EP2690184B1 - 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
EP2690184B1
EP2690184B1 EP12178332.8A EP12178332A EP2690184B1 EP 2690184 B1 EP2690184 B1 EP 2690184B1 EP 12178332 A EP12178332 A EP 12178332A EP 2690184 B1 EP2690184 B1 EP 2690184B1
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temperature
weight
cold
strip
content
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German (de)
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EP2690184A1 (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 PCT/EP2013/065838 priority patent/WO2014016421A1/fr
Priority to CN201380048837.7A priority patent/CN104641008B/zh
Priority to JP2015523569A priority patent/JP6202579B2/ja
Priority to US14/417,659 priority patent/US20150218684A1/en
Publication of EP2690184A1 publication Critical patent/EP2690184A1/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 flat steel product with a tensile strength Rm of at least 1400 MPa and an elongation A80 of at least 5%. Products of this type are characterized by very high strength in combination with good elongation properties and as such are particularly suitable for the production of components for motor vehicle bodies.
  • the invention also relates to a method for producing a flat steel product according to the invention.
  • flat steel product is understood here to mean steel sheets or steel strips produced by a rolling process, as well as blanks and the like separated therefrom.
  • alloy contents are only given here in “%”, this always means “% by weight”, unless expressly stated otherwise.
  • a process for the production of a flat steel product that has tensile strengths of significantly more than Should have 1000 MPa.
  • a steel melt containing (in% by weight) 0.0005-1% C, 0.5-10% Cu, up to 2% Mn, up to 5% Si, up to 0.5 % Ti, up to 0.5% Nb, up to 5% Ni, up to 2% Al and the remainder iron and unavoidable impurities due to manufacturing.
  • the melt is poured into a strip, the thickness of which is max. 10 mm and which is quickly cooled to a temperature of at most 1000 ° C by sprinkling with water or a water-air mixture.
  • the cast strip is then hot rolled at a usual reduction rate.
  • the hot rolling is ended at a final temperature at which all of the copper is still in solid solution in the ferrite and / or austenite matrix.
  • the tape is then subjected to a rapid cooling step to keep the copper in supersaturated solid solution in the ferrite and / or austenite solution.
  • the hot strip obtained in this way can be rolled into a cold strip with a degree of cold rolling of 40-80%.
  • This cold strip is then subjected to a recrystallizing annealing, in which it is brought as quickly as possible to an annealing temperature in the range of 840 ° C. and held there in order to dissolve as much of the copper contained in the steel as possible.
  • Another method for producing an extremely strong cold strip is from the US 7,591,977 B2 known. According to this process, a hot strip containing (in% by weight) 0.1-0.25% C, 1.0-2.0% Si and 1.5-3.0% Mn with a cold rolling degree of 30-70 % rolled into a cold strip, which is then subjected to a continuous heat treatment.
  • a first annealing step the cold strip is heated to a first annealing temperature above its Ar3 temperature in order to dissolve the carbides present in the cold strip. This is followed by cooling to a second annealing temperature, starting from the first annealing temperature and at a cooling rate of at least 10 ° C./s.
  • This second annealing step which is carried out to form bainite, 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 of polygonal ferrite.
  • the aim is that the structure is as completely bainitic as possible and that other structural components are only present in traces.
  • the cold strip produced in this way achieves tensile strengths of up to 1180 MPa with an elongation of at least 9% and, if necessary, can be covered with a metallic layer that protects against corrosion.
  • a high-strength cold-rolled steel sheet is known, which is made from a steel with (in% by weight) 0.17-0.73% C, up to 3% Si, 0.5-3.0% Mn, up to 0.1% P, up to 0.07% S, up to 3.0% Al, up to to 0.010% N and in each case optional contents of Cr of 0.05-5,%, 0.005-1.0% V, 0.005-0.5% Mo, 0.01-0.1% Ti, 0.01-0 , 1% Nb, 0.0003-0.0050% B, 0.05-2.0% Ni, 0.05-2.0% Cu, 0.001-0.005% Ca and 0.001-0.005% REM, remainder iron and unavoidable impurities, the sum of the Al and Si contents should be at least 0.7%.
  • the sheet metal assembled in this way has a structure which (in area%) consists of 10-90% lower bainite and martensite and a total martensite content of up to 75% and 5-50% residual austenite.
