Macroscopic dislocation model of a wedge twin with allowance for the shape of its boundaries

Stress fields for wedge twins with various shapes of boundaries are calculated on the basis of a macroscopic dislocation model. It is shown that the deviation of a wedge twin from a symmetric shape leads also to the loss of symmetry in the stress-field distribution near the twin. Cases of a uniform and an equilibrium distribution of twinning dislocations at twin boundaries are considered.     

Plasticity of bcc micropillars controlled by competition between dislocation multiplication and depletion

Recent micropillar experiments have shown strong size effects at small pillar diameters. This “smaller is stronger” phenomenon is widely believed to involve dislocation motion, which can be studied using dislocation dynamics (DD) simulations. In the present paper, we use a three-dimensional DD model to study the collective dislocation behavior in body-centered cubic micropillars under compression. Following the molecular dynamics (MD) simulations of Weinberger and Cai, we consider a surface-controlled cross-slip process, involving image forces and non-planar core structures, that leads to multiplication without the presence of artificial dislocation sources or pinning points. The simulations exhibit size effects and effects of initial dislocation density and strain rate on strength, which appear to be in good agreement with recent experimental results and with a simple dislocation kinetics model described here. In addition, at the high strain rates considered, plasticity is governed mainly by the kinetics of dislocation motion, not their elastic interactions.     

Study on dislocation multiplication in the head of Germanium single crystal

The high strength, radiation hardness and cost-effectiveness make Germanium the substrate of choice for high-efficiency multi-junction solar cells for space applications.Numerical modeling and large-scale simulation are important and indispensable tools in the analysis and development of crystal growth process.In this study, germanium single crystals with low dislocation density were produced by Czochralski method by applying the necking technique.Chemical etching pits method was used to measure the dislocation density, and a professional modeling software CrysVUn was used to obtain the thermal-stress distribution.The results show that the thermal-stress of the sample with diameter of 15 mm is nearly equal to that of other samples, so the thermal-stress does not influence the dislocation multiplication.Based on the result, the dislocation density must be strangely increased caused by gravity.     

On the multiplication of dislocations during martensitic transformations in NiTi shape memory alloys

In situ and post-mortem diffraction contrast transmission electron microscopy (TEM) was used to study the multiplication of dislocations during a thermal martensitic forward and reverse transformation in a NiTi shape memory alloy single crystal. An analysis of the elongated dislocation loops which formed during the transformation was performed. It is proposed that the stress field of an approaching martensite needle activates an in-grown dislocation segment and generates characteristic narrow and elongated dislocation loops which expand on {1 1 0}_B2 planes parallel to {0 0 1}_B19′ compound twin planes. The findings are compared with TEM results reported in the literature for NiTi and other shape memory alloys. It is suggested that the type of dislocation multiplication mechanism documented in the present study is generic and that it can account for the increase in dislocation densities during thermal and stress-induced martensitic transformations in other shape memory alloys.     

The evolution of dislocation density during heat treatment and creep of tempered martensite ferritic steels

The evolution of dislocation density in two tempered martensite ferritic steels (a 12% and a 9% chromium steel, “X20” and “P91”) during heat treatment and creep is analyzed using transmission electron microscopy (TEM) and X-ray diffraction (XRD); both methods yield results which are in good agreement when rationalizing the XRD-data based on densities of free dislocations. It is shown that due to the intermediate formation of martensite, standard heat treatments produce very high dislocation densities in tempered martensite ferritic steels (TMFSs). Long term tempering and creep are characterized by a decrease of dislocation density; but dislocation densities are still high as compared to alloys where the formation of microstructure does not involve a martensitic transformation. A heterogeneous microstructure after long term tempering and creep is a characteristic feature of TMFSs. Micro grains with high dislocation densities co-exist next to micro grains without dislocations. The XRD method yields average data and cannot account for this microstructural heterogeneity; but it supports the TEM results which in isolation suffer from providing insufficient statistics. The results of the present study are discussed in the light of earlier work published in the literature and contribute to a better understanding of the role of free dislocations in TMFSs during tempering, creep and high temperature low cycle fatigue.     

