掺氮类金刚石薄膜的纳米力学及纳米摩擦特性研究

利用微波电子回旋共振化学气相沉积技术制备了不同氮掺杂量的类金刚石(DLC)薄膜,采用俄歇电子能谱仪、Raman光谱仪和Hysitron型纳米力学测试系统对掺氮类金刚石薄膜的化学成分和结构、纳米力学及其纳米摩擦特性进行研究.结果表明:反应气体中氮气流量比例越大,类金刚石薄膜中的氮含量越高;随着薄膜中氮含量增加,掺氮类金刚石薄膜中sp3比例下降,sp2比例明显增加,而薄膜的纳米力学性能如纳米硬度和弹性模量明显下降;纳米划擦试验中的划痕深度与薄膜中氮含量有关,当载荷相同时,氮含量越高,所对应的划痕深度越深;名义摩擦系数(LF/NF)随着载荷增加而增大;当载荷相同时,摩擦系数与沉积膜中的氮含量无关.     

氮化钛沉积膜的摩擦性能研究

采用等离子电弧沉积法在9Crl8钢表面制备了厚约0．5μm的TiN薄膜，通过显微硬度测试以及纳米压痕和纳米划痕试验，对比考察了9Crl8钢及其表面T|N薄膜的机械和摩擦性能．结果表明，9Crl8钢及其表面T．N沉积膜的纳米硬度分别为8GPa和38GPa，弹性模量分别为250GPa和580GPa，9Crl8、TiN和有机薄膜的摩擦系数分别为0．40、0．12和0．10；TiN沉积膜可显著提高基体钢的承载和耐磨能力．     

脉冲直流等离子体增强化学气相沉积Ti—Si—N纳米薄膜的摩擦磨损特性

采用工业型脉冲等离子体增强化学气相沉积设备，通过调节氯化物混合比例控制薄膜成分，在高速钢基材表面于550℃下沉积由纳米晶TiN和纳米非晶Si3N4组成的Ti—Si—N复合薄膜；采用扫描电子显微镜、透射电子显微镜、X射线衍射仪及X射线光电子能谱仪分析了薄膜的结构、组成和化学状态；采用球-盘高温摩擦磨损试验机考察了薄膜同GCrl5钢对摩时的摩擦磨损性能．结果表明：薄膜的Si含量在0％～35％范围内变化，随着Si含量增大，薄膜沉积速率增大，但薄膜由致密形态向大颗粒疏松态过渡；薄膜的晶粒尺寸为7～50nm；Ti—Si—N薄膜的显微硬度高于TiN的硬度，最高可达60GPa；引入少量Si可以显著改善TiN薄膜的抗磨性能，但薄膜的摩擦系数较高(室温下约0．8、400℃下约0．7)；随着Si含量的增加，Ti—Si—N薄膜的耐磨性能有所降低，其原因在于引入导电性较差的Si元素使得薄膜的组织变得疏松．     

亚微米氮化钛膜的纳米压痕和划痕测定

采用等离子电弧沉积的方法，分别在GT35和40CrNiMo钢上沉积厚约为0．5μm的氮化钛(TiN)膜．为了筛选基材，采用纳米压痕和划痕技术，评价膜基界面结合和固体润滑效果．纳米压痕结果，GT35，40CrNiMo和TiN的纳米硬度／弹性模量的典型值分别约为11．5GPa／330GPa，6．0GPa／210GPa，30GPa／450GPa．纳米划痕结果，GT35有较理想的膜基结合能力；GT35，40CrNiMo，TiN及其有机膜的摩擦系数分别约为0．25，0．45，0．i5，0．i0．同40CrNiMo相比，GT35是较为理想的基体材料．纳米压痕和划痕技术能提供丰富的近表面的弹塑性变形、断裂和摩擦等的信息，是评价亚微米薄膜力学性能的有效手段．     

