热处理对激光立体成形Ti_3Al/TC11连接界面组织性能的影响

通过对激光立体成形Ti3Al/TC11连接界面沉积态、去应力退火和固溶时效3种状态的组织进行对比研究,探索改善Ti3Al/TC11连接界面组织以提高其性能的新途径。研究表明,沉积态试样在两个基体与过渡区交界处组织形貌差异较大,经去应力退火后试样连接界面的组织形貌与沉积态相比变化不大,但针状α′相长度明显减小,Ti3Al侧β晶界厚度减小且变模糊。经固溶时效处理后,两个基体与过渡区交界处组织形貌差异较小,均为等轴、细小α相、α2相和转变β相的三重混合组织,β晶界消失,沿整个试样显微硬度值分布均匀,相比去应力退火态其显微硬度整体较高,这可能与弥散相的固溶强化作用有关。     

NiCrAlY涂层/TC4基体界面反应机理

采用电弧离子镀技术在TC4(Ti6Al4V)合金基体表面沉积制备NiCrAlY涂层.通过扫描电镜与能谱分析、X射线衍射分析及显微硬度测试,研究真空热处理对NiCrAlY涂层组织性能的影响;分析界面反应产物的形成过程;讨论Cr元素在界面反应中的作用机制.研究结果表明:真空热处理后NiCrAlY涂层中有γ'-Ni3Al相析出,提高了涂层的表面硬度;在870℃以下热处理,NiCrAlY涂层/TC4基体界面反应产物的出现顺序依次为:相变影响区→Ni3(Al,Ti)和Ti2Ni化合物层→TiNi化合层;Cr元素在870℃以上开始扩散并参与界面反应,形成TiCr2化合物.     

固溶处理对Mg-6Al-5Pb-1Zn-0.3Mn阳极组织和性能的影响

为了改善铸态Mg-6Al-5Pb-1Zn-0.3Mn(质量分数,%)阳极的加工性能,对其进行固溶退火处理。采用浸泡法、恒电流和动电位极化扫描法及电化学阻抗法,研究不同固溶时间对其在3.5%(质量分数)NaCl中自腐蚀和电化学行为的影响;采用光学显微镜、扫描电镜对其显微组织和腐蚀形貌进行观察。研究结果表明:经400℃固溶24h,粗大的β-Mg17Al12相完全回溶于基体中,枝晶偏析基本消除;与铸态合金相比,晶界附近富Al区的消失使得固溶态合金耐蚀性能降低,晶体缺陷的减少使得放电性能变差;随着固溶时间延长,阴极β-Mg17Al12相的减少使得合金耐蚀性能提高,合金元素固溶度的增大使得合金放电性能提高;在放电过程中,放电产物层不断脱落,维持了镁合金阳极的放电活性。     

固溶处理对TC16钛合金显微组织和拉伸性能的影响

通过金相显微镜和室温拉伸性能测试,研究固溶处理对TC16钛合金棒材显微组织和拉伸性能的影响.结果表明:TC16钛合金低于800℃进行固溶处理,初始组织为初生α相和亚稳态β相,随着固溶温度的升高,亚稳态β相会发生α"马氏体转变,温度达到900℃时,α"马氏体析出晶界完整的β相,出现过烧组织,抗拉强度和屈服强度先降后升,温度对塑性影响不大.该合金固溶处理后,冷镦性能差,不同的冷却速度使钛合金有不同的α和β相比率,冷却速度决定β→α转变反应中间相的形成条件,水淬、空冷、炉冷后的TC16钛合金显微组织和拉伸性能差异较大.     

