碳含量对Ti-60合金时效过程中硅化物的影响

Ti-60合金在β和α β相区固溶处理后空冷,形成的片状组织和双态组织中没有硅化物析出.随后在700～800℃时效处理168 h,在α/β片层界面、α片层内及初生α相内析出S2类型的硅化物(Ti,Zr)6Si3.C的加入阻碍硅化物在界面处和基体中的形核和长大,降低硅化物的析出速率.随着合金中C含量的增加,显著减小时效过程中硅化物的析出尺寸,这是由于C的加入,基体中固溶Si的能力增加及Zr原子扩散速度降低所导致的结果.相同温度下时效处理,双态组织中析出的硅化物尺寸比片状组织大.时效温度升高,硅化物的析出直径增大.     

Ti600高温钛合金蠕变前后的组织变化

通过OM,TEM等对航空用近α高温钛合金Ti600试样蠕变前后的显微组织进行了观察研究,结果发现：随着蠕变条件的不同,硅化物粒子（Ti5Si3)和α2（Ti3Al)粒子有着不同程度的析出,而且合金的残留β相及次生α相也有相应的变化。在蠕变过程中,α3粒子的析出阻碍位错移动,强化了合金基体。稀土氧化物粒子（Y2O3）在蠕变前后比较稳定,其形貌和大小没有多大变化,粒子平均直径为0．6μm。还研究了600～650℃之间的蠕变试样,通过TEM观察得知,在650℃／150MTa/100h试验条件下,Ti600合金的组织形貌仍然没有大的改变。     

Ti600合金中硅化物与蠕变性能关系的研究

研究了Ti600高温钛合金在固溶处理过程中,不同冷却速率对组织结构的影响及结构与性能之间的关系.重点考察冷却速度对抗蠕变强度的影响,以确定最合适的热处理制度.实验内容包括:观察α片层宽度与晶间α形貌随冷却速度的变化规律;测试不同状态下棒材的高温蠕变性能;分析组织特征与性能之间的相互关系;测定了Ti600合金中硅化物的溶解温度,研究硅化物对合金晶粒尺寸的影响规律.结果表明,在固溶处理过程中,随着冷却速率的增加,α片层宽度减小,硅化物对合金晶粒长大具有明显的抑制作用.当合金在硅化物溶解温度以下进行固溶处理时,其晶粒尺寸的增加比较缓慢,而当固溶温度一旦超过硅化物溶解温度,其晶粒尺寸则迅速增大.研究得出,合金的固溶处理温度处在相变点与硅化物溶解温度之间,合金可获得良好的综合性能.     

Ti-Al-Zr-Mo-Nb-Sn-Si系铸造钛合金高温蠕变性能及显微组织研究

针对Ti-Al-Zr-Mo-Nb-Sn-Si铸造高温钛合金,研究了其在600℃、750℃下的蠕变性能与组织变化。结果显示,该铸造钛合金在750℃/180 MPa/0.5 h和600℃/400 MPa/0.5 h条件下的蠕变残余伸长率分别<3%和<0.4%,持久断裂时间分别为>2 h和14 h,具有良好的蠕变性能;高温蠕变断口存在细小颗粒;高温蠕变后塑性变形区的组织变化较小,呈魏氏组织,而集中变形区存在部分晶界消失、α片层宽化现象;高温蠕变后位错明显增多,与析出相相互纠缠。      

TNW700高温钛合金热过程中的相组织变化分析

本工作利用EPMA、SEM、EDS等测试手段分析了TNW700高温钛合金的相组织形态和元素分布,并利用原位X射线衍射(XRD)测试技术对该合金升温过程和热暴露过程中发生的相转变和表面氧化物进行了分析。结果表明TNW700高温钛合金是一种高铝当量合金,通过硅化物和α₂的析出强化共同提高其抗蠕变持久性能。在升温过程中,600 ℃时Zr元素开始固溶至Ti中,并在900 ℃达到饱和;从880 ℃开始TiC、Ti₃Al相随着温度升高而增多;700 ℃热暴露实验表明TNW700钛合金表面生成的氧化物以Ti₆O、Ti₃O为主,氧化物增加缓慢,没有大量的TiO₂和Al₂O₃出现,合金短时内有良好的抗表面氧化性能。     

