Ni_3Al基高温自润滑复合涂层的制备和摩擦学性能

采用高能球磨结合喷雾造粒制备喷涂喂料,利用等离子喷涂方法制备Ni_3Al基高温自润滑复合涂层,通过HT-1000销-盘式高温摩擦试验机测试大气气氛不同温度下涂层的摩擦磨损性能,并采用SEM、EDS和Raman等表征分析涂层微观组织、物相组成和摩擦磨损机理.结果表明:涂层在25℃至800℃具有良好的自润滑性能,摩擦系数为0.14～0.42,磨损率为2.41×10~(–4)～5.76×10~(–4) mm~3/(Nm). 25℃到400℃之间,随温度升高,Ni_3Al金属间化合物韧性和软金属银塑性变形能力均提高,形成了有效的转移润滑膜,从而提高了涂层摩擦学性能,涂层磨损形式主要为脆性断裂、磨粒磨损和黏着磨损;600℃时软金属Ag过度软化,BaF_2/CaF_2共晶脆-塑性转变不完全,磨损表面不能形成完整致密的润滑膜,摩擦系数和磨损率大幅升高,涂层的磨损形式主要为剥层磨损和磨粒磨损;800℃时磨损表面形成富含NiO、Ag_2MoO_4和NiCr_2O_4等高温润滑剂的连续光滑釉质层,摩擦系数和磨损率大幅降低,磨损形式主要为氧化磨损和黏着磨损.     

TA2合金激光熔覆钛基自润滑耐磨复合涂层的高温摩擦学性能

为提升TA2合金的摩擦学性能,选用Ti-TiC-WS_2复合粉末在TA2合金表面激光熔覆钛基高温自润滑耐磨复合涂层.系统地分析了涂层的物相、显微组织结构和显微硬度;分别在室温(20℃)、250℃和500℃下测试了基体和涂层的摩擦学性能,并分析了其磨损机理.结果表明:涂层的显微硬度(约HV_(0.5)1 005.4)是基体(HV_(0.5)190)的5倍;由于增强相TiC/(Ti,W)C_(1–x)和自润滑相Ti_2SC/TiS的综合效应,相比基体,复合涂层在所有试验温度下均具有较小的摩擦系数和磨损率;随着温度的升高,涂层的摩擦系数先变小后升高,在250℃下具有最低的摩擦系数(0.257);涂层的磨损率随温度的升高一直降低,在500℃下磨损率最低[0.487×10~(–5) mm~3/(Nm)].     

NiCr/Cr3C2-BaF2·CaF2高温自润滑耐磨涂层的制备与摩擦磨损特性

采用加压氢气还原和固相合金化技术,以BaF2·CaF2共晶、Cr3C2颗粒为核心,制备了NiCr合金包覆的NiCr/Cr3C2-BaF2·CaF2复合粉末,采用大气等离子喷涂技术制备相应涂层.采用扫描电子显微镜、X射线衍射和SRV摩擦磨损试验机等分析测试技术,研究了涂层组成、结构以及从室温到500 ℃涂层的摩擦磨损性能.研究结果表明:研制的NiCr/Cr3C2-BaF2·CaF2复合涂层是一种性能优良的高温自润滑耐磨涂层,表面包覆的致密NiCr层抑制了喷涂过程中颗粒的氧化、脱碳和烧蚀,涂层的显微硬度和结合强度较高;涂层在室温下的摩擦系数为0.74±0.02,随温度升高摩擦系数逐渐降低,500 ℃时降低为0.38±0.03,涂层和对偶球Si3N4的磨损率与室温相比显著下降.摩擦机理研究发现,高温下BaF2·CaF2共晶软化,导致涂层剪切强度比室温时明显变低,在摩擦表面形成了连续的BaF2·CaF2润滑膜.     

Ni3Al基自润滑复合材料摩擦学性能的研究

采用真空热压烧结方法制备了Ni3Al基自润滑复合材料,通过HT-1000型球盘式高温摩擦仪分别测试了不同条件下Ni3Al基自润滑复合材料的摩擦磨损性能.结果表明：复合材料在20～1 000℃均具有良好的自润滑性能,其摩擦系数在0.24～0.43之间.研究发现复合材料在低载（5 N、滑动速度为0.2 m/s）低温（20～400℃）下具有最低的摩擦系数（0.24～0.29）,但在低载高温下（600℃以上）摩擦系数较高（0.39～0.41）;而在高载（20 N）时在整个温度测试区间（20～1 000℃）拥有低而稳定的摩擦系数（0.28～0.31）.Ni3Al基自润滑材料优异的高温摩擦学性能归因于高温下材料摩擦表面形成的银、氟化物、氧化物以及钼酸盐等低剪切化合物的协同润滑作用.     

