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Effect of multi-component carbides on the mechanical behavior of a multi-element alloy
Materials Science & Engineering A 758 (2019) 99–102
Contents lists available at ScienceDirect
Materials Science & Engineering A journal homepage: www.elsevier.com/locate/msea
Short communication
Effect of multi-component carbides on the mechanical behavior of a multielement alloy
T
Rui Zhou, Mou Li, Hong Wu∗∗, Bin Liu, Yong Liu∗ State Key Laboratory of Powder Metallurgy, Central South University, Changsha, 410083, PR China
A R T I C LE I N FO
A B S T R A C T
Keywords: Multi-element entropy alloy Multi-component carbide Microstructure Mechanical properties
A (Fe40Co50Ni10)94(TaNbZrVC2)6 multi-element alloy (MEA) was developed. The alloy is composed of a multicomponent carbide (MCC) phase and two BCC solid solution phases. The compressive yield strength is about 1373 MPa, while the compressive plasticity is over 60% at room temperature, which is mainly contributed by the MCC strengthening phase.
1. Introduction Multi-element alloys (MEAs) as a new type of alloys are composed of several alloying elements in the range of 5–35 at.% [1], and have caught a considerable interests [2]. With complicated compositions, most MEAs still have a monophase microstructure [3], and the alloys have shown attractive properties such as excellent ductility, good oxidation and corrosion resistance [4–6]. However, for structural application, their yield strengths are generally insufficient [4]. The introduction of carbides into MEAs has been an effective way to improve the mechanical properties. For example, the formation of M23C6- and M7C3-type carbides in CoCrFeNiMnCx increased significantly the hardness [7]. A pronounced increment of tensile strength was observed in CoCrFeMnNiCx with the carbon content above 1.0 at. %, because the presence of fine carbides can induce particle strengthening [8]. Furthermore, the precipitation of MC-type carbides led to the improvement of the compressive strength in Mo0.5NbHf0.5ZrTiCx [9], Al0.15CoCrCuFeNiTixC and (FeCoCrNi)1-x(WC)x [10,11]. But, the widespread application of carbides hardening is limited by poor ductility in hardened alloys, which is related to the brittle nature of conventional carbides. Multi-component carbides (MCCs), containing several principle carbide components with the equiatomic or near-equiatomic ratios, have been reported [12].Compared to conventional monocarbides, MCCs exhibit better mechanical properties, such as a higher hardness, elastic modulus and toughness. For instance, compared with singleelement carbides, (Hf,Zr,Ta,Nb,Ti)C has higher elastic modulus and hardness [12]. (Hf,Ta,Zr,Nb)C MCCs also exhibits a higher modulus and
∗
hardness than the value of prediction by using the mixing rule for each carbides [13]. In this work, a (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy was designed, in order to evaluate the effect of MCCs on the mechanical behavior of MEA. 2. Material and methods The MEA with a composition of (Fe40Co50Ni10)94(TaNbZrVC2)6 was produced by vacuum arc melting. The purity of raw metals (Fe, Co, Ni, Ta, Zr, V, Nb) and graphite was over 99.9 wt%. The selection of refractory metal elements was according to the ternary phase diagram (shown in Fig. 1). There was complete diffusion of carbides at high temperature, and the multi-component carbide may form during the arc melting processing. For promoting chemical homogeneity, the ingot was remelted over 5 times in argon atmosphere. The microstructures were characterized by using scanning electron microscope (SEM, FEI Helios Nanolab G3 UC) equipped with an electron backscatter diffraction (EBSD) analyzer. The chemical composition was investigated by using energy dispersive spectrometry (EDX). The samples with a diameter of 6 mm were machined by wire-electrode cutting. The microhardness of different phases was measured by a nanoindenter (UNHTL + MCT, Switzerland) with a load of 10 mN for 15s. Every phase was tested 5 times, and the results were averaged. Compressive tests were carried out at room temperature employing an Instron 3369 machine with a strain rate of 5 × 10−3/s.
Corresponding authors. Corresponding author. E-mail addresses: [email protected] (H. Wu), [email protected] (Y. Liu).
∗∗
https://doi.org/10.1016/j.msea.2019.04.106 Received 7 March 2019; Received in revised form 26 April 2019; Accepted 27 April 2019 Available online 29 April 2019 0921-5093/ © 2019 Elsevier B.V. All rights reserved.
