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The one-dimensional (1D) glide motion of dislocation loops along the direction of Burgers vector in various metallic materials has attracted considerable attention in recent years. During the operation of nuclear fusion reactor, component materials will be bombarded by high energy neutrons, resulting in production of radiation defects such as self-interstitial-atoms (SIAs), vacancies and their clusters. These defects feature large difference in migration energy, which may lead to concentration imbalance between SIAs and vacancies, and eventually irradiation damages such as swelling and embrittlement. Generally speaking, the mobility of a defect cluster is lower than that of a point defect. However, fast 1D motion may also take place among SIA clusters in the form of prismatic dislocation loops. This increases the transport efficiency of SIAs towards grain boundaries, surface and interface sites in the material, in favour of defect concentration imbalance and damage accumulation. To date, most literature works have found that the 1D motion of dislocation loops exhibited short-range (nanometer-scale) character. In addition, such experimental studies were generally conducted in pure metals using high voltage electron microscopes (HVEM) operated at acceleration voltages ≥1000 kV. However, for pure aluminum (Al), the maximum transferable kinetic energy from 200 keV electrons is 19.5 eV, while the displacement threshold energy is only 16 eV. Therefore, the observation and mechanistic investigation of 1D motion of dislocation loops in Al should also be possible with conventional transmission electron microscopes (C-TEM), as it may also exhibit the effects of beam heating and point defect production in HVEM. In view of the shortage of HVEM, this work reports the 1D motion of dislocation loops in pure Al implanted with hydrogen ions using C-TEM. Simultaneous dislocation loop motion in opposite directions of Burgers vector 1/2
$\left\langle {110} \right\rangle $ has been captured, as well as the collective 1D motion of an array of dislocation loops in the direction of Burgers vector 1/3$\left\langle {111} \right\rangle $ under 200 keV electron irradiation. In addition, 1D motion of dislocation loops up to micron-scale range along the direction of Burgers vector 1/3$\left\langle {111} \right\rangle $ , and up to a few hundred nanometers range along the direction of Burgers vector 1/2$\left\langle {110} \right\rangle $ have been found, which is different from previous literature works. A characteristic migration track would form behind the moving dislocation loop, lasting for about tens of seconds. The more rapid the dislocation loop motion, the longer the migration track length is. The concentration gradient of SIAs by electron irradiation and the redistribution of hydrogen atoms caused by the moving dislocation loops may account for the observed micron-scale 1D motion of dislocation loops and the migration tracks.-
Keywords:
- one-dimensional motion /
- electron irradiation /
- dislocation loops /
- aluminum
[1] 万发荣 1993 金属材料的辐照损伤 (北京: 科学出版社) 第7页
Wan F R 1993 Irradiation Damage of Metal Materials (Beijing: Science Press) p7 (in Chinese)
[2] 郭立平, 罗凤凤, 于雁霞 2016 核材料辐照位错环 (北京: 国防工业出版社) 第37页
Guo L P, Luo F F, Yu Y X 2016 Dislocation loops in irradiated nuclear materials (Beijing: National Defense Industry Press) p37 (in Chinese)
[3] Du Y F, Cui L J, Han W T, Wan F R 2019 Acta Metall. Sin. 32 566
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Google Scholar
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Google Scholar
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Google Scholar
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Google Scholar
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Google Scholar
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Google Scholar
[19] Matsukawa Y, Zinkle S J 2007 Science 318 959
Google Scholar
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Google Scholar
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Google Scholar
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Google Scholar
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Rong Y H 2006 Introduction to Analytical Electron Microscopy (Beijing: Higher Education Press) p28 (in Chinese)
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Google Scholar
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Google Scholar
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Google Scholar
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Google Scholar
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图 1 由SRIM-2013计算得到的注氢纯铝的辐照损伤值和氢离子浓度随样品厚度的分布
Figure 1. Depth profiles of displacement damage (dpa) and hydrogen concentration (H, at.%) of ion irradiations in pure Al calculated by SRIM-2013 software.
