Dislocation structures introduced by high-speed deformation in bcc metals

Systematic experiments were carried out over a wide range of strain rate, 10⁰–10⁶ s⁻¹, so as to reveal the deformation mode in bcc crystals, especially at high strain rate. Dislocation structure showed heterogeneous distribution at low strain rates in all three bcc metals examined. At higher strain rates exceeding 10³ s⁻¹, distribution of dislocations was random, and the formation of small dislocation loops was observed in V and Nb. In Mo, small dislocation loops were not formed by deformation, even at high strain rates. However, post-deformation annealing of an Mo specimen that had been deformed by 20% at 5×10⁵ s⁻¹ produced dislocation loops. The inside–outside contrast method identified these loops to be of vacancy type. These results reveal that in Mo vacancy clusters are not formed directly from the interaction of dislocations, but by the aggregation of vacancies. In V and Nb, the same formation process is believed to occur at high strain rates. These results suggest that the different mode of plastic deformation at high strain rates accompanied by production of vacancies also occurred in bcc metals.     

Analysis of strain rate dependence of tensile elongation for a mechanical milling Al–1.1Mg–1.2Cu alloy tested at 748 K from a dislocation dynamics viewpoint

Tensile deformation was carried out for a mechanically milled and thermo-mechanically treated Al–1.1Mg–1.2Cu (at.%) alloy at 748 K and three nominal strain rates of 10⁻³, 10⁰, and 10² s⁻¹. Despite the prevailing belief that superplasticity occurs by grain boundary sliding which requires slow strain rates at high temperatures, the maximum elongation was observed at the intermediate strain rate of 10⁰ s⁻¹, neither at the lowest nor the highest strain rates. In order to explain this phenomenon, the true stress–true strain behaviors at these three nominal strain rates were analyzed from a viewpoint of dislocation dynamics by computer-simulation with four variables of the thermal stress component σ*, dislocation immobilization rate U, re-mobilization probability of unlocked, immobile dislocations Ω and dislocation density at yielding ρ₀. It can then be concluded that the large elongation (>400% in nominal strain) at the intermediate strain rate is produced by a combination of a very large Ω and a moderate U, resulting in a large strain rate sensitivity m value.     

On the question of flow stress at high strain rates controlled by dislocation viscous flow

Moving dislocation experience a damping force because of their interactions with lattice phonons and electrons. Except at velocities close to the transverse sound velocity this force is proportional to the dislocation velocity. A high plastic strain rates dislocations may be required to move so quickly that dislocation damping forces determine the flow stress. In this note an estimate is made of strain rate at which dislocation damping becomes important. In the plastic flow stress range of 10 MPa to 100 MPa (for aluminum) the critical strain rate is of the order of 4 × 10⁵ s⁻¹to 10⁶ s⁻¹ if almost all the dislocation within a piece of metal are mobile during plastic straining. If only a small fraction of the dislocations during plastic straining is mobile, the critical strain rate is reduced by an amount equal to this fraction.     

Structural characterization of molecular beam epitaxy grown ZnSe-based layers on GaAs substrates for blue–green laser diodes

ZnSe films and fully developed p-on-n laser structures, including CdZnSe-active and ZnSSe-guiding layers were grown by molecular beam epitaxy (MBE) on lattice matched p-GaAs, p-AlGaAs and p-GaInP buffer layers. The structural characteristics of these layers were studied by combined cross-section and planar view transmission electron microscopy (TEM). The defect density of the ZnS_xSe_1−x epilayers was shown to be very low, <10⁵ cm⁻². However, on their interfaces with the GaAs substrate, a high density of small dislocation loops and clusters of the order of 3×10¹⁰ cm⁻² was observed. In situ TEM experiments revealed that dislocations and stacking faults (SFs) were generated under the electron beam influence. From them, the perfect dislocations were confined at the ZnSe/GaAs interface, while the SFs propagated to the ZnSe overgrowth or the GaAs substrate, having one of their partial dislocations at the interface. The generation of dislocations under the electron beam was not related to radiation damage but to thermal strain, which was developed by the heating effect due to differential thermal dilatation. Defects around the active zone of fully developed p-on-n laser structures were also studied. The nature of such defects was defined by Burgers vector determination experiments. The critical role of growth variations, such as compositional changes resulting in strain, in the MBE process of II–VI materials was demonstrated. The destructive role of the defected guiding layers in the laser structure was shown.     

