EP2327810B1 - Feuille d'acier de résistance élevée et son procédé de fabrication - Google Patents

Feuille d'acier de résistance élevée et son procédé de fabrication Download PDF

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Publication number
EP2327810B1
EP2327810B1 EP09813166.7A EP09813166A EP2327810B1 EP 2327810 B1 EP2327810 B1 EP 2327810B1 EP 09813166 A EP09813166 A EP 09813166A EP 2327810 B1 EP2327810 B1 EP 2327810B1
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Prior art keywords
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steel sheet
amount
seconds
microstructure
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EP09813166.7A
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German (de)
English (en)
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EP2327810A1 (fr
EP2327810A4 (fr
Inventor
Hiroshi Matsuda
Yoshimasa Funakawa
Yasushi Tanaka
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JFE Steel Corp
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JFE Steel Corp
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the workability of the steel sheet is affected by the workability of the hard phase significantly. This is because in the case where the proportion of the hard phase is small and that of soft polygonal ferrite is large, the deformability of polygonal ferrite is predominant over the workability of the steel sheet, and even in the case where the workability of the hard phase is inadequate, the workability, e.g., the elongation, is ensured, whereas in the case where the proportion of the hard phase is large, the deformability of the hard phase in itself rather than deformation of polygonal ferrite exerts an influence directly on the formability of the steel sheet and, therefore, if the workability of the hard phase in itself is inadequate, deterioration of the workability of the steel sheet becomes significant.
  • a steel sheet in which the hard phase is other than martensite
  • a steel sheet in which a primary phase is specified to be polygonal ferrite, a hard phase is specified to be bainite and pearlite, and carbides are generated in these bainite and pearlite serving as the hard phase.
  • This steel sheet is a steel sheet, in which the workability is improved not only by polygonal ferrite, but also by generating carbides in the hard phase so as to improve the workability of the hard phase in itself, and in particular, an improvement of the stretch-flangeability is intended.
  • Patent Document 2 proposes a complex microstructure steel sheet having excellent bake hardenability, wherein predetermined alloy components are specified, the steel microstructure is specified to be bainite including retained austenite, and the amount of retained austenite in the bainite is specified.
  • the bake hardenability is obtained.
  • TS tensile strength
  • the workability e.g., the elongation and the stretch-flangeability
  • the present inventors conducted intensive research on the component composition and the microstructure of a steel sheet.
  • the strength was increased through the use of a lower bainite microstructure and/or a martensite microstructure, stable retained austenite, which was advantageous to obtain a TRIP effect, was able to be ensured through the use of upper bainite transformation while the C content was increased in such a way that the amount of C in the steel sheet became 0.17% or more, a part of martensite was converted to tempered martensite and, thereby, a high strength steel sheet having excellent workability, especially a balance between the strength and the elongation and a balance between the strength and the stretch-flangeability in combination, and a tensile strength of 980 MPa or more was obtained.
  • the lower bainite and the martensite are microstructures necessary for increasing the strength of the steel sheet. If the area percentage of a total amount of lower bainite and whole martensite is less than 10%, the steel sheet does not satisfy the tensile strength (TS) of 980 MPa or more. On the other hand, if the total amount of lower bainite and whole martensite exceeds 90%, the upper bainite is reduced and, as a result, stable retained austenite, in which C is concentrated, cannot be ensured. Consequently, a problem occurs in that the workability, e.g., elongation, deteriorates. Therefore, the area percentage of the total amount of lower bainite and whole martensite is specified to be 10% or more, and 90% or less. A preferable range is 20% or more, and 80% or less. A more preferable range is 30% or more, and 70% or less.