  • the cold-rolled sheet undergoes a heat treatment after cold rolling, in which it is initially annealed for 15 - 600 s at an annealing temperature above its Ac3 temperature and then at a cooling rate of at least 5 ° C / s to 350 - 490 ° C amounting first holding temperature is cooled, at which it is held for 15 - 1000 s. The sheet is then cooled to a second holding temperature of 200-350 ° C in order to be held there for a period of 15-1000 s.
  • the object of the invention was to create a cold-rolled flat steel product that can be produced in a simple and reliable manner and has an optimized combination of further increased strength and good deformability.
  • a method for producing such a cold-rolled flat steel product should be mentioned.
  • the solution according to the invention to the above-mentioned object consists in that at least the work steps specified in claim 9 are carried out to produce a cold-rolled flat steel product according to the invention.
  • the cold-rolled flat steel product according to the invention is characterized in that it has (in% by weight) C: 0.27-0.60%, Si: 0.4-2.5%, Mn: 0.4-3.0 %, Cr: 0.3 - 2% and optionally made of Al: up to 3.0%, Ni: up to 1.0%, Cu: up to 2.0%, Mo: up to 0.4%, Co: up to 1.5%, Ti: up to 0.2%, Nb: up to 0.2%, V: up to 0.5%, and the remainder consists of iron and unavoidable impurities.
  • the structure of the flat steel product according to the invention in the cold-rolled state consists of at least 20% by volume of bainite, 10-35% by volume of retained austenite and the remainder of martensite, whereby it goes without saying that in the structure of the flat steel product, technically unavoidable traces of others Structural components can be present.
  • a cold-rolled flat steel product according to the invention of this type regularly achieves tensile strengths Rm of at least 1400 MPa and an elongation A80 of at least 5%.
  • the C content of the retained austenite is typically more than 1.0% by weight.
  • a steel strip according to the invention has a three-phase structure, the dominant component of which is bainite and which also consists of retained austenite and the remainder of martenisite.
  • the bainite content is at least 60% by volume and the residual austenite content in the range of 10-25% by volume, with the rest of the structure also being filled with martensite.
  • the optimal martensite content is at least 10% by volume.
  • a structure composed in this way produces the best combination of Rm * A80 with the required tensile strength.
  • the retained austenite is predominantly film-like with small globular islands of blocky retained austenite with a grain size ⁇ 5 ⁇ m , so that the retained austenite has high stability and, as a result, a low tendency to undesired transformation into martensite and enables the TRIP effect .
  • Cold strip produced according to the invention regularly reaches tensile strengths Rm of more than 1400 MPa, with elongations A80 which are also regularly above 5%.
  • the quality Rm * A80 of flat steel products according to the invention is regularly above 7000 MPa *%, with qualities Rm * A80 of at least 13500 MPa *% typically being achieved.
  • a cold strip according to the invention has an optimal combination of extreme strength and sufficient formability.
  • the martensite start temperature ie the temperature from which martensite is formed in the steel processed according to the invention, can according to the method described in the article Thermodynamic Exatrapolation and Martensite-Start-Temperature of Substitutionally Alloyed Steels "by H. Bhadeshia, published in Metal Science 15 (1981), pages 178-180 explained procedure.
  • the C content of the flat steel product according to the invention has been set to at least 0.27% by weight.
  • the C content is at least 0.28% by weight.
  • the effects achieved by the comparably high carbon content can be used particularly reliably if the C content is in the range of 0.27-0.4% by weight or 0.28-0.4% by weight.
  • 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 wt.% Cu, in particular at least 0.2 wt.% Cu can be present in the flat steel product according to the invention.
  • Cu makes a particularly effective contribution to strength when it is present in the flat steel product according to the invention in contents of at least 0.55% by weight, with the negative effects of the presence of Cu being limited by reducing the Cu content to at most 1.5 Wt .-% is limited.
  • Cr lowers the martensite start temperature and suppresses the tendency of the bainite to transform into pearlite or cementite. Furthermore, Cr promotes ferritic conversion in contents up to the upper limit of a maximum of 2 wt. % is limited. In order to effectively utilize the positive influence of Cr, at least 0.3% by weight of Cr is present in the flat steel product according to the invention.
