Dislocation–grain boundary interaction in 〈1 1 1〉 textured thin metal films

The interaction of lattice dislocations with symmetrical and asymmetrical tilt grain boundaries in 〈1 1 1〉 textured thin nickel films was investigated using atomistic simulation methods. It was found that the misorientation angle of the grain boundary, the sign of the Burgers vector of the incoming dislocation and the exact site where the dislocation meets the grain boundary are all important parameters determining the ability of the dislocation to penetrate the boundary. Inclination angle, however, does not make an important difference on the transmission scenario of full dislocations. Only limited partial dislocation nucleation was observed for the investigated high-angle grain boundary. The peculiarities of nucleation of embryonic dislocations and their emission from tilt grain boundaries are discussed.     

DISLOCATION BEHAVIOR IN THE SUPERPLASTIC DEFORMATION OF ALLOY Al-Li 2091

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Deformation induced grain boundaries in commercially pure aluminium

The structure of commercially pure aluminium processed by equal channel angular extrusion at room temperature, to an equivalent strain up to 8, was studied by transmission electron microscopy. Attention was paid to the structure evolution of the generated boundaries. Three types of boundaries were found, namely polygonized dislocation wall, partially transformed boundary, and grain boundary. By increasing strain, polygonized dislocation walls transform firstly into partially transformed boundaries, then into grain boundaries. Dissociation of lattice dislocations is suggested to cause the transformation to occur. At equivalent strain equal to 8, most of the generated boundaries transform into grain boundaries.     

Grain rotation by dislocation climb in a finite-size grain boundary

We investigate the kinetics of grain rotation in a bicrystal with a tilt grain boundary by studying the relaxation of an edge dislocation wall in a discrete-dislocation approach. The boundary is infinitely extended in one direction and of finite size in the orthogonal one. The relaxation process is simulated numerically by solving the equations of motion of the dislocations, assuming climb by diffusive transport in the boundary plane. Surprisingly, we find that boundaries never rotate all the way into coincidence. Instead, the final state is a metastable array with 18 dislocations and, hence, with a finite misorientation that depends on the boundary length and the Burgers vector. All boundaries with fewer than 18 dislocations are also metastable. The relaxation time to reach the metastable configuration is found to be proportional to the logarithm of the number of dislocations and to the cube of the length of the boundary. We give a critical discussion of image force arguments that underlie earlier work on grain rotation, and verify that the present analysis of image forces does satisfy the boundary conditions at the free surfaces. The results have implications for the kinetics of rotation of nanoparticles on a substrate and for the stability of grain and subgrain boundaries in thin metal films.     

Coalescence of wustite grains during iron oxidation in a hot-stage environmental SEM

The growth of wustite grains during the initial stages of iron oxidation at 1050°C and atm has been investigated in situ in a hot-stage environmental SEM (HSESEM). Adjacent wustite grains were seen to coalesce by annihilation of the grain boundary dislocations constituting original boundaries. Specifically, dissociation of a grain boundary into an array of dislocations followed by their annihilation either by glide or climb was observed. The grain boundaries exhibiting this coalescence are believed to be low-angle boundaries. A controlled extent of oxidation followed by rapid cooling in the HSESEM enabled the study of wustite grain boundaries. Dissociation of a grain boundary into dislocations without their annihilation was also observed in later stages of oxidation when the dislocation mobility was severely reduced.In this case, instead of grain coalescence, nucleation of a new grain with an orientation different from either of the two original grains took place.     

晶界非平衡偏聚与晶体缺陷构型的关系

对Ｆｅ－３０％Ｎｉ合金和超低碳贝氏体钢在高温进行不同方式变形和保温,通过变形、回复、与再结晶,获得秒同的晶体缺陷数量与构型（主要是位错分布形态）。用硼径迹显微照相技术研究了 空冷过程中硼向晶界的非平衡偏聚及与不同形态晶体缺陷的关系。结果表明,在再结晶新晶粒冷却时晶界偏聚明显。晶界附近会出现较显著的贫硼现象,而变形并回复后的原始晶粒中此现象不明显,高温回复阶段形成的多边形化亚晶界（位错墙）对冷却时硼     

Self-Diffusion in Grain Boundaries and Dislocation Pipes in Al,Fe, and Ni and Application to AlN Precipitation in Steel

Diffusion along microstructural defects, such as grain boundaries or dislocation pipes, is significantly faster than diffusion through an undisturbed crystal. The ratio of diffusion enhancement is 3-4 orders of magnitude close to the melting point and reaches up to several ten orders of magnitude close to room temperature. An assessment of literature shows a large scatter in the available data and emphasizes the need for representative mean values. Applying a least mean square fit to selected experimental information delivers temperature-dependent functions for the ratio of grain boundary and dislocation pipe to bulk diffusion, respectively. We demonstrate that application of the attained results in a computational framework for the kinetics of precipitation makes the predictive simulation possible for the evolution of particles located at dislocations and grain boundaries.     

