EP2831299B2 - Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type - Google Patents

Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type Download PDF

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EP2831299B2
EP2831299B2 EP13717208.6A EP13717208A EP2831299B2 EP 2831299 B2 EP2831299 B2 EP 2831299B2 EP 13717208 A EP13717208 A EP 13717208A EP 2831299 B2 EP2831299 B2 EP 2831299B2
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Prior art keywords
cold rolled
steel sheet
rolled steel
temperature
cooling
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German (de)
English (en)
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EP2831299B1 (fr
EP2831299A1 (fr
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Daniel Krizan
Stefan Paul
Andreas Pichler
Michiharu Nakaya
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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Priority claimed from PCT/EP2013/056957 external-priority patent/WO2013144377A1/fr
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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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • 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
    • C22C38/02—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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C21D2211/005—Ferrite
    • 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 present invention relates to high strength cold rolled steel sheet suitable for applications in automobiles, construction materials and the like, specifically high strength steel sheet excellent in formability.
  • the invention relates to a cold rolled steel sheet having a tensile strength of at least 980 MPa.
  • TRIP steels possess a multi-phase microstructure, which includes a meta-stable retained austenite phase, which is capable of producing the TRIP effect.
  • the austenite transforms into martensite, which results in remarkable work hardening. This hardening effect, acts to resist necking in the material and postpone failure in sheet forming operations.
  • the microstructure of a TRIP steel can greatly alter its mechanical properties. The most important aspects of the TRIP steel microstructure are the volume percentage, size and morphology of the retained austenite phase, as these properties directly affect the austenite to martensite transformation when the steel is deformed. There are several ways in which to chemically stabilize austenite at room temperature.
  • the austenite In low alloy TRIP steels the austenite is stabilized through its carbon content and the small size of the austenite grains.
  • the carbon content necessary to stabilize austenite is approximately 1 wt. %.
  • high carbon content in steel cannot be used in many applications because of impaired weldability.
  • a common TRIP steel chemistry also contains small additions of other elements to help in stabilizing the austenite as well as to aid in the creation of microstructures which partition carbon into the austenite.
  • the most common additions are 1.5 wt. % of both Si and Mn.
  • the silicon content should be at least 1 wt. %.
  • the silicon content of the steel is important as silicon is insoluble in cementite. US 2009/0238713 discloses such a TRIP steel.
  • TRIP steels The formability of TRIP steels is mainly affected by the transformation characteristics of the retained austenite phase, which is in turn affected by the austenite chemistry, its morphology and other factors.
  • ISIJ International Vol. 50(2010) No. 1, p. 162 -168 aspects influencing on the formability of TBF steels having a tensile strength of at least 980 MPa are discussed.
  • the cold rolled materials examined in this document were annealed at 950 °C and the austempered at 300-500 °C for 200 s in salt bath. Accordingly, due to the high annealing temperature these materials are not suited for the production in a conventional industrial annealing line.
  • the present invention is directed to a high strength cold rolled steel sheet having a tensile strength of at least 980 MPa and having an excellent formability and a method of producing the same on an industrial scale.
  • the invention relates to a cold rolled TBF steel sheet having properties adapted for the production in a conventional industrial annealing -line. Accordingly, the steel shall not only possess good formability properties but at the same time be optimized with respect to A c3 - temperature, M s - temperature, austempering time and temperature and other factors such as sticky scale influencing the surface quality of the hot rolled steel sheet and the processability of the steel sheet in the industrial annealing line.
  • the cold rolled high strength TBF steel sheet has a steel composition consisting of the following elements (in wt. %): C 0.15 - 0.18 Mn 2.2 - 2.4 Si 0.7 - 0.9 Cr 0.1 - 0.9 Si + 0.8 Al +Cr 0.5 - 1.8 Al 0.2 - 0.6 Nb ⁇ 0.1 Mo ⁇ 0.3 Ti ⁇ 0.2 V ⁇ 0.2 Cu ⁇ 0.5 Ni ⁇ 0.5 S ⁇ 0.01 P ⁇ 0.02 N ⁇ 0.02 B ⁇ 0.005 Ca ⁇ 0.005 Mg ⁇ 0.005 REM ⁇ 0.005 balance Fe apart from impurities.
