Carbon and nitrogen effects on microstructure and kinetics associated with bainitic transformation in a low-alloyed steel

Catteau, S.D.; Landeghem, H.P. Van; Teixeira, Julien; Dulcy, J.; Dehmas, Moukrane; Denis, S.; Redjaïmia, A.; Courteaux, M.

doi:10.1016/j.jallcom.2015.11.007

Cited by 26 publications

(34 citation statements)

References 23 publications

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“…One might also expect lower martensite stability in agreement with the results by Grange et al [37]. If we consider the precipitation of MnSiN 2 [5,6] also depleting the matrix from manganese, martensite becomes even more unstable. As per Catteau et al [5], although equilibrium is not reached under the current experimental conditions, it is not far.…”

Section: Tempering Effectssupporting

confidence: 88%

“…These nitrides have already been reported by Catteau et al [6], evidencing the precipitation of MN nitrides at grain boundaries of previous austenite and also homogeneously distributed in the matrix of alloy 23MnCrMo5, but no Si 3 N 4 (as predicted by Thermo-Calc [21], database TCFE7) has been found either in the present work or in Catteau et al [6]. The authors [6] also report the presence of VN, not identified in the present work, and MnSiN 2 (space group Pna2 1 [29]) formed at relatively lower nitrogen contents with regards to the present work such as 0.25 wt.%. The presence of MnSiN 2 is confirmed in the present study but not predicted by thermodynamic calculations with the used database.…”

Section: Transmission Electron Microscopysupporting

confidence: 80%

“…Thus, the understanding of attainable mechanical properties is based on carbon-nitrogen martensite behavior. Conversely to nitrogen effects [5,6], much has been reported about the role of carbon on martensite transformation of steels [7]. For nitrogen martensite, literature remains mostly limited to the Fe-N system, for which metallurgical transformations through tempering and room temperature aging are established [8][9][10][11][12][13][14][15].…”

Section: Introductionmentioning

confidence: 99%

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Carbonitriding of low alloy steels: Mechanical and metallurgical responses

Silva

Dulcy

Ghanbaja

et al. 2017

Materials Science and Engineering: A

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Metallurgical and mechanical responses to the introduction of carbon and/or nitrogen have been investigated for alloys 16NiCrMo13 and 23MnCrMo5 through atmospheric pressure carbonitriding, carburizing and austenitic nitriding. Treatments were performed at 1173 K using CO − H 2 and/or NH 3 based atmospheres. As-quenched hardness is studied in terms of solid solution interstitial content, which is estimated from electron probe micro-analyses and thermodynamic simulations. This aims to quantify high-temperature precipitation of nitrides, which is accompanied by consumption of nitrogen in solid solution. Plots of as-quenched hardness versus the square root of the total content expressed in atomic fraction of interstitial elements, i.e. the sum of solution carbon and nitrogen, show the complementary character of these elements in determining the mechanical properties of the as-quenched alloys. Tempering of carbon-nitrogen martensite-for both carbonitriding and austenitic nitriding-led to lower hardness loss when compared to the same total content of interstitial carbon in martensite. Transmission electron microscopy analyses highlight precipitation of fine Fe 16 N 2 zones in the nitrogen-rich depth.

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Section: Tempering Effectssupporting

confidence: 88%

Section: Transmission Electron Microscopysupporting

confidence: 80%

Section: Introductionmentioning

confidence: 99%

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Carbonitriding of low alloy steels: Mechanical and metallurgical responses

Silva

Dulcy

Ghanbaja

et al. 2017

Materials Science and Engineering: A

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“…Since the average grain size of the Ringhals RPV steels is not available, the value of 88 µm, yielded by the microstructural examination of the Fe–C–MnNi model alloy , was adopted. However, the bainitic structure of RPV steels is typically characterized by smaller elongated laths and sub‐laths , whose thickness and length can range down to tens and hundreds of nanometers, respectively. The equivalent diameter of a spherical lath with the same absorption efficiency can be calculated by assuming that the sink strength is inversely proportional to the lath dimensions: k 2 ∝1/ lt (where l is the length and t the thickness of the lath), whereas for spherical grains (with radius r ) k 2 ∝1/ r 2 .…”

Section: Okmc Modelmentioning

confidence: 99%

An object kinetic Monte Carlo model for the microstructure evolution of neutron‐irradiated reactor pressure vessel steels

Messina

Chiapetto

Olsson

et al. 2016

Physica Status Solidi (a)

