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Physical property and material mechanical performance of nanocrystalline (single crystal, polycrystalline) CoNiCrFeMn alloy can be known well through an in-depth understanding of the micro-evaluation behaviour of micro dislocation, so that it can better be used in defense fields, such as nuclear reactor cladding tubes, aircraft engines, jet turbine blades and others. In this paper we propose to study the correlation between micro-structure evolution and mechanical properties for nanocrystalline CoNiCrFeMn high entropy alloy. The force driven material deformation behaviors and mechanical properties of nanocrystalline alloy and Ni material are studied by using the nanoindentation method, and effects of temperature on the mechanical properties and micro-structure evolution are compared as well. Research results show that the mechanical properties (maximum load, hardness, Young’s modulus and contact stiffness) of single crystal alloy are superior to those of single crystal Ni, which mainly stems from the fact that the single crystal high entropy alloy with a drum-shape structure is produced under loading period, and the slip and expansion of dislocations in the bulge structure are blocked. At a low temperature (5 K), the maximum load, hardness, Young's modulus and contact stiffness of polycrystalline Ni decrease by 28.9%, 20.27%, 32.61% and 36.4% respectively in comparison with those of single crystal Ni. The maximum load, hardness, Young's modulus and contact stiffness of polycrystalline CoNiCrFeMn material decrease by 21.74%, 23.61%, 23.79% and 22.90% respectively with respect to those of single CoNiCrFeMn high entropy alloy. In addition, the mechanical properties of polycrystalline alloy are more sensitive to temperature than those of single crystal high entropy alloy, whose mechanical properties decrease approximately linearly with temperature increasing. For polycrystalline CoNiCrFeMn and Ni material, the grain boundary is not merely the origin region of dislocation breeding, expansion and reproduction, but also the concentration region of defect initiation, crack expansion and failure. Its mechanical properties are weaker than those of single crystal materials due to micro-structure evolution of grain boundaries driven from stress concentration and defects existence.
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Keywords:
- CoNiCrFeMn high entropy alloy /
- nano indentation /
- temperature response /
- mechanical performance /
- molecular simulation
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Google Scholar
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Google Scholar
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Google Scholar
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Google Scholar
[5] Tripathi P K, Chiu Y C, Bhowmick S 2021 J. Nanomater 11 2111
Google Scholar
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[11] Gou S Y, Li S C, Hu H L, Fang Y T, Liu J B, Dong W P, Wang H T 2021 Mater. Res. Lett 9 437
Google Scholar
[12] Li X Y, Sun S J, Zou Y 2022 Mater. Res. Lett 10 385
Google Scholar
[13] Zhao W R, Han J K, Kuzminova Y O 2021 Mater. Sci. Eng. , A 807 140898
Google Scholar
[14] Laplanche G, Kostka K, Horst O M, Eggeler G, George E P 2016 Acta Mater 118 152
Google Scholar
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Google Scholar
[16] He J Y, Zhu C, Zhou D Q 2014 Intermetallics 55 9
Google Scholar
[17] Otto F, Dlouhy A, Somsen C, Bei H, Eggeler G, George E P 2013 Acta Mater 61 5743
Google Scholar
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Google Scholar
[20] Guo J, Chen J J, Wang Y Q 2020 Ceram. Int 46 12686
Google Scholar
[21] Xiang H G, Li H T, Fu T 2017 Acta Materialia 138 131
Google Scholar
[22] Xiang H G, Li H T, Fu T, Huang C, Peng X H 2017 Acta Mater. 138 131
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Google Scholar
[24] 董斌, 王雪梅, 朱子亮 2020 原子与分子物理学报 37 591
Dong B, Wang X M, Zhu Z L 2020 J. At. Mol. Phys. 37 591
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Google Scholar
[26] Foiles, S M, Baskes, M I, Daw M S 1988 Phys. Rev. B 33 7983
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图 1 纳米晶Ni和纳米晶CoNiCrFeMn高熵合金的四种待测样品物理模型 (a) 单晶Ni模型; (b) 单晶CoNiCrFeMn高熵合金模型; (c) 多晶Ni模型; (d) 多晶CoNiCrFeMn高熵合金模型; (e) CoNiCrFeMn高熵合金五种元素均匀分布
Figure 1. Atomic nanoindentation simulation of physical model for single crystal high entropy alloy CoNiCrFeMn and single crystal Ni: (a) Single crystal Ni; (b) single crystal CoNiCrFeMn high entropy alloy; (c) polycrystal Ni; (d) polycrystal CoNiCrFeMn high entropy alloy; (e) uniform distributions of five elements in CoNiCrFeMn high entropy alloy.
