Mg-11Gd-2Y-1.5Ag-0.5Zr合金的高温蠕变行为

本工作研究了Mg-11Gd-2Y-1.5Ag-0.5Zr合金在225～275℃/110～150 MPa条件下的高温蠕变行为和组织演变.结果表明:合金在225℃/110～150 MPa蠕变状态下,蠕变应力指数n=3.4,蠕变机制为位错滑移机制;在250℃/110～150 MPa蠕变状态下,蠕变应力指数n=4.7,蠕变机制为位错滑移机制;在275℃/110～130 MPa蠕变状态下,蠕变应力指数n=5.8,蠕变机制为位错滑移机制;在275℃/130～150 MPa蠕变状态下,蠕变应力指数n=10.5,幂律蠕变定律失效,蠕变机制较为复杂.根据蠕变激活能Q值对蠕变机制的分析结果与蠕变激活能n值分析结论基本一致.合金在同一温度下,晶粒尺寸随着应力的增大而增大;在同一应力下,晶粒尺寸随着温度的升高而减小.在本研究中,110～150 MPa的高应力范围内,合金在250℃以下有着良好的抗蠕变性能.     

FGH95粉末镍基合金的组织结构与蠕变特征

通过蠕变曲线的测定及组织形貌的观察,研究了FGH95粉末镍基合金的蠕变行为及变形特征.结果表明:FGH95粉末镍基合金在试验的温度和应力范围内,具有明显的施加温度和应力敏感性,并测算出合金的蠕变激活能和应力指数.合金的组织结构由一次、二次、三次γ'相及弥散分布的碳化物组成,在粉末颗粒之间具有较宽的晶界.蠕变期间,在合金晶粒内的变形以单取向或双取向滑移方式进行,并在滑移迹线附近有细小碳化物析出,而较宽的晶界由于剧烈变形可发生碎化形成细小晶粒.合金在蠕变期间的微观变形机制是位错发生双取向滑移,其中(1/2)《110》位错在γ基体相中运动,《110》超位错存在于γ'相内,而层错的形成是由于《110》超位错分解为(1/3)《112》超肖克莱不全位错所致.     

原位反应液相线铸造半固态铝合金的晶粒长大行为

采用原位反应液相线铸造方法制备含有少量原位TiC颗粒的7075铝合金,在其固液两相区进行二次加热保温实验,淬火固定其半固态组织后,通过扫描电镜观察合金的晶粒长大行为,并利用平均截线法测量晶粒尺寸,研究原位颗粒对晶粒长大行为的影响.结果发现,原位TiC颗粒不仅对合金的铸态组织产生细化和球化作用,而且在合金的二次加热过程中对晶粒长大行为具有明显的抑制作用,从而对优化半固态组织提供了一种有效的方法.     

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。     

固溶处理的热连轧GH4169合金的组织与蠕变特征

通过对热连轧GH4169合金进行固溶和时效处理、组织形貌观察和蠕变性能测试,研究了固溶和时效处理合金的组织结构和蠕变特征。结果表明,经固溶和时效处理合金由较大尺寸晶粒组成,并具有明显的孪晶特征,且细小γ′、γ″相在晶内弥散析出,可提高合金的蠕变抗力;在实验应力和温度范围内,测得该合金的蠕变激活能为537.8kJ/mol,且对施加应力和温度具有敏感性;在蠕变期间,热连轧GH4169合金的变形特征是位错的单双取向滑移和孪晶变形,随着蠕变进行,裂纹沿晶界萌生和扩展到发生沿晶断裂是该合金的蠕变断裂机制。     

