 실험 결과는 비드 표면 품질이 향상되고 빔 진동 주파수가 증가함에 따라 버튼 홀이 형성되는 것으로 나타났습니다. 표면의 변동 데이터에 대한 푸리에 변환 및 웨이블릿 변환의 결과에 따라 다음과 같은 주요 주파수 구성 요소가 발견되었습니다. 1  및 2 버튼 홀 형성이없는 주파수, 불안정한 용융 풀 거동이있는 빔 진동 주파수, 안정적인 버튼 홀 형성이있는 중요한 주파수 성분이 없습니다. 이들 중 불안정한 용융 풀 동작과 관련된 빔 진동 주파수 성분은 완전히 관통 된 키홀과 반복적으로 생성 및 붕괴되는 불안정한 버튼 홀의 특성으로 인해 웨이블릿 변환 결과에서 명확한 실선 형태로 나타나지 않았습니다. 분석 결과는 윗면보다 바닥면에서 더 분명했습니다. 이는 필러 와이어 공급 및 키홀 링 공정에서 강한 하향 흐름으로 인해 용융 풀 역학이 바닥 표면 영역에서 더 강했기 때문입니다. 진동 주파수가 증가함에 따라 용융 풀 역학과 상단 표면과 하단 표면 간의 차이가 감소했습니다.

    첫 번째 주파수 (2 x 빔 진동 주파수)는이 연구에서 관찰 된 가장 분명한 구성 요소였습니다. Schultz et al. (2018)은 또한 실험을 통해 동일한 성분을 발견했습니다 [32] , 용융 풀 표면 운동에 대한 푸리에 분석을 수행했습니다. 첫 번째 주파수 성분은 빔 발진주기 당 두 개의 주요 이벤트가 있음을 의미합니다. 이것은 레이저 빔이 빔 진동주기 당 두 번 와이어를 절단하거나 절단하는 프로세스와 일치합니다. 용융 된 와이어 팁은 낮은 진동 주파수에서 고르지 않고 날카로운 모서리를 갖는 것으로 나타났습니다 (Cho et al., 2018 [26] ). 이것은 첫 번째 원인이 될 수 있습니다.용융 된 풀에서 지배적이되는 주파수 성분. 진동 주파수가 증가하면 용융 된 와이어 팁이 더 균일 해 지므로 효과가 감소합니다. 용접 방향으로의 정현파 횡 방향 빔 진동을 통한 에너지 집중도 빔 진동주기 당 두 번 발생합니다. 그림 10 은 발진 주파수에 따른 레이저 빔의 라인 에너지 (단위 길이 당 에너지)의 변화를 보여줍니다. 그림 10 b) 의 라인 에너지 는 레이저 출력을 공정 속도로 나누어 계산했습니다. 여기서 처리 속도는(w이자형엘디나는엔지에스피이자형이자형디)2+(디(에스나는엔유에스영형나는디ㅏ엘wㅏV이자형나는엔에프나는지.10ㅏ))디티)2. 낮은 발진 주파수에서 라인 에너지는 발진 폭의 양쪽 끝에 과도하게 집중됩니다. 이러한 집중된 에너지는 과도한 키홀 링 프로세스를 초래하므로 언더컷 결함이 나타날 수있는 높은 흐름 역학이 발생합니다. 진동 주파수가 증가함에 따라 집중 에너지는 더 작은 조각으로 나뉩니다. 따라서 높은 진동 주파수에서 과도한 키홀 링 및 수반되는 언더컷 결함의 발생이 감소되었습니다. 위에서 언급 한 두 가지 현상 (불균일 한 와이어 팁과 집중된 라인 에너지)은 빔 발진주기 당 두 번 발생하며 발진 주파수가 증가하면 그 효과가 감소합니다. 따라서 저주파 에서 2  주파수 성분 (4 x 빔 발진 주파수)이 나타나는 것은이 두 현상의 동시 작용입니다.

    그림 10

    두 가지 현상 중 첫 번째 주파수 에 대한 주된 효과 는 집중된 라인 에너지입니다. Cho et al. (2018)은 전력 흡수 데이터를 푸리에 변환을 사용하여 분석했을 때 1  주파수 성분이 더 우세 해졌고, 2  주파수 성분은 발진 주파수가 증가함에 따라 상대적으로 약화 되었음을 보여주었습니다 [26] . 용융 된 와이어 팁은 또한 빈도가 증가함에 따라 더욱 균일 해졌습니다. 결과는 진동 주파수의 증가가 용융 풀에 대한 와이어의 영향을 제거하는 것으로 나타났습니다. 따라서 발진 주파수가 증가함에 따라 라인 에너지 집중의 영향 만 남을 수 있습니다. 그림 10 과 같이, 집중 선 에너지가 작은 조각으로 분할되기 때문에 효과도 감소하지만 최대 값이 변경되지 않았기 때문에 여전히 효과적입니다.

    빔 진동 주파수 성분은 불안정한 단추 구멍 및 열쇠 구멍 붕괴를 수반하는 불안정한 용융 풀 동작과 관련이 있습니다. 언더컷 결함이있는 케이스 8 (발진 주파수 200Hz)에서 발진 주파수 성분이 관찰되었습니다. 이것은 특히 완전히 관통 된 열쇠 구멍과 불안정한 단추 구멍에서 불안정한 용융 풀 동작을 보여주었습니다. 경우 10 (진동 주파수 250Hz)의 경우 상대적으로 건강한 비드가 형성 되었으나, 도 11 (a) 와 같이 웨이블릿 변환 결과에서 t1의 시간 간격으로 진동 주파수 성분이 관찰되었다 . 이 시간 간격 t1의 용융 풀 거동은 그림 11에 나와 있습니다.(비). 완전히 관통 된 열쇠 구멍이 즉시 무너지는 것이 분명하게 관찰되었습니다. 이것은 진동 주파수 성분이 불안정한 용융 풀 거동과 밀접한 관련이 있음을 보여줍니다. 발견 된 주파수 성분으로부터 완전히 관통 된 열쇠 구멍과 같은 불안정한 용융 풀 거동을 예측할 수 있습니다. 완전히 관통 된 키홀이 반복적으로 붕괴되기 때문에 빔 진동 주파수 성분은 그림 9 (d) 와 같이 웨이블릿 변환 결과에서 명확한 실선 형태로 보이지 않습니다 .

    그림 11

    Cho and Woizeschke (2020)에 따르면 단추 구멍 형성은 자체 지속 가능한 카테 노이드처럼 작용하기 때문에 용융 풀 역학을 감소시킬 수 있습니다 [30] . 그림 12 는 버튼 홀 형성 측면에서 t2의 시간 간격에서 용융 풀 거동의 변화를 보여줍니다. 단추 구멍은 t2의 간헐적 인 부분에만 형성되었습니다. 1st 이후이 시간 동안 웨이블릿 변환의 결과로 주파수 성분이 사라졌고, 버튼 홀 형성은 용융 풀 역학을 줄이는 데 효과적이었습니다. 따라서, 웨이블릿 변환의 결과로 주파수 성분이 지워지는 것을 관찰함으로써 버튼 홀 형성을 예측할 수있다. 이와 관련하여 웨이블릿 변환 기술은 시간에 따른 용융 풀 변화를 나타낼 수 있습니다. 이 기술은 향후 용융 풀 동작을 모니터링하는 데 사용될 수 있습니다.

    그림 12

    5 . 결론

    CFD 시뮬레이션 결과를 사용하여 빔 진동 및 필러 와이어 공급을 통한 레이저 용접에서 용융 풀 역학을 분석 할 수있었습니다. 용융 풀 표면의 변동 데이터의 푸리에 변환 및 웨이블릿 변환은 여기서 용융 풀 역학을 분석하는 데 사용되었습니다. 결과는 다음과 같은 결론으로 ​​이어집니다.1.

     주파수 (2 x 빔 발진 주파수, 이른바 초핑 주파수), 2  주파수 (4 x 빔 발진 주파수) 및 빔 발진 주파수 성분은 푸리에 변환 및 웨이블릿 변환 분석에서 발견 된 주요 성분이었습니다.2.

     주파수와 2  주파수 성분 의 출현은 두 가지 사건, 즉 레이저 빔에 의한 필러 와이어의 절단 공정과 집중된 레이저 라인 에너지의 효과의 결과였습니다. 이는 빔 진동주기 당 두 번 발생했습니다. 따라서 두 번째 주파수 성분은 동시 작용으로 인해 발생했습니다. 빔 진동 주파수 성분은 불안정한 용융 풀 동작과 관련이 있습니다. 구성 요소는 열쇠 구멍과 단추 구멍의 붕괴와 함께 나타났습니다.삼.

    낮은 발진 주파수에서는 1  주파수와 2  주파수 성분이 함께 나타 났지만 발진 주파수가 증가함에 따라 그 크기가 함께 감소했습니다. 집중 선 에너지는 주파수가 증가함에 따라 최대 값이 변하지 않는 반면, 잘게 잘린 선단이 평평 해져 그 효과가 사라졌기 때문에 쵸핑 프로세스보다 더 큰 영향을 미쳤습니다.4.

    용융 풀 거동의 빠른 시간적 변화는 웨이블릿 변환 방법을 사용하여 분석되었습니다. 따라서이 방법은 열쇠 구멍 및 단추 구멍의 형성 및 붕괴와 같은 일시적인 용융 풀 변화를 해석하는 데 사용할 수 있습니다.

    CRediT 저자 기여 성명

    조원익 : 개념화, 방법론, 소프트웨어, 검증, 형식 분석, 조사, 데이터 큐 레이션, 글쓰기-원고, 글쓰기-검토 및 편집. Peer Woizeschke : 감독, 프로젝트 관리, 작문-검토 및 편집.

    경쟁 관심의 선언

    저자는이 논문에보고 된 작업에 영향을 미칠 수있는 경쟁적인 재정적 이해 관계 나 개인적 관계가 없다고 선언합니다.

    감사의 말

    이 작업은 알루미늄 합금 용접 역량 센터 (Centr-Al)에서 수행되었습니다. Deutsche Forschungsgemeinschaft (DFG, 프로젝트 번호 290705638 , “용접 풀 캐비티를 생성하여 레이저 깊은 용입 용접에서 매끄러운 이음매 표면”) 의 자금은 감사하게도 인정됩니다.

    부록 A . 사용 된 지배 방정식 및 레이저 용접 모델

    1 . 지배 방정식 (Cho 및 Woizeschke [ 30 ])

    -대량 보존 방정식,(A1)∇·V→=미디엄˙에스ρ어디, V→속도 벡터입니다. ρ밀도이고 미디엄˙에스필러 와이어를 공급하여 질량 소스의 비율입니다. 단위미디엄에스단위 부피당 질량입니다. WFS (와이어 공급 속도) 및 필러 와이어의 직경과 같은 매스 소스 및 필러 와이어 조건,디w계산 영역에서 다음과 같은 관계가 있습니다.(A2)미디엄=∫미디엄에스디V=미디엄0+씨×ρ×W에프에스×π디w24×티어디, 미디엄총 질량, 미디엄0초기 총 질량, V볼륨입니다.씨단위 변환 계수입니다. 티시간입니다.

    -운동량 보존 방정식,(A3)∂V→∂티+V→·∇V→=−1ρ∇피+ν∇2V→−케이V→+미디엄˙에스ρ(V에스→−V→)+지어디, 피압력입니다. ν동적 점도입니다. 케이뭉툭한 영역의 다공성 매체 모델에 대한 항력 계수, V에스→질량 소스에 대한 속도 벡터입니다. 지신체 힘으로 인한 신체 가속도입니다.

    -에너지 절약 방정식,(A4)∂h∂티+V→·∇h=1ρ∇·(케이∇티)+h˙에스어디, h특정 엔탈피입니다. 케이열전도율, 티온도이고 h˙에스특정 엔탈피 소스로, Eq 의 질량 소스와 연관됩니다 (A1) . 계산 영역의 총 에너지,이자형다음과 같이 계산됩니다.(A5)이자형=∫미디엄에스h에스디V=∫미디엄에스씨Vw티w디V어디, 씨Vw질량 원의 비열, 티w질량 소스의 온도입니다.

    또한, 엔탈피 기반 연속체 모델을 사용하여 고체-액체 상 전이를 고려했습니다.

    -VOF 방정식,(A6)∂에프∂티+∇·(V→에프)=에프˙에스어디, 에프유체가 차지하는 부피 분율이며 0과 1 사이의 값을 가지며 에프˙에스질량의 소스와 연결된 유체의 체적 분율의 비율 식. (A1) . 질량 공급원에 해당하는 부피 분율은 다음에 할당됩니다.에프에스.

    -스칼라 보존 방정식,(A7)∂Φ∂티+∇·(V→Φ)=Φ˙에스어디, Φ필러 와이어의 스칼라 값입니다. 셀의 유체가 전적으로 필러 와이어로 구성된 경우Φ1이고 유체에 대한 필러 와이어의 부피 분율에 따라 0과 1 사이에서 변경됩니다. Φ˙에스Eq 에서 질량 소스에 연결된 스칼라 소스의 비율입니다 (A1) . 스칼라 소스는 전적으로 필러 와이어이기 때문에 1에 할당됩니다. 확산 효과는 고려되지 않았습니다.