  • C is an element which stabilizes austenite and is important for obtaining sufficient carbon within the retained austenite phase. C is also important for obtaining the desired strength level. Generally, an increase of the tensile strength in the order of 100 MPa per 0.1 %C can be expected. When C is lower than 0.1 % then it is difficult to attain a tensile strength of 980 MPa. If C exceeds 0.3 % then weldability is impaired. For this reasons, the preferred range is 0.15 - 0.18 %, depending on the desired strength level.
  • Manganese is a solid solution strengthening element, which stabilises the austenite by lowering the Ms temperature and prevents ferrite and pearlite to be formed during cooling.
  • Mn lowers the Ac3 temperature. At a content of less than 2% it might be difficult to obtain a tensile strength of 980 MPa and the austenitizing temperature might be too high for conventional industrial annealing lines. However, if the amount of Mn is higher than 3 % problems with segregation may occur and the workability may be deteriorated. The preferred range is therefore 2.2 - 2.4%.
  • Si acts as a solid solution strengthening element and is important for securing the strength of the thin steel sheet.
  • Si is insoluble in cementite and will therefore act to greatly delay the formation of carbides during the bainite transformation as time must be given to Si to diffuse away from the bainite grain boundaries before cementite can form.
  • the preferred range is therefore 0.7 - 0.9 %.
  • Cr is effective in increasing the strength of the steel sheet.
  • Cr is an element that forms ferrite and retards the formation of pearlite and bainite.
  • the Ac3 temperature and the Ms temperature are only slightly lowered with increasing Cr content.
  • the amount of Cr is preferably limited to 0.6 %.
  • the preferred range is 0.1-0.35
  • Si, Al and Cr when added in combination have a synergistic and completely unforeseen effect, resulting in an increased amount of residual austenite, which, in turn, results in an improved ductility.
  • the amount of Si + 0.8 Al + Cr is limited to the range 1.4 - 1.8 %.
  • Al promotes ferrite formation and is also commonly used as a deoxidizer.
  • Al like Si, is not soluble in the cementite and therefore diffuses away from the bainite grain boundaries before cementite can form.
  • the Ms temperature is increased with increasing Al content.
  • a further drawback of Al is that it results in a drastic increase in the Ac3 temperature such that the austenitizing temperature might be too high for conventional industrial annealing lines.
  • the contents of Al refers to acid soluble Al.
  • the steel may optionally contain one or more of the following elements in order to adjust the microstructure, influence on transformation kinetics and/or to fine tune one or more of the mechanical properties of the steel sheet.
  • Nb is commonly used in low alloyed steels for improving strength and toughness because of its remarkable influence on the grain size development. Nb increases the strength elongation balance by refining the matrix microstructure and the retained austenite phase due to precipitation of NbC. At contents above 0.1 % the effect is saturated.
  • Preferred ranges are therefore 0.02-0.08 %, 0.02 - 0.04 % and 0.02 - 0.03 %.
  • Mo can be added in order to improve the strength of the steel sheet. Addition of Mo together with Nb results in precipitation of fine NbMoC which results in a further improvement in the combination of strength and ductility.
  • Ti may be added in preferred amounts of ⁇ 0.01 - 0.1 %, 0.02 - 0.08 % or 0.02 - 0.05 %.
  • V may be added in preferred amounts of 0.01 - 0.1 % or 0.02 - 0.08 %.
  • These elements are solid solution strengthening elements and may have a positive effect on the corrosion resistance.
  • The may be added in amounts of 0.05 - 0.5 % or 0.1 - 0.3 % if needed.
  • S preferably ⁇ 0.003 P preferably ⁇ 0.01 N preferably ⁇ 0.003
  • B suppresses the formation of ferrite and improves the weldability of the steel sheet. For having a noticeable effect at least 0.0002 % should be added. However, excessive amounts of deteriorate the workability. Preferred ranges are ⁇ 0.004 %, 0.0005- 0.003 % and 0.0008 -0.0017 %.
  • These elements may be added in order to control the morphology of the inclusions in the steel and thereby improve the hole expansibility and the stretch flangeability of the steel sheet.
  • Preferred ranges are 0.0005 -0.005 % and 0.001-0.003 %.
