Research progress on C-coated Ti composite powders used for preparing high-performance Ti matrix composites
-
摘要:
钛基复合材料中增强相的形貌和分布是决定材料性能的关键,常规粉体机械混合后烧结引入增强相的方式存在形貌难调控、分布单一且均匀性差等问题,导致其强化效果不佳。针对该问题,本团队开发了一系列碳包覆钛复合粉体,通过设计包覆碳源的结构与组成调控粉体烧结过程中增强相的形成路径,不仅实现了增强相形貌调控和不同形貌的组合搭配,而且得到了晶内和晶界双增强相组织,大幅提升了钛基复合材料的力学性能。在此基础上,将碳包覆钛复合粉体拓展应用至钛基复合材料的3D打印领域,解决了高品质复合粉体缺乏并制约其发展的瓶颈问题。总结并评述了碳包覆钛复合粉体在制备钛基复合材料中取得的研究结果与工作进展,为增强相设计与调控提供新的研究思路及技术路线。
Abstract:The morphology and distribution of reinforcements in the titanium matrix composites (TMCs) are crucial in determining the material performances. Due to the uncontrollable morphology and inhomogeneous distribution of the reinforcements in the current TMCs, a series of C-coated Ti composite powders were developed by fluidization technology. By designing the structure and composition of C-coatings, the different morphology combinations and the intragranular/interface reinforcements were both achieved, which significantly improved the mechanical properties of TMCs. Furthermore, the composite powders were also extended to the 3D printing of TMCs, which solved the bottleneck issue of lacking the high-quality composite powders. The research results and work progress of the C-coated Ti composite powders in the preparation of high-performance TMCs were summarized and reviewed, providing the new insight and technical route for the design and control of reinforcements in TMCs.
-
粉末冶金摩擦材料是一种含有金属和非金属的多组元假合金。一般由基体组元、摩擦组元和润滑组元三部分组成[1-2]。与有机摩擦材料相比, 粉末冶金摩擦材料的力学强度高、抗冲击载荷强、摩擦系数稳定、热稳定性高、热传导性好、抗腐蚀能力强, 以及耐磨性能优良, 是现代刹车材料中应用较为广泛的材料之一[3-5]。目前已被应用于各种大型民用飞机、高性能军用飞机、火车、汽车、风电行业以及其它机械制动装置中[6-10]。
相对比于铁基粉末冶金摩擦材料高温下容易产生胶合、摩擦系数波动大、异常磨损明显、噪声大等情况, 铜基摩擦材料因其良好的导热性和自润湿性能, 在干、湿条件下均具备稳定的摩擦性能, 并在高速制动摩擦过程中, 基体与铜结构形成热扩散通道, 能够在相对短的时间内将大量摩擦热散发到环境中, 有效避免了热聚集引起胶粘对制动盘性能造成不利的影响[11]。长期以来, 对铜基粉末冶金摩擦材料的研究主要集中在配方研究和制备工艺对摩擦磨损性能的影响方面, 而刹车速度对铜基粉末冶金摩擦材料的摩擦磨损机理的研究相对较少。本文以铜基粉末冶金摩擦材料为研究对象, 探讨不同的刹车速度对铜基粉末冶金摩擦材料摩擦磨损性能的影响规律, 并对其微观组织进行研究表征, 为新型铜基粉末冶金摩擦材料的深入研究提供参考与理论支持。
1. 实验
1.1 试样制备
实验中所用的材料主要包括电解铜粉、还原铁粉、鳞片状天然石墨, SiO2粉和铬铁等。按表 1的配方分别称取各种粉料, 并在双锥形混合机中混合20~24 h, 将混合均匀的混合料制成压坯, 压坯尺寸为20 mm×15 mm, 厚度大于5 mm。将压坯置于钟罩式加压烧结炉内, 并在氢气保护气氛中进行加压烧结, 烧结温度为850~900℃, 烧结压力为0.3~0.5 MPa, 烧结时间为3.5~4 h。烧结完成后冷却至500℃后再随箱水冷至≤60℃, 出砂。
表 1 铜基粉末冶金摩擦材料化学成分(质量分数)Table 1. Chemical composition of the copper-based powder metallurgy brake materials% Cu Sn Fe SiO2 铬铁 其它 60~70 1~6 6~15 5~10 2~5 10~20 1.2 性能表征