热处理NiAl-Bi2O3涂层的宽温域循环摩擦学行为及高低温润滑相再生机制

采用UMT-3高温摩擦试验机评价了氩气气氛800℃热处理等离子喷涂NiAl-Bi₂O₃涂层在室温至800℃的摩擦磨损性能.通过分析热处理前后涂层及其摩擦表/界面的组成和微结构演变,首次研究了热处理NiAl-Bi₂O₃涂层的高低温润滑相(NiBi、Bi₂O₃和NiO)自适应再生机制及宽温域循环摩擦学行为.结果表明：热处理能使涂层中产生弥散增强的Al₂O₃和具有中低温润滑性的金属间化合物NiBi,提高了涂层室温至800℃的减摩抗磨性能,尤其使涂层在400℃的摩擦系数和磨损率分别从0.39和35.56×10^-5 mm³/(N·m)降至0.28和8.53×10^-5 mm³/(N·m);在800℃时,接触表面通过摩擦氧化再次产生润滑相(Bi₂O₃、NiO),并与增强相Al₂     

镍基自润滑涂层的摩擦学性能

镍基自润滑复合粉末(NiCrMoAl-Ag-BaF_2/CaF_2)采用高能球磨结合喷雾造粒法制备,镍基自润滑涂层利用等离子喷涂技术制备.涂层摩擦磨损性能利用HT-1000型销-盘摩擦试验机在不同摩擦速度(0.2~1.0 m/s)及不同试验温度(25~800℃)条件下测试.涂层微观组织、物相组成及摩擦磨损机理利用SEM、EDS和Raman等表征分析.结果表明:在25℃到800℃,涂层的摩擦系数随着温度的增加呈先增加后降低的趋势,400℃时摩擦系数达到最高值0.37;800℃时摩擦系数降至最低值0.17.涂层摩擦系数随摩擦速度的增加呈现先降后增的趋势,0.8 m/s时摩擦系数最低,约在0.17~0.29范围内;1.0 m/s时摩擦系数升高至0.20~0.27范围内.涂层优异的自润滑性能得益于软金属Ag的低剪切性,以及600~800℃范围内BaF_2/CaF_2、Ag与钼酸盐、铬酸盐等高温产物的协同润滑效应.     

挡板尺寸对电弧离子镀TiAlN涂层微观结构和摩擦学性能的影响

利用电弧离子镀技术,采用Ti50Al50合金靶,在304不锈钢基体上沉积TiAlN涂层.在Ti50Al5合金靶和基体挂架中间设置直径分别为80、100和120 mm圆形挡板,并与无挡板沉积的TiAlN涂层对比,采用SEM/EDS、XRD研究挡板尺寸对涂层微观结构、成分的影响,通过显微硬度计、划痕仪和摩擦磨损试验研究挡板尺寸对TiAlN涂层力学性能及摩擦学性能的影响.结果表明：随着挡板尺寸增大,TiAlN涂层中Ti含量逐渐降低,Al含量逐渐升高,涂层表面熔滴数量显著减少,沉积速率降低.增大挡板尺寸后,涂层硬度下降,膜基结合力减小.添加挡板后TiAlN涂层表面凹坑缺陷增多,摩擦系数增大,与无挡板的TiAlN涂层相比,耐磨性显著提高.     

Ti6Al4V合金表面激光熔覆复合涂层的高温摩擦学性能研究

为了改善Ti6Al4V合金的摩擦学性能,采用预置NiCrBSiFe复合粉末激光熔覆制备高温耐磨复合涂层,分析了涂层的显微组织,测试了其显微硬度、室温(25℃)及高温(600℃)磨损性能,并分析了其机理.结果表明:复合涂层与钛合金基体为冶金结合,以γ-(Ni,Cr,Fe)固溶体为基体,原位生成的TiC、TiB_2和CrB增强相均匀分布于涂层中,涂层的平均硬度为HV0.5950,约为钛合金基体(HV0.5360)的3倍.室温下,由于涂层具有很高硬度,改善了钛合金表面严重的黏着磨损,涂层表现出优异的耐磨性;高温下,钛合金表面生成氧化膜表现出固体润滑效果,摩擦系数和磨损量均下降,而涂层中基体相硬度下降,磨损表面出现犁沟和破碎磨粒,摩擦系数和磨损率相比室温略有上升,但相比钛合金仍表现出较好的高温耐磨性.     

