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The δ-ferrite toγ-austenite phase transformation process of low carbon steel was observed in-situ under a confocal scanning laser microscope and the influence of manganese and chromium on the migration ofδ/γinterphase boundary during theδtoγphase transformation was studied.It was found that theδ/γinterphase boundary becomes unstable with the decrease of temperature,from planar to curved morphology during theδtoγphase transformation of Fe-0.08 Csteel and Fe-0.08C-0.8 Mn steel.But in Fe-0.08C-0.8Cr steel,theδ/γinterphase boundaries are stable with planar morphology during the wholeδ-ferrite toγ-austenite transformation.The destabilization ofδ/γinterphase boundary in Fe-0.08 C and Fe-0.08C-0.8Mn steels results from high degree of supercooling and sub-boundaries inγ,respectively.The stabilization ofδ/γinterphase boundary in Fe-0.08C-0.8Cr steel results from the slow diffusion rate of carbon atom induced by the addition of chromium.
The δ-ferrite to γ-austenite phase transformation process of low carbon steel was observed in-situ under a confocal scanning laser microscope and the influence of manganese and chromium on the migration of δ / γ interphase boundary during the δtoγphase transformation was studied. It was found that the δ / γinterphase boundary becomes unstable with the decrease of temperature, from planar to curved morphology during the δtoγphase transformation of Fe-0.08 Csteel and Fe-0.08C-0.8 Mn steel.But in Fe-0.08C-0.8Cr steel, the δ / γinterphase boundaries are stable with planar morphology during the whole δ-ferrite to γ-austenite transformation. The destabilization of δ / γinterphase boundary in Fe-0.08 C and Fe-0.08C-0.8Mn steels results from high degree of supercooling and sub-boundaries in γ, respectively. stabilization of δ / γinterphase boundary in Fe-0.08C-0.8Cr steel results from the slow diffusion rate of carbon atom induced by the addition of chromium.