Cu/Mo_5Si_(3p)复合材料的摩擦磨损性能研究

采用销—盘式摩擦磨损试验机研究了液相烧结制备Mo5Si3颗粒弥散强化铜合金在滑动干摩擦条件下的摩擦磨损行为。结果表明:Cu/Mo5Si3p复合材料具有优良的摩擦磨损性能。随着Mo5Si3含量的增加Cu/Mo5Si3p复合材料的硬度增加,摩擦系数和磨损失重量降低。Mo5Si3含量低时,Cu/Mo5Si3p复合材料的磨损机制为犁沟变形和粘着磨损为主,而Mo5Si3含量高时则为犁沟变形磨损为主。     

热压法制备Mo_5Si_3-Al_2O_3复合材料及力学性能研究

以MoO_3粉、Mo粉、Si粉和Al粉为原料,采用机械合金化结合热压烧结法制备了Mo5Si3-Al_2O_3复合材料,研究了Al_2O_3含量对Mo5Si3-Al_2O_3复合材料微观结构和力学性能的影响。结果表明:复合材料的主要物相组成为Mo5Si3、Al_2O_3和Mo3Si,其平均晶粒尺寸在51~99 nm之间,具有纳米晶结构。Al_2O_3的引入细化了晶粒,提高了复合材料的致密度和力学性能。Mo5Si3-30%Al_2O_3复合材料的致密度、硬度、抗弯强度和断裂韧性分别为99.6%、13.2 GPa、322 MPa和6.43 MPa·m1/2。     

Mo_5Si_3-Al_2O_3复合材料的制备及抗氧化性能研究

采用机械化学还原法结合热压烧结制备了Mo_5Si_3-Al_2O_3复合材料,并对复合材料在600℃下的氧化行为进行了研究。结果表明:以MoO_3粉、Mo粉、Si粉和Al粉为原料,机械球磨10h,可获得具有纳米晶结构的Mo_5Si_3-Al_2O_3复合粉体;相比纯Mo5Si3试样,Mo_5Si_3-Al_2O_3复合材料的烧结相对密度和硬度提高,分别达97.2%和1350HV;Al_2O_3的引入可有效防止Mo_5Si_3的低温"粉化"现象,使Mo_5Si_3-Al_2O_3复合材料的抗氧化性明显提高,其氧化动力学曲线呈近似抛物线规律。     

球磨参数对机械合金化制备Al_2O_3/Mo_5Si_3复合粉体特性的影响

以MoO3粉、Mo粉、Si粉及Al粉为原料,采用机械化学还原法制备了Al2O3/Mo5Si3复合粉体。利用XRD、SEM等对复合粉体在球磨过程中的物相转变和形貌进行表征,并对球磨参数对机械合金化过程的影响进行探讨。结果表明,原料粉体球磨10 h后转变为Al2O3/Mo5Si3复合粉体,反应较完全。随球磨时间延长,复合粉体细小均化,粉体粒度较小,球磨20h后粉体粒度在3~5μm之间,随球磨转速的提高,球磨时间延长,球磨提供能量提高,反应开始时间变短。     

La_2O_3增强增韧(Mo_(0.7),W_(0.3))Si_2复合材料的作用机理

通过多组元自蔓延反应及热压烧结方法制备了(Mo0.7,W0.3)Si2材料及掺杂1.5.%(质量分数)La2O3的(Mo0.7,W0.3)Si2复合材料。采用X射线衍射(XRD)、扫描电镜(SEM)、电子探针(EPMA)、透射电镜(TEM)及物理机械性能测试方法对复合材料组织性能进行了表征,并深入探讨了其强韧化机理。结果表明:La2O3掺杂的(Mo0.7,W0.3)Si2复合材料由(Mo,W)Si2、(Mo,W)5Si3、硅酸镧构成。掺杂La2O3后,La2O3与脆性相Si O2形成硅酸镧化合物,与未掺杂La2O3的(Mo0.7,W0.3)Si2相比,复合材料的晶粒明显细化,强度和韧性均明显提高,其强化原因有细晶强化及颗粒弥散强化;韧化原因有晶粒细化、Si O2的减少、位错缠结、颗粒的拔出、裂纹偏转及微裂纹产生。     

热解炭微观结构对C/C复合材料摩擦磨损性能的影响

研究了热解发光学特性分别为粗糙层结构和光滑层结构试样的摩擦磨损性能。粗糙层结构试样由于具有较高的导热系数,其传热和散热能力比光滑层结构试样的强。在300～800℃时,粗糙层结构试样的膨胀系数基本保持稳定,而光滑层结构试样的膨胀系数随温度升高递增,使刹车过程中前者摩擦因数稳定,后者摩擦性能差。利用场发射高分辨电子显微镜研究了粗糙层结构和光滑层结构试样的微观结构。结果表明;前者生长择优取向明显,生长表面光滑,在摩擦过程中形成片状的石墨结构磨屑,保持稳定的摩擦性能;后者则为低织构疏松层状结构,生长表面粗糙。在磨擦过程中形成颗粒状或大团状结构,导致摩擦性能不稳定。热解炭微观结构的差异是导致2种结构试样热性能、摩擦磨损性能差异的根本原因。     