制备工艺对MoS_2粘结固体润滑涂层微动磨损寿命的影响

在不同载荷和位移振幅条件下,考察了2种基体材料表面MoS2粘结固体润滑涂层的微动磨损性能,深入分析了基体表面预处理、涂层厚度及涂层固化温度等对涂层微动磨损寿命的影响.结果表明,通过提高基体材料硬度、增加涂层厚度、对基体表面进行喷砂预处理以及对涂层进行高温固化等均可不同程度地提高涂层的微动磨损寿命,其中高温固化对涂层磨损寿命的影响最显著;而基体表面喷砂处理对高温固化涂层磨损寿命的影响减弱.喷砂42CrMo基体表面涂覆的经高温固化的厚16±1μm的MoS2粘结固体润滑涂层的抗微动磨损性能最佳.     

Ti6Al4V合金激光熔覆Ti3SiC2增强Ni60复合涂层组织与摩擦学性能

为了提高Ti6Al4V合金的耐磨减摩性能,在其表面利用激光熔覆技术制备出两种不同配比的Ti₃SiC₂/Ni60复合涂层,分别是5%Ti₃SiC₂+Ni60(N1)和10%Ti₃SiC₂+Ni60(N2)(均为质量分数),研究了这两种涂层在室温、300和600 ℃下的微观组织、显微硬度、摩擦学性能表现及相关磨损机理. 结果表明:涂层主要由硬质相TiC/TiB/Ti_xNi_y,γ-Ni固溶体连续相和润滑相Ti₃SiC₂组成. N1、N2涂层的显微硬度均为基体(350HV_0.5)的3倍左右,分别为1 101.90HV_0.5 和1 037.23HV_0.5 ,在室温、300和600 ℃下的摩擦系数分别为0.39、0.35、0.30和0.41、0.45、0.44,均小于基体的摩擦系数(0.51、0.49、0.47). N1、N2涂层在室温、300和600 ℃下的磨损率分别为3.07×10?5、1.47×10?5、0.77×10?5 mm3/(N·m)和1.45×10?5、0.96×10?5、0.62×10?5 mm3/(N·m),均远小于基体[35.96×10?5、25.99×10?5、15.18×10?5mm3/(N·m)]. 在本文中Ti₃SiC₂提高了Ti6Al4V合金的耐磨减摩性能,使得N1涂层表现出更好的减摩性能,N2涂层表现出更好的耐磨性能. 室温下,磨粒磨损、塑性变形以及轻微的黏着磨损为两种涂层的主要磨损机理;300 ℃时,塑性变形、氧化磨损和黏着磨损是N1涂层的对应机理,600 ℃时出现了三体磨粒磨损;在300和600 ℃时,黏着磨损、氧化磨损及磨粒磨损为N2涂层的主要磨损机理.      

Measurement of the concentration diffusion coefficient for Ne-Ar, Ne-Xe, Ne-H2, Xe-H2, H2-N2 and H2-O2 gas systems

The concentration diffusion coefficient, D ₁₂, is measured for the equimolar mixtures of Ne-Ar, Ne-Xe, Ne-H₂, Xe-H₂, H₂-N₂ and H₂-O₂ binary gas systems in a two-bulb metal apparatus in the temperature range 0 C to 100 C. These values are compared with the existing data on these systems and with the predictions of the kinetic theory in conjunction with the modified Buckingham exp-six potential. Unlike the thermal diffusion coefficient, with the simple theory it is possible to predict D ₁₂ within a few percent even for systems involving polyatomic gases. The smoothed experimental D ₁₂ values are also used to obtain data for the coefficients of viscosity and thermal conductivity at round temperatures and compositions for these systems.Nomenclature C ₂ ^t relative amount of a gas in the mixture in the bulb 2 at an instant t - C ₂ relative amount of the same gas in the mixture in the bulb 2 at equilibrium - D ₁₂ diffusion coefficient - X ₁ mole-fraction of the heavier component in the mixture - _mix viscosity coefficient - _mix thermal conductivity coefficient     

