纳米/超细Ti(CN)基金属陶瓷的研究进展

概述了纳米/超细Ti(CN)基金属陶瓷的研究进展,重点对纳米Ti(CN)粉末的制备方法、纳米/超细Ti(CN)基金属陶瓷烧结过程中相组织的变化以及烧结工艺进行了介绍.指出成功制备纳米/超细Ti(CN)基金属陶瓷的关键在于控制烧结过程中Ti(CN)晶粒及环形相的长大,探索新的快速烧结方法.     

纳米Ti(C,N)增强Ti(C,N)基金属陶瓷的制备研究

采用Ti(C,N)纳米粉末制备Ti(C,N)基金属陶瓷.研究了烧结温度、保温时间和升温速度等工艺参数对含10wt％纳米粉末的Ti(C,N)基金属陶瓷性能的影响,得到优化烧结工艺为1450℃,保温75min,升温速度3℃/min.用优化工艺制备的Ti(C,N)基金属陶瓷抗弯强度提高了约36.7％,增强机理主要表现为细晶强化、弥散强化和固溶强化.     

碳纳米管增韧超细Ti(C|N)基金属陶瓷

Ti(C,N)基金属陶瓷的低韧性限制了其广泛应用于切削刀具领域。为探究碳纳米管对超细Ti(C,N)基金属陶瓷断裂韧性的影响,采用化学镀工艺在碳纳米管表面镀Ni,采用粉末冶金法真空烧结制备了不同碳纳米管含量的超细Ti(C,N)基金属陶瓷。研究了不同含量镀镍和未镀镍的碳纳米管对Ti(C,N)金属陶瓷组织和断裂韧性的影响。扫描电镜照片表明 , 添加CNTs后,组织中出现无芯晶粒及微孔洞。压痕法测试断裂韧性的结果表明,纳米管的加入使超细Ti(C,N)金属陶瓷的断裂韧性提高 29. 4 %～62. 7 % , 碳纳米管增韧机制为裂纹偏转和桥接增韧、无芯晶粒增韧及微孔洞增韧。此外,随着碳纳米管含量的增加,超细CNTs/Ti(C,N)金属陶瓷复合材料的相对密度和硬度均有轻微下降。添加镀镍和未镀镍碳纳米管对超细Ti(C,N)金属陶瓷都具有很好的增韧作用。     

Ti(C,N)基金属陶瓷的组织结构与合金化

Ti(C,N)基金属陶瓷的高温红硬性、耐磨性和抗氧化性好,与金属材料间的摩擦系数低,是制作工模具和耐磨零部件的理想材料.简要介绍了合金化成分对Ti(C,N)基金属陶瓷组织结构和力学性能的影响以及多元(Ti,M)(C,N)固溶体粉末制备和金属陶瓷烧结技术的研究现状.     

Ti(C,N)基金属陶瓷烧结过程的冶金基础及其显微组织特征Ⅱ芯-环结构的形成机理及烧结过程中的脱气演化

综述了Ti(C,N)基金属陶瓷烧结过程中的冶金反应规律.介绍和分析了Ti(C,N)基金属陶瓷典型芯-环结构组织的形成过程和机理,以及烧结过程的脱气现象和规律.     

金属陶瓷刀具切削不锈钢的磨损机理研究

利用真空烧结工艺制备了纳米复合Ti(C,N)基金属陶瓷刀片.进行了奥氏体不锈钢的单因素切削试验,并利用SEM、EPMA对金属陶瓷刀具的磨损失效机理进行了详细的研究.结果表明:纳米复合Ti(C,N)基金属陶瓷刀片在切削奥氏体不锈钢时表现出较高的耐磨性,其主要的磨损失效机理为粘结磨损,同时伴随一定的氧化磨损和扩散磨损.     

搅拌球磨制备亚微米晶粒Ti(C,N)基金属陶瓷

用搅拌球磨方法制备了亚微米TiC-TiN-WC-Mo-Ni-C金属陶瓷复合粉，并烧结成亚微米晶粒Ti(C,N）基金属陶瓷；研究了原始粉末粒度，磨球大小，球磨时间对复合粉粒度的影响，研究了球磨过程中氧和铁元素对粉末的污染情况；并对烧结合金的组织，性能进行了分析，表明亚微米晶粒Ti(C,N）金属陶瓷的性能优良。     