石墨对三氧化二铝/铜金属陶瓷复合材料摩擦磨损性能的影响

采用粉末冶金技术制备了Al2O3／Cu石墨复合材料；采用MM-200型摩擦磨损试验机考察了石墨对Al2O3／Cu基金属陶瓷复合材料摩擦磨损性能和硬度的影响；采用扫描电子显微镜分析了复合材料磨损表面形貌．结果表明：Al2O3／Cu基复合材料的摩擦系数随石墨含量的增加而降低，当石墨含量大于1.0％后，摩擦系数降低明显；当石墨含量低于3％时，Al2O3／Cu基复合材料的磨损体积损失随石墨含量的增加而降低；当石墨含量低于2．0％时，石墨对Al2O3／Cu基复合材料的硬度无明显影响；当石墨含量超过3．0％后，Al2O3／Cu基复合材料的硬度随石墨含量的增加迅速降低；此外，石墨使得Al2O3／Cu基复合材料磨损表面的微裂纹减少、裂纹长度缩短；当石墨含量达到2．5％时，复合材料磨损表面微裂纹消失．这是由于石墨在磨损表面形成固体润滑膜，从而降低摩擦力并减少裂纹源所致．     

非晶含氢碳薄膜摩擦与抗擦伤性能的实验研究

用射频等离子体增强化学气相沉积法在钛合金表面制备了非晶含氢碳（a-C:H)薄膜,利用原小孩子显微镜、纳米力学探针、划痕仪以及滑动摩擦和微动摩擦试验仪器等研究了其表面形貌、粗糙度、硬度和摩擦性能,分析了薄膜的表面粗糙度、硬度及载荷对摩擦系数的影响。结果表明：随着薄膜厚度的增加,硬度略有提高,划痕临界载荷明显提高,而表面粗糙度先增加后降低,最后趋于稳定;室温空气中的滑动摩擦系数随硬度的增大以及表面粗糙度和载荷的减小而降低;在微动摩擦试验中,随相对湿度增加,摩擦系数降低,这有利于其在体液环境中的应用;薄膜具有良好的耐磨性能,经5000次摩擦后磨损很小。     

纳米复合材料激光熔覆层组织及抗磨性能

利用5kWCO2激光器，在Ni基高温合金表面制备了纳米Al2O3／钴基合金熔覆层，分析了熔覆层的组织结构及其抗磨性能．结果表明，当纳米Al2O3颗粒含量较低时，Al2O3颗粒能均匀分布于熔覆层中，从而形成纳米氧化物弥散强化的复合材料涂层；Al2O3颗粒在熔池中长大，尺寸为250-450nm；复合材料熔覆层的硬度随纳米Al2O3含量的增加而提高；当纳米Al2O3颗粒含适中时，熔覆层的抗磨性能较好；而当纳米Al2O3颗粒含量过高(3．0％)时，复合材料熔覆层的抗磨性能反而降低。     

C2H2/Ar流量比对a-C:H涂层结构及摩擦学性能的影响

a-C:H涂层因具有高硬度、低摩擦系数及良好的化学惰性等性能,使其作为表面防护材料具有广泛的应用前景,而涂层中的H含量和sp2C/sp3C比值是影响其力学及摩擦学性能的重要因素. 本研究中采用非平衡磁控溅射技术在9Cr18钢表面制备了a-C:H涂层,对比研究了前驱体组成对不同结构含H碳膜的氢含量、微观结构、力学性能和摩擦学性能的影响. 结果表明:增大C₂H₂/Ar流量比,涂层的生长率及H含量逐渐增大,但致密性降低. 由于涂层中C-H键及致密性的变化,a-C:H涂层的硬度和弹性模量随C₂H₂/Ar流量比的增大而逐渐减小,但结合强度却先增大后降低. 当C₂H₂/Ar流量比低于4:3时,涂层表现出良好的减摩耐磨性能,当C₂H₂/Ar流量比高于4:3时,涂层的摩擦系数和磨损率出现了急增的现象. 总体而言,a-C:H涂层的摩擦系数和磨损率随C₂H₂/Ar流量比的增加呈现先增大后降低的趋势. 由于H原子的钝化作用及涂层力学性能的变化,使a-C:H涂层的磨损机制由磨粒磨损和黏着磨损变为磨粒磨损. 当C₂H₂/Ar流量比为1:1时,a-C:H涂层具有最低的摩擦系数(约为0.1)和磨损率[8.0×10?8 mm3/(N·m)],表现出最佳的力学及摩擦学性能,这种性能的变化与涂层中的H含量和sp2C/sp3C比密切相关.      

