以沥青为前驱体制备TiC/FeCrNi反应火焰喷涂复合涂层

以钛铁粉、CrFe粉、羰基镍粉和碳的前驱体（石油沥青）为原料,通过前驱体碳化复合技术制备了Ti-Fe-Cr-Ni-C反应喷涂复合粉末,并通过普通火焰喷涂成功地合成与沉积了TiC/FeCrNi复合涂层.采用XRD和SEM对喷涂粉末和涂层的相组成和显微结构进行了分析,同时对涂层耐磨性能进行了对比研究.研究结果表明：采用前驱体碳化复合技术制备的Ti-Fe-Cr-Ni-C反应喷涂复合粉末粒度均匀、无有害相生成;所制备的TiC/FeCrNi复合涂层由不同含量TiC颗粒分布于金属基体内部而形成的复合强化片层叠加而成,TiC颗粒呈纳米级;基体由（Fe,Cr）和Cr0.19Fe0.7Ni0.11两相组成;相同条件下,所获TiC/FeCrNi复合涂层磨损体积大约是常规火焰喷涂Ni60涂层的1/8.     

以蔗糖为前驱体火焰喷涂原位TiC增强Ni基复合涂层的制备

以蔗糖为碳源,采用前驱体热分解技术制备Ni-Ti-C系反应热喷涂混合粉末,通过氧乙炔火焰喷涂技术合成并同时沉积原位TiC颗粒增强的Ni基合金复合涂层.利用XRD和SEM研究混合粉末和涂层的相成分和组织结构,分析TiC/Ni复合涂层的硬度和耐磨性.结果表明:反应火焰喷涂TiC/Ni复合涂层主要由TiC和Ni基体组成,并含少量的Ni3Ti和Ti3O5;涂层由复合强化片层相瓦叠加而成,复合强化片层中TiC颗粒均匀分布于Ni基体中,TiC颗粒呈球形,粒度达到亚微米级:涂层具有较高的硬度和耐磨性,复合强化片层显微硬度为FIV0.21433,涂层的耐磨性能远优于基板材料45号钢和对比涂层Ni60的耐磨性.     

反应火焰喷涂的TiC/Fe金属陶瓷复合涂层

以TiFe粉和碳的前驱体(石油沥青)为原料,通过碳化制备Ti-Fe-C系反应喷涂复合粉末,并通过普通火焰喷涂技术成功制备了TiC/Fe金属陶瓷复合涂层;采用XRD、SEM和EDS对喷涂粉末和涂层的成分、组织结构进行了分析,同时对涂层耐磨性能进行了对比研究.结果表明:采用前驱体碳化复合技术制备的Ti-Fe-C系复合喷涂粉末粒度均匀、无有害相生成;喷涂所得到的TiC/Fe金属陶瓷复合涂层由片状的铁基体和弥散分布的TiC颗粒组成;TiC颗粒大致呈球形,粒度一般在0.5 μm以下;相同条件下所获涂层的磨损体积大约是常规火焰喷涂Ni60涂层的1/5.     

反应等离子喷涂TiC/Fe-Ni金属陶瓷复合涂层的显微组织

采用前驱体碳化复合技术制备Ti-Fe-Ni-C系粉末,并通过反应等离子喷涂技术（RPS）原位合成并沉积了TiC/Fe-Ni基金属陶瓷复合涂层。利用XRD、SEM和EDS研究复合粉末和涂层的成分、组织结构,考察复合粉末的TiC含量及复合粉末粒度对涂层组织结构的影响。结果表明：采用前驱体碳化复合技术制备的反应喷涂复合粉末粒度均匀、无有害相生成;TiC/Fe-Ni复合涂层由不同含量TiC颗粒分布于晶粒内部而形成的晶内型复合强化片层叠加而成,基体主要为（Fe、Ni）固溶体,TiC颗粒呈纳米级;涂层TiC含量较高时,纳米级TiC颗粒弥散分布更均匀;喷涂粉末粒度较大时,片层厚度较大,孔隙率较高。     

激光熔覆TiC／FeAl复合材料涂层显微组织及初生TiC生长机制研究

利用激光熔覆技术在1Cr18Ni9Ti奥氏体不锈钢基体上制得了以TiC为增强相、以FeAl金属间化合物为基体的快速凝固TiC／FeAl复合材料涂层，分析了该涂层的显微组织及初生TiC的生长形态和生长机制。研究结果表明，激光熔覆TiC／FeAl快速凝固复合材料涂层主要由初生TiC碳化物、初生FeAl树枝晶和枝晶间少量的FeAl／TiC共晶组成，初生TiC具有独特的径向辐射分枝小面枝晶团簇状生长形态，其生长机制为侧向生长。     

激光熔覆H13/TiC复合涂层中TiC的生长机制

采用激光熔覆技术,在H13钢表面制备H13/TiC复合涂层.通过XRD、TEM和SEM对熔覆层中的物相、微观形貌和组成进行表征,研究了不同TiC含量形成的熔覆层中,TiC颗粒的形貌变化.结果表明:随着TiC含量的增加,熔覆层内TiC颗粒由少增多,由分散的不规则的多边形演变为放射状的树枝晶和花状;并对TiC的生长机理进行了初步分析.     