SD成型剂对Ti(C,N)基金属陶瓷显微结构和力学性能的影响

采用低压烧结的方法制备Ti(C,N)基金属陶瓷材料,并结合C、N、O分析,XRD、BSE、EDS等测试手段研究了SD成型剂对Ti(C,N)基金属陶瓷合金的C含量、相组成及显微结构和力学性能的影响。结果表明,随着SD成型剂添加量的增加,脱胶后压坯的C含量逐渐增加,N含量逐渐减小;烧结后Ti(C,N)基金属陶瓷由(Ti,Me)(C,N)(Me=W、Mo、Ta)和Ni/Co固溶体相组成;显微组织以黑芯-白环结构为主,并伴随着少量白芯-灰环的结构。SD添加量为100mL/kg时,Ti(C,N)基金属陶瓷材料的抗弯强度达1929MPa,硬度为1588HV30,添加量为180mL/kg时,合金组织中石墨相的出现使其抗弯强度大幅度下降。     

金属陶瓷与金属焊接技术的研究现状与展望

Ti(C,N)基金属陶瓷与金属的焊接是Ti(C,N)基金属陶瓷材料得以发展和应用的关键技术之一.介绍了Ti(C,N)基金属陶瓷材料的特点和应用现状,概述了金属陶瓷与金属焊接的技术方法及其研究进展,展望了金属陶瓷与金属焊接技术的应用前景.     

Ti(C,N)基金属陶瓷注射成形脱脂技术研究

使用传统蜡基粘结剂和改进型蜡基粘结剂分别研究了Ti(C,N)基金属陶瓷粉末注射成形,热脱脂和溶剂脱脂 热脱脂工艺过程,其中包括根据粘结剂TGA制定并优化热脱脂的工艺曲线、不同的溶剂和温度对溶剂脱脂的影响、后续热脱脂工艺路线的确定.结果表明:使用改进型蜡基粘结剂的2#试样热脱脂工艺简单、周期短并易于控制;2#溶剂脱脂率明显高于使用传统蜡基粘结剂的1#试样;经过溶剂脱脂 热脱脂,1#试样脱脂率达到93%,2#试样脱脂率达到96%以上;1#烧结试样的抗弯强度为700 MPa左右,2#则达到1300 MPa,从烧结样品抗弯断口和显微组织的SEM图片得到了验证.Ti(C,N)基金属陶瓷注射成形采用改进型蜡基粘结剂比传统蜡基粘结剂脱脂效果好、力学性能高,改进型蜡基粘结剂更适合Ti(C,N)基金属陶瓷注射成形.     

Effect of Ni powder characteristics on the consolidation of ultrafine TiMoCN cermets by means of SPS and HIP technologies

Fully dense titanium carbonitride cermets have been consolidated from Ti(C,N)–Ni–Mo₂C–TiAl₃ powder mixtures either by spark plasma sintering or hot isostatic pressing techniques. Carbonyl Ni powders enhance the densification of the cermets produced by SPS (spark plasma sintering), a phenomenon likely related to a more efficient dissolution of Mo₂C additions and the possible precipitation of α″ phase. Both SPS and HIP (hot isostatic pressing) processes lead to materials with a bimodal Ti(C,N) grain size distribution containing a considerable fraction of nanometric grains. Unlike SPS, HIP induces significant graphite precipitation which could be explained by the destabilization of the carbonitride phase under high isostatic pressures at high temperature. Optimized compositions processed by SPS exhibit a combination of hardness and toughness close to the range covered by ultrafine WC–Co hardmetals of similar binder contents.     

Denitrification of Ti(C,N) based cermet during powder mixing process

Changes in the nitrogen content of Ti(C,N)-based cermets during powder mixing and sintering processes were investigated and the denitrification mechanism was re-evaluated. The denitrification of N-containing cermets occurrs mainly during the powder mixing process, and is relatively small during sintering periods. Denitrification during powder mixing is caused by oxidation of the Ti(C,N) powders in contrast to denitrification during sintering, which is caused by the decomposition of the nitrides due to the high nitrogen partial pressure. It was concluded that the main source of oxygen for the powder oxidation was the water present in the ethanol solvent.     

功能梯度Ti(C, N)基金属陶瓷制备技术

通过真空液相烧结制备出Ti(C,N)基金属陶瓷基体,并对基体表面进行双辉等离子渗碳处理。运用扫描电子显微镜(SEM) 、电子探针(EPMA)、X射线衍射(XRD)等分析手段对渗碳前后材料的显微组织形貌、成分分布以及物相组成进行分析。结果表明,双辉等离子渗碳后金属陶瓷表面富Ti、Mo、W、C、N元素,贫Ni。渗碳过程中表层高的碳活度驱使内部的Ti、Mo、W元素向外迁移,从而迫使Ni向内迁移。渗碳后,材料表层富硬质相,近表层富粘结相。渗碳处理使试样表层硬度得到提高,对横向断裂强度影响不大。     

