Strengthening-Toughening Mechanism and Mechanical Properties of Span-Scale Heterostructure High-Entropy Alloy

doi:10.11900/0412.1961.2022.00322

Acta Metall Sin

2022, Vol. 58

Issue (11): 1441-1458 DOI: 10.11900/0412.1961.2022.00322

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Strengthening-Toughening Mechanism and Mechanical Properties of Span-Scale Heterostructure High-Entropy Alloy

AN Zibing¹, MAO Shengcheng¹(

), ZHANG Ze¹^,², HAN Xiaodong¹(

)

^1.Institute of Microstructure and Properties of Advanced Materials, Faculty of Materials and Manufacturing, Beijing University of Technology, Beijing 100124, China
^2.Department of Materials Science and Engineering, Zhejiang University, Hangzhou 310058, China

Cite this article:

AN Zibing, MAO Shengcheng, ZHANG Ze, HAN Xiaodong. Strengthening-Toughening Mechanism and Mechanical Properties of Span-Scale Heterostructure High-Entropy Alloy. Acta Metall Sin, 2022, 58(11): 1441-1458.

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Abstract

High-entropy alloys overcome the limitations posed by traditional alloys due to features such as high strength, toughness, high wear resistance, and corrosion resistance. These alloys are novel metallic materials with excellent application potential; however, typically an inverse relationship is observed between the strength and ductility of a metal, which includes high-entropy alloys. Therefore, the design and development of high entropy alloys with high strength and high ductility have become a limitation in current research. Recently, heterostructure design has achieved great success in strengthening and toughening traditional metallic materials. Heterostructured and high-entropy alloys has garnered much attention and research interest to realize the strength and toughness of high-entropy alloys with high strength and high ductility. This study reviews the existing design models for heterostructures from the heterostructure scale perspective. Furthermore, the effects of different heterostructures on the strengthening and toughening mechanism and mechanical properties were analyzed, and future microstructural designs with high strength and toughness were anticipated.

Key words: high-entropy alloy heterostructure strengthening and toughening mechanical property

Received: 04 July 2022

ZTFLH:

TG146

Fund: National Key Research and Development Program of China(2021YFA1200201);National Natural Science Foundation of China(52071003);National Natural Science Foundation of China(91860202);National Natural Science Foundation of China(51988101);Interdisciplinary Cooperation Project of Beijing Science and Technology Nova Program(Z211100002121170);Beijing Municipal Education Commission Project(PXM2020_014204_000021);Discipline Innovation and Talent Introduction Program in Colleges and Universities(DB18015)

About author: MAO Shengcheng, professor, Tel: (010)67396769, E-mail: scmao@bjut.edu.cn;

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00322 OR https://www.ams.org.cn/EN/Y2022/V58/I11/1441

Fig.1 Comparison of strength and ductility of high-entropy alloys (HEAs) with other conventional alloys and homogeneous HEAs^{[25,34,43,46~48]}

Fig.2 Chemical distribution and mechanical properties of CoCrFeNiMn, CoCrFeNiPd^[38], and HfNbTaTiV^[49] HEAs
(a) atomic-resolution chemical distribution of CoCrFeNiMn alloy
(b) atomic-resolution chemical distribution of CoCrFeNiPd alloy
(c) chemical distribution line scan of CoCrFeNiMn and CoCrFeNiPd alloys
(d) high-angle annular dark field scanning transmission electron microscopy (HAADF-STEM) image of CoCrFeNiPd alloys and lattice strain distribution (Inset is the SAED pattern)
(e) tensile mechanical properties of CoCrFeNiMn, CoCrFeNiPd alloys and compared with other alloys
(f) lattice distortion analysis and compressive properties of HfNbTaTiV alloy

Fig.3 Microstructure and mechanical properties of (HfNbTiZr)₉₈O₂ high-entropy alloy^[56] (O-2 represents (TiZrHfNb)₉₈O₂, and N-2 represents (TiZrHfNb)₉₈N₂)
(a) atom probe tomography image and the O composition profile as a function of the distance to the interface for a selection of particles (left axis) and evolution of the composition of the main constituents relative to their respective matrix composition (right axis) (N_i is the number of the ith atom, while C_i and C_i_{, matrix} are the concentrations of the ith atom in the ordered oxygen complexes (OOCs) and in the matrix, respectively; and the inset shows a close-up of one OOC)
(b) TEM image of O-2 HEA at 8% tensile strain (The red arrows indicate the dipolar walls)
(c) tensile mechanical properties of the (HfNbTiZr)₉₈O₂ alloy and compared alloys (σ_y is the yield strength (squares), σ_UTS is the ultimate strength (diamonds), and ε is the elongation (circles). The inset shows the corresponding strain-hardening response (dσ/dε))

Fig.4 Microstructure and mechanical properties of CoCrNi alloy^[65]
(a, b) energy-filtered dark-field images from different diffuse superlattice peaks; examples showing the same domain contrast are marked with the arrows
(c) energy-filtered diffraction pattern of the region of interest; the red and blue circles indicate the dark-field imaging conditions of Figs.4a and b
(d) magnified view of the boxed part of the dark-field image in Fig.4a, with identified short-range-ordering (SRO) domains marked by the red circles
(e) the histogram of identified domain diameters (d is the average diameter, σ' isthe standard deviation)
(f-i) tensile mechanical properties of the CoCrNi alloys without (f, h) and with (g, i) SRO structure, respectively (DIC—digital image correlation) (Insets in Figs.4f and g are the sample images of the strain distribution during elastic leading, as determined by DIC)

