Interfacial Compatibility for Laser Melting Deposition of CoCrNiCu Medium-Entropy Alloy on 316L Austenitic Stainless Steel Surface

doi:10.11900/0412.1961.2022.00426

Acta Metall Sin

2024, Vol. 60

Issue (9): 1213-1228 DOI: 10.11900/0412.1961.2022.00426

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Interfacial Compatibility for Laser Melting Deposition of CoCrNiCu Medium-Entropy Alloy on 316L Austenitic Stainless Steel Surface

YU Yunhe¹, XIE Yong¹, CHEN Peng¹, DONG Haokai², HOU Jixin¹(

), XIA Zhixin¹(

)

^1.Shagang School of Iron and Steel, Soochow University, Suzhou 215137, China
^2.School of Mechanical and Automotive Engineering, South China University of Technology, Guangzhou 510641, China

Cite this article:

YU Yunhe, XIE Yong, CHEN Peng, DONG Haokai, HOU Jixin, XIA Zhixin. Interfacial Compatibility for Laser Melting Deposition of CoCrNiCu Medium-Entropy Alloy on 316L Austenitic Stainless Steel Surface. Acta Metall Sin, 2024, 60(9): 1213-1228.

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Abstract

Dissimilar materials can achieve multifunction and multiperformance coupling and have broad development prospects in areas, such as aerospace, energy, automotive, and biomedicine. The properties of dissimilar materials can be improved by enhancing the compatibility of the heterogeneous interface. Herein, a laser melting deposition experiment of CoCrNiCu medium-entropy alloy (MEA) on the surface of 316L stainless steel was carried out. The microstructure morphology and interface characteristics of the dissimilar materials were characterized using SEM, STEM, EBSD, and transmission Kikuchi diffraction (TKD). The interfacial mechanical properties of the dissimilar materials were tested. The methods for promoting the bonding strength of dissimilar materials were then proposed by systematically exploring the interfacial compatibility of the microstructure and crystallography. The results show that a total solution transition zone of CoCrNiCuFe, a high-entropy alloy, was formed at the interface between CoCrNiCu MEA and 316L stainless steel. The shear strength of the dissimilar material can reach 324 MPa. Through the synergistic effect of austenite stability reduction caused by C interfacial partitioning and the plastic deformation induced by residual stress, some austenite grains of 316L stainless steel near the interface of the dissimilar materials undergo strain-induced martensitic transformation. This can promote the transformation-induced plasticity (TRIP) effect to improve the strength and ductility of the dissimilar materials while reducing interface matching. Therefore, as for the dissimilar materials with small physical discrepancies, single-phase matching with the same crystal structure should be maintained to increase the interfacial bonding strength by improving the interfacial crystallography compatibility. The TRIP effect can be used to design a duplex structure to improve the process of coordinated deformation for dissimilar materials with large physical discrepancies.

Key words: additive manufacturing laser melting deposition dissimilar material interface design medium-entropy alloy stainless steel

Received: 08 October 2022

ZTFLH:

TG113.12

Fund: National Natural Science Foundation of China(52071124,U2030102);Fund of Key Laboratory of Advanced Materials of Ministry of Education(ADV22-12);Jiangsu Funding Program for Excellent Postdoctoral Talent

Corresponding Authors: XIA Zhixin, professor, Tel: (0512) 67580785, E-mail: xiazhixin2000@163.com
HOU Jixin, associate professor, Tel: (0512) 67580785, E-mail: jxhou@foxmail.com

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	YU Yunhe
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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00426 OR https://www.ams.org.cn/EN/Y2024/V60/I9/1213

Fig.1 Schematic of laser melting deposition for dissimilar materials (a) and specimen macroscopic morphology of deposition layers with total scanning length of 18 cm (b) (MEA—medium-entropy alloy)

Fig.2 Secondary electron (SE) (a, b) and back-scattered electron (BSE) (c) SEM images of the dissimilar materials of CoCrNiCu MEA and 316L stainless steel at different magnifications