  • the high strength cold rolled steel sheet according to the invention has a silicon aluminium based design, i.e. the cementite precipitation during the bainitic transformation is accomplished by Si and Al.
  • Si silicon aluminium based design
  • the amount of Si is reduced is preferably that it is larger than the amount of Al, preferably Si > 1.1 Al, more preferably Si > 1.3 Al or even Si > 2 Al.
  • the amount of Si is preferred to be larger than the amount of Cr and to restrict the amount of Cr in order to retard the bainite transformation too much. For this reason it preferred to keep Si > Cr, preferably Si > 1.5 Cr, more preferably Si > 2 Cr, most preferably Si > 3 Cr.
  • the cold rolled high strength TBF steel sheet has a multiphase microstructure comprising (in vol. %) retained austenite 5 - 20 bainite + bainitic ferrite + tempered martensite ⁇ 80 polygonal ferrite ⁇ 10
  • the amount of retained austenite is 5-20%, preferably from 5 - 16 %, most preferably from 5 - 10 %. Because of the TRIP effect retained austenite is a prerequisite when high elongation is necessary. High amount of residual austenite decreases the stretch flangeability.
  • the polygonal ferrite is replace by bainitic ferrite (BF) and the microstructure generally contains more than 50 % BF.
  • the matrix consists of BF laths strengthened by a high dislocation density and between the laths the retained austenite is contained.
  • MA (martensite/austenite) constituent represents the individual islands in the microstructure consisting of retained austenite and/or martensite. These two microstructural compounds are difficult to be distinguished by common etching technique for advanced high strength steels (AHSS) - Le Pera etching and also by investigations with scanning electron microscopy (SEM). Le Pera etching, which is very common to the person skilled in the art can be found eg in "F.S. LePera, Improved etching technique for the determination of percent martensite in high-strength dual-phase steels Metallography, Volume 12, Issue 3, September 1979, Pages 263-268". Furthermore, for properties such as hole expansion the amount and size of MA constituent plays an important role. Therefore, in an industrial practice the fraction and size of MA constituent are often used by AHSS for the correlations in terms of their mechanical properties and formability.
  • the size of the martensite-austenite (MA) shall be max 5 ⁇ m, preferably 3 ⁇ m. Minor amounts of martensite may be present in the structure.
  • the amount of MA shall be max 20 %, preferably max 16 %, most preferably below 10 %.
  • the cold rolled high strength TBF steel sheet preferably has the following mechanical properties tensile strength (Rm) ⁇ 980 - 1200 MPa total elongation (A80) ⁇ 11 % hole expanding ratio ( ⁇ ) ⁇ 45 %, preferably ⁇ 50 %.
  • the R m and A 80 values were derived according to the European norm EN 10002 Part 1, wherein the samples were taken in the longitudinal direction of the strip.
  • the hole expanding ratio ( ⁇ ) was determined by the hole expanding test according to ISO/WD 16630. In this test a conical punch having an apex of 60 ° is forced into a 10 mm diameter punched hole made in a steel sheet having the size of 100 x 100 mm 2 . The test is stopped as soon as the first crack is determined and the hole diameter is measured in two directions orthogonal to each other. The arithmetic mean value is used for the calculation.
  • the formability properties of the steel sheet were further assessed by the parameters: strength-elongation balance (R m x A 80 ) and stretch-flangeability (R m x ⁇ ).
  • An elongation type steel sheet has a high strength-elongation balance and a high hole expansibility type steel sheet has a high stretch flangeability.
  • the steel sheet of the present invention fulfils at least one of the following conditions: R m ⁇ A 80 ⁇ 13 000 MPa ⁇ % R m ⁇ ⁇ ⁇ 50 000 MPa ⁇ %
  • the mechanical properties of the steel sheet of the present invention can be largely adjusted by the alloying composition and the microstructure.
  • a comparative chemical composition may comprise 0.19 C, 2.6 Mn, 0.82 Si, 0.3-0.7 Al, 0.10 Mo, rest Fe apart from impurities.
  • the steel sheets of the present invention can be produced using a conventional CA-line.
  • the processing comprises the steps of:
  • the process shall preferably further comprise the steps of:
  • the amount of polygonal ferrite in the steel sheet can be controlled. If the annealing temperature, T an , is below the temperature at which the steel is fully austenitic, A c3 , there is a risk that the amount of polygonal ferrite in the steel sheet will exceed 10%. Too much polygonal ferrite gives larger size of the MA constituent.