图 2 不同电子束斑中心位置的电子辐照下位错环的一维迁移运动 (a)原位观察对应的运动学双束衍射条件(g = 111), 一维迁移方向(//柏氏矢量B = 1/3
$\left\langle {111} \right\rangle $ 或者1/2$\left\langle {110} \right\rangle $ 方向)以及与其最相近的两组晶向; (b), (c)电子辐照期间电子束斑中心与观察区域的相对位置; (d)—(i)位错环在电子辐照下的一维迁移现象. 不同形状符号所对应的数字“1, 2, 3, ···11”分别指第“1, 2, 3, ···11”编号位错环Figure 2. One-dimensional motion of dislocation loops under electron irradiation at different electron beam center locations: (a) Diffraction pattern illustrating the two-beam kinematical condition during in-situ observation (g = 111), and one-dimensional motion direction (// the direction of Burgers vector, B =1/3
$\left\langle {111} \right\rangle $ or 1/2$\left\langle {110} \right\rangle $ ) and the two groups of crystal orientation closest to it; (b), (c) the positions of electron beam center for different durations of electron irradiation; (d)−(i) one-dimensional motion of dislocation loops under electron irradiation. Shapes numbered “1, 2, 3, ···11” correspond to dislocation loops “1, 2, 3, ···11”, respectively.
图 3 相同电子辐照条件下两个相邻区域不同位错环的一维迁移运动 (a)运动学双束条件下的电子衍射图(
$ g = {\bar 2}20 $ ); (b)一维迁移方向(//柏氏矢量B = 1/3$ \left\langle {111} \right\rangle $ 或者1/2$ \left\langle {110} \right\rangle $ 的方向)以及与其最相近的两组晶向; (c)—(j)位错环12—14在电子辐照下的一维迁移现象Figure 3. One-dimensional motion of dislocation loops in two adjacent regions under the same electron irradiation: (a) Diffraction pattern illustrating the two-beam kinematical imaging condition (
$g = {\bar 2}20 $ ); (b) one-dimensional motion direction (// the direction of Burgers vector, B = 1/3$ \left\langle {111} \right\rangle $ or 1/2$ \left\langle {110} \right\rangle $ ) and the two groups of crystal orientation closest to it; (c)−(j) one-dimensional motion of dislocation loops 12−14 under electron irradiation.
图 4 相邻两个位错环的一维迁移距离与电子束辐照时间的关系 (a)运动学双束条件下的电子衍射图(g = 200); (b)一维迁移方向(//柏氏矢量B = 1/3
$ \left\langle {111} \right\rangle $ 或者1/2$ \left\langle {110} \right\rangle $ 的方向)以及与其最相近的两组晶向; (c)位错环16和17一维迁移距离随辐照时间的变化; (d)—(k)位错环在电子辐照下的一维迁移现象. 黑色箭头表示一维迁移方向Figure 4. The relationship between one-dimensional motion distance and electron irradiation time of two adjacent dislocation loops: (a) Diffraction pattern illustrating the two-beam kinematical imaging condition (g = 200); (b) one-dimensional motion direction (// the direction of Burgers vector, B = 1/3
$ \left\langle {111} \right\rangle $ or 1/2$ \left\langle {110} \right\rangle $ ) and the two groups of crystal orientation closest to it; (c) the one-dimensional migration distance of dislocation loops (16, 17) under electron irradiation as a function of time; (d)−(k) the one-dimensional motion of dislocation loops 16, 17 under electron irradiation. The black arrows indicate the direction of one-dimensional motion of dislocation loops.
图 5 电子辐照下不同位错环一维迁移形成的运动轨迹
Figure 5. The migration tracks of different dislocation loops formed by one-dimensional motion under electron irradiation.
表 1 不同辐照时间内位错环1—7的一维迁移距离、平均迁移速率以及轨迹长度
Table 1. The migration distance, average migration speed and migration track length of one-dimensional motion for dislocation loops 1–7 for different durations of electron irradiation.
