晶体相场方法模拟高温应变作用的预熔化晶界的位错运动
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摘要
采用晶体相场模型,分别模拟了小角对称倾侧双晶体系在高温接近熔点温度和达到固-液共存温度时,在外加应变作用下的小角度晶界以及位错的湮没过程.研究表明,没有加外应变时,当体系接近熔点温度情况下,晶界处的晶格位错周围出现预熔化现象,此时预熔化区域内的位错结构并没有发生改变;当温度达到高温固-液共存温度时,预熔化区域明显增大.经高温预熔化后,再施加外应变作用,这时,已存在预熔化的晶界位错发生滑移运动,然后出现位错相遇湮没,晶界消失,同时,伴随的预熔化区域也消失.在预熔化温度情况下的晶界位错的湮没规律基本相同.预熔化温度越接近熔点温度,位错缺陷周围预熔化区域出现晶格原子软化现象越明显,降低了位错周围原子之间的结合强度.这时,在施加外应变作用下,晶格原子对位错滑移运动的阻力降低,位错运动得更快.对于达到高温固-液共存温度情况,此时施加外加应变后,原预熔化区域会出现应变诱发更大面积的预熔化区域.观察到外加应变诱发预熔化区域变化过程中,出现了位错成对地增殖,并发生位错对的旋转和湮没等相互作用;同时,外加应变诱发的预熔化区域的形状随预熔化区内的位错的相互作用而发生变化,出现了预熔化区域相向扩展、连通,然后又分解、分离;尽管这时的预熔化区域形状随外应变作用在不断变化,但此时的预熔化区并不会出现合并消失现象,与较低的预熔化温度的位错运动情况完全不同.
The properties of modern materials, especially superplastic, nanocrystalline or composite materials, depend critically on the properties of internal interfaces such as grain boundaries(GBs) and interphase boundaries(IBs). All processes which can change the properties of GBs and IBs affect drastically the behaviour of polycrystalline metals and ceramics. In this work, the annihilation processes of low-angle symmetric tilt GBs and dislocations during plastic deformation in the representative system of these materials near but below the melting point and the temperature at liquid-solid coexistence line were simulated using the phase-field crystal model, respectively. The results show that local premelting occurs around lattice dislocations near the melting point but the dislocation structure in the premelting region does not change, while the region become significantly larger when the system reaches the melting temperature. After premelting, deformation to the system causes dislocations in the premelting GB to begin to glide then annihilate with opposite Burgers vectors via the movement, finally the GB and the premelting region disappear. The annihilation mechanisms of dislocations are similar to those for premelting conditions. The more the temperature is closer to the melting point, the more obvious the atomic lattice around the premelting region is softened leading to the atomic binding strength around the dislocations being lowered. Only at this moment, the lattice atoms enable to reduce the resistance of the dislocation motion and accelerate its velocity during deformation. At the temperature reaching to the liquid-solid coexisting region in the simulation, the original premelting regions are induced to develop into bigger ones by the external strain acting. During this process, it can be seen some interactions including the multiplication dislocation pairs, the rotation of dislocation pairs and their annihilation. Furthermore, the shape of the premelting region changes with the variation of the interaction of dislocations inside the region, it is observed that the premelting regions approach each other and consolidate together,then decompose and segregate from each other. Although the shape of the premelting region changes with the applied strain, these regions do not disappear at the end of the simulation, totally different those in lower premelting temperature.
