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EP2690184A1 - Cold rolled steel flat product and method for its production - Google Patents

Cold rolled steel flat product and method for its production Download PDF

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Publication number
EP2690184A1
EP2690184A1 EP12178332.8A EP12178332A EP2690184A1 EP 2690184 A1 EP2690184 A1 EP 2690184A1 EP 12178332 A EP12178332 A EP 12178332A EP 2690184 A1 EP2690184 A1 EP 2690184A1
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Prior art keywords
cold
temperature
content
hot
flat steel
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EP12178332.8A
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German (de)
English (en)
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EP2690184B1 (fr
Inventor
Brigitte Dr. Hammer
Thomas Dr. Heller
Frank Dr. Hisker
Rudolf Prof.Dr.-Ing. Kawalla
Grzegorz Korpala
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Priority to EP12178332.8A priority Critical patent/EP2690184B1/fr
Priority to JP2015523569A priority patent/JP6202579B2/ja
Priority to PCT/EP2013/065838 priority patent/WO2014016421A1/fr
Priority to CN201380048837.7A priority patent/CN104641008B/zh
Priority to US14/417,659 priority patent/US20150218684A1/en
Publication of EP2690184A1 publication Critical patent/EP2690184A1/fr
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Publication of EP2690184B1 publication Critical patent/EP2690184B1/fr
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    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
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    • 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
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    • 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
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
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    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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 invention relates to a cold-rolled steel flat product having a tensile strength Rm of at least 1400 MPa and an elongation A80 of at least 5%. Products of this type are characterized by a very high strength in combination with good elongation properties and are suitable as such, in particular for the production of components for motor vehicle bodies.
  • the invention likewise relates to a method for producing a flat steel product according to the invention.
  • alloy contents are stated here only in “%”, this always means “% by weight”, unless expressly stated otherwise.
  • the cast strip is hot rolled at a conventional reduction rate. Hot rolling is terminated at a final temperature at which all copper is still in solid solution in the ferrite and / or austenite matrix. Then, the strip is subjected to a rapid cooling step to hold the copper in supersaturated solid solution in the ferrite and / or austenite solution. After coiling into a coil, a cold strip can be rolled from the hot strip thus obtained with a cold rolling amount of 40-80%. This cold strip is then subjected to a recrystallizing annealing, where it is brought as quickly as possible to a lying in the range of 840 ° C annealing temperature and held there to bring the largest possible proportion of the copper contained in the steel in solution.
  • Another method for producing an extremely strong cold strip is from US 7,591,977 B2 known.
  • a hot rolled strip (containing wt%) of 0.1-0.25% C, 1.0-2.0% Si and 1.5-3.0% Mn having a cold rolling degree of 30-70 rolled to a cold-rolled strip, which is then subjected to a continuous heat treatment.
  • the cold strip is heated in a first annealing step to a lying above its Ar3 temperature first annealing temperature to bring in the cold strip carbides in solution.
  • a cooling proceeding from the first annealing temperature takes place, with a cooling rate of at least 10 ° C./s, to a second annealing temperature.
  • This second annealing step carried out for bainite formation is carried out until the structure of the cold strip consists of at least 60% bainite and at least 5% residual austenite and the remainder polygonal ferrite.
  • the aim is that the structure is as completely as possible bainitic and other structural constituents are present in traces at best.
  • the cold-rolled strip obtained in this way achieves tensile strengths of up to 1180 MPa at an elongation of at least 9% and, if necessary, can be covered with a metallic, corrosion-protective layer.
  • the object of the invention was to provide a cold rolled flat steel product which is manufactured in a simple and reliable way can and has an optimized combination of further increased strength and good ductility.
  • a method for producing such a cold-rolled steel flat product should be mentioned.
  • the solution according to the invention of the abovementioned object consists in that at least the working steps specified in claim 12 are run through to produce a cold-rolled flat steel product according to the invention.
  • a steel strip according to the invention has a three-phase structure, the dominant constituent of which is bainite and which, moreover, consists of retained austenite and the remainder of martensite.
  • the bainite content is at least 60% by volume and the residual austenite content is in the range from 10% to 25% by volume, the remainder of the microstructure in each case also being filled with martensite.
  • the optimum martensite content is at least 10% by volume.
  • Such a composite structure gives the best combination of Rm * A80 at the required tensile strength.
  • the retained austenite is in a cold strip according to the invention predominantly film-like with small globular islands of blocky retained austenite with a particle size ⁇ 5 microns, so that the retained austenite has a high stability and, consequently, a low tendency to undesirable conversion to martensite and allows the TRIP effect.
