单晶镍基高温合金的高温蠕变及相关参数

通过测定一种单晶镍基高温合金的高温拉伸蠕变曲线和位错运动的内摩擦应力σ0,建立了综合蠕变方程,计算出不同蠕变阶段的激活能和相关参数.结果表明在蠕变期间,内摩擦应力σ0随外加应力σ的增加而略有提高,但随温度升高而明显下降.在实验温度和应力范围内,在不同蠕变阶段,具有不同的激活能Q,时间指数m和结构常数Bi.因此,合金在不同蠕变阶段具有不同的蠕变机制.蠕变初期,形变机制是位错在基体通道中运动;而大量位错切入筏状γ'相中是蠕变第3阶段的主要特征,在γ'/γ两相界面产生空洞及空洞的聚集和微裂纹扩展是蠕变断裂的直接原因.     

一种[001]取向镍基单晶高温合金蠕变特征

研究了一种[001]取向镍基单晶合金的蠕变特征和变形期间的微观组织结构.结果表明:在低温高应力和高温低应力条件下,合金具有较长的蠕变寿命和较低的稳态蠕变速率;在700℃,720MPa条件下,透射电镜(TEM)观察显示蠕变期间的变形特征是$\\frac{1}{2}研究了一种[001]取向镍基单晶合金的蠕变特征和变形期间的微观组织结构.结果表明:在低温高应力和高温低应力条件下,合金具有较长的蠕变寿命和较低的稳态蠕变速率;在700℃,720MPa条件下,透射电镜(TEM)观察显示蠕变期间的变形特征是1/2110位错在基体中运动,发生反应形成1/3112超肖克利(Shockley)不全位错,切入γ′相后产生层错.在900℃,450MPa条件下,没有出现蠕变初始阶段,γ′相从立方体形态演化成筏形;在加速蠕变阶段,多系滑移开动,大量位错剪切γ′相是变形的主要机制.在1070℃,150MPa条件下,γ′相逐渐转变成筏形组织,并在γ/γ′界面处形成致密的六边形位错网,位错网可以阻止位错切入γ′相,提高蠕变抗力;在蠕变后期,位错以位错对形式切入γ′相,是合金变形的主要方式.     

用修正的θ函数预测单晶镍基高温合金的蠕变寿命

 采用修正的θ函数影射概念对单晶镍基高温合金的蠕变曲线进行了拟合和预测。根据一系列的实验数据建立了蠕变方程中有关参数的数学表达式,据此对1 040 ℃、137 MPa下的蠕变寿命进行了预测,预测精度达96%,远高于用早期的θ函数影射概念预测结果。该方法仅需确定3个参数,简化了计算,同时,线性参数表达式确保了预测精度。     

一种镍基单晶高温合金的显微偏析行为

研究了一种新型镍基单晶高温合金DD98铸态组织的显微偏析行为.实验结果表明,当合金以枝晶凝固时,组织中存在显微偏析.其中元素Mo、Cr、Ti、Ta、Al在枝晶间富集,Ti、Mo、Ta、Cr的偏析较为严重,Al的偏析程度相对小一些,Ni、Co、W为枝晶干偏析元素,其中W的偏析最为严重;共晶中富集Al、Ta、Ti、Ni,贫Co、W、Cr、Mo.凝固速率对枝晶偏析有显著的影响.随着抽拉速率的增加,元素Al、Mo、Co、Ti的偏析程度增加,而Ta的偏析程度降低,其它元素的偏析程度变化不大.     

一种镍基单晶高温合金的瞬态液相连接

研究了一种镍基单晶高温合金的瞬态液相连接方法(TLP)及其对合金组织性能的影响.结果表明,不同温度下Ni-Cr-B熔体对基片均具有良好的润湿性,平衡接触角均小于20°.在等温凝固过程中,随保温时间的增加,固-液界面不断由两侧向中间推移,共晶区宽度不断减小,直至接头中无任何残余液相存在,等温凝固完全结束.共晶区上的硼化物分别为MB和M23B6.TLP连接后的1010℃×248MPa的持久性能达到母材的90%以上.     

一种镍基单晶合金的组织演化与蠕变行为

通过蠕变曲线测定及组织形貌观察,研究了一种镍基单晶合金的蠕变行为和变形特征.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.由所得数据测算出合金的蠕变激活能和应力指数.蠕变初期在施加温度和应力场的作用下,立方γ′相逐渐转变成与施加应力轴方向垂直的N型筏状结构.稳态蠕变期间,合金的变形机制是位错攀移越过筏状γ′相,由于高温蠕变稳态阶段形成的N型γ′相筏状组织厚度较小,位错易于攀移,因而合金具有较大的应变速率.蠕变后期,由于塑性变形,在近断口处筏形γ′相转变成与应力轴方向呈45°角的形貌,合金的变形机制是位错剪切筏状γ′相.     

