EP2831299B2 - Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung eines solchen stahlblechs - Google Patents

Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung eines solchen stahlblechs 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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French (fr)
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EP2831299A1 (de
EP2831299B1 (de
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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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    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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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Claims (13)

  1. Hochfestes kaltgewalztes Stahlblech, mit
    a) einer Zusammensetzung bestehend aus den folgenden Elementen (in Gew.-%): 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
    der Rest Fe, bis auf Unreinheiten
    b) mehrphasige Mikrostruktur, umfassend (in Vol.-%) Restaustenit 5 - 20 Bainit + bainitischer Ferrit + temperierter Martensit ≥ 80 polygoner Ferrit ≤ 10
    c) mindestens eine der folgenden mechanischen Eigenschaften Zugfestigkeit (Rm) 980 - 1200 MPa Dehnung (A80) ≥ 11 % Lochaufweitungsrate (λ) ≥ 45 %,
    und mindestens eine der folgenden Bedingungen erfüllt Rm x A80 ≥ 13000 MPa% Rm x λ ≥ 50000 MPa%.
  2. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, das zumindest eines der folgenden erfüllt: 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. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, das mindestens eines der folgenden erfüllt: S ≤ 0,01 vorzugsweise ≤ 0,003 P ≤ 0,02 vorzugsweise ≤ 0,01 N ≤ 0,02 vorzugsweise ≤ 0,003 Ti > 3,4 N
  4. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, wobei die maximale Größe der Martensit-Austenit-Konstituent (MA) ≤ 5 µm ist, vorzugsweise ≤ 3 µm.
  5. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, wobei die mehrphasige Mikrostruktur umfasst (in Vol.-%) Restaustenit 5 - 16, vorzugsweise unter 10% Bainit + bainitischer Ferrit + temperierter Martensit ≥ 80 polygonaler Ferrit ≤ 10 Martensit-Austenit-Konstituent (MA) ≤ 20%, vorzugsweise ≤ 16%, am meisten bevorzugt unter 10%
  6. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, wobei der Stahl umfasst: Nb 0,02 - 0,03
  7. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, wobei das Verhältnis (Mn + Cr) /(Si + Al) ≥ 1,6 ist.
  8. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, wobei die Menge von Si in der Größenordnung der Menge von Al oder größer als die Menge von Al ist, vorzugsweise Si > 1,1 Al, noch bevorzugter Si > 1,3 Al, oder sogar Si > 2 Al.
  9. Hochfestes kaltgewalztes Stahlblech nach einem der vorhergehenden Ansprüche, das nicht mit einer feuerverzinkten Schicht versehen ist.
  10. Verfahren zum Herstellen eines hochfesten kaltgewalzten Stahlblechs nach einem der vorhergehenden Ansprüche, umfassend die Schritte:
    a) Bereitstellen eines kaltgewalzten Stahlstreifens mit einer Zusammensetzung wie in einem der vorhergehenden Ansprüche angegeben
    b) Glühen des kaltgewalzten Stahlstreifens bei einer Temperatur oberhalb der Ac3-Temperatur, um den Stahl vollständig zu austenitisieren, gefolgt von
    c) Abkühlen des kaltgewalzten Stahlstreifens von der Glühtemperatur, Tan, auf eine Kühlstoptemperatur einer Schnellabkühlung, TRC, die zwischen 360 und 460°C liegt, bevorzugt zwischen 380 und 420°C, bei einer Kühlrate, die ausreichend ist, um Ferritbildung zu verhindern, wobei die Kühlrate 20-100°C/s beträgt, gefolgt von
    d) Austempern des kaltgewalzten Stahlstreifens bei einer Überalterungs-/Austempertemperatur, TOA, die zwischen 360 und 460 °C liegt, vorzugsweise zwischen 380 und 420°C, und
    e) Abkühlen des kaltgewalzten Stahlstreifens auf Raumtemperatur,
    wobei der Stahl ein hochdehnfähiger Stahl mit einer Festigkeits-Dehn-Balance von Rm x A80 ≥ 13000 MPa%, bevorzugt ≥ 15000 MPa% ist.
  11. Verfahren zum Herstellen eines hochfesten kaltgewalzten Stahlblechs nach einem der Ansprüche 1 bis 9, umfassend die Schritte:
    a) Bereitstellen eines kaltgewalzten Stahlstreifens mit einer Zusammensetzung wie in einem der vorhergehenden Ansprüche angegeben,
    b) Glühen des kaltgewalzten Stahlstreifens bei einer Temperatur oberhalb der Ac3-Temperatur, um den Stahl vollständig zu austenitisieren, gefolgt von
    c) Abkühlen des kaltgewalzten Stahlstreifens von der Glühtemperatur, Tan, auf eine Kühlstoptemperatur einer Schnellabkühlung, TRC < TMS, wobei TMS zwischen 300 und 400°C liegt, bevorzugt zwischen 340 und 370°C, bei einer Kühlrate, die ausreichend ist, um Ferritbildung zu verhindern, wobei die Kühlrate 20-100°C/s beträgt, gefolgt von
    d) Austempern des kaltgewalzten Stahlstreifens bei einer Überalterungs-/Austempertemperatur, TOA, die zwischen 360 und 460 °C liegt, vorzugsweise zwischen 380 und 420°C, bevorzugt TOA > TRC, und
    e) Abkühlen des kaltgewalzten Stahlstreifens auf Raumtemperatur,
    wobei das Stahlblech ein Stahlblech mit hoher Lochaufweitung mit einer Streckbarkeit von Rm x λ ≥ 50000 MPa%, bevorzugt ≥ 55000 MPa % ist.
  12. Verfahren zum Herstellen eines hochfesten kaltgewalzten Stahlblechs gemäß Anspruch 10 und 11, wobei
    in Schritt b) das Glühen bei einer Glühtemperatur, Tan, durchgeführt wird, die zwischen 910 und 930°C liegt, während einer Glühhaltezeit, tan, die zwischen 150 und 200s liegt, vorzugsweise 180 s,
    in Schritt c) das Abkühlen gemäß einem Abkühlmuster durchgeführt wird, das zwei separate Kühlraten aufweist; eine erste Kühlrate, CR1, von 80-100°C/s, vorzugsweise von 85 - 95°C/s, bevorzugt um 90°C/s, auf eine Temperatur, die zwischen 530 bis 570°C liegt, bevorzugt 550°C, und eine zweite Kühlrate, CR2, von 35-45°C, bevorzugt um 40°C/s, auf die Stoptemperatur der Schnellabkühlung, TRC, und
    in Schritt d) das Austempern des Stahls in einem Zeitintervall von 150-600s durchgeführt wird, bevorzugt 180-540s.
  13. Verfahren zum Herstellen eines hochfesten kaltgewalzten Stahlblechs gemäß den Ansprüchen 10 und 11, wobei zwischen den Schritten c) und d) keine Erhitzung von außen auf das Stahlblech angewandt wird.
EP13717208.6A 2012-03-30 2013-04-02 Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung eines solchen stahlblechs Active EP2831299B2 (de)