  • Cold rolled strip produced according to the invention regularly reaches tensile strengths Rm of more than 1400 MPa, with strains A80 which likewise regularly exceed 5%. Accordingly, the quality Rm * A80 of flat steel products according to the invention is regularly above 7000 MPa *%, with grades Rm * A80 of at least 13500 MPa *% being typically achieved.
  • An inventive cold strip as such has a optimal combination of extreme strength and sufficient formability.
  • the martensite starting temperature ie the temperature at which martensite is formed in steel processed according to the invention, can be determined according to the Thermodynamic Exatrapolation and Martensite Start-Temperature of Substituted Alloyed Steels "by H. Bhadeshia, published in Metal Science 15 (1981), pages 178-180 explained procedure can be calculated.
  • the C content of the flat steel product according to the invention can be set to at least 0.25% by weight, in particular at least 0.27% by weight or at least 0.28% by weight, wherein the be used by the comparably high carbon content effects particularly safe when the C content in the range of> 0.25 to 0.5 wt .-%, in particular 0.27 to 0.4 wt .-% or 0.28 - 0.4 wt .-%, is.
  • the strength-increasing effect of copper can also be used in a cold-rolled flat steel product according to the invention.
  • a minimum content of 0.15% by weight of Cu, in particular at least 0.2% by weight of Cu may be present in the flat steel product according to the invention.
  • a particularly effective contribution to strength is made by Cu, if it contains at least 0.55 wt .-% in the flat steel product according to the invention is present, whereby negative effects of the presence of Cu can be limited by limiting the Cu content to at most 1.5% by weight.
  • the martensite start temperature can be lowered and the tendency of the bainite to convert to pearlite or cementite can be suppressed.
  • Cr at levels up to the upper limit of not more than 2% by weight given in accordance with the invention promotes the ferritic transformation, with optimum effects of the presence of Cr in the cold-rolled flat steel product of the invention when the Cr content is reduced to 1.5% by weight. % is limited.
  • the positive influence of Cr can be used particularly effectively if at least 0.3% by weight of Cr is present in the flat steel product according to the invention.
  • Ti, V or Nb which is also optional, can help to create finer-grained microstructures and promote bainitic transformation.
  • these microalloying elements carry through the Formation of precipitates to increase hardness.
  • the positive effects of Ti, V and Nb in the cold-rolled flat steel product according to the invention can be used particularly effectively if their content is in each case in the range from 0.002 to 0.15% by weight, in particular 0.1% by weight does not exceed.
  • Si is present in a flat steel product according to the invention in contents of 0.4-2.5% by weight and causes a marked solid solution hardening.
  • the Si content can be set to at least 1.0 wt .-%.
  • Al can partially replace the Si content in the steel processed according to the invention. At the same time, Al and Si are deoxidizing during steelmaking. For this purpose, a minimum content of 0.01 wt .-% Al can be provided. Higher contents of Al prove to be useful, for example, if the addition of Al should set the hardness or tensile strength of the steel to a lower value in favor of improved ductility.
  • Si and Al Another function of Si and Al is to suppress carbide formation in the bainite and thus to stabilize the retained austenite by dissolved C.
  • the formation of the structure prescribed according to the invention can be ensured, in particular, by the contents of the steel processed according to the invention and, accordingly, the contents of the flat steel product according to the invention of Mn, Cr, Ni, Cu and C having the following condition 1 ⁇ 0 . 5 % Mn + 0 . 167 % Cr + 0 . 125 % Ni + 0 . 125 % Cu + 1 .
  • 334 % C ⁇ 2 meet, where with% Mn the respective Mn content in wt .-%, with% Cr of the respective Cr content in wt .-%, with% Ni of the respective Ni content in wt .-%, with% Cu of the respective Cu content in wt .-% and with% C of the respective C content in wt .-% are designated.
  • the precursor cast from a composite steel according to the invention is first brought to a temperature or maintained at a temperature sufficient to terminate the hot rolling carried out from said temperature at a hot rolling end temperature in the range of 830-1000 ° C lie.
  • the hot strip is cooled on the roller table following the relevant stand. This is followed by the roller table Hot strip in a coiler, where it is wound into a coil.
  • the reel temperature must be at least 560 ° C, so that a relatively soft hot-band structure of ferrite and pearlite is formed.
  • An optimum temperature profile for this purpose results when the hot rolling end temperature is in the range of 850-950 ° C., in particular in the range of 880-950 ° C.
  • the precursor is heated or maintained at a temperature in the range of 1100-1300 ° C temperature before hot rolling.
  • the structure of the hot strip thus obtained consists mainly of ferrite and pearlite. The risk of grain boundary oxidation can be minimized by limiting the coiler temperature to a maximum of 750 ° C.
  • the hot strip After coiling, the hot strip is cold rolled, wherein the hot strip can of course be descaled chemically or mechanically before cold rolling in the usual way.
  • the cold rolling is carried out with a degree of cold rolling of at least 30%, in particular at least 45%, in order to accelerate the recrystallization and conversion during the subsequent annealing. In general, a better surface quality is achieved by maintaining a correspondingly high degree of cold rolling. Cold rolling degrees of at least 50% have proven to be particularly favorable for this purpose.
