EP2690183B1 - Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung - Google Patents

Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung Download PDF

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Publication number
EP2690183B1
EP2690183B1 EP12178330.2A EP12178330A EP2690183B1 EP 2690183 B1 EP2690183 B1 EP 2690183B1 EP 12178330 A EP12178330 A EP 12178330A EP 2690183 B1 EP2690183 B1 EP 2690183B1
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Prior art keywords
temperature
content
hot
flat steel
steel product
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EP12178330.2A
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German (de)
English (en)
French (fr)
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EP2690183A1 (de
Inventor
Brigitte Hammer
Thomas Heller
Frank Hisker
Rudolf Kawalla
Grzegorz Korpala
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to EP12178330.2A priority Critical patent/EP2690183B1/de
Priority to KR1020157005074A priority patent/KR20150038426A/ko
Priority to BR112015001456A priority patent/BR112015001456A2/pt
Priority to CN201380049258.4A priority patent/CN104662179B/zh
Priority to PCT/EP2013/065836 priority patent/WO2014016420A1/de
Priority to US14/417,685 priority patent/US20150203946A1/en
Priority to JP2015523568A priority patent/JP6154010B2/ja
Publication of EP2690183A1 publication Critical patent/EP2690183A1/de
Publication of EP2690183B1 publication Critical patent/EP2690183B1/de
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
    • 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
    • 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
    • C22C38/06—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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • C22C38/40—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
    • C22C38/46—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • 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