采用JEOL公司的JSM-6390A型扫描电子显微镜(scanning electron microscope, SEM)对铜基粉末冶金摩擦材料实验前后的表面形貌进行观测; 采用HRF-150型洛氏硬度计和夏比冲击试验机分别对烧结后粉末层的硬度和冲击韧性进行表征; 在MM-3000型摩擦磨损性能试验台上进行摩擦磨损性能试验, 对偶盘材料为30CrMnSiA。试验前, 摩擦副表面先磨合至摩擦副贴合面积≥80%, 摩擦磨损试验条件及要求见表 2。
表 2 摩擦磨损试验条件Table 2. Condition of friction and wear test编号 惯量/ (kg·m2) 刹车压力/ MPa 刹车速度/ (m·s-1) 刹车转速/ (r·min-1) 次数 1# 0.225 0.66 27.78 2652 10 2# 33.33 3183 10 3# 38.89 3714 10 4# 44.44 4244 10 5# 50.00 4775 10 6# 55.56 5305 10 摩擦试验机记录摩擦吸收功率、刹车力矩与刹车时间关系。根据式(1)可计算出摩擦系数。
$$ \mu = \frac{{2M}}{{\left( {{\gamma _1} + {\gamma _2}} \right) \cdot F}} $$ (1) 式中:μ为摩擦系数, M为力矩(N·m), F为荷重(N), γ1为内圈半径(m), γ2为外圈半径(m)。用电子天平测量试样摩擦试验前后的质量变化; 用千分尺测量试样上6个不同位置处摩擦试验前后的厚度变化, 计算出摩擦试验前后试样厚度差, 求出平均值即试样的线性磨损量。
2. 结果与分析
2.1 微观结构
图 1为烧结后铜基粉末冶金摩擦材料表面显微组织形貌。图中黑色的为鳞片石墨, 白色的为铜, 灰色的可能为铁、铬铁或SiO2颗粒。从图可以看出, 大量的鳞片石墨稳定地分布在铜基体当中, 从而保证了刹车过程的平稳性和摩擦系数的稳定性。从图 1 (b)可以清楚地看到大量的灰色颗粒, 其中近似球状的较大颗粒为铬铁(200目, 如箭头所示), 其与基体接触良好, 两者之间观测不到明显的界面[12]; 较小的球状物可能为铁、二氧化硅等颗粒(100目); 这些颗粒均匀地分布在铜基体当中, 铜基体包裹着鳞片状石墨分布在摩擦片表面, 具有稳定的摩擦系数。
2.2 物理性能
铜基粉末冶金摩擦材料的力学性能如表 3所示。从表中可以看出, 摩擦材料的密度较高, 说明摩擦材料中的非金属组元所占体积较小; 材料的洛氏硬度较低, 说明摩擦试验中的对偶磨损相对较小; 材料的抗冲击韧性较大, 表明摩擦组元在材料烧结过程中以机械镶嵌的方式存在基体材料中, 提高了摩擦材料的耐磨性。在高速刹车过程中, 摩擦材料的力学性能确保了其在较大冲击力和较大磨损量条件下的使用。
表 3 摩擦材料的力学性能Table 3. Mechanical properties of friction material密度/ (g·cm-3) 洛氏硬度,HB 冲击韧性/ (J·cm-2) ≥5.72 ≥27 ≥33.5 2.3 摩擦磨损试验
图 2为试样在55.56 m/s刹车速度下的摩擦磨损曲线图。在此刹车速度下, 最大摩擦系数为0.5061, 平均摩擦系数为0.4521;经计算, 离均差率为11.94%, 较小的离均差率说明了铜基摩擦材料具有稳定的摩擦系数。从图中还可以看出, 摩擦系数曲线无明显的振颤现象, 力矩曲线也呈稳定增长趋势, 这也充分表明了该铜基粉末冶金摩擦材料的刹车制动效果平稳, 产生这种现象的原因可能是由于摩擦材料配方中摩擦组元铬铁和铜基体具有良好的润湿性能, 从而提高了摩擦系数的稳定性[12]。
图 3 (a)是在不同刹车速度条件下摩擦磨损性能试验后试样的摩擦吸收功率和摩擦系数曲线图。摩擦吸收功率是指试样在单位时间单位面积内所吸收的功, 它与摩擦面的温度升高有着直接对应关系, 因此影响试样的摩擦系数。从图 3 (a)可以看出, 随着刹车速度增大, 刹车能量升高, 摩擦面的温度进一步升高, 试样的摩擦吸收功率呈近似线性升高。刹车速度从27.78 m/s增加到44.44 m/s, 试样的摩擦吸收功率速率增长最快; 当刹车速度从44.44 m/s增加到55.56 m/s, 试样的摩擦吸收功率增加相对缓慢, 这表明铜基粉末冶金摩擦材料在低速条件下, 吸收的动能可能主要被铜基摩擦材料中的孔隙吸收并传导到空气当中; 当制动速率超过44.4 m/s时, 摩擦材料的吸收动能会被铜基摩擦材料自身所吸收, 并通过高的导热性将吸收能量传导至空气中。从图中还可以看出, 当刹车速度从27.78 m/s增加到44.44 m/s时, 摩擦系数也相对从0.4040增加到0.5071。但随着刹车速率的提高, 试样的摩擦系数出现了明显下降的趋势, 这可能与摩擦材料的摩擦机理和微观结构有关。
图 3 (b)是在不同刹车速度条件下摩擦磨损性能试验后试样的线性磨损率和质量磨损。从图 3 (b)可以看出, 试样的线磨损率随刹车速度的变化与质量损失随刹车速度的变化一致, 都呈上升的趋势。当刹车速度从27.78 m/s增加到33.33 m/s, 试样的线磨损率和质量磨损均较大, 这是由于在较低的速度下, 刹车未进入平稳阶段, 出现了较为明显的磨粒磨损; 当刹车速度从33.33 m/s增加到50.00 m/s时, 粘着磨损起主要作用, 因此线性磨损率和质量磨损都相对较小; 当刹车速率增长至55.56 m/s时, 试样的质量磨损呈明显增长趋势, 这可能是由于在高速条件下, 铜基摩擦材料自身软化造成摩擦组元脱落, 从而质量损耗明显。但由于线性磨损率数据的获得是通过千分尺测量一定面积上的厚度损耗而计算得到的, 因此线性磨损率并不能完全反应出摩擦组元的脱落引起厚度的微小变化, 因而线性损耗率增长不明显。