  • the cold strip according to the invention undergoes an annealing cycle in a continuous pass, in which it is heated in a first annealing phase to a temperature of at least 800 ° C., preferably at least 830 ° C. This first annealing phase lasts at least as long that the cold strip is completely austenitized. This typically requires 50-150 seconds.
  • the product is quenched, the cooling rate being at least 8 ° C / s, in particular 10 ° C / s.
  • the target temperature of this quenching is a holding temperature which is at most 470 ° C and higher than the martensite start temperature MS, starting from the martensite in the structure of the cold strip.
  • the range of 300-420 ° C, in particular 330-420 ° C can be used as an indication of the range in which the holding temperature should be.
  • the cold strip is kept in the holding temperature range in the second annealing phase, specifically until the structure of the cold strip has changed to at least 20% by volume in bainite.
  • the holding can be carried out as an isothermal hold on the holding temperature achieved during the cooling or as a slow decrease in temperature within the holding temperature range.
  • the flat steel product produced according to the invention can be treated in the usual way with a metallic protective layer be occupied. This can be done for example by hot dip coating. If an annealing is required before the application of the metallic coating, the heat treatment provided according to the invention can be carried out as part of this annealing.
  • the correspondingly assembled steel melts have been cast in a conventional manner into a strand from which slabs have been divided.
  • the thin slabs were then heated to a reheating temperature in a conventional manner as well.
  • the heated slabs were hot rolled in a conventional hot rolling mill to hot strip with a thickness of 2 mm.
  • the hot rolling end temperature was in the range of 830 - 900 ° C. Starting from this temperature, the hot strips were cooled to a lying above 560 ° C reel temperature and then coiled into coils.
  • the hot strips thus obtained are descaled after coiling and cold rolled after descaling at cold rolling degrees of 50% to cold strip.
  • a larger number of samples of these cold strips were then subjected to a heat treatment in which they were heated in a first annealing step at a heating rate of at least 1.9 ° C / s to a first annealing temperature in the range of 830-850 ° C was. At this temperature, the cold strips were held for a period of 120 seconds until fully warmed.
  • a quenching in which cold strips were quenched with a cooling rate of at least 8 ° C / s to a holding temperature T2, which was in the range of 350-420 ° C.
  • the holding temperatures T2 for a first batch of tests were 300 ° C, 310 ° C, 330 ° C, 340 ° C, 375 ° C, 390 ° C and 410 ° C.
  • the cold strip samples have been kept for an annealing period t2.
  • Fig. 1 the tensile strengths Rm achieved are plotted against the respective annealing temperature T2. It can be seen that the cold strip samples made of the steel S5 only achieved the required minimum tensile strength of 1400 MPa under certain annealing conditions, whereas the tensile strengths of the cold strip samples produced from the other steels always safely exceeded the minimum limit of 1400 MPa. The reason for this is the comparatively low carbon content of the steel S5, which is located at the lower limit of the content range prescribed according to the invention.
  • Fig. 2 the tensile strengths of the cold strip samples produced from the steel S4 are plotted over the annealing time t2 of the second annealing stage. It turns out that the cold strip samples held at a holding temperature of 310 ° C., 330 ° C. and 350 ° C., ie in the holding temperature range of 310 ° to 350 ° C., have reached the required tensile strength Rm of 1400 MPa irrespective of the respective annealing time t 2.
  • Fig. 3 the tensile strengths of the cold strip samples produced from the steel S5 are plotted over the annealing time t2 of the second annealing stage. It can be seen here that the cold strip samples held at a holding temperature of 350 ° C. and 390 ° C., ie in the holding temperature range of 350 ° -390 ° C., reach the required tensile strength R m of 1400 MPa if the annealing time t 2 is shorter than 145 s.
  • Fig. 4 the strain A80 of the cold strip samples produced from the steel S4 is plotted over the annealing time t2 of the second annealing stage.
  • Fig. 5 the strain A80 of the cold strip samples produced from the steel S5 is plotted over the annealing time t2 of the second annealing stage.
  • the cold strip samples have the required elongation A80 of at least 5%, regardless of their respective holding temperature T2 and independently of the respective holding temperature Reach annealing time t2. Accordingly, while maintaining a short annealing time and suitably low holding temperatures T2, a cold-rolled steel flat product according to the invention can be produced from the steel S5 despite its comparatively low C content, in which a high tensile strength Rm is combined with a sufficient elongation A80.
  • Fig. 6 is shown in a section of an enlargement of a cross section of a cold strip according to the invention.
  • residual austenite blocks RA-b are marked and a point is highlighted by an encircling, on which film-like retained austenite RA-f is present in a lamellar layering.
  • Table 1 stolen C Mn Si Cu Cr Ti Nb V al N other S1 0.52 1.48 0.40 1.51 0, 88 0, 009 - 0.093 1,400 - - S2 0.301 1.41 1.46 1.47 0.87 0,014 0.005 0.09 0,021 0.0015 Ni: 0.021 Mo: ⁇ 0.002 S3 0,505 1.50 0.40 0, 6 1.30 0.011 - 0.098 0,012 0,002 Ni: 0.63 Mo: 0.30 S4 0.384 1.97 0.41 0.57 1.37 0.0016 - ⁇ 0.0005 0,018 0.0014 Ni: 0.59 Mo: 0.30 S5 0.252 1.47 2.15 0.32 0.41 0,020 - 0.11 0.009 - Ni: 0.02 Mo: ⁇ 0.002 In% by weight, Remaining iron and unavoidable impurities