几种典型镍基单晶高温合金成分设计的热力学分析

利用热力学计算软件JMatPro和相应的镍基高温合金数据库,研究了几种典型镍基单晶高温合金和GE公司的低Re成分单晶高温合金专利,分析了合金成分设计中与单晶叶片设计、微观组织稳定性以及加工工艺性能密切相关的一系列参数,包括合金的初熔温度、密度、γ'相体积分数、γ/γ'相错配度、TCP相含量、热加工窗口以及糊状区区间等,...     

铼在镍基单晶高温合金中的作用

镍基单晶高温合金因其优异的高温强度和良好的组织稳定性,广泛应用于航空航天领域.为了提高其承温能力,自第二代开始镍基单晶高温合金中便加入了铼(Re).经过几十年的发展,镍基单晶高温合金已经发展到第七代,Re已经成为了先进镍基单品高温合金中不可缺少的元素.简述了镍基单晶高温合金的发展历程,综述了Re对镍基单品高温合金显微组...     

一种镍基单晶高温合金的再结晶

 研究了喷丸压力和喷丸时间对一种镍基单晶高温合金再结晶的影响。运用再结晶动力学,分析并探讨了喷丸处理后镍基单晶高温合金的再结晶动力学特征。结果表明:在固溶处理条件下,该镍基单晶高温合金很容易发生再结晶。喷丸处理压力越大,再结晶趋势越强。     

[011] Creep in a single crystal nickel base superalloy at 1033K

TEM investigation are performed on [011] single crystals of SRR99 after at 1033 K under a load at 680 MPa. At the creep rate minimum, multiple slip in the matrix occurs on four octahedral slip systems. Octahedral cross slip or cubic slip is not activated. Due to the superposition of coherency and external stressein small matrix channels, deformation is concentratedned in the “roof” matrix channels. During secondary creep, screw interfaial dislocations cross slip in the cube γ/gg' interfaces. In this stage, γ' precipitates are sheared by Shocley super parrials. Common shereing of matrix and γ' particles by Shockley super partials is observed. The high creep rate in the [011] orientation is considered to be caused by the stress concentration in roof matrix channels and the few actiated slip sysems.     

基于微观参数的镍基单晶合金CMSX-4蠕变寿命预测

摘要：对变截面CMSX-4试样进行了不同温度下的蠕变试验，对比研究了不同应力处的微观组织筏化情况。结果表明：CMSX-4在温度和应力较低时筏化速率极慢，而在温度和应力较高时会快速完成筏化，在合适的温度和应力范围内γ相通道宽度会与材料损伤程度有显著的关联。基于相关结果，提出了一种以γ相通道宽度预测镍基单晶合金CMSX-4剩余蠕变寿命有效方法，通过对比本试验和其他相关报道的结果，本方法的预测结果分散性较小，均位于±1.5倍分散带内。     

氢化物发生-原子荧光光谱法测定DD6单晶镍基高温合金中砷

DD6单晶镍基高温合金中含有Ta、Re、W等合金元素,因此样品溶解较为困难,得到的样品溶液也不稳定。实验采用盐酸-硝酸体系溶解样品,以镍基体匹配法绘制校准曲线克服了基体镍的干扰,实现了氢化物发生-原子荧光光谱法对DD6单晶镍基高温合金样品中As含量的测定。对溶样方法进行了探讨,结果表明,采用20mL盐酸-5mL硝酸、加热(100℃左右)溶解样品后,虽然会有少量不溶物存在,但待测元素As已完全溶出,即不溶物中未夹带元素As,因此实验选择该溶样方法进行溶样。对仪器的负高压、灯电流进行了优化试验,确定负高压为280V,灯电流为60mA。根据样品中镍的含量,分别采用无基体匹配和镍基体匹配法建立校准曲线,结果表明,对于同样质量浓度的As标准溶液,有基体镍存在时的测定结果均较无基体镍时明显偏低,说明镍基体的干扰对测定不可忽略,故实验采用镍基体匹配法绘制校准曲线。方法线性范围为0.00005%~0.001%,方法检出限为2×10^-5μg/mL。按实验方法对6个DD6单晶镍基高温合金样品进行测定,测得结果与高流速辉光放电质谱法基本一致,测得结果的相对标准偏差(RSD,n=8)为2.3%~8.7%。     

一种单晶合金的高温蠕变行为及其变形特征

通过测定一种单晶镍基合金的高温拉伸蠕变曲线及位错运动的内摩擦应力σ0,建立了综合蠕变方程,计算出稳态蠕变期间的表观蠕变激活能及相关参数.结果表明：在蠕变期间,位错运动的内摩擦应力σ0,随外加应力的提高略有提高,随温度的升高而明显降低.蠕变后期,由于缩径使样品不同位置承受不同的有效的应力,导致筏状γ＇相具有不同的粗化特征,在近断口处,载荷的有效应力增大,使筏状γ＇相扭曲且粗化加剧.界面位错网对形变硬化和回复软化具有协调作用,并减缓位错切入γ＇相,因此有利于合金蠕变抗力的提高.     