MoSi2-Mo5Si3-Mo5SiB2/SiC配对副的摩擦磨损性能

MoSi₂-Mo₅Si₃-Mo₅SiB₂复合材料是一种很有发展前景的高温耐磨材料,但MoSi₂-Mo₅Si₃-Mo₅SiB₂/SiC配对副的干滑动摩擦磨损性能尚不清楚. 本文中通过销-盘式干滑动摩擦磨损试验,考察了MoSi₂-Mo₅Si₃-Mo₅SiB₂/SiC配对副在不同温度(25~1 000 ℃)和载荷下(2.5~10 N)的摩擦学特性. 结果表明:试验温度和载荷对MoSi₂-Mo₅Si₃-Mo₅SiB₂/SiC配对副的摩擦系数影响较大,而对其磨损率影响较小. 载荷为5 N时,在25~1 000 ℃区间,摩擦系数和磨损率分别在0.11~0.43和0.513×10-7~0.544×10-7 mm3/(N·m)范围;在25~400 ℃时,磨损机制以轻微的氧化和黏着磨损为主,在600~1 000 ℃磨损机制主要表现为严重的氧化和黏着磨损. 在1 000 ℃时,随着载荷(2.5~10 N)的增加,摩擦系数和磨损率分别为0.29~0.38和0.540×10-7~0.547×10-7 mm3/(N·m);载荷为2.5~10 N时,始终存在黏着和氧化磨损;载荷为7.5~10 N时,材料磨损表面还伴随碾压塑性变形的特征.      

Structure cellulaire de la détonation des mélanges H2–NO2/N2O4Cellular structure of the detonation of gaseous mixtures H2–NO2/N2O4

Calculations of the detonation reaction zone of gaseous reactive mixtures of NO₂/N₂O₄ as oxidizer and H₂, CH₄ or C₂H₆ as fuel, in the range of equivalence ratio Φ between 0.5 and 2, show that, for Φ?1, the chemical energy is released in two distinct and successive exothermic steps with different chemical induction times. The first exothermic stage is mainly due to the reaction NO₂+H→NO+OH, NO being the main oxidizer of the second one.The experimental study conducted on the same range of equivalence ratio (0.5?Φ?2) shows that, for Φ?1, the detonation wave of these mixtures contains a double set of cellular structures. A similar result had already been obtained with the detonation of gaseous Nitromethane, the NO₂ group being here included in the molecule. Consequently, the oxidizer NO₂ being either initially separated from the fuel or included inside the molecule of a monopropellant (Nitromethane) is responsible, because of its specific chemical kinetics, of a chemical energy release in two main steps and of the existence of a double cellular structure in the detonation wave for the same range of equivalence ratio. These results reinforce the assumption that the cellular structure of the detonation finds its origin in the strong rates of chemical energy release inside the reaction zone. To cite this article: F. Joubert et al., C. R. Mecanique 331 (2003).     

Etude de la détonation de mélanges pauvres H2NO2/N2O4

Calculations of the detonation reaction zone of gaseous H₂NO₂/N₂O₄ mixtures in the range of equivalence ratio Φ between 0.25 and 0.7 show that for 0.25Φ0.4 the chemical energy is released in two distinct and successive exothermic steps characterised by different chemical characteristic times. As for rich mixtures, the first exothermic step is mainly due to the reaction NO₂ + H → NO + OH, but the second one is different since it results from the exothermic decomposition of NO into N₂ and O₂. For Φ=0.3 the measured detonation velocity in a tube of 52 mm internal diameter is very much smaller than the calculated value and the mean size of the cellular structure is very much larger than the value extrapolated from data obtained with mixtures of higher but close equivalence ratio. All these results show that the detonation, though self-sustained and steady, is ‘non-ideal’, i.e. it is supported only by a part of the available chemical energy, that provided mainly by the first exothermic step. To cite this article: D. Desbordes et al., C. R. Mecanique 332 (2004).     

Kinetics of ultrafine coating of SiO2 nanoparticles, suspended in non-thermal CH4/C2H6 plasma

Capacitively coupled RF discharges in methane and ethane (1000–3000 Pa, 5–15 W/cm³) were used for the in-flight coating of SiO₂ nanopowders (NP) with an a-C:H layer [A. Kouprine, F. Gitzhofer, M. Boulos, A. Fridman, Polymer-like C:H thin film coating of nanopowders in capacitively coupled RF discharge, Plasma Chemistry and Plasma Processing 24 (2) (2004) 189–215]. In this present work a model of the chemical kinetics of this plasma processing has been developed, based on the GRI-Mech 3.0 mechanism [G.P. Smith, D.M. Golden, M. Frenklach, Gas Research Institute, Detailed chemical reaction mechanism. Available from: ], and calculations are performed, using the Chemkin-II code. The model includes the formation of two solid phases: an amorphous C:H coating, deposited on the suspended NP, and soot, incepted in the gas phase. Non-equilibrium plasma effects are taken into account by the rates of radical species’ production, using the reference data on the “G-value”. The CH₃ and H species appear to have key roles in surface activation and the nanofilm growth. The results demonstrate the competitive character of the formation of the two solid phases: the C:H coating is dominant under T_gas < 1400–1600 K, depending on the conditions, and soot commencing to dominate at higher temperatures. This division corresponds to the passage from non-thermal plasma conditions, with the dominance of single-valent radicals and solid phase growth on the substrate only, to the plasma thermalisation with the formation of two-valent radicals and v. inception of the solid phase. The results are validated experimentally by the observation of soot formation as a function of the gas temperature, by the mass spectrograph data on the gas composition after plasma reforming, and by the reference data on coating growth rates and induction times for soot formation.     