Dislocation Source and Pile-up in a Twinning-induced Plasticity Steel at High-Cycle Fatigue

Dislocation behaviour of a twinning-induced plasticity(TWIP) steel subjected to high-cycle fatigue tests is investigated in the present study. Grain boundaries are the important sources of dislocation generation during fatigue tests, contributing to the increase in dislocation density. Continuous emission of dislocations from grain boundaries is observed in many grains. Inclusions can sustain large dislocation pile-ups at the inclusion interfaces, leading to a high stress concentration and therefore acting as potential sites of microcrack nucleation. In contrast, annealing twin boundaries are relatively weak boundaries for dislocation pile-ups. When the number of dislocations in a pile-up is large, dislocations can crossover twin boundaries and glide inside the annealing twins. The stress concentration at the twin boundary is relatively low so that twin boundaries could not act as the sites for microcrack initiation.     

Formation of Strain-Induced Broken Dislocation Boundaries at Faceted Grain Boundaries

Typical configurations of broken dislocation boundaries formed during plastic deformation at faceted grain boundaries have been analyzed. The reasons for their formation have been determined. It has been shown that the shape and sizes of strain-induced broken dislocation boundaries can be determined by the geometry of a faceted boundary and the relevant slip systems of lattice dislocations. The calculations carried out in the framework of the 2D model make it possible to explain the morphology of the observed broken dislocation boundaries.     

High-temperature grain boundary sliding behavior and grain boundary energy in cubic zirconia bicrystals

Misorientation dependence of grain boundary energy and grain boundary sliding at high temperature were examined in cubic zirconia bicrystals with [1 1 0] symmetric tilt boundaries, which were fabricated by diffusion bonding method from two cubic zirconia single crystals. High-resolution transmission electron microscopy observation revealed that the grain boundary in cubic zirconia bicrystals was clean and atomically sharp without any void or grain boundary amorphous layer. Grain boundary energy of the tilt boundaries was estimated from the dihedral angles on thermal grooved surface measured with atomic force microscope techniques. The misorientation dependence of the grain boundary energy in cubic zirconia bicrystals shows similar tendency to that of fcc metal such as aluminum and copper. Grain boundary sliding associated with intragranular dislocation slip in cubic zirconia bicrystals was observed for all specimens. The amount of the grain boundary sliding showed a good correlation with the misorientation factor of each boundary. Grain boundary migration also took place accompanying with the grain boundary sliding. The observed grain boundary sliding and migration can be explained based on a dislocation mechanism for sliding which is based on the movement of lattice dislocations along the grain boundary by a combination of climb and glide.     

晶粒尺寸和孪晶界间距对纳米多晶铝合金塑性变形影响的分子动力学模拟研究

采用分子动力学模拟方法,分别研究了晶粒尺寸和孪晶密度对纳米多晶铝合金塑性变形的影响。模拟结果表明,弛豫后的位错密度对纳米多晶Al的微观结构演变和逆Hall-Petch关系产生了重要影响。变形受晶粒大小限制,在细晶中可形成层错四面体和复杂层错结构,从而激活了晶界的辅助变形。当孪晶界间距（TBS）较大时,Shockley分位错在晶界处形核并增殖。然而,随着TBS的减小,孪晶界成为Shockley分位错的来源。孪晶界上大量的分位错形核会导致孪晶界迁移甚至消失。在塑性变形过程中还观察到形变纳米孪晶。研究结果为开发具有可调节力学性能的先进纳米多晶Al提供了理论基础。     

Quasi-four-dimensional analysis of dislocation interactions with grain boundaries in 304 stainless steel

The application of diffraction contrast electron tomography to dynamic experiments involving dislocation interactions with grain boundaries is demonstrated for the first time. Two applications are shown: the first is concerned with post-mortem analysis of dislocation interactions with grain boundaries and illustrates the usefulness of the tomography technique for defect analysis; the second is in conjunction with in situ straining experiments in which the dynamics of dislocation interactions with grain boundaries are observed directly and the resulting structure visualized three-dimensionally. The in situ straining experiments were conducted at room and elevated temperatures to determine the influence, if any, of thermal processes on the slip transfer mechanism. It was found that increasing the temperature lowers the barrier for dislocation absorption and emission from the boundary and increases the complexity of the interactions, but does not change the fundamental mechanisms governing slip transmission. Previous experimentally determined criteria for slip transmission across boundaries were extended to interactions involving partial dislocations, where it was found that the reaction continues to be governed predominately by reduction of the Burgers vector of the residual grain boundary dislocation left after slip transfer.     

Structural changes associated with strain-induced grain boundary migration in Si-Fe

Strain-induced grain boundary migration was observed in several bicrystal sheet specimens of Si-Fe (3¼ pct Si) which were cold rolled 2 to 12 pct and then annealed at temperatures up to 1200°C. A chrome-acetic acid electroetching method was used to reveal the dislocation sites before and after grain boundary migration. Recovery effects were noted in the microstructure prior to boundary motion. Consequently, the residual strain energy in neighboring grains may determine if boundary migration with resulting increase of area occurs, and its direction of movement. Microstructural data indicate that the region initially traversed by the moving grain boundary has many structural defects in the form of low-angle boundaries and random dislocations of relatively high density. With increased distance of grain boundary migration, the density of these imperfections was found to decrease. Continued annealing at 1200°C, after boundary migration, lowered the density of random dislocations in the swept region to a limiting value of about 2×10⁶ lines per sq cm.     

