5.1 Introduction

Murch, Graeme E.; Bruff, C. M.

doi:10.1007/10390457_56

Cited by 7 publications

(6 citation statements)

References 2 publications

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“…19) Therefore, there would form a sharp peak of C profile in the SUS304 layer next to the initial interface, as schematically drawn in Fig. 8(a), a feature of which was indeed observed for weld joints of ferritic-steel/austenitic-steel.…”

Section: Carbide Formation and Element Diffusion Behav-mentioning

confidence: 59%

Microstructure Evolutions at Severely-deformed Austenite/Martensite Interfaces of a Layer-integrated Steel

et al. 2009

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The microstructure evolution at interfaces of a layer-integrated steel sheet artificially constructed by ductile austenitic stainless (SUS304) and high-strength martensitic (SCM415) steel layers, which were bonded through a cold-rolling and a subsequent annealing at 1 000°C, has been investigated using scanning transmission electron microscopy (STEM) combined with energy dispersive X-ray spectroscopy (EDS). We find that a significant microstructural reconstruction around the SUS304/SCM415 interface has been accomplished during a short-time annealing followed by water-quenching; the resultant microstructures are found to consist of recrystallized austenite and lath martensite grains for the SUS304 and SCM415 layers, respectively. Interestingly, the original SUS304/SCM415 interface appears to migrate and extend into the SUS304 side, an occurrence of which can be reasonably explained by the martensitic transformation across the composition-gradient interface during quenching. These microstructural evolutions fairly account for a microscopic mechanism on how hetero-interface bonding can be achieved via simple cold-rolling/annealing procedures.KEY WORDS: steels; interface structure; scanning transmission electron microscopy; phase transformation; severe plastic deformation.observed microstructural features, we will discuss how the strong-bonding between the austenite/martensite heterointerface can be accomplished during the annealing-quenching procedures. Experimental ProcedureThe multi-layered steel was produced by a cold rolling process with reduction of about 60 % in total thickness, and then annealed at 1 000°C for 1-10 min followed by quenching into water. As shown in Fig. 1, the outer two layers (0.16 mm in thickness after rolled) are composed of commercial-grade stainless steel SUS304, and the inner layer (0.33 mm in thickness after rolled) is composed of commercial-grade martensitic steel SCM415. Compositions of SUS304 and SCM415 are summarized in Table 1. Details of the manufacturing process of the multi-layered steel are described in elsewhere.13) The as-rolled and annealed samples were cut into small pieces, polished by SiC abrasive paper, and thinned by a Gatan PIPS ion mill or focused ion beam system for transmission electron microscopy (TEM) and STEM observations. TEM, STEM, and EDS analysis were performed using a JEOL JEM-2010F field emission gun microscope at acceleration voltage of 200 kV. Composition mapping analysis was constructed by using C-K, O-K, Si-K, Mn-K, Cr-K, Fe-K, Ni-K, and Mo-L lines. Results Microstructure Changes around the InterfaceFigures 2(a)-2(d) show bright-field (BF) STEM images of the SCM415/SUS304 interfaces. For the as-rolled specimen, the microstructures are found to be composed of heavily deformed fine grains both in the SUS304 and SCM415 layers, in which the grains are significantly elongated with large aspect ratios along the roll direction (RD). In particular, the grains in the SUS304 layer, which are composed of deformed austenite and strain induced martensite, exhibit l...

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Section: Carbide Formation and Element Diffusion Behav-mentioning

confidence: 59%

Microstructure Evolutions at Severely-deformed Austenite/Martensite Interfaces of a Layer-integrated Steel

et al. 2009

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“…9 They are both, however, less than that for the bulk diffusion coefficient (1.8 eV) at high temperatures. 12 Previous analysis suggests that interdiffusion in the gold-nickel thin-film system is characterized principally by type B kinetics. 3 Here also diffusion along the boundary is accompanied by lateral leakage of the diffusant by volume diffusion, but the extent of this leakage is limited to distances much smaller than the grain size so that no overlapping of the diffusion fields from the neighbouring boundaries occurs and the boundaries can be considered as essentially isolated.…”

Section: Resultsmentioning

confidence: 99%

Grain boundary diffusion coefficients in gold–nickel thin films

Abdul-Lettif

2003

Surface & Interface Analysis

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“…In fact, microwave sintered compacts attained nearly full (>98.5%) density at 1450 • C. The increase in densification with increasing temperature can be attributed to the greater diffusivity of W in the binder. It has been reported [25,26] that the diffusivity of tungsten in nickel shows a drastic increase from 10 −10 cm 2 /s to about 10 −5 cm 2 /s as the temperature increases from 1200 • C to 1350 • C. Fig. 6a and b show the variation in the radial and axial shrinkage with sintering temperature for the 90W-7Ni-3Fe alloys consolidated in conventional and microwave furnace, respectively.…”

Section: Effect Of Heating Mode and Sintering Temperature On Densificmentioning

confidence: 89%

Effect of heating mode and sintering temperature on the consolidation of 90W–7Ni–3Fe alloys

Mondal

Upadhyaya

Agrawal

2011

Journal of Alloys and Compounds

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5.1 Introduction

Cited by 7 publications

References 2 publications

Microstructure Evolutions at Severely-deformed Austenite/Martensite Interfaces of a Layer-integrated Steel

Microstructure Evolutions at Severely-deformed Austenite/Martensite Interfaces of a Layer-integrated Steel

Grain boundary diffusion coefficients in gold–nickel thin films

Effect of heating mode and sintering temperature on the consolidation of 90W–7Ni–3Fe alloys

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