  • retained austenite in which the amount of concentrated C is increased, is formed in the upper bainite through the use of upper bainite transformation.
  • retained austenite capable of making the TRIP effect apparent even in a high strain region during working can be obtained.
  • TS tensile strength
  • the value of TS ⁇ T.E1 can be made 20,000 MPa ⁇ % or more, and a steel sheet having an excellent balance between the strength and the elongation can be obtained.
  • the upper bainite and the lower bainite are distinguished on the basis of presence or absence of fine carbides regularly arranged in the bainitic ferrite.
  • the above-described difference in the generation state of carbides in the bainitic ferrite exerts a significant influence on concentration of C into the retained austenite. That is, in the case where the area percentage of bainitic ferrite in the upper bainite is less than 5%, even when bainite transformation proceeds, the amount of C formed into carbides in the bainitic ferrite increases. As a result, the amount of concentration of C into the retained austenite present between laths decreases, and a problem occurs in that the amount of retained austenite, which exerts the TRIP effect in a high strain region during working, decreases.
  • the area percentage of bainitic ferrite in the upper bainite is 5% or more in terms of area percentage relative to the whole steel sheet microstructure.
  • the area percentage of bainitic ferrite in the upper bainite exceeds 85% relative to the whole steel sheet microstructure, it may become difficult to ensure the strength. Consequently, it is preferable that the area percentage is specified to be 85% or less.
  • both Si and Al are elements useful for suppressing generation of carbides and facilitating generation of retained austenite.
  • an effect is exerted by containing Si or Al alone, but it is necessary to satisfy that a total of the amount of Si and the amount of Al is 0.7% or more.
  • the amount of Al in the above-described formula is the amount of Al contained in the steel sheet after deoxidation.
  • FIG. 1 A heat treatment shown in Fig. 1 is applied to the resulting cold-rolled steel sheet. The explanation will be conducted below with reference to Fig. 1 .
  • the keeping time is specified to be 15 seconds or more, and 1,000 seconds or less. preferably, the range is 30 seconds or more, and 600 seconds or less.
  • the temperature of the plating bath may be within the range of usual 450°C or higher, and 500°C or lower, and furthermore, in the case where the galvannealing treatment is applied, it is preferable that the temperature during alloying is specified to be 550°C or lower. In the case where the alloying temperature exceeds 550°C, carbides are deposited from untransformed austenite and in some cases, pearlite is generated. Consequently, the strength or the workability, or the two are not obtained. In addition, the powdering property of the coating layer deteriorates. On the other hand, if the temperature during alloying is lower than 450°C, in some cases, alloying does not proceed. Therefore, it is preferable that the alloying temperature is specified to be 450°C or higher.
  • the coating mass is specified to be within the range of 20 g/m 2 or more, and 150 g/m 2 or less per surface. If the coating mass is less than 20 g/m 2 , the corrosion resistance becomes inadequate. On the other hand, even when 150 g/m 2 is exceeded, the corrosion-resisting effect is saturated and merely an increase in the cost is invited.
  • the degree of alloying of the coating layer (Fe percent by mass (Fe content)) is within the range of 7 percent by mass or more, and 15 percent by mass or less. If the degree of alloying of the coating layer is less than 7 percent by mass, alloying variations occur, so that the quality of outward appearance deteriorates, or a so-called a ⁇ phase is generated in the coating layer, so that the sliding property of the steel sheet deteriorates. On the other hand, if the degree of alloying of the coating layer exceeds 15 percent by mass, large amounts of hard brittle ⁇ phase is formed, so that the adhesion of the coating deteriorates.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)

