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Distribution of carbon in martensite during quenching and tempering of dual phase steels and consequences for damage properties

hal.structure.identifierInstitut Jean Lamour [IJL]
dc.contributor.authorPUSHKAREVA, Irina
hal.structure.identifierArcelorMittal Maizières Research SA
dc.contributor.authorSCOTT COLIN, Philip
hal.structure.identifierInstitut de Chimie de la Matière Condensée de Bordeaux [ICMCB]
dc.contributor.authorGOUNÉ, Mohamed
hal.structure.identifierDepartment of Science and Analysis of Materials
dc.contributor.authorVALLE, Nathalie
hal.structure.identifierInstitut Jean Lamour [IJL]
dc.contributor.authorREDJAÏMIA, Abdelkrim
hal.structure.identifierArcelorMittal Maizières Research SA
dc.contributor.authorMOULIN, Antoine
dc.date.issued2013
dc.identifier.issn0915-1559
dc.description.abstractEnThe microstructural evolution of martensite in as-quenched and quenched and tempered Fe-0.15C-0.215Si-1.9Mn-0.195Cr wt.% dual phase (DP) steels processed to give four different errite/martensite ratios was studied. It was found that partial thermodynamic equilibrium was obtained after intercritical annealing for 130 s. The local carbon distribution in as-quenched martensite was heterogeneous for all quenching temperatures. Significant carbon enrichment was observed at the ferrite/martensite interface at annealing temperatures of 790°C, whereas carbon depletion occurred when the annealing temperature was reduced to 755°C. A possible explanation for the carbon profile in terms of the effect of Mn partitioning on the austenite phase transformation kinetics is given. The kinetics of carbide formation during tempering is strongly influenced by these carbon gradients. A simple analysis shows that the interface carbon depletion observed at lower intercritical annealing temperatures could induce a beneficial increase in the void nucleation strain ! n, due to a reduction in the backstress at the ferrite/martensite interface which decreases the local stress triaxiality. We estimate that the upper limit for the improvement in the asquenched microstructure is ~8%, so the effect could provide a moderate delay in the onset of damage. Further, we propose that the improvement in damage resistance during tempering is mainly due to dispersed void formation at tempered carbides and that this mechanism will be compromised if those carbides are localised at ferrite/martensite interfaces. This argument mitigates for the carbon-depleted interface structure obtained at lower intercritical temperatures.
dc.language.isoen
dc.publisherIron & Steel Institute of Japan
dc.subject.enDual-phase
dc.subject.enSteel
dc.subject.enMicrostructure
dc.subject.enCarbon distribution
dc.subject.enPhase transformation
dc.subject.enThermodynamics
dc.subject.enDamage
dc.title.enDistribution of carbon in martensite during quenching and tempering of dual phase steels and consequences for damage properties
dc.typeArticle de revue
dc.identifier.doi10.2355/isijinternational.53.1215
dc.subject.halChimie/Matériaux
bordeaux.journalISIJ international
bordeaux.page1215-1223
bordeaux.volume53
bordeaux.issue7
bordeaux.peerReviewedoui
hal.identifierhal-00845782
hal.version1
hal.popularnon
hal.audienceInternationale
hal.origin.linkhttps://hal.archives-ouvertes.fr//hal-00845782v1
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