为进一步研究刹车速度对摩擦磨损性能的影响, 探讨摩擦磨损性能与摩擦面的关系, 采用扫描电子显微镜对在不同刹车速度下试样的摩擦面进行分析。图 4所示为不同刹车速度试验后铜基粉末冶金摩擦材料表面的扫描电子显微形貌。从图中可以看出, 当刹车速度为27.78 m/s和33.33 m/s时, 由于刹车速度较低, 摩擦剪切力较小, 因此摩擦表面温度较低, 且未能形成连续完整的氧化膜, 从而出现了较小面积的剥落且剥落的块状物较小, 其中剥落后较小的硬质颗粒在剪切力作用下从摩擦表面脱落, 在摩擦副之间形成磨粒, 在摩擦表面产生犁沟, 发生磨料磨损和剥层损耗, 其磨损主要是由机械啮合作用造成的; 当刹车速度为38.89 m/s和44.44 m/s时, 摩擦表面较为光滑, 无明显的脱落。这是由于随着刹车速度的增大, 摩擦吸收功率增大, 摩擦面的温度提高, 摩擦剪切力的作用也逐渐增强, 氧化膜趋于平滑连续, 摩擦表面与摩擦副的真实接触面积越大, 其机械啮合作用减弱, 粘着机理起主要作用。随着刹车速度的进一步增大, 摩擦表面在较大剪切力的作用下发生了较为严重的脱落。当刹车速度从50.00 m/s逐渐增大到55.56 m/s, 试样摩擦表面单位面积吸收的能量进一步增大, 温度进一步升高, 摩擦表面在较大剪切力的作用下发生了较为严重的脱落。这是由于摩擦产生的高温引起材料软化, 破坏了形成的氧化膜, 降低了分子键的抗剪切强度, 从而在摩擦面上出现了不同程度的犁沟[13-14]。
3. 结论
(1) 铜基粉末冶金摩擦材料的摩擦磨损性能与刹车速度密切相关。随着刹车速度的增大, 刹车能量急剧升高, 摩擦材料的摩擦吸收功率近似线性增长, 而摩擦系数呈先增大后减小的趋势, 并且铜基粉末冶金摩擦材料的线磨损率与质量磨损随刹车速度增长呈上升趋势。
(2) 在一定的刹车速度下, 铜基粉末冶金摩擦材料摩擦表面的氧化膜愈趋平滑连续。但随着刹车速度的提高, 铜基体自身发生软化, 破坏了已形成的氧化膜, 降低了分子键的抗剪切强度, 从而增大了磨损量。
-
图 2 不同碳包覆钛粉体显微形貌[29‒32]:(a)A–C/TC4粉的表面微观形貌;(b)A–C/TC4粉的截面微观形貌;(c)CNTs/Ti粉的微观形貌;(d)CNTs的透射电镜图片;(e)H–C/TC4粉的微观形貌;(f)两种碳源的透射电镜图片
Figure 2. Morphologies of the different C-coated Ti powders[29‒32]: (a) SEM image of the A–C/TC4 powder surface; (b) sectional SEM image of the A–C/TC4 powder; (c) SEM image of CNTs/Ti powder; (d) TEM image of the extracted CNTs; (e) SEM image of H–C/TC4 powder; (f) TEM image of the extracted CNTs and A–C
图 3 A‒C/TC4粉的热压烧结组织及增强相[29]:(a)和(b)A–C/TC4粉体的烧结组织和增强相分布的扫描电镜照片;(c)和(d)α-Ti晶内分布纳米片状增强相的形貌及物相分析;(e)和(f)β-Ti晶内分布颗粒增强相的形貌及物相分析
Figure 3. Sintered A–C/TC4 samples and the reinforcements[29]: (a) and (b) SEM images of the sintered A–C/TC4 samples and the reinforcement distribution; (c) and (d) the morphology and phase analysis of the nanoplatelets inside α-Ti grains; (e) and (f) the morphology and phase analysis of the nanoparticles inside β-Ti grains
图 4 CNTs/Ti粉在不同温度的烧结组织和增强相形貌分布[31]:(a)和(b)900 ℃;(c)和(d)1000 ℃;(e)和(f)900 ℃烧结样品中保留的CNTs和形成的TiC颗粒
Figure 4. Microstructure of the CNTs/Ti powder samples sintered at different temperatures[31]: (a) and (b) 900 ℃; (c) and (d) 1000 ℃; (e) and (f) TEM images of the remained CNTs and the formed TiC nanoparticles in the CNTs/Ti powder samples sintered at 900 ℃
图 7 H‒C/TC4粉体烧结组织及增强相[32]:(a)和(b)H–C/TC4粉体烧结组织及增强相分布;(c)~(e)晶界增强相的透射电子显微镜照片;(f)晶内增强相的透射电子显微镜照片
Figure 7. Sintered H–C/TC4 samples and the reinforcements[32]: (a) and (b) sintered H–C/TC4 sample microstructures and the reinforcement distribution; (c)~(e) TEM images of the interfacial reinforcements; (f) TEM images of the intragranular reinforcements
图 8 不同形貌和分布组合增强相强化钛基复合材料[29‒32]:(a)与文献报道中钛基复合材料压缩屈服强度对比;(b)晶界增强相的强化机制;(c)晶内增强相的强化机制;(d)晶内/晶界双增强相组织的强化机制示意图
