30CrlMo1V钢蠕变性能研究

测试了30CrlM01V钢的蠕变极限,通过透射电镜对稳态蠕变阶段位错的结构、分布、组态及其运动方式进行了探讨。试验结果表明,蠕变稳态阶段位错的运动是以滑移为主,稳态蠕变速率受位错的攀移控制。     

一种单晶镍基合金蠕变期间位错网的形成与作用

对「００１」取向单晶镍基合金的恒温拉伸蠕变组织形貌的ＴＥＭ观察表明，蠕变初期，基体γ相八面体滑系中两组１／２〈１１０〉位错运动至同一晶面相遇，发生反应形成三维节点的位错网络；稳态期间，其体中运动位错可通过界面位错网攀移过筱状γ’相；蠕变形变的特征是运动位错在位错网损坏处切处筏状γ’相内。     

Ti65合金的初级蠕变和稳态蠕变

使用透射电镜(TEM)研究了Ti65合金在600~650℃、120~160 MPa条件下的蠕变变形行为及其微观变形机制。结果表明：初级蠕变变形机制主要由受攀移控制的位错越过α₂相的过程主导;稳态蠕变阶段蠕变机制主要由受界面处扩散控制的位错攀移的过程主导,且应力指数为5~7。在初级蠕变阶段α₂相与位错的相互作用是α₂相对合金高温强化的主要方式,在稳态蠕变阶段沿α/β相界分布的硅化物阻碍位错运动与限制晶界滑移是硅化物对合金强化的主要方式。     

热挤压AZ31镁合金的组织结构与蠕变行为

通过对热挤压态AZ31镁合金进行组织形貌观察、内摩擦应力测定及蠕变性能测试,研究了热挤压AZ31合金的组织结构和蠕变行为.结果表明:热挤压AZ31镁合金的组织具有带状结构特征,并沿轧制方向分布,且有β-Mg17Al12相在合金中弥散析出.蠕变期间,位错运动的内摩擦力有较强的温度敏感性,随温度增加,内应力值明显降低,致使合金具有较高的蠕变速率.合金在蠕变期间,大量位错的形成与运动是蠕变初期的变形机制;蠕变稳态阶段,高密度位错逐渐束集形成位错胞,进一步发生蠕变期间的动态再结晶.随裂纹在晶界处萌生使蠕变进入第三阶段,而裂纹沿晶界韧性撕裂扩展是合金的蠕变断裂机制.     

SiCw／6061A1复合材料温度循环拉伸变形行为

本文采用热循环拉伸试验方法研究了ＳｉＣｗ／６０６１Ａ１复合材料的变形行为．结果表明，ＳｉＣｗ／６０６１Ａ１复合材料温度循环拉伸变形行为与蠕变类似分为初始变形阶段、稳态变形阶段和快速断裂三个阶段；温度循环拉伸变形稳态流变速率明显提高；温度循环拉伸变形的应力指数低于恒温蠕变的应力指数．     

一种含4.2%Re单晶镍基合金的蠕变行为与组织演化规律

通过蠕变曲线测定及组织形貌观察,研究了一种含4.2%Re镍基单晶合金的蠕变行为和组织演化规律。结果表明:单晶合金在试验的温度和应力范围内,对施加应力和温度有明显的敏感性,并测算出合金在稳态蠕变期间的激活能和应力指数。在蠕变初期,合金中γ′相沿垂直于应力轴方向形成N-型筏状结构,蠕变断裂后在远离断口区域形成的筏状γ′相逐渐转变成扭曲形态,在近断口区域的筏状组织转变成与施加应力轴方向呈近45°角度倾斜。合金在稳态蠕变期间的变形机制是位错攀移越过γ′相,位错的攀移通过割阶沿位错线运动而逐步实现;而在蠕变后期,合金的变形机制是位错剪切筏状γ′相。     

单晶镍基合金高温蠕变期间的组织结构及演化

通过测定［００１］取向单晶镍基合金的蠕变曲线，结合ＳＥＭ、ＴＥＭ观察表明，合金中组织结构的变化对蠕变抗力有明显影响。蠕变Ⅰ、Ⅱ阶段，蠕变的微观机制是位错的攀移；蠕变第三阶段，位错大量切入筏状γ相中，降低了合金的蠕变抗力，发现交替滑移使筏状γ相扭曲，致使γ／γ两相界面产生空穴或微裂纹，是蠕变断裂的直接原因。     