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Phone: þ32 (0)14 33 31 81This work presents a full object kinetic Monte Carlo framework for the simulation of the microstructure evolution of reactor pressure vessel (RPV) steels. The model pursues a "gray-alloy" approach, where the effect of solute atoms is seen exclusively as a reduction of the mobility of defect clusters. The same set of parameters yields a satisfactory evolution for two different types of alloys, in very different irradiation conditions: an Fe-C-MnNi model alloy (high flux) and a high-Mn, high-Ni RPV steel (low flux). A satisfactory match with the experimental characterizations is obtained only if assuming a substantial immobilization of vacancy clusters due to solute atoms, which is here verified by means of independent atomistic kinetic Monte Carlo simulations. The microstructure evolution of the two alloys is strongly affected by the dose rate; a predominance of single defects and small defect clusters is observed at low dose rates, whereas larger defect clusters appear at high dose rates. In both cases, the predicted density of interstitial loops matches the experimental solute-cluster density, suggesting that the MnNi-rich nanofeatures might form as a consequence of solute enrichment on immobilized small interstitial loops, which are invisible to the electron microscope.

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“…Clark et al performed FIB-lift out TEM analysis on the interphase of A-F during phase transformation from austenite to ferrite to investigate VC/VN interphase precipitate distribution and reported that the precipitates were distributed in irregularly spaced curvilinear patterns [15]. It has been demonstrated that FIB lift-out TEM analysis allows to investigate site specific chemical distribution of the solute atoms or precipitates, and to monitor their interaction with the grain boundary [15,42,43]. This paper aims to apply correlative and quasi in-situ material characterisation techniques to investigate recrystallization behaviour and evolution of alpha and gamma fibres by analysing geometrically necessary dislocation (GND) density in respective fibres during annealing of cold-rolled steel microalloyed with Titanium (Ti) and Vanadium (V).…”

Section: Introductionmentioning

confidence: 99%

Quasi in-situ analysis of geometrically necessary dislocation density in α-fibre and γ-fibre during static recrystallization in cold-rolled low-carbon Ti-V bearing microalloyed steel

Kapoor

Lan

Rijkenberg

et al. 2018

Materials Characterization

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NonCommercial-NoDerivatives 4.0 International http://creativecommons.org/licenses/by-nc-nd/4.0/. Publisher's statement:Please refer to the repository item page, publisher's statement section, for further information.For more information, please contact the WRAP Team at: wrap@warwick.ac.uk.Quasi in-situ analysis of geometrically necessary dislocation density in α-fibre and γ-fibre during static recrystallization in cold-rolled low-carbon Ti-V bearing microalloyed steel Abstract In the present study, cold-rolled low-carbon steel is annealed at three different conditions: 700 o C for 0 s, 800 o C for 0 s and 800 o C for 2 min at the heating rate of ~10 o C/s. Recrystallization behaviour on sample surface is studied using a heated stage Scanning Electron Microscopy and Electron Backscattered Diffraction. For the lower annealing temperature of 700 o C with no dwell, almost no recrystallization is observed and microstructure resembles the as-received deformed material with the exception of occasional sub-micron sized nuclei. For the annealing conditions of 800 o C 0 s and 800 o C 2 min, onset and evolution of recrystallization is observed in-situ as a function of the initial as-cold rolled texture. Slower recovery rate of alpha fibre than gamma fibre is observed and confirmed by lower drop in average geometrically necessary dislocation (GND) density for un-recrystallized alpha fibres(1.1E+14 m -2 for 700 o C 0 s , 1.4E+14 m -2 for 800 o C 0 s and 4.5E+14 m -2 for 800 o C 2 min) than for un-recrystallized gamma fibre grains (3.0E+14 m -2 for 700 o C 0 s , 6.2E+14 m -2 for 800 o C 0 s and 9.8E+14 m -2 for 800 o C 2 min) during annealing. Strong gamma texture in recrystallized matrix is found for annealing conditions of 800 o C 0 s and 800 o C 2 min. From TEM characterisation it was shown that sub-grain boundaries are decorated with fine precipitates (diameter d < 15 nm) of titanium-vanadium carbides (Ti,V)C for the annealing condition of 700 o C 0 s, which suggests that these precipitates play a major overall role in retardation of the recrystallization kinetics.

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Carbon and nitrogen effects on microstructure and kinetics associated with bainitic transformation in a low-alloyed steel

Cited by 26 publications

References 23 publications

Carbonitriding of low alloy steels: Mechanical and metallurgical responses

Carbonitriding of low alloy steels: Mechanical and metallurgical responses

An object kinetic Monte Carlo model for the microstructure evolution of neutron‐irradiated reactor pressure vessel steels

Quasi in-situ analysis of geometrically necessary dislocation density in α-fibre and γ-fibre during static recrystallization in cold-rolled low-carbon Ti-V bearing microalloyed steel

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