  • Ti, V or Nb can support the creation of a finer-grain structure and promote the bainitic transformation.
  • these micro-alloy elements contribute to the increase in hardness through the formation of precipitates.
  • 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 the range of 0.002-0.15% by weight, in particular does not exceed 0.1% by weight.
  • Si is present in a flat steel product according to the invention in contents of 0.4-2.5% by weight and causes a significant solid solution strengthening.
  • the Si content can be set to at least 1.0% by weight. It can also be used for To avoid negative influences, it is advisable to limit the Si content to a maximum of 2% by weight.
  • Al can partially replace the Si content in the steel processed according to the invention.
  • Al like Si, has a deoxidizing effect in steel production.
  • a minimum content of 0.01% by weight Al can be provided.
  • Higher contents of Al prove to be expedient, for example, when the hardness or tensile strength of the steel is to be adjusted to a lower value in favor of improved deformability by adding Al.
  • Si and Al Another function of Si and Al is to suppress the formation of carbide in the bainite and thus to stabilize the retained austenite through dissolved C.
  • the positive influences of the simultaneous presence of Al and Si can be used particularly effectively if the Si and Al contents meet the following condition within the limits specified according to the invention:% Si + 0.8% Al> 1.2% by weight ( with% Si: respective Si content in% by weight,% Al: respective Al content in% by weight).
  • the formation of the structure specified according to the invention can in particular be ensured by the fact that the Mn, Cr, Ni, Cu and C contents of the steel processed according to the invention and accordingly the Mn, Cr, Ni, Cu and C contents of the steel flat product according to the invention meet the following condition 1 ⁇ 0.5% Mn + 0.167% Cr + 0.125% Ni + 0.125% Cu + 1.334% C ⁇ 2, with% Mn the respective Mn content in% by weight, with% Cr the respective Cr content in wt .-%, with% Ni the respective Ni content in wt .-%, with% Cu the respective Cu content in wt .-% and with% C the respective C content in wt .-%.
  • the intermediate product cast from a steel composed according to the invention is first brought to a temperature or kept at a temperature sufficient to end the hot rolling carried out starting from this temperature at a hot rolling end temperature in the range of 830-1000 ° C lie.
  • the hot strip cools down on the roller table following the roll stand in question. After the roller table, the hot strip runs into a coiler, in which it is wound into a coil.
  • the coiling temperature must be at least 560 ° C so that a relatively soft hot strip structure made of ferrite and pearlite is created.
  • An optimal temperature profile for this purpose is obtained when the final hot rolling temperature is in the range from 850 to 950 ° C, in particular in the range from 880 to 950 ° C.
  • the intermediate product is typically heated to a temperature in the range of 1100-1300 ° C. or kept at this temperature before hot rolling.
  • the structure of the hot strip obtained in this way exists mainly made of ferrite and pearlite. The risk of grain boundary oxidation occurring can be minimized by limiting the coiling temperature to a maximum of 750 ° C.
  • the hot strip After coiling, the hot strip is cold-rolled, it being understood that the hot strip can of course be descaled chemically or mechanically in the usual way before cold-rolling.
  • the cold rolling takes place 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, maintaining a correspondingly high degree of cold rolling also results in a better surface quality. Cold rolling degrees of at least 50% have proven to be particularly favorable for this.
  • the cold strip obtained according to the invention undergoes an annealing cycle in one continuous run, in which it is heated to a temperature of at least 800 ° C., preferably at least 830 ° C., in a first annealing phase.
  • This first annealing phase lasts at least long enough for the cold strip to be completely austenitized. This typically takes 50 - 150 s.
  • 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 470 ° C or less and higher than that Martensite start temperature MS, from which martensite occurs in the structure of the cold strip.
  • the range of 300-420 ° C, in particular 330-420 ° C can be used as a guide for the range in which the holding temperature should be.
  • the cold strip is held in the holding temperature range in the second annealing phase until the structure of the cold strip has changed to at least 20% by volume in bainite.
  • the holding can be carried out as isothermal holding at the holding temperature reached during cooling or as a slow temperature decrease within the holding temperature range.
  • the flat steel product produced according to the invention can be covered in the usual way with a metallic protective layer. 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 within the scope of this annealing.