碳化硅薄膜的力学性能测试分析

对利用射频磁控溅射及真空退火方法在(100)硅晶片衬底上制备的纳米晶碳化硅(SiC)薄膜,用纳米压痕仪进行了力学性能测试分析。纳米压痕技术测试给出两块SiC薄膜样品I和II的弹性模量/硬度分别约为106GPa/9.5GPa和175GPa/15.6GPa。纳米划痕技术测试两块SiC薄膜的摩擦系数分别约为0.02~0.15和0.05~0.18,显示出良好的润滑性能;对薄膜的临界附着力等进行测量以评价膜基结合强度,分析了划痕过程中薄膜近表面弹塑性变形和断裂信息。在原子力显微镜下对SiC薄膜样品的初始表面及残余压痕和划痕形貌进行了观察分析,与测试结果相符。综合比较,样品II的整体性能优于样品I。本文中薄膜的弹性模量和硬度值较低可归因于制膜技术的不同和表层碳含量偏高。     

C/N共掺MoS2复合薄膜的微结构及其摩擦特性研究

采用射频磁控溅射法,在氩和氮混合气氛下共溅射二硫化钼和石墨靶制备不同石墨靶溅射功率的C/N共掺MoS_2复合薄膜(MSCN).通过EDS、XPS、SEM和TEM对薄膜的成分及微观组织结构进行分析;利用纳米压痕仪,高真空摩擦试验机和UMT-2摩擦试验机分析薄膜的力学和摩擦学性能,并探讨了C/N共掺及对薄膜结构、力学和摩擦学性能的影响.结果表明:MSCN复合薄膜中的C含量随着石墨靶溅射功率的增加而增加;C/N共掺使得薄膜结构致密平整;当石墨靶溅射功率350 W时,薄膜呈现自形成纳米多层结构,该结构的出现使得薄膜最高硬度可达9.76 GPa,并且在高真空和大气环境下相比纯MoS_2薄膜表现出更低的摩擦系数以及良好的高耐磨性.     

PU/PMMA IPNs复合材料的摩擦学性能和阻尼性能研究

聚合物互穿网络(IPNs),结构可调且设计性强,是制备具有阻尼减振效果兼具海水润滑特性复合材料的一种有效选择.本研究中设计合成了一系列组成成分不同的基于聚四氢呋喃二元醇(PTMG)-聚氨酯(PU)/聚甲基丙烯酸甲酯(PMMA)的互穿网络结构(IPNs),并系统研究了PU/PMMA IPNs在海水润滑条件下的摩擦学性能及其阻尼性能.结果表明:随着PU含量的增加,其摩擦系数和磨损率均显著降低,当PU与PMMA的组成比例为60/40时,复合材料的摩擦系数降低至0.15,质量磨损率0.10%;同时材料的阻尼因子从0.77降至0.24,有效阻尼温域从40℃降至25℃,阻尼性能呈下降趋势.     