图 2 四种待测样品载荷与位移曲线的温度响应 (a) 单晶Ni; (b) 多晶Ni; (c) 单晶CoNiCrFeMn高熵合金; (d) 多晶高熵合金
Figure 2. Temperature effects on curves of load versus indentation depth at nanoindentation simulation for four samples: (a) Single crystal Ni; (b) polycrystal Ni; (c) single crystal CoNiCrFeMn; (d) polycrystal CoNiCrFeMn.
图 3 极端低温5 K的纳米晶CoNiCrFeMn高熵合金和纳米晶Ni上表面受载诱导的剪切变形 (a), (b) 加载过程; (c) 卸载过程
Figure 3. Atomic snapshoot of shear strain deformation induced by maximum loads at nanoindentation test ((a), (b) loading and (c) unloading process) during extremely low temperature 5 K for single crystal and polycrystal material (Ni and CoNiCrFeMn ) that can be seen from XY horizontal plane perspective view.
图 4 纳米晶Ni、纳米晶CoNiCrFeMn高熵合金力学性能受温度影响的变化
Figure 4. Temperature response of the mechanical properties of nanocrystalline Ni and nanocrystalline CoNiCrFeMn high entropy alloys
图 5 最大压深载荷时的纳米晶Ni(a), (b)、纳米晶CoNiCrFeMn高熵合金(c), (d)受极端高低温(5—1100 K)影响的表面形貌特征; 相应地接触面积 (e)纳米晶Ni; (f)纳米晶CoNiCrFeMn高熵合金
Figure 5. Surface topography snapshot of nanocrystalline nickel and nanocrystalline high entropy alloys at maximum loading moment for testing four specimen with ambient temperature (5 K~1100 K)variations as shown in Fig. 5(a)-(d), among then, the locked position of virtual indenter was indicated with black dotted line. In addition, whose corresponding contact area was statisticed and quantified at Fig. 5(e) and 5(f).
图 6 纳米晶Ni (a), (b)和纳米晶CoNiCrFeMn高熵合金(c), (d)极端低温下的微结构演化特征
Figure 6. Micro-structure evolution characteristics of nanocrystalline nickel (a), (b) and nanocrystalline CoNiCrFeMn (c), (d) high Entropy alloy at extremely low temperature.
图 7 纳米晶Ni(a)和纳米晶CoNiCrFeMn高熵合金(b)极端高低温下的微结构演化特征
Figure 7. Micro-structure evolution characteristics of nanocrystalline Ni (a) and nanocrystalline CoNiCrFeMn high entropy alloys (b) at extremely high and low temperatures.
图 8 纳米晶Ni和纳米晶CoNiCrFeMn高熵合金材料内部的位错类型分布与量化统计 (a) 单晶Ni和CoNiCrFeMn; (b) 多晶Ni和CoNiCrFeMn
Figure 8. Distribution characteristics and data statistics of dislocation types in nanocrystalline Ni and nanocrystalline CoNiCrFeMn high entropy alloys: (a) Single crystal Ni and CoNiCrFeMn; (b) polycrystal Ni and CoNiCrFeMn.
图 9 极端低温5 K下的纳米晶Ni和CoNiCrFeMn高熵合金的应力分布状态 (a) 加载下多晶Ni; (b) 加载下多晶CoNiCrFeMn; (c) 卸载后单晶Ni和CoNiCrFeMn; (d) 卸载后多晶Ni和CoNiCrFeMn
Figure 9. Atomic stress distribution of nanocrystalline Ni and nanocrystalline CoNiCrFeMn high entropy alloys under extremely low temperature with 5 K: (a) Polycrystal Ni under loading; (b) polycrystal CoNiCrFeMn under loading; (c) single crystal Ni and CoNiCrFeMn under unloading; (d) polycrystal Ni and CoNiCrFeMn under unloading.
图 10 加载期的纳米晶Ni和纳米晶CoNiCrFeMn高熵合金的应力分布受温度响应的影响 (a) 单晶Ni; (b) 多晶Ni; (c) 单晶CoNiCrFeMn; (d) 多晶CoNiCrFeMn
Figure 10. Atomic stress distribution of nanocrystalline Ni and nanocrystalline CoNiCrFeMn high entropy alloys effected by temperature variations at loading process: (a) Single crystal Ni; (b) polycrystal Ni; (c) single crystal CoNiCrFeMn; (d) polycrystal CoNiCrFeMn.