热处理工艺对AZ80镁合金显微组织的影响

利用光学显微镜、扫描电子显微镜、X射线衍射仪等分析手段研究了固溶时效及退火工艺对AZ80铸造镁合金显微组织的影响。结果表明,固溶处理可获得单相α-Mg固溶体组织;在随后的时效处理中β-Mg17Al12相以连续析出和不连续析出两种方式重新析出;在退火处理的缓慢冷却过程中β-Mg17Al12相以层片状形式析出;退火后的球化处理使层片状β-Mg17Al12相通过自身溶断的方式获得均匀细小的球状β-Mg17Al12相。     

扩散连接Al/Ni/0Cr18Ni9Ti复合材料的界面组织

选取纯Ni箔作过渡层,采用真空热压扩散工艺,在加热温度480℃、压力10 MPa、真空度1.0×10-2Pa的工艺条件下,制备了变形铝合金2024和不锈钢0Cr18Ni9Ti双金属复合材料.利用扫描电子显微镜、能谱仪、X射线衍射仪和显微硬度仪等测试分析方法,对双金属复合材料的2个连接界面及基体进行了组织、性能分析.结果表明:不锈钢/纯Ni界面形成了宽约8μm的互扩散区,但其过渡区无金属间化合物生成;Al/Ni界面生成了宽约4μm的扩散过渡区,过渡区的相组成为金属间化合物Al3Ni2、Al3Ni及Al3Ni5.     

金属Sc对Ti-6Al-4V合金组织演变与性能的影响

采用真空电弧熔炼技术制备了含Sc(质量分数)为0,0.1%,0.3%,0.5%的4种Ti-6Al-4V合金,并利用X射线衍射技术、光学金相显微镜和SHIMADZU HMV硬度计对铸态合金的相组成、等温退火后进行淬火的合金的显微组织和显微硬度进行研究.研究结果表明:在合金的铸态组织中存在大量的类魏氏组织,添加金属Sc减小了魏氏组织的含量与尺寸;经过等温退火及淬火处理后,在合金组织中存在细针状的马氏体组织和少量的类魏氏体组织,同时,随着退火温度的降低,组织中针状马氏体尺寸减小,金属Sc对合金组织起明显的细化作用;在铸态合金中存在的相为Ti3Al,添加金属Sc使α-Ti在低角度的衍射峰强度变弱,在高角度的衍射峰强度变强;添加金属Sc导致Ti-6Al-4V合金片层组织的显微硬度大幅度提高,当Sc含量在0.1%～0.3%时,其显微硬度最适宜;退火态合金的显微硬度比铸态合金的显微硬度提高了很多;金属Sc对α-Ti的固溶强化效果最明显.     

热处理对蒸汽发生器用国产690合金管显微组织和显微硬度的影响

为改善蒸汽发生器常用国产690合金管的抗微动磨损性能,通过实验研究不同的热处理条件对合金显微组织和显微硬度的影响规律.首先,对690合金管进行固溶处理和TT处理(也称脱敏处理),以改变690合金管的晶粒平均直径和晶界碳化物形貌;然后用光学显微镜观察晶粒平均直径的大小,用场发射扫描电子显微镜观察晶界碳化物的形貌;最后,用显微硬度计分别测量690合金管基体和晶界的显微硬度.结果表明:对于国产690合金管,当固溶处理温度为1 080℃时,晶界的碳化物未完全溶解,基体的显微硬度低于晶界;当固溶处理温度达到1 090℃后,晶界的碳化物完全溶解进入基体;升高固溶处理温度和延长处理时间,晶粒平均直径会增大,基体和晶界的显微硬度都会降低,并且基体的显微硬度高于晶界的显微硬度.对固溶处理后的国产690合金管进行TT处理时,晶界碳化物尺寸和间距都随着TT处理温度升高和处理时间的延长而增大,晶界碳化物逐渐变得离散;基体的显微硬度基本不变并低于晶界,晶界的显微硬度在TT处理温度715℃、时间5 h都会出现一个峰值.研究表明,通过固溶处理可调整690合金管的晶粒度,TT处理获得不同的晶界碳化物形貌,进一步影响材料的显微硬度,进而可能改善材料在蒸汽发生器中应用的抗微动磨损性能.     