Materials Science & Engineering A 758 (2019) 99–102
R. Zhou, et al.
Fig. 1. Vertical section of ternary phase diagram.
3. Results and discussion
HV) are both harder than matrix phase (658 HV). The movement of dislocations will be impeded at the phase interfaces, leading to an increment of yield strength. Monocarbides hardened alloys usually have poor ductility. In (FeCoNi)86–Al7Ti7 multi-element alloy, (NiFeCo)3(AlTiFe) multi-component intermetallic compound is substantially stronger and more ductile than the simple Ni3Al intermetallic compound [16]. Similarly for ordered monocarbides, alloying with other alloys may decrease the ordering energy and increase the intrinsic toughness [12]. In Fe–18Ni3Al4Mo0.8Nb0.08C0.01B maraging steel, NiAl alloyed with Fe element formed Ni(Al,Fe) intermetallic compound, which reduced lattice misfits between the bcc matrix and Ni(Al,Fe) precipitates. Low lattice misfits minimized nucleation barrier and stabilized the Ni(Al,Fe) precipitates with a small size [17]. Likewise, the complex composition of MCC may decrease the lattice misfit, and make it difficult to grow in the matrix [16]. The MCC is stabilized at the fine scale and distributes uniformly without heterogeneous coarsening. During the plastic deformation, the fine MCC can decrease the tressstrain concentrations at phase interfaces, and also impede the propagation of micro-cracks [16].
Fig. 2 shows the microstructures and chemical profiles of (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy. The chemical compositions of the MEA composite in different regions are listed in Table 1. But, the content of carbon measured by EDS is not accurate, due to its light atomic weight. It is clear that the MEA consists of three different phases as shown in Table 1. The bright phase (A) is rich in Ta, Zr and C, and also contains other elements. It indicates that phase A is a multi-component carbide phase. The gray phase (B) is rich in Co and contains other elements. Due to the low content of carbon, phase B can be seen as a solid solution phase. The black matrix phase (C) is also rich in Co, and Fe, but there are few refractory elements. The carbide phase in a size of several microns is embedded in the matrix phase, and the solid solution phase forms near the carbide phase. In order to identify the mechanical properties of different phases, the nanoindentation was used. The carbide phase has the highest mirohardness of 2346 HV, the solid solution phase and the matrix phase are about 1025 HV and 658 HV, respectively. Fig. 3 demonstrates EBSD analyses of the (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy. As shown in Fig. 3 (a), the grains with an average size of 2.9 μm are of random orientations. The precipitation of fine carbides can shorten the processing of recrystallization by particle stimulated nucleation, leading to a grain refinement [14]. Fig. 3 (b) shows the area fraction of different phases, which present different crystal structures. The region marked as red shows that the MCC phase has a FCC structure. The green region represents the solid solution phase and matrix phase, which are both BCC structures. Fig. 4 (a) shows the compressive engineering stress-strain curves of the MEA. The yield strength is 1373 MPa, and the compressive plasticity is over 60%. Compared with the FeCoNi alloy [15], the introduction of MCCs has a significant effect on the yield strength. Furthermore, the (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy kept well in shape after compression. Fig. 4 (b) presents a comparison of compressive properties of some HEAs at room temperature. The present alloy is located at the upper-right position, indicating outstanding mechanical properties. The high yield strength of the alloy is mainly due to precipitation hardening. As the MCC phase (2346 HV) and solid solution phase (1025
4. Conclusions To summarize, a new (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite strengthened by MCC was successfully developed. The MEA composite consists of two solid solution phases and MCC phase. The solid solution phases possess BCC structures, and MCC phase has a FCC structure. The fine complex-compositional MCC is responsible for strengthening the FeCoNi alloy matrix while maintaining high compressive plasticity. 5. Originality statement I write on behalf of myself and all co-authors to confirm that the results reported in the manuscript are original and neither the entire work, nor any of its parts have been previously published. The authors confirm that the article has not been submitted to peer review, nor has been accepted for publishing in another journal. The author(s) confirms that the research in their work is original, and that all the data given in 100
Materials Science & Engineering A 758 (2019) 99–102
R. Zhou, et al.
Fig. 2. Microstructures and elemental distribution of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite.
the article are real and authentic. If necessary, the article can be recalled, and errors corrected.