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[1] Fu W J, Huang Y J, Sun J F, Ngan A H W 2022 Int. J. Plast 154 103296
Google Scholar
[2] Tran N D, Saengdeejing A, Suzuki K, Miura H, Chen Y 2021 J. Phase Equilib. Diffus 42 606
Google Scholar
[3] Gorban V F, Andreev A A, Chikryzhov A M, Karpets M. V, Krapivka N A, Kovteba D V 2019 Powder Metall 58 58
Google Scholar
[4] Zheng T F, Lü J C, Wu Y 2021 Appl. Phys. Lett 119 201907
Google Scholar
[5] Tripathi P K, Chiu Y C, Bhowmick S 2021 J. Nanomater 11 2111
Google Scholar
[6] Li C, Xue Y, Hua M, Cao T Q, Ma L L, Wang L 2016 Mater. Des 90 601
Google Scholar
[7] Wang F J, Zhang Y, Chen G L 2009 J. Alloys Compd 478 321
Google Scholar
[8] Sun S J, Tian Y Z, Lin H R, Yang H J, Dong X G, Wang Y H, Zhang Z F 2018 Mater. Sci. Eng. , A 712 603
Google Scholar
[9] Juan C C, Tsai M H, Tsai C W, Hsu W L, Lin C M, Chen S K, Lin S J, Yeh J W 2016 Mater. Lett 184 200
Google Scholar
[10] Seol J B, Bae J W, Li Z, Han J C, Kim J G, Raabe D, Kim H S 2018 Acta Mater 151 366
Google Scholar
[11] Gou S Y, Li S C, Hu H L, Fang Y T, Liu J B, Dong W P, Wang H T 2021 Mater. Res. Lett 9 437
Google Scholar
[12] Li X Y, Sun S J, Zou Y 2022 Mater. Res. Lett 10 385
Google Scholar
[13] Zhao W R, Han J K, Kuzminova Y O 2021 Mater. Sci. Eng. , A 807 140898
Google Scholar
[14] Laplanche G, Kostka K, Horst O M, Eggeler G, George E P 2016 Acta Mater 118 152
Google Scholar
[15] Schuh B, Mendez-Martin F, Völker B, George E P, Clemens H, Pippan R 2015 Acta Mater 96 258
Google Scholar
[16] He J Y, Zhu C, Zhou D Q 2014 Intermetallics 55 9
Google Scholar
[17] Otto F, Dlouhy A, Somsen C, Bei H, Eggeler G, George E P 2013 Acta Mater 61 5743
Google Scholar
[18] Yu Y, Wang J, Li J S, Yang J, Kou H C, Liu W M 2016 J. Mater. Sci. Technol 32 470
Google Scholar
[19] Plimpton S 1995 J. Comput. Phys 117 1
Google Scholar
[20] Guo J, Chen J J, Wang Y Q 2020 Ceram. Int 46 12686
Google Scholar
[21] Xiang H G, Li H T, Fu T 2017 Acta Materialia 138 131
Google Scholar
[22] Xiang H G, Li H T, Fu T, Huang C, Peng X H 2017 Acta Mater. 138 131
[23] Lee B J, Shim J H, Baskes M I 2003 Phys. Rev. B 68 144112
Google Scholar
[24] 董斌, 王雪梅, 朱子亮 2020 原子与分子物理学报 37 591
Dong B, Wang X M, Zhu Z L 2020 J. At. Mol. Phys. 37 591
[25] Fang Q H, Chen Y, Li J 2019 Int. J. Plast 114 161
Google Scholar
[26] Foiles, S M, Baskes, M I, Daw M S 1988 Phys. Rev. B 33 7983
[27] Qian Y, Shang F, Wan Q 2018 J. Phys. D 24 115102
[28] Qian Y, Shang F, Wan Q 2018 Comput. Mater. Sci 149 230
Google Scholar
[29] Goel S, Luo X, Reuben R L 2012 Appl. Phys. Lett 100 231
[30] Shimizu F, Ogata S, Li J 2007 Mater. Trans 48 2923
Google Scholar
[31] Oliver W C, Pharr G M 1992 J. Mater. Sci 7 1564
[32] Fan X, Rui Z, Cao H, Fu R, Feng R 2019 Materials 12 770
Google Scholar
[33] Belak J, Boercker D B, Stowers I F 1993 MRS Bull 18 55
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