MoSi2—Mo5Si3复合材料的烧结工艺

系统研究了ＭｏＳｉ２－ｍＯ５Ｓｉ３复合材料的烧结工艺。结果表明,ＭｏＳｉ２－Ｍｏ５Ｓｉ３复合材料理想的烧结温度为１４００～１５００℃,保温时间为１．０～１．５ｈ,当Ｍｏ５Ｓｉ３含量为１６％时,ＭｏＳｉ２－Ｍｏ５Ｓｉ３复合材料具有最大的相对密度和硬度。     

MoS_2对铝基材料摩擦磨损性能的影响

以Al,Fe,Zn等金属粉末和Si粉为原料,采用热压法制备MoS_2含量(质量分数)分别为0和3%的铝基复合材料,在滑动速度为0.377~1.131 m/s以及载荷为4~10 N的条件下进行摩擦试验,研究MoS_2对铝基复合材料摩擦磨损性能的影响。结果表明:在0.377 m/s的滑动速度下,3%MoS_2/铝基复合材料在10 N载荷下具有较低的平均摩擦因数0.4,比不含MoS_2材料的摩擦因数降低近一半;在0.755 m/s的滑动速度下,2种材料的摩擦因数和磨损率接近;在1.131 m/s的滑动速度下,载荷7~10 N时2种材料都严重磨损,3%MoS_2/铝基材料具有相对较低的磨损率,磨损机理为熔化磨损,未添加MoS_2材料的磨损机理为严重塑性变形磨损。添加3%MoS_2可显著改善铝基材料的摩擦磨损性能。     

Al2O3短纤维增强Al-Cu合金的微观组织结构和机械性能研究

为了研究铜元素含量变化对复合材料界面反应、微观组织结构和机械性能的影响，利用挤压铸造法制备了体积分数均为40％的Al2O3纤维增强纯铝和Al—Cu合金（1％，3％和5％）复合材料。采用X射线、TEM、SEM和拉伸实验手段，观察和测试了4种复合材料的微观组织和机械性能。结果表明，Al2O3纤维表面含有非晶SiO2成分，在高应力下易于开裂。铜元素的加入对材料的析出产生和机械性能有重要影响。铜元素引入后在复合材料中纤维表面处偏聚和富集，促进了界面θ相析出，并随基体中Cu含量提高而增加。当铜含量增加到5％后，基体内部也出现明显的析出相。拉伸实验结果表明随着Cu含量的增加复合材料的抗拉强度增高，Al2O3f/Al-Cu与Al2O3f／纯Al相比，抗拉强度分别增加了102％，146％和171％。SEM断口观察表明：基体合金的断口基本上都呈宏观脆性断口，具有低的展延性和撕裂纹理；大量的纤维从复合材料基体中拔出，一些纤维被拉断，这些特点与界面结合物和多晶的Al2O3纤维结构密切相关。     

载荷和速率对(W,Mo)C/Al2O3/La2O3材料高温摩擦磨损性能的影响

采用热分解法和还原法制备了(W,Mo)C/Al₂O₃/La₂O₃粉末,利用等离子烧结技术在1600℃烧结制备了(W,Mo)C/Al₂O₃/La₂O₃复合陶瓷材料,并测试其力学性能。以Si3N4为对磨件在HT-1000试验机上进行高温摩擦磨损实验,研究材料在600℃时摩擦速率和载荷对摩擦系数以及磨损率的影响,并利用扫描电镜(SEM)和能谱仪(EDS)分析微观形貌,探究其磨损机制。实验结果表明,在600℃,7.5 N条件下,随着摩擦速率的增加摩擦系数和磨损率都在减小。当摩擦速率为33.6 m·min^-1时具有最低的摩擦系数和磨损率,分别为0.4和4.21×10^-6mm³·Nm^-1。在600℃,16.8 m·min^-1条件下,随着载荷的增大,摩擦系数和磨损率逐渐增加。在600℃,5.0 N,16.8 m·min...     