    2 . 레이저 용접 모델 (Cho et al. [26] )

    흡수율을 계산하기 위해 프레 넬 반사 모델을 사용했습니다. ㅏ=1−ρ씨재료의 표면 상에 도시 된 바와 같이 수학 식. (A8) 원 편광 빔의 경우.(A8)ㅏ=1−ρ씨=1−12(ρ에스+ρ피)어디,ρ에스=(엔1씨영형에스θ−피)2+큐2(엔1씨영형에스θ+피)2+큐2,ρ에스=(피−엔1에스나는엔θ티ㅏ엔θ)2+큐2(피+엔1에스나는엔θ티ㅏ엔θ)2+큐2,피2=12{[엔22−케이22−(엔1에스나는엔θ)2]2+2엔22케이22+[엔22−케이22−(엔1에스나는엔θ)2]},큐2=12{[엔22−케이22−(엔1에스나는엔θ)2]2+2엔22케이22−[엔22−케이22−(엔1에스나는엔θ)2]}.어디, 복잡한 인덱스 엔1과 케이1반사 지수와 공기의 흡수 지수이며 엔2과 케이2공작물을위한 것입니다. θ입사각입니다. 도시 된 바와 같이 수학 식. (A9)에서 , 혼합물의 흡수율은 식에서 얻은 모재 및 필러 와이어 분획의 가중 평균이됩니다 . (A7) .(A9)ㅏ미디엄나는엑스티유아르 자형이자형=Φㅏw나는아르 자형이자형+(1−Φ)ㅏ비ㅏ에스이자형어디, ㅏ비ㅏ에스이자형과 ㅏw나는아르 자형이자형각각 비금속과 필러 와이어의 흡수율입니다.

    자유 표면 경계에서의 반동 압력 에이 싱은 Eq. (A10) .(A10)피아르 자형(티)≅0.54피에스ㅏ티(티)=0.54피0이자형엑스피(엘V티−티비아르 자형¯티티비)어디, 피에스ㅏ티포화 압력, 피0대기압입니다. 엘V기화의 잠열, 티비끓는 온도이고 아르 자형¯보편적 인 기체 상수입니다.

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    Fig. 2: Scheme of the LED photo-crosslinking and 3D-printing section of the microfluidic/3D-printing device. The droplet train is transferred from the chip microchannel into a microtubing in a straight section with nearly identical inner channel and inner microtubing diameter. Further downstream, the microtubing passes an LED-section for fast photo cross-linking to generate the microgels. This section is contained in an aluminum encasing to avoid premature crosslinking of polymer precursor in upstream channel sections by stray light. Subsequently, the microtubing is integrated into a 3D-printhead, where the microgels are jammed into a filament that is directly 3D-printed into the scaffold.

    On-chip fabrication and in-flow 3D-printing of cellladen microgel constructs: From chip to scaffold materials in one integral process

    cellladen 마이크로 겔 구조의 온칩 제작 및 인플 로우 3D 프린팅 : 하나의 통합 프로세스에서 칩에서 스캐폴드 재료까지

    Benjamin Reineke 1,2, Ilona Paulus 3, Jonas Hazur 6, Madita Vollmer 4, Gültekin Tamgüney 4,5, Stephan Hauschild1
    , Aldo R. Boccacini 6, Jürgen Groll 3, Stephan Förster *1,2
    1 Jülich Centre for Neutron Science (JCNS-1/IBI-8), Forschungszentrum Jülich GmbH, 52425 Jülich, Germany
    2 Institute of Physical Chemistry, RWTH Aachen University, 52074 Aachen, Germany
    3 Department of Functional Materials in Medicine and Dentistry (FMZ) and Bavarian Polymer Institute (BPI),
    University of Würzburg, 97070 Würzburg, Germany
    4 Forschungszentrum Jülich GmbH, Institute of Biological Information Processing – Structural Biochemistry (IBI7), Jülich, Germany
    5 Heinrich-Heine-Universität Düsseldorf, Institut für Physikalische Biologie, Düsseldorf, Germany
    6 Institute of Biomaterials, University of Erlangen-Nuremberg, Cauerstr. 6, 91058, Erlangen, Germany

    Summary

    Bioprinting has evolved into a thriving technology for the fabrication of cell-laden scaffolds. Bioinks are the most critical component for bioprinting. Recently, microgels have been introduced as a very promising bioink enabling cell protection and the control of the cellular microenvironment. However, their microfluidic fabrication inherently seemed to be a limitation. Here we introduce a direct coupling of microfluidics and 3D-printing for the microfluidic production of cell-laden microgels with direct in-flow bioprinting into stable scaffolds. The methodology enables the continuous on-chip encapsulation of cells into monodisperse microdroplets with subsequent in-flow cross-linking to produce cell-laden microgels, which after exiting a microtubing are automatically jammed into thin continuous microgel filaments. The integration into a 3D printhead allows direct in-flow printing of the filaments into free-standing three-dimensional scaffolds. The method is demonstrated for different cross-linking methods and cell lines. With this advancement, microfluidics is no longer a bottleneck for biofabrication.

    Bioprinting은 세포가있는 스캐 폴드 제작을 위한 번성하는 기술로 진화했습니다. 바이오 잉크는 바이오 프린팅에 가장 중요한 구성 요소입니다. 최근 마이크로 젤은 세포 보호 및 세포 미세 환경 제어를 가능하게 하는 매우 유망한 바이오 잉크로 도입되었습니다.

    그러나 이들의 미세 유체 제작은 본질적으로 한계로 보였습니다. 여기에서 우리는 안정적인 스캐 폴드에 직접 유입 바이오 프린팅을 사용하여 세포가 실린 마이크로 겔의 미세 유체 생산을 위한 미세 유체 및 3D 프린팅의 직접 결합을 소개합니다.

    이 방법론은 세포를 단 분산 미세 방울로 연속 온칩 캡슐화하고 후속 유입 교차 연결을 통해 세포가 가득한 마이크로 겔을 생성 할 수 있으며, 이는 마이크로 튜브를 종료 한 후 얇은 연속 마이크로 겔 필라멘트에 자동으로 걸린다. 3D 프린트 헤드에 통합되어 필라멘트를 독립형 3 차원 스캐 폴드로 직접 유입 인쇄 할 수 있습니다.

    이 방법은 다양한 가교 방법 및 세포주에 대해 설명됩니다. 이러한 발전으로 미세 유체 학은 더 이상 바이오 패브리 케이션의 병목 현상이 아닙니다.

    Bioprinting은 신체 조직을 모방하거나 대체하기위한 3 차원 세포 실장 구조를 제작하는 새로운 기술입니다.

    (1) 조직 공학 및 약물 전달뿐만 아니라 질병 연구 및 치료 개발에 중요한 역할을합니다. 바이오 프린팅에서 세포와 물질은 바이오 잉크 (2,3)로 공식화되어 계층 적으로 구조화 된 3D 스캐 폴드로 직접 인쇄됩니다. 바이오 프린팅의 궁극적 인 목표는 3 차원 적으로 제작 된 구조적 배열이 생물학적 성숙을 촉진하고 가속화한다는 근거를 바탕으로 표적 조직 또는 기관의 전체 또는 부분 기능을 나타내는 세포가있는 스캐 폴드를 생산하는 것입니다.

    (4) 따라서 바이오 잉크는 바이오 프린팅 기술의 중요한 구성 요소입니다. 그들은 주로 세포와 생물 활성 분자를 캡슐화 할 수있는 물질, 즉 하이드로 겔에 의존하며 압출 인쇄와 같은 적합한 인쇄 기술에 사용하여 원하는 3 차원 스캐 폴드 또는 구조물을 제작할 수 있습니다. 바이오 잉크의 설계는 유동성 및 탄성 특성을 미세 조정하여 압출 중에 충분히 전단 얇게 만들고,이어서 응고 후 원하는 기계적 안정성과 탄성을 빠르게 개발하여 안정적인 스캐 폴드를 형성해야하기 때문에 까다롭습니다.

    또한, 바이오 잉크는 생체 적합성이어야하며 세포 생존력과 적절한 제조 후 행동을 촉진 할 수있을만큼 충분히 생체 기능적이어야하며 충분한 영양분과 산소를 ​​공급할 수 있어야합니다. 바이오 잉크로 가장 두드러진 하이드로 겔 전구체 용액이 사용되며, 때로는 약간 사전 가교된 형태로 사용되며, 프린팅 후 가교되어 구조를 안정화합니다.

    종종 발생하는 문제는 세포 침강, 불균일 혼합 및 생체 적합성 제형과 인쇄 사이의 상충 관계이며, 세포가 유동 제형에서 전단력을 직접 경험하기 때문에 결과적인 모양 충실도입니다. 이러한 한계를 극복하기 위해 Highley et al.

    (5) 최근 microgel bioinks의 사용을 제안했습니다. 콜로이드 특성으로 인해 마이크로 겔 바이오 잉크는 전단 얇아지고 정지 상태에서 빠르게 응고되는 반면 부드러운 콜로이드에로드 된 세포는 전단 보호됩니다. 인쇄 된 마이크로 겔 스캐 폴드는 계면 중합체 얽힘이 충분하지 않은 경우 2 차 가교에 의해 추가로 안정화 될 수 있습니다.

    Microgels는 세포 미세 환경을 조정하는 이점을 더 제공합니다. 따라서, 세포가 가득 찬 마이크로 겔을 제조하는 방법은 이미 개발되었으며, 특히 매우 균일 한 크기의 마이크로 겔을 연속 공정으로 제작할 수있는 마이크로 유체 학 분야에서 이미 개발되었습니다. (6-8) 마이크로 겔은 EDTA- 복합체 (11,12) 또는 열 유도에 의해 조절 될 수있는 알기 네이트 / Ca2 + 이온 복합체 형성 (9,10)과 같은 물리적 가교에 의해 형성 될 수 있음이 입증되었습니다. 젤라틴 용액을 20 ° C 이하로 냉각하는 것과 같은 겔화. (9,13) 화학적 가교 반응은 마이크로 겔의 더 큰 안정성과 더 나은 기계적 특성을 제공합니다.

    예를 들면 기능화 된 젤라틴, 히알루 노 레이트, 폴리에틸렌 글리콜 또는 폴리 글리세롤 (12, 14-16)에 대한 마이클 유형 반응, 폴리 글리세롤 (17) 및 광 가교 (18)에 대한 아 지드-알킨 클릭 반응은 다음과 같은 광개시제 및 가교기를 필요로 합니다. 폴리에틸렌 글리콜에 대해 나타났습니다.

    캡슐화된 세포에는 줄기 세포 (9,12,14,15), 크립트 및 페 이어 세포 (10), 간 세포 (HepG2) 및 내피 세포 (HUVEC) (18), NIH 3T3 섬유 아세포 (6)가 포함됩니다. 지금까지 Fan et al.에 의해 세포가 실린 마이크로 겔을 기반으로하는 기능성 스캐 폴드의 제작이 보여졌습니다.

    (19) 겔 -MA 마이크로 겔의 에멀젼 기반 제조 및 Compaan et al. (20) 젤라틴 마이크로 겔 충전제 입자. 미세 유체 생성 마이크로 겔의 경우 이것은 최근 Highley et al.에 의해 처음으로 입증되었습니다. (5). 마이크로 겔 기반 바이오 잉크 및 스캐 폴드에 대한 바이오 프린팅에 대한 지금까지 제한된 수의 연구에 대한 이유는 소량의 마이크로 겔을 생성하는 마이크로 유체의 필수 조합과 교차 결합, 준비를 포함하는 여러 포스트 칩 배치 공정 단계가 뒤 따르기 때문입니다. bioink의, 그리고 원하는 스캐 폴드에 후속 bioprinting.

    이것은 현재 microgel biofabrication을 시간 소모적이고 생산성이 낮은 다단계 공정으로 만듭니다. 따라서 원하는 스캐 폴드의 제조를위한 마이크로 겔 및 바이오 프린팅을위한 미세 유체가 하나의 연속적이고 자동화 가능한 프로세스에 통합 될 수 있다면 매우 바람직 할 것입니다.

    여기에서 우리는 미세 유체 칩이 세포를 방울로 온칩 캡슐화하도록 설계 될 수 있음을 보여줍니다. 이는 마이크로 겔을 생성하기 위해 흐름에서 광 가교 결합 된 다음 다운 스트림 마이크로 튜브에서 자동으로 잼되어 얇은 마이크로 겔 필라멘트를 지속적으로 형성합니다. 마이크로 튜브는 3D 프린터의 프린트 헤드에 통합되어 필라멘트를 독립형 3 차원으로 직접 유입 인쇄합니다.

    Results and discussion

    Microfluidic device and controlled droplet production

    우리의 목표는 (i) 낮은 전단 응력 세포 캡슐화, (ii) 물리적 또는 화학적 가교에 대한 가변성, (iii) 미세 액적 직경의 큰 변화, (iv)이를 결합 할 수 있는 기능을 위한 미세 유체 칩을 3D 프린터로 설계하는 것이었습니다.

    따라서 디자인은 높은 세포 생존력을 위해 좁은 채널 섹션 내의 세포에 대한 전단력을 최소화해야 합니다. 다양한 물리적 및 화학적 가교 반응을 수행 할 수 있도록 입구 채널 설계는 세포, 폴리머, 가교 및 추가 제제를 포함하는 용액의 순차적 혼합을 허용해야 합니다. 단일 세포 캡슐화가 필요한 경우 미세 방울은 300 µm에서 50 µm까지 제어 가능한 직경을 가져야 106 / ml의 세포 밀도에 도달 할 수 있습니다.

    Fig. 1: Three-dimensional schematic view of the multilayer double 3D-focusing microfluidic channel system, (b) control of droplet diameter via the Capiilary number Ca, and accessible hydrodynamic regimes for droplet production: squeezing (c), dripping (d) and jetting (e). The scale bars are 200 µm.
    Fig. 1: Three-dimensional schematic view of the multilayer double 3D-focusing microfluidic channel system, (b) control of droplet diameter via the Capiilary number Ca, and accessible hydrodynamic regimes for droplet production: squeezing (c), dripping (d) and jetting (e). The scale bars are 200 µm.