Simulation of dislocation penetration through a general low-angle grain boundary

The interaction of dislocations with low-angle grain boundaries (LAGBs) is considered one important contribution to the mechanical strength of metals. Although LAGBs have been frequently observed in metals, little is known about how they interact with free dislocations that mainly carry the plastic deformation. Using discrete dislocation dynamics simulations, we are able to quantify the resistance of a LAGB—idealized as three sets of dislocations that form a hexagonal dislocation network—against lattice dislocation penetration, and examine the associated dislocation processes. Our results reveal that such a coherent internal boundary can massively obstruct and even terminate dislocation transmission and thus make a substantial contribution to material strength.     

Accommodation processes during deformation of nanocrystalline palladium

Atomistic simulations of uniaxial tensile and compressive straining of three-dimensional nanocrystalline palladium were performed at room temperature and different strain rates. Detailed analysis revealed that initial plastic deformation is due to grain boundary sliding accommodated by localized bending inside the grains and the formation of dislocation embryos. Intergranular cracking in the absence of dislocation activity was found at later stages of tensile straining. During compressive straining the sample shows a plastic response which is brought about mainly by intergranular accommodation processes. The contribution of extended partial dislocations emitted from the grain boundaries as well as full dislocations and twinning at later stages of deformation to the total strain was found to be insignificant.     

Atomistic simulations of lattice defects in tungsten

The mechanical behavior of materials is ultimately determined by events occurring at the atomic scale. The onset of plastic yield corresponds to triggering of dislocation motion. Subsequent hardening is mainly controlled by interaction of gliding dislocations with other lattice defects such as forest dislocations, grain boundaries, interfaces and surfaces. Finally, material failure is influenced by processes at the tip of a crack propagating in a crystal lattice. In this work we review atomistic simulations of lattice defects in tungsten. We show that these studies are able to provide not only a detailed understanding of defect properties but also reveal how the fundamental processes at the atomic scale are linked to macroscopic material behavior.     

2024-T4铝合金搅拌摩擦焊搅拌区位错及组织性能

采用金相、显微硬度及透射分析方法对2024铝合金搅拌摩擦焊接头搅拌微区的组织性能和位错分布特征进行试验分析,基于位错分析深入了解各微区位错形成与接头组织结构与硬度变化之间的关系。研究表明,WNZ位错主要分布在晶粒内部,大部分是以位错缠结的形式存在,并伴随有大量的沉淀强化析出相Cu_2Mg;而在TMAZ区,大量的位错是以位错塞积的形式存在于晶界或晶粒内部;HAZ区域的位错多以位错塞积的形式存在于晶界附近,并伴随一些典型的Al Cu_3析出相。WNZ和TMAZ区中并未随晶粒细化而造成位错数量和类型的减少,这与FSW特殊的动态回复和动态再结晶过程有关,此外位错分布特征与接头微区硬度分布特征基本吻合。     

Contribution of Diffusion Processes to Structure Formation in Intense Cold Plastic Deformation of Metals

The problems of distribution of the chemical potential of vacancies in a crystal with a cellular dislocation structure, the evolution of the properties of the lattice and its imperfections in the process of plastic flow, the contribution of diffusion to the motion of lattice dislocations, and their annihilation and transformation into grain boundary dislocations are considered. An analysis of the phenomena that occur inside and in the walls of dislocation cells in the formation of large-angle boundaries shows that intense cold plastic deformation activates the diffusion mass transfer.     

Partial dislocation configurations in a low-angle boundary in α-Al2O3

The dislocation structures of a low-angle tilt grain boundary in alumina bicrystal were investigated by transmission electron microscopy. The grain boundary was found to consist of two regions: an area with pairs of partial dislocations and an area with groups of odd numbered partial dislocations (multiple-partial-structure). Eight kinds of multiple-partial-structures were found in the fabricated grain boundary. The Burgers vectors of each partial dislocation in the grain boundary can be distinguished by dark-field imaging, and thus the arrangement of partial dislocations in the multiple-partial-structures are determined. It is concluded that a slight twist component of the boundary is the origin of the characteristic multiple-partial-structures.     

Heterogeneous dislocation formation and solute redistribution near grain boundaries in austenitic stainless steel under electron irradiation

We investigated the radiation-induced segregation (RIS) near grain boundaries in austenitic stainless steel under electron irradiation, taking into account the simultaneous evolution of faulted dislocation loops and network dislocations. The formation of a dislocation-free zone (DLFZ) in the vicinity of the grain boundary due to in situ irradiation was observed using a high-voltage electron microscope (HVEM). Predicted temperature and dose dependencies of DLFZ formation agreed with the experimental results. The relationship between RIS and DLFZ formation near a grain boundary has been substantially clarified.