Characterization and tribological behavior of cast In-Situ Al (Mg,Mo)-Al2O3 (MoO3) composite

Aluminum alloy—based cast in-situ composite has been synthesized by dispersion of externally added molybdenum trioxide particles (MoO₃) in molten aluminum at the processing temperature of 850 °C. During processing, the displacement reaction between molten aluminum and MoO₃ particles results in formation of alumina particles in situ and also releases molybdenum into molten aluminum. A part of this molybdenum forms solid solution with aluminum and the remaining part reacts with aluminum to form intermetallic phase Mo(Al_1−x Fe _x )₁₂ of different morphologies. Magnesium (Mg) is added to the melt in order to help wetting of alumina particles generated in situ, by oxidation of molten aluminum by molybdenum trioxide, and helps to retain these particles inside the melt. The mechanical properties of the cast in-situ composite, as indicated by ultimate tensile stress, yield stress, percentage elongation, and hardness, are relatively higher than those observed either in cast commercial aluminum or in cast Al-Mo alloy. The wear and friction of the resulting cast in-situ Al(Mg,Mo)-Al₂O₃(MoO₃) composites have been investigated using a pin-on-disc wear testing machine under dry sliding conditions at different normal loads of 9.8N, 14.7N, 19.6N, 24.5N, 29.4N, 34.3N, and 39.2 N and a constant sliding speed of 1.05 m/s. The results of the current investigation indicate that the cumulative volume loss and wear rate of cast in-situ composites are significantly lower than those observed either in cast commercial aluminum or in cast Al-Mo alloy, under similar load and sliding conditions. Beyond about 30 to 35 N loads, there appears to be a higher rate of increase in the wear rate in the cast in-situ composite as well as in cast commercial aluminum and cast Al-Mo alloy. For a given normal load, the coefficient of friction of cast in-situ composite is significantly lower than those observed either in cast commercial aluminum or in cast Al-Mo alloy. The coefficient of friction of cast in-situ composite increases gradually with increasing normal load while those observed in cast commercial aluminum or in cast Al-Mo alloy remain more or less the same. Beyond a critical normal load of about 30 to 35 N, the coefficient of friction decreases with increasing normal load in all the three materials.     

Microstructure and properties of Al2O3-Al(Si) and Al2O3-Al(Si)-Si composites formed byin situ reaction of Al with aluminosilicate ceramics

Al₂O₃-Al(Si) and Al₂O₃-Al(Si)-Si composites have been formed byin situ reaction of molten Al with aluminosilicate ceramics. This reactive metal penetration (RMP) process is driven by a strongly negative Gibbs energy for reaction. In the Al/mullite system, Al reduces mullite to produce α-Al₂O₃ and elemental Si. With excess Al (i.e., x > 0), a composite of α-Al₂O₃, Al(Si) alloy, and Si can be formed. Ceramic-metal composites containing up to 30 vol pct Al(Si) were prepared by reacting molten Al with dense, aluminosilicate ceramic preforms or by reactively hot pressing Al and mullite powder mixtures. Both reactive metal-forming techniques produce ceramic composite bodies consisting of a fine-grained alumina skeleton with an interpenetrating Al(Si) metal phase. The rigid alumina ceramic skeletal structure dominates composite physical properties such as the Young’s modulus, hardness, and the coefficient of thermal expansion, while the interpenetrating ductile Al(Si) metal phase contributes to composite fracture toughness. Microstructural analysis of composite fracture surfaces shows evidence of ductile metal failure of Al(Si) ligaments. Al₂O₃-Al(Si) and Al₂O₃-Al(Si)-Si composites produced byin situ reaction of aluminum with mullite have improved mechanical properties and increased stiffness relative to dense mullite, and composite fracture toughness increases with increasing Al(Si) content. This article is based on a presentation made in the “In Situ Reactions for Synthesis of Composites, Ceramics, and Intermetallics” symposium, held February 12–16, 1995, at the TMS Annual Meeting in Las Vegas, Nevada, under the auspices of SMD and ASM-MSD (the ASM/TMS Composites and TMS Powder Materials Committees).     

机械合金化制备Al2O3/Mo5Si3粉末研究

以MoO3粉、Mo粉、Si粉和Al粉为原料,利用机械合金化制备了具有纳米晶组成的Al2O3/Mo5Si3复合粉体,利用X射线衍射(XRD)、激光粒度分析仪(LPS)和扫描电子显微镜(SEM)对Al2O3/Mo5Si3复合粉体的形成以及在球磨过程中的粉体演变进行分析和表征.结果表明:球磨10h后,原料粉末发生反应生成了A...     