Table 1 Chemical compositions of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite. Element (at%)
Fe
Co
Ni
Ta
Zr
Nb
V
C
Phase A Phase B Phase C
8.61 19.97 39.81
8.33 43.87 43.99
3.42 12.86 9.00
27.34 3.98 0.31
17.26 8.68 0.01
4.28 2.34 0.20
3.39 1.11 1.57
27.37 7.20 5.11
Acknowledgment The authors would like to appreciate the support from the National Natural Science Foundation of China under grant No. 51671217.
Fig. 3. EBSD analyses of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite; (a) Inverse pole figure (IPF), (b) phase figure. 101
Materials Science & Engineering A 758 (2019) 99–102
R. Zhou, et al.
Fig. 4. (a) Typical engineering stress-strain curves of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite; (b) Summary of compressive properties of HEA [18–26].
References
high-entropy ultra-high temperature carbides, Sci. Rep. 8 (1) (2018) 8609. [14] Z.G. Zhu, Y.F. Sun, F.L. Ng, M.H. Goh, P.K. Liaw, H. Fujii, Q.B. Nguyen, Y. Xu, C.H. Shek, S.M.L. Nai, J. Wei, Friction-stir welding of a ductile high entropy alloy: microstructural evolution and weld strength, Mater. Sci. Eng., A 711 (2018) 524–532. [15] P. Li, A. Wang, C.T. Liu, Composition dependence of structure, physical and mechanical properties of FeCoNi(MnAl)x high entropy alloys, Intermetallics 87 (2017) 21–26. [16] T. Yang, Y.L. Zhao, Y. Tong, Z.B. Jiao, J. Wei, J.X. Cai, X.D. Han, D. Chen, A. Hu, J.J. Kai, K. Lu, Y. Liu, C.T. Liu, Multicomponent intermetallic nanoparticles and superb mechanical behaviors of complex alloys, Science 362 (6417) (2018) 933. [17] S. Jiang, H. Wang, Y. Wu, X. Liu, H. Chen, M. Yao, B. Gault, D. Ponge, D. Raabe, A. Hirata, M. Chen, Y. Wang, Z. Lu, Ultrastrong steel via minimal lattice misfit and high-density nanoprecipitation, Nature 544 (2017) 460. [18] K.B. Zhang, Z.Y. Fu, J.Y. Zhang, W.M. Wang, H. Wang, Y.C. Wang, Q.J. Zhang, J. Shi, Microstructure and mechanical properties of CoCrFeNiTiAlx high-entropy alloys, Mater. Sci. Eng., A 508 (1) (2009) 214–219. [19] O.N. Senkov, G.B. Wilks, J.M. Scott, D.B. Miracle, Mechanical properties of Nb25Mo25Ta25W25 and V20Nb20Mo20Ta20W20 refractory high entropy alloys, Intermetallics 19 (5) (2011) 698–706. [20] B.S. Li, Y.P. Wang, M.X. Ren, C. Yang, H.Z. Fu, Effects of Mn, Ti and V on the microstructure and properties of AlCrFeCoNiCu high entropy alloy, Mater. Sci. Eng., A 498 (1) (2008) 482–486. [21] X.F. Wang, Y. Zhang, Y. Qiao, G.L. Chen, Novel microstructure and properties of multicomponent CoCrCuFeNiTix alloys, Intermetallics 15 (3) (2007) 357–362. [22] Y. Cao, Y. Liu, B. Liu, W. Zhang, Precipitation behavior during hot deformation of powder metallurgy Ti-Nb-Ta-Zr-Al high entropy alloys, Intermetallics 100 (2018) 95–103. [23] T. Li, B. Liu, Y. Liu, W. Guo, A. Fu, L. Li, N. Yan, Q. Fang, Microstructure and mechanical properties of particulate reinforced NbMoCrTiAl high entropy based composite, Entropy 20 (7) (2018). [24] O.N. Senkov, S.V. Senkova, D.B. Miracle, C. Woodward, Mechanical properties of low-density, refractory multi-principal element alloys of the Cr–Nb–Ti–V–Zr system, Mater. Sci. Eng., A 565 (2013) 51–62. [25] X. Yang, Y. Zhang, P.K. Liaw, Microstructure and compressive properties of NbTiVTaAlx high entropy alloys, Procedia Engineering 36 (2012) 292–298. [26] O.N. Senkov, S.V. Senkova, C. Woodward, Effect of aluminum on the microstructure and properties of two refractory high-entropy alloys, Acta Mater. 68 (2014) 214–228.
