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The deformed layer of specimen F is much thicker than that of E, and is related to wear rate and ratcheting.
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The sub-skin layer of specimens without weld-lines was significantly reduced with increasing amount of EPR-M.
Results of the tests indicate that cementite is the main phase in the surface layer of specimens carburized at 400 and 450 °C, while that in those carburized at 500 and 550 °C is mainly the carbon expanded martensite.
Since the Rietveld calculations were performed on XRD patterns taken when the whole cement specimens, including both the core and the outermost layer of the specimen, were ground and homogenized into a powder, it is likely that the OCP present in all cement specimens actually came only from the periphery of the specimens.
Based on the radial distribution function, they found that the ultimate depth of the deformed layer of a specimen is 5.0 nm.
Based on the radial distribution function, they found that the ultimate depth of the deformed layer of a specimen is 5.0 nm[3 5].
To protect the thin surface layer of the specimen against destruction during cutting and milling, the samples were usually covered by an approximately 100-nm Cr-layer before FIB processing.
In addition, no hardening is observed at the surface layer of the specimen despite the formation of the hydride and hydrogen enrichment.
The oxide protective layer of the specimen treated by 7 LSP impacts is homogeneous and compact without obvious crack, spalling and pits.
These phenomena can be explained by the residual compressive stress formed at the surface layer of the specimen by the fatigue test and the surface roughness of crack section.
The hydrogen concentration at the surface layer of the specimen is evaluated to be above 3500 mass ppm; nevertheless, no fracture associated with the stress-induced martensite transformation occurs.
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