微束等离子喷涂Mo涂层

采用微束等离子喷涂方法在Q235上制备了Mo涂层.研究喷涂电流、喷涂距离对涂层组织结构和性能的影响.采用光学显微镜观察涂层的组织结构并计算孔隙率,测试涂层的显微硬度和结合强度,并记录粉末沉积率.结果表明,在本试验条件下微束等离子喷涂电流与喷涂距离对涂层组织和性能产生较大的影响.适当工艺参数条件下粉末沉积率高于80 %,可以获得显微硬大于400 HV_(0.1),平均结合强度仍然大于40 MPa的涂层.     

微束等离子喷涂制备羟基磷灰石涂层

采用微束等离子喷涂系统制备羟基磷灰石涂层,通过扫描电子显微分析(SEM)和X射线衍射分析(XRD)对涂层形貌、相组成和结晶度进行了研究.结果表明,随着喷涂电流和离子气流量的增加,羟基磷灰石粒子的熔化和撞击后的铺展更充分,在70～130 mm范围内随着喷涂距离的增加粒子熔化程度增加.适当的喷涂工艺条件下微束等离子喷涂制备羟基磷灰石涂层的结晶度可以相当或高于传统大气等离子喷涂制备的涂层,有利于涂层在体液环境中稳定性的提高.     

热处理对微束等离子喷涂羟基磷灰石涂层的影响

羟基磷灰石由于其良好的生物活性,被广泛的用作医用植入体的表面涂层材料.采用微束等离子喷涂(Microplasma Spraying,MPS)I艺在Ti-6Al-4V基体上制备羟基磷灰石涂层,通过扫描电镜(SEM)、X射线衍射(XRD)和傅里叶红外光谱(FTIR)分析了热处理对涂层相组成和表面形貌的影响规律.研究表明:微束等离子喷涂制备的羟基磷灰石涂层在经过热处理后结晶度提高,并且非晶相和杂质相转化成为HA结晶相.同时,羟基和磷酸根的完整性得到了恢复.过高的热处理温度易引起涂层裂纹等缺陷的增加,也容易造成羟基脱离造成HA分解.合理的热处理温度范围为600～700℃,保温时间为3 h.     

微束等离子喷涂氧化锆增韧羟基磷灰石复合涂层

采用微束等离子喷涂方法,在Ti-6Al-4V基体上制备了羟基磷灰石 氧化锆(70HA-30ZrO2,质量分数,%)复合涂层.将复合涂层置于模拟体液中分别浸泡了3,7,14,28 d并观察表面磷灰石的生长情况以评价涂层生物活性.采用扫描电镜(SEM)和X射线衍射(XRD)分析技术对涂层浸泡前后的表面形貌和相组成进行了研究.结果表明,涂层中ZrO2主要以立方相存在;喷涂过程中羟基磷灰石(HA)出现了一定的分解,产生大量的α-Ca3(PO4)2杂质相.HA涂层熔化效果很好,但涂层中有未熔化的ZrO2颗粒.涂层在模拟体液中浸泡28 d后表面可以形成磷灰石,说明涂层具有很好的生物活性.     

微束等离子喷涂羟基磷灰石涂层的体外生物活性研究

采用微束等离子喷涂(MPS)方法在Ti6A14V基体上制备羟基磷灰石(HA)涂层.利用扫描电镜(SEM)和x射线衍射(XRD)分析技术对HA涂层的表面形貌、相组成和结晶度进行表征,并通过模拟体液进行体外生物活性试验.结果表明,微束等离子喷涂制备的HA涂层具有一定粗糙度,存在气孔以及微裂纹.涂层存在热分解现象,涂层中含有HA、α-TCP、β-TCP和非晶相,不含CaO等杂质相.模拟体液试验表明,微束等离子喷涂工艺制备的HA涂层具有较好的生物活性和稳定性.涂层表面均有较大比例的CaP沉积层,且涂层整体保持完整,没有出现明显的剥离.     