Fig.5 Microstructure and chemical distributions of VCoNi alloy^[39]
(a) HAADF-STEM image and CSRO region size distributions of VCoNi alloy (CSRO—chemical short-range order, FFT—fast Fourier transformation)
(b) atomic resolution energy dispersive spectroscopy (EDS) mapping showing the chemical distribution
(c) lattice strain (ε) distribution of VCoNi alloy before and after tensile tests, respectively (Insets in Fig.5c are a close-up view showing the edge dislocation-induced strain-field)

Fig.6 Microstructure and mechanical properties of (FeCoNi)₈₆Al₇Ti₇ alloy^[34]
(a) TEM image
(b) high-resolution TEM image and corresponding FFT images
(c) tensile properties of (FeCoNi)₈₆Al₇Ti₇ alloy at room temperature, the alloy exhibits ductile dimpled structures without macroscopic necking
(d) work-hardening rate vs true strain curves of (FeCoNi)₈₆Al₇Ti₇ alloy at room temperature (MBIP—microband-induced plasticity)
(e) TEM images of the sample at different tensile strains (MBs—microbands, HDDWs—high density dislocation walls)

Fig.7 Microstructures and mechanical properties of Al_0.5Cr_0.9FeNi_2.5V_0.2and_{HfNbTiV alloys}
(a) HAADF-STEM image and the corresponding FFT images of Al_0.5Cr_0.9FeNi_2.5V_0.2 alloy^[72]
(b) tensile properties of Al_0.5Cr_0.9FeNi_2.5V_0.2 alloy at room temperature (ST—solution-treated)^[72]
(c) HAADF-STEM images and the corresponding SAED patterns of HfNbTiV alloy^[73]
(d) tensile property of HfNbTiV alloy at room temperature^[73] (Insets are SEM images of the fracture surface)

Fig.8 Microstructure and mechanical properties of Ni_32.8Fe_21.9Co_21.9Cr_10.9Al_7.5Ti_5.0 alloy^[74]
(a) TEM image and the size distributions of L1₂ phase and fcc matrix
(b) tensile properties of Ni_32.8Fe_21.9Co_21.9Cr_10.9Al_7.5Ti_5.0 alloy at room temperature (CNL—coherent nanolamellar)
(c) TEM images of Ni_32.8Fe_21.9Co_21.9Cr_10.9Al_7.5Ti_5.0 alloy at different tensile strains

Fig.9 Microstructures of RASP CoCrFeNiMn alloy before and after tensile tests^[84] (RASP—rotationally accelerated shot peening, CG—coarse grain, TD—tensile direction, LD—longitudinal direction)
(a) typical IPF image before tensile test (IPF—inverse pole figure)
(b) image quality map before tensile test
(c) KAM map before tensile test (KAM—kernel average misorientation)
(d) image quality map of the coarse grain sample after tensile test
(e) KAM map of the coarse grain sample after tensile test
(f) image quality map of the RASP sample after tensile tests
(g) KAM map of the RASP sample after tensile test

Fig.10 Hierarchically arranged herringbone microstructure of Fe₂₀Co₂₀Ni₄₁Al₁₉high entropy alloy^[35]
(a-c) conventionally cast eutectic high-entropy alloy (EHEA) serving here as reference material
(a) SEM backscattered electron image
(b) electron backscattering diffraction (EBSD) phase map (left) and IPF map (right)
(c) schematic diagram
(d-i) directionally solidified EHEA with a hierarchical herringbone microstructure (The black arrows in Figs.10d and e indicate the directional solidification (DS) direction; AEC—aligned eutectic colonies, BEC—branched eutectic colonies)
(d) SEM backscatter electron image showing that the microstructure is composed of columnar grains. Grain boundaries are marked by black dashed lines
(e) enlarged EBSD phase and IPF maps showing the columnar grain consisting of AEC and BEC. Black solid and dashed lines mark grain and colony boundaries, respectively
(f, i) schematic diagram of herringbone structure and its formation principle, respectively
(g) HAADF-STEM image and related SAED patterns of B2 and L1₂ phases. The HAADF-STEM image shows clean dual-phase lamellae without evidence of nanoprecipitates or other phases, as is also indicated in Fig.10f
(h) synchrotron high-energy X-ray diffraction (SHE-XRD) of B2 and L1₂ phases

Fig.11 Microstructure and hetero-deformation induced (HDI) hardening of CoCrNi alloy^[46]
(a) EBSD and TEM image of CoCrNi alloy (LAGB—low angle grain boundary, HAGB—high-angle grain boundary, TB—twin boundary, UFG—ultrafine-grained)
(b) true stress-strain curves during LUR (loading-unloading-reloading) tests at 298 K and 77 K. Hysteresis loops at the maximum uniform strain. Comparison of HDI hardening with the total strain hardening in the CoCrNi alloy at 298 K and 77 K (ε_rp—reverse plastic strain, σ_f—flow stress, σ_0.2—yield stress, σ_b—back stress, σ_{b, 0.2}—back stress at yielding)
(c) TEM image of the deformed CoCrNi alloy (NG—nanograin)

Fig.12 Gradient microstructures of the RASP treated Co_21.5Cr_21.5Fe_21.5Mn_21.5Ni₁₄ alloy^[42]
(a) schematic of the grain size gradient through the plate thickness
(b-d) EBSD images of the alloy at different depths from the surface
(e-g) TEM images of twin structures in regions (I), (II) and (III) (The insets are SAED patterns from each region)
(h) a high-resolution HAADF-STEM image of the deformation twins in region (I)
(i) variation of the average grain size through the plate thickness
(j) variation of the average thickness of deformation twins through the plate thickness

Fig.13 Tensile properties for coarse grain (CG), SMAT and SMAT-aged samples^[92] (SMAT—surface mechanical attrition treatment)
(a) engineering stress-strain curves
(b) hardening rate and true stress as a function of true strain

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