Freezing of silver cluster and nanowire: A comparison study by molecular dynamics simulation

The crystallization of liquid Ag cluster and nanowire, about 2.3 nm in diameter, has been studied by molecular dynamics simulation at three different cooling rates (i.e., 2 × 10¹³ K/s, 2 × 10¹² K/s, 2 × 10¹¹ K/s). It is found that the structure of Ag cluster in the specified size changes from amorphous to crystalline directly during the cooling process, rather than follows the route of amorphous–icosahedra–crystalline. The Ag nanowire in the specified size also changes from amorphous to crystalline directly, rather than follows the route of amorphous–(multi-shelled)–crystalline. All the finial structures of Ag cluster and nanowire after relaxation are FCC despite the different cooling rates, which means that the FCC is the most stable structure. Furthermore, the crystallization temperature of Ag nanowire is higher than that of cluster at the same cooling rate, which suggests that the crystallization temperature is dimensional-dependent.     

高分辨X射线衍射表征氮化镓外延层缺陷密度

利用高分辨X射线衍射方法, 分析了在4H-SiC(0001)面上采用金属有机物化学气相沉积(MOCVD)生长的GaN薄膜的位错。采用对称面衍射和斜对称面衍射等方法研究了晶面倾转角、面内扭转角、晶粒尺寸和晶面弯曲半径等参数, 通过排除仪器、晶粒尺寸及晶面弯曲对摇摆曲线半高宽的影响, 从而获得GaN薄膜的螺位错密度和刃位错密度分别为4.62×10⁷ cm^-2和5.20×10⁹ cm^-2, 总位错密度为5.25×10⁹ cm^-2。     

Plastic flow in b c c solid solutions

Available data on the temperature dependence of the CRSS of potassium, sodium, niobium, tantalum and of several binary bcc alloys are examined with reference to the kink-pair process of dislocation movement described by Butt and Feltham [1]. The model is found to account for the observations on the pure metals; equally the temperature and concentration dependence of the CRSS of the alloys are encompassed by it when the alloy-atom pinning of edge dislocations becomes strong enough to render the latter less mobile under stress than the screws.     

Deformation mechanisms in tensile fracture of Al foils containing Si precipitates

Recently, Kiritani et al. proposed a new mechanism of plastic deformation without involving dislocations in tensile fracture of metal foils. The paper reports transmission electron microscopy (TEM) study of tensile fracture of Al containing hard precipitates (Si) that are considered to act as obstacles to dislocation motion. In sawtooth-shaped thin-foils formed at the fracture tip (‘sawtooth portion’), tensile strain was as high as 10³, but only a few dislocations were pinned to precipitates. Instead, voids were formed at precipitate/matrix interface, elongated in the direction of tension, and broke up into several smaller voids, due to stress concentration around hard precipitates. The thicker area of the specimen (‘base portion’), where tensile strain was 30, did not contain voids but showed a dislocation cell structure. In tensile fracture of pre-thinned specimen, voids were formed in the sawtooth portion, despite the tensile strain also being 30. These results suggest that the sawtooth portion is formed by a new mechanism that does not involve dislocations.     

Peculiar features of the dynamics of dislocations in radiated metals and alloys with giant magnetostriction

Dynamic interaction between moving dislocations and dislocation loops has been studied in radiated metals and alloys with giant magnetostriction. Dynamic retardation of moving dislocations by dislocation loops in crystals with giant magnetostriction has been analyzed. It is shown that at, high concentration of loops-in particular, in radiated crystals-this mechanism can lead to an increase in yield stress by tens of percents.     