Figure 8. Reinforcements with the different morphologies and distribution combinations in TMCs[29‒32]: (a) comparison of the TMCs compressive yield strength reported in literatures; (b) strengthening mechanisms of the interfacial reinforcements; (c) strengthening mechanisms of the intragranular reinforcements; (d) strengthening mechanism of the interfacial/intragranular double reinforced phase
图 9 CNTs/GA–TC4粉体的扫描电镜形貌(a)、原位合成CNTs扫描电镜形貌(b)、复合粉体打印样品宏观形貌(c)及打印样品的三维重构照片(d)[47]
Figure 9. SEM image of the CNTs/GA–TC4 powders (a), SEM image of the in situ synthesized CNTs (b), macro-profile of the samples printed by the CNTs/GA–TC4 powders (c), and 3D reconstructed images of the printed sample (d)[48]
-
[1] Hayat M D, Singh H, He Z, et al. Titanium metal matrix composites: An overview. Composites Part A, 2019, 121: 418 DOI: 10.1016/j.compositesa.2019.04.005
[2] Huang L J, An Q, Geng L, et al. Multiscale architecture and superior high-temperature performance of discontinuously reinforced titanium matrix composites. Adv Mater, 2021, 33(6): 2000688 DOI: 10.1002/adma.202000688
[3] Jiao Y, Huang L J, Geng L. Progress on discontinuously reinforced titanium matrix composites. J Alloys Compd, 2018, 767: 1196 DOI: 10.1016/j.jallcom.2018.07.100
[4] Huang L J, Geng L, Peng H X. Microstructurally inhomogeneous composites: Is a homogeneous reinforcement distribution optimal? Prog Mater Sci, 2015, 71: 93
[5] Namini A S, Dilawary S A A, Motallebzadeh A, et al. Effect of TiB2 addition on the elevated temperature tribological behavior of spark plasma sintered Ti matrix composite. Composites Part B, 2019, 172: 271 DOI: 10.1016/j.compositesb.2019.05.073
[6] Liao Z R, Abdelhafeez A, Li H N, et al. State-of-the-art of surface integrity in machining of metal matrix composites. Int J Mach Tool Manuf, 2019, 143: 63 DOI: 10.1016/j.ijmachtools.2019.05.006
[7] Froes F H, Eylon D. Powder metallurgy of titanium alloys. Int Mater Rev, 1990, 35(1): 162 DOI: 10.1179/095066090790323984
[8] Ezugwu E O, Wang Z M. Titanium alloys and their machinability–a review. J Mater Process Technol, 1997, 68: 262 DOI: 10.1016/S0924-0136(96)00030-1
[9] Ma F C, Wang T R, Liu P, et al. Mechanical properties and strengthening effects of in situ (TiB+TiC)/Ti-1100 composite at elevated temperatures. Mater Sci Eng A, 2016, 654: 352 DOI: 10.1016/j.msea.2015.12.071
[10] 黄陆军, 耿林. 网状结构钛基复合材料. 北京: 国防工业出版社, 2015 Huang L J, Geng L. Titanium Matrix Composites with Network Microstructure. Beijing: National Defense Industry Press, 2015