    따라서 우리는 두 개의 후속 혼합 교차로 3 차원 흐름 초점을 허용 한 다음 제어 된 액적 형성을위한 하류 좁은 오리피스가 뒤 따르는 채널 설계를 사용했습니다. 디자인은 그림 1에 개략적으로 표시되어 있습니다. 여기에는 세포와 전구체 폴리머를 포함하는 중앙 스트림 용액을위한 입구 채널과 완충 용액, 배양 배지, 생리 활성 물질 또는 가교제를 포함 할 수있는 두 개의 측면 채널이 있습니다. 측면 채널 흐름은 입구 채널 흐름을 세포에 대한 전단력이 최소 인 채널의 중앙에 3 차원 적으로 집중시킵니다. 그 후, 수성 스트림은 액적 형성을 제어하는 ​​좁은 오리피스 섹션으로 들어가기 위해 오일 상으로 3 차원 적으로 집중됩니다. 좁은 섹션은 다양한 유체 역학 체제에 액세스하여 다양한 범위에 걸쳐 액적 크기를 변경할 수 있습니다. 다운 스트림 채널은 방울이 채널 중심 유선에서 안정적인 방울 트레인을 형성하도록 충분히 좁게 유지됩니다. 3D 이중 초점 칩은 다층 기술을 사용하는 소프트 리소그래피로 제작되었으며 지원 정보 (그림 S2-S4, S7)에 설명 된대로 흐름이 시뮬레이션되었습니다. 액적 분해는 외부 유체에 의해 가해지는 점성 전단력 𝐹𝑠ℎ𝑒ar 표면 장력에서 발생하는 고정 계면 력 𝐹𝐹𝛾𝛾을 초과 할 때 발생합니다. 두 힘은 직접 연속 유상 η 평균 유입 흐름 속도 (V)의 점도 환산 수 무차 모세관 수가 CA = 𝐹𝑠ℎ𝑒ar/𝐹γ, 그리고 CA = 𝐹𝑠ℎ𝑒ar/𝐹γ = 같은 표면 장력 γ가 관련 𝜂𝜂 𝛾. 캐 필러 리 수에 따라 액적 생성을위한 다양한 유체 역학 체제를 구별 할 수 있습니다. c) 분사 체제 (Ca> 1). (21-25) 그림 1에서 볼 수 있듯이 가변 3D 수축 설계를 사용하면 액적 생산을위한 세 가지 유체 역학 체제에 모두 액세스 할 수 있으며 모세관 수는 액적 생산을위한 주요 제어 매개 변수입니다. 체적 유량, 오일 점도 및 계면 장력을 조정하여 50 ~ 300 µm 범위의 목표 범위에서 액적 직경을 정밀하게 제어 할 수 있습니다. 각 점도 및 계면 장력은 지원 정보의 표 SI에 요약되어 있습니다.

    Fig. 2: Scheme of the LED photo-crosslinking and 3D-printing section of the microfluidic/3D-printing device. The droplet train is transferred from the chip microchannel into a microtubing in a straight section with nearly identical inner channel and inner microtubing diameter. Further downstream, the microtubing passes an LED-section for fast photo cross-linking to generate the microgels. This section is contained in an aluminum encasing to avoid premature crosslinking of polymer precursor in upstream channel sections by stray light. Subsequently, the microtubing is integrated into a 3D-printhead, where the microgels are jammed into a filament that is directly 3D-printed into the scaffold.
    Fig. 2: Scheme of the LED photo-crosslinking and 3D-printing section of the microfluidic/3D-printing device. The droplet train is transferred from the chip microchannel into a microtubing in a straight section with nearly identical inner channel and inner microtubing diameter. Further downstream, the microtubing passes an LED-section for fast photo cross-linking to generate the microgels. This section is contained in an aluminum encasing to avoid premature crosslinking of polymer precursor in upstream channel sections by stray light. Subsequently, the microtubing is integrated into a 3D-printhead, where the microgels are jammed into a filament that is directly 3D-printed into the scaffold.
    Fig. 3: a) Photograph of a standard meander-shaped layer fabricated by microgel filament deposition printing. The lines have a thickness of 300 µm. b) photograph of a cross-bar pattern obtained by on-top deposition of several microgel filaments. The average linewidth is 1 mm. c) photograph of a donut-shaped microgel construct. The microgels have been fluorescently labelled by FITC-dextran to demonstrate the intrinsic microporosity corresponding to the black non-fluorescent regions, d) light microscopy image of a construct edge showing that fused adhesive microgels form a continuous, three-dimensional selfsupporting scaffold with intrinsic micropores.
    Fig. 3: a) Photograph of a standard meander-shaped layer fabricated by microgel filament deposition printing. The lines have a thickness of 300 µm. b) photograph of a cross-bar pattern obtained by on-top deposition of several microgel filaments. The average linewidth is 1 mm. c) photograph of a donut-shaped microgel construct. The microgels have been fluorescently labelled by FITC-dextran to demonstrate the intrinsic microporosity corresponding to the black non-fluorescent regions, d) light microscopy image of a construct edge showing that fused adhesive microgels form a continuous, three-dimensional selfsupporting scaffold with intrinsic micropores.
    Fig. 4: a) Scheme of the perfusion chamber consisting of an upstream and downstream chamber, perfusion ports, and removable scaffolds to stabilize the microgel construct during 3D-printing, b) photograph of a microgel construct in the perfusion chamber directly after printing and removal of the scaffolds, c) confocal microscopy image of the permeation front of a fluorescent dye, where the high dye concentration in the micropores can be clearly seen, d) confocal microscopy image of YFP-labelled HEK-cells within a microgel construct.
    Fig. 4: a) Scheme of the perfusion chamber consisting of an upstream and downstream chamber, perfusion ports, and removable scaffolds to stabilize the microgel construct during 3D-printing, b) photograph of a microgel construct in the perfusion chamber directly after printing and removal of the scaffolds, c) confocal microscopy image of the permeation front of a fluorescent dye, where the high dye concentration in the micropores can be clearly seen, d) confocal microscopy image of YFP-labelled HEK-cells within a microgel construct.
    Fig. 5: a) Layer-by-layer printing of microgel construct with integrated perfusion channel. After printing of the first layer, a hollow perfusion channel is inserted. Subsequently, the second and third layers are printed. b) The construct is directly printed into a perfusion chamber. The perfusion chamber provides whole construct permeation via flows cin and cout, as well as independent flow through the perfusion channel via flows vin and vout. c) Photograph of a perfusion chamber containing the construct directly after printing. The flow of the fluorescein solution through the integrated PVA hollow channel is clearly visible.
    Fig. 5: a) Layer-by-layer printing of microgel construct with integrated perfusion channel. After printing of the first layer, a hollow perfusion channel is inserted. Subsequently, the second and third layers are printed. b) The construct is directly printed into a perfusion chamber. The perfusion chamber provides whole construct permeation via flows cin and cout, as well as independent flow through the perfusion channel via flows vin and vout. c) Photograph of a perfusion chamber containing the construct directly after printing. The flow of the fluorescein solution through the integrated PVA hollow channel is clearly visible.
    Fig. 6: a) Photograph of an alginate capsule fiber formed after exiting the microtube. b) Confocal fluorescence microscopy image of part of a 3D-printed alginate capsule construct. The fluorescence arises from encapsulated fluorescently labelled polystyrene microbeads to demonstrate the integrity and stability of the alginate capsules.
    Fig. 6: a) Photograph of an alginate capsule fiber formed after exiting the microtube. b) Confocal fluorescence microscopy image of part of a 3D-printed alginate capsule construct. The fluorescence arises from encapsulated fluorescently labelled polystyrene microbeads to demonstrate the integrity and stability of the alginate capsules.

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    Fig. 1 Fixed staff gauge for head measurement at the upstream side of the Yuanshanzi Flood Diversion Work in the Keelung River, Taiwan

    Velocity distribution and discharge calculation at a sharp-crested weir

    Shun-Chung Tsung • Jihn-Sung Lai •
    Der-Liang Young

    sharp-crested weir에서 속도 분포 및 배출 계산

    개방 수로의 harp-crested 위어는 수두-방류 관계를 통해 방류를 계산하는데 유용한 장치입니다. 그러나 수위 측정 사이트와 배출 계수는 배출 계산 정확도에 큰 영향을 미칩니다. 따라서 본 연구는 각각 16MHz MicroADV와 FLOW-3D를 사용하여 위어 부분의 속도 분포를 측정하고 시뮬레이션합니다. 감마 확률 밀도 함수를 사용하여 속도 분포를 특성화하기 위해 위어 섹션의 수심 및 표면 속도가 선택됩니다. 본 연구에서는 측정된 수심과 수면 속도에서 도출된 속도 분포를 기반으로 속도-면적 통합 방법으로 정확한 배출을 계산합니다. 이 연구의 주요 기여는 정확한 측정 사이트를 제공하고, 속도 분포와 방류를 연결하고, 방류 계수 영향을 피하고, 방류 계산 정확도를 향상시키는 것입니다.

    A sharp-crested weir in open channel is a useful device to calculate discharge via head-discharge relationship. However, water stage measurement site and discharge coefficient significantly influence discharge calculation accuracy. Therefore, this study measures and simulates velocity distribution at the weir section using 16-MHz MicroADV and FLOW-3D, respectively. The water depth and surface velocity at the weir section are selected to characterize velocity distribution using gamma probability density function. In this study, accurate discharge is calculated by velocity–area integration method based on velocity distribution derived from measured water depth and surface velocity. The main contributions of this study are to give an exact measurement site, link velocity distribution and discharge, avoid discharge coefficient influence, and improve discharge calculation accuracy.

    Fig. 1 Fixed staff gauge for head measurement at the upstream side of the Yuanshanzi Flood Diversion Work in the Keelung River, Taiwan
    Fig. 1 Fixed staff gauge for head measurement at the upstream side of the Yuanshanzi Flood Diversion Work in the Keelung River, Taiwan

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    Figure 7. Formation of incident and reflected waves.

    Investigate Impact Force of Dam-Break Flow against Structures by Both 2D and 3D Numerical Simulations

    2D 및 3D 수치 시뮬레이션에 의한 댐 붕괴유동의 구조물 충격력 조사

    1 Faculty of Water Resources Engineering, Thuyloi University, 175 Tay Son, Dong Da, Ha Noi 116705, Vietnam
    2 Hydraulic Construction Institute, 3/95 Chua Boc, Dong Da, Ha Noi 116705, Vietnam
    * Author to whom correspondence should be addressed.
    Academic Editor: Costanza Aricò
    Water 2021, 13(3), 344;

    Abstract

    본 논문의 목적은 일부 2D 및 3D 수치 모델이 침수 지역에 고립된 건물 또는 건물 배열이 있는 곳에서 홍수 파동을 시뮬레이션하는 능력을 조사하는 것이었습니다.

    먼저, 제안된 2D 수치 모델은 구조화된 메시에서 2D 얕은 물 방정식(2D-SWEs)을 해결하기 위한 유한 볼륨 방법(FVM)을 기반으로 했습니다.

    FDS (flux-difference splitting)은 정확한 질량 균형을 얻기 위해 사용되었고 Roe 체계는 Riemann 문제를 근사하기 위해 호출되었습니다.

    둘째, 상업적으로 이용 가능한 3D CFD 소프트웨어 패키지가 선택되었으며, 여기에는 두 가지 난류 모델이 포함된 Flow 3D 모델이 포함되어 있습니다.

    RNG(Renormalized Group) 및 LES(Large-eddy Simulation)를 사용하는 레이놀즈 평균 Navier-Stokes(RAN)입니다. 댐 붕괴 흐름으로 인한 장애물에 대한 충격력의 수치 결과는 3D 솔루션이 2D 솔루션보다 훨씬 낫다는 것을 보여주었습니다.

    건물 배열에 작용하는 충격력의 3D 수치 힘 결과를 보유하고 있는 실험 데이터와 비교함으로써, 속도 유도력이 동적 힘에 미치는 영향은 Froude 숫자의 함수와 사고 파동의 수심 함수에 의해 정량화 되었습니다. 또한, 우리는 힘의 강도의 피크 값의 3D 계산 결과에 대한 초기 물 단계와 댐 붕괴 폭의 영향을 조사했습니다.

    The aim of this paper was to investigate the ability of some 2D and 3D numerical models to simulate flood waves in the presence of an isolated building or building array in an inundated area. Firstly, the proposed 2D numerical model was based on the finite-volume method (FVM) to solve 2D shallow-water equations (2D-SWEs) on structured mesh. The flux-difference splitting method (FDS) was utilized to obtain an exact mass balance while the Roe scheme was invoked to approximate Riemann problems. Secondly, the 3D commercially available CFD software package was selected, which contained a Flow 3D model with two turbulent models: Reynolds-averaged Navier-Stokes (RANs) with a renormalized group (RNG) and a large-eddy simulation (LES). The numerical results of an impact force on an obstruction due to a dam-break flow showed that a 3D solution was much better than a 2D one. By comparing the 3D numerical force results of an impact force acting on building arrays with the existence experimental data, the influence of velocity-induced force on a dynamic force was quantified by a function of the Froude number and the water depth of the incident wave. Furthermore, we investigated the effect of the initial water stage and dam-break width on the 3D-computed results of the peak value of force intensity.

    Keywords: dam-break wave2D numerical modelFlow 3D modelstructuresimpact force

    Introduction

    홍수 위험 분석에 따른 도시 계획은 최근에 큰 연구 과제였습니다.

    건물 또는 건물 그룹에 대한 홍수 파동의 영향에 대한 연구는 하류 지역에 대한 조기 경고 또는 안전 의식 향상에 중요한 역할을 했습니다. 기본적으로 댐 파괴 흐름에 대한 연구는 실험 측정이나 수치 시뮬레이션을 통해 추정 할 수 있습니다 [1,2,3,4,5,6].

    컴퓨터 처리 능력의 증가로 인해 불연속 흐름에 대한 수치 연구가 비용 효율적이되었습니다. 지난 10 년 동안 얕은 물 솔버는 정확성과 계산 능력면에서 크게 향상되었습니다. 침수 가능 지역의 수심 및 속도 프로파일과 같은 유체 역학적 매개 변수에 많은주의를 기울였습니다 [1,2,3,4,5,6,7,8].

    Migot et al. [9]는 도시 홍수의 실험적 모델링에 관한 많은 기사를 검토했습니다. 그 논문에 언급 된 45 개의 작품 중 단 4 개의 프로젝트 만이 장애물에 가해지는 일정한 또는 비정상적인 흐름의 힘 또는 압력을 측정했습니다.

    또한 물리적 및 2D 수치 모델에서 건물 또는 건물 그룹에 돌발 홍수가 미치는 영향에 대한 연구는 거의 없었습니다. 얕은 물 모델은 [10,11]에서 고립된 장애물에 대한 충격의 힘을 예측하는데 사용되었습니다.