在役设备材料弹塑性力学参数测定方法综述--小冲杆实验力学研究进展之一

20多年以来,采用小型试件的小冲杆试验技术来测量在役设备材料的各种力学参数已经取得了很大进展,这个方法已经用来确定材料的弹性模量、屈服强度、塑性性能、抗拉强度、韧一脆转变温度、断裂韧度、蠕变性能和黏塑性性能等各种力学性能。由于从小冲杆试验的测量结果来确定材料的力学性能是一个反问题,因此,与此有关的反问题分析方法也得到了相应的发展。本文系统综述小冲杆试验的测量技术及从测量数据来确定材料弹塑性参数的各种经验方法和计算方法,例如有限元分析和参数法、反向有限元法、有限元和反方法、反向识别和人工神经网络、有限元优化和试验变形形状以及杂交反方法等。     

山东龙口北皂煤矿软岩力学特性实验研究

根据室内实验结果, 本文讨论了北皂煤矿的岩石力学性质, 物化特性。泥质岩类的力学性质和水理性质、物化特性有关。泥质岩类具有显著的流动变形和各向异性。     

Rheological properties of pressure-sensitive adhesives: polyisobutylene/sodium carboxymethylcellulose

The viscoelastic properties of polyisobutylene filled with sodium carboxymethylcellulose were studied. Using shear viscosity data, the relaxation time,, defined as the ratio ₀/G ₀ of the initial viscous and elastic constants was evaluated. The flow activation energy, melt flow index and superposition shift factor were also determined and master curves were generated. A relatively small effect of filler concentration on viscosity was observed, whereas its effect on and the initial first normal-stress coefficient, ₀, was found to be significant.     

An alternative approach to the linear theory of viscoelasticity and some characteristic effects being distinctive of the type of material

In the introduction some postulates on which the linear theory of viscoelasticity is based are recalled, and the postulate of passivity is substituted by a stronger postulate called detailed passivity.Next, a symmetric formulation of this theory is presented which is founded in a well-balanced way on the limiting properties of elasticity and viscosity. This leads to the introduction of the basic functions of creep compliance J ⁺(t) and stressing viscosity ⁺(t) associated to one another, whereas the basic functions retardation fluidity ⁺(t) and relaxation modulus G ⁺(t) emerge as their time derivatives. Correspondingly, four complex basic functions are defined as their Carson transforms.In addition to the proper retardation and relaxation terms, these basic functions contain the non-disappearing constants of either instantaneous compliance J ₀ or instantaneous viscosity ₀ and also of either ultimate fluidity or ultimate modulus G . Therefrom ensues a classification of linear viscoelastic materials into four types: instantaneous elasticity or viscosity is allowed to combine with ultimate viscosity or elasticity. The latter alternative, signifying fluidlike or solidlike materials, leads, of course, to a quite different behavior in many situations; however, remarkable distinctive features are associated to the first one as well.A few respective examples are outlined: 1) propagation of shear waves in a half-space with periodic and step-shaped excitation, 2) dissipation of work in a torsional vibration damper, and 3) shear flow between two parallel porous plates with injection and suction.Finally, materials with viscous initial behavior are defended against the notion that they be of no or almost no real significance.Delivered as a Plenary Lecture at the Fourth European Rheology Conference, Seville (Spain), 4–9 September 1994. The herein only outlined topics are taken from a recently pulished monograph (Geisekus, 1994) in which complete derivations of the results and more detailed discussions are given.Dedicated to Professor K. Walters on the occasion of his 60th birthday.     

Dynamic and transient rheological properties of glass filled polymer melts

The dynamic and transient rheological properties of a low density polyethylene melt and a plasticized polyvinylchloride melt filled with glass beads were measured at 200 °C and 180 °C respectively in a modified Weissenberg Rheogoniometer R-17. Its main modification consisted of the use of a piezoelectric transducer instead of the conventional torsion bar, and of the interfacing of a microcomputer Apple II plus to the Rheogoniometer for data acquisition and analysis. The glass beads were pretreated with silane and titanate coupling agents to observe the effect of the chemical modification of the polymer filler interface on these properties. It was observed that both the dynamic viscosity and the storage modulus increased with the weight fraction, but this last parameter did appreciably affect the stress growth and stress relaxation curves of the polymeric matrices at low shear rates. The effect of coupling agents on these properties was varied.     