  • the size of MA constituent in the steel sheet can be controlled. If the cooling stop temperature of rapid cooling, T RC , exceeds the martensite start temperature, T MS , the size of MA constituent becomes larger which lowers the R m x ⁇ product under the value necessary for a high hole expansion type steel sheet. In the case of a high elongation type steel sheet the cooling stop temperature, T RC might be above the martensite start temperature, T MS .
  • the size of MA constituent and the amount of retained austenite, RA can be controlled.
  • a lower austempering temperature, T 0A will lower the amount of RA.
  • a higher austempering temperature, T 0A will lower the amount of RA and increase the size of MA constituent. In both cases, this will lower the uniform elongation, Ag, and total elongation, A 80 , of the steel sheet.
  • the amount of polygonal ferrite can be controlled. Lowering the cooling rates will increase the amount of polygonal ferrite to more than 10%.
  • the steel sheet is a high elongation type steel having strength-elongation balance R m x A 80 ⁇ 13 000 MPa%, preferably ⁇ 15 000 MPa.
  • the steel sheet is a high hole expansibility type steel having stretch-flangeability R m x ⁇ ⁇ 50 000 MPa%, preferably ⁇ 55 000 MPa.
  • test alloys A-M were manufactured having chemical compositions according to table I. Steel sheets were manufactured and subjected to heat treatment in a conventional CA-line according to the parameters specified in Table II. The microstructure of the steel sheets were examined along with a number of mechanical properties and the result is presented in Table II
  • Amount of retained austenite was measured by X ray analysis at a 1/4 position of the sheet thickness.
  • a photograph of a microstructure taken by the SEM was subjected to image analysis to measure each of a volume-% of a MA, volume-% of matrix phase (bainitic ferrite + bainite + tempered martensite), volume-% of retained austenite and volume-% of polygonal ferrite.
  • Bainitic ferrite + bainite + tempered martensite
  • the present invention can be widely applied to high strength steel sheets having excellent formability for vehicles such as automobiles.

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  • Engineering & Computer Science (AREA)
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Claims (13)

  1. Une tôle d'acier laminée à froid à haute résistance ayant,
    a) une composition constituée des éléments suivants (en % en poids) : C 0.15 - 0.18 Mn 2.2 - 2.4 Si 0.7 - 0.9 Cr 0.1 - 0.9 Al 0.2 - 0.6 Si + 0.8 Al +Cr 1.4 - 1.8 Nb < 0.1 Mo < 0.3 Ti < 0.2 V < 0.2 Cu < 0.5 Ni < 0.5 S ≤ 0.01 P ≤ 0.02 N ≤ 0.02 B < 0,005 Ca < 0,005 Mg < 0,005 REM < 0,005
    complément en Fe à l'exception des impuretés,
    b) une microstructure multiphase comprenant (en % du vol.) austénite résiduelle 5 - 20 bainite + ferrite bainitique + martensite trempée ≥ 80 ferrite polygonale ≤ 10
    c) au moins une des propriétés mécaniques suivantes une résistance à la traction (Rm) 980 - 1200 MPa un allongement (A80) ≥ 11 % un taux d'expansion de trous (λ) ≥ 45 %,
    et remplissant au moins une des conditions suivantes Rm x A80 ≥ 13 000 MPa% Rm x λ ≥ 50 000 MPa%
  2. Une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, répondant à au moins un parmi ce qui suit : Nb 0,02 - 0,08 Mo 0,05 - 0,3 Ti 0,02 - 0,08 V 0,02 - 0,1 Cu 0,05 - 0,4 Ni 0,05 - 0,4 B 0,0005 - 0,003 Ca 0.0005 - 0.005 Mg 0,0005 - 0,005 REM 0.0005 - 0.005
  3. Une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, répondant à au moins un parmi ce qui suit : S ≤ 0,01 de préférence ≤ 0,003 P ≤ 0,02 de préférence ≤ 0,01 N ≤ 0,02 de préférence ≤ 0,003 Ti > 3,4N
  4. Tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, dans laquelle la taille maximale du constituant martensite-austénite (MA) est ≤ 5 µm, de préférence ≤ 3 µm.
  5. Tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, dans laquelle la microstructure multiphase comprend (en% du vol.) austénite résiduelle 5 - 16, de préférence inférieure à 10% bainite + bainite ferrite + martensite trempée ≥ 80 ferrite polygonale ≤ 10 constituant martensite-austénite (MA) ≤ 20%, de préférence ≤ 16%, de manière la plus préférée, inférieur à 10%
  6. Une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, dans laquelle l'acier comprend Nb 0,02 à 0,03
  7. Une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, dans laquelle le rapport (Mn + Cr) / (Si + Al) ≥ 1,6.
  8. Une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, dans laquelle la quantité de Si est de l'ordre de la quantité d'Al, ou supérieure à la quantité d'Al, de préférence Si > 1,1 Al, plus préférablement Si > 1,3 Al ou même Si > 2 Al.
  9. Une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, qui n'est pas pourvue d'une couche de galvanisation à chaud.
  10. Un procédé de production d'une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications précédentes, comprenant les étapes consistant à :
    a) fournir une bande d'acier laminée à froid ayant une composition telle que définie dans l'une quelconque des revendications précédentes,
    b) réaliser un recuit de la bande d'acier laminé à froid à une température supérieure à la température Ac3 afin d'austénitiser complètement l'acier, suivie du fait de
    c) refroidir la bande d'acier laminée à froid depuis la température de recuit, Tan, jusqu'à une température d'arrêt de refroidissement du refroidissement rapide, TRC, qui est comprise entre 360 et 460°C, de préférence entre 380 et 420°C, à une vitesse de refroidissement suffisante pour éviter la formation de ferrite, la vitesse de refroidissement étant de 20 à 100°C / s, suivie du fait
    d) d'opérer une trempe bainitique de la bande d'acier laminée à froid à une température de dépassement / de trempe bainitique, TOA, comprise entre 360 et 460°C, de préférence 380 et 420°C, et
    e) refroidir la bande d'acier laminée à froid à la température ambiante,
    la tôle d'acier étant une tôle d'acier de type à allongement élevé ayant un solde de résistance à l'allongement Rm x A80 ≥ 13 000 MPa%, de préférence ≥ 15 000 MPa%.
  11. Un procédé de production d'une tôle d'acier laminée à froid à haute résistance selon l'une quelconque des revendications 1 à 9, comprenant les étapes consistant à :
    a) fournir une bande d'acier laminée à froid ayant une composition telle que définie dans l'une quelconque des revendications précédentes,
    b) opérer un recuit de la bande d'acier laminée à froid à une température supérieure à la température Ac3 afin d'austénitiser complètement l'acier, suivie du fait de
    c) refroidir la bande d'acier laminée à froid depuis la température de recuit, Tan, jusqu'à une température d'arrêt de refroidissement du refroidissement rapide TRC < TMS, TMS étant comprise entre 300 et 400°C, de préférence entre 340 et 370°C, à une vitesse de refroidissement suffisante pour éviter la formation de ferrite, la vitesse de refroidissement étant de 20 à 100°C/s, suivie du fait
    d) d'opérer une trempe bainitique de la bande d'acier laminée à froid à une température de dépassement / de trempe bainitique, TOA, qui est comprise entre 360 et 460°C, de préférence entre 380 et 420°C, de préférence TOA > TRC, et
    e) refroidir la bande d'acier laminée à froid à la température ambiante,
    la tôle d'acier étant une tôle d'acier de type à haute capacité de dilatation de trous ayant une résistance à l'étirement Rm x λ ≥ 50 000 MPa%, de préférence ≥ 55 000 MPa.
  12. Un procédé de production d'une tôle d'acier laminée à froid à haute résistance selon les revendications 10 et 11, dans lequel :
    à l'étape b), le recuit est effectué à une température de recuit, Tan, qui est entre 910 et 930°C, pendant un temps de maintien de recuit, tan, qui est compris entre 150 et 200 s, de préférence 180 s,
    à l'étape c), le refroidissement est effectué selon un schéma de refroidissement ayant deux vitesses de refroidissement séparées ; une première vitesse de refroidissement, CR1, de 80 à 100°C/s, de préférence de 85 à 95°C/s, de préférence d'environ 90°C/s jusqu'à une température comprise entre 530 et 570°C, de préférence de 550°C, et une deuxième vitesse de refroidissement, CR2, de 35 à 45°C, de préférence d'environ 40°C/s jusqu'à la température d'arrêt du refroidissement rapide, TRC, et
    à l'étape d) la trempe bainitique de l'acier est effectuée sur un intervalle de temps de 150 à 600 s, de préférence de 180 à 540 s.
