EP2924140B1 - Procédé de génération d'un produit plat en acier haute résistance - Google Patents

Procédé de génération d'un produit plat en acier haute résistance Download PDF

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Publication number
EP2924140B1
EP2924140B1 EP14161606.0A EP14161606A EP2924140B1 EP 2924140 B1 EP2924140 B1 EP 2924140B1 EP 14161606 A EP14161606 A EP 14161606A EP 2924140 B1 EP2924140 B1 EP 2924140B1
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EP
European Patent Office
Prior art keywords
hot
rolling
flat steel
content
coiling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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EP14161606.0A
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German (de)
English (en)
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EP2924140A1 (fr
Inventor
Dr. Alexander Gaganov
Wolfgang Gervers
Prof. Dr. Andreas Kern
Gabriel Kolek
Elena Schaffnit
Hans-Joachim Tschersich
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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Publication date
Priority to DK17191293.4T priority Critical patent/DK3305935T3/da
Application filed by ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Priority to DK14161606.0T priority patent/DK2924140T3/en
Priority to EP17191293.4A priority patent/EