Interfacial Characterization and Surface Wear Mechanism of Ti(C, B)/Ni60A Composite Coating Prepared by In Situ Extra High-Speed Laser Cladding
XU Yifei1,2, ZHANG Nan1,2(), XU Peixin2, DU Borui1,2, SHI Hua2, WANG Miaohui2
1 Beijing National Innovation Institute of Lightweight Ltd., Beijing 100083, China 2 China Machinery Institute of Advanced Materials Co. Ltd., Zhengzhou 450001, China
Cite this article:
XU Yifei, ZHANG Nan, XU Peixin, DU Borui, SHI Hua, WANG Miaohui. Interfacial Characterization and Surface Wear Mechanism of Ti(C, B)/Ni60A Composite Coating Prepared by In Situ Extra High-Speed Laser Cladding. Acta Metall Sin, 2024, 60(12): 1721-1730.
H13 die steel easily fails under friction and wear due to its low purity, poor homogeneity, and unreasonable matching between strength and toughness. The preparation of wear-reducing and wear-resistant coatings through extra high-speed laser cladding (EHLA) is important for the restoration and remanufacturing of metallurgical spare parts. This method provides an solution for the in-service life extension of H13 die steel. However, cracking at the EHLA interfaces induced by residual stresses due to low substrate dilution rates, remarkable cooling rates, and differences in thermal expansion between dissimilar metals acts as a limitation to the application of EHLA. This work aimed to alleviate stress mutation at the fusion interface of EHLA coatings, improve the fusibility of EHLA coatings on H13 die steel, and obtain wear-reducing and abrasion-resistant features on the surfaces of EHLA coatings. In this study, a Ti(C, B)/Ni60A composite coating was prepared with almost defect-free microstructures on an H13 die steel substrate by coupling EHLA with direct reaction synthesis to introduce an in situ exothermic reaction into EHLA cladding to achieve the above aims. The obtained material was compared with the pure Ni60A coating prepared through EHLA alone. Residual stress distribution at the fusion interface of the Ti(C, B)/Ni60A composite and Ni60A coatings was determined using the Giannakopoulos & Suresh (G&S) energy method based on nanoindentation. SEM, EDS, and EBSD were performed to investigate the microstructures, phase compositions, and characteristics of the two coatings and cladding interfaces. A focused ion beam setup was used to obtain information on the superficial wear of the two samples, and double spherical aberration TEM was conducted to analyze the superficial wear characteristics of the two coatings. The superficial wear mechanism of the Ti(C, B)/Ni60A composite coating was determined along with the changes in the surface microhardness of the two coatings.Results revealed that the Ti(C, B)/Ni60A composite coating interface was affected by the emission of approximately 670 kJ Joule heat by the in situ reaction of Ti and B4C. The interfacial width of the coatings reached 22 μm, which was 11 times that of the Ni60A coating prepared through EHLA (2 μm). This increase effectively reduced the stress gradient in the interfacial region and alleviated the stress mismatch on both sides of the interface. However, the surface hardness of the Ti(C, B)/Ni60A composite coating was only 360-400 HV0.2, which was less than half of that of the Ni60A coating. The wear losses of the two materials were in the same order of magnitude owing to the support provided to the Ti(C, B)/Ni60A composite coating matrix by the in situ authigenic TiCB, Ti3B4, and other phases. Such support reduced abrasion and conferred wear resistance. The above observation was also a result of the formation of equiaxed ultrafine grains at a depth of 180 nm below the wear surface area through the coupling of the plastic rheology-heat-force fields. This phenomenon dynamically strengthened the worn surface.
Fund: National Key Research and Development Program(2021YFB3702003);National Natural Science Foundation of China(51975240);Beijing Natural Science Foundation(2222093);Technical Development Foundation of China Academy of Machinery Science and Technology Group(812201Q9)
Table 1 Preparation methods and particle size of pre-alloyed powders, and EDS results of points 1-3 in Fig.1
Fig.2 Interfacial zone morphologies of Ti(C, B)/ Ni60A composite coating with EDS distribution of Ni (a) and Ni60A coating (b)
Fig.3 Backscattered electron (BSE) morphologies of Ni60A coating (a); columnar crystals (b) and equiaxial crystals (c) of Ti(C, B)/Ni60A composite coating and the corresponding EBSD (red area—TiCB phase, green area—Ti3B4 phase, and yellow area—TiCrB4 phase) (d) and kernel average misorientation (KAM) map (e)
Fig.4 Residual stress distribution on the cross section of coating by ultra-high speed laser cladding
Fig.5 Surface wear morphologies of Ti(C, B)/Ni60A composite coating (a), Ni60A coating (b), and H13 steel (c)
Fig.6 Double spherical aberration-transmission electron microscopy (DSA-TEM) images of Ti(C, B)/Ni60A composite coating based on focused ion beam (FIB) fabricated sample and in situ reactive particle phase analyses (a, b) DSA-TEM (a) and local magnified (b) images (c) corresponding high magnified image of Fig.6b and in situ reactive particle phase analyses (c1-c6) EDS mappings of B (c1), Ti (c2), Ni (c3), C (c4), Cr (c5), and Al (c6) (d1, d2) SAED patterns of corresponding positions shown in Fig.6c
Fig.7 DSA-TEM image of the worn surface of Ni60A coating based on FIB sample (a), selected high-resolution image (b), and corresponding inverse fast Fourier transforms and fast Fourier transforms (insets) of specific regions in Fig.7b (c-f)
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