Characteristics of dislocation structure in creep deformed lamellar tial alloy within primary regime

In this investigation, dislocations of a lamellar TiAl alloy are analyzed after creeping in the primary range at 800°C/200MPa in order to interpret their mobility It was found that the dislocation density in γ-laths decreased as the creep deformation proceeds within primary creep regime Schmid factor analysis suggests that the creep deformation in the early stage of the primary creep regime is controlled by the gliding of some of the initial dislocations which have a high enough Schmid factor As the creep deformation progressed, those dislocations with high Schmid factors slip preferentially to be annihilated at the α-γ interface For further continuous deformation, dislocation generation is required, and for this, α-phase is transformed to γ-phase in order to generate new dislocations A slow dislocation generation process by phase transformation of α-phase compared with the absorbing rate to sinks is responsible for the decreasing dislocation density as the creep strain increases     

High temperature deformation mechanism and evolution of dislocation structure during creep of Ni-Base superalloy 713LC

Creep deformation of cast nickel base superalloy 713LC has been investigated in a temperature range of 723 to 982°C. The values of the stress exponent and activation energy for creep of the alloy vary with a combination of temperature and stress. Introduction of threshold stress for creep of the alloy provided an explanation of the high values of the stress exponent and the apparent activation energy. Microstructural evolution of the alloy with creep deformation has also been studied. The analysis of the creep mechanism has been supplemented by microstructural observations after deformation under various test conditions. The dislocation structure of the alloy at high temperature and low stress was different from that at low temperature and high stress. Shearing of γ′ particles by dislocation pairs was the dominant creep mechanism at low temperature and high stress whereas dislocation climb over γ′ particles was the rate controlling process of creep at high temperature and low stress.     

Interfacial dislocation mechanism for diffusional phase transformations exhibiting martensitic crystallography: formation of TiAl + Ti3Al lamellae

The displacive–diffusive transformation, which gives rise to lamellar γ-TiAl+α₂-Ti₃Al microstructures, has been analysed theoretically. Using the formulation due to Hirth and Pond, the shear produced and extent of diffusional flux associated with interfacial defect motion can be quantified in terms of the Burgers vectors, step heights of the defects and the chemical compositions of the adjacent crystals. Moreover, this formulation also enables the effects of chemical composition, misfit at the interface and ordering to be investigated systematically. It is shown that for the defects observed on such interfaces in recent high-resolution transmission electron microscopy studies, their motion would lead to the conservation of sites and, correspondingly, to equal and opposite fluxes of Ti and Al atoms. Consequently, although this transformation is diffusional, it exhibits crystallographic features consistent with martensitic processes.     

Model of grain-boundary diffusion with allowance for near-boundary layers of equilibrium composition

Fisher model of intercrystalline diffusion is refined based on an analysis of previously obtained results of emission Mössbauer studies of grain boundaries. It is shown that under conditions of dominating intercrystalline diffusion, the existence of monatomic near-boundary layers of equilibrium composition should be taken into account. It has been found that the allowance for these layers does not change the expressions for the distribution of the concentration of the diffusing impurity in a polycrystal in the case of a type-B kinetic regime, whereas in the type-C regime the corresponding expressions change somewhat. The technique that was used previously for the determination of parameters of grain-boundary diffusion and segregation, which is based on the results of emission Mössbauer investigations of grain boundaries, has been modified; the application of the new approach has been demonstrated on the example of processing data of Mössbauer investigations of grain boundaries in polycrystalline Nb at ^119mSn nuclei.     

Characterization of creep and creep damage by in-situ microtomography

Application of in-situ microtomography to characterization of power law creep and creep damage in structural materials is presented. It is shown first that the successively reconstructed volumes are adequately monitoring the macroscopic sample shape and that microtomography is an optimal tool to characterize inhomogeneous specimen deformation. Based on a two-step image correlation technique the evolution of single voids is revealed and the basis of a pioneering approach to creep damage studies is presented. The method allows the unequivocal separation of three concurrent damage mechanisms: nucleation, growth, and coalescence of voids. The results indicate that growth rate of voids with equivalent diameters in the range of 2–5 mm is of about one order of magnitude higher than the prediction of continuum solid mechanics. Analysis of void coalescence points out the presence of two stable growth regimes related to coalescence between primary and secondary voids, respectively.     