基材类型对钛合金电子束熔丝沉积成形的组织与硬度的影响

采用TC4钛合金焊丝,在α钛合金、α+β钛合金和β钛合金表面进行电子束熔丝沉积增材成形试验,研究了异种材料增材成形时基材对成形层及附近材料的显微组织和硬度的影响规律。结果表明:成形层的宏观组织均是沿成形高度方向外延生长的粗大柱状晶,基材类型对柱状晶的尺寸有较大影响,TB5为基材时柱状晶尺寸较小;成形层的微观组织为典型的网篮组织,但以TA3为基材的成形层中α片层较为粗大且无马氏体α’相,以TC4为基材的成形层中片层α相的尺寸较小,而以TB5为基材的成形层中有α’相析出,且越靠近基材,α’相的尺寸越小,数量越多。在基材原表面附近的基材内部有一层过渡区域,其中部分金属在成形过程中被熔化。熔化区尺寸与基材类型有关,以TA3为基材时熔化区最小;过渡区内材料的硬度发生明显变化,尤其是以TB5合金作为基材、表面沉积TC4合金时,该区域的显微硬度高于TB5和TC4合金的硬度。研究表明,基材的热物理性能对成形过程中热传导的影响、合金元素含量对材料组织转变的影响,是过渡区域内熔化区尺寸、成形层与过渡层中组织与硬度变化的主要影响因素。     

固溶时效处理对Ni50Ti44Al6合金微观组织和力学性能的影响

采用扫描电子显微镜、X射线衍射、室温和高温压缩试验等方法研究了固溶时效对Ni50Ti44Al6合金微观组织和力学性能的影响.Ni50Ti44Al6合金的铸态微观组织是由NiTi基体和沿晶界分布的网状组织构成.随着固溶温度升高,合金中的网状组织部分消失,第二相在基体中趋向于均匀的弥散分布;随时效时间延长,合金的强度先升高后降低.固溶时效处理能有效改善Ni50Ti44Al6合金的力学性能.最佳的处理制度为:合金在1150℃固溶6 h,水淬,再在700℃时效6 h.     

Microstructure and property of the Ti-24Al-15Nb-1.5Mo/TC11 joint welded by electron beam welding

The Ti-24Al-15Nb-1.5Mo alloy, in the as-forged and heat-treated states, was joined to the as-forged TC 11 titanium alloy by electron beam welding with the heat inputs of 135 and 150 kJ/m. Then the microstructure and property of the Ti-24Al-15Nb-1.5Mo/TC 11 welding interface were investigated. The results show that the phase constitution of the weld is not related to the heat input, and is mainly composed of α' phase. Moreover, the intermetallic phases of TiEAlNb, MoNb, Nb₃Al, and TiAl₃ are formed in the weld zone. Therefore, the microhardness value of the weld zone is higher than that of the other portions in the same sample. The profile of the weld is asymmetrically fimnel-like. The grain sizes of the weld and its heat-affected zones are increased with increasing heat input. There is an obvious difference in the element content of the welding interface; only the alloying elements in the fusion zone reach a new balance during solidification.     

MA-SPS制备超细晶Ti-8Mo-3Fe合金的摩擦磨损性能

以机械合金化+放电等离子烧结(MA-SPS)制备的超细晶Ti-8Mo-3Fe合金为研究对象,研究了合金在模拟体液(SBF)中的摩擦磨损性能,并与放电等离子烧结制备的微米尺寸晶粒的Ti-8Mo-3Fe合金、铸造纯Ti及Ti-6Al-4V(TC4)合金进行了对比.结果表明:采用MA-SPS工艺可制备出高致密度、组织均匀的超细晶Ti-8Mo-3Fe合金,合金由β相及少量α相组成,平均晶粒尺寸为1.5μm,显微硬度为448 HV;在相同摩擦磨损条件下,超细晶Ti-8Mo-3Fe合金的摩损程度明显低于微米晶粒Ti-8Mo-3Fe和铸态的纯Ti及TC4合金,具有最低的磨损体积和较稳定的摩擦系数.超细晶Ti-8Mo-3Fe合金的磨损机制为磨粒磨损,而微米晶粒Ti-8Mo-3Fe和铸态纯Ti及TC4合金的磨损机制为磨粒磨损和黏着磨损并存的混合磨损.     