C元素对600℃高温钛合金热处理温度窗口的影响

研究了间隙元素C对600℃高温钛合金(Ti60)热处理温度窗口的影响。结果表明:微量C元素对Ti60合金的a+β→β相变过程有明显影响,C元素不仅提高了合金的相转变温度(T_β),而且显著减缓了初生a相含量的变化。微量的C元素(质量分数<0.1％)可以使a体积分数的变化速率从(1.5％～2％)·℃~(-1)(Ti60)减缓到0.5％·℃~(-1)(Ti60-C)左右。C元素的这种特性改善了Ti60钛合金在a+β上部区的热处理温度窗口,可以确保该合金在较宽温度范围内进行固溶处理时初生a相的体积分数保持相对稳定,同时也确保了合金具有稳定的高温蠕变抗力。     

热处理对Ti6242S钛合金组织性能及探伤的影响

采用固溶时效及退火两种工艺对Ti6242S钛合金大棒材进行热处理,研究了不同热处理坯料尺寸对显微组织、力学性能以及探伤杂波水平的影响。结果表明:固溶时效态Ti6242S钛合金大棒材越靠近心部初生α含量越高,而退火态显微组织中等轴初生α相含量较固溶时效态更高;普通退火处理后蠕变性能较差,固溶时效态综合性能最好;固溶时效处理后大棒材水浸探伤底波的均匀性略有提高,而普通退火无此效果。     

高温钛合金中杂质元素Fe的扩散行为及其对蠕变抗力的损害作用

高温钛合金是先进航空发动机压气机应用的理想材料,代替钢或镍基高温合金,可以显著提高发动机的推重比和服役性能.随着钛合金使用温度的提高,高温蠕变抗力越来越成为影响其使用温度和使用寿命最关键的力学性能.在400～600℃的温度范围内,钛合金的蠕变变形一般受位错攀移机制所控制,蠕变激活能近似等于有效扩散激活能,因此,扩散是影响钛合金高温蠕变抗力的最主要因素.杂质元素Fe在钛合金中具有反常大的扩散能力,是Ti自扩散系数的103～105倍,在Ti中的扩散可能受离解扩散机制所控制.钛合金中的微量Fe同时会显著促进Ti的自扩散,提高位错攀移速率,从而降低蠕变抗力.为了改善高温钛合金的蠕变性能,需要严格控制原材料如海绵钛和中间合金中杂质Fe的含量.     

固溶温度对亚稳β钛合金Ti-4Mo-6Cr-3Al-2Sn的组织和拉伸性能的影响

对自主设计的新型亚稳β钛合金Ti-4Mo-6Cr-3Al-2Sn(%,质量分数)在不同温度进行固溶和固溶时效处理,观察其显微组织和测试室温拉伸性能。结果表明：随着固溶温度的提高固溶态组织中的初生α相减少,当固溶温度高于相变点后初生α相完全消失,几乎全部为明显长大的粗大β晶粒。固溶温度为900℃的固溶态合金具有良好的强度和塑性匹配,屈服强度为898.7 MPa、抗拉强度为962.5 MPa、断裂伸长率为12.7%。在不同温度固溶处理的时效态合金,均析出了细小的次生α相。固溶温度低于相变点时,在初生α相间析出的细小次生α相呈60°或者平行交错排列;固溶温度高于相变点时初生α相几乎完全消失,随着固溶温度的提高析出的次生α相片层间距变大并粗化。在所有固溶温度下,时效态组织中沿原始β晶界处均析出了连续的晶界α相,合金的塑性均较差。经过750℃/0.5 h固溶和500℃/4 h时效的合金具有良好的强度和塑性匹配,其抗拉强度为1282 MPa,屈服强度为1210.6 MPa,断裂伸长率为5.3%。     

碳对高温钛合金Ti-60组织和性能的影响

在Ti-60合金中碳的加入量大于0.17%时,组织中析出TiC结构的碳化物.在α β相区再结晶,碳偏聚于初生α(αp)相,导致碳化物主要在β转变组织中析出,其析出的百分数取决于αp体积分数.在β相区热处理,析出的碳化物钉扎β原始晶界,阻碍β晶粒的长大.β晶粒尺寸D、碳化物颗粒直径d和体积分数f三者遵循D/d∝f-1/3关系.随着碳含量的增加,β晶粒尺寸减小,α'片层通过界面迁移迅速长大以及形成α片层的合金元素的扩散速度加快,导致α'或α片层的厚度增加.碳的加入量小于0.09%时,碳完全固溶于基体中,产生固溶强化,β晶粒细小,导致合金的强度和蠕变抗力提高.碳含量增加导致粗大碳化物颗粒的析出,变形时产生应力集中使合金的塑性和蠕变性能降低.     