    한편 Shige-eda [12]는 액체와 건물 배열 간의 상호 작용을 결정하기 위해 물리적 모델과 2D 수치 체계를 선택했습니다. Aureli와 Shige-eda는 수직 속도와 가속도를 무시하기 때문에 댐 파괴 흐름의 힘을 추정하기 위한 2D 얕은 물 방정식 (SWE)의 단점을 보여주었습니다 [10,12].

    Migot [9]은 또한 장애물 주변의 시뮬레이션된 홍수 흐름에 대한 2D SWE에 대한 여러 출판물이 있었지만 이 주제에 대한 3D 수치 모델에 대한 연구는 거의 없다고 지적했습니다. 최근 전산 유체 역학 (CFD) 3D 시뮬레이션은 유체 흐름과 관련된 문제를 해결하기위한 광범위한 도구가되었습니다.

    댐 파괴 파의 특성은 [13,14,15,16]에 의해 주목되었고 Issakhov [17]는 다양한 종류의 장애물이 압력 분포에 미치는 영향을 조사하기 위해 CFD 방법을 사용했습니다. 그들은 분포가 댐 표면에서 3 배 더 낮다는 것을 밝혔다.

    Aureli [10]는 댐 파괴 파가 구조물에 미치는 영향의 정적 힘을 평가하기 위해 실험 테스트와 2D 및 3D 수치 모델을 사용했습니다. Mokarani [18]는 댐 브레이크 흐름 영향의 VOF 시뮬레이션에서 피크 압력 안정성 조건을 연구했습니다.

    앞서 언급한 작품에서 구조물이나 구조물 군에 작용하는 힘은 압력에 의한 정 수력 또는 정력이었다. 한편, 급류에서 속도로 인한 힘은 압력 력보다 크거나 같았습니다 [19]. Armanini [20]는 정상 흐름에 대해이 항을 추정하기 위한 분석적 표현 만을 제시했습니다. 우리가 아는 한, 건물 그룹에 작용하는 비정상 흐름의 동적 힘을 생성하기 위해 2D 및 3D 수학적 모델을 모두 사용하는 작업은 없습니다.

    따라서 본 연구에서는 제안된 2D 수치 모델과 3D 수학적 모델 모두에 의해 고립 된 장애물 또는 장애물 그룹에 대한 급격한 비정상 흐름의 테스트 사례를 재현했습니다. 수심 및 유속 수문 그래프와 같은 몇 가지 수력 학적 특성이 추정되었으며 측정 된 데이터와 매우 잘 일치했습니다.

    특히 댐 브레이크 흐름이 서로 다른 건물에 가하는 동적인 힘도 시뮬레이션했습니다. 속도 유도 힘이 동적 힘에 미치는 영향 수준을 나타내는 매개 변수는 Froude 수와 입사 파동의 수심의 함수인 것으로 밝혀졌습니다. 또한 붕괴된 댐 사이트 폭 (b)과 초기 수위 (h0)는 충격력의 최대 값에 영향을 미치는 변수로 고려되었습니다.

    Figure 1. (a) Configuration of experiment test (dimension in meters); (b) Gauges on the vertical front face of building.
    Figure 1. (a) Configuration of experiment test (dimension in meters); (b) Gauges on the vertical front face of building.
    Figure 2. (a) Distributed pressure profiles at centerline of front face of column; (b) Comparison of load-time histories simulated by different numerical models
    Figure 2. (a) Distributed pressure profiles at centerline of front face of column; (b) Comparison of load-time histories simulated by different numerical models
    Figure 3. Group of buildings in flooded area.
    Figure 3. Group of buildings in flooded area.
    Figure 4. Water depth and u-velocity profiles at gauge b.
    Figure 4. Water depth and u-velocity profiles at gauge b.
    Figure 5. Water hydrographs at gauges a and c.
    Figure 5. Water hydrographs at gauges a and c.
    Figure 6. Velocity component profiles at gauges a and c.
    Figure 6. Velocity component profiles at gauges a and c.
    Figure 7. Formation of incident and reflected waves.
    Figure 7. Formation of incident and reflected waves.
    Figure 8. Snapshots of streamlines of Froude number at different times: 1.0 s, 2.0 s, 5.0 s and 10 s.
    Figure 8. Snapshots of streamlines of Froude number at different times: 1.0 s, 2.0 s, 5.0 s and 10 s.
    Figure 9. Force in the flow direction exerted on 6 buildings.
    Figure 9. Force in the flow direction exerted on 6 buildings.
    Figure 10. The linear regression between forces per unit width (F) and q2b/h0.
    Figure 10. The linear regression between forces per unit width (F) and q2b/h0.

    Conclusions

    댐 붕괴 흐름으로 인한 홍수 파도는 높은 속도 또는 큰 깊이가 관련되었을 때 건물에 큰 영향을 미칩니다. 본 논문에서는 2D 및 3D 수치 모델의 건물 및 건물 그룹에 대한 빠른 흐름에 의해 발생하는 유압 특성과 충격 부하를 추정할 수 있는 능력을 조사했습니다. 얕은 물 방정식에 기초한 2D 수학 모델은 FDS 방법으로 해결되었으며, FDS 방법은 최신 버전의 Flow 3D 유체 역학 모델과 함께 사용되었습니다. 연구의 주요 발견은 다음과 같습니다.
    (1) 수심 또는 속도 프로파일을 공식화하기 위해 2D 및 3D 수치 솔루션은 모두 매우 유사합니다. 제안된 2D 수치 모델은 정적 힘의 최대 값 뿐만 아니라 수심 및 속도 구성 요소를 포함하는 유압 특성을 예측하는 데 적합합니다. 그러나 LES 및 RAN 난류 모듈이 포함된 3D 유체역학 모델은 2D 얕은 흐름 모델이 1개만 제공하는 동안 두 개의 최고 충격 부하를 잘 포착할 수 있습니다. 일반적으로 3D 결과는 실험 결과와 더 가깝습니다.
    (2) 여러 건물에 대한 정적 및 동적 힘은 모두 LES 모듈을 사용하여 Flow 3D에 의해 계산되었습니다. 건물에서 속도에 의한 힘과 압력의 역할은 위치에 따라 다릅니다. 댐 현장 근처에서, 속도 유도 힘은 댐 파괴 파동의 주 방향에서 멀리 떨어져 있거나 두 번째 배열에서 압력 힘이 더 중요합니다. 속도 유도 힘의 영향은 매개 변수 α에 의해 정량화되며, 이는 사고파의 Froude 숫자와 수심 함수로 수행됩니다. q2b/h0과 정적 힘과 동적 힘의 피크 강도 사이의 선형 회귀 관계는 합리적인 R-제곱 양으로 해결됩니다.

    추가 연구에서, 제시된 2D 수치 모델의 견고성과 효과는 더 명확하게 드러날 것입니다. 대규모 도메인에 대한 홍수 흐름을 시뮬레이션하는 데 쉽게 적용할 수 있습니다. 또한, α 매개변수의 제안된 방정식(21)은 실제 사례 연구에서 다운스트림 영역의 건물에 대한 속도 유도 힘의 영향을 정확하게 평가하기 위한 매우 의미가 있습니다. 이 매개 변수의 정확도 수준을 높이려면 서로 다른 조건에서 장애물에 작용하는 여러 가지 힘 실험이 구현되어야 합니다.

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    Fig. 9 (a) Velocity field, keyhole profile, and breakage of the keyhole to form bubble and (b) 2D temperature and velocity field along the longitudinal section

    A Numerical Study on the Keyhole Formation During Laser Powder Bed Fusion Process

    Keyhole에 대한 수치적 연구 : 레이저 분말 중 형성 베드 퓨전 공정

    Subin Shrestha1
    J.B. Speed School of Engineering,University of Louisville,Louisville, KY 40292
    e-mail: subin.shrestha@louisville.edu

    Y. Kevin Chou
    J.B. Speed School of Engineering,University of Louisville,Louisville, KY 40292
    e-mail: kevin.chou@louisville.edu

    LPBF (Laser Powder Bed fusion) 공정 중 용융 풀의 동적 현상은 복잡하고 공정 매개 변수에 민감합니다. 에너지 밀도 입력이 특정 임계 값을 초과하면 키홀이라고 하는 거대한 증기 함몰이 형성 될 수 있습니다.

    이 연구는 수치 분석을 통해 LPBF 과정에서 키홀 거동 및 관련 기공 형성을 이해하는 데 중점을 둡니다. 이를 위해 이산 분말 입자가 있는 열 유동 모델이 개발되었습니다.

    이산 요소 방법 (DEM)에서 얻은 분말 분포는 계산 영역에 통합되어 FLOW-3D를 사용하는 3D 프로세스 물리학 모델을 개발합니다.

    전도 모드 중 용융 풀 형성과 용융의 키홀 모드가 식별되고 설명되었습니다. 높은 에너지 밀도는 증기 기둥의 형성으로 이어지고 결과적으로 레이저 스캔 트랙 아래에 구멍이 생깁니다.

    또한 다양한 레이저 출력과 스캔 속도로 인한 Keyhole 모양을 조사합니다. 수치 결과는 동일한 에너지 밀도에서도 레이저 출력이 증가함에 따라 Keyhole크기가 증가 함을 나타냅니다. Keyhole은 더 높은 출력에서 ​​안정되어 레이저 스캔 중 Keyhole 발생을 줄일 수 있습니다.

    The dynamic phenomenon of a melt pool during the laser powder bed fusion (LPBF) process is complex and sensitive to process parameters. As the energy density input exceeds a certain threshold, a huge vapor depression may form, known as the keyhole. This study focuses on understanding the keyhole behavior and related pore formation during the LPBF process through numerical analysis. For this purpose, a thermo-fluid model with discrete powder particles is developed. The powder distribution, obtained from a discrete element method (DEM), is incorporated into the computational domain to develop a 3D process physics model using flow-3d. The melt pool formation during the conduction mode and the keyhole mode of melting has been discerned and explained. The high energy density leads to the formation of a vapor column and consequently pores under the laser scan track. Further, the keyhole shape resulted from different laser powers and scan speeds is investigated. The numerical results indicated that the keyhole size increases with the increase in the laser power even with the same energy density. The keyhole becomes stable at a higher power, which may reduce the occurrence of pores during laser scanning.

    Keywords: additive manufacturing, keyhole, laser powder bed fusion, porosity

    Fig. 1 (a) Powder added to the dispenser platform and (b) powder particles settled over build plate after the recoating process
    Fig. 1 (a) Powder added to the dispenser platform and (b) powder particles settled over build plate after the recoating process
    Fig. 2 3D computational domain used for single-track simulation
    Fig. 2 3D computational domain used for single-track simulation
    Fig. 3 Temperature-dependent material properties of Ti-6Al-4V
    Fig. 3 Temperature-dependent material properties of Ti-6Al-4V
    Fig. 4 Powder and substrate melting during laser application
    Fig. 4 Powder and substrate melting during laser application
    Fig. 5 Melt region formed after complete melting and solidification
    Fig. 5 Melt region formed after complete melting and solidification
    Fig. 6 Melt pool boundary comparison between the experiment [25] and the simulation
    Fig. 6 Melt pool boundary comparison between the experiment [25] and the simulation
    Fig. 7 Equilibrium points during the formation of vapor column [27]
    Fig. 7 Equilibrium points during the formation of vapor column [27]
    Fig. 8 Multiple reflection vectors from the keyhole wall
    Fig. 8 Multiple reflection vectors from the keyhole wall
    Fig. 9 (a) Velocity field, keyhole profile, and breakage of the keyhole to form bubble and (b) 2D temperature and velocity field along the longitudinal section
    Fig. 9 (a) Velocity field, keyhole profile, and breakage of the keyhole to form bubble and (b) 2D temperature and velocity field along the longitudinal section
    Fig. 10 Fluid flow in the transverse direction during keyhole melting
    Fig. 10 Fluid flow in the transverse direction during keyhole melting
    Fig. 11 Melt pool boundary compared with the experiment [21] for 195 W laser power and 400 mm/s scan speed
    Fig. 11 Melt pool boundary compared with the experiment [21] for 195 W laser power and 400 mm/s scan speed
    Fig. 12 Melt region formed after complete melting and solidification
    Fig. 12 Melt region formed after complete melting and solidification
    Fig. 13 2D images of the pores formed at the beginning of the single track and their 3D-rendered morphology
    Fig. 13 2D images of the pores formed at the beginning of the single track and their 3D-rendered morphology
    Fig. 14 Pore number and volume from a different level of power with LED = 0.4 J/mm [29]
    Fig. 14 Pore number and volume from a different level of power with LED = 0.4 J/mm [29]
    Fig. 15 Keyhole shape at different time steps from different parameters: (a) P = 100 W, v = 250 mm/s, (b) P = 200 W, v = 500 mm/s, (c) P = 300 W, v = 750 mm/s, and (d) P = 400 W, v = 1000 mm/s
    Fig. 15 Keyhole shape at different time steps from different parameters: (a) P = 100 W, v = 250 mm/s, (b) P = 200 W, v = 500 mm/s, (c) P = 300 W, v = 750 mm/s, and (d) P = 400 W, v = 1000 mm/s
    Fig. 16 Intensity dependence in the relationship between vapor column and evaporation pressure [27]
    Fig. 16 Intensity dependence in the relationship between vapor column and evaporation pressure [27]
    Fig. 17 Temperature distribution when laser has moved 0.8 mm with P = 300 W, v = 750 mm/s and P = 400 W, v = 1000 mm/s
    Fig. 17 Temperature distribution when laser has moved 0.8 mm with P = 300 W, v = 750 mm/s and P = 400 W, v = 1000 mm/s
    Fig. 18 Melt region with different level of power with LED of 0.4 J/mm
    Fig. 18 Melt region with different level of power with LED of 0.4 J/mm

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    Figure 1. Experimental flume used (a) Side view of the flume; (b) Pool detail.