Definitions

  • the invention relates to a hot-rolled flat steel product with a product of tensile strength Rm and elongation A80 of at least 18000 MPa *%.
  • Flat steel 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 product of tensile strength Rm and elongation A80 is also referred to in technical jargon as "quality”.
  • the cast strip is hot rolled at a reduction rate of at least 10%.
  • the hot rolling is terminated at a final temperature at which all the copper is still in solid solution in the ferrite and / or austenite matrix.
  • the strip is subjected to a rapid cooling step to hold the copper in supersaturated solid solution in the ferrite and / or austenite solution.
  • the thus cooled tape is finally wound into a coil.
  • the copper precipitates cause precipitation hardening to achieve the desired strength level of the steel.
  • the copper content should increase the corrosion and embrittlement resistance of the steel by forming a protective oxide layer.
  • a hot strip with a tensile strength exceeding 1200 MPa and an elongation of up to 10% and a method for its production are known from US 2009/0107588 A1 known.
  • the steel should have a microstructure consisting of at least 75% bainite, at least 5% retained austenite and at least 2% martensite.
  • a suitably composed melt is cast into a precursor, which is then heated to more than 1150 ° C and then hot rolled at a hot rolling end temperature at which the steel is still fully austenitic.
  • the resulting hot strip is then cooled in three stages. In the first stage, the cooling takes place from a temperature which is above the Ar3 temperature of the steel, with a cooling rate of at least 70 ° C / s to a first intermediate temperature above 650 ° C.
  • cooling then takes place to a second intermediate temperature which is between the bainite start temperature, ie at which bainite begins to form in the steel, and below the limit temperature, which is 50 ° C. higher than the martensite start temperature, ie the temperature from which martensite forms in steel.
  • the cooling rate in this second stage of cooling is 20 - 90 ° C / s.
  • This is followed by a third cooling step, in which the hot strip is cooled to room temperature. The temperature at which this third stage of cooling starts becomes determined as a function of the respective cooling rate.
  • the hot strip has a microstructure containing 5-20% of retained austenite and 20-50% of bainite besides ferrite, with copper precipitates present in the structure which contribute to the strength of the resulting hot strip by precipitation hardening.
  • the hot strip produced and produced in this way has an elongation of up to 23% at strengths which lie in the range of 1000 MPa, so that altogether high quality values of more than 20,000 MPa *% are achieved.
  • hot rolled steel strip which contains (in wt%) 0.05-0.3% C, 0.03-1.0% Si, 1.5-3.5% Mn, up to 0.02 % P, up to 0.005% S, up to 0.15 Al, not more than 0.02% N, in each case 0.005-0.2% Nb and / or Ti and optionally further alloying elements.
  • the microstructure of this hot strip should be fine-grained bainite having a grain size of at most 3 microns and a proportion of not less than 90 area%.
  • a slab is cast from said steel, the slab reheated to up to 1200 ° C and then hot rolled from the slab a hot strip with a hot rolling end temperature of 800 ° C. Within two seconds after hot rolling, the hot strip is then cooled at a cooling rate of 20-150 ° C / sec to a coiler temperature of 300-550 ° C.
  • the hot strips produced and obtained in this way achieve a product Rm * A80 of elongation A80 and tensile strength Rm of up to 19550 MPa *%.
  • the object of the invention was to provide a hot rolled flat steel product which can be produced in a simple and reliable manner and has an optimized combination of particularly high strength and good deformability.
  • a method for producing such a flat steel 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 7 are run through to produce a hot-rolled flat steel product according to the invention.
  • the structure of the flat steel product consists not only optionally present proportions of up to 5 vol .-% of ferrite and up to 10 vol .-% martensite to at least 60 vol .-% of bainite and the balance of retained austenite, wherein at least a portion of the retained austenite in block Form and the blocks of austenite present in block form at least 98% have a mean diameter of less than 5 microns.
  • a flat steel product according to the invention has a structure dominated by two phases, of which one dominant component is bainite and its second dominant component is retained austenite.
  • one dominant component is bainite and its second dominant component is retained austenite.
  • small amounts of martensite and ferrite may be present, but their contents are too low to have an influence on the properties of the hot-rolled steel flat product.
  • the invention is based on the finding that it is favorable for the required properties of the hot-rolled steel flat product, if the retained austenite is in block form, as long as the diameter of the austenite blocks Restestenten not exceed 5 microns.
  • block-like retained austenite should be avoided in principle, since block-shaped retained austenite is the cause of instabilities in the microstructure and a associated with the tendency to form unwanted martensite. Accordingly, the highest possible proportions of film-like retained austenite in the structure of a steel of the type in question have always been sought in the prior art (see FIG.
  • blocky retained austenite is used when the ratio of length / width, that is to say, of the structural constituents of retained austenite present in the microstructure. H. longest extent / thickness, 1 to 5.
  • retained austenite is referred to as “film-like” if, in the case of retained austenite accumulations in the microstructure, the ratio of length / width is greater than 5 and the width of the respective structural constituents of retained austenite is less than 1 ⁇ m. Accordingly, film-like retained austenite is typically present as a finely distributed lamella.
  • the blocky retained austenite in the expansion measures at most 4 ⁇ m, in particular at most 3 ⁇ m.
  • the maximum extent of the retained austenite present in block form is regularly in the range of 1 to 3 ⁇ m, the maximum extent of the retained austenite blocks being typically limited to 2 ⁇ m on average.
  • a complex, multi-stage temperature control during the production of the flat steel product is not required to surprisingly.
  • Hot-rolled flat steel products produced according to the invention regularly reach tensile strengths Rm of more than 1000 MPa, in particular at least 1200 MPa, at elongations A80, which likewise regularly exceed 17%, in particular above 19%. Accordingly, the quality Rm * A80 of hot strips according to the invention is regularly in the range of 18000-30,000 MPa *%. In particular, it is regularly at least 20000 MPa *%. As such, a flat steel product according to the invention has an optimum combination of extreme strength and good formability.
  • the strength-increasing effect of copper can be used.