Table 1 Chemical compositions of original CoCrNiCu MEA and 316L stainless steel and different positions of heterogeneous interface between CoCrNiCu MEA and 316L stainless steel measured by EDS

Fig.3 STEM analyses of the dissimilar materials of CoCrNiCu MEA and 316L stainless steel
(a) bright field (BF) image (b) high-angle annular dark field (HAADF) image
(c) EDS diagram (d) Fe mapping (e) Co mapping (f) Cu mapping

Fig.4 EBSD analyses of the dissimilar materials of CoCrNiCu MEA and 316L stainless steel
(a) bond contrast (BC) image (The high-angle boundaries with misorientation angle >15° and low-angle boundaries with misorientation angle at 2°~15° are marked with black and red lines, respectively)
(b) inverse pole figure (IPF)
(c) phase distribution (PD) figure
(d) kernel average misorientation (KAM) map
(e1, e2) comparisons of the IPF (e1) and KAM map (e2) for the local magnification area of dissimilar material interface in Figs.4b and d, respectively (Types 1, 2, and 3 represent the interfaces with complete martensitic transformation, without martensitic transformation, and with incomplete martensitic transformation, respectively)

Fig.5 TEM images and interfacial element partitioning of the dissimilar materials of CoCrNiCu MEA and 316L stainless steel
(a) TEM image of 316L stainless steel (b) TEM image of CoCrNiCu MEA
(c) EDS element mapping near the interface (d) EDS line scan profile across the interface

Fig.6 Microhardness, strength, and fracture morphology for the dissimilar materials of CoCrNiCu MEA and 316L stainless steel
(a) sampling location for microhardness
(b) microhardness distribution
(c) strength profile (σ_y—yield strength, τ—shear strength)
(d) fracture morphology of dissimilar materials (Inset shows the locally enlarged image)

Fig.7 Calculation results of solid solution criterions for the dissimilar materials of CoCrNiCu MEA and 316L stainless steel
(a) Ω-δ criterion (Ω—ratio parameter, δ—atomic size difference)
(b) mixing enthalpy (ΔH_mix) criterion

Table 2 Calculated nickel equivalents (Ni_eq), chromium equivalents (Cr_eq), and predicted microstructure based on the Schaeffler diagram.

Fig.8 Effects of interfacial partitioning of substitu-tional elements (w(C)—mass fraction of C) (a) and interstitial element C (b) on the predicted microstructures of 316L stainless steel based on the Schaeffler diagram

Fig.9 Finite element model creating and mesh generation for the single-layer single-pass laser melting deposition of CoCrNiCu MEA on 316L stainless steel surface (Inset shows the mesh details near the interfaces of dissimilar materials) (a); simulation results of temperature field (Inset shows the temperature distribution on the cross section perpendicular to the scanning direction, T—temperature) (b); and simulation results of residual thermal stress including the equivalent Mises stress (σ_Mises) (c1) and corresponding components along X (σ₁₁) (c2), Y (σ₂₂) (c3), and Z (σ₃₃) (c4) directions

Fig.10 Evolutions of residual thermal stress perpendicular to the interface of dissimilar materials of CoCrNiCu MEA and 316L stainless steel

Fig.11 TEM analyses of matching mechanism of the heterogeneous interface between CoCrNiCu MEA and 316L stainless steel
(a) dark field (DF) image
(b, c) locally enlarged BF images of square areas of 1 (b) and 2 (c) in Fig.11a
(d-f) high resolution TEM images of the heterogeneous interface show the incoherent interface (d), coherent interface (e), and semi-coherent interface (f)

Fig.12 Transmission Kikuchi diffraction (TKD) analyses of martensitic transformation microstructure in 316L stainless steel
(a) SEM-SE image (b) PD figure (c) IPF
(d-f) Kikuchi band patterns of positions 1 (d), 2 (e), and 3 (f) in Fig.12a

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