[1] Y. Dong, X. Gao, Y. Lu, T. Wang, T. Li, A multi-component AlCrFe2Ni2 alloy with excellent mechanical properties, Mater. Lett. 169 (2016) 62–64. [2] J.W. Bae, J.B. Seol, J. Moon, S.S. Sohn, M.J. Jang, H.Y. Um, B.-J. Lee, H.S. Kim, Exceptional phase-transformation strengthening of ferrous medium-entropy alloys at cryogenic temperatures, Acta Mater. 161 (2018) 388–399. [3] Y. Liu, J. Wang, Q. Fang, B. Liu, Y. Wu, S. Chen, Preparation of superfine-grained high entropy alloy by spark plasma sintering gas atomized powder, Intermetallics 68 (2016) 16–22. [4] I. Moravcik, J. Cizek, Z. Kovacova, J. Nejezchlebova, M. Kitzmantel, E. Neubauer, I. Kubena, V. Hornik, I. Dlouhy, Mechanical and microstructural characterization of powder metallurgy CoCrNi medium entropy alloy, Mater. Sci. Eng., A 701 (2017) 370–380. [5] W. Kai, F.P. Cheng, C.Y. Liao, C.C. Li, R.T. Huang, J.J. Kai, The oxidation behavior of the quinary FeCoNiCrSix high-entropy alloys, Mater. Chem. Phys. 210 (2018) 362–369. [6] H. Feng, H. Li, X. Wu, Z. Jiang, S. Zhao, T. Zhang, D. Xu, S. Zhang, H. Zhu, B. Zhang, M. Yang, Effect of nitrogen on corrosion behaviour of a novel high nitrogen medium-entropy alloy CrCoNiN manufactured by pressurized metallurgy, J. Mater. Sci. Technol. 34 (10) (2018) 1781–1790. [7] N.D. Stepanov, N.Y. Yurchenko, M.A. Tikhonovsky, G.A. Salishchev, Effect of carbon content and annealing on structure and hardness of the CoCrFeNiMn-based high entropy alloys, J. Alloy. Comp. 687 (2016) 59–71. [8] J.Y. Ko, S.I. Hong, Microstructural evolution and mechanical performance of carbon-containing CoCrFeMnNi-C high entropy alloys, J. Alloy. Comp. 743 (2018) 115–125. [9] N.N. Guo, L. Wang, L.S. Luo, X.Z. Li, R.R. Chen, Y.Q. Su, J.J. Guo, H.Z. Fu, Microstructure and mechanical properties of in-situ MC-carbide particulates-reinforced refractory high-entropy Mo0.5NbHf0.5ZrTi matrix alloy composite, Intermetallics 69 (2016) 74–77. [10] R. Zhou, G. Chen, B. Liu, J. Wang, L. Han, Y. Liu, Microstructures and wear behaviour of (FeCoCrNi)1-x(WC)x high entropy alloy composites, Int. J. Refract. Metals Hard Mater. 75 (2018) 56–62. [11] S. Nam, M.J. Kim, J.Y. Hwang, H. Choi, Strengthening of Al0.15CoCrCuFeNiTix–C (x = 0, 1, 2) high-entropy alloys by grain refinement and using nanoscale carbides via powder metallurgical route, J. Alloy. Comp. 762 (2018) 29–37. [12] L. Feng, W.G. Fahrenholtz, G.E. Hilmas, Y. Zhou, Synthesis of single-phase highentropy carbide powders, Scripta Mater. 162 (2019) 90–93. [13] E. Castle, T. Csanádi, S. Grasso, J. Dusza, M. Reece, Processing and properties of
102
Contents lists available at ScienceDirect
Materials Science & Engineering A journal homepage: www.elsevier.com/locate/msea
Short communication
Effect of multi-component carbides on the mechanical behavior of a multielement alloy
T
Rui Zhou, Mou Li, Hong Wu∗∗, Bin Liu, Yong Liu∗ State Key Laboratory of Powder Metallurgy, Central South University, Changsha, 410083, PR China
A R T I C LE I N FO
A B S T R A C T
Keywords: Multi-element entropy alloy Multi-component carbide Microstructure Mechanical properties
A (Fe40Co50Ni10)94(TaNbZrVC2)6 multi-element alloy (MEA) was developed. The alloy is composed of a multicomponent carbide (MCC) phase and two BCC solid solution phases. The compressive yield strength is about 1373 MPa, while the compressive plasticity is over 60% at room temperature, which is mainly contributed by the MCC strengthening phase.