Surface recrystallization of a single crystal nickel-base superalloy

The recrystallization behavior of a single crystal nickel-base superalloy was investigated by shot peening and subsequent annealing. Two kinds of recrystallization microstructures, which are intensively dependent on the annealing temperature, are shown in the nickel-base superalloy after shot peening and subsequent annealing. Surface recrystallized grains are obtained when the superalloy is anparticles occurs. Cellular recrystallization is observed after annealing at lower temperatures. Cellular structures induced by high diffusivity of the shot-peened alloy annealed at 1050℃ accords with the Johnson-Mehl-Avrami-Kolmogorov equation. The low Avrami exponent is caused by the inhomogeneous distribution of stored energy, the decreasing of stored energy during recovery, and the strong resistance of boundary migration yb γ' particles.     

Creep resistance of CMSX-3 nickel base superalloy single crystals

Creep deformation in 〈001〉 oriented nickel base superalloy single crystals has been studied in an effort to assess the factors which contribute to the overall creep resistance of superalloys with high volume fractions of γ′ phase. Detailed observations of three dimensional dislocation arrangements produced by creep have been made with the use of stereo electron microscopy. In the temperature range of 800–900°C at stresses of 552 MPa or lower, the dislocation-free γ′ precipitates are resistant to shearing by dislocations. As a result, creep deformation occurs by forced bowing of dislocations through the narrow γ matrix channels on {111} planes. At moderate levels of temperature and stress there are incubation periods in virgin crystals prior to the onset of primary creep. The incubations arise because of the difficult process of filling the initially dislocation starved material with creep dislocations from widely spaced sources. When the newly generated dislocations percolate through the cross section, incubation comes to an end and primary creep begins. In primary creep neither work hardening nor any type of recovery plays an important role. The creep rate decelerates because the favorable initial thermal misfit stresses between γ and γ′ phases are relieved by creep flow. Continued creep leads to a build-up of a three-dimensional nodal network of dislocations. This three-dimensional network fills the γ matrix channels during steady state creep and achieves a quasi-stationary structure in time. In situ annealing experiments show that static recovery is ineffective at causing rearrangements in the three-dimensional network at temperatures of 850°C or lower. The kinematical dislocation replacement processes which maintain the quasi-stationary dislocation network structures during apparent steady state creep are not understood and require further study. Because of the impenetrability of the γ′ precipitates, dislocations move through the γ matrix by forced Orowan bowing, and this accounts for a major component of the creep resistance. In addition, the frictional constraint of the coherent or semi-coherent precipitates leads to the build-up of pressure gradients in the microstructure, and this provides load carrying capacity. There is also a smaller component of solid solution strengthening. Work hardening is comparatively unimportant. Finite element analysis shows that the non-deforming precipitates are increasingly stressed as creep deformation accumulates in the matrix. In the later stages of steady state creep and during tertiary creep the stresses in the precipitates rise to high enough levels to cause shearing of the γ′ particles by dislocations entering from the γ matrix. The recovery resistance of the material is in part due to a very low effective diffusion constant and in another part due to the fact that the three-dimensional dislocation networks formed in the γ matrix serve to neutralize the misfit between the γ and γ′ phases.     

粉末高温合金FGH97疲劳裂纹扩展行为

测定不同晶粒尺寸、γ'相以及不同Hf含量的粉末高温合金FGH97在650℃高温条件下的疲劳裂纹扩展速率,并将其与FGH95和FGH96两代粉末合金的疲劳裂纹扩展速率进行对比.用定量分析的方法对FGH97合金在疲劳断裂各个阶段的行为特征进行分析.较大晶粒尺寸的FGH97合金具有较低的裂纹扩展速率,合理的二次和三次γ'相匹配析出,可以获得较高的疲劳寿命;Hf元素的添加使合金的整体疲劳寿命增大;FGH97合金与FGH95和FGH96相比,具有较高的疲劳裂纹萌生抗力,更低的高温疲劳裂纹扩展速率.     

金相分析法标定铸态镍基单晶高温合金晶体取向

摘要：精确标定晶体取向对镍基单晶高温合金的制备与应用具有重要意义,研究了金相观察结合定向切割的金相分析法标定铸态镍基单晶高温合金晶体学方向的原理及标定误差。结果表明,采用3次金相观察结合定向切割可以精确标定任意形状的铸态镍基单晶高温合金试样的晶体学方向。EBSD测定和显微组织分析验证了金相分析法标定单晶取向偏差在2°以内,并分析了引起标定误差的主要原因。