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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
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  • Heat Treatment Of Sheet Steel (AREA)
EP12178332.8A 2012-07-27 2012-07-27 Cold rolled steel flat product and method for its production Not-in-force EP2690184B1 (fr)

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EP12178332.8A EP2690184B1 (fr) 2012-07-27 2012-07-27 Cold rolled steel flat product and method for its production
JP2015523569A JP6202579B2 (ja) 2012-07-27 2013-07-26 冷間圧延による平鋼製品及びそれを製造するための方法
PCT/EP2013/065838 WO2014016421A1 (fr) 2012-07-27 2013-07-26 Produit plat en acier laminé à froid et son procédé de fabrication
CN201380048837.7A CN104641008B (zh) 2012-07-27 2013-07-26 冷轧扁钢产品及其制造方法
US14/417,659 US20150218684A1 (en) 2012-07-27 2013-07-26 Cold-Rolled Flat Steel Product and Method for the Production Thereof

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DE102017209982A1 (de) * 2017-06-13 2018-12-13 Thyssenkrupp Ag Hochfestes Stahlblech mit verbesserter Umformbarkeit
EP3418412A4 (fr) * 2016-02-19 2019-08-21 Nippon Steel Corporation Acier

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US11384415B2 (en) 2015-11-16 2022-07-12 Benteler Steel/Tube Gmbh Steel alloy with high energy absorption capacity and tubular steel product
WO2017109539A1 (fr) * 2015-12-21 2017-06-29 Arcelormittal Procédé de fabrication d'une tôle d'acier à haute résistance présentant une résistance et une formabilité améliorées et tôle d'acier à haute résistance obtenue par ce procédé
KR101822292B1 (ko) 2016-08-17 2018-01-26 현대자동차주식회사 고강도 특수강
KR101822295B1 (ko) 2016-09-09 2018-01-26 현대자동차주식회사 고강도 특수강
CN108546881B (zh) * 2018-05-16 2020-06-26 东北大学 一种无屈服平台冷轧中锰钢薄带的制备方法
DE102021119047A1 (de) 2021-07-22 2023-01-26 Thyssenkrupp Steel Europe Ag Verfahren zur Herstellung eines kaltgewalzten Stahlflachprodukts mit einem bainitischen Grundgefüge und kaltgewalztes Stahlflachprodukt mit einem bainitischen Grundgefüge

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EP3418412A4 (fr) * 2016-02-19 2019-08-21 Nippon Steel Corporation Acier
DE102017209982A1 (de) * 2017-06-13 2018-12-13 Thyssenkrupp Ag Hochfestes Stahlblech mit verbesserter Umformbarkeit

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JP2015528065A (ja) 2015-09-24
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US20150218684A1 (en) 2015-08-06
WO2014016421A1 (fr) 2014-01-30
EP2690184B1 (fr) 2020-09-02

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