Pressure-shear impact and the dynamic viscoplastic response of metals

Pressure-shear plate impact experiments are used to investigate the viscoplastic response of metals at shear strain rates ranging from 10⁵ s⁻¹ to 10⁷ s⁻¹. Flat specimens with thicknesses between 300 μm and 3 μm are sandwiched between two hard, parallel plates that are inclined relative to their direction of approach. Nominal stresses and strains in the specimens are determined from elastic wave profiles monitored at the rear surface of one of the hard plates. Results are reviewed for two fcc metals: commercially pure aluminum and an aluminum alloy. New results are presented for bcc high purity iron, a high strength steel alloy and vapor deposited aluminum. For commercially pure aluminum the flow stress increases strongly with strain rate as strain rate increases from 10⁴ s⁻¹ to 10⁵ s⁻¹. At strain rates above 10⁵ s⁻¹ the flow stress, based on results for thin vapor-deposited aluminum specimens, increases strongly, but less than linearly, with increasing strain rate until it saturates at strain rates between 10⁶ s⁻¹ and 10⁷ s⁻¹. Preliminary results for high purity alpha-iron indicate that the flow stress increases smoothly over eleven decades of strain rate, and faster than logarithmically for strain rates from 10² s⁻¹ to greater than 10⁶ s⁻¹. In contrast, for a high strength steel alloy the flow stress depends only weakly on the strain rate, even at strain rates at high as 10⁵ s⁻¹. Such contrasting behavior is attributed to differences in the relative importance of viscous glide and thermal activation as rate controlling mechanisms for dislocation motion in the various metals. Numerical studies indicate that experiments performed at the highest strain rates on the thinnest specimens are not adiabatic, thus requiring a full thermal-mechanical analysis in order to interpret the data.     

Deformation of thin foil of fcc and bcc metals containing pre-introduced He bubbles

Thin foil of fcc and bcc metals subjected to tensile deformation has been found to exhibit an anomalously high density of small vacancy clusters, probably in the absence of dislocations. Deformation of fcc Au and bcc Fe containing pre-introduced He bubbles is carried out, at strain rates ranging from 10⁻³ to 10⁵ s⁻¹ to a 10²% strain at −180 and 25 °C. Microstructures in the deformed regions are examined by transmission electron microscopy. Rows of bubbles are formed due to extreme elongation of bubbles under stress and its subsequent division into smaller pieces in response to vacancy diffusion around the bubble surfaces. The bubble rows are parallel to the low-index crystallographic directions, 001, 011, and 012 for Au and 011 and 001 for Fe, which can be resolved into ‘slip directions’. The results indicate that displacement of atoms in these thin-foil specimens during tensile deformation progresses while conforming to the nature of the crystal, even in the absence of dislocations.     

Stress relaxation in the interface between creep particle and elastic matrix-strengthening mechanism

The effect of a power law creep particle on interface behavior between the particle and elastic matrix is investigated by stress analysis. Using the results obtained through the stress analysis, the forces due to interaction of an applied stress and stress concentration with an edge dislocation are determined. The direct interaction between the edge dislocation and the creeping particle is studied under fully relaxed stress conditions. Through the investigation the following results are derived. Stress relaxation in the interface can be caused by power law creep along or by diffusion, or a combination of both mechanisms. The degree of stress relaxation caused by diffusion can be defined in terms of the relaxation time for both boundary diffusion and volume diffusion. The amount of stress relaxation caused by the power law creep particle is characterized by the quantity ₂ which is a function of Γ₀ = 2(1/√3)^{1 + m} × (σ_∞/2μ)^m(σ₀/σ_∞t^m), where m is strain rate hardening exponent, σ_∞ is applied stress, μ is the shear modulus, σ₀ is the material constant of the power law creep particle, and t is elapsed time. The value ₂ = 1.0 corresponds to the fully relaxed condition and ₂ = −0.6 corresponds to the initial state. The time to reach a fully relaxed condition is very sensitive to the strain rate exponent, with the smaller m values leading to longer times. The stress state of complete relaxation in the elastic matrix is equivalent to the solution of a void in an elastic matrix superposed on the solution of positive surface traction on the void. This result is identical to that obtained by Srolovitz et al. [Acta. Metall.32, 1979 (1984)]. When the stress is completely relaxed in the particle, all stress components (σ_r, σ_θand σ_rθ) are relaxed, while in the matrix relaxations are observed only for σ_rand σ_θ. The critical resolved shear stress and critical stress to climb the dislocation in the neighborhood of the particle exceed the Orowan stress. Also, the particle attracts the dislocation. Therefore the strengthening of a power law creep particle in an elastic matrix is caused by the Orowan mechanism and by attraction of the dislocation.     