TiC生成方式对激光熔覆镍基涂层组织和性能的影响

分别以TiC粉和Ti+C粉为原料,采用外加法和原位法制备了TiC/Ni激光熔覆涂层,分析了TiC生成方式对涂层物相组成、微观组织、硬度和磨损性能的影响。结果表明,涂层的物相组成不受生成方式的影响;但Ti+C质量分数高于30%时,原位法涂层无法成型,而外加法可获得40%TiC的涂层。外加法涂层中TiC以原料TiC为主,少量溶解析出的结晶TiC;而原位法涂层中TiC全部为结晶析出,分布更加均匀,颗粒细小,枝晶数量增多。原位法涂层的平均硬度和耐磨性均优于相同TiC含量的外加法涂层;涂层中TiC含量(质量分数)由20%增至30%时,涂层硬度升高,耐磨性下降,生成方式引起的磨损性能差异由5%降至0.6%。     

TiC/Fe-Ni金属陶瓷复合涂层反应等离子喷涂研究

以钛铁粉、镍粉、铁粉和碳的前驱体(蔗糖)为原料采用前驱体碳化复合技术制备了Ti-Fe-Ni-C系反应热喷涂粉末,并通过等离子喷涂(RPS)技术原位合成并沉积了TiC/Fee-Ni金属陶瓷复合涂层.采用XRD、SEM和EDS对喷涂粉末和涂层的成分、组织结构进行了分析.研究表明该反应喷涂粉末粒度均匀、无有害相生成;所得涂层由不同TiC颗粒含量的TiC/Fe-Ni复合片层组成;TiC颗粒大致呈球形,粒度呈纳米级;所获涂层在相同条件下耐磨性是Ni60涂层的7倍.     

TiC含量对W-30Cu/TiC复合材料显微组织和性能影响研究

经简化预处理后,采用化学法制得W–30Cu/(0-4) wt.% TiC复合粉末,在400MPa的压力下将制得的复合粉末压制成毛坯块体试样,随后在1300 °C下烧结1 h制得块体复合材料试样。采用场发射扫描电子显微镜来表征原始W 和TiC粉末、预处理后的W和TiC粉末、化学法制得的W–30Cu/(0, 0.25, 0.5, 1, 2, 3, 4) wt.% TiC复合粉末的显微形貌,以及制得的W–30Cu/TiC复合材料的显微结构。本文对不同TiC含量对W–30Cu/TiC复合材料的性能（如相对密度、硬度、导电性和抗弯强度等）进行研究。结果表明：对简单预处理后的W、TiC粉末化学镀Cu所获得的W–30Cu/TiC复合粉末的显微结构均匀。TiC含量低于1%时,W–30Cu/TiC复合材料的抗弯强度和硬度随TiC含量的增加而显著增大。而导电性则随TiC含量增加而减小,但仍高于国家标准值。添加一定量的TiC有利于获得综合性能能较好的W–30Cu/TiC复合材料。     

纳米TiC涂层的制备技术研究

TiC涂层由于具备良好的性能而广泛地应用于机械加工行业.以高温CVD方法制备TiC涂层技术为基础,研究了在反应腔中设置温度达到1600℃的高温处理装置,使原料气经过高温处理装置后在基体上沉积出TiC涂层.经金相显微镜测量厚度约为10μm,经XRD检测成分为:界面出现脱碳相Co 6W 6C,膜层除含有少量氧化物杂质外,为纯净的TiC涂层,颗粒尺寸平均为84.8nm.探索了制备纳米TiC涂层工艺的机制,其中高温处理、大温度梯度、惰性气体及冷却腔体避免引入杂质是形成纳米TiC涂层的关键因素.制备纳米级TiC涂层,可使涂层硬度、断裂韧性、表面光洁度、耐高温性能等性能指标得到提高,提高了TiC涂层产品的综合性能.     