多级热处理对TC21钛合金组织和力学性能的影响

Duplex-structured TC21 alloy samples were first solution-treated at a higher temperature in the α + β region (940°C) with furnace cooling (FC), air cooling (AC), and water cooling (WC), followed by a second-stage solution treatment at a lower temperature in the α + β region (900°C), and then finally aged at 590°C. The effects of the morphology and quantity of α phases on the structure and properties of the TC21 alloy after the different heat treatments were analyzed. The in-situ tensile deformation process and crack propagation behavior were observed using scanning electron microscopy (SEM). The quantity of equiaxed α phases as well as the thickness of lamellar α phases reduced, the tensile strength increased firstly and then decreased, the elongation decreased with the increasing cooling rate after the first-stage solution treatment. The amount and size of lamellar α phases increased after the second-stage solution treatment because of sufficient diffusion of the alloying elements, thereby leading to increased tensile strength. The amount of dispersed α phases increased after the third-stage aging treatment owing to the increase in the nucleation rate, resulting in a noteworthy strengthening effect. After the third-stage aging treatment, the first-stage FC sample exhibited better mechanical properties because it contained more equiaxed α and β_trans phases than the first-stage AC and WC samples.     

Burn-resistant behavior and mechanism of Ti14 alloy

The direct-current simulation burning method was used to investigate the burn-resistant behavior of Ti14 titanium alloy. The results show that Ti14 alloy exhibits a better burn resistance than TC4 alloy (Ti–6Al–4V). Cu is observed to preferentially migrate to the surface of Ti14 alloy during the burning reaction, and the burned product contains Cu, Cu₂O, and TiO₂. An oxide layer mainly comprising loose TiO₂ is observed beneath the burned product. Meanwhile, Ti₂Cu precipitates at grain boundaries near the interface of the oxide layer, preventing the contact between O₂ and Ti and forming a rapid diffusion layer near the matrix interface. Consequently, a multiple-layer structure with a Cu-enriched layer (burned product)/Cu-lean layer (oxide layer)/Cu-enriched layer (rapid diffusion layer) configuration is formed in the burn heat-affected zone of Ti14 alloy; this multiple-layer structure is beneficial for preventing O₂ diffusion. Furthermore, although Al can migrate to form Al₂O₃ on the surface of TC4 alloy, the burn-resistant ability of TC4 is unimproved because the Al₂O₃ is discontinuous and not present in sufficient quantity.     

Ductile fracture behavior of TA15 titanium alloy at elevated temperatures

To better understand the fracture behavior of TA15 titanium alloy during hot forming, three groups of experiments were conducted to investigate the influence of deformation temperature, strain rate, initial microstructure, and stress triaxiality on the fracture behavior of TA15 titanium alloy. The microstructure and fracture surface of the alloy were observed by scanning electronic microscopy to analyze the potential fracture mechanisms under the experimental deformation conditions. The experimental results indicate that the fracture strain increases with increasing deformation temperature, decreasing strain rate, and decreasing stress triaxiality. Fracture is mainly caused by the nucleation, growth, and coalescence of microvoids because of the breakdown of compatibility requirements at the α/β interface. In the equiaxed microstructure, the fracture strain decreases with decreasing volume fraction of the primary α-phase (α_p) and increasing α/β-interface length. In the bimodal microstructure, the fracture strain is mainly affected by α-lamella width.     

铸造1060/AZ31包铝镁合金界面结构与显微组织

为探索和改善轧制包铝镁合金板的界面结合状况,用气体保护铸造法制备了1060铝板包覆AZ31镁合金铸锭．借助金相显微镜、扫描电镜以及X射线衍射等分析方法,研究了复合铸锭芯材及界面的显微组织和相结构,并进行了硬度测试．发现AZ31镁合金芯材组织由α-Mg基体以及沿晶界分布的不连续网状α-Mg＋p＋Mg17A112共晶体组成,是一种典型的铸造离异共晶组织．铸造包铝镁合金锭界面形成扩散溶解层,扩散溶解层由α-Mg固溶体层、共晶层（α-Mg＋β＋Mg17A112）、β-Mg17A112及A1Mg化合物层组成,形成具有多层结构的冶金结合界面．提出了浇注AZ31熔体的瞬间在1060铝板表面形成“熔池”并快速凝固的界面形成机制．     