  • a metallic protective layer 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 within the scope of this annealing.
  • the invention is explained in more detail below on the basis of exemplary embodiments.
  • the correspondingly composed steel melts are cast in a conventional manner to form a strand from which slabs have been separated.
  • the thin slabs were then reheated to a reheating temperature in an equally conventional manner.
  • the heated slabs were hot-rolled into hot strips with a thickness of 2 mm in a likewise conventional hot-rolling stage.
  • the final hot rolling temperature was in the range of 830-900 ° C. Starting from this temperature, the hot strips were cooled to a coiling temperature above 560 ° C. and then reeled into coils.
  • the hot strips obtained in this way have been descaled after coiling and, after descaling, have been cold-rolled to cold strip at cold rolling degrees of 50%.
  • a large 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 lay.
  • the cold strips were held at this temperature for a period of 120 seconds until they were completely heated.
  • the holding temperatures T2 were one first batch of tests at 300 ° C, 310 ° C, 330 ° C, 340 ° C, 375 ° C, 390 ° C and 410 ° C. At the respective holding temperature T2, the cold strip samples were held for an annealing period t2.
  • Fig. 1 the achieved tensile strengths Rm are plotted against the respective annealing temperature T2. It can be seen that the cold strip specimens made from steel S5 only achieve the required minimum tensile strength of 1400 MPa under certain annealing conditions, while the tensile strengths of the cold strip specimens made from the other steels were always safely above the minimum limit of 1400 MPa. The reason for this was determined to be the comparatively low carbon content of steel S5, which is at the lower limit of the content range specified according to the invention.
  • Fig. 2 the tensile strengths of the cold strip samples produced from steel S4 are plotted over the annealing duration t2 of the second annealing stage. It can be seen that the cold strip samples held at a holding temperature of 310 ° C, 330 ° C and 350 ° C, i.e. in the holding temperature range of 310 - 350 ° C, reached the required tensile strength Rm of 1400 MPa regardless of the respective annealing duration t2.
  • Fig. 3 the tensile strengths of the cold strip samples produced from steel S5 are plotted in the same way 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, i.e. in the holding temperature range of 350 - 390 ° C, met the requirements Achieve tensile strength Rm of 1400 MPa if the annealing time t2 is shorter than 145 s.
  • Fig. 4 the elongation A80 of the cold strip samples produced from steel S4 is plotted over the annealing duration t2 of the second annealing stage.
  • elongation A80 of the cold strip samples produced from steel S5 is plotted over the annealing duration t2 of the second annealing stage.
  • the cold strip samples achieve the required elongation A80 of at least 5% regardless of their respective holding temperature T2 and regardless of the respective annealing duration t2. Accordingly, if a short annealing time and suitably low holding temperatures T2 are maintained, a cold-rolled flat steel product according to the invention can also be produced from steel S5 despite its comparatively low C content, in which a high tensile strength Rm is combined with sufficient elongation A80.
  • FIG. 6 an enlargement of a cross section of a cold strip according to the invention is shown in a detail.
  • retained austenite blocks RA-b are marked by way of example and a point is highlighted by a circle where film-like retained austenite RA-f is present in a lamellar layer.
  • Table 1 steel C Table 1 steel C.

Claims (12)

  1. Produit plat en acier laminé à froid, avec une résistance à la traction Rm d'au moins 1 400 MPa et un allongement A80 d'au moins 5 %, se composant de, en % en poids :
    C : 0,27 - 0,60 %,
    Si : 0,4 - 2,5 %,
    Mn : 0,4 - 3,0 %,
    Cr : 0,3 - 2 %,
    ainsi que respectivement au choix
    Al jusqu'à 3,0 %
    Ni : jusqu'à 1,0 %,
    Cu : jusqu'à 2,0 %,
    Mo : jusqu'à 0,4 %,
    Co : jusqu'à 1,5 %,
    Ti : jusqu'à 0,2 %,
    Nb : jusqu'à 0,2 %,
    V : jusqu'à 0,5 %,
    et le reste étant constitué de fer et d'impuretés inévitables, la structure du produit plat en acier se composant au moins de 20 % en volume de bainite, de 10 - 35 % en volume d'austénite résiduelle étant essentiellement de type pelliculaire avec des petits îlots globulaires d'austénite résiduelle compacte ayant une granulométrie < 5 µm, et le reste étant constitué de martensite.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que sa teneur en Si est d'au moins 1,0 % en poids.
