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The analysis shows that in the coating, TiB2 and TiB phases appeared as hexagonal or rectangular shape, whereas TiC as spherical shape within the matrix of unreacted Ti, Ti-6Al-4V alloy form the substrate and intermetallic phase like TiAl3 formed during the cladding process.
The superalloy grains are deformed during the cladding process with several slip systems appearing.
X-Ray diffraction and scanning electronic microscopy results show that TiC and WC phases were in situ synthesized during the cladding process and they appear in a Ni Al matrix.
However, during the cladding process, WC particles tend to fall down to the bottom of the melted coating, and as a consequence, the percentage of carbides increases near the interface with the C45E steel substrate, and decreases on the top of the coating.
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The laser energy input is another factor influencing the cladding process.
The dilution rate is the key factor influencing the cladding process.
The results showed that TiC carbides were formed via in situ reaction between ferrotitanium and graphite in the molten pool during the laser-clad process.
The results indicated that, Al/Ti3Al2N2-Ti3Al coatingte canting can successfully form on Ti surface during GTAW cladding process.
The model is tested experimentally for the laser cladding process in two different set-ups.
Results showed that the laser cladding process can form a strong metallurgical bonding at the interface between the substrate and the clad coating.
Over the past decade, researchers have demonstrated interest in tribology and prototyping by the laser cladding process.
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