等离子喷涂Al_2O_3-TiO_2陶瓷涂层的显微组织及摩擦学性能

以Al_2O_3-TiO_2(x=0%,3%,13%,20%,40%,质量分数)复合陶瓷粉末为原料,采用等离子喷涂工艺在316L不锈钢基体表面制备5种陶瓷涂层。利用扫描电镜(SEM)、能谱仪(EDS)和X线衍射仪(XRD)、荧光金相显微镜分析粉末和涂层形貌、微观结构、物相组成及涂层孔隙率;利用显微硬度计及摩擦磨损试验机测试涂层力学及摩擦学性能,观察试样磨损形貌,分析磨损机理。结果表明:涂层呈典型的等离子喷涂层状堆积特征,涂层与基体结合良好。随TiO_2含量增加,涂层主相由γ-Al_2O_3向Al_2TiO_5相过渡,涂层韧性升高,硬度和孔隙率降低。在大气环境下,低TiO_2含量的涂层(Al_2O_3、AT3)发生应力疲劳磨损,高TiO_2含量的涂层(AT13、AT20和AT40)发生应变疲劳磨损;而在水环境下,5种涂层均发生应力疲劳磨损。     

Preparation and tribological performance of electrodeposited Ni-TiB2-Dy2O3 composite coatings

TiB2 and Dy2O3 were used as codeposited particles in the preparation of Ni-TiB2-Dy2O3 composite coatings to improve its per-formance. Ni-TiB2-Dy2O3 composite coatings were prepared by electrodeposition method with a nickel cetyltrimethylanunonium bromide and hexadecylpyridinium bromide solution containing TiB2 and Dy2O3 particles. The content of codeposited TiB2 and Dy2O3 in the compos-ite coatings was controlled by adding TiB2 and Dy2O3 particles of different concentrations into the solution, respectively. The effects of TiB2 and Dy2O3 content on microhardness, wear mass loss and friction coefficients of composite coatings were investigated. The composite coat-ings were characterized by X-ray diffraction (XRD), inductively coupled plasma-atomic emission spectrometer (ICP-AES) and scanning electron microscopy (SEM) techniques. Ni-TiB2-Dy2O3 composite coatings showed higher microhardness, lower wear mass loss and friction coefficient compared with those of the pure Ni coating and Ni-TiB2 composite coatings. The wear mass loss of Ni-TiB2-Dy2O3 composite coatings was 9 and 1.57 times lower than that of the pure Ni coating and Ni-TiB2 composite coatings, respectively. The friction coefficient of pure Ni coating, Ni-TiB2 and Ni-TiB2-Dy2O3 composite coatings were 0.723, 0.815 and 0.619, respectively. Ni-TiB2-Dy2O3 composite coat-ings displayed the least friction coefficient among the three coatings. DY2O3 particles in composite coatings might serve as a solid lubricant between contact surfaces to decrease the friction coefficient and abate the wear of the composite coatings. The loading-bearing capacity and the wear-reducing effect of the Dy2O3 particles were closely related to the content of Dy2O3 particles in the composite coatings.     

Activities in CaO-SiO2-Al2O3 slags and deoxidation equilibria of Si and Al

By using the data in previous and present slag-metal equilibrium experiments, the activities of SiO₂ along the liquidus lines in CaO-SiO₂-Al₂O₃ slags were determined at 1823 and 1873 K from the reaction Si+2O=SiO₂ (s), in which the oxygen activities were estimated from the measured oxygen contents or from the combination of nitrogen distribution ratios (L _N) and nitride capacities (C _N). The activities of Al₂O₃ were also determined from the reaction 2Al+3O=Al₂O₃ (s), in which the oxygen activities were estimated from the values for L _N and C _N, or from the reaction 3SiO₂ (s)+4Al=2Al₂O₃ (s)+3Si, in which the activities of SiO₂ and the contents of Al and Si along with the respective interaction coefficients were used. The activities of Al₂O₃ and CaO in the entire liquid region were estimated from the Rein and Chipman’s activities of SiO₂ by using the method of Schuhmann. On the basis of these activities, the deoxidation equilibria of Si and Al in steels were discussed.     

Computer study of structure, thermodynamic, and electrical transport properties of Na3AlF6-Al2O3 and CaF2-Al2O3 melts

Structure, thermodynamic, and electrical transport properties of Na₃AlF₆-Al₂O₃ and CaF₂-Al₂O₃ melts were examined by molecular dynamics. Ionic models were constructed for Na₃AlF₆-Al₂O₃ and CaF₂-Al₂O₃ melts at 1283 and 2000 K, respectively. It was found that in the Na₃AlF₆-Al₂O₃ melts, stable aluminum-fluorine-oxygen groups are formed. Although bonds between F⁻ and Al³⁺ ions in the first coordination shell are weaker than between O²⁻ and Al³⁺ ions, very stable negatively charged AlF ₆ ³⁻ groups are formed at low oxygen concentrations in the Na₃AlF₆-Al₂O₃. This results in migration of aluminum to the anode in an external electric field. In the CaF₂-Al₂O₃ melts, positively charged aluminum-oxygen groups dominate. This results in migration of aluminum to the cathode at almost all Al₂O₃ concentrations. Therefore, in Na₃AlF₆-Al₂O₃ melts, the Al³⁺ ion as a component of the complex anion has a negative partial conductivity and the O²⁻ ion has positive partial conductivity; in CaF₂-Al₂O₃ melts, Al³⁺ has a positive transport number while O²⁻ has a negative transport number.