    Modelling of Pool-Type Fishways Flows: Efficiency and Scale Effects Assessment

    by Ana L. Quaresma *OrcID andAntónio N. PinheiroOrcID
    CERIS—Civil Engineering for Research and Innovation for Sustainability, Instituto Superior Técnico (IST), Universidade de Lisboa, 1049-001 Lisboa, Portugal*
    Author to whom correspondence should be addressed.
    Academic Editor: Bommanna Krishnappan
    Water 2021, 13(6), 851; https://doi.org/10.3390/w13060851
    Received: 16 January 2021 / Revised: 8 March 2021 / Accepted: 18 March 2021 / Published: 20 March 2021
    (This article belongs to the Special Issue Ecohydraulics of Pool-Type Fishways)

    Abstract

    이 연구에서는 전산 유체 역학 (CFD) 소프트웨어 (FLOW-3D®)를 사용하여 바닥 오리피스가 있는 풀형 어로에서 흐름의 3D 수치 모델링을 수행했습니다. 수치 결과는 음향 도플러 속도계 (ADV) 및 입자 이미지 속도계 (PIV) 측정에서 얻은 실험 데이터와 비교되었습니다.

    흐름 깊이, 흐름 패턴, 수속, 난류 운동 에너지, Reynolds 수직 응력 및 바닥 구성 요소에 평행한 Reynolds 전단 응력과 같이 어로 효율에 영향을 미치는 여러 유체 역학적 변수를 정성 및 정량적으로 비교했습니다.

    수치 모델은 복잡한 유동장을 정확하게 재현하여 수치 모델 예측과 분석 된 변수에 대한 실험 데이터 사이에 전반적으로 좋은 일치를 보여줍니다. 분석중인 모든 매개 변수에 대한 수치 모델 검증 수행의 중요성이 강조되었습니다.

    또한 프로토 타입 어로의 업 스케일 된 수치 모델을 실행하여 스케일링 효과를 분석했습니다. 스케일 효과의 증거없이 실제 모델과 프로토 타입 치수 모두에 대해 유사한 정확도로 모델을 수행했습니다.

    현재 연구는 CFD 모델 (즉, FLOW-3D®)이 새로운 수영장 유형 어로 형상을 위한 적절하고 효율적인 설계 및 분석 도구로 사용될 수 있으며 물리적 모델 테스트를 줄이고 보완 할 수 있다고 결론지었습니다.

    In this study, the 3D numerical modelling of flow in a pool-type fishway with bottom orifices was performed using computational fluid dynamics (CFD) software (FLOW-3D®). Numerical results were compared with experimental data obtained from acoustic Doppler velocimetry (ADV) and particle image velocimetry (PIV) measurements. Several hydrodynamic variables that influence fishways efficiencies, such as flow depths, flow patterns, water velocity, turbulent kinetic energy, Reynolds normal stresses, and Reynolds shear stress parallel to the bottom component, were qualitatively and quantitatively compared. The numerical model accurately reproduced the complex flow field, showing an overall good agreement between the numerical model predictions and the experimental data for the analysed variables. The importance of performing a numerical model validation for all the parameters under analyses was highlighted. Additionally, scaling effects were analysed by running an upscaled numerical model of the prototype fishway. The model performed with similar accuracy for both physical model and prototype dimensions with no evidence of scale effects. The present study concludes that CFD models (namely FLOW-3D®) may be used as an adequate and efficient design and analysis tool for new pool-type fishways geometries, reducing and complementing physical model testing.Keywords: pool-type fishways3D numerical modellingLESscale effectsflow patternsCFD model assessment

    Introduction

    강의 종단 연결성을 복원하는 것은 담수 생태계의 회복에있어 여전히 중요한 문제입니다 [1,2]. 잘 설계되고 건설된 경우 어로는 물고기가 댐과 둑을 지나 계속 이동할 수 있는 경로를 제공합니다.

    물고기 통과 효율성에 대한 검토에서 Noonan et al. [3]은 기존의 많은 어로의 설계 특성이 어종의 요구를 적절하게 충족시키지 못했지만, 풀형 어로가 모든 어류 그룹에 대해 가장 높은 효율성을 보여 주었다는 것을 발견했습니다.
    여러 어종에 적합한 수영 조건을 제공하는 것은 어항의 흐름과 난류 패턴이 성공에 중요한 역할을 하기 때문에 다소 어려운 일입니다 [2,4,5,6,7,8,9,10,11,12].

    물리적 모델링은 풀형 유형 어로의 유체 역학을 연구하기 위한 주요 접근 방식이었습니다 (예 : [13,14,15,16,17,18,19,20,21,22]). 그러나 물리적 실험은 비용과 시간이 많이 소요됩니다. 따라서 컴퓨터 기술의 발전으로 인해 물리적 모델 테스트를 줄이기 위해 복잡한 기하학적 구조를 가진 유압 구조의 흐름 패턴을 분석하는 데 전산 유체 역학 (CFD) 3 차원 (3D) 모델이 점점 더 많이 사용되고 있습니다 [23,24].

    따라서 이러한 모델은 어로 유체 역학 연구 및 효율적인 어로 설계에 필수적인 역할을 할 수 있습니다.
    어로에 대한 수치 모델링 연구는 주로 수직 슬롯 어로에 초점을 맞추고 있습니다 [12,25,26,27,28,29,30,31,32,33,34,35,36,37]. 수영장의 주요 부분에서 수직 슬롯 어로 흐름은 거의 2 차원 (2D)이고 수직 속도 구성 요소가 수평 요소 [26]보다 훨씬 작기 때문에 이러한 연구의 대부분은 2D 모델을 사용했습니다.

    바닥 오리피스가있는 수영장 유형 어로에서는 흐름이 매우 복잡하고 3D이므로 정확한 유동장 특성화를 얻기 위해 3D 모델을 사용해야합니다. 이 어로 구성을 모델링하는 것은 높은 속도 구배, 높은 와도 및 높은 전단 영역을 포함하기 때문에 다소 어렵습니다.

    이 연구에서는 FLOW-3D® (Flow Science, Inc., Santa Fe, NM, USA)를 사용하여 바닥 오리피스가 있는 수영장 유형 어로의 3D 수치 시뮬레이션을 수행하여 흐름 깊이, 속도 및 난류 패턴을 예측하는 능력을 평가했습니다. .

    최근 몇 년 동안 실내에 가까운 프로토 타입 수영장 형 어로가 사이프 린드 종의 행동과 움직임을 연구하는데 사용되었습니다 [1,7,8,11,38,39,40,41,42,43]. Silva et al. [38]은 노치, 급락 및 스트리밍에 대한 두 가지 다른 유동 체제와 관련하여 조정 가능한 치수를 가진 침수된 오리피스와 표면 노치의 동시 존재에 대한 Iberian barbel Luciobarbus bocagei (Steindachner, 1864)의 반응을 평가했습니다.

    이 연구의 결과는 이베리아 바벨이 어로를 협상하기 위해 오리피스 (76 %)를 선호했으며 어로에 들어가는 데 걸리는 시간도 오리피스에 비해 훨씬 적다는 것을 보여주었습니다.

    Silva et al. [39] 오프셋 및 직선 오리피스가있는 수영장 유형 어로의 이베리아 바벨에 대한 적합성을 테스트했습니다. 이 연구는 오프셋 구성이 직선 오리피스 레이아웃 (28 %)에 비해 물고기 통과 성공률 (68 %)이 훨씬 더 높음을 발견했습니다. 어로를 성공적으로 협상하는 데 걸리는 시간도 오프셋 구성, 특히 작은 성인의 경우 훨씬 더 낮았습니다.

    이 연구에서는 유속과 난류 매개 변수가 물고기 수영 성능에 미치는 영향을 분석했습니다. 수영장의 유동장을 특성화하기 위해 음향 도플러 속도계가 사용되었습니다.

    이 연구의 결과에 따르면 레이놀즈 전단 응력은 어로 내 이베리아 미늘의 움직임에 가장 큰 영향을 미치는 매개 변수임이 입증되었습니다. Branco et al. [40] 두 가지 다른 흐름을 가진 오리피스와 노치가 있는 풀형 유형 어로에서 형태 학적 및 생태학적 특성이 다른 두 종, 바닥 지향 이베리아 바벨 Luciobarbus bocagei 및 물기둥 수영 자 Iberian chub Squalius pyrenaicus의 거동과 성능을 평가했습니다.

    풀의 유체 역학을 특성화하기 위해 음향 도플러 속도계가 사용되었습니다. 결과는 두 종 모두 흐름 흐름이있는 노치를 선호했으며 이 흐름 체제로 상류로 이동하는데 더 성공적이었습니다.
    이 연구에서는 이 시설의 1 : 2.5 스케일 어로 모델을 사용하여 Silva et al.에 의해 테스트된 바닥 오리피스 구성이 있는 풀형 유형 어로의 속도와 난류를 측정했습니다.

    [7,38] 효과가 입증된 바벨 사용. 2D 입자 이미지 속도계 (PIV) 시스템 및 음향 도플러 속도계 (ADV)를 사용하여 순간 속도의 광범위한 측정을 수행하고, 후 처리하고, 수치 모델 정확도를 평가하는 데 사용했습니다.

    Haque et al. [44] 대부분의 경우 수치 모델의 검증에 사용할 수있는 실험 데이터 세트에 높은 측정 오류가 있고 / 또는 측정 메시가 너무 거칠어 서 이들의 예측 기능을 올바르게 평가할 수없는 문제를 언급했습니다.

    모델. Blocken과 Gualtieri [23]는 검증 및 검증 연구가 필수적이며 CFD 연구를 검증하기위한 데이터를 제공하기 위해 고품질 실험이 필요하다고 언급합니다.

    Fuentes-Pérez et al. [35]는 특히 난류 메트릭에 대한 어로 연구에서 수치 모델 검증 데이터를 찾는 데 어려움을 언급합니다. 두 가지 측정 기술을 사용하고 상당한 양의 실험 데이터를 얻었기 때문에 이 연구에서는 이러한 문제를 극복했습니다.

    물리적 모델은 종종 Froude 수 유사성을 기반으로하며, 두 유사성 법칙을 모두 충족하는 데 어려움이있어 무시되는 레이놀즈 수 유사성입니다. 프로토 타입 레이놀즈 수가 일반적으로 훨씬 더 크기 때문에 레이놀즈 수 관련 스케일 효과가 도입될 수 있습니다.

    레이놀즈 수 증가는 속도 분포와 경계층 속성에 영향을 미칠 수 있습니다 [45]. 척도 효과를 평가하기 위해 수치 시뮬레이션을 사용할 수 있습니다 [46,47]. 따라서 본 연구에서는 바닥 오리피스 흐름이있는 풀형어도에 대한 스케일 효과를 분석하기 위해 두 가지 크기의 수치 모델을 개발했습니다.

    프로토 타입 치수의 대형 모델과 물리적 모델 치수의 스케일 된 소형 모델입니다. .
    바닥 오리피스가있는 수영장 형 어로의 유동장은 수직 슬롯 어로 (VSF)의 유동장보다 매우 3 차원 적이며 훨씬 더 복잡합니다. 이는 어로 수치 모델 검증에 대한 이전 연구에서 더 자주 고려 된 설계입니다 [26, 27,28,29,35].

    저자가 아는 한, 이것은 바닥 오리피스가있는 풀형 어로에 대한 최초의 CFD 연구이며, 여기에는 실험 속도 데이터와 풀형 어로에 대한 3 차원 수치 모델링 결과 간의 가장 광범위한 비교도 포함됩니다. 두 가지 다른 측정 기술 (PIV 및 ADV)이 사용되어 자세한 비교가 가능하고 이러한 유형의 유동장에 대한 CFD 시뮬레이션 결과에 대한 확신을 제공합니다.

    이 연구는 다른 어로 유형의 이전 수치 모델 연구에서 제시되지 않았던 난류 매개 변수를 포함하여 수치 모델 결과와 측정 간의 일치에 대한 통계적 테스트를 통해 정성적 비교 뿐만 아니라 상세한 정량적 비교도 제공합니다. 스케일 효과도 다룹니다.

    따라서 이 연구는 전 세계적으로 가장 많이 사용되는 풀 유형 어로의 CFD 모델 검증을 원활하게 할 것이며 [10] 설계자들의 사용을 장려 할 것입니다.
    또한 새로운 풀 유형 어로 형상을 위한 설계 도구로 CFD 모델 (즉, FLOW 3D®)을 사용하는 방법에 대해 설명합니다.

    Figure 1. Experimental flume used (a) Side view of the flume; (b) Pool detail.
    Figure 1. Experimental flume used (a) Side view of the flume; (b) Pool detail.
    Figure 2. Three dimensional representations of a pool showing the measurement planes and the acoustic Doppler velocimetry (ADV) measurement grid (a) measurement planes parallel to the flume bottom; (b) vertical measurement planes (ADV measurement grid is only shown in one plane).
    Figure 2. Three dimensional representations of a pool showing the measurement planes and the acoustic Doppler velocimetry (ADV) measurement grid (a) measurement planes parallel to the flume bottom; (b) vertical measurement planes (ADV measurement grid is only shown in one plane).
    Figure 3. Computational domain, showing Pool 3 mesh block.
    Figure 3. Computational domain, showing Pool 3 mesh block.
    Figure 4. Streamlines of time-averaged velocities (left: PIV; right: mesh Amodel): (a,b) plane 2 (z = 0.088 m); (c,d) plane 5 (y = 0.20 m).
    Figure 4. Streamlines of time-averaged velocities (left: PIV; right: mesh Amodel): (a,b) plane 2 (z = 0.088 m); (c,d) plane 5 (y = 0.20 m).
    Figure 5. Longitudinal variation of velocity components: (a,c,e) planes 1 and 6 intersection (y = 0.36 m and z = 0.04 m); (b,d,f) planes 2 and 5 intersection (y = 0.20 m and z = 0.088 m).
    Figure 5. Longitudinal variation of velocity components: (a,c,e) planes 1 and 6 intersection (y = 0.36 m and z = 0.04 m); (b,d,f) planes 2 and 5 intersection (y = 0.20 m and z = 0.088 m).
    Figure 6. Longitudinal variation of Reynolds normal stress components and Reynolds shear stress parallel to the bottom component: (a,c,e,g) planes 1 and 6 intersection (y = 0.36 m and z = 0.04m); (b,d,f,h) planes 2 and 5 intersection (y = 0.20 m and z = 0.088 m).
    Figure 6. Longitudinal variation of Reynolds normal stress components and Reynolds shear stress parallel to the bottom component: (a,c,e,g) planes 1 and 6 intersection (y = 0.36 m and z = 0.04m); (b,d,f,h) planes 2 and 5 intersection (y = 0.20 m and z = 0.088 m).