[11] Liu Q, Qi F G, Wang Q, et al. The influence of particles size and its distribution on the degree of stress concentration in particulate reinforced metal matrix composites. Mater Sci Eng A, 2018, 731: 351 DOI: 10.1016/j.msea.2018.06.067
[12] Yan Q, Chen B, Cao L, et al. Improved mechanical properties in titanium matrix composites reinforced with quasi-continuously networked graphene nanosheets and in-situ formed carbides. J Mater Sci Technol, 2022, 96: 85 DOI: 10.1016/j.jmst.2021.03.073
[13] 汤慧萍, 黄伯云, 刘咏, 等. 粉末冶金颗粒增强钛基复合材料研究进展. 粉末冶金技术, 2004, 22(5): 293 DOI: 10.3321/j.issn:1001-3784.2004.05.008 Tang H P, Huang B Y, Liu Y, et al. Progress in powder metallurgy particle reinforced Ti matrix composite. Powder Metall Technol, 2004, 22(5): 293 DOI: 10.3321/j.issn:1001-3784.2004.05.008
[14] 杨宇承, 潘宇, 路新, 等. 粉末冶金法制备颗粒增强钛基复合材料的研究进展. 粉末冶金技术, 2020, 38(2): 150 DOI: 10.19591/j.cnki.cn11-1974/tf.2020.02.011 Yang Y C, Pan Y, Lu X, et al. Research progress on particle-reinforced titanium matrix composites prepared by powder metallurgy method. Powder Metall Technol, 2020, 38(2): 150 DOI: 10.19591/j.cnki.cn11-1974/tf.2020.02.011
[15] Saba F, Zhang F M, Liu S L, et al. Tribological properties, thermal conductivity and corrosion resistance of titanium/nanodiamond nanocomposites. Compos Commun, 2018, 10: 57 DOI: 10.1016/j.coco.2018.06.008
[16] Wang F C, Zhang Z H, Sun Y J, et al. Rapid and low temperature spark plasma sintering synthesis of novel carbon nanotube reinforced titanium matrix composites. Carbon, 2015, 95: 396 DOI: 10.1016/j.carbon.2015.08.061
[17] Lü S, Li J S, Li S F, et al. Effects of heat treatment on interfacial characteristics and mechanical properties of titanium matrix composites reinforced with discontinuous carbon fibers. J Alloys Compd, 2021, 877: 160313 DOI: 10.1016/j.jallcom.2021.160313
[18] Munir K S, Zheng Y F, Zhang D L, et al. Improving the strengthening efficiency of carbon nanotubes in titanium metal matrix composites. Mater Sci Eng A, 2017, 696: 10 DOI: 10.1016/j.msea.2017.04.026
[19] Munir K S, Li Y C, Qian M, et al. Identifying and understanding the effect of milling energy on the synthesis of carbon nanotubes reinforced titanium metal matrix composites. Carbon, 2016, 99: 384 DOI: 10.1016/j.carbon.2015.12.041
[20] Munir K S, Li Y C, Li J X, et al. Interdependencies between graphitization of carbon nanotubes and strengthening mechanisms in titanium matrix composites. Materialia, 2018, 3: 122 DOI: 10.1016/j.mtla.2018.08.015