Effect of Long-term Thermal Exposure on Microstructure and Stress Rupture Properties of GH3535 Superalloy

The evolution of microstructure and the stress rupture properties of long term thermally exposed GH3535 alloy have been investigated. It was found that M6 C carbides presented in the solid solution heat treated samples. During long term thermal exposure at 700 C, fine M12 C carbides precipitated preferentially at grain boundaries. These carbides coexisted with the pre-exiting M6 C. The stress rupture life of700 C/1000 h exposed sample under creep testing at 650 C/324 MPa is 93 h. It is much longer than that of the solid solution samples. No noticeable changes could be detected in both the microstructure and stress rupture lives when the samples were exposed for time longer than 1000 h M12 C carbides were found to be beneficial to the creep properties. The cracks initiated at the interface of M6 C carbides and matrix, which led to a lower creep rupture life.     

High temperature creep of a hot-pressed β-sialon

The four-point bending creep properties of a hot-pressed β-sialon with Sm–melilite solid solution (denoted as M′) as intergranular phase have been studied in the temperature range 1250–1350°C in air. Creep rates plotted against stresses gave stress exponents of 1.45, 1.51 and 1.72 at 1250, 1300 and 1350°C, respectively, and Arrhenius plot between creep rate and temperature yielded a creep activation energy of 576 kJ mol⁻¹. Cavities were found to be mainly on the triple grain junctions. Diffusion coupled with grain boundary sliding and accompanied by the formation of wedge-shaped cavities was identified as the dominant creep mechanism.     

Effect of NiCr and NiCrAl coatings on the creep resistance of a Ni alloy

The effect of plasma sprayed NiCr and NiCrAl coatings on the creep resistance of Nickel alloy 690 at temperature of 1033 K was investigated. Experimental results showed that the coatings had a beneficial effect on the improvement of the creep resistance of substrate. However, there was almost no difference in the creep lives between the NiCr and NiCrAl coated specimens at a given stress level. The relation between the applied stress and time to rupture of the coated specimens can be estimated by using Larson-Miller equation. For the coated specimens tested at low applied stress levels, the product of the minimum creep rate and the time to rupture was a constant value. The θ projection method can be used to accurately characterize the creep behavior of the coated specimens. The variation of the creep strain along with time predicted by using θ projection method agreed well with the experimental results.     

Microstructural evolution during creep of a hot extruded 2D70Al-alloy

Microstructural evolution during creep of a hot extruded Al–Cu–Mg–Fe–Ni (2D70) Al-alloy was investigated in this study using transmission electron microscopy (TEM). The samples for creep test were carried out two-stage homogenization, followed by extruding. The creep ultimate strength dropped and the temperature increased gradually from 312 to 117 MPa and from 423 to 513 K, respectively. The microstructural observation for the crept samples showed that the S′ phase coarsened with increased creep temperature and the aging precipitates transformed from S″ phase to S′ phase during creep process. Meanwhile, excess solute atoms in supersaturated solid solution dynamically precipitated to further form finer S′ phase and S″ phase, which pinned the dislocations and impeded the dislocation movements. Large amount of dislocations piled up around the micron-scale Al₉FeNi phase, and a lot of dislocation walls were generated along 〈220〉 orientation. S phase accumulates around these defects. The interaction between dislocations and precipitates was beneficial for the improved performances at elevated temperature.     

Short-term flexural creep deformation in synroc-C

The flexural creep behaviour of synroc-C in an inert atmosphere was studied at temperatures of 860°C, 900°C and 940°C under constant-load conditions in four-point bending. Applied stresses ranged from 100 to 160 MPa. Individual creep curves show primary and secondary creep but little or no tertiary creep stage. The log of the creep rate was found to increase linearly with log of the applied stress at each temperature over the entire stress range. Analysis of the creep data using the Norton power-law function revealed that the stress exponent decreased from 3.3 ± 0.6 for the 860°C and 900°C data to 2.0 ± 0.2 for the 940°C data, and an activation energy of 440 ± 40 kJ/mol was obtained over the entire temperature and stress range. Comparative analysis with the theta-projection equation was found to adequately represent the data yielding an activation energy of 464 kJ/mol while also showing a trend for the stress exponent to decrease with increasing temperature. Microstructural examination revealed extensive cavitation on the tensile surface of the creep specimens subjected to higher stresses at 900°C and 940°C. Dynamic high temperature X-ray diffraction analysis indicated little change in the phase assemblage apart from a slight reduction in the amount of the hollandite phase at higher temperatures which was attributed to a minor amount of oxidation. The possible creep damage mechanism was explored with reference to creep test results and microstructural modifications and the implications of the observations are discussed.     

