18Cr2Ni4WA钢渗碳层深度的测定

用金相法测定合金钢渗碳层深度时，试样通常为退火状态。18Cr2Ni4WA钢作为一种高淬透性渗碳钢，其试样经退火、正火及普通淬火后均难以测定渗碳层深度，只有经过等温淬火使渗碳层获得淬火马氏体（白色）组织，心部获得回火马氏体（黑色）组织，才能可靠地进行渗碳层深度的测定。     

HP40奥氏体耐热钢炉管长期高温时效的安全性分析

为判别炉管的损伤程度和运行安全性,本文对运行了约46 000 h的苯乙烯生产加热炉炉管,在大修期间进行了宏观检查、氧化物的XRD(X-ray d iffraction)分析、管径测量、超声波测厚、硬度试验、金相组织分析及炉管的危险点计算分析等。实验结果表明:炉管表面发生了高温氧化以及碳化腐蚀,炉管壁厚明显减薄。与新管相比硬度也明显下降,显微组织明显退化,骨架状共晶碳化物形态消失,一次碳化物和从奥氏体晶内析出的二次碳化物明显粗化,且析出少量块状σ相。并在此基础上对炉管的剩余使用寿命作了估算。     

粉末锻造钢12Cr2Ni4A和18Cr2Ni4WA的组织与性能

讨论了粉末锻造钢１２Ｃｒ２Ｎｉ４Ａ和１８Ｃｒ２Ｎｉ４ＷＡ的组织与性能。氧含量低于０．２％，碳含量为０．０８～０．１２％的粉末锻造钢１２Ｃｒ２Ｎｉ４Ａ和碳含量为０．１１～０．１６％的粉末锻造钢１８Ｃｒ２Ｎｉ４ＷＡ有较好的力学性能。长时间扩散退火可有效地提高粉末锻造钢的韧性。     

25Cr3MoA合金棒材组织与性能的研究

研究了25Cr3MoA合金棒材热处理对组织和性能的影响。结果表明:电弧炉加电渣重熔冶炼的25Cr3MoA钢组织均匀、纯净度高;艾氏冲击功与夏比冲击功没有对应关系;WS9-6001组别低温冲击韧性最好;在600℃以下仍保持较好的高温性能;400℃时仍具有较高的高温疲劳强度。     

LY12铝合金表面铈纳米膜的制备及显微组织特征

采用Sol-gel提拉法在LY12铝合金表面制备了铈的纳米膜。研究了成膜的最佳工艺条件。试验结果表明,处理溶液中铈的起始浓度、焙烧温度等都是影响膜质量的因素。在焙烧温度为400℃,铈的起始浓度为30g/L的条件下,可获得均匀,重复性好的膜。XPS测试结果证明了膜的主要成分为铈的氧化物,利用XRD测试结果估算出膜中的铈的粒径为10纳米。扫描电镜的结果指出了焙烧温度高低对膜层表面结构特征的影响。     

Topology Optimal Design of Material Microstructures Using Strain Energy-based Method

提出了基于能量法的微结构灵敏度计算和构型优化新方法,与均匀化方法相比,虽然本质相同,但计算效率高、且软件实现更加简便。本文以微结构等效弹性矩阵各分量的不同组合为设计目标,采用对偶凸规划方法结合周长约束策略进行二维、三维微结构构型优化设计。算例结果表明,采用能量法的微结构优化方法与均匀化方法具有相同的效果,不仅能获得具有极端特性构型的材料微结构,而且具有推导简洁、编程简单的优点。     

喷射沉积Ni3Al基高温合金及其复合材料的显微组织和力学性能

利用喷射沉积技术成功地制备了Ｎｉ－Ａｌ－Ｍｏ系Ｎｉ３Ａｌ基高温合金及其复合材料盘坯，对其显微组织和力学性能进行了测试和分析，并对陶瓷粒子的复合机制进行了初步探讨。     

钛基稀土激光熔覆层组织细化机制及性能

采用通快TruDisk 4002光纤激光器在TC4合金表面分别制备了0wt% Y₂O₃和3wt% Y₂O₃的TC4+Ni45+Co-WC钛基耐磨复合涂层。利用XRD、SEM、EDS、EPMA、显微硬度计和摩擦磨损试验机等分析了涂层组织、显微硬度和摩擦学性能。结果表明，两种涂层表面均无裂纹孔隙等缺陷，且生成相一致，主要包括TiC、TiB₂、Ti₂Ni、WC和α-Ti；0wt% Y₂O₃涂层组织存在明显偏析，析出相尺寸粗大且方向性明显；3wt% Y₂O₃涂层组织呈均匀弥散状态分布，细化特征明显；经Bramfitt二维点阵错配度计算，（100）_Y2O3和（100）_Ti2Ni、（111）_Y2O3和（110）_TiC、（110）_Y2O3和（1010）_TiB2间的错配度分别为5.75%、6.72%和10.10%，Y₂O₃作为异质形核核心对Ti₂Ni、TiC和TiB₂的细化能力依次为Ti₂Ni > TiC > TiB₂；0wt% Y₂O₃和3wt% Y₂O₃涂层显微硬度分别为600~630 HV_0.5和470~480 HV_0.5，较基材分别提高了约62%和26%；3wt% Y₂O₃涂层耐磨减摩性最优，其磨损体积和摩擦系数较0wt% Y₂O₃涂层分别下降了约47.8%和5.0%，磨损机制主要为磨粒磨损。     

Design and Coupled Thermo-Mechanical Analysis of Silicon Carbide Primary Mirror Assembly

Based on the principle that the thermal expansion coefficient of the support structure should match that of the mirror, three schemes of primary mirror assembly were designed. Of them, the first is fused silica mirror plus 4J32 flexible support plus ZTC4 sup-port back plate, the second K9 mirror plus 4J45 flexible support plus ZTC4 support back plate, and the third SiC mirror plus SiC rigid support back plate. A coupled thermo-mechanical analysis of the three primary mirror assemblies was made with finite element method. The results show that the SiC assembly is the best of all schemes in terms of their combination properties due to its elimination of the thermal expansion mismatch between the materials. The analytical results on the cryogenic property of the SiC primary mirror assembly show a higher surface finish of the SiC mirror even under the cryogenic condition.     

Creep Behaviors of FGH95 Powder Ni-Base Superalloy

This article makes an investigation into the creep behavior and deformation features of FGH95 powder Ni-base superalloy by means of creep curves and microstructural observation. Results show that this superalloy exposes obvious sensibility to the applied temperature and stresses in the experimental range. Microstructure of the alloy consists of γ′ phase of various sizes and dispersed carbide particles precipitated in the wider crystal boundaries between the powder particles. During the creep, the deformation of the alloy occurs in the form of single- or double-oriented slipping inside the grains, and some of the finer carbide particles are precipitated near the slipping traces. The wide grain boundaries might be broken into the finer grains due to severe deformation. The deformation mechanism of the alloy during creep is thought to be the activation of dislocations of double-oriented slipping, including (1/2)<110> dislocation inside the γ matrix phase and <110> super-dislocation inside the γ′ phase. The formation of the stacking faults and (1/3)<112> super-Shockleys partial dislocation configuration is attributed to the decomposition of <110> super-dislocation in the γ′ phase.