SiCP/ Ni 纳米复合材料的超塑性

研究了SiC_P / Ni 纳米复合材料的超塑性。SiC_P / Ni 采用脉冲电沉积方法获得。拉伸实验温度为410 ℃和450 ℃, 应变速率范围为8.3 ×10 -4～ 5 ×10 -2 s -1 。温度为450 ℃、应变速率为1.67 ×10 -2 s-1时, 获得的最大延伸率为836 %。采用SEM、TEM 分析了沉积态材料的表面形貌、断口形貌及变形后的组织, 并对变形机理进行了探讨。通过SiC 颗粒稳定基体组织有利于实现材料的超塑性, 低空洞体积分数有助于获得大延伸率。晶粒长大到微米尺度时, 变形机制主要是位错协调的晶界滑移和位错滑移塑性。      

电沉积纳米复合材料的超塑性研究

采用脉冲电沉积技术制备了含不同Al2O3颗粒的Al2O3/Ni-Co纳米复合材料,在应变速率从8.33×10-4s-1到1.67×10-2s-1,温度从723K到823K的范围内,研究了它们的超塑性拉伸变形行为,确定了最佳超塑性条件并获得了最大延伸率.采用SEM和TEM对电沉积和超塑变形前后试件的显微结构进行了表征.应用晶粒长大行为和协调机制对合金和复合材料的超塑性进行了对比研究和讨论.     

Ti6A14V合金的低温超塑性拉伸变形行为

在700℃-850℃的温度范围内对Ti-6%Al-4%V(质量分数)合金板材进行超塑性拉伸试验,研究了应变速率为3×10-4-5×10-38-1条件下的拉伸变形行为.结果表明:Ti6A14V合金在空气中表现出良好的低温超塑性变形能力.在800℃初始应变速率ε=5×10-4s-1条件下,延伸率达到536%.在较低的700℃下变形(ε=5×10-4s-1),延伸率仍然超过了300%.在整个变形温度区间内,应变速率敏感性指数m均为0.3左右,最大值为0.63.在850℃变形激活能与晶界自扩散激活能十分相近,表明晶界扩散控制的晶界滑动是超塑性变形的主要机制.在700-750℃,变形激活能远大于晶界自扩散激活能,位错运动是激活能升高的原因.在800℃变形的激活能介于两者之间,表明随着温度的降低变形机制逐渐发生改变.     

喷雾沉积法制造的铝基复合材料的超塑性

喷雾沉积法制造的SiC_P/LY12复合材料经热压和热正挤压后,晶粒得以细化,SiC_P分布的均匀性大大改善.超塑性拉伸试验结果表明:SiC_P/LY12复合材料具有超塑性;变形温度、应变速率对极限延伸率和应变速率敏感性指数m值均有较大的影响.在变形温度为500℃和初始应变速率为1.0×10-3s-1时,获得的极限延伸率为345%.      

2A97 铝锂合金超塑变形规律及其本构方程

目的研究2A97铝锂合金在390~470℃温度范围和3×10-4~3×10-2s-1应变速率范围内的超塑变形行为,揭示温度和应变速率对延伸率和峰值应力的影响规律,并建立超塑拉伸变形本构方程。方法采用单轴超塑拉伸试验方法进行研究。结果当变形应变速率低于3×10-3s-1时,2A97铝锂合金真应力-真应变曲线呈现稳态流变特征;当应变速率高于3×10-3s-1时,则呈现软化特征。在450℃,应变速率为1×10-3s-1条件下,达到最大延伸率600%。结论 2A97铝锂合金具有良好的超塑变形性能,其应变速率敏感性指数m平均值为0.35,超塑变性激活能Q值为145.87 k J/mol,远高于纯铝自扩散激活能65.6 k J/mol,表明此时铝锂合金变形机制仍以晶内滑移为主。     