GH3536合金的蠕变性能及蠕变行为

对GH3536合金在815～900℃不同应力水平下进行了高温蠕变试验,绘制了蠕变曲线并讨论了试验温度和试验应力水平对GH3536合金蠕变性能的影响规律,通过最小二乘法拟合得到了稳态蠕变速率的应力指数和Monkan-Grant关系式的参数,采用L-M参数法建立了外推公式,并对GH3536合金的蠕变断裂强度进行了外推。结果表明:在试验温度和试验应力水平下,GH3536合金的高温蠕变机制主要为位错的滑移和攀移,蠕变过程中有第二相析出,在晶界以及第二相颗粒处形成R型和W型裂纹;蠕变断裂由颈缩引起,为韧性断裂,断裂过程中发生了微孔的聚集和长大;根据外推公式GH3536合金在815℃下蠕变断裂时间2 000h所对应的蠕变断裂强度为58MPa。     

原位自生(TiB+TiC)/Ti-1100复合材料的高温力学性能及强化机制

利用常规钛合金的真空自耗熔炼以及热加工技术,制备了原位自生(TiB+TiC)/Ti-1100复合材料。对该复合材料的微观结构进行研究,并分别在高温环境下测试了基体合金以及复合材料的高温拉伸性能,最后对其强化机制进行研究。结果表明:钛基复合材料的屈服强度可以用数学模型来计算。增强体的加入使复合材料的高温力学性能明显优于基体合金,且其高温强度的提高主要受益于碳的固溶强化、TiB纤维的传递载荷、TiC颗粒的强化位错等因素的贡献。     

Al_2O_3-SiO_(2(sf))/AZ91D镁基复合材料蠕变本构方程

利用常应力拉伸蠕变试验法对体积分数为25%的硅酸铝短纤维(Al2O3-Si O2(sf))增强AZ91D镁基复合材料及其基体合金AZ91D在温度为473 K和573 K、外加应力为30～100 MPa下进行蠕变测试。根据应变和应变速率曲线,计算出复合材料的真应力指数、真蠕变激活能、真门槛应力、载荷转移因子和蠕变本构方程。TEM分析结果表明,复合材料蠕变后的门槛应力来源于短纤维表面上的MgO颗粒和Mg17Al12析出相对可动位错的钉扎作用,短纤维具有承载和传递载荷作用,从而提高了复合材料的抗蠕变性能。     

锰对ZA27合金压缩蠕变的影响

为了解质量分数为0.5%Mn对铸态ZA27合金压缩蠕变行为的影响,采用自制的试验装置研究了ZA27-Mn合金和ZA27合金第一阶段的压蠕变量和稳态蠕变速率.结果表明:ZA27-Mn合金第一阶段的压蠕变量和稳态蠕变速率低于ZA27合金,而两种合金的压蠕变均符合于lnt=C-nlnσ Q/RT,ZA27-Mn合金的应力指数(n)和蠕变激活能(Q)分别为3.83和82.76 kJ·mol-1,而ZA27合金的应力指数和蠕变激活能分别为3.46和81.09kJ·mol-1,材料结构常数C不同,合金压蠕变不同,ZA27-Mn合金的压蠕变抗力高于ZA27合金;加入0.5%Mn对ZA27合金蠕变机制并无影响,均是锌的点阵自扩散和位错的攀移机制.     

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.     

Microstructure and properties of austenitic stainless steel reinforced with in situ TiC particulate

Austenitic stainless steel reinforced with 5 vol.% TiC particulate was in situ synthesized by in situ reaction during melting process successfully and its microstructure, mechanical properties as well as oxidation behavior were investigated. Microstructure observations revealed that in situ TiC particulates with an average size of 2–10 μm distributed uniformly in the matrix and the interface boundaries between TiC particulates and austenite matrix were clean without any impurities and contaminations. Addition of TiC particulates refined the grain structure of austenitic matrix, but did not cause formation of any new phases in microstructure. Beneficial effects of TiC addition to austenitic stainless steel on both mechanical properties and oxidation resistance were found. Both at ambient and elevated temperature, tensile strengths of the steel with TiC addition were notably higher than those of its matrix alloy, however, a decrease in ductility also appeared, as exhibited by other particulate reinforced alloys. Besides tensile strengths, creep resistance of austenitic stainless steel was also significantly increased by TiC addition at elevated temperature of 923 K. Oxidation test at 1073 K revealed that TiC addition to austenitic stainless steel raised the oxidation resistance of the steel remarkably.     

