“…noting that in the case of specimens subjected to dispersed laser hardening, UBS and εf of specimens treated by LDQ are about 1086.2 MP and3.8%, significantly higher than those observed in specimens treated with LCQ. Compared to LCQ treatment, selective laser hardening in graphical form not only enhances the material's bending yield strength (σb0.2) but also its ultimate bending yield strength (UBS) [23,25,26]. Moreover, the fracture strain is notably increased by dispersed laser heat treatment, indicating exceptional plastic deformation capabilities during bending, consistent with previous studies.…”
Section: Sliding Wear Behaviorssupporting
confidence: 88%
“…This is attributed to the presence of fine carbide particles, which impede stress release through slip and thus induce relative rotation deformation for stress relaxation and specimen continuity maintenance. In Figure17(c), the smaller-sized carbides and martensitic matrix remain unchanged in shape, while a minor fraction of carbides undergo noticeable deformation[25,27]. Undistorted carbides with a diameter of approximately 1 μm are still observable at the hardening unit, indicating significant deformation differences between the substrate and the hardening unit during bending processes.…”
“…noting that in the case of specimens subjected to dispersed laser hardening, UBS and εf of specimens treated by LDQ are about 1086.2 MP and3.8%, significantly higher than those observed in specimens treated with LCQ. Compared to LCQ treatment, selective laser hardening in graphical form not only enhances the material's bending yield strength (σb0.2) but also its ultimate bending yield strength (UBS) [23,25,26]. Moreover, the fracture strain is notably increased by dispersed laser heat treatment, indicating exceptional plastic deformation capabilities during bending, consistent with previous studies.…”
Section: Sliding Wear Behaviorssupporting
confidence: 88%
“…This is attributed to the presence of fine carbide particles, which impede stress release through slip and thus induce relative rotation deformation for stress relaxation and specimen continuity maintenance. In Figure17(c), the smaller-sized carbides and martensitic matrix remain unchanged in shape, while a minor fraction of carbides undergo noticeable deformation[25,27]. Undistorted carbides with a diameter of approximately 1 μm are still observable at the hardening unit, indicating significant deformation differences between the substrate and the hardening unit during bending processes.…”
“…1,2 Despite their widespread use, these welding methods often encounter a significant challenge: the weld thermal cycles and subsequent post-weld heat treatment (PWHT) can result in a non-uniform surface hardness zone spanning tens of millimetres. 3 This zone comprises both hardened and softened subzones, 4 leading to mechanical property discrepancies between the joined region and the steel rail itself. 5,6 Additionally, these welded joints are required to withstand the same load of rolling contact fatigue as the high-strength steel rail during their service.…”
U75V rail steel rods underwent continuous-drive friction welding (CDFW). Joint properties were evaluated through microstructural analysis and mechanical testing (tensile, impact, and microhardness). The thermo-mechanical behaviour of the CDFW process was simulated by the finite element method, while a computed continuous cooling transformation diagram was used to predict phase transformation, microstructures, and hardness variations. By reducing the spindle speed to 1000 r/min, the peak temperature in the weld centre zone (WCZ) remained below Ac1. Microstructures in WCZ exhibited a high density of geometrically necessary dislocations. The joints demonstrated comparable tensile strength, impact toughness, and microhardness to BM, with underlying mechanisms elucidated. This study showcases CDFW's potential in achieving rail steel joints with quasi-equal strength and toughness to the BM.
“…The study of the decay of martensite, perlite and quasi-perlite structures has been carried out in a number of works [25][26][27][28][29]. Pereira H.B.…”
The previously unknown process of homogeneous and heterogeneous crystallization of FeC iron monocarbide and its co-crystallizations with ε-carbide Fe2C from a supersaturated solid solution based on ε-carbide Fe2C or polycarbide quasi-eutectic formed in the process of peritectoid decomposition during prolonged heating (isothermal annealing) of the lamellar eutectoid ledeburite in cast eutectic white iron has been investigated. Crystallization of 2D monolayers of FeC monocarbide allotropes in the form of translucent extended and elastic crystalline nanofilms has been experimentally proved. The carbide phases in white cast iron can be characterized as a single isomorphic and isostructural quasi-carbide solid solution, which structurally crystallizes as a mixture of carbide phases as a quasi-eutectic, in which the carbon content is free to vary widely without indentification of the carbide phases proper. The decomposition product of the lamellar eutectoid as a result of peritectoid transformation during isothermal annealing is polycarbide with a gradient crystal lattice of solid solutions corresponding in carbon concentration to this or that carbide.
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