1. Introduction Multi-element alloys (MEAs) as a new type of alloys are composed of several alloying elements in the range of 5–35 at.% [1], and have caught a considerable interests [2]. With complicated compositions, most MEAs still have a monophase microstructure [3], and the alloys have shown attractive properties such as excellent ductility, good oxidation and corrosion resistance [4–6]. However, for structural application, their yield strengths are generally insufficient [4]. The introduction of carbides into MEAs has been an effective way to improve the mechanical properties. For example, the formation of M23C6- and M7C3-type carbides in CoCrFeNiMnCx increased significantly the hardness [7]. A pronounced increment of tensile strength was observed in CoCrFeMnNiCx with the carbon content above 1.0 at. %, because the presence of fine carbides can induce particle strengthening [8]. Furthermore, the precipitation of MC-type carbides led to the improvement of the compressive strength in Mo0.5NbHf0.5ZrTiCx [9], Al0.15CoCrCuFeNiTixC and (FeCoCrNi)1-x(WC)x [10,11]. But, the widespread application of carbides hardening is limited by poor ductility in hardened alloys, which is related to the brittle nature of conventional carbides. Multi-component carbides (MCCs), containing several principle carbide components with the equiatomic or near-equiatomic ratios, have been reported [12].Compared to conventional monocarbides, MCCs exhibit better mechanical properties, such as a higher hardness, elastic modulus and toughness. For instance, compared with singleelement carbides, (Hf,Zr,Ta,Nb,Ti)C has higher elastic modulus and hardness [12]. (Hf,Ta,Zr,Nb)C MCCs also exhibits a higher modulus and
∗
hardness than the value of prediction by using the mixing rule for each carbides [13]. In this work, a (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy was designed, in order to evaluate the effect of MCCs on the mechanical behavior of MEA. 2. Material and methods The MEA with a composition of (Fe40Co50Ni10)94(TaNbZrVC2)6 was produced by vacuum arc melting. The purity of raw metals (Fe, Co, Ni, Ta, Zr, V, Nb) and graphite was over 99.9 wt%. The selection of refractory metal elements was according to the ternary phase diagram (shown in Fig. 1). There was complete diffusion of carbides at high temperature, and the multi-component carbide may form during the arc melting processing. For promoting chemical homogeneity, the ingot was remelted over 5 times in argon atmosphere. The microstructures were characterized by using scanning electron microscope (SEM, FEI Helios Nanolab G3 UC) equipped with an electron backscatter diffraction (EBSD) analyzer. The chemical composition was investigated by using energy dispersive spectrometry (EDX). The samples with a diameter of 6 mm were machined by wire-electrode cutting. The microhardness of different phases was measured by a nanoindenter (UNHTL + MCT, Switzerland) with a load of 10 mN for 15s. Every phase was tested 5 times, and the results were averaged. Compressive tests were carried out at room temperature employing an Instron 3369 machine with a strain rate of 5 × 10−3/s.
Corresponding authors. Corresponding author. E-mail addresses: [email protected] (H. Wu), [email protected] (Y. Liu).
∗∗
https://doi.org/10.1016/j.msea.2019.04.106 Received 7 March 2019; Received in revised form 26 April 2019; Accepted 27 April 2019 Available online 29 April 2019 0921-5093/ © 2019 Elsevier B.V. All rights reserved.
Materials Science & Engineering A 758 (2019) 99–102
R. Zhou, et al.
Fig. 1. Vertical section of ternary phase diagram.
3. Results and discussion
HV) are both harder than matrix phase (658 HV). The movement of dislocations will be impeded at the phase interfaces, leading to an increment of yield strength. Monocarbides hardened alloys usually have poor ductility. In (FeCoNi)86–Al7Ti7 multi-element alloy, (NiFeCo)3(AlTiFe) multi-component intermetallic compound is substantially stronger and more ductile than the simple Ni3Al intermetallic compound [16]. Similarly for ordered monocarbides, alloying with other alloys may decrease the ordering energy and increase the intrinsic toughness [12]. In Fe–18Ni3Al4Mo0.8Nb0.08C0.01B maraging steel, NiAl alloyed with Fe element formed Ni(Al,Fe) intermetallic compound, which reduced lattice misfits between the bcc matrix and Ni(Al,Fe) precipitates. Low lattice misfits minimized nucleation barrier and stabilized the Ni(Al,Fe) precipitates with a small size [17]. Likewise, the complex composition of MCC may decrease the lattice misfit, and make it difficult to grow in the matrix [16]. The MCC is stabilized at the fine scale and distributes uniformly without heterogeneous coarsening. During the plastic deformation, the fine MCC can decrease the tressstrain concentrations at phase interfaces, and also impede the propagation of micro-cracks [16].