纳米Si/C/N复相粉体的制备及其在不同基体中的微波介电特性

以六甲基二硅胺烷（（Ｍｅ_３Ｓｉ）_２ＮＨ）（Ｍｅ：ＣＨ_３）为原料,用双反应室激光气相合成纳米粉体装置制备了纳米Ｓｉ／Ｃ／Ｎ复相粉体．研究了纳米Ｓｉ／Ｃ／Ｎ复相粉体在不同基体中８．２～１２．４ＧＨｚ的微波介电特性,纳米粉体介电常数的实部（ε’）和虚部（ε”）随频率增大而减小,介电损耗（ｔｇδ＝ε”／ε’）较高·纳米Ｓｉ／Ｃ／Ｎ复相粉体中的ＳｉＣ微晶固溶了大量的Ｎ原子,在纳米Ｓｉ／Ｃ／Ｎ复相粉体中形成大量的带电缺陷;极化弛豫是吸收电磁波的主要原因．     

Sintering of ultrafine SiC powders prepared by plasma CVD

Ultrafine SiC powders with a nanometre particle size were synthesized by r.f. plasma chemical vapour deposition (CVD) using a chemical system of SiH₄−C₂H₄−Ar. The powder was also ultrapure with a grade of 99.999% purity. The product was polytype 3C−SiC and black in colour, in spite of its high purity, because of its ultrafine size. Silicon carbide is a difficult ceramic to sinter; it is possible to sinter it to full density with the aid of sintering additives. Ultrafine and ultrapure SiC powders were hot-pressed without sintering additives in the present study, in order to investigate the sintering behaviour. The CVD powders proved sinterable to 88% theoretical density without sintering additives. The present experiments revealed that powder treatment before firing was a key technology when using ultrafine powders as starting materials in the sintering process. The sintering behaviour of the powder was characterized by a large shrinkage. Phase transformation was negligible after hot pressing at 2200°C for 30 min.     

Ti(C,N)基金属陶瓷烧结过程的冶金基础及其显微组织特征Ⅰ烧结过程的冶金基础

综述了Ti(C,N)基金属陶瓷烧结过程中的冶金基础.涉及烧结冶金过程中的几个重要的基础问题:Ti(C,N)的稳定性,粘结相同硬质相的润湿性,碳、氮化合物在粘结上中的溶解度及其选择溶解性.     

Ti(C,N)基金属陶瓷的研究进展

介绍了Ti(C,N)基金属陶瓷的晶体结构和高温力学性能,综述了其主要制备方法和研究进展,详细地分析了其冶金机理和相结构特点,并讨论了环型相的形成机理及缺点,最后指出了Ti(C,N)基金属陶瓷研究方向和提高其性能的基本途径,并认为系统考虑其相平衡、粉末冶金机制和加工工艺是制备性能优良的Ti(C,N)基金属陶瓷刀具和涂层的关键.     

On the disappearance of Mo2C during low-temperature sintering of Ti(C,N)-Mo2C-Ni cermets

In order to seek a better understanding of the mechanisms leading to the disappearance of Mo₂C during the sintering of Ti(C,N)-based cermets at or below 1200 °C, the sintering reactions occurring in ternary phase mixtures Ti(C,N)-Mo₂C-Ni and their associated binary counterparts Ni-Mo₂C, Ti(C,N)-Mo₂C and Ni-Ti(C,N) at 1200 °C were investigated by X-ray diffraction analysis. It was shown that the decrease and disappearance of Mo₂C during the sintering of Ti(C,N)-MoC-Ni cermet composites at or below 1200 °C are dictated by the relative amount of Mo₂ to Ni, through enhanced dissolution of Mo₂C in Ni by the presence of Ti(C,N). The reprecipitation of (Ti,Mo)(C,N) onto Ti(C,N) grains does not occur to a large extent under these conditions. On average, when the ratio of Mo₂C to Ni is below or around 0.3, all of the Mo₂C phases present in the Ti(C,N)-Mo₂C-Ni alloys can be dissolved in Ni after 1 h at 1200 °C. However, when the ratio is well over 0.3, only partial dissolution of Mo₂C can be observed even when the alloys are sintered at 1200 °C for 10 h. Both Mo₂C and Ti(C,N) can be dissolved in Ni in the solid state, but the dissolution of Mo₂C in Ni in the Ti(C,N)-Mo₂C-Ni alloys is enhanced by the presence of Ti(C,N), hence N, compared to the dissolution of Mo₂C in the Ni-Mo₂C alloys. Negligible phase interactions are detected between Ti(C,N) and Mo₂C when sintered at 1200 °C for up to 5 h, either with or without Ni presence.