等离子喷涂Al2O3/TiO2纳米复合涂层的制备、结构及摩擦学性能

采用喷雾干燥法对溶胶-凝胶法合成的系列A l2O3/TiO2纳米复合粉体进行造粒,使用等离子喷涂技术制备系列A l2O3/TiO2纳米复合涂层.对涂层结构和形貌分析表明所制备的A l2O3/TiO2纳米复合涂层形成了具有熔融区和半熔融区的双区形态的纳米复合结构.使用UMT-2MT试验机研究了复合涂层的摩擦磨损性能,结果表明复合涂层的磨损率随TiO2含量的增加表现出先降低而后增大的趋势,TiO2质量百分数为10%的纳米复合涂层的磨损率最低;而涂层的摩擦系数随TiO2含量的增加变化不大.复合涂层的磨损机制为裂纹扩展导致的磨损剥落.     

Mo/Al2O3复合材料的耐磨性

无压烧结制备了不同组分的Mo/Al2O3复合材料样品,对样品的磨损行为和磨损机理进行了研究,并用电子探针分析了其磨损形貌.结果表明:Mo/Al2O3复合材料的磨损率随Mo含量的增加呈上升趋势,在30vol.%Mo时出现峰值;摩擦系数随着Mo含量的增加而增大,20vol.%Mo样品的摩擦系数较小;Mo含量不超过60%时,当出现Mo的连续相或者Al2O3的连续相时复合材料表现出较好的耐磨性;Mo含量较低时磨损机理表现为脆性脱落,而Mo含量较高时材料的磨损机理主要为磨粒磨损.     

Ar稀释C2H2+2.5O2预混气高频爆轰的端面结构

为了研究预混气爆轰的内部结构,对不同浓度的Ar稀释的C₂H₂+2.5O₂预混气进行爆轰实验和数值计算。首先,在内径63.5 mm的管道内进行爆轰实验,使用烟熏玻璃记录了不同初始压力下C₂H₂+2.5O₂预混气的爆轰端面结构。使用数字化图像处理技术来分析烟熏玻璃记录的三波点轨迹,以减少人为误差。然后,观察实验结果并描绘规则图形,图像识别程序经过验证后,用于分析实验结果。从端面结构中对封闭图形进行圆的拟合,用胞格半径方差来表示胞格大小的均匀程度;用相邻胞格圆心距的方差来表示胞格分布的规则程度。通过对比不同Ar稀释下半径方差和圆心距方差随胞格数量的变化,给出不同浓度Ar稀释下C₂H₂+2.5O₂预混气的端面胞格尺寸及分布规律,随着Ar浓度的升高,预混气端面胞格分布更加规律。     

KH2PO4/SiO2复合粉体抑制铝粉爆燃效果及机理分析

为研究KH₂PO₄/SiO₂复合粉体抑爆剂对铝粉爆燃的抑制作用,采用球磨机将KH₂PO₄和SiO₂混合研磨制备出新型的KH₂PO₄/SiO₂复合粉体抑爆剂。在哈特曼管实验装置上,开展爆燃火焰传播抑制实验,结果表明:随着KH₂PO₄/SiO₂复合粉体抑爆剂含量的增加,爆燃火焰传播长度和速度逐渐减小,当添加质量比10∶6的KH₂PO₄/SiO₂复合粉体抑爆剂时,可实现铝粉爆燃火焰传播的抑制。在20 L球形爆炸装置上,开展复合粉体抑爆剂抑制铝粉爆炸压力测试实验,结果表明:随着KH₂PO₄/SiO₂复合粉体抑爆剂含量的增加,铝粉爆炸最大爆炸压力p_max和最大爆炸压力上升速率(dp/dt)_max逐渐减小,当添加质量比10∶9的KH₂PO₄/SiO₂复合粉体抑爆剂时,可实现铝粉爆燃的完全抑制。通过KH₂PO₄粉体、SiO₂粉体与复合粉体抑爆剂对比可知,复合粉体抑爆剂对铝粉火焰传播和爆炸压力的抑制效果都优于单体粉体抑爆剂。通过对铝粉在空气中燃烧的热分析研究,从化学和物理两个方面分析了KH₂PO₄/SiO₂复合粉体抑爆剂对铝粉爆燃的抑制机理。