Fig. 2 shows the microstructures and chemical profiles of (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy. The chemical compositions of the MEA composite in different regions are listed in Table 1. But, the content of carbon measured by EDS is not accurate, due to its light atomic weight. It is clear that the MEA consists of three different phases as shown in Table 1. The bright phase (A) is rich in Ta, Zr and C, and also contains other elements. It indicates that phase A is a multi-component carbide phase. The gray phase (B) is rich in Co and contains other elements. Due to the low content of carbon, phase B can be seen as a solid solution phase. The black matrix phase (C) is also rich in Co, and Fe, but there are few refractory elements. The carbide phase in a size of several microns is embedded in the matrix phase, and the solid solution phase forms near the carbide phase. In order to identify the mechanical properties of different phases, the nanoindentation was used. The carbide phase has the highest mirohardness of 2346 HV, the solid solution phase and the matrix phase are about 1025 HV and 658 HV, respectively. Fig. 3 demonstrates EBSD analyses of the (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy. As shown in Fig. 3 (a), the grains with an average size of 2.9 μm are of random orientations. The precipitation of fine carbides can shorten the processing of recrystallization by particle stimulated nucleation, leading to a grain refinement [14]. Fig. 3 (b) shows the area fraction of different phases, which present different crystal structures. The region marked as red shows that the MCC phase has a FCC structure. The green region represents the solid solution phase and matrix phase, which are both BCC structures. Fig. 4 (a) shows the compressive engineering stress-strain curves of the MEA. The yield strength is 1373 MPa, and the compressive plasticity is over 60%. Compared with the FeCoNi alloy [15], the introduction of MCCs has a significant effect on the yield strength. Furthermore, the (Fe40Co50Ni10)94(TaNbZrVC2)6 alloy kept well in shape after compression. Fig. 4 (b) presents a comparison of compressive properties of some HEAs at room temperature. The present alloy is located at the upper-right position, indicating outstanding mechanical properties. The high yield strength of the alloy is mainly due to precipitation hardening. As the MCC phase (2346 HV) and solid solution phase (1025
4. Conclusions To summarize, a new (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite strengthened by MCC was successfully developed. The MEA composite consists of two solid solution phases and MCC phase. The solid solution phases possess BCC structures, and MCC phase has a FCC structure. The fine complex-compositional MCC is responsible for strengthening the FeCoNi alloy matrix while maintaining high compressive plasticity. 5. Originality statement I write on behalf of myself and all co-authors to confirm that the results reported in the manuscript are original and neither the entire work, nor any of its parts have been previously published. The authors confirm that the article has not been submitted to peer review, nor has been accepted for publishing in another journal. The author(s) confirms that the research in their work is original, and that all the data given in 100
Materials Science & Engineering A 758 (2019) 99–102
R. Zhou, et al.
Fig. 2. Microstructures and elemental distribution of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite.
the article are real and authentic. If necessary, the article can be recalled, and errors corrected.
Table 1 Chemical compositions of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite. Element (at%)
Fe
Co
Ni
Ta
Zr
Nb
V
C
Phase A Phase B Phase C
8.61 19.97 39.81
8.33 43.87 43.99
3.42 12.86 9.00
27.34 3.98 0.31
17.26 8.68 0.01
4.28 2.34 0.20
3.39 1.11 1.57
27.37 7.20 5.11
Acknowledgment The authors would like to appreciate the support from the National Natural Science Foundation of China under grant No. 51671217.
Fig. 3. EBSD analyses of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite; (a) Inverse pole figure (IPF), (b) phase figure. 101
Materials Science & Engineering A 758 (2019) 99–102
R. Zhou, et al.
Fig. 4. (a) Typical engineering stress-strain curves of (Fe40Co50Ni10)94(TaNbZrVC2)6 MEA composite; (b) Summary of compressive properties of HEA [18–26].
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