异步轧制AZ31镁合金板材的超塑性工艺及变形机制

经过异步轧制工艺获得AZ31镁合金薄板。在300~450℃范围内,分别通过5×10-3,1×10-3s-1和5×10-4s-1不同应变速率进行高温拉伸实验研究其超塑性变形行为,计算应变速率敏感指数m值、超塑性变形激活能Q及门槛应力σ0值。通过EBSD分析和扫描电镜观察拉伸断裂后的断口形貌,分析AZ31镁合金的超塑性变形机制。结果表明:AZ31镁合金的塑性变形能力随着变形温度的升高及应变速率的降低而增强。当拉伸温度为400℃、m=0.72、应变速率为5×10-4s-1时,AZ31具有良好的超塑性,伸长率最大为206%。温度为400℃时,异步轧制AZ31镁合金的超塑性变形是以晶格扩散控制的晶界滑移和基面滑移共同完成的。     

7075Al/SiCp复合材料的热压缩变形流变应力和组织行为

采用圆柱试样在Gleeble-1500热模拟机上对喷射沉积7075Al/SiCp复合材料进行高温压缩变形实验,实验条件为:变形温度300～450℃,应变速率0.001～1s-1.结果表明:7075Al/SiCp复合材料的流变应力大小受到变形温度和应变速率的强烈影响,流变应力随应变的增加而逐渐增加,出现一峰值后逐渐下降;流变应力随变形温度的升高、应变速率的降低而降低.可用Zener-Hollomon参数的双曲正弦形式来描述7075Al/SiCp复合材料高温压缩变形流变应力.随着变形温度的升高和应变速率的降低,7075Al/SiCp复合材料热变形过程中SiCp的分布逐渐均匀化,有利其热加工性能的改善.     

电沉积制备纳米镍的拉伸变形行为

为了系统研究纳米材料的超塑性变形特点,用电沉积方法制备了平均晶粒尺寸为70 nm的纳米镍.采用单向拉伸实验研究了其在室温和高温时的力学性能,并用透射电子显微镜TEM、扫描电子显微镜SEM和X射线能谱仪EDS观察分析了纳米镍变形前后的显微组织.实验结果表明:制备的纳米镍在室温时表现出的延伸率很低,但强度可达1000 MPa以上.当温度升高至450℃,应变速率为1.67×10-3 s-1时单向拉伸实验得到380%的延伸率,说明制备的纳米镍具有低温超塑性性能.实验过程中,材料内部的晶粒发生明显的长大与拉长.拉伸过程中形成的氧化物夹杂成为裂纹源,断口表现为沿晶断裂.     

粉末冶金法生产SiCp／MR64复合材料及其超塑性的研究

本文用粉末冶金法生产SiCp/MR64复合材料,并对其超塑性进行了研究。在500℃～520℃、应变速率为8.33×10~(-3)s~(-1)获得最大延伸率为210％。SiCp数量和尺寸对超塑性有很大影响,复合材料超塑性低的原因在于变形过程中产生大量孔洞,孔洞是应变软化的主要原因。     

AZ61镁合金薄板超塑性变形特征的SEM研究

利用扫描电镜(SEM)和超塑性拉伸实验对一次热挤压加工成型的AZ61镁合金薄板(晶粒尺寸～12μm)超塑性变形特征进行了研究.结果显示,在最佳的变形温度(623K)和应变速率(1×10-4s-1)条件下,可获得的最大的超塑性形变量为920%.在523～673 K实验温度和1×10-2～1×10-5s-1应变速率范围内,材料的应变速率敏感指数(m值)随实验温度升高和应变速率的降低而增加.较高的m值(0.42～0.46)对应于晶界滑动机制(GBS),而较低的m值(0.22～0.25)则对应于位错滑移机制.变形温度和应变速率是影响超塑性变形量和变量机制的主要因素.     

Preparation of self-supporting nickel targets from Ni, Ni and Ni

The investigation of the distribution of the fusion-barrier height by heavy-ion collisions requires thin self-supporting targets. To increase the accuracy of the measurement the thickness and homogeneity has to be known as precisely as possible.We prepared the self-supporting nickel foils out of the isotopes ⁵⁸Ni, ⁶⁰Ni and ⁶¹Ni. The resulting targets were between 75 and 105 μg/cm^² thick. The foils were produced on copper backing by electron-beam gun evaporation and by extracted ion-beam sputtering, both in high vacuum. To obtain self-supporting nickel foils the copper was removed by etching. We will discuss and compare both methods.     