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    55. Bayon, A.; Valero, D.; García-Bartual, R.; López-Jiménez, P.A. Performance assessment of OpenFOAM and FLOW-3D in the numerical modeling of a low Reynolds number hydraulic jump. Environ. Model. Softw. 2016, 80, 322–335. [CrossRef]
    56. Duguay, J.M.; Lacey, R.W.J.; Gaucher, J. A case study of a pool and weir fishway modeled with OpenFOAM and FLOW-3D. Ecol. Eng. 2017, 103, 31–42. [CrossRef]
    1. Hirt, C.W.; Nichols, B.D. Volume of fluid (VOF) method for the dynamics of free boundaries. J. Comp. Phys. 1981, 39, 201–225. [CrossRef]
    2. Van Leer, B. Towards the ultimate conservative difference scheme. IV. A new approach to numerical convection. J. Comp. Phys. 1977, 23, 276–299. [CrossRef]
    3. Celik, I.B.; Ghia, U.; Roache, P.J.; Freitas, C.J.; Coleman, H.; Raad, P.E. Procedure for Estimation and Reporting of Uncertainty Due
      to Discretization in CFD Applications. J. Fluids Eng. 2008, 130, 078001 (4pages). [CrossRef]
    4. Smagorinsky, J. General circulation experiments with the primitive equations: I. The Basic Experiment. Mon. Weather Rev. 1963,
      91, 99–164. [CrossRef]
    5. Meyers, J.; Geurts, B.J.; Baelmans, M. Database analysis of errors in large-eddy simulation. Phys. Fluids 2003, 15, 2740–2755.[CrossRef]
    6. Celik, I.B.; Cehreli, Z.N.; Yavuz, I. Index of Resolution Quality for Large Eddy Simulations. J. Fluids Eng. 2005, 127, 949–958. [CrossRef]
    7. Freitag, M.; Klein, M. An improved method to assess the quality of large eddy simulations in the context of implicit filtering. J. Turbul. 2006, 7, 1–11. [CrossRef]
    8. Gousseau, P.; Blocken, B.; van Heijst, G.J.F. Quality assessment of Large-Eddy Simulation of wind flow around a high-rise building: Validation and solution verification. Comput. Fluids 2013, 79, 120–133. [CrossRef]
    9. Celik, I.; Li, J.; Hu, G.; Shaffer, C. Limitations of Richardson Extrapolation and Some Possible Remedies. J. Fluids Eng. 2005, 127, 795–805. [CrossRef]
    10. Pope, S.B. Turbulent Flows; Cambridge University Press: Cambridge, UK, 2000.
    11. Legates, D.R.; McCabe, G.J., Jr. Evaluating the use of “goodness-of-fit” Measures in hydrologic and hydroclimatic model validation. Water Resour. Res. 1999, 35, 233–241. [CrossRef]
    12. Bennett, N.D.; Crok, B.F.W.; Guariso, G.; Guillaume, J.H.A.; Hamilton, S.H.; Jakeman, A.J.; Marsili-Libelli, S.; Newhama, L.T.H.; Norton, J.P.; Perrin, C.; et al. Characterising performance of environmental models. Environ. Model. Softw. 2013, 40, 1–20. [CrossRef]
    13. Willmott, C.J.; Robeson, S.M.; Matsuura, K. A refined index of model performance. Int. J. Climatol. 2012, 32, 2088–2094. [CrossRef]
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      and Hydraulic Research; Bates, P.D., Anderson, M.G., Eds.; John Wiley: Hoboken, NJ, USA, 2001; pp. 413–438.
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    Simulation Gallery

    Simulation Gallery

    Simulation Gallery | 시뮬레이션 갤러리

    시뮬레이션 비디오 갤러리에서 FLOW-3D  제품군으로 모델링 할 수 있는 다양한 가능성을 살펴보십시오 .

    적층 제조 시뮬레이션 갤러리

    FLOW-3D AM 은 레이저 파우더 베드 융합, 바인더 제트 및 직접 에너지 증착과 같은 적층 제조 공정을 시뮬레이션하고 분석합니다. FLOW-3D AM 의 다중 물리 기능은 공정 매개 변수의 분석 및 최적화를 위해 분말 확산 및 압축, 용융 풀 역학, L-PBF 및 DED에 대한 다공성 형성, 바인더 분사 공정을 위한 수지 침투 및 확산에 대한 매우 정확한 시뮬레이션을 제공합니다. 

    Multi-material Laser Powder Bed Fusion | FLOW-3D AM

    Micro and meso scale simulations using FLOW-3D AM help us understand the mixing of different materials in the melt pool and the formation of potential defects such as lack of fusion and porosity. In this simulation, the stainless steel and aluminum powders have independently-defined temperature dependent material properties that FLOW-3D AM tracks to accurately capture the melt pool dynamics. Learn more about FLOW-3D AM’s mutiphysics simulation capabilities at https://www.flow3d.com/products/flow3…

    Laser Welding Simulation Gallery

    FLOW-3D WELD 는 레이저 용접 공정에 대한 강력한 통찰력을 제공하여 공정 최적화를 달성합니다. 더 나은 공정 제어로 다공성, 열 영향 영역을 최소화하고 미세 구조 진화를 제어 할 수 있습니다. 레이저 용접 공정을 정확하게 시뮬레이션하기 위해 FLOW-3D WELD 는 레이저 열원, 레이저-재료 상호 작용, 유체 흐름, 열 전달, 표면 장력, 응고, 다중 레이저 반사 및 위상 변화를 특징으로 합니다.

    Keyhole welding simulation | FLOW-3D WELD

    물 및 환경 시뮬레이션 갤러리

    FLOW-3D 는 물고기 통로, 댐 파손, 배수로, 눈사태, 수력 발전 및 기타 수자원 및 환경 공학 과제 모델링을 포함하여 유압 산업에 대한 많은 응용 분야를 가지고 있습니다. 엔지니어는 수력 발전소의 기존 인프라 용량을 늘리고, 어류 통로, 수두 손실을 최소화하는 흡입구, 포 이베이 설계 및 테일 레이스 흐름을위한 개선 된 설계를 개발하고, 수세 및 퇴적 및 공기 유입을 분석 할 수 있습니다.

    금속 주조 시뮬레이션 갤러리

    FLOW-3D CAST  에는 캐스팅을 위해 특별히 설계된 광범위하고 강력한 물리적 모델이 포함되어 있습니다. 이러한 특수 모델에는 lost foam casting, non-Newtonian fluids, and die cycling에 대한 알고리즘이 포함됩니다. FLOW-3D CAST 의 강력한 시뮬레이션 엔진과 결함 예측을 위한 새로운 도구는 설계주기를 단축하고 비용을 절감 할 수 있는 통찰력을 제공합니다.

    HPDC |Comparison of slow shot profiles and entrained air during a filling simulation |FLOW-3D CAST

    Shown is a video comparing two slow shot profiles. The graphs highlight the shot profiles through time and the difference in entrained air between the slow shots. Note the lack of air entrained in shot sleeve with calculated shot profile which yields a much better controlled flow within the shot sleeve.

    Coastal & Maritime Applications | FLOW-3D

    FLOW-3D는 선박 설계, 슬로싱 다이내믹스, 파동 충격 및 환기 등 연안 및 해양 애플리케이션에 이상적인 소프트웨어입니다. 연안 애플리케이션의 경우 FLOW-3D는 연안 구조물에 심각한 폭풍과 쓰나미 파장의 세부 정보를 정확하게 예측하고 플래시 홍수 및 중요 구조물 홍수 및 손상 분석에 사용됩니다.

    education_banner

    FLOW-3Dv12.0 온라인 교육

    FLOW-3 D v12.0 온라인 교육 과정은 미국 FSI에서 제공되는 컨텐츠로 FLOW-3D 사용자(구매/임차 및 기술지원 계약이 되어 있는 고객)에게 제공되는 교육 리소스입니다. 이 온라인 교육 과정은 FLOW-3D 기본 모델 사용법 전반에 대한 온라인 주문형 비디오를 제공합니다.

    각 과정에서는 사용자가 스스로 시뮬레이션을 설정할 수 있도록 예제와 설명을 제공합니다. 모든 신규 FLOW3D사용자는 프로젝트별 시뮬레이션 작업을 시작하기 전에 기본 과정을 완료하는 것이 좋습니다.

    또한 기존 사용자는 FLOW3D v12.0모델 설정 프로세스에서 사용할 수 있는 향상된 기능과 새로운 기능에 대해 배우고 기본 모델 설정 항목에 대한 리프레시로 배우는 데 유용한 새로운 교육 시리즈를 찾게 될 것입니다. 과정 비디오는 특정 주제 및 세그먼트를 쉽게 찾을 수 있도록 구성되어 있고, 즐겨 찾기에 추가될 수 있으며, 언제든지 참조할 수 있는 유용한 리소스를 제공합니다.

    본 교육 과정은 미국 본사 정책에 따라 유지보수 계약이 체결된 고객 ID를 통해 미국의 Users Site 에서 제공됩니다.

    FLOW-3D Training Modules

    FLOW-3D GUI PART 1 OF THE FLOW-3D V12.0 TRAINING SERIES

    FLOW-3D GUI

    • Introduction to FLOW-3D graphical user interface
    • Simulation Manager Tab
    • Portfolio
    • Running Simulations and the Queue
    • Runtime Diagnostics: Text Output
    • Runtime Diagnostics: Plots
    • Runtime Controls
    • FLOW-3D File Structure
      Review the important files that are created when running simulations in FLOW-3D. Access the simulation files through a link on the Simulation Manager Tab. Identify the important setup and solver outputs files
    Model Setup Tab PART 2 OF THE FLOW-3D V12.0 TRAINING SERIES

    모델 설정 탭

    • Introduction to the Model Setup TabIntroduction to the Model Setup Tab including an orientation to its layout and how to access model inputs though the dock widgets on the process toolbar. Options for customizing the layout of the process toolbar are also reviewed.
    • Navigating the 3D ViewportLearn the basic controls for navigating the 3D viewport. This includes mouse controls, toolbar shortcuts, saving views, and moving the pivot point.
    • Other Menu/Toolbar Navigation Options
    • Working with Dock Widget Inputs
    • Model DependenciesRecognize and understand dock widget input dependencies.
    Global Settings PART 3 OF THE FLOW-3D V12.0 TRAINING SERIES

    전역 설정

    • Global Dock Widget Overview
    • Pressure Type
    • Finish Time
    • Finish Options: Additional Finish Condition
    • Finish Options: Active Simulation ControlDefine a logical condition to stop the simulation using active simulation control.
    • Restart OptionsHow to manually define the Restart options to continue running a previously completed simulation.
    • Version OptionsDefine the Version options to specify the solver version and the number of processors used when starting a new simulation run.
    Physics Models PART 4 OF THE FLOW-3D V12.0 TRAINING SERIES

    물리 모델

    • Physics Dock Widget OverviewDescription of the available options in the Physics dock widget
    • Interface Tracking, Number of Fluids and Flow ModeBackground information on interface tracking methods and defining the number of fluids. Description of the Volume of Fluid (VOF) method for simulation of complex free surfaces, and how this affects the selection of the number of fluids. Examples are presented for one fluid and two fluid simulations.
    • Activating Physics ModelsDemonstration for how to activate physics models and how to limit the display of inactive physics models using the physics model filter.
    Fluid Properties PART 5 OF THE FLOW-3D V12.0 TRAINING SERIES

    유체 속성

    • Fluids Dock Widget OverviewIntroduction to the Fluids dock widget and how to define properties for fluids in the simulation.
    • Defining Fluid Properties ManuallyExample for how to manually define fluid properties.
    • Defining Fluid Properties from the Materials DatabaseExample for how to load fluid properties from the fluids database.
    • Managing the Materials Database
      How to add and edit entries in the materials database.
    Geometry PART 6 OF THE FLOW-3D V12.0 TRAINING SERIES

    지오메트리

    • Introduction
    • Component and Subcomponent Overview
    • Creating Subcomponents: Overview
    • Creating Subcomponents: STL
    • Creating Subcomponents: Primitives Manually
    • Creating Subcomponents: Primitives Interactively
    • Creating Subcomponents: Raster
    • Subcomponent Types
    • Subcomponent Order
    • Component Order
    • Component and Subcomponent Properties
    • Transformations
    Meshing PART 7 OF THE FLOW-3D V12.0 TRAINING SERIES

    Meshing

    • Meshing Introduction
    • Coordinate Systems
    • FAVOR™
    • Meshing Basics: Meshing Overview
    • Meshing Basics: Creating Mesh Blocks
    • Meshing Basics: Domain Extents
    • Meshing Basics: Global Controls
    • Meshing Basics: Local Controls
    • Reviewing Mesh Quality: FAVORize
    • Reviewing Mesh Quality: Preprocessing
    • Multi-block Meshing
    • Conforming Mesh Blocks
    • Meshing Best Practices
    Boundary Conditions PART 8 OF THE FLOW-3D V12.0 TRAINING SERIES

    Boundary Conditions

    • Introduction
      Introductory comments regarding how boundary conditions are applied and other considerations when defining BCs.
    • Boundaries Dock Widget Overview
    • Velocity
    • Volume Flow Rate
    • Wall
    • Symmetry
    • Grid Overlay
    • Pressure
    • Continuative
    • Outflow
      Description and example setup of the Outflow BC type.
    Initial Conditions PART 9 OF THE FLOW-3D V12.0 TRAINING SERIES

    Initial Conditions

    • Introduction
      Discussion of how the initial conditions and can affect simulation results and run times.
    • Options for Defining ICs
      Example: Global Settings
      Example: Fluid Regions
    • Example: Function Coefficients
      Description and example for defining spatially varying fluid properties with user defined functions.
    • Example: Pointers
      Description and example for defining an initial condition by filling contiguous cells with the Pointer object.
    Output Options PART 10 OF THE FLOW-3D V12.0 TRAINING SERIES

    Output Options

    • Output Dock Widget Overview
    • Spatial Data
    • Spatial Data: Restart Data
    • Spatial Data: Selected Data
    • History Data
    • Diagnostics: Short Print Data
    • Diagnostics: Long Print Data
    • Example Setup
    • Batch Post-processing
    • Batch Mode: Context File
    • Batch Mode: Manual
    • Batch Mode: Generate Reports
    Baffles PART 11 OF THE FLOW-3D V12.0 TRAINING SERIES

    Baffles

    Introduction
    An introduction to the available options for creating and defining baffle objects.
    Creating Baffle Objects
    Limitations
    Force Outputs
    Porosity
    Scalar Reset Options
    Summary
    A summary of the important options for creating baffles and defining properties.

