本文以CoCrFeNi高熵合金为基体粉末，采用激光熔覆技术在Q235钢表面分别制备了原位碳化物、硼化物和碳/硼化物增强的高熵合金涂层。表征了涂层的物相组成、显微组织、元素分布、晶粒尺寸及析出相形貌。此外，测试了涂层的显微硬度、摩擦磨损性能和耐腐蚀性能，研究了原位增强相对高熵合金涂层组织与性能的影响。具体研究内容和结果如下：

       采用激光熔覆制备了不同Ti和C含量的高熵合金涂层，研究了Ti和C元素添加对高熵合金涂层组织和性能的影响。研究表明，CoCrFeNi高熵合金涂层为单相FCC固溶体。由于高熵合金的晶格畸变效应，导致基体相的晶格常数增大。随着Ti和C元素添加，涂层中生成了原位TiC和Cr₇C₃增强相，并主要以块体形式沿晶界和晶内分布。此外，原位碳化物的产生提高了形核率，细化了晶粒尺寸。高熵合金基体和TiC之间的取向关系被确定为基体相(1-1-1 )//TiC(1-1-1 )，基体相[110]//TiC[-1-1 0]。固溶强化、第二相强化、细晶强化的协同作用使高熵合金涂层的硬度和耐磨性得到显著提高。然而，生成过量的增强相会导致在磨损的过程中碳化物剥落，使得涂层的磨损反而加剧。

       在高熵合金涂层中制备了原位硼化物，并研究了原位硼化物对高熵合金涂层的物相组成、组织演变、元素分布、显微硬度及摩擦磨损性能的影响。结果表明，在高熵合金中引入Ti和B元素可以形成原位TiB，Cr₂B，FeCrB，(FeCr)₂B增强相。大量的硼化物在高熵合金涂层中生成提高了形核率，使高熵合金涂层的组织逐渐细化，由粗大的柱状晶和树枝晶向细小的树枝晶和等轴晶转变。由于多种强化机制的影响，导致涂层的显微硬度和摩擦磨损性能都有显著提升。然而，涂层中产生过多的硼化物反而会导致磨损量增大。Cr₂B相与高熵合金基体相之间的晶体学位向关系为基体相(002)//Cr₂B(-1-3-1 )，基体相[-510]//Cr₂B[01-3]。随着原位硼化物含量的增加，涂层的磨损机制由粘着磨损逐渐转变为磨粒磨损和粘着磨损。

       通过添加不同含量的Ti、C和B元素制备出原位碳/硼化物增强的高熵合金涂层，研究了高熵合金涂层的物相组成、显微组织演变、显微硬度、摩擦磨损性能及耐腐蚀性能。研究发现，高熵合金涂层中的原位碳化物和硼化物随着Ti、C和B元素添加量的增大而增多。Ti、C和B元素加入后，高熵合金涂层显微组织转变为枝晶和枝晶间组织，并且在枝晶间区域生成了原位碳化物和硼化物。原位增强相的形成使高熵合金涂层的显微硬度和摩擦磨损性能显著提升。高熵合金涂层的磨损机制以粘着磨损、磨粒磨损和氧化磨损为主。不同高熵合金涂层在3.5 wt% NaCl溶液中表现出不同的耐腐蚀性，其中未添加Ti、C和B元素的涂层的耐腐蚀性能最佳。由于Ti、C和B元素添加后，涂层中生成了富Fe和Cr元素的碳硼化物消耗了耐腐蚀的Cr元素，导致涂层的耐腐蚀性能下降。

       In this paper, high-entropy alloy (HEA) coatings reinforced by in-situ carbides, borides and carbon/borides were prepared on the surface of Q235 steel by laser cladding using CoCrFeNi HEA as matrix powder. The phase composition, microstructure, element distribution, grain size and precipitated phase morphology of the coating were characterized. In addition, the microhardness, friction and wear properties and corrosion resistance of the coatings were tested. The effects of in-situ reinforced phases on the microstructure and properties of HEA were studied. The specific research contents and results are as follows:

       HEA coatings with different Ti and C contents were prepared by laser cladding. The effects of Ti and C addition on the microstructure and properties of HEA coatings were studied. The study reveals that the CoCrFeNi HEA coating exhibit a single-phase FCC structure solid solution. Due to the lattice distortion effect of HEA, the lattice constant of the matrix phase increases. With the addition of Ti and C elements, in-situ TiC and Cr₇C₃ reinforced phases were formed in the coating, and mainly distributed along the grain boundary and intragranular in the form of blocks. In addition, the formation of in-situ carbides increases the nucleation rate and refines the grain size. The orientation relationship between the HEA matrix and TiC is determined as the matrix phase (1-1-1 )//TiC(1-1-1 ) and the matrix phase [110]//TiC[-1-1 0]. The hardness and wear resistance of the HEA coating are significantly improved by the synergistic effect of solid solution strengthening, second phase strengthening and fine grain strengthening. However, the formation of excessive reinforced phases will lead to the spalling of carbides during the wear process, which will aggravate the wear of the coating.

       In-situ borides were prepared in HEA coatings, and the effects of in-situ borides on the phase composition, microstructure evolution, element distribution, microhardness and friction and wear properties of HEA coatings were studied. The results show that in-situ TiB, Cr₂B, FeCrB, (FeCr)₂B reinforced phases can be formed by introducing Ti and B elements into HEA. The formation of a large number of borides in the HEA coating increases the nucleation rate, so that the microstructure of the HEA coating is gradually refined, from coarse columnar crystals and dendrites to fine dendrites and equiaxed crystals. Due to the influence of various strengthening mechanisms, the microhardness and friction and wear properties of the coating are significantly improved. However, excessive boride produced in the coating will lead to an increase in wear. The crystal orientation relationship between Cr₂B phase and HEA matrix phase is matrix phase (002)//Cr₂B(-1-3-1 ), matrix phase [-510]//Cr₂B[01-3 ]. With the increase of in-situ boride content, the wear mechanism of the coating gradually changed from adhesive wear to abrasive wear and adhesive wear.

       In-situ carbon/boride reinforced HEA coatings were prepared by adding different contents of Ti, C and B elements. The phase composition, microstructure evolution, microhardness, friction and wear properties and corrosion resistance of HEA coatings were studied. It was found that the in-situ carbides and borides in the HEA coating increased with the increase of Ti, C and B elements. After the addition of Ti, C and B elements, the microstructure of the HEA coating is transformed into dendrite and interdendritic structure, and in-situ carbides and borides are formed in the interdendritic region. The formation of in-situ reinforced phases significantly improves the microhardness and friction and wear properties of the HEA coating. The wear mechanism of HEA coating is mainly adhesive wear, abrasive wear and oxidation wear. Different HEA coatings show different corrosion resistance in 3.5 wt% NaCl solution, and the coating without Ti, C and B elements has the best corrosion resistance. Due to the addition of Ti, C and B, the formation of carbon borides rich in Fe and Cr elements in the coating consumes the corrosion resistance element Cr, resulting in a decrease in the corrosion resistance of the coating.

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