Claims (4)

  1. Tôle d'acier de haute résistance caractérisée en ce qu'elle a une composition constituée, sur une base de pourcentage en masse, de
    C : 0,17 % ou plus et 0,73 % ou moins ;
    Si : 3,0 % ou moins ;
    Mn : 0,5 % ou plus et 3,0 % ou moins ;
    P : 0,1 % ou moins ;
    S : 0,07 % ou moins ;
    Al : 3,0 % ou moins ; et
    N : 0,010 % ou moins,
    étant satisfait que Si + Al est égal à 0,7 % ou plus, comprenant éventuellement au moins un type d'élément choisi parmi
    Cr : 0,05 % ou plus et 5,0 % ou moins ;
    V : 0,005 % ou plus et 1,0 % ou moins ;
    Mo : 0,005 % ou plus et 0,5 % ou moins ;
    Ti : 0,01 % ou plus et 0,1 % ou moins ;
    Nb : 0,01 % ou plus et 0,1 % ou moins ;
    B : 0,0003 % ou plus et 0,0050 % ou moins ;
    Ni : 0,05 % ou plus et 2,0 % ou moins ;
    Cu : 0,05 % ou plus et 2,0 % ou moins ;
    Ca : 0,001 % ou plus et 0,005 % ou moins ;
    terres rares : 0,001 % ou plus et 0,005 % ou moins ;
    le reste incluant du Fe et des impuretés inévitables,
    où concernant la microstructure de la tôle d'acier, les conditions suivantes sont satisfaites : le pourcentage surfacique d'une quantité total de bainite inférieure et de martensite totale est de 10 % ou plus et de 90 % ou moins par rapport à la microstructure totale de la tôle d'acier, la quantité d'austénite résiduelle est de 5 % ou plus et de 50 % ou moins, le pourcentage surfacique de ferrite bainitique dans la bainite supérieure est de 5 % ou plus par rapport à la microstructure totale de la tôle d'acier, la martensite à l'état trempé est de 75 % ou plus de la quantité totale de bainite inférieure et de martensite totale et le pourcentage surfacique de ferrite polygonale est de 10 % ou moins (0 % inclus) par rapport à la microstructure totale de la tôle d'acier, la quantité moyenne de C dans l'austénite résiduelle est de 0,70 % ou plus et la résistance à la traction est de 980 MPa ou plus.
  2. Tôle d'acier de haute résistance caractérisée en ce qu'elle comprend une couche galvanisée ou une couche galvanisée après recuit sur une surface de la tôle d'acier selon la revendication 1.
  3. Procédé de fabrication d'une tôle d'acier de haute résistance, caractérisé en ce qu'il comprend les étapes consistant à laminer à chaud une billette ayant une composition de constituants selon la revendication 1, effectuer un laminage à froid de façon à produire une tôle d'acier laminée à froid, recuire la tôle d'acier laminée à froid résultante pendant 15 secondes ou plus et 600 secondes ou moins dans une région monophasique d'austénite et, après cela, effectuer un refroidissement jusqu'à une température finale de refroidissement T °C déterminée dans une première plage de température de 350 °C ou plus et 490 °C ou moins, où un refroidissement jusqu'à au moins 550 °C est effectué tout en régulant la vitesse de refroidissement moyenne à 5 °C/s ou plus, après quoi on effectue un maintien dans la première plage de température pendant 15 secondes ou plus et 1000 secondes ou moins, puis on effectue un maintien dans une seconde plage de température de 200 °C ou plus et 350 °C ou moins pendant 15 secondes ou plus et 1000 secondes ou moins.
  4. Procédé de fabrication d'une tôle d'acier de haute résistance selon la revendication 3, caractérisé en ce qu'un traitement de galvanisation ou un traitement de galvanisation après recuit est appliqué pendant le refroidissement jusqu'à la température finale de refroidissement T °C ou dans la première plage de température.
EP09813166.7A 2008-09-10 2009-09-08 Feuille d'acier de résistance élevée et son procédé de fabrication Active EP2327810B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2008232437A JP5365112B2 (ja) 2008-09-10 2008-09-10 高強度鋼板およびその製造方法
PCT/JP2009/065981 WO2010030021A1 (fr) 2008-09-10 2009-09-08 Feuille d'acier de résistance élevée et son procédé de fabrication

Publications (3)

Publication Number Publication Date
EP2327810A1 EP2327810A1 (fr) 2011-06-01
EP2327810A4 EP2327810A4 (fr) 2013-11-20
EP2327810B1 true EP2327810B1 (fr) 2019-02-27

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ID=42005270

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EP09813166.7A Active EP2327810B1 (fr) 2008-09-10 2009-09-08 Feuille d'acier de résistance élevée et son procédé de fabrication

Country Status (8)

Country Link
US (1) US20110162762A1 (fr)
EP (1) EP2327810B1 (fr)
JP (1) JP5365112B2 (fr)
KR (1) KR101341731B1 (fr)
CN (1) CN102149841B (fr)
CA (1) CA2734978C (fr)
TW (1) TWI412609B (fr)
WO (1) WO2010030021A1 (fr)

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ES2648415T5 (es) 2012-03-30 2021-02-15 Voestalpine Stahl Gmbh Chapa de acero de alta resistencia laminada en frío y procedimiento de fabricación de dicha chapa de acero
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JP5365112B2 (ja) 2013-12-11
CN102149841A (zh) 2011-08-10
JP2010065273A (ja) 2010-03-25
CA2734978A1 (fr) 2010-03-18
KR20110042369A (ko) 2011-04-26
CA2734978C (fr) 2016-03-29
CN102149841B (zh) 2013-11-20
TW201020329A (en) 2010-06-01
US20110162762A1 (en) 2011-07-07
EP2327810A1 (fr) 2011-06-01
EP2327810A4 (fr) 2013-11-20
WO2010030021A1 (fr) 2010-03-18
TWI412609B (zh) 2013-10-21

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