多层氩弧熔敷含TiC颗粒增强涂层的微观组织及耐磨性能

利用多层多道钨极氩弧熔覆技术,熔融预涂于钢基体表面钛铁和石墨混合粉末,可以在普通碳钢表面获得综合性能优异的复合材料表面熔敷层;测试和分析表明,熔敷层微观组织主要由铁素体、低碳马氏体、原位生成的TiC颗粒及碳化物等组成;熔敷层表面硬度达到了HRC 57以上,呈梯度分布特征;滑动磨损试验表明,由于TiC增强颗粒的存在,熔敷层与摩擦副的摩擦系数在磨损过程中不稳定,变化范围较大;TiC颗粒对摩擦的阻碍、钉扎作用大大提高了熔敷层的抗磨损性能,熔敷层磨损体积比基体金属小15～20倍,具有良好的耐磨性能.     

钛合金表面激光熔化沉积钛基复合材料涂层的组织及性能

通过激光熔化沉积TA15+30%TiC(体积分数)混合粉末,在TA15钛合金表面制备出钛基复合材料涂层,分析了涂层的组织、硬度及界面结合强度。结果表明,激光熔化沉积过程中原始TiC颗粒发生溶解,并在凝固过程中重新析出细小的TiC,TiC有等轴状及枝晶两种形态,涂层中存在部分未熔的TiC颗粒;涂层硬度达HRC 60;涂层与基体界面为完全冶金结合,涂层的界面结合强度大于310 MPa,抗剪切强度为330 MPa;经弯曲及热震试验后,涂层未出现剥落现象,表明涂层与基体具有很好的相容性     

氩弧熔覆 TiC 颗粒增强 Fe 基涂层组织性能研究

目的研究氩弧熔覆条件下TiC颗粒增强Fe基涂层的组织和性能。方法在Fe45自熔性合金粉末中添加TiC颗粒,利用氩弧熔覆技术在Q235钢基材表面制备出含TiC颗粒增强的Fe基合金复合涂层,并对熔覆层的显微组织结构、硬度分布及耐磨性能进行分析研究。结果复合涂层是由(Fe,Ni)形成的枝晶和枝晶间的(Fe,Cr)23(C,B)6,Fe3(C,B)共晶组织以及TiC增强颗粒组成,TiC颗粒细小弥散分布在基体金属内,部分TiC颗粒聚集生长为棒状、十字状和放射状。结论熔覆层的显微硬度最高可达980HV,较Q235钢提高了4倍,耐磨性提高了约11倍。     

Effect of Dispersed TiC Content on the Microstructure and Thermal Expansion Behavior of Shrouded-Plasma-Sprayed FeAl/TiC Composite Coatings

FeAl intermetallic matrix composites reinforced by ceramic particles such as titanium carbide have attracted much attention in recent years. In this study, shrouded plasma spraying with nitrogen as a protective gas was employed to deposit FeAl/TiC composite coatings. Fe-35Al powder and Fe-35Al/TiC composite powders containing 35 and 45?vol.% TiC prepared by mechanical alloying were used as feedstock powders. The microstructures of the ball-milled powders and the as-sprayed coatings were characterized by scanning electron microscopy and x-ray diffraction. The mean coefficients of thermal expansion (CTEs) of FeAl and FeAl/TiC were measured. The results showed that dense FeAl and FeAl/TiC coatings with low oxide inclusions were deposited by shrouded plasma spraying. The mean CTEs measured in the present study were reasonably consistent with those calculated based on the formula. As a result, the mean CTE of FeAl-based composite coating can be properly controlled by adjusting TiC content in the composite coating to match with those of different substrate materials.     

In Situ TiC-Reinforced Ni-Based Composite Coating Prepared by Flame Spraying Using Sucrose as the Source of Carbon

A Ni-Ti-C composite powder for Reactive Thermal Spraying is made by heating a mixture of titanium, nickel, and sucrose to carbonize the sucrose, which is used as the source of carbon. The carbon obtained by pyrolysis of sucrose is a reactive constituent as well as the binder in the composite powder. The titanium and nickel particles are bound by the carbon to form granules of the composite powder. This powder feedstock was used to prepare in situ TiC-reinforced Ni-based composite coating by oxyacetylene flame spraying. The TiC-Ni composite coating is made of TiC, Ni, and some Ni₃Ti. In the coating, a mass of fine TiC particles is uniformly distributed within the metallic matrix. The microhardness and surface hardness of the coating are, respectively, 1433 HV_0.2kg and 62 ± 6 (HR30N). The wear resistance is much better for the TiC-Ni composite coating than for the substrate and Ni60 coating.     

