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在辐照环境下, 载能粒子与材料相互作用导致材料中原子移位, 造成辐照损伤. 其中, 由辐照形成的过饱和自间隙原子团簇形成的间隙型位错环, 是体心立方Fe为基的材料中常见的辐照缺陷之一, 其与材料中其他缺陷之间相互作用, 是导致辐照硬化、脆化、肿胀及蠕变等辐照损伤的原因之一. 除此相互作用外, 在材料表面或内部沿晶界、沉积相、惰性气体形成的气泡所导致的微裂纹, 是诱发辐照促进应力腐蚀开裂的重要原因. 因此, 理解辐照条件下间隙型位错环与微裂纹之间的相互作用, 是理解辐照促进应力腐蚀开裂微观机制的重要一步. 在本研究中, 利用分子动力学方法, 模拟了原子尺度微裂纹与间隙型位错环之间的相互作用, 研究了位错环与微裂纹之间的距离、相对位置及位错环尺寸对二者相互作用的影响, 揭示了位错环对微裂纹是否沿滑移面扩展的影响, 发现当二者的相互作用起主导作用时(如在临界水平或垂直距离之内), 形成的以
$ \langle 100 \rangle $ 为主或高密度的1/2$ { \left\langle {111} \right\rangle} $ 位错网络可以抑制微裂纹沿滑移面的扩展. 当位错环尺寸发生变化时, 只有当位错环位错核与微裂纹尖端相互作用时, 才能抑制微裂纹沿滑移面的扩展. 这些结果为进一步理解辐照应力开裂提供了新的参考.The interactions between the energetic particles and atoms in materials would result in the atomic displacements and the associated radiation defects. The interstitial dislocation loop, as one of the primary radiation defects, is formed by the clustering of the supersaturated self-interstitial atoms from the displacement damages in body centered cubic (bcc) iron based materials. The radiation hardening, embrittlement, swelling, creep, etc. are generally related to these loops and their interactions with other defects. In addition, the irradiation would also result in the formation of the micro-cracks from the surface of the materials and also from the interface of grains, precipitates, and gas-bubbles inside the materials, which would result in the irradiation assisted stress corrosion crack (IASCC). Therefore, to understand the interaction between interstitial dislocation loop and micro-crack under the irradiation, is one of key steps to understand the underlying mechanism of IASCC. In this work, the interaction between interstitial dislocation loop and micro-crack is simulated by molecular dynamics method on an atomic scale. The distance, relative position between them and radius of dislocation loop, as the main factors affecting their interactions, are studied to explore the underlying reason for inducing the micro-crack to expand on the slip plane. The simulation results indicate that when the interaction between them dominates the whole process with the distance between them within the critical value, the dislocation network containing the$ \langle 100 \rangle $ and 1/2$ \langle 111 \rangle $ segments, would interact with the crack tip to inhibit the crack from expanding through the pinning effect. When the size of loop is different, the pining effect would be available only when the interaction between loop core and crack tip dominates with the distance between them within the critical value. All these results provide new understanding for further exploring the IASCC under irradiation.-
Keywords:
- radiation damage /
- micro-crack /
- dislocation loop /
- molecular dynamics simulation
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图 1 位错环与微裂纹扩展相互作用模型示意图 (a)无位错环时的微裂纹自由扩展; (b)存在不同位置的位错环时与裂纹扩展相互作用的模型
Fig. 1. Schematic of interaction between the interstitial dislocation loop and expansion of micro-crack: (a) The model of micro-crack expansion without the effect of dislocation loop; (b) the model after including the effect of interstitial dislocation loop located at different positions.
图 2 外应力作用下自由微裂纹扩展的过程 (a)−(c) 1.0, 40.0 和122.4 ps时的形貌
Fig. 2. Expansion of free micro-crack under the effect of external stress: (a)−(c) Results at time of 1.0, 40.0, and 122.4 ps, respectively.