等离子喷涂-重熔NiCrBSi涂层的显微组织与耐磨性能

采用等离子喷涂和等离子重熔技术,在2Cr13基体表面制备2mm厚的自熔性NiCrBSi涂层。利用扫描电镜、X射线衍射仪和能谱仪研究涂层形貌、微观组织和微区成分的演变规律,采用拉伸和硬度试验测试涂层的结合强度和显微硬度,通过室温和高温摩擦磨损试验评价和比较涂层与基体的耐磨性能。结果表明,重熔前后涂层都是由γ-Ni固溶体以及Ni₃B,CrB,Cr₂B,Cr₇C₃和Cr₂₃C₆等组成;重熔涂层由层状喷涂态转变为致密的铸造态,涂层组织和力学性能大大提高,结合强度和显微硬度分别高达200MPa和1010HV。重熔涂层的耐磨性显著优于2Cr13基体,其600℃时的磨损体积仅为基体的20%。     

微束等离子喷涂气体对HA涂层结晶度的影响

采用微束等离子喷涂方法,分别选用工业纯氩气和含50%氦气的氦氩混合气体为工作气体,在Ti-6Al-4V基体上制备羟基磷灰石涂层.通过SEM和XRD对涂层形貌、相组成和结晶度进行研究.结果表明,两种工作气体均可以制备杂质相含量少且不产生TTCP(磷酸四钙)和CaO等杂质相的涂层,结晶度高于70%,对植入体在体内的稳定性有利.采用氦氩混合气体为工作气体的微束等离子弧热焓值高于氩气工作气体,前者涂层中的结晶相主要以再结晶的为主,后者结晶相以大量未熔HA内核为主.     

微束等离子喷涂制备羟基磷灰石涂层微观结构的特征研究

目的 通过与大气等离子喷涂和超音速火焰啧涂的对比,研究微束等离子喷涂制备的羟基磷灰石涂层的微观组织特点.方法 以高结晶度的羟基磷灰石粉末为原料,采用三种不同的喷涂方法(微束等离子喷涂、大气等离子喷涂和超音速火焰喷涂),在Ti-6Al-4V基体上制备羟基磷灰石(HA)涂层.利用冷场发射扫描电子显微镜和X射线衍射仪,对三种涂层的形貌、相组成和择优取向进行分析.结果 与大气等离子喷涂及超音速火焰喷涂制备的涂层相比,应用该设备制备的羟基磷灰石涂层表面平整致密,无大量的气孔存在;涂层截面呈典型的层状结构,在近三分之一表面处观察到柱状晶;涂层中仅有少量的非晶相及分解相,结晶度高达90％以上.这些特征均有利于羟基磷灰石涂层在体液环境中的稳定性.结论 比较三种喷涂方法,采用微束等离子喷涂制备的羟基磷灰石涂层致密,结晶度高,杂相少,且存在择优取向的柱状晶.     

等离子喷涂制备典型涂层研究进展

从航空航天到交通运输、电子设备和医疗器械等,大大小小的行业中均可见到涂层的应用,涉及到这些领域的涂层种类主要有耐磨、耐蚀涂层、热障涂层、压电陶瓷涂层和生物陶瓷涂层等。等离子喷涂技术具有喷涂材料范围广、工艺简单等优点,是制备上述典型涂层的常用工艺方法。虽然同种工艺可制备出不同种类涂层,但由于所选的喷涂材料、喷涂参数不同,所获得的涂层性能和涂层结构之间也存在着一定差异,须对等离子喷涂各类涂层的研究进行分析与总结。基于此,文中简要介绍了国内外等离子喷涂涂层的应用现状,之后从不同种类涂层功能需求和技术特点出发,分析喷涂工艺对涂层结构和性能的影响。最后对提升涂层性能的工艺方法进行总结,并对今后等离子喷涂涂层技术的发展趋势进行了展望。     