初始状态对2124铝合金蠕变时效行为与力学性能的影响

通过光学、透射电子显微、蠕变与室温拉伸实验研究了2124铝合金板的蠕变时效行为与力学性能。结果表明:185℃/150MPa条件下,经固溶-淬火处理(QCA)板材的蠕变机制从位错增殖发展为位错增殖-消毁平衡,其蠕变曲线第一阶段与第二阶段分界点较为明显;而经固溶-淬火-预压缩处理(PCA)板材的蠕变机制主要为预压缩引入的位错消毁,蠕变曲线第一阶段特征并不明显。蠕变时效过程中,S′相的析出总是伴随着位错线形核,其析出方位受位错运动机制的影响,PCA处理初期,经预压缩引入的位错缠结使S′相可以在互相垂直的{210}面上析出,从而抑制了S′相的位向效应。PCA处理试样的力学性能优于该合金的T6和T87状态的,且各向异性小于QCA处理的。     

锰对铸态ZA27合金压缩蠕变的影响

本文采用自制的试验装置研究了锰对铸态ZA27合金压缩蠕变行为的影响。结果表明，在所试验的温度为20℃到160℃和压应力为50MPa到137.5MPa的范围内，ZA27-Mn和ZA27合金的第一阶段压蠕变量和稳态蠕变速率随着温度和应力的增高而增大，但ZA27-Mn合金的第一阶段的蠕变量和稳态蠕变速率低于ZA27合金。两种合金的压蠕变均符合Int=C-nln Q/RT，材料结构常数C不同合金压蠕变不同，ZA27-Mn合金的应力指数n和蠕变激活能Q分别为3.89和83.97KJmol^-1合金的应力指数和蠕变激活能分别为3.46和81.09KJmol^-1，合金的压蠕变由锌的点阵自扩散和位错的攀移控制。在整个试验温度和应力范围内，ZA27-Mn合金的压蠕变抗力高于ZA27合金。     

Ti-6Al-3Nb-2Zr-1Mo合金室温压缩蠕变行为及位错类型研究

研究Ti-6Al-3Nb-2Zr-1Mo合金在不同外加应力下的室温压缩蠕变行为,拟合了蠕变曲线,计算出蠕变发生第二阶段的临界值,并对不同应力水平压缩后的合金显微组织进行TEM观察,研究其位错滑移类型.结果表明:室温条件下,Ti-6Al-3Nb-2Zr-1Mo合金压缩蠕变-时间曲线符合时间强化指数模型,该合金发生蠕变第二...     

The high-temperature creep behaviour of an Al-1 wt% Cu solid-solution alloy

The creep behaviour of an Al-1 wt% Cu solid-solution alloy is investigated at a temperature of 813 K under stress range of 0.5–5 MPa. The creep characteristics of the alloy including the stress dependence of the steady-state creep rate (n=4.4), the shape of creep curve (normal primary stage), the transient creep after stress increase, and the value of the true activation energy for creep, suggest that some form of dislocation climb is the rate-controlling process at higher stresses above 1 MPa. However, at low stresses (< 1 MPa), the creep curves show no distinguished steady state, and the stress dependence of the minimum creep rate is as high as ～ 8. The creep behaviour of the alloy is discussed based on recent theories available for describing creep in solid-solution alloys.     

Microstructure evolution and its influence on deformation mechanisms during high temperature creep of a nickel base superalloy

The interaction of dislocation with strengthening particles, including primary and secondary γ′, during different stages of creep of Rene-80 was investigated by scanning electron microscopy (SEM) and transmission electron microscopy (TEM). During creep of the alloy at 871 °C under stress of 290 MPa, the dislocation network was formed during the early stages of creep, and the dislocation glide and climb process were the predominant mechanism of deformation. The density of dislocation network became more populated during the later stages of the creep, and at the latest stage of the creep, primary particles shearing were observed alongside with the dislocation glide and climb. Shearing of γ′ particles in creep at 871 °C under stress of 475 MPa was commenced at the earlier creep times and governed the creep deformation mechanism. In two levels of examined stresses, as far as the creep deformation was controlled by glide and climb, creep curves were found to be at the second stage of creep and commence of the tertiary creep, with increasing creep rate, were found to be in coincidence with the particles shearing. Microstructure evolution, with regard to γ′ strengthening particles, led to particles growth and promoted activation of other deformation mechanisms such as dislocation bypassing by orowan loop formation. Dislocation-secondary γ′ particles interaction was detected to be the glide and climb at the early stages of creep, while at the later stages, the dislocation bypassed the secondary precipitation by means of orowan loops formation, as the secondary particle were grown and the mean inter-particle distance increased.     