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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
WO2025087716A1 (en) * 2023-10-26 2025-05-01 Tata Steel Nederland Technology B.V. High strength steel sheet with excellent hole expandability and method of producing the same

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EP2831299B2 (de) 2012-03-30 2020-04-29 Voestalpine Stahl GmbH Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung eines solchen stahlblechs
SE1651545A1 (en) * 2016-11-25 2018-03-06 High strength cold rolled steel sheet for automotive use
KR20210127922A (ko) * 2019-02-18 2021-10-25 타타 스틸 이즈무이덴 베.뷔. 기계적 특성이 개선된 고강도 강
US12286682B2 (en) 2019-04-30 2025-04-29 Tata Steel Nederland Technology B.V. High strength steel product and a process to produce a high strength steel product
PT3754036T (pt) 2019-06-17 2022-04-20 Tata Steel Ijmuiden Bv Tratamento térmico de tira de aço laminada a frio de alta resistência
PT3754037T (pt) 2019-06-17 2022-04-19 Tata Steel Ijmuiden Bv Método de tratamento térmico de uma tira de aço laminada a frio de alta resistência
EP3754035B2 (de) 2019-06-17 2025-04-30 Tata Steel IJmuiden B.V. Verfahren zur wärmebehandlung eines kaltgewalzten stahlbandes
EP3754034B1 (de) 2019-06-17 2022-03-02 Tata Steel IJmuiden B.V. Wärmebehandlung von kaltgewalztem stahlband
SE545209C2 (en) * 2020-12-23 2023-05-23 Voestalpine Stahl Gmbh Coiling temperature influenced cold rolled strip or steel
EP4490329A1 (de) * 2022-03-10 2025-01-15 Tata Steel Nederland Technology B.V. Hochfestes stahlblech mit hervorragender lochdehnbarkeit und herstellungsverfahren dafür

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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
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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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WO2025087716A1 (en) * 2023-10-26 2025-05-01 Tata Steel Nederland Technology B.V. High strength steel sheet with excellent hole expandability and method of producing the same

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