辐照时间/s 0 20 42 65 126 209 位错环1 迁移距离/nm × 600 57 0 152 0 平均速率/(nm·s–1) × 30 2.59 0 2.47 0 轨迹长度/nm 326 917 890 405 0 0 位错环2 迁移距离/nm × 144 46 187 307 133 平均速率/(nm·s–1) × 7.2 2.09 8.13 5.03 1.6 轨迹长度/nm 178 334 260 305 478 222 位错环3 迁移距离/nm × 257 57 61 0 100 平均速率/(nm·s–1) × 12.9 2.59 2.65 0 1.2 轨迹长度/nm 165 370 174 175 91 131 位错环4 迁移距离/nm × 192 41 78 41 50 平均速率/(nm·s–1) × 9.6 1.86 3.39 0.67 0.6 轨迹长度/nm 487 259 190 148 0 0 位错环5 迁移距离/nm × 109 0 78 52 61 平均速率/(nm·s–1) × 5.45 0 3.39 0.85 0.73 轨迹长度/nm 292 231 139 243 0 0 位错环6 迁移距离/nm × 244 44 30 0 0 平均速率/(nm·s–1) × 12.2 2 1.3 0 0 轨迹长度/nm 161 288 210 137 114 110 位错环7 迁移距离/nm × 139 48 39 0 44 平均速率/(nm·s–1) × 6.95 2.18 1.7 0 0.53 轨迹长度/nm 107 265 152 157 82 0 *迁移距离为不同时间段位错环的一维迁移距离; 平均速率为该时间与前一时间点之间的平均迁移速率; 轨迹长度为对应时间点一维迁移所能显示出的迁移轨迹. 所有数据均是基于图2进行统计计算的结果. “×”表示对应条件下无相关数据. 
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[1] 万发荣 1993 金属材料的辐照损伤 (北京: 科学出版社) 第7页
Wan F R 1993 Irradiation Damage of Metal Materials (Beijing: Science Press) p7 (in Chinese)
[2] 郭立平, 罗凤凤, 于雁霞 2016 核材料辐照位错环 (北京: 国防工业出版社) 第37页
Guo L P, Luo F F, Yu Y X 2016 Dislocation loops in irradiated nuclear materials (Beijing: National Defense Industry Press) p37 (in Chinese)
[3] Du Y F, Cui L J, Han W T, Wan F R 2019 Acta Metall. Sin. 32 566
Google Scholar
[4] Terentyev D, He X, Bonny G, Bakaev A, Zhurkin E, Malerba L 2015 J. Nucl. Mater. 457 173
Google Scholar
[5] 万发荣 2020 工程科学学报 42 1535
Google Scholar
Wan F R 2020 Chin. J. Eng. 42 1535
Google Scholar
[6] Hwang T, Hasegawa A, Tomura K, Ebisawa N, Toyama T, Nagai Y, Fukuda M, Miyazawa T, Tanaka T, Nogami S 2018 J. Nucl. Mater. 507 78
Google Scholar
[7] Ipatova I, Wady P T, Shubeita S M, Barcellini C, Impagnatiello A, Jimenez-Melero E 2018 J. Microsc. 270 110
Google Scholar
[8] Satoh Y, Abe H, Matsukawa Y, Matsunaga T, Kano S, Arai S, Yamamoto Y, Tanaka N 2015 Philos. Mag. 95 1587
Google Scholar
[9] Wang J, Hou Q, Zhang B L 2021 Solid State Commun. 325 114158
Google Scholar
[10] Chen D, Murakami K, Abe H, Li Z, Sekimura N 2019 Acta Mater. 163 78
Google Scholar
[11] Marian J, Wirth B D, Caro A, Sadigh B, Odette G R, Perlado J M, de la Rubia T D 2002 Phys. Rev. B 65 144102
Google Scholar
[12] Arakawa K, Ono K, Isshiki M, Mimura K, Uchikoshi M, Mori H 2007 Science 318 956
Google Scholar
[13] Osetsky Y N, Bacon D J, Serra A 1999 Philos. Mag. Lett. 79 273
Google Scholar
[14] Abe Y, Satoh Y, Hashimoto N, Ohnuki S 2020 Philos. Mag. 100 110
Google Scholar