The Dislocation Structure of a Single-Crystal γ + γ′ Two-Phase Alloy After Tensile Deformation

The dislocation structures of an industrial single-crystal γ + γ′ two-phase alloy DD3 after tensile deformation from room temperature to 1273K were studied by transmission electron microscopy. The strength of this alloy decreased with an increase in the temperature, and showed a strength peak at 1033K. At room temperature, the dislocations shearing the γ′ particles were found to be 1/3<112> partial dislocations on the dodecahedral slip system <112>{111}. Some dislocation pairs on the cubic <110>{100} system that blocked the glide of dislocations were found at a medium temperature of 873K. As a result, dislocation bands were formed. Shearing of γ′ particles by 1/3<112> partial dislocations on the dodecahedral slip system <112>{111} was also found at this temperature. At the peak temperature of 1033K, because of the strong interaction between dislocations on the {111} and {100} planes, the extent of dislocation bands with high dislocation densities was extensive. The 1/3<112> partial dislocations on the dodecahedral slip system <112>{111} also existed. When the temperature reached the high temperature of 1133K, the range of dislocation bands was limited. The γ′ particles were sheared by <110> dislocation pairs on the octagonal <110>{111} system and the cubic <110>{100} system. At 1273K, the regular hexagonal dislocation networks were formed in the γ matrix and at the γ/γ′ interface. The Burgers vectors of the network were found to be b₁ = 1/2[110], b₂ = 1/2[1–10], b₃ = [100], and the last one was formed by the reaction of b₁ + b₂ → b₃. Dislocations shearing the γ′ particles were found to be <110> dislocation pairs on the octagonal system <110>{111} and cubic slip system <110>{100} at 1273K.     

He+辐照对CLAM钢焊缝微观组织和性能的影响

在室温下用强度为70 ke V的He⁺辐照CLAM钢焊缝,使用扫描电子显微镜(SEM)、透射电子显微镜(TEM)和连续刚度纳米压痕技术(CSM)对其表征,研究了He⁺辐照对CLAM钢焊缝的微观组织和性能的影响。结果表明,随辐照剂量的增大焊缝表面黑色孔洞的尺寸增大、密度提高;辐照剂量为1×10¹⁷ions·cm^-2时,在两种焊缝中形成的位错环的尺寸分别约为18.97 nm、15.73 nm,数密度分别约为2.24×10²¹m^-3、1.78×10²¹m^-3,氦泡引起的辐照肿胀率分别约为1.7%和0.4%;辐照缺陷(位错环、氦泡)导致的辐照硬化率分别为49.0%和29.9%。与焊态焊缝相比,调质处理态焊缝的辐照损伤较弱,在一定程度上表明经调质处理后焊缝的抗辐照性能有所提高。     

高压扭转大塑性变形Al–Mg合金中的晶界结构*

利用透射电镜和高分辨透射电镜(HRTEM)研究了高压扭转大塑性变形纳米结构Al–Mg合金中的位错和晶界结构。结果表明: 对尺寸小于100 nm的晶粒, 晶内无位错, 其晶界清晰平直; 而尺寸大于200 nm的大晶粒通常由几个亚晶或位错胞结构组成, 局部位错密度可高达10¹⁷ m^-2, 这些位错往往以位错偶和位错环的形式出现。用HRTEM观察到了小角度及大角度非平衡晶界、小角度平衡晶界和大角度Σ9平衡晶界等不同的晶界结构。基于实验结果, 分析了局部高密度位错、位错胞和非平衡晶界等在晶粒细化过程中的作用, 提出了高压扭转Al–Mg合金的晶粒细化机制。     

Microscopic observation of cold-deformed Al–4Cu–Mg alloy samples after semi-solid heat treatments

Wrought aluminum alloys can be effectively fabricated by a strain-induced, melt-activated (SIMA) process. The SIMA method involves plastic deformation of an alloy to some critical reduction point and a semi-solid heat treatment in the solid–liquid temperature range. The semi-solid heat treatment is a key process to control the semisolid microstructures. In this paper, the microscopic morphology of a cold-deformed SIMA treated Al–4Cu–Mg alloy has been investigated, and the effects of microstructural evolution, precipitation behavior and dislocation morphology on the mechanical properties are discussed. The experimental results show that the number of CuAl₂ (θ phase) precipitates and the dislocation density of Al–4Cu–Mg alloy decreased gradually by the semi-solid heat treatment. Moreover, unique dislocation morphologies including helical dislocations and dislocation loops appeared and evolved to reduce the stored energy. With an increase of the holding time in the semi-solid heat treatment, the ultimate strength and yield strength decreased. The reduction of these mechanical properties of the SIMA treated Al–4Cu–Mg alloy is mainly due to the decrease of refinement strengthening, solution strengthening, and dislocation strengthening in the semi-solid heat treatment.     

