The effect of carbon content on the kinetics of decarburization in Fe−C alloys

Marder, A. R.; Perpetua, S. M.; Kowalik, Janusz; Stephenson, E. T.

doi:10.1007/bf02811686

Cited by 19 publications

(6 citation statements)

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“…3 The mean thickness l of the α layer versus the annealing temperature T at t = 1600 s. T ≤ 973 K and T ≥ 1093 K. At T = 1033K, l takes the maximum value. Hence, the growth of the α layer occurs most remarkably at T = 1033 K. The decarburization was experimentally observed by many investigators for various carbon steels [3][4][5][6][7][8][9][10][11][12][13][14][15]. Most of the results also indicate that the growth of the α layer considerably takes place at T = 1023−1073 K [4,5,[13][14][15].…”

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confidence: 87%

Decarburization of 0.21C-1.3Mn-0.2Si Steel for Hot Stamping at Various Heating Temperatures

Hayashi¹,

Nishibata²,

Kojima³

et al. 2011

SSP

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In order to examine the decarburization behavior in the hot stamping (HS) method, the dependence of the microstructure evolution on the annealing temperature was experimentally studied using a Fe-0.21 mass% C-1.3 mass% Mn-0.2 mass% Si steel. The steel was isothermally annealed in the temperature range ofT= 773-1173 K for various times oft= 100-12800 s in an ambient atmosphere. Here, the steel possesses the ferrite (α) + cementite (θ) two-phase microstructure atT= 773-923 K, the α + austenite (γ) two-phase microstructure atT= 1013-1073 K, and the γ single-phase microstructure atT= 1093-1173 K. During annealing atT= 1013-1073 K fort= 1600 s, however, the α layer with a uniform thickness is formed at the surface of the steel due to decarburization and gradually grows into the inside. Such formation of the a layer was not clearly observed atT973 K and T1093 K. Thus, the formation of the α layer hardly occurs under the HS annealing conditions. AtT= 1033 K, the thickness of the α layer is mostly proportional to the square root of the annealing time. Such a relationship is called the parabolic relationship. Furthermore, the grain size of the α layer monotonically increases with increasing annealing time. Hence, the parabolic relationship guarantees that the growth of the α layer is controlled by volume diffusion.

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confidence: 87%

Decarburization of 0.21C-1.3Mn-0.2Si Steel for Hot Stamping at Various Heating Temperatures

Hayashi¹,

Nishibata²,

Kojima³

et al. 2011

SSP

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“…11–15 and it was observed to induce time-dependent (autocatalytic) nucleation of lath martensite. 12,13,15…”

Section: Introductionmentioning

confidence: 99%

Thermally activated growth of lath martensite in Fe–Cr–Ni–Al stainless steel

Villa¹,

Hansen²,

Pantleon³

et al. 2015

Materials Science and Technology

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The austenite-to-martensite transformation in a partially hardened stainless steel containing 17wt %Cr, 7wt %Ni and 1wt % Al was investigated with Vibrating Sample Magnetometry and Electron Back-Scatter Diffraction. Magnetometry demonstrated that measurable martensite formation can be suppressed on fast cooling to 77K as well as on subsequent fast heating to 373 K. Surprisingly, martensite formation was observed during moderate heating from 77 K, instead. Electron Back-Scatter Diffraction demonstrated that the morphology of martensite is lath type. The kinetics of the transformation is interpreted in terms of athermal nucleation of lath martensite followed by thermally activated growth. It is anticipated that substantial autocatalytic martensite formation occurs during thermally activated growth. The observation of several retardations and accelerations of the transformation rate during slow isochronal cooling is interpreted in terms of the contribution of self-induced mechanical stabilization of austenite during martensite formation.

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“…Solid steel processing can significantly reduce the resource costs associated with new projects and simultaneously solve the problems of excess energy use, carbon dioxide emissions, and processing time in steel production [20][21][22][23][24]. Most research [25][26][27][28][29][30][31][32][33][34][35][36][37] on the solid-state steelmaking process is concentrated on the feasibility of the solid-state steelmaking and the average carbon change during decarburisation. The process flow is described as follows: the molten iron produced by a blast furnace or smelting reduction undergoes pretreatment outside the furnace and is directly solidified into strips through continuous casting equipment.…”

Section: Introductionmentioning

confidence: 99%

Analysis of decarburisation mechanism of Fe-C alloy strip

Zhou

Hong

et al. 2023

Materials Science and Technology

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Comparative experiments on different decarburisation processes of Fe-C alloys in Ar-CO-CO2 and Ar-H2O-H2 atmospheres were carried out. The fundamental principles of carbon distribution, migration, and conversion are elucidated during decarburisation in both atmospheres. The completely decarburised layer of 2-mm-thick strip in Ar-CO-CO2 atmosphere appeared about 20 min later than the decarburisation in Ar-H2O-H2 atmosphere. Compared with the decarburisation in the Ar-H2O-H2 atmosphere, the carbon-rich phase dissolution zone is wider and the solid solution carbon content in the centre side is lower in the Ar-CO-CO2 atmosphere. The concentration gradient of solid solution carbon on the centre side of the interface of austenite zone in Ar-CO-CO2 atmosphere is smaller than that in the Ar-H2O-H2 atmosphere.

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The effect of carbon content on the kinetics of decarburization in Fe−C alloys

Cited by 19 publications

References 0 publications

Decarburization of 0.21C-1.3Mn-0.2Si Steel for Hot Stamping at Various Heating Temperatures

Decarburization of 0.21C-1.3Mn-0.2Si Steel for Hot Stamping at Various Heating Temperatures

Thermally activated growth of lath martensite in Fe–Cr–Ni–Al stainless steel

Analysis of decarburisation mechanism of Fe-C alloy strip

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