[21] Zhang X, Zhao N Q, He C N. The superior mechanical and physical properties of nanocarbon reinforced bulk composites achieved by architecture design–A review. Prog Mater Sci, 2020, 113: 100672 DOI: 10.1016/j.pmatsci.2020.100672
[22] 冯俊, 姜中涛, 韩骐璘. 不连续增强钛基复合材料的研究进展. 粉末冶金技术, 2020, 38(5): 392 DOI: 10.19591/j.cnki.cn11-1974/tf.2019070001 Feng J, Jiang Z T, Han Q L. Research progress on discontinuous reinforced titanium matrix composites. Powder Metall Technol, 2020, 38(5): 392 DOI: 10.19591/j.cnki.cn11-1974/tf.2019070001
[23] Luo S D, Li Q, Tian J, et al. Self-assembled, aligned TiC nanoplatelet-reinforced titanium composites with outstanding compressive properties. Scr Mater, 2013, 69: 29 DOI: 10.1016/j.scriptamat.2013.03.017
[24] Geng L, Ni D R, Zhang J, et al. Hybrid effect of TiBw and TiCp on tensile properties of in situ titanium matrix composites. J Alloys Compd, 2008, 463(1): 488
[25] Huang L J, Geng L, Xu H Y, et al. In situ TiC particles reinforced Ti6Al4V matrix composite with a network reinforcement architecture. Mater Sci Eng A, 2011, 528: 2859 DOI: 10.1016/j.msea.2010.12.046
[26] Huang L J, Geng L, Peng H X, et al. High temperature tensile properties of in situ TiBw/Ti6Al4V composites with a novel network reinforcement architecture. Mater Sci Eng A, 2012, 534: 688 DOI: 10.1016/j.msea.2011.12.028
[27] Zadra M, Girardini L. High-performance, low-cost titanium metal matrix composites. Mater Sci Eng A, 2014, 608: 155 DOI: 10.1016/j.msea.2014.04.066
[28] 宋杰光, 纪岗昌, 李世斌, 等. 粉体包覆技术的研究进展. 材料导报, 2009, 23(增刊1): 164 Song J G, Ji G C, Li S B, et al. Review on coating technology of powder. Mater Rev, 2009, 23(Suppl 1): 164
[29] Li S F, Tan C, Liu Y, et al. Designing core-shell C-coated Ti–6Al–4V powders for high-performance nano-sized TiC platelets/particles synergistically reinforced Ti–6Al–4V composites. Materialia, 2018, 2: 68 DOI: 10.1016/j.mtla.2018.06.010
[30] Li S F, Liu Y, Yang Y F. Activating trace Fe impurity as catalyst to plant carbon nanotubes within Ti–6Al–4V powders for high-performance Ti-matrix composites. Metall Mater Trans A, 2019, 50: 3975 DOI: 10.1007/s11661-019-05321-x
[31] Li S F, Cui J Y, Yang Y F, et al. In situ growth of carbon nanotubes on Ti powder for strengthening of Ti matrix composite via nanotube-particle dual morphology. Metall Mater Trans A, 2020, 51: 5932 DOI: 10.1007/s11661-020-05988-7