AlCoCrFeNi高熵合金的高温摩擦磨损性能

AlCoCrFeNi高熵合金因其优异的综合力学性能而有望成为新一代高温结构材料,但对其高温摩擦磨损性能的研究还较为少见.本文中应用放电等离子烧结(SPS)技术制备了AlCoCrFeNi高熵合金,研究了其显微组织和力学性能,系统地考察了其在室温至800℃时的摩擦磨损性能.结果表明:应用SPS技术制备的AlCoCrFeNi高熵合金主要由FCC相、无序BCC相和少量有序BCC相组成;呈网格状分布的FCC相使高熵合金具有良好的塑性和韧性,而呈等轴状分布的BCC相赋予了高熵合金优异的强度;高熵合金室温至800℃时的摩擦系数在0.43~0.51之间,磨损率低于10–5mm3/(N·m).室温至中温阶段主要为磨粒磨损,中温至高温阶段的磨损机制为磨粒磨损、黏着磨损和塑性变形综合作用.高温下高熵合金表面形成了一层主要由为Al2O3和Cr2O3组成的氧化物膜,在一定程度上起到抗磨作用.     

Characterization of powder flow properties from micron to nanoscale using FT4 powder rheometer and PT-X powder tester

The rapid development of nanotechnology has led to a need to further understand the physical characteristics of nanoparticles. In this paper, the flow characteristics of micro-nano alumina particles with different particle sizes were characterized. The FT4 powder rheometer and the PT-X powder tester were used to measure the compression, friction, and dynamic properties of powders. Powder compressibility increased significantly as the particle size decreased from 27 μm to 30 nm. Pressure distribution in the silo was measured and predicted by Janssen's theory, with errors mostly less than 10%. The basic flow energy and the specific energy of the three powders were 4983, 1734, and 244 mJ, and 6.80, 11.70, and 6.70 mJ/g, respectively, indicating that there was no linear relationship between the change in flowability and particle size. The dynamic properties of the powders change from particle-dominated to agglomeration-dominated as the particle size decreases. The conclusion is supported by the results of field emission scanning electron microscopy.     

On thermodynamic potentials in thermoelasticity under small strain and finite thermal perturbation assumptions

Expressions for thermodynamic potentials (internal energy, Helmholtz energy, Gibbs energy and enthalpy) of a thermoelastic material are developed under the assumption of small strains and finite changes in the thermal variable (temperature or entropy). The literature provides expressions for the Helmholtz energy in terms of strain and temperature, most often as expansions to the second order in strain and to a higher order in temperature changes, which ensures an affine stress–strain relation and a certain temperature dependence of the moduli of the material. Expressions are here developed for the four potentials in terms of all four possible pairs of independent variables. First, an expression is obtained for each potential as a quadratic function of its natural mechanical variable with coefficients depending on its natural thermal variable that are identified in terms of the moduli of the material. The form of the coefficients’ dependence on the thermal variable is not specified beforehand so as to obtain the most general expressions compatible with an affine stress–strain relation. Then, from each potential expressed in terms of its natural variables, expressions are derived for the other three potentials in terms of these same variables using the Gibbs–Helmholtz equations. The paper provides a thermodynamic framework for the constitutive modeling of thermoelastic materials undergoing small strains but finite changes in the thermal variables, the properties of which are liable to depend on the thermal variables.     

A pattern-based method for bounding the effective response of a nonlinear composite

This paper deals with the prediction of the effective properties of nonlinear composites. Rather than bounding the effective energy, this work aims at bounding directly the effective stress-strain response, by extending a method originally introduced by Milton and Serkov (J. Mech. Phys. Solids 48 (2000) 1295) and recently refined by Talbot and Willis (Proc. Roy. Soc. 460 (2004) 2705). In this paper, bounding the effective response is achieved by introducing a linear comparison composite with the same micro-geometry as the given nonlinear composite, as Ponte Castañeda (J. Mech. Phys. Solids 39 (1991) 45) did for the energy. It is found that any lower bound for the energy of the linear comparison composite generates a corresponding bound for the stress-strain response of the nonlinear composite. A selection of examples is presented to illustrate the method and compare the bounds obtained with existing results.