图 3 d = 1.5 nm, R = 1.5 nm, 位错环与微裂纹扩展的相互作用过程, (a)−(c)分别为15, 20和120 ps时的形貌 (a) 反应初始阶段在微裂纹尖端形成凹凸不平; (b)二者反应形成位错网络阶段; (c) 裂纹尖端被位错网络钉扎并保持在XOZ平面
Fig. 3. Interaction between interstitial dislocation loop with radius R = 1.5 nm and micro-crack with distance to loop d = 1.5 nm. (a) to (c) are results at time of 15, 20, and 120 ps: (a) The initial stage with the formation of rugged crack tip; (b) the state with the formation of dislocation network after the interaction between loop and crack; (c) the final state with crack tip pinned by dislocation network located on XOZ plane.
图 4 d = 3.0 nm, R = 1.5 nm, 位错环与微裂纹扩展的相互作用过程, (a)−(c)分别为46, 75和122.6 ps时的形貌 (a)微裂纹在滑移面上开始扩展的初始阶段; (b)形成以1/2
$\left\langle {111} \right\rangle $ 为主的位错网络阶段; (c)微裂纹沿滑移面扩展导致材料断裂的阶段Fig. 4. Interaction between interstitial dislocation loop with radius R = 1.5 nm and micro-crack with distance d = 3.0 nm to loop. (a) to (c) are results at time of 46, 75, and 122.6 ps: (a) The stage at the beginning of crack on slip plane by changing the expansion direction; (b) the state with the formation of dislocation network and 1/2
$\left\langle {111} \right\rangle $ segments dominate the network; (c) the final state with crack expansion on slip plane, resulting in the fracture of material.
图 5 d = 1.5 nm, R = 1.5 nm, l = 1.5 nm, 位错环与微裂纹扩展的相互作用过程 (a)−(e)分别为36.8, 48.6, 50.5, 95.0和122.6 ps时的形貌
Fig. 5. Interaction between dislocation loop and micro-crack with d = 1.5 nm, R = 1.5 nm, and l = 1.5 nm: (a) to (e) are results at time of 36.8, 48.6, 50.5, 95.0, and 122.6 ps, respectively.
图 6 d = 1.5 nm, R = 3.0 nm, 位错环与微裂纹扩展的相互作用过程 (a)−(d)分别为29, 32, 80 和123 ps时的形貌
Fig. 6. Interaction between dislocation loop and micro-crack with d = 1.5 nm and R = 3.0 nm: (a) to (d) are results at time of 29, 32, 80, and 123 ps.
图 7 d =5.5 nm, R = 3.0 nm, 计算122.5 ps后的相互作用结果
Fig. 7. Results of interaction between dislocation loop and micro-crack with d = 5.5 nm, R = 3.0 nm after 122.5 ps.
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[1] Rana M A 2012 Radit. Meas. 47 50
Google Scholar
[2] Ascheron C, Schindler A, Flagmeyer R, Otto G 1989 Nucl. Instrum. Methods B 36 163
Google Scholar
[3] Ascheron C, Schindler A, Flagmeyer R, Otto G 1986 Phys. Status Solidi A 96 555
Google Scholar
[4] Mikkelson R C, Miller J W, Holland R E, Gemmell D S 1973 J. Appl. Phys. 44 935
Google Scholar
[5] Kohyama A, Hishinuma A, Gelles D S, Klueh R L, Dietz W, Ehrlich K 1996 J. Nucl. Mater. 233–237 138
[6] Jung P 2002 J. Nucl. Mater. 301 15
Google Scholar