退火对表面纳米化纯钛热稳定性的影响

采用表面机械研磨技术实现纯钛材料表面纳米化,并研究了纳米化处理后的材料表层组织结构,详细分析了样品表层纳米晶组织在不同温度、不同时间退火后的热稳定性.结果表明:纯钛TA2经过表面机械研磨处理后可以在表面形成等轴且取向随机的纳米晶层,晶粒尺寸约为12nm.对表面纳米化样品退火后发现,表层纳米晶组织在773 K以下温度退火后具有良好的热稳定性,晶粒尺寸没有明显增大;在773 K温度退火150min后晶粒尺寸稍有增大,而在773 K温度退火240min后晶粒尺寸明显增大,且横截面显微硬度也比表面纳米化后未退火样品显著下降,良好的热稳定性消失.     

Microstructure and properties of an Al-Ti-Cu-Si brazing alloy for SiC-metal joining

An Al-Ti-Cu-Si solid-liquid dual-phase alloy that exhibits good wettability and appropriate interfacial reaction with SiC at 500-600℃ was designed for SiC-metal joining. The microstructure, phases, differential thermal curves, and high-temperature wetting behavior of the alloy were analyzed using scanning electron microscopy, X-ray diffraction analysis, differential scanning calorimetry, and the sessile drop method. The experimental results show that the 76.5Al-8.5Ti-5Cu-10Si alloy is mainly composed of Al-Al₂Cu and Al-Si hypoeutectic low-melting-point microstructures (493-586℃) and the high-melting-point intermetallic compound AlTiSi (840℃). The contact angle, determined by high-temperature wetting experiments, is approximately 54°. Furthermore, the wetting interface is smooth and contains no obvious defects. Metallurgical bonding at the interface is attributable to the reaction between Al and Si in the alloy and ceramic, respectively. The formation of the brittle Al₄C₃ phase at the interface is suppressed by the addition of 10wt% Si to the alloy.     

Microstructures and mechanical properties of a new titanium alloy for surgical implant application

A new titanium alloy Ti12.5Zr2.5Nb2.5Ta (TZNT) for surgical implant application was synthesized and fully annealed at 700℃ for 45 min. The microstructure and the mechanical properties such as tensile properties and fatigue properties were investigated. The results show that TZNT mainly consists of a lot of lamella α-phase clusters with different orientations distributed in the original β-phase grain boundaries and a small amount of β phases between the lamella α phases. The alloy exhibits better ductility, lower modulus of elasticity, and lower admission strain in comparison with Ti6Al4V and Ti6Al7Nb, indicating that it has better biomechanical compatibility with human bones. The fatigue limit of TZNT is 333 MPa, at which the specimen has not failed at 107 cycles. A large number of striations present in the stable fatigue crack propagation area, and many dimples in the fast fatigue crack propagation area are observed, indicating the ductile fracture of the new alloy.     

Creep behavior and effect factors of a TiAl–Nb alloy at high temperature

The effect of solution treatment on the microstructure and creep properties of forged TiAl–Nb alloys was investigated. The results showed that the microstructure of forged alloy mainly consisted of γ/α₂ lamellar colonies and fine equiaxed recrystallized γ/α₂ grains. During the solution treatment the microstructure of the alloy transformed into a fully lamellar structure due to the lamellar colonies growth by consuming equiaxed grains. Compared with the forged alloy the creep life of the solution treated alloy at 800 ?°C/220 ?MPa increased from 116 ?h to 339 ?h. The better creep resistance may be attributed to the transform of fine equiaxed γ/α₂ grain to the lamellar colonies with serrated grain boundaries due to the solution treatment. The deformation mechanism of the solution treated alloy during creep is considered to be dislocation slipping within the lamellar γ/α₂ phases, and the dislocation movement may be hindered by the γ/α₂ interface and the formation of dislocation tangles. The interaction of the dislocations with the tangles may increase the resistance of the dislocation motion and hence improve the creep resistance of the alloy. It was found that during the creep of the forged alloys the cracks mainly initiated at the equiaxed grain, and in the solution treated alloy the cracks initiated at the grain boundaries. As creep continued the cracks propagated and connected to each other, leading to the damage and rupture of the forged and solution treated alloys.