Ti-B-C composite coating produced by electrothermally exploded powder-spray technique

Composite coatings of a Ti-B-C system were reactively produced by the electrothermally exploded powderspray (ELTEPS) technique. First, the electrical characteristics of the ELTEPS system were determined. The starting powder of the coatings was titanium powder mixed with boron carbide powder. This powder was prepared for production of Ti-B-C composite coatings on substrates using the ELTEPS technique. The coatings obtained were composed of titanium carbide and titanium diboride. The thickness of the coating obtained by onefold spray was not uniform. The coating obtained by the twofold spray covered the substrate. The coating obtained by threefold spray was still more precise. The thickness of the coating obtained by threefold spray was about 50 μm and its hardness value was about 30.7±4.5 GPa.     

Sliding abrasive wear characteristic of TIG cladded TiC reinforced Inconel825 composite coating

TiC reinforced Inconel 825 alloy matrix composite coating with different weight percentage (20, 40, and 60) of TiC has been produced by TIG cladding process. With the increase in TiC percentage in the produced coating a drastic alteration in the coating morphology perceived predominantly due to the degree of melting of pre-deposited TiC particles. The sliding abrasive wear measured through the height loss of the coated pin extracted from the TiC-Inconel825 composite coatings executed against alumina abrasive wheel show the effect of TiC percentage as well as the sliding velocity during the test. The worn surfaces characterized by SEM suggested that the abrasion wear is predominant for removal of the coating along with delamination through oxidation. The coefficient of friction of the coating assessed against harden steel plate (HRC58) indicated a gradual reduction from 0.71 to 0.60 with the increase in TiC content in the TiC-Inconel825 composite coating.     

TC4合金表面氩弧熔覆TiCp/Ti基复合涂层组织及耐磨性

利用氩弧熔覆技术在TC4合金表面制备出TiC增强的Ti基复合涂层。利用SEM、XRD和EDS分析了熔覆涂层的显微组织;利用显微硬度仪测试了复合涂层的显微硬度;利用摩擦磨损试验机测试了涂层在室温干滑动磨损条件下的耐磨性能。结果表明:氩弧熔覆涂层组织均匀致密,熔覆层与基体呈冶金结合,涂层中有大量的TiC树枝晶和条块状TiC颗粒;复合涂层明显改善了TC4合金的表面硬度,HV平均硬度可达9GPa;复合涂层室温干滑动磨损机制为磨粒磨损和轻微粘着磨损。     

Fabrication and characterization of Ti6A14V/TiB_2-TiC composites by powder metallurgy method

Titanium matrix(Ti6A14V) composites reinforced with TiB_2 and TiC were produced through powder metallurgy method. The effect of addition of both TiB_2 and TiC with different contents(2.5 wt% 5.0 wt% and7.5 wt%) on the density, microstructure and hardness properties of titanium matrix was investigated. The size distributions of the matrix alloy and reinforcement particles were measured by particle size analyzer. Microhardness of the sintered composites was evaluated using Vickers' s hardness tester with a normal load of 3 N and a dwell time of 10 s. Ti6A14V alloy and Ti6A14V/TiB_2-TiC composites were characterized through X-ray diffraction(XRD) and field emission scanning electron microscope(FESEM)equipped with energy-dispersive spectrometer(EDS). The addition of TiB_2 and TiC particles enriches the properties of Ti6A14V alloy. The sintered Ti6A14V/TiB_2-TiC composite features a dense and pore-free microstructure with varying TiB_2 and TiC particle distribution in the metal matrix. The results of this study show that the development of new phases plays a significant role in the properties of these composite materials.     

In-situ laser-fabrication and characterization of TiC-containing Ti–Co composite on pure Ti substrate

This work presents the in-situ fabrication of a layered metal-matrix composite coating on a pure Ti substrate. The coating consists of a matrix of cobalt-titanium intermetallics and the reinforcement phase of titanium carbide. The fabrication process is laser cladding, conducted using a pre-placed powder mixture of elemental titanium, cobalt, and graphite. Several materials characterization methods including microscopy, microhardness and nano-indentation are used to study the coating and coating–substrate interface. The intermetallic phases in the matrix vary from Co-rich phases at the coating surface to Ti-rich compounds near the substrate. The interface is revealed to have a smooth profile, free of any porosity or cracks, with good metallurgical bonding to the substrate. A relatively uniform hardness in the range of 1200–1300 HVN is achieved through a depth of 200 μm into the coating. The hardness then gradually decreases to 480 HVN at the substrate interface, approximately 300 μm from the surface. The hardness evolution, which is predictable using the Rule of Mixtures, is explained by the fraction of the carbide particles and the type of intermetallic compounds in the matrix.