[32] Li S F, Yang Y F, Misra R D K, et al. Interfacial/intragranular reinforcement of titanium-matrix composites produced by a novel process involving core-shell structured powder. Carbon, 2020, 164: 378 DOI: 10.1016/j.carbon.2020.04.010
[33] Li S F, Geng K, Misra R D K, et al. Commercial scale uniform powder coating for metal additive manufacturing. JOM, 2020, 72: 4639 DOI: 10.1007/s11837-020-04386-z
[34] Vasanthakumar K, Karthiselva N S, Chawake N M, et al. Formation of TiCx during reactive spark plasma sintering of mechanically milled Ti/carbon nanotube mixtures. J Alloys Compd, 2017, 709: 829 DOI: 10.1016/j.jallcom.2017.03.216
[35] Adegbenjoa A O, Olubambia P A, Potgieter J H, et al. Spark plasma sintering of graphitized multi-walled carbon nanotube reinforced Ti6Al4V. Mater Des, 2017, 128: 119 DOI: 10.1016/j.matdes.2017.05.003
[36] Munir K S, Oldfield D T, Wen C. Role of process control agent in the synthesis of multi-walled carbon nanotubes reinforced titanium metal matrix powder mixtures. Adv Eng Mater, 2016, 18: 294 DOI: 10.1002/adem.201500346
[37] Lee H J, Kim S H, Lee J C. Promotion of C diffusion to prepare a high-strength wear-resistant Ti alloy. Scr Mater, 2016, 115: 33 DOI: 10.1016/j.scriptamat.2015.12.024
[38] Hao Y J, Liu J X, Li J H, et al. Rapid preparation of TiC reinforced Ti6Al4V based composites by carburizing method through spark plasma sintering technique. Mater Des, 2015, 65: 94 DOI: 10.1016/j.matdes.2014.09.008
[39] Zhang X J, Song F, Wei Z P, et al. Microstructural and mechanical characterization of in-situ TiC/Ti titanium matrix composites fabricated by graphene/Ti sintering reaction. Mater Sci Eng A, 2017, 705: 153 DOI: 10.1016/j.msea.2017.08.079
[40] Zhang D Y, Qiu D, Gibson M A, et al. Additive manufacturing of ultrafine-grained high-strength titanium alloys. Nature, 2019, 576: 91 DOI: 10.1038/s41586-019-1783-1
[41] Yu W H, Sing S L, Chua C K, et al. Particle-reinforced metal matrix nanocomposites fabricated by selective laser melting: A state of the art review. Prog Mater Sci, 2019, 104: 330 DOI: 10.1016/j.pmatsci.2019.04.006
[42] Yan Q, Chen B, Li J S. Super-high-strength graphene/titanium composites fabricated by selective laser melting. Carbon, 2021, 174: 451 DOI: 10.1016/j.carbon.2020.12.047
[43] Zeng X, Yamaguchi T, Nishio K. Characteristics of Ti(C, N)/TiB composite layer on Ti–6Al–4V alloy produced by laser surface melting. Opt Laser Technol, 2016, 80: 84 DOI: 10.1016/j.optlastec.2016.01.004