    Measurement Devices PART 12 OF THE FLOW-3D V12.0 TRAINING SERIES

    Measurement Devices

    • History Probes 
      History probes are point measurement devices and are used to record solver output at a specific location. Examples are provided for how to create these objects interactively and by defining a coordinate value.
    • Flux Surfaces 
      Flux surfaces are a special type of baffle object with a fixed porosity of 1, and are used to calculate flux quantities. Examples are provided for how to create flux surfaces and the types of data available from their output.
    • Sampling volumes 
      Sampling volumes are are three-dimensional data collection regions. Examples are provided for how to create sampling volumes and the types of data available from their output.
    W&E Exercise: Ogee Weir

    W&E Exercise: Ogee Weir

    • This exercise demonstrates the steps to setup a basic free surface or open channel flow simulation in FLOW-3D. It is intended to be a simple and fast running simulation that demonstrates the key setup steps that can be applied to a wide range of other common open channel flow applications. In this exercise, we will simulate flow over an ogee weir to predict the discharge capacity. Simulation results can be validated against discharge rating curves obtained from physical model measurements (USBR, 1996).  Special attention is given to the common types of boundary conditions used in open channel flow simulations and how to select them during the model setup. We also provide examples for common post-processing tasks using both FLOW-3D and FlowSight.

    레이저 용접 수치해석 (FLOW-3D WELD)

    FLOW-3D WELD Products

    레이저 용접 수치해석 (FLOW-3D WELD)

    FLOW-3D@ WELD는 레이저 용접 공정에 대한 정확한 시뮬레이션 기능을 제공하여 최적화된 공정을 개발하게 합니다. 더 나은 공정 제어를 통해 기공, 열 영향 영역을 최소화하고 미세 구조 변화를 제어할 수 있습니다.

    레이저 용접 프로세스를 정확하게 시뮬레이션하기 위해 FLOW-3D@ WELD는 레이저 열원, 레이저-재료 상호 작용, 유체 흐름, 열 전달, 표면 장력, 응고, 다중 레이저 반사 및 위상 변화와 같은 모든 관련 물리 모델을 제공합니다.

    Laser Welding

    최근에는 뛰어난 생산성과 속도, 낮은 열 입력이 결합되어 기존의 용접 프로세스를 대체하는 레이저 용접 프로세스가 주목 받고 있습니다. 레이저 용접이 제공하는 장점은 용접강도가 좋고, 열 영향 부위가 작으며, 정밀도가 낮고 변형이 적으며, 강철, 알루미늄, 티타늄 및 이종 금속을 포함한 광범위한 금속 및 합금을 용접 할 수 있는 기능이 있습니다.

    FLOW-3D@는 레이저 용접 공정에 대한 강력한 통찰력을 제공하고 궁극적으로 프로세스 최적화를 달성하는 데 도움이 됩니다.

    보다 나은 프로세스 제어를 통해 기공을 최소화할 수 있습니다. 열 영향부위 및 미세조직을 제어가 가능합니다. FLOW-3D는 자유표면 추적 알고리즘을 통해 매우 복잡한 용접 POOL 시뮬레이션을 해석하는데 매우 적합합니다.

    용접 모듈은 레이저 소스에 의해 생성된 Heat flux, 용융 금속에 대한 증발압력, shield gas 효과, 용융 풀의 반동압력 및 다중 레이저 반사와 같은 물리적 모델을 FLOW-3D에 적용하기 위해 개발되었습니다. 키홀 용접과 같은 현실적인 프로세스 시뮬레이션을 위해서는 모든 관련 물리적 현상을 적용하는 것이 중요합니다.

    FLOW-3D는 레이저 용접의 conduction and keyhole 방식을 시뮬레이션 할 수 있습니다. 전 세계의 연구원들은 FLOW-3D를 사용하여 용접역학을 분석하고, 공정 매개 변수를 최적화하여 기공을 최소화하며, 레이저 용접공정에서의 dendrite 결정 성장 양상을 예측합니다.

    Shallow penetration weld (top left); deep penetration weld with shield gas effects (top right); deep penetration weld with shield gas and evaporation pressure (bottom left); and deep penetration weld with shield gas, evaporation pressure and multiple laser reflections effects (bottom right).

    Full Penetration Laser Welding Experiments

    한국 카이스트와 독일 BAM은 16K kW레이저를 사용하여 10mm강판에 완전 침투 레이저 용접 실험을 수행하였습니다. CCD카메라의 도움을 받아 완전 용입 레이저 용접으로 형성된 상단 및 하단 용융풀 거동을 확인할 수 있었습니다. 그들은 또한 FLOW-3D 로 용접 공정 해석으로 해석과 실험결과의 경향이 일치하는 것을 알 수 있었습니다.

    Experimental setup with CCD cameras observing the top and bottom molten pools
    Schematic of computation domain in FLOW-3D

     

    Simulation results at the top show melt pool lengths of 8mm and 15mm, whereas experiments indicated melt pool lengths of 7mm and 13mm

    Laser Welding Porosity Case Study

    General Motors, Michigan, 중국의 상하이 대학교는 용접 공정 변수, 즉 keyhole 용접에서 기공의 발생에 대해 용접 속도 및 용접 각도와 같은 공정 매개 변수가 미치는 영향을 알아보기 위해 협력하여 연구를 진행하였습니다.

    레이저 용접된 Al 접합부 단면의 기공을 분석합니다. Keyhole이 유도 된 기공들은 유동 역학으로 인해 발생되고 균열을 일으킬 수 있습니다. 최적화 공정의 매개변수는 이러한 종류의 기공을 완화할 수 있습니다. FLOW-3D를 사용하여 연구원들은 증발 및 반동 압력, 용융풀, 온도에 따른 표면장력 및 Keyhole내의 다중 레이저 반사, 프레넬 흡수를 포함한 모든 중요한 물리적 현상을 설명했습니다.

    연구진은 시뮬레이션 모델을 기반으로 Keyhole 용접에서 생성된 기공들의 주요 원인으로 불안정한 Keyhole을 규정하였습니다. 아래 이미지에서 볼 수 있듯이 뒤쪽 용융 풀의 과도한 재순환은 뒤쪽 용융 풀이 앞쪽 용융 풀 경계를 무너뜨리며 기공들을 생성시킵니다. 갇힌 공간이 증가하는 응고 전면에 의해 갇혔을때 기공들이 발생되었습니다.

    Distribution of porosity in longitudinal welding sections as seen in simulations (top) and experiments (bottom)

    용접 속도가 빠를수록 더 큰 keyhole이 생성되며 이로 인해, 보다 안정적인 keyhole이 생성됩니다. 연구진은 FLOW-3D를 사용하여 용접 속도와 용접 경사각으로 기공들의 생성을 완화시킬 수 있었습니다.


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    레이저 용접에서의 키홀 동력학과 유도를 통한 Porosity 형성

    레이저 용접에서의 Key Hole 동력학과 유도를 통한 Porosity 형성

    자료 제공: General Motors Company, Shanghai Jiao Tong University
    자료 제공: FLOW Science Japan

    이 사례를 통해 FLOW-3D@ WELD를 이용하여 레이저 용접 프로세스의 키홀 형성 유도를 통한 porosity 형성에 대하여 검토가 가능한 것을 알 수 있습니다.

    • porosity 형성을 유도하는 키홀의 메커니즘
    • 레이저 출력과 용접 속도의 영향
    • 레이저 빔의 경사각의 영향으로 porosity 형성을 유도하는 키홀의 메커니즘
    Porosity 형성을 유도하는 Key Hole 해석모델
    Porosity 형성을 유도하는 Key Hole 해석모델

    위 그림과 같이 온도에 따른 표면장력 값과 강한 우회전 소용돌이에 의해 후방으로의 유동은 거의 억제되는 것을 확인할 수 있습니다. 강한 용융 유동에 의한 Key Hole 붕괴는 초기 porosity 형성의 원인이 되지만, Key Hole 재개나 기포가 자유표면으로 빠져 나가도록 반드시 porosity를 이끌지는 않습니다.

    그러나 키홀 바닥부에서 강한 소용돌이에 의해 기포가 키홀 용융지 후방 저부로 운반될 때는 높은 열전도율로 응고면이 빠르게 이동하므로, 응고면에 의해 포획될 위험이 매우 높습니다.

    또한 용융 시의 알루미늄은 소용돌이가 강하기 때문에, 기포를 용융지의 바닥 후방에 있는 상태에서 배출시키는 것은 거의 불가능합니다. 기포가 응고면에 의해 포획될 경우 porosity가 형성됩니다.

    레이저 출력과 용접속도의 영향

    일반적으로 용접속도를 크게 하면 결합부에서 Porosity가 감소합니다. 이는 용접 속도 상승으로 모재 내 용해 및 키홀 깊이가 감소하여 키홀이 안정되기 때문입니다.

    레이저 출력과 용접 속도의 영향
    레이저 출력과 용접 속도의 영향
    저속과 고속의 2 케이스에서 예측된 용융지의 유속장과 온도 분포
    저속과 고속의 2 케이스에서 예측된 용융지의 유속장과 온도 분포

    실험에 의한 길이 방향 단면의 Porisity 분포와 FLOW-3D@ WELD에 의한 분석 결과를 보여줍니다. 3번 케이스도 실험과 비슷한 용해 깊이를 가지고 있으며, 분석 결과도 실험과 매우 잘 일치하고 있습니다.

    용접 단면의 Porosity 분포
    용접 단면의 Porosity 분포

    용접 단면의 Porosity 분포를 보면, 레이저 조사 각도가 증가할 수록 Porosity가 뚜렷이 감소하고 있음을 알 수 있습니다. 위의 오른쪽 그림에 용융지 내의 유속장과 온도분포를 보면 레이저 빔의 경사각도는 키홀의 생성 방향을 결정하여 후방의 용융지와 용융유동에 영향을 미치고 있습니다.

    또한, 레이저의 경사각도가 작을 경우 강력한 증발 반력이나 중력에 의해 용융금속이 다른 방향으로 이동합니다. 이는 강한 소용돌이 흐름의 원인이 되는 구동력으로 작용하여 키홀 붕괴로 이어지기 쉽다는 것을 확인할 수 있습니다.

    The realm of operations of FLOW-3D

    ADDITIVE MANUFACTURING SIMULATIONS

    Capabilities of FLOW-3D

    FLOW-3D는 자유 표면 유체 흐름 시뮬레이션을 전문으로하는 다중 물리 CFD 소프트웨어입니다. 자유 표면의 동적 진화를 추적하는 소프트웨어의 알고리즘인 VOF (Volume of Fluid) 방법은 Flow Science의 설립자인 Tony Hirt 박사가 개척했습니다.

    또한 FLOW-3D에는 금속 주조, 잉크젯 인쇄, 레이저 용접 및 적층 제조 (AM)와 같은 광범위한 응용 분야를 시뮬레이션하기위한 물리 모델이 내장되어 있습니다.
    적층 제조 시뮬레이션 소프트웨어, 특히 L-PBF (레이저 파우더 베드 융합 공정)의 현상 유지는 열 왜곡, 잔류 응력 및지지 구조 생성과 같은 부분 규모 모델링에 도움이되는 열 기계 시뮬레이션에 초점을 맞추고 있습니다.

    유용하지만 용융 풀 역학 및 볼링 및 다공성과 같은 관련 결함에 대한 정보는 일반적으로 이러한 접근 방식의 영역 밖에 있습니다. 용융 풀 내의 유체 흐름, 열 전달 및 표면 장력이 열 구배 및 냉각 속도에 영향을 미치며 이는 다시 미세 구조 진화에 영향을 미친다는 점을 명심하는 것도 중요합니다.

    FLOW-3D와 이산 요소법 (DEM) 및 WELD 모듈을 사용하여 분말 및 용융 풀 규모에서 시뮬레이션 할 수 있습니다.
    구현되는 관련 물리학에는 점성 흐름, 열 전달, 응고, 상 변화, 반동 압력, 차폐 가스 압력, 표면 장력, 움직이는 물체 및 분말 / 입자 역학이 포함됩니다. 이러한 접근 방식은 합금에 대한 공정을 성공적으로 개발할 수 있게 하고, AM 기계 제조업체와 AM 기술의 최종 사용자 모두에게 관심있는 미세 구조 진화에 대한 통찰력을 제공하는데 도움이 됩니다.

    The realm of operations of FLOW-3D
    The realm of operations of FLOW-3D

    FLOW-3D는 레이저 분말 베드 융합 (L-PBF), 직접 에너지 증착 (DED) 및 바인더 제트 공정으로 확장되는 기능을 가지고 있습니다.
    FLOW-3D를 사용하면 분말 확산 및 패킹, 레이저 / 입자 상호 작용, 용융 풀 역학, 표면 형태 및 후속 미세 구조 진화를 정확하게 시뮬레이션 할 수 있습니다. 이러한 기능은 FLOW-3D에 고유하며 계산 효율성이 높은 방식으로 달성됩니다.