  • a minimum content of 0.15% by weight of Cu may be present in the hot-rolled flat steel product according to the invention.
  • the C content of the flat steel product according to the invention can be set to at least 0.3% by weight.
  • Mn in contents of up to 2.5% by weight, in particular up to 2.0% by weight promotes bainite formation in the steel processed according to the invention, with the optionally additionally present contents of Cu, Cr and Ni also leading to the formation of bainite contribute.
  • the optional addition of Cr can also lower the martensite start temperature and suppress the tendency of the bainite to convert to perlite or cementite.
  • Cr at contents up to the upper limit of not more than 2% by weight specified in the invention promotes the ferritic transformation, whereby optimum effects of the presence of Cr in a flat steel product according to the invention result if the Cr content is reduced to 1.5% by weight. % is limited.
  • Ti, V or Nb helps to promote the formation of fine-grained microstructures and promote ferritic transformation.
  • these micro-alloying elements contribute to increasing the hardness by forming precipitates.
  • the positive effects of Ti, V and Nb in the 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 not exceeding 0.14% by weight.
  • Si and Al Due to the presence of Si and Al, carbide formation in the bainite can be suppressed and consequently the residual austenite can be stabilized by dissolved carbon.
  • Si in particular contributes to solid solution hardening.
  • Al can replace the Si content to a part in the steel processed according to the invention. For this purpose, a minimum content of 0.4 wt .-% Al may be provided. This is especially true if the addition of Al should set the hardness or tensile strength of the steel to a lower value in favor of improved ductility.
  • the formation of the structure 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 kept at a temperature sufficient to produce the hot rolling carried out from this temperature
  • To end hot rolling temperature in which the hot strip obtained has a fully recrystallized, austenitic structure, which provides optimal conditions for bainite formation.
  • the inventive method can run particularly reliable when the hot rolling end temperature is set to at least 900 ° C and 1100 ° C, in particular 1050 ° C, does not exceed.
  • the precursor is heated to a temperature in the range of 1100 - 1300 ° C temperature before hot rolling.
  • the hot rolling end temperature is lower than 900 ° C, austenite softening can be achieved as much as possible by the main forming of the hot strip in the final passes of hot rolling.
  • the resulting hot strip also has a microstructure with Restaustenitan turnover that meet the requirements of the invention.
  • the hot strip is accelerated at a cooling rate of at least 5 ° C / sec to a coiler temperature which is in the range of 350-600 ° C. Cooling is optimally started when 50-60% of the austenite has softened.
  • a break of approximately up to 2 s is provided between the end of the hot rolling and the beginning of the cooling.
  • the formula indicates the minimum time after which 50-60% of debonded austenite is present.
  • the calculated break times are: T [° C] t [s] 850 1.21 900 0.59 950 0.30 1000 0.16
  • the cooling to the coiler temperature is carried out in such a way that there is no conversion of the austenite until reeling. As a result, bainite formation takes place exclusively in the coil for a sufficiently long time.
  • this coil is cooled in a temperature range whose upper limit is equal to the temperature at which bainite is formed from austenite and whose lower limit is above the temperature the martensite is created in the microstructure of the hot strip.
  • the duration over which the coil is held in this temperature range is chosen so that the bainite content sought according to the invention of at least 60% by volume is achieved. In practice, a duration of at least 0.5 h is regularly sufficient for this, with longer bainite contents being established over a longer period.
  • the desired course of bainite formation in practice can be ensured by setting the upper limit of the coiler temperature to 550 ° C.
  • the correspondingly assembled molten steel was cast into slabs in a conventional manner and then heated in a conventional manner to a reheating temperature TDC.
  • the heated slabs were hot rolled in a conventional hot rolling mill to hot strips W1 - W10 with a thickness of 2.0 mm.
  • the hot strips W1-W10 emerging from the hot rolling scale each had a hot rolling end temperature ET, from which they have been acceleratedly cooled at a cooling rate KR to a coiling temperature HT. At this coiler temperature HT, the hot strips W1 - W10 have been wound into coils.
  • the coils have then each been cooled in a temperature range whose upper limit was determined by the respective reel temperature HT and the lower limit thereof by the martensite starting temperature MS determined for the respective steel S1-S7.
  • the calculation of the martensite start temperature MS was carried out according to the article " Thermodynamic Exatrapolation and Martensite Start-Temperature of Substituted Alloyed Steels "by H. Bhadeshia, published in Metal Science 15 (1981), pages 178-180 explained procedure.
  • the duration over which the coil has been cooled in the temperature range defined in the manner described above was such that the hot strips thus obtained each had a structure consisting of bainite and retained austenite, in which the proportions of other structural components were at most ineffective against "0" outgoing quantities were present.
  • Table 3 also shows the mechanical properties determined for the individual hot strips: tensile strength Rm, yield strength Rp, elongation A80, quality Rm * A80 and the respective residual austenite content RA.
  • the hot strip W4 which was also produced from steel S4 but in compliance with the specifications according to the invention, had only up to 1% by volume of coarse blocky retained austenite with an average expansion of more than 5 ⁇ m. The remaining retained austenite was in filmy and fine blocky form, with the result that a high elongation A80 was achieved.
  • the hot-rolled strip W7 produced from the steel S5 and the hot-rolled strip W10 produced from the steel S7 also did not reach the minimum tensile strength of 1200 MPa which was aimed for here. The reason was in these cases in each case too high reel temperature HT.
  • the cross-section of a cold strip is shown as an example of the RA excretions discussed.
  • 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 Si al Mn Ni Cu Cr other S1 0.48 1.5 0.02 1.48 0.034 1.51 0, 9 S2 0.51 1.5 0.02 1.58 0,015 1.53 0, 9 Ti: 0,013 V: 0, 099 S3 0.52 0.4 1.40 1.48 0,030 1.51 0, 9 V: 0.09 S4 0.30 1.4 0.02 1.46 0,021 1.47 0.9 Ti: 0,014 V: 0.09 S5 0.51 1.5 0.01 0.40 0.63 0.60 1.3 Ti: 0.011 V: 0, 098 Not a word: 0.3 S6 0.49 1.5 0.01 0.41 0.60 0.61 1.5 Ti: 0,014 V: 0.1 S7 0.38 2.0 0.02 0.41 0.59 0.57 1.4 Not a word: 0.30 In% by weight, Remaining iron and unavoidable impurities hot strip stole OT [° C] ET [° C] KR [° C / s] HT [° C] MS [° C] According to the invention?