[44] Gu D D, Hagedorn Y C, Meiners W, et al. Selective laser melting of in-situ TiC/Ti5Si3 composites with novel reinforcement architecture and elevated performance. Surf Coat Technol, 2011, 205: 3285 DOI: 10.1016/j.surfcoat.2010.11.051
[45] Gu D D, Meng G B, Li C, et al. Selective laser melting of TiC/Ti bulk nanocomposites: Influence of nanoscale reinforcement. Scr Mater, 2012, 67: 185 DOI: 10.1016/j.scriptamat.2012.04.013
[46] He B B, Chang K, Wu W H, et al. The formation mechanism of TiC reinforcement and improved tensile strength in additive manufactured Ti matrix nanocomposite. Vacuum, 2017, 143: 23 DOI: 10.1016/j.vacuum.2017.05.029
[47] Liu Y, Li S F, Misra R D K, et al. Planting carbon nanotubes within Ti–6Al–4V to make high-quality composite powders for 3D printing high-performance Ti–6Al–4V matrix composites. Scr Mater, 2020, 183: 6 DOI: 10.1016/j.scriptamat.2020.03.009
[48] Gu D D, Rao X W, Dai D H, et al. Laser additive manufacturing of carbon nanotubes (CNTs) reinforced aluminum matrix nanocomposites: Processing optimization, microstructure evolution and mechanical properties. Addit Manuf, 2019, 29: 100801
[49] Aboulkhair N T, Simonelli M, Salama E, et al. Evolution of carbon nanotubes and their metallurgical reactions in Al-based composites in response to laser irradiation during selective laser melting. Mater Sci Eng A, 2019, 765: 138307 DOI: 10.1016/j.msea.2019.138307
[50] Zhang B C, Bi G J, Chew Y X, et al. Comparison of carbon-based reinforcement on laser aided additive manufacturing Inconel 625 composites. Appl Surf Sci, 2019, 490: 522 DOI: 10.1016/j.apsusc.2019.06.008
-
期刊类型引用(10)
1. 徐琴,张驰,樊江磊,刘建秀. Cr-Fe粒度对铜基粉末冶金材料摩擦磨损性能的影响. 特种铸造及有色合金. 2024(05): 587-590 . 百度学术
2. 陈孝婷,卢纯,莫继良,张庆贺,赵婧. 考虑摩擦升温的铁路列车制动摩擦块高温磨损机制演变. 中国表面工程. 2023(03): 142-151 . 百度学术
3. 刘思涵,耿雪骞,王晔,马运章,陈德峰,张波,曹宏发,齐冀,吕宝佳. Cu基粉末冶金闸片高速制动性能. 粉末冶金技术. 2023(03): 210-217 . 本站查看
4. 安先龙,王国权,王立勇,陈勇. 铜基粉末冶金摩擦块摩擦磨损特性研究. 机械设计与制造. 2023(12): 209-213+218 . 百度学术
5. 贾潞. 铜基粉末冶金摩擦材料粘接层失效机理研究. 铁道机车车辆. 2023(06): 111-116 . 百度学术
6. 刘喜双,许雄飞,王秀飞,文国富,尹彩流,冯驰原. 鳞片石墨含量对地铁集电靴用铜基粉末冶金材料性能的影响. 粉末冶金工业. 2021(03): 18-24 . 百度学术
7. 任澍忻,陈文革,冯涛,欧阳方明. 粉末冶金制备碳纤维增强铁-铜基摩擦材料的组织与性能. 粉末冶金技术. 2020(02): 104-112 . 本站查看
8. 韩明,杜建华,宁克焱,李辉,王志勇,邱倩. 温度分布对铜基摩擦材料点蚀损伤的影响. 粉末冶金技术. 2019(01): 18-22 . 本站查看
9. 姚萍屏,肖叶龙,张忠义,周海滨,贡太敏,赵林,邓敏文. 高速列车粉末冶金制动材料的研究进展. 中国材料进展. 2019(02): 116-125 . 百度学术
10. 丁干,王国权,曾圣迪,陈勇,王立勇,雷桐辉. 铜基粉末冶金材料摩擦磨损性能分析. 北京信息科技大学学报(自然科学版). 2019(04): 61-65+96 . 百度学术
其他类型引用(6)