  3. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Al est au moins de 0,01 % en poids.
  4. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cu est au moins de 0,2 % en poids.
  5. Produit plat en acier selon la revendication 4, caractérisé en ce que sa teneur en Cu est au moins de 0,55 % en poids.
  6. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que ses teneurs en Mn, Cr, Ni, Cu et C remplissent la condition suivante : 1 < 0,5 % Mn + 0,167 % Cr + 0,125 % Ni + 0,125 % Cu + 1,334 % C < 2
    Figure imgb0003
    avec: % Mn : teneur respective en Mn en % en poids,
    % Cr : teneur respective en Cr en % en poids,
    % Ni : teneur respective en Ni en % en poids,
    % Cu : teneur respective en Cu en % en poids,
    % C : teneur respective en C en % en poids.
  7. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa structure contient au moins 50 % en volume de bainite.
  8. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa structure contient 10 - 25 % en volume d'austénite résiduelle.
  9. Procédé pour la fabrication d'un produit plat en acier obtenu selon l'une des revendications 1 à 8, comportant les étapes de travail suivantes :
    - Mise à disposition d'un produit intermédiaire sous la forme d'une brame, d'une brame mince ou d'une bande coulée qui se compose de, en % en poids : C : 0,27 - 0,60 %, Si : 0,4 - 2,5 %, Mn : 0,4 - 3,0 %, Cr : 0,3 - 2 %, ainsi que respectivement au choix Al: jusqu'à 3,0 %, Ni : jusqu'à 1,0 %, Cu : jusqu'à 2,0 %, Mo : jusqu'à 0,4 %, Co : jusqu'à 1,5 %, Ti : jusqu'à 0,2 %, Nb : jusqu'à 0,2 %, V : jusqu'à 0,5 % et le reste étant constitué de fer et d'impuretés inévitables ;
    - Réchauffement du produit intermédiaire à une température comprise dans une plage de 1 100 à 1 300 °C ou maintien de ce produit intermédiaire à cette température ;
    - Laminage à chaud du produit intermédiaire en une bande à chaud en une ou plusieurs passes de laminage, la bande à chaud obtenue, en sortant de la dernière passe de laminage, présentant une température finale de laminage à chaud de 830 - 1 000 °C ;
    - Bobinage de la bande à chaud obtenue à une température d'embobinage qui se situe entre la température finale de laminage à chaud et 560 °C ;
    - Laminage à froid de la bande à chaud en une bande à froid avec un degré de laminage à froid d'au moins 30 % ;
    - Traitement thermique de la bande à froid obtenue, la bande à froid, dans le cadre du traitement thermique,
    - étant réchauffée à une température de recuit d'au moins 800 °C, la bande à froid étant maintenue à la température de recuit pendant une durée de recuit de 50 - 150 s,
    - étant refroidie, à partir de la température de recuit, avec au moins une vitesse de refroidissement de 8 °C/s, à une température de maintien qui se situe dans une plage de température de maintien, dont la limite supérieure est de 470 °C et dont la limite inférieure est supérieure à la température de démarrage de la martensite MS, à partir de laquelle la martensite se forme dans la structure de la bande à froid, et
    - étant maintenue à une température de maintien pendant un laps de temps suffisant à former, dans la structure de la bande à froid, au moins 20 % en volume de bainite.
  10. Procédé selon la revendication 9, caractérisé en ce que la température finale de laminage à chaud est de 850 - 950 °C.
  11. Procédé selon l'une des revendications 9 ou 10, caractérisé en ce que la température de maintien est de 300 - 420 °C.
  12. Procédé selon l'une des revendications 9 à 11, caractérisé en ce que la bande à froid, après le traitement thermique, est recouverte d'une couche de protection métallique.
EP12178332.8A 2012-07-27 2012-07-27 Cold rolled steel flat product and method for its production Active 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
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
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
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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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
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EP2690184A1 (fr) 2014-01-29
US20150218684A1 (en) 2015-08-06
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JP6202579B2 (ja) 2017-09-27
CN104641008A (zh) 2015-05-20

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