HA粉末粒径对微束等离子喷涂扁平粒子形貌及涂层微结构的影响

目的研究粉末粒径对微束等离子喷涂羟基磷灰石(HA)扁平粒子形貌和涂层的微观组织结构的影响。方法选取三组不同粒径范围(25～38μm、38～45μm、45～63μm)HA球形粉末,采用微束等离子喷涂方法在经镜面抛光的Ti-6Al-4V基体上收集扁平粒子,在经过喷砂处理的Ti-6Al-4V基体上沉积HA涂层。利用冷场发射扫描电子显微镜和X射线衍射仪,对扁平粒子形貌,以及涂层的形貌、相组成和择优取向进行分析。通过激光共聚焦显微镜(LSCM)观察扁平粒子的三维相貌,并对比分析扁平粒子的差异。结果微束等离子喷涂过程中,可形成几种典型形貌特征的扁平粒子,一是中间区域较厚,边缘位置较薄的扁球形;二是中间区域较薄,边缘位置较厚的圆盘状,该种扁平粒子相比于扁球形,其厚度较薄,直径较大;三是边缘位置存在"指状"溅射的圆盘状,其厚度与圆盘状扁平粒子厚度相当,但其直径范围较大。HA涂层的结晶度随着粉末粒径的减小而减小,HA的分解和非晶化逐渐增强,涂层的择优取向强度减弱,涂层中柱状晶比例减少。结论微束等离子喷涂过程中,粉末粒径对扁平粒子形貌和涂层相结构有显著影响。随着粒径的增加,扁平粒子由扁球形转变为边缘有少量"指状"溅射的圆盘状。粒径较小的HA粉末在等离子焰流中的熔化程度较高,导致涂层中分解相和非晶相含量增多,择优取向程度减小。     

WC-12Ni/NiCrBSi爆炸喷涂涂层制备及其滑动磨损特性

利用爆炸喷涂方法制备了不同比例的WC-12Ni/NiCrBSi涂层,研究了NiCrBSi含量对涂层的组织形貌、硬度与结合强度的影响,用扫描电镜和能谱仪分析了涂层的滑动磨损行为.结果表明:由于NiCrBSi的加入,改善了WC颗粒的熔融状态,提高了涂层的结合力,涂层中含15%的NiCrBSi时,可以明显的提高涂层的磨损抗力.     

等离子喷涂纳米氧化锆涂层摩擦性能研究

利用大气等离子喷涂技术,在不锈钢基体上用不同颗粒尺寸的纳米粉末制备了两种纳米氧化锆涂层S1(平均粒度较小颗粒的喷雾造粒粉末所得)和B1(平均粒度较大颗粒的喷雾造粒粉末所得).运用XRD、SEM、TEM、拉曼光谱和金相技术等分析手段对喷涂用的粉末原料和涂层的显微结构、物相组成进行了观察与确定;利用环-块摩擦试验在干摩擦条件下对涂层的摩擦磨损性能进行了测试.结果表明,两种氧化锆涂层的摩擦系数均随载荷增大而减小.在较低载荷(100 N)条件下,S1涂层与不锈钢的摩擦系数低于B1涂层与不锈钢的摩擦系数;而在较高(400 N)载荷下,两种氧化锆涂层的摩擦系数开始趋于一致.其原因在于:较低的载荷下两种涂层与不锈钢摩擦副的摩擦磨损机制不同,S1涂层的磨损属于粘着磨损,B1涂层的磨损属于磨粒磨损;而在较高载荷下,两种涂层的磨损机制趋于一致,均为粘着磨损.     

热喷涂NiCrBSi基耐磨涂层的研究进展

磨损失效是工业生产及材料使用寿命最主要的消耗方式之一,通过热喷涂表面涂层技术提高摩擦副表面摩擦磨损性能受到越来越多的关注。作为一种重要的表面处理技术,热喷涂在防腐、耐磨等方面均有出色的表现。NiCrBSi是以Ni、Cr为主要组元的Ni基自熔性合金,近年来,NiCrBSi基涂层在制备方法、性能表征和应用推广等方面都取得了重要进展。本文主要论述了热喷涂NiCrBSi和NiCrBSi-Mo涂层的自润滑性能、NiCrBSi-碳化物涂层的硬质相增强效果、NiCrBSi-氧化物涂层综合性能等方向的研究现状,分别对火焰重熔、激光重熔、炉内重熔及感应重熔NiCrBSi基涂层的原理、特点及相关应用实例进行了阐述,分析了这四种后处理重熔态涂层结构与磨损性能,着重比较添加组元和重熔工艺对涂层的组织结构、力学性能和耐磨损性能等方面的影响规律,并阐明了各自在机理上的异同。最后总结了NiCrBSi基耐磨涂层研究面临的主要问题,并针对这些问题,从材料、工艺和后处理方面提出了三点展望性建议。     