Nanostructured Ni3Al layers and Ni3Al/Ni multilayers obtained by magnetron sputtering

Intermetallic Ni₃Al thin layers and Ni₃Al/Ni multilayers were deposited on a Si wafer by means of magnetron sputtering. The structure and morphology of the layers have been characterized by X-ray diffraction, transmission electron microscopy and atomic force microscopy. The polycrystalline films are textured in the (111) direction and have grain sizes below 20 nm. Superlattice reflections due to chemical order have been observed in the electron microscope. It is shown by x-ray diffraction that the multilayers grow coherently on the amorphous substrate.     

Modulated Structures in 10Ni and 18Ni Maraging Steels

1.IntroductionSince the theory of spinodal decompo-sition in a supersaturated solid solution wasformulated by Hillert[1]and Cahn[2],thephenomena of spinodal decomposition havebeen found in many alloys.Tamura[3]haspointed out that spinodal decompositioncould also occur in maraging steels.A mod-ulated structure in 8Ni maraging steel was     

Ni and Ni/Pt filling inside multiwalled carbon nanotubes

Multiwalled carbon nanotubes are grown by microwave plasma chemical vapor deposition with CH4 and H2 as precursor gases. Ni and Ni/Pt electroplated layers are used as catalysts for the synthesis of the tubes. We observe that a very efficient filling of the tubes takes place with Ni. In some cases Ni/Pt filling is also observed inside the tubes. High-resolution transmission electron microscopy (HRTEM) studies, coupled with energy-dispersive X-ray analyses of the tubes, indicate Ni nanorods with a highly symmetrical cylindrical structure. The diameter of the cylindrical nanorods is on the order of 40 nm, and their length is 660 nm. The nano area diffraction pattern of the nanorods reveals the cubic structure of nickel, and electron diffraction spots corresponding to (111), (200), (220) planes are evident. The lattice constant of Ni measured from the diffraction spots was found to be 0.347 +/- 0.0013 nm. This should be compared with 0.352 nm, the value of "a" in bulk Ni. The decrease in the lattice constant may be due to the strain experienced inside the tubes. Raman spectroscopy shows the typical signature of the tangential breathing mode present in the tubes at 1580 cm-1 that shifts to a new position when the C12 is replaced by 13C. The shift, however, is too small and is difficult to explain on the basis of mass difference. HRTEM experiments indicate the presence of Ni3C in the samples dominantly in the interfacial region.     

铝材表面Ni-MoS2自润复合镀层及其性能

采用扫描电镜、化学分析法和电化学方法，详细研究了阴极电流密度、镀液温度、镀液中MoS     

Magnetic Properties of Ni Nanoparticles and Ni（C） Nanocapsules

Structure and magnetic properties of Ni nanoparticles and Ni(C) nanocapsules were studied.The carbon atoms hardly affect the lattice of Ni to form Ni-C solid solution or nickel carbides.The large thermal irreversibility in zero-field-cooled and zero-field magnetization curves indicates magnetic blocking with a wide energy barrier.Saturation magnetization,remanent magnetization and coercivity of Ni(C) nanocapsules decrease with increasing temperature.magnetization,remanent magnetization and coercivity of Ni(C) nanocapsules decrease with increasing temperature.     

Sintering behaviour of Ti-2Ni and Ti-5Ni elemental powders

The effect of nickel powder additions (2 and 5 at.%) on the sintering behaviour of titanium powder has been investigated through the dilatometric sintering study. The sintering of titanium powder was found to be enhanced significantly and the activation energies were decreased with increasing nickel content. The sintering of Ti-2 at.% Ni system at lower temperature was found to be controlled by Ti-Ti and Ti-Ni solid state sintering, whereas inter-diffusion dominates in Ti-5 at.% Ni sintering. At higher temperatures, sintering was found to be controlled by mixed mechanisms, i.e. inter-diffusion, chemical reaction and transient liquid phase formation.