    예를 들어 1.0mm x 0.4mm x 0.3mm 크기의 계산 영역에서 레이저 빔의 단일 트랙을 시뮬레이션하기 위해 레이저 용융 모델은 단 8 개의 물리적 코어에서 약 2 시간이 걸립니다.
    FLOW-3D는 모든 관련 물리 구현 간의 격차를 해소하는 동시에 업계 및 연구 표준에서 허용하는 시간 프레임으로 결과를 생성합니다. 분말 패킹, 롤러를 통한 파워 확산, 분말의 레이저 용융, 용융 풀 형성 및 응고를 고려하고 다층 분말 베드 융합 공정을 위해 이러한 단계를 순차적으로 반복하여 FLOW-3D에서 전체 AM 공정을 시뮬레이션 할 수 있습니다.

    FLOW-3D의 다층 시뮬레이션은 이전에 응고된 층의 열 이력을 저장한다는 점에서 독특하며, 열 전달을 고려하여 이전에 응고된 층에 확산된 새로운 분말 입자 세트에 대해 시뮬레이션이 수행됩니다.
    또한, 응고 된 베드의 열 왜곡 및 잔류 응력은 FLOW-3D를 사용하여 평가할 수 있으며, 보다 복잡한 분석을 수행하기 위해 FLOW-3D의 압력 및 온도 데이터를 Abaqus 및 MSC Nastran과 같은 FEA 소프트웨어로 내보낼 수 있습니다.

    Sequence of a multi-layer L-PBF simulation setup in FLOW-3D

    Ease of Use

    FLOW-3D는 다양한 응용 분야에서 거의 40 년 동안 사용되어 왔습니다. 사용자 피드백을 기반으로 UI 개발자는 소프트웨어를 사용하기 매우 직관적으로 만들었으며 새로운 사용자는 시뮬레이션 설정의 순서를 거의 또는 전혀 어려움없이 이해합니다.
    사용자는 FLOW3D에서 구현 된 다양한 모델의 이론에 정통하며 새로운 실험을 설계 할 수 있습니다. 실습 튜토리얼, 비디오 강의, 예제 시뮬레이션 및 기술 노트의 저장소도 사용할 수 있습니다.
    사용자가 특정 수준의 경험에 도달하면 고급 수치 교육 및 소프트웨어 사용자 지정 교육을 사용할 수 있습니다.

    Available Literature

    실험 데이터에 대해 FLOW-3D 모델을 검증하는 몇 가지 독립적으로 발표된 연구가 있습니다. 여기에서 수록된 저널 논문은 레이저 용접 및 적층 제조 공정으로 제한됩니다. 더 많은 참조는 당사 웹 사이트에서 확인할 수 있습니다.

    Laser Welding

    1. L.J.Zhang, J.X.Zhang, A.Gumenyuk, M.Rethmeier, S.J.Na, Numerical simulation of full penetration laser welding of thick steel plate with high power high brightness laser, Journal of Materials Processing Technology, Volume 214, Issue 8, 2014.
      A study by researchers from BAM in Germany, KAIST in Korea, and State Key Laboratory of Mechanical Behavior of Materials in China that focuses on keyhole dynamics and full penetration laser welding of steel plates.
    2. Runqi Lin, Hui-ping Wang, Fenggui Lu, Joshua Solomon, Blair E.
      Carlson, Numerical study of keyhole dynamics and keyhole-induced porosity formation in remote laser welding of Al alloys, International Journal of Heat and Mass Transfer, Volume 108, Part A, 2017.
      General Motors (GM) and Shangai University collaborated on a study on the influence of welding speed and weld angle of inclination on porosity occurrence in laser keyhole welding.
    3. Koji Tsukimoto, Masashi Kitamura, Shuji Tanigawa, Sachio Shimohata, and Masahiko Mega, Laser Welding Repair for Single Crystal Blades, International Gas Turbine Congress, Tokyo, 2015.
      Mitsubishi Heavy Industry’s study on laser welding repair using laser cladding for single Ni crystal alloys used in gas turbine blades.

    Additive Manufacturing

    1. Yu-Che Wu, Cheng-Hung San, Chih-Hsiang Chang, Huey-Jiuan Lin, Raed Marwan, Shuhei Baba, Weng-Sing Hwang, Numerical modeling of melt-pool behavior in selective laser melting with random powder distribution and experimental validation, Journal of Materials Processing Technology, Volume 254, 2018
      This paper discusses powder bed compaction with random packing for different powder-size distributions, and the importance of considering evaporation effects in the melting process to validate the melt pool dimensions.
    2. Lee, Y.S., and W.Zhang, Mesoscopic simulation of heat transfer and fluid flow in laser powder bed additive manufacturing, Proceedings of the Annual International Solid Freeform Fabrication Symposium, Austin, TX, USA. 2015
      A study conducted by Ohio State University researchers to understand the influence of process parameters in formation of balling defects.
    3. Y.S. Lee, W.Zhang, Modeling of heat transfer, fluid flow and solidification microstructure of nickel-base superalloy fabricated by laser powder bed fusion, Additive Manufacturing, Volume 12, Part B, 2016
      A study conducted by Ohio State University researchers to understand the influence of solidification parameters, calculated from the temperature fields, on solidification morphology and grain size using existing theoretical models in laser powder bed fusion processes.

     

     

    Casting Case Study

    Casting Case Study

    금속 주조물의 결함을 식별하고, 가볍고 튼튼한 주조 부품을 위해 새로운 재료로 부품을 설계하거나, 최적의 설계를 위해 반복적인 설계 작업을 수행하는 것은 고객이 당사의 소프트웨어를 사용하여 작업 요구 사항을 충족하고, 고철 비율을 줄임으로써 조직의 비용을 절감하는 일부 방법입니다.

    이를 통해 제품 개발 시간을 단축함으로써 제품의 시장 출시 및 경쟁 우위를 위한 시간 확보가 용이해 집니다.

    Customer Case Studies

    Increasing Productivity by Reducing Ejection Times
    Realizing Da Vinci’s Il Cavallo
    Aluminum Integral Foam Molding Process

    Solidification model

    Solidification model

    FLOW-3D CAST v5.1 solidification model

    FLOW-3D CAST v5.1의 새로운 최첨단 화학 기반 고체화 모델은 주조 시뮬레이션을 새로운 단계로 발전시킬것 입니다. 사용자는 주조 부품의 강도와 무결성을 예측하면서도 고철을 줄이고 제품 안전 및 성능 요구사항을 충족할 수 있습니다.

    Solidification model capabilities

    새로운 응고모델은 핵, 분리, 냉각 조건을 고려한 온도와 화학의 진화로 인한 잠열, 열전도도, 열 용량, 밀도, 점성 등을 포함한 고체화 경로와 재료 특성을 계산합니다.

    응고모델은 이차 덴드라이트 암 사핑(SDAS) 및 입자 크기와 같은 구성 및 냉각 조건에 기반한 미세 구조 진화를 예측합니다. 또한 확산과 집착으로 인한 매크로 분리를 예측합니다. 기계적 특성과 미세구조 사이의 경험적 관계는 실험 측정을 기반으로 합니다. 독특하고 강력한 마이크로 구조와 기계적 특성 예측 기능을 갖춘 새로운 고체화 모델은 마이크로도 예측을 위한 차원 없는 니야마 기준과 같은 다른 모델의 기초를 제공합니다.

    응고 미세 구조와 다공성 결함은 주물의 기계적 특성에 영향을 미치는 주요 요소입니다. 또한, 국소 미세 구조는 합금 원소의 분리에 따른 합금의 화학적 구성, 응고율 및 화학적 비동종성에 의해 결정됩니다. 공정 설계자는 새로운 응고 모델을 사용하여 다양한 공정 매개변수 및 합금 조합이 기계적 특성에 미치는 영향을 판단하여 주조물의 성능을 최적화하여 가능한 최고 품질의 안전한 제품을 생산할 수 있습니다.

    Solidification of A356

     

    Solidification of A206

    MICROSTRUCTURE OUTPUT

    • Secondary dendrite arm spacing (SDAS)
    • Grain size

    MECHANICAL PROPERTY OUTPUT

    • Ultimate tensile strength (UTS)
    • Elongation
    • Quality index
    • Yield strength for heat treated properties

    DEFECT INDICATORS

    • Dimensionless Niyama criterion
    • Microporosity

    완전하고 단순화된 화학 기반 응고 모델

    유연성 모델

    솔리드화 모델에는 전체 모델과 단순화된 모델이 모두 포함되어 있어 사용자가 시뮬레이션 워크플로우를 보다 효과적으로 제어할 수 있습니다. 전체 모델은 용융이 응고될 때 화응고 모델에는 전체 모델과 단순 모델이 모두 포함되어 있어 사용자가 시뮬레이션 워크 플로우를 보다 효과적으로 제어할 수 있습니다. 전체 모델은 용해가 응고됨에 따라 화학적 구성과 위상 변화를 고려하는 반면, 단순화된 모델은 보다 빠른 런트를 제공하고 전체 모델만큼 많은 메모리를 필요로 하지 않습니다. 전체 모델을 기반으로 한 재시작 시뮬레이션은 단순화된 모델에서 시작하거나 그 반대로 시작할 수 있습니다. 이를 통해 다양한 시뮬레이션 유형과 시뮬레이션 단계에 적합한 모델을 사용할 수 있는 완전한 유연성을 제공합니다.

    사용할 모델

    자원을 적게 사용하는 것의 명백한 이점 때문에 사용자는 가능한 단순화된 모델을 많이 사용할 것을 권장한다. 매크로 분리가 중요한 경우에는 사용자가 전체 모델을 사용하는 것이 좋습니다. 열 다이 사이클 시뮬레이션의 경우, 이러한 모델링 시나리오에서는 완전한 분석이 필요하지 않기 때문에 소프트웨어가 단순화된 모델을 적용합니다.

    일부 박막형 주조물의 경우 확산 및 홍보에 기반한 매크로 세그멘테이션은 중요하지 않습니다. 이러한 주조물에서 응고 경로는 전체적으로 거의 동일합니다. 따라서 각 개별 계산 셀에 대해 응고 중에 조성 및 위상 변화를 추적할 필요가 없습니다. 이러한 유형의 시나리오에서는 사용자가 간소화된 응고 모델을 사용하여 솔루션에 더 빨리 도달하는 것이 좋습니다.

    FLOW-3D CAST Bibliography

    FLOW-3D CAST bibliography

    아래는 FSI의 금속 주조 참고 문헌에 수록된 기술 논문 모음입니다. 이 모든 논문에는 FLOW-3D CAST 해석 결과가 수록되어 있습니다. FLOW-3D CAST를 사용하여 금속 주조 산업의 응용 프로그램을 성공적으로 시뮬레이션하는 방법에 대해 자세히 알아보십시오.

    Below is a collection of technical papers in our Metal Casting Bibliography. All of these papers feature FLOW-3D CAST results. Learn more about how FLOW-3D CAST can be used to successfully simulate applications for the Metal Casting Industry.

    33-20     Eric Riedel, Martin Liepe Stefan Scharf, Simulation of ultrasonic induced cavitation and acoustic streaming in liquid and solidifying aluminum, Metals, 10.4; 476, 2020. doi.org/10.3390/met10040476

    20-20   Wu Yue, Li Zhuo and Lu Rong, Simulation and visual tester verification of solid propellant slurry vacuum plate casting, Propellants, Explosives, Pyrotechnics, 2020. doi.org/10.1002/prep.201900411

    17-20   C.A. Jones, M.R. Jolly, A.E.W. Jarfors and M. Irwin, An experimental characterization of thermophysical properties of a porous ceramic shell used in the investment casting process, Supplimental Proceedings, pp. 1095-1105, TMS 2020 149th Annual Meeting and Exhibition, San Diego, CA, February 23-27, 2020. doi.org/10.1007/978-3-030-36296-6_102

    12-20   Franz Josef Feikus, Paul Bernsteiner, Ricardo Fernández Gutiérrez and Michal Luszczak , Further development of electric motor housings, MTZ Worldwide, 81, pp. 38-43, 2020. doi.org/10.1007/s38313-019-0176-z

    09-20   Mingfan Qi, Yonglin Kang, Yuzhao Xu, Zhumabieke Wulabieke and Jingyuan Li, A novel rheological high pressure die-casting process for preparing large thin-walled Al–Si–Fe–Mg–Sr alloy with high heat conductivity, high plasticity and medium strength, Materials Science and Engineering: A, 776, art. no. 139040, 2020. doi.org/10.1016/j.msea.2020.139040

    07-20   Stefan Heugenhauser, Erhard Kaschnitz and Peter Schumacher, Development of an aluminum compound casting process – Experiments and numerical simulations, Journal of Materials Processing Technology, 279, art. no. 116578, 2020. doi.org/10.1016/j.jmatprotec.2019.116578

    05-20   Michail Papanikolaou, Emanuele Pagone, Mark Jolly and Konstantinos Salonitis, Numerical simulation and evaluation of Campbell running and gating systems, Metals, 10.1, art. no. 68, 2020. doi.org/10.3390/met10010068

    102-19   Ferencz Peti and Gabriela Strnad, The effect of squeeze pin dimension and operational parameters on material homogeneity of aluminium high pressure die cast parts, Acta Marisiensis. Seria Technologica, 16.2, 2019. doi.org/0.2478/amset-2019-0010

    94-19   E. Riedel, I. Horn, N. Stein, H. Stein, R. Bahr, and S. Scharf, Ultrasonic treatment: a clean technology that supports sustainability incasting processes, Procedia, 26th CIRP Life Cycle Engineering (LCE) Conference, Indianapolis, Indiana, USA, May 7-9, 2019. 

    93-19   Adrian V. Catalina, Liping Xue, Charles A. Monroe, Robin D. Foley, and John A. Griffin, Modeling and Simulation of Microstructure and Mechanical Properties of AlSi- and AlCu-bas