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EP12178330.2A 2012-07-27 2012-07-27 Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung Revoked EP2690183B1 (de)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP12178330.2A EP2690183B1 (de) 2012-07-27 2012-07-27 Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung
PCT/EP2013/065836 WO2014016420A1 (de) 2012-07-27 2013-07-26 Warmgewalztes stahlflachprodukt und verfahren zu seiner herstellung
BR112015001456A BR112015001456A2 (pt) 2012-07-27 2013-07-26 produto de aço plano laminado a quente e método para a produção do mesmo.
CN201380049258.4A CN104662179B (zh) 2012-07-27 2013-07-26 热轧扁钢产品及其生产方法
KR1020157005074A KR20150038426A (ko) 2012-07-27 2013-07-26 열간 압연된 평강 제품 및 이의 제조 방법
US14/417,685 US20150203946A1 (en) 2012-07-27 2013-07-26 Hot-Rolled Flat Steel Product and Method For the Production Thereof
JP2015523568A JP6154010B2 (ja) 2012-07-27 2013-07-26 熱間圧延平鋼製品およびその製造方法

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EP12178330.2A EP2690183B1 (de) 2012-07-27 2012-07-27 Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung

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EP2690183A1 EP2690183A1 (de) 2014-01-29
EP2690183B1 true EP2690183B1 (de) 2017-06-28

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EP12178330.2A Revoked EP2690183B1 (de) 2012-07-27 2012-07-27 Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung

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US (1) US20150203946A1 (pt)
EP (1) EP2690183B1 (pt)
JP (1) JP6154010B2 (pt)
KR (1) KR20150038426A (pt)
CN (1) CN104662179B (pt)
BR (1) BR112015001456A2 (pt)
WO (1) WO2014016420A1 (pt)

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WO2017109539A1 (en) * 2015-12-21 2017-06-29 Arcelormittal Method for producing a high strength steel sheet having improved strength and formability, and obtained high strength steel sheet
KR101751530B1 (ko) * 2015-12-28 2017-06-27 주식회사 포스코 공구용 강판 및 그 제조방법
KR102035525B1 (ko) * 2016-06-27 2019-10-24 한국기계연구원 필름형 잔류 오스테나이트를 포함하는 강재
KR101822292B1 (ko) 2016-08-17 2018-01-26 현대자동차주식회사 고강도 특수강
KR101822295B1 (ko) 2016-09-09 2018-01-26 현대자동차주식회사 고강도 특수강
MX2019008649A (es) * 2017-01-20 2019-12-16 Thyssenkrupp Steel Europe Ag Producto de acero plano laminado en caliente que consiste en un acero de fase compleja con una microestructura y un metodo predominantemente bainitico para la fabricacion de un producto de acero plano.
EP3658307B9 (de) * 2017-07-25 2022-01-12 ThyssenKrupp Steel Europe AG Blechbauteil, hergestellt durch warmumformen eines stahlflachprodukts und verfahren zu dessen herstellung
KR101989236B1 (ko) * 2017-09-26 2019-06-13 현대제철 주식회사 전단 특성이 우수한 열연강판 제조방법 및 이에 의해 제조된 열연강판
CN111542635B (zh) * 2017-12-28 2022-07-01 通用汽车环球科技运作有限责任公司 具有增强的抗氧化性的用于热冲压的钢
CN112513310A (zh) 2018-05-24 2021-03-16 通用汽车环球科技运作有限责任公司 改善压制硬化钢的强度和延性的方法
JP7492460B2 (ja) 2018-06-12 2024-05-29 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフト 平鋼製品およびその製造方法
CN112534078A (zh) 2018-06-19 2021-03-19 通用汽车环球科技运作有限责任公司 具有增强的机械性质的低密度压制硬化钢
US11530469B2 (en) 2019-07-02 2022-12-20 GM Global Technology Operations LLC Press hardened steel with surface layered homogenous oxide after hot forming
EP3872194A1 (de) 2020-02-26 2021-09-01 ThyssenKrupp Steel Europe AG Verfahren zur herstellung eines warmgewalzten stahlflachprodukts und stahlflachprodukt
EP3872193A1 (de) 2020-02-26 2021-09-01 ThyssenKrupp Steel Europe AG Verfahren zur herstellung eines warmgewalzten stahlflachprodukts und stahlflachprodukt
CN112795852A (zh) * 2020-11-23 2021-05-14 唐山钢铁集团有限责任公司 1200MPa级高扩孔性能冷轧镀锌带钢及其生产方法
CN114790530B (zh) * 2021-01-26 2024-03-08 宝山钢铁股份有限公司 一种高塑性超高强钢板及其制造方法

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JP6154010B2 (ja) 2017-06-28
CN104662179B (zh) 2018-01-12
BR112015001456A2 (pt) 2017-07-04
EP2690183A1 (de) 2014-01-29
CN104662179A (zh) 2015-05-27
KR20150038426A (ko) 2015-04-08
US20150203946A1 (en) 2015-07-23
JP2015528064A (ja) 2015-09-24
WO2014016420A1 (de) 2014-01-30

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