采用激光熔覆技术，在Q235 钢表面分别制备了316L、不同质量分数(5%、10%、13.26%)和不同尺寸(纳米、微米)的316L-SiC 熔覆层。利用光学显微镜(OM)、扫描电子显微镜(SEM)、X 射线能谱仪(EDS)、X 射线衍射仪(XRD)等检测了熔覆层显微组织并分析了强化机制，利用显微硬度计和摩擦磨损试验机分析了熔覆层的横截面硬度分布和表面摩擦磨损性能。结果表明，316L+10%SiC 为适当的添加量。在相同添加量时，微米SiC 发生部分分解，有残留的SiC 相；纳米SiC 发生完全分解，生成新的强化相碳化物M7C3 和硅化物FeSi，新的强化相有效地抑制了柱状晶生长，使熔覆层组织转变为胞状晶，并且抑制了搭接重熔区的g-CrFeNi晶粒长大，其熔覆层硬度最高达到527 HV，比316L熔覆层提高了132%，与微米SiC 熔覆层相比，其硬度提高100 HV 以上，摩擦系数和磨损量均最小，具有优良的抗磨损性能。

The thin surface layers of 316 L stainless steel with different mass fractions (5%, 10%, 13.26%) and sizes (nano, micro) SiC composite powder are deposited on Q235 steel substrates by laser cladding process. Sections of such coatings are examined to reveal their microstructure and properties and to analyze the strengthen mechanism, by using optical microscope (OM), scanning electron microscope (SEM), energy dispersive spectrometer (EDS) and X-ray diffractometer (XRD). The distribution of the hardness on the cross section of cladding layer and wear resistance of the coatings also are tested by microhardness tester and frictional wear tester. The results show that 316L stainless steel with 10% of the SiC is appropriate. With the same proportion, micro SiC just dissolve partly, but some SiC phase exists; while nano SiC will be dissolved totally, producing new strengthening phase M7C and FeSi, which can effectively inhibit the growth of the columnar crystal, and change the microstructure of the cladding layer for cellular crystal, also restrain the growth of g-CrFeNi grain in the overlapping remelting area, the coating hardness reaches 527HV increase by 132% compare with the pure 316L coating; the coating hardness is higher than 100HV, compare with the cladding layer with the addition of 10% micro SiC, and the friction coefficient and wear weight loss are minimal, which leads excellent wear resistance.