Contribution of coarsening of MX carbonitrides to creep strength degradation in high chromium ferritic steel

Abstract

The coarsening process of MX carbonitrides during creep and its effect on creep behaviour have been investigated for P92 steel (9Cr-0.5Mo-1.8W-VNb). At 1023 K after long term aging, creep rupture strength and tertiary stage creep rate rapidly decrease and increase, respectively. The stress exponent n of minimum creep rate decreases with increasing temperature, and the value of n at 1023 K was evaluated to be 5.7. MX carbonitrides coarsen during creep and the coarsening process corresponds to the early stage of Ostwald ripening. Creep deformation accelerates the coarsening of the MX carbonitrides. At 1023 K, the coherent strain between the MX carbonitrides and matrix reduces to a negligibly small value at times longer than 550 h, leading to a decrease in the resistance to dislocation motion. This contributes to the rapid increase of creep rate in the tertiary stage and the abrupt decrease of creep rupture strength in the long term.     

Microstructure evolution and deformation features of AZ31 Mg-alloy during creep

By means of the measurement of the creep curve and the observation of SEM and transmission electron microscope (TEM), an investigation has been made into the microstructure evolution and deformation features of AZ31 Mg-alloy during high temperature creep. Results show that the deformation features of the alloy in the primary stage of creep are that significant amount of dislocation slips are activated on basal and non-basal planes, then these ones are concentrated into the dislocation cells or walls as creep goes on. At the same time, twinning occurs as an additional deformation mechanism in the role of the compatibility stress. During steady state creep, the dislocation cells are transformed into the subgrains, then, the protrusion and coalition of the sub-boundaries results in the occurrence of dynamic recovery (DRV). After the dynamic recrystallization (DRX), the multiple slips in the grain interiors are considered to be the main deformed mechanism in the later stage of the steady state creep. An obvious feature of creep entering the tertiary stage is that the cracks appear on the locations of the triple junction. As creep continues, the cracks are viscous expanded along the grain boundaries; this is taken for being the fracture mechanism of the alloy crept to failure. The multiple slips in the grain interiors and the cracks expanded viscous along the grain boundary occur in whole of specimens, that, together with the twins and dynamic recrystallization, is responsible for the rapid increase of the strain rate in the later stage during creep.     

The formation of multipoles during high-temperature creep of austenitic stainless steels

It is shown that multipole dislocation configurations can arise during power-law creep of certain austenitic stainless steels. These multipoles have been analysed in some detail for two particular steels (Alloy 800 and a modified AISI 316L) and it is suggested that they arise either during instantaneous loading or during the primary creep stage. Trace analysis has shown that the multipoles are confined to {1 1 1} planes during primary creep but are not necessarily confined to these planes during steady-state creep unless they are pinned by interstitials.     

Effect of initial temper on the creep behavior of a Mg–Gd–Nd–Zr alloy

The effect of initial temper on the tensile creep behavior of a cast Mg–Gd–Nd–Zr alloy has been investigated. Specimens in unaged, underaged and peak-aged conditions exhibit a sigmoidal creep stage between the primary and steady-state creep stage, while the overaged specimens have no such creep stage. Transmission electron microscope observations revealed that sigmoidal creep stage was induced by the dynamic precipitation in the microstructure, and the rapid formation of β₁-phase and β-phase plates takes responsibility for the softening of material in this stage. Comparative evaluation of creep properties of the specimens showed that alloy in overaged condition had creep resistance superior to those in other conditions. Stress and temperature dependence of the steady-state creep rate were studied over a temperature range of 250–300 °C and stress range of 50–100 MPa, and a dislocation creep mechanism was proposed for the alloy.     

Al-3.36wt-%Mg合金在中温循环蠕变时的应变突发行为

Al-3.36wt-%Mg 合金在中温下的循环蠕变实验结果表明,在一定的温度和应力范围内,循环蠕变的第一和第二阶段都有应变突发发生,且这类应变突发具有明显的周期性,是动态应变时效的结果。根据 McCormick 提出的位错与溶质原子交互作用模型,讨论了应变突发时的位错运动机制,从而说明了应变突发周期随应变速率单调变化的规律。     

Effects of cyclic stress on the creep behaviour and dislocation microstructure of pure copper in the temperature range 0.4 to 0.5T m

The creep deformation behaviour of polycrystalline pure copper under static and cyclic stress was studied in the temperature range 0.4 to 0.5T _m. Both cyclic creep acceleration and retardation occurred depending on the condition of peak stress and temperature combination. The comparison of dislocation microstructures, developed during steady state static and cyclic creep deformation, has also been performed to determine the effect of cyclic stress on the dislocation microstructure and evidence for the enhanced recovery of the cell wall under cyclic stress was found. These effects of cyclic stress on the creep rate and dislocation microstructure were interpreted on the basis of diffusion-controlled recovery creep theory and the cyclic creep acceleration mechanism is suggested as the enhanced recovery of the cell wall with the help of athermally generated excess vacancies.