Effect of alloying elements on the creep behavior of high Pb-based solders

This study examines the high temperature creep behavior of several Pb-based alloys. All compositions tested were found to follow power-law dislocation creep in the strain rate range of 10⁻⁹-10⁻³ s⁻¹. Both the stress exponent and activation energy were measured from 298 to 473 K to identify the rate controlling mechanism for creep deformation. Creep of 95Pb-5In, 92.5Pb-5Sn-2.5Ag, 93Pb-3Sn-2Ag-2In was rate limited by dislocation climb from the observed stress exponent. A transition in the controlling climb mechanism from pipe diffusion to lattice diffusion was observed around 0.7T_m. Creep of 90Pb-10Sn was, however, rate limited by viscous solute drag rather than dislocation climb due to the greater concentration of Sn in Pb. The enhancement in self-diffusion of Pb was dependent on the degree of solid solution with solute atoms. The outcome of this work identifies variables related to the alloy elements that control creep behavior of Pb-based alloys used in high temperature applications where traditional solders cannot be used.     

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.     

Evolution of precipitated phases during prolonged tempering in a 9%Cr1%MoVNb ferritic-martensitic steel: Influence on creep performance

Ferritic-martensitic steels of the 9%Cr1%Mo type have been extensively used in power plant components, heat exchangers, piping and tubing, etc., due to an excellent combination of properties such as creep resistance, toughness and resistance to oxidation at high temperatures. In these steels the stabilizing role of MX carbonitrides (M = Nb, V; X = C, N) is one of the main factors responsible for the resistance under creep conditions. The control of precipitation and coarsening of MX phases during prolonged, high temperature tempering or post-weld heat treatment is then a key point to obtain the desirable microstructure and hence, to achieve high temperature resistance under service conditions.In the present contribution we report the evolution of the precipitated phases during heat treatment at 780 °C for increasing times in the range 40 min to 7 h for an ASTM A213 T91 steel. The Nb and V contents in solid solution were determined as a function of the time of treatment and maxima were observed for 5 and 5.66 h, respectively. Creep tests to rupture were also conducted at 600 °C - 190 MPa for as-treated specimens. A maximum creep rate was observed to occur in coincidence with the maximum values of Nb and V contents in solid solution. We suggest possible relationships between the observed second phase evolution and the creep resistance behavior.     

Tensile creep of whisker-reinforced silicon nitride

This paper presents a study of the creep and creep rupture behaviour of hot-pressed silicon nitride reinforced with 30 vol% SiC whiskers. The material was tested in both tension and compression at temperatures ranging from 1100 to 1250°C for periods as long as 1000 h. A comparison was made between the creep behaviour of whisker-reinforced and whisker-free silicon nitride. Principal findings were: (i) transient creep due to devitrification of the intergranular phase dominates high-temperature creep behaviour; (ii) at high temperatures and stresses, cavitation at the whisker-silicon nitride interface enhances the creep rate and reduces the lifetime of the silicon nitride composite; (iii) resistance to creep deformation is greater in compression than in tension; (iv) the time to rupture is a power function of the creep rate, so that the temperature and stress dependence of the failure time is determined solely by the temperature and stress dependence of the creep rate; (v) as a consequence of differences in grain morphology and glass composition between whisker-free and whisker-reinforced material, little effect of whisker additions on the creep rate was observed.     

Investigation of the compressive creep behavior of AZ91D magnesium alloy

The creep resistance of AZ91D alloy has been studied in uniaxial compression tests at temperature ranges from 275 °C to 325 °C. The initial microstructure of the alloy consists of α phase and β phase precipitated in the grain boundary. The minimum creep rate dependence on applied stress and the temperature is also analyzed in detail. We find that the stress exponent n is close to the theoretical values (3 or 5) and the activation energy Q for creep varies from 121 kJ/mol to 171 kJ/mol. Creep could be controlled by high-temperature climb and cross-slip of dislocation at different temperatures.