Tribological behavior and mechanism of NiCrBSi–Y2O3 composite coatings

The NiCrBSi–Y₂O₃ composite coatings were prepared on the surface of 45 carbon steel by plasma spray, the microstructure and tribological properties of the coatings were investigated. The results show that the NiCrBSi–Y₂O₃ composite coatings are mainly composed of γ-Ni, CrB, Cr₇C₃ and Y₂O₃. With addition of Y₂O₃, hard phases such as CrB, Cr₇C₃ emerge in composite coating, and the density of the composite coatings also increases. The NiCrBSi–0.5Y₂O₃ composite coating presents excellent tribological properties. Its friction coefficient is 0.175, which is about 37% of that of the pure NiCrBSi coating. The mass wear loss is 1.2 mg, which is reduced by 43% compared with the pure NiCrBSi coating. When the loads are 6–10 N, the NiCrBSi–0.5Y₂O₃ composite coating suffers from slight wear and the wear mechanisms are mainly adhesive wear accompany with slight micro-cutting wear and micro-fracture wear. As the load increases to 12 N, the wear mechanisms are adhesive wear and severe micro-cutting wear.     

Quality of coatings produced by microplasma spraying

Summary

The purpose of this paper is to clarify welded joint performance, especially the impact properties of the weld metal produced by heavy‐current electroslag welding (ESW) and submerged‐arc welding (SAW), with special reference to the high heat input welding processes generally applied in the fabrication of four‐sided thick‐plate box columns. Two types of SM490A 40 mm thick plates were used in the tests. The results obtained may be summarised as follows:

1. The impact properties of the high heat input weld metal produced under standard conditions (thickness of 40 mm) are generally such that ESW has a lower absorbed energy value (vE value) than SAW.

2. The impact value of ESW high heat input weld metal is non‐uniform, and distinctive impact properties are found. That is to say, the vE value of the weld metal core is lower than that of the weld metal rim.

3. ESW weld metal macrostructures have a non‐uniform morphology in both the core and rim. That is to say, a fine‐grained columnar zone is generated in the core and a coarse‐grained columnar zone in the rim.

4. The results presented above in (1) and (2) suggest that the fine‐grained columnar zone in the ESW weld metal core has a low absorbed energy value (vE value) and that the coarse‐grained columnar zone in the rim conversely has a high one. This conflicts with what is conventionally stated about effects of grain size in otherwise identical microstructures, i.e. that the vE value decreases with an increasing grain size.

5. The vE value of ESW weld metal tends to decrease in relation to the welding heat input Q. That is to say, it tends to have a low value at Q > 30.0 kJ/mm (up to around 80.0 kJ/mm).

6. The analyses of the gas composition and five principal elements of the ESW weld metal at different Q values suggest that there is little change in relation to any heat input change. This suggests that the decrease in the vE value in relation to the welding heat input Q is not due to a change in the weld metal composition.

     

Microstructures and erosion resistance of plasma-sprayed WCp/NiCrBSi composite coatings

WCp/NiCrBSi composite coatings have been deposited by plasma spraying with the mixed powders of WC-12Ni and NiCrBSi. The coatings consist mainly of WC, γ-Ni, Ni3B, CrB, Cr2B, M7C3, M23C6 and W2C phases. The W2C content increases with increasing WC mass fraction in the powders. The porosity and microhardness of the coatings are related to the coating WC content. The excessive WC results in decreasing the microhardncss due to increasing the porosity. The WCp/ NiCrBSi coating with 35 % WC mass fraction powder has more excellent erosion resistance. With an increase of impact angles from 15°to 90°the erosion rate of the coating increases, the erosion rate at 15°impact angle being approximately two times lower than that at 90°impact angle. Based on the wear morphology of the coatings at different impact angles, the wear mechanisms were discussed.