Screw dislocation in the two-phase isotropic thin film of an interfacial crack

The screw dislocation in the two-phase isotropic thin film of an interfacial crack has been investigated. The stress field, stress intensity factors at the crack tip and for dislocation emission, crack extension force, strain energy and the image force on the dislocation are obtained and found to be related to the thickness and effective shear modulus. The effect of size on fracture is pronounced when the thickness is smaller than the distance between dislocation and crack tip by a factor of 1000. The effect of the second phase on fracture is pronounced when μ⁽²⁾/μ⁽¹⁾ is in the range from 0.01 to 100. Newton's third law is proved to be valid for any thickness and shear modulus ratio. This result can be reduced to three special cases.     

Laser-shock processing effects on surface microstructure and mechanical properties of low carbon steel

The effects of laser-shock processing (LSP) on the microstructure, microhardness, and residual stress of low carbon steel were studied. Laser-shock processing was performed using a Nd:glass phosphate laser with≈600 ps pulse width and up to 120 J pulse energy at power densities above 10¹² W cm⁻². The effects of shot peening were also studied for comparison. Laser-shock induced plastic deformation caused the surface to be recessed by≈1.5 μm and resulted in extensive formation of dislocations. Surface hardness increased by up to 80% after the LSP. The microstructure and mechanical properties were altered up to≈100 μm in depth. The LSP strengthening effect on low carbon steel was attributed to the presence of a high dislocation density. Shot peening resulted in a relatively higher compressive residual stress throughout the specimen than did LSP.     

Simulation of dislocation glide in precipitation hardened materials

Precipitation hardening is a widely used method for increasing the critical resolved shear stress (CRSS) of a material. Our simulations offer a flexible means to calculate the CRSS as a function of many parameters involved, e.g. the average precipitate size. For this, one or more dislocations are simulated while gliding through obstacle fields of arbitrary type or spatial arrangement. The elastic self-interaction is fully allowed for. Unlike analytical approaches and simulations known from literature, our method covers both shearing and circumventing of obstacles in a single model. To start with, the obstacles used in this contribution were chosen to be spheres with a constant obstacle stress inside; the distribution of the radii and the spatial arrangement suit the case of Ostwald-ripened particles. This corresponds to the case of the nickel base superalloy NIMONIC PE16 where a dislocation has to create an antiphase boundary in order to shear the long range ordered precipitates. Typical examples for dislocation arrangements are presented, and the results for various obstacle concentrations and mean radii are compared with published results.     

Internal friction and microdeformation due to the intrinsic properties of dislocations: The Bordoni relaxation

A review is presented of the relaxation phenomena due to the intrinsic properties of dislocations. The Bordoni peaks of internal friction were first observed in f.c.c. metals. Their essential features (primary and secondary characteristics) have been deduced from the ensemble of experimental results in the literature. The stability of these peaks during annealing after cold work strongly suggests that the Bordoni relaxation is linked to the intrinsic properties of dislocations. Thus, we present the principal theoretical models proposed to explain intrinsic dislocation relaxations. There are: the relaxation models based upon the thermally-activated generation of double-links, models based upon the migration of dislocation dipoles and jogs. A detailed comparison of the predictions of these models with the published experimental results leads us to the conclusion that the double-kink relaxation model is the most suitable.

The experimental results obtained on deformed h.c.p. and b.c.c. metals, ionic and covalent crystal-line materials are also reviewed. In these materials there are many relaxation phenomena attributed to dislocations, and there is a good deal of variability in the results reported from one laboratory to another. A coherent picture appears to be emerging in the case of h.c.p. and b.c.c. metals; but at present, it is difficult to attribute a precise mechanism to each internal friction peak.

In addition, studies are reviewed of microplasticity in the temperature range of the Bordoni relaxation. A correlation between the mechanisms of microplasticity and internal friction is demonstrated. This analysis yields an estimate of the Peierls stress in f.c.c. metals of about 10⁻⁴ μ.