  13. Un procédé de production d'une tôle d'acier laminée à froid à haute résistance selon les revendications 10 et 11, dans lequel aucun chauffage externe n'est appliqué sur la tôle d'acier entre les étapes c) et d).
EP13717208.6A 2012-03-30 2013-04-02 Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type Active EP2831299B2 (fr)

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EP13717208.6A EP2831299B2 (fr) 2012-03-30 2013-04-02 Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type
PCT/EP2013/056957 WO2013144377A1 (fr) 2012-03-30 2013-04-02 Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type

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DE102022102418A1 (de) 2022-02-02 2023-08-03 Salzgitter Flachstahl Gmbh Hochfestes schmelztauchbeschichtetes Stahlband mit durch Gefügeumwandlung bewirkter Plastizität und Verfahren zu dessen Herstellung
DE102022132188A1 (de) 2022-12-05 2024-06-06 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines hochfesten Stahlflachproduktes mit einem Mehrphasengefüge und entsprechendes hochfestes Stahlflachprodukt

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EP2831299B2 (fr) 2012-03-30 2020-04-29 Voestalpine Stahl GmbH Tôle d'acier laminée à froid à haute résistance et procédé de production d'une tôle d'acier de ce type
SE1651545A1 (en) * 2016-11-25 2018-03-06 High strength cold rolled steel sheet for automotive use
US11732320B2 (en) 2019-02-18 2023-08-22 Tata Steel Ijmuiden B.V. High strength steel with improved mechanical properties
EP3754037B1 (fr) 2019-06-17 2022-03-02 Tata Steel IJmuiden B.V. Procédé de traitement thermique d'une bande d'acier laminée à froid à haute résistance
PT3754035T (pt) 2019-06-17 2022-04-21 Tata Steel Ijmuiden Bv Método de tratamento térmico de uma tira de aço laminada a frio
ES2911661T3 (es) 2019-06-17 2022-05-20 Tata Steel Ijmuiden Bv Tratamiento térmico de un fleje de acero laminado en frío de alta resistencia
ES2911655T3 (es) 2019-06-17 2022-05-20 Tata Steel Ijmuiden Bv Tratamiento térmico de un fleje de acero laminado en frío
SE545209C2 (en) * 2020-12-23 2023-05-23 Voestalpine Stahl Gmbh Coiling temperature influenced cold rolled strip or steel
WO2023170245A1 (fr) * 2022-03-10 2023-09-14 Tata Steel Nederland Technology B.V. Tôle d'acier à haute résistance présentant une excellente extensibilité de trou et son procédé de production

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WO2013144376A1 (fr) † 2012-03-30 2013-10-03 Voestalpine Stahl Gmbh Tôle d'acier laminée à froid de haute résistance et procédé de fabrication d'une telle tôle d'acier
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Publication number Priority date Publication date Assignee Title
DE102022102418A1 (de) 2022-02-02 2023-08-03 Salzgitter Flachstahl Gmbh Hochfestes schmelztauchbeschichtetes Stahlband mit durch Gefügeumwandlung bewirkter Plastizität und Verfahren zu dessen Herstellung
WO2023148199A1 (fr) 2022-02-02 2023-08-10 Salzgitter Flachstahl Gmbh Bande d'acier haute résistance revêtue par immersion à chaud dont la plasticité est due à une transformation microstructurale, et procédé de production correspondant
DE102022132188A1 (de) 2022-12-05 2024-06-06 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines hochfesten Stahlflachproduktes mit einem Mehrphasengefüge und entsprechendes hochfestes Stahlflachprodukt
WO2024120962A1 (fr) 2022-12-05 2024-06-13 Salzgitter Flachstahl Gmbh Procédé de production d'un produit en acier plat à haute résistance présentant une microstructure multiphase, et produit en acier plat à haute résistance correspondant

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