[15] Nandipati G, Setyawan W, Roche K J, Kurtz R J, Wirth B D 2020 J. Nucl. Mater. 542 152402
Google Scholar
[16] Satoh Y, Matsui H, Hamaoka T 2008 Phys. Rev. B 77 094135
Google Scholar
[17] Satoh Y, Matsui H 2009 Philos. Mag. 89 1489
Google Scholar
[18] Osetsky Y N, Bacon D J, Serra A, Singh B N, Golubov S I 2000 J. Nucl. Mater. 276 65
Google Scholar
[19] Matsukawa Y, Zinkle S J 2007 Science 318 959
Google Scholar
[20] Derlet P M, Gilbert M R, Dudarev S L 2011 Phys. Rev. B 84 134109
Google Scholar
[21] Wirth B D, Odette G R, Maroudas D, Lucas G E 2000 J. Nucl. Mater. 276 33
Google Scholar
[22] Wirth B D 2000 Ph D Dissertation (Santa Barbara: University of California)
[23] Arakawa K, Hatanaka M, Mori H, Ono K 2004 J. Nucl. Mater. 329 1194
Google Scholar
[24] Hamaoka T, Satoh Y, Matsui H 2013 J. Nucl. Mater. 433 180
Google Scholar
[25] Hayashi T, Fukmuto K, Matsui H 2002 J. Nucl. Mater. 307 993
[26] Satoh Y, Abe Y, Abe H, Matsukawa Y, Kano S, Ohnuki S, Hashimoto N 2016 Philos. Mag. 96 2219
Google Scholar
[27] Amino T, Arakawa K, Mori H 2016 Sci. Rep. 6 26099
Google Scholar
[28] Williams D B, Carter C B 2009 Transmission Electron Microscopy (New York: Springer Science+Business Media) p68
[29] Stoller R E, Toloczko M B, Was G S, Certain A G, Dwaraknath S, Garner F A 2013 Nucl. Instrum. Methods Phys. Res., Sect. B 310 75
Google Scholar
[30] Astm-Committee 2003 Standard Practice for Neutron Radiation Damage Simulation by Charged-particle Irradiation (West Conshohocken: Copyright © ASTM International) p8
[31] 戎咏华 2006 分析电子显微学导论 (北京: 高等教育出版社) 第28页
Rong Y H 2006 Introduction to Analytical Electron Microscopy (Beijing: Higher Education Press) p28 (in Chinese)
[32] Ono K, Kino T, Furuno S, Hojou K, Izui K, Mizuno K, Ito K 1991 J. Nucl. Mater. 179-181 978
Google Scholar
[33] Kuramoto E 2009 Materia Jpn. 48 111
Google Scholar
[34] Schulthess T C, Turchi P E A, Gonis A, Nieh T G 1998 Acta Mater. 46 2215
Google Scholar
[35] Sarma V S, Wang J, Jian W W, Kauffmann A, Conrad H, Freudenberger J, Zhu Y T 2010 Mater. Sci. Eng., A 527 7624
Google Scholar
[36] Gallagher P 1970 Metall. Trans. 1 2429
Google Scholar
[37] Kim J, Lee S, De Cooman B C 2011 Scr. Mater. 65 363
Google Scholar
[38] Yan J A, Wang C Y, Wang S Y 2004 Phys. Rev. B 70 174101
Google Scholar
[39] Portavoce A, Treglia G 2014 Acta Mater. 65 1
Google Scholar
[40] Tapasa K, Barashev A V, Bacon D J, Osetsky Y N 2007 J. Nucl. Mater. 361 52
Google Scholar
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