[7] Beyerlein I J, Caro A, Demkowicz M J, Mara N A, Misra A, Uberuaga B P 2013 Mater. Today 16 443
Google Scholar
[8] Litwa P, Kurpaska L, Varin R A, Perkowski K, Jagielski J, Jozwiak S, Czujko T 2017 J. Alloys Compd. 711 111
Google Scholar
[9] Wei Y P, Liu P P, Zhu Y M, Wang Z Q, Wan F R, Zhan Q 2016 J. Alloys Compd. 676 481
Google Scholar
[10] Masters B C 1965 Philos. Mag. 11 881
Google Scholar
[11] Scott P 1994 J. Nucl. Mater. 211 101
Google Scholar
[12] Was G S, Busby J T 2005 Philos. Mag. 85 443
Google Scholar
[13] Fukuya K, Nakano M, Fujii K, Torimaru T, Kitsunai Y 2004 J. Nucl. Sci. Technol. 41 1218
Google Scholar
[14] 梁晋洁, 高宁, 李玉红 2020 69 036101
Google Scholar
Liang J J, Gao N, Li Y H 2020 Acta Phys. Sin. 69 036101
Google Scholar
[15] 黄依娜, 万发荣, 焦治杰 2011 60 036802
Google Scholar
Huang Y N, Wan F R, Jiao Z J 2011 Acta Phys. Sin. 60 036802
Google Scholar
[16] 杜玉峰, 崔丽娟, 万发荣 2019 工程科学学报 41 1016
Google Scholar
Du Y F, Cui L J, Wan F R 2019 Chin. J. Eng. 41 1016
Google Scholar
[17] 崔丽娟, 高进, 杜玉峰, 张高伟, 张磊, 龙毅, 杨善武, 詹倩, 万发荣 2016 65 066102
Google Scholar
Cui L J, Gao J, Du Y F, Zhang G W, Zhang L, Long Y, Yang S W, Zhan Q, Wan F R 2016 Acta Phys. Sin. 65 066102
Google Scholar
[18] 邓平, 孙晨, 彭群家, 韩恩厚, 柯伟 2015 中国腐蚀与防护学报 35 479
Deng P, Sun C, Peng Q J, Han E H, Ke W 2015 J. Chin. Soc. Corros. Prot. 35 479
[19] Gurrutxaga-Lerma B 2018 Int. J. Eng. Sci. 128 165
Google Scholar
[20] Gupta J, Hure J, Tanguy B, Laffont L, Lafont M C, Andrieu E 2018 J. Nucl. Mater. 501 45
Google Scholar
[21] Decelis B, Argon A S, Yip S 1983 J. Appl. Phys. 54 4864
Google Scholar
[22] 董杰, 陈学东, 范志超, 江慧峰, 陆守香 2008 金属学报 44 1167
Google Scholar
Dong J, Chen X D, Fan Z C, Jiang H F, Lu S X 2008 Acta Metall. Sin. 44 1167
Google Scholar
[23] 赵芳欣, 张瑛洁, 张松, 赵祖欣, 尹绍奎, 李德成 1996 金属学报 32 1056
Zhao F X, Zhang Y J, Zhang S, Zhao Z X, Yin S K, Li D C 1996 Acta Metall. Sin. 32 1056
[24] 徐永波, 白以龙, 沈乐天, 薛青, 李环, 孔丹 1995 金属学报 31 485
Xu Y B, Bai Y L, Shen T L, Xue Q, Li H, Kong D 1995 Acta Metall. Sin. 31 485
[25] 陈奇志, 褚武扬, 乔利杰, 王燕斌, 肖纪美 1994 金属学报 30 248
Chen Q Z, Chu W Y, Qiao L J, Wang Y B, Xiao J M 1994 Acta Metall. Sin. 30 248
[26] Ackland G J, Mendelev M I, Srolovitz D J, Han S, Barashev A V 2004 J. Phys. Condens. Matter 16 S2629
Google Scholar
[27] Mendelev M I, Han S, Srolovitz D J, Ackland G J, Sun D Y, Asta M 2003 Philos. Mag. 83 3977
Google Scholar
[28] Plimpton S 1995 J. Comput. Phys. 117 1
Google Scholar
[29] Stukowski A, Albe K 2010 Modell. Simul. Mater. Sci. Eng. 18 085001
Google Scholar
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