GH4169合金小余量小尺寸静子叶片锻造工艺及显微组织控制

针对GH4169合金叶片锻件粗晶、混晶等晶粒组织不合格问题,以某压气机小余量小尺寸静子叶片锻件为研究对象,首先分析锻件结构,确定锻造工艺路线,然后通过选取2种规格坯料、5个变形量、4个锻造温度来组成12组试验,探究变形量、锻造温度对组织的影响以及演化规律,同时对选取的保温时间、锻造火次的稳定性进行分析,得到合理锻造工艺参数。研究表明,变形量在35%~45%内可获得均匀的组织,但对晶粒度大小无明显影响;温度是影响晶粒度的主要因素,大于1000℃时叶身晶粒粗化现象明显,在990~1000℃之间叶身可获得细腻、均匀的组织;预锻时组织已成形稳定,终锻无明显变化,在选取的保温时间内组织稳定;在变形量40%及锻造温度990℃下获得的叶片锻件具有优良的综合力学性能及细晶组织,均高于标准要求。     

Predicting creep strengths and lifetimes of creep resistant engineering alloys

The physical basis for predicting the long-term creep strengths and lifetimes at application temperatures using creep parameters determined from short-term creep tests is investigated for complex creep resistant engineering alloys. It is shown that the seemingly unpredictable stress and temperature dependence of minimum creep rate of such alloys can be rationalised using an approach based on the new power law creep equation that incorporate the tensile strength. This is demonstrated using the tensile and creep data measured for two completely different types of alloys: steel 11Cr-2W-0.4Mo-1Cu-Nb-V and Ni base superalloy 15Cr-28Co-4Mo-2.5Ti-3Al. For both alloys, the stress exponent n determined does not depend on temperature and activation energy of creep does not depend on stress. Consequently, it becomes possible to use the new power law creep equation in combination with the Monkman-Grant relationship to predict the long term creep rupture strengths and lifetimes and microstructure stability of the two alloys from short term creep test data. The implications of the results for creep mechanism identification and future microstructure analysis are discussed.     

低倍数泡沫灭火系统设计探讨

介绍了中国铝业股份有限公司河南分公司扩建700kt/a氧化铝工程中的储油罐消防设计过程.     

Apparatus for investigating phase transformations and properties of metals and alloys with programmed electromechanical treatment

Conclusions An apparatus was developed for investigations of phase transformations and mechanical properties under programmed thermal and mechanical conditions, which makes it possible to study electrothermal treatment processes under any desired conditions, high-temperature thermomechanical treatment, lowtemperature thermomechanical treatment, machining, and treatment to obtain superplasticity.This paper will be presented at the All-Union Symposium on New in Metal Science and Heat Treatment of Metals and Alloys, September 10–12, 1975, in Minsk.Peoples Republic of Bulgaria. Translated from Metallovedenie i Termicheskaya Obrabotka Metallov, No. 8, pp. 74–76, August, 1975.     

On the effect of grain boundary segregation on creep and creep rupture

The present work investigates the effect of grain boundary chemistry and crystallography on creep and on creep damage accumulation in Cu–0.008 wt.% Bi and Cu–0.92 wt.% Sb at stresses ranging from 10 to 20 MPa and temperatures between 773 and 873 K. Small additions of Bi and Sb significantly reduce the rupture strain and rupture time during creep of Cu. High stress exponents (Cu–Bi) and high apparent activation energies for creep (Cu–Bi and Cu–Sb) are obtained. Sb promotes creep cavitation on random high-angle grain boundaries. Bi, on the other hand, causes brittle failure when small crack-like cavities cause decohesion. Both elements suppress dynamic recrystallization, which occurs during creep of Cu at high stresses and temperatures.