A parameter for power law creep

Experimental investigations on the creep rupture behaviour of type 304, 304£ and 316 stainless steels, a nickel-base superalloy SuperNi 600 and a turbine disc alloy (equivalent to MAR M 200) have been carried out. Stainless steels 304£ and 316 have been tested with and without weldment, and materials 304 SS and SuperNi 600 have been tested with and without corrosive coatings. MAR M 200 was tested in air. A parametric method is suggested for obtaining the master curves for these alloys under test conditions. The applicability of the parameter to 25-20 stainless steel and a modified nuclear grade 316 type stainless steel has been verified.     

Effect of TiC and NbC carbides on creep life of stainless steels

The effect of TiC and NbC carbides on creep life has been investigated for 321HTB and 347HTB steels at 600–750°C for about 20–200,000 h. The creep data for 304HTB steel are used as reference data. The precipitation hardening is larger for the 321HTB than for the 347HTB at short times during creep. Then the reduction of precipitation hardening due to coarsening of TiC and NbC carbides takes place for up to long times, which is less significant in the 321HTB than in the 347HTB. The smaller coarsening rate of the TiC carbides than the NbC carbides during creep is discussed on the base of a rate equation for diffusion-controlled Ostwald ripening.     

Evaluation of electroslag remelting in TiC particle reinforced 304 stainless steel

This study is focused on the effect of electroslag remelting (ESR) on microstructure and mechanical properties of TiC particle reinforced 304 stainless steel synthesized by in situ reaction in vacuum introduction melting (VIM). Microstructure observations revealed that applying ESR process resulted in a more uniform distribution of TiC particles with reduced size, however, a slight aggregation with large TiC particles existed in the VIM ingot was found. Additionally, some tiny TiC precipitates with nano-scale were observed in the microstructure of the TiC reinforced steel after ESR process. Introduction of in situ TiC particles into the 304 stainless steel caused a significant increase of tensile properties, creep properties and wear resistance, but a decrease in ductility. Moreover, further improvement on tensile properties, creep properties, wear resistance as well as the ductility of the steel were obtained by using ESR process successfully.     

基于EBSD技术的P91钢蠕变过程中小角度晶界演化行为表征

在620℃、145 MPa条件下对给定的P91钢进行高温蠕变持久与间断试验,采用电子背散射衍射(EBSD)技术研究其在蠕变过程中小角度晶界的演化行为。通过引入EBSD图像中的取向差分布来表征小角度晶界处(0.5~5°)的边界位错密度,分析了边界位错密度在蠕变过程中与小角度边界的数量、塑性应变以及内部微观组织演化之间的关系。此外,通过改变EBSD像素点与像素点之间的计算步长,探讨了步长选择对边界位错密度计算结果的影响。结果表明,小角度晶界处的位错密度在蠕变过程中先迅速上升,在最小蠕变率处达到极值后缓慢下降,直到最后基本保持不变;同时,EBSD的计算步长越小,得到的位错密度值越准确。     

CONTINUOUS SEM OBSERVATIONS OF CREEP-FATIGUE DAMAGE PROCESSES

In order to examine the relation between damage evolution and changes in microstructure, e.g. from creep cavities, surface micro-cracks and dislocation structures at high temperature, strain controlled creep-fatigue tests were performed and interrupted at several damage levels on Types 304 and 316 stainless steels. The creep-fatigue tests on Type 304 stainless steel at a low strain level were conducted in a high-temperature fatigue testing machine combined with a scanning electron microscope, and the micro-crack initiation and growth behaviour were continuously observed to clarify the damage extension mechanism. It was found that even though many cavities were initiated and grew on the internal grain boundaries of the specimens during the strain-controlled tests, the failure life was governed by the propagation of surface cracks. On the other hand, micro-cracks of about the order of one grain size were initiated mainly along grain boundaries normal to the loading axis under low stress creep-fatigue, and the crack propagation rate of the micro-cracks was slow and random due to the nature of the microstructures. The micro-cracks gradually opened in the loading direction with increasing number of cycles and coalescence contributed to growth.     