The properties of modern materials, especially superplastic, nanocrystalline or composite materials, depend critically on the properties of internal interfaces such as grain boundaries(GBs) and interphase boundaries(IBs). All processes which can change the properties of GBs and IBs affect drastically the behaviour of polycrystalline metals and ceramics. In this work, the annihilation processes of low-angle symmetric tilt GBs and dislocations during plastic deformation in the representative system of these materials near but below the melting point and the temperature at liquid-solid coexistence line were simulated using the phase-field crystal model, respectively. The results show that local premelting occurs around lattice dislocations near the melting point but the dislocation structure in the premelting region does not change, while the region become significantly larger when the system reaches the melting temperature. After premelting, deformation to the system causes dislocations in the premelting GB to begin to glide then annihilate with opposite Burgers vectors via the movement, finally the GB and the premelting region disappear. The annihilation mechanisms of dislocations are similar to those for premelting conditions. The more the temperature is closer to the melting point, the more obvious the atomic lattice around the premelting region is softened leading to the atomic binding strength around the dislocations being lowered. Only at this moment, the lattice atoms enable to reduce the resistance of the dislocation motion and accelerate its velocity during deformation. At the temperature reaching to the liquid-solid coexisting region in the simulation, the original premelting regions are induced to develop into bigger ones by the external strain acting. During this process, it can be seen some interactions including the multiplication dislocation pairs, the rotation of dislocation pairs and their annihilation. Furthermore, the shape of the premelting region changes with the variation of the interaction of dislocations inside the region, it is observed that the premelting regions approach each other and consolidate together,then decompose and segregate from each other. Although the shape of the premelting region changes with the applied strain, these regions do not disappear at the end of the simulation, totally different those in lower premelting temperature.
引文
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[2]Straumal B,Kogtenkova O,Protasova S,Mazilkin A,Zieba P.Mater Sci Eng,2008;A495:126
[3]Luo J.Curr Opin Solid State Mater Sci,2008;12:81
[4]Alsayed A M,Islam M F,Zhang J,Collings P J,Yodh A G.Science,2005;309:1207
[5]Tallon J L.Nature,1978;276:849
[6]Bartis F J.Nature,1977;268:427
[7]Oxtoby D W.Nature,1990;347:725
[8]Pusey P N.Science,2005;309:1198
[9]Hsich T E,Ballaffi R W.Acta Metall,1989;37:1637
[10]Lu K,Sheng H W,Jin Z H.Chin J Mater Res,1997;11:658(卢柯,生红卫,金朝晖.材料研究学报,1997;11:658)
[11]Chaudron G,Lacombe P,Yannacguis N.C R Acad Sci,1948;226:1372
[12]Balluffi R W,Maurer R.Scr Metall,1988;22:709
[13]Hsieh T E,Balluffi R W.Acta Metall,1989;37:1637
[14]Divinski S,Lohman M,Herzig C,Straumal B,Baretzky B,Gust W.Phys Rev,2005;71B:104104
[15]Straumal B B,Noskovich Q I,Semenov V N.Acta Metall Mater,1992;40:795
[16]Wang N,Mokadam S,Rappaz M,Kurz W.Acta Mater,2004;52:3173
[17]Inoko F,Okada T,Maraga T,Nakano Y,Yoshikawa T.Interf Sci,1997;4:263
[18]Inoko F,Hama T,Tagami M,Yoshikawa T.Ultramicroscopy,1991;39:118
[19]Zhang L,Wang S Q,Ye H Q.Acta Phys Sin,2004,53:2497(张林,王绍青,叶恒强.物理学报,2004;53:2497)
[20]Willians P L,Mishin Y.Acta Mater,2009;57:3786
[21]Frolov T,Mishin Y.Phys Rev,2009;79B:174110
[22]Keblinski P,Phillpot S R,Wolf D,Gleiter H.Acta Mater,1997;45:987
[23]Besold G,Mouritsen O G.Phys Rev,1994;50B:6573
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[36]Yang T,Chen Z,Dong W P.Acta Metall Sin,2011;47:1301(杨涛,陈铮,董卫平.金属学报,2011;47:1301)
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[38]Gao Y J,Wang J F,Luo Z R,Lu Q H,Liu Y.Chin J Comput Phys,2013;30:577(高英俊,王江帆,罗志荣,卢强华,刘瑶.计算物理,2013;30:577)
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