Nanoindentation creep deformation behaviour of high nitrogen nickel-free austenitic stainless steel

Nanoindentation tests of the high nitrogen nickel-free austenitic stainless steel (HNS) were performed with peak load in a wide range of 100–600?mN to investigate the nanoindentation creep deformation behaviours. The results of the nanoindentation creep tests have demonstrated that the load plateaus, creep strain rate and creep stress of the cold-rolled HNS are larger and its creep stress exponent is smaller than the solution-treated HNS. The analysis reveals that the obvious creep deformation behaviour in the cold-rolled HNS arises from the rapidly relaxed dislocation structures in the initial transition regime, while the small creep deformation behaviour of the solution-treatedHNS is mainly attributed to that the stable dislocation structures for the intensive interactions between dislocations.     

Creep ductility considerations for high energy components manufactured from creep strength enhanced steels

Abstract

It is well established that the tendency for low ductility ‘creep brittle’ fracture behaviour in tempered martensitic steels is linked to the formation and growth of micro voids or ‘cavities’. Details of the contributions of all factors affecting damage development are still under investigation. However, it is known that for tempered martensitic steels voids often initiate over most of the creep life. Nucleation has been recorded on both prior austenite grain boundaries and at other micro structural features such as lath boundaries. The number of voids formed, and the fracture behaviour observed, depend on the type of creep strength enhanced ferritic (CSEF) steel and specific details of fabrication and heat treatment. In Grade 91 steel, void nucleation is sensitive to metallurgical factors such as composition and steel making practices. Key indicators of susceptibility to creep cavitation also include the levels of trace elements present and the presence of hard non-metallic inclusions. In Grade 92 steel, creep void formation has been linked to boron nitrides and other inclusions. These inclusions are present when there has been insufficient control of composition and heat treatment. Metallurgical factors linked to whether a particle will nucleate a void include the nature of the inclusion/matrix interface, the shape and size and the location of the inclusions within the microstructure. This paper describes the results of critical uniaxial and multiaxial testing for CSEF steels and compares data from nominally the same steels which have different metallurgical susceptibilities to void formation.     

Steady State Creep Rate Equation of Inconel 718 Superalloy

The steady state creep rate equdtion ofa nickel base superalloy Inconel 718, strengthenedby coherent ordered disc-shaped bct γ~(11) phaseand coherent spherical fcc γ~1 phase precipitates,has been established in the stress and temperatureranges of 620-840 MN m~(-2) and 853-943K, respecti-vely. Constant stress tensile creep tests wereused to medsure the values of steady state creeprate, ε_s, and the consecutive stress reductionmethod was used to measure the back stress duringcreep deformation. The values of effective stressexponent, n_e, were detemined from the slopesof the lgε_s vs. lg(σ_a-σ_0)/G plots. The effectof grain size, d, on steady state creep rdtehas been also studied in this investigation,and the grain size sensitive exponents m weredetemined from the slopes of lgε_s vs. lg(b/d)plots. The creep rate equations of Inconel 718,in the above stress and temperature ranges,have been proposed to beε_s=1.6×10~(-5)(D_1Gb/KT) (b/d )~(0.19)[(σ_a-σ_0)/G]~(1.35)in diffusional creep region, andε_s =75(D_1Gb/KT) (b/d)~(-0.42)[(σ_a-σ_0)/G]~(5.5)in dislocation power law creep region.     

X70管线钢的室温蠕变及其对流变应力的影响

利用MTS万能试验机研究了X70管线钢在不同应力加载速率和不同加载过程下的室温蠕变现象,以及室温蠕变对流变应力的影响.结果表明,X70管线钢有明显的室温蠕变现象存在,应力加载速率和加载过程对室温蠕变变形量有明显的影响,而且室温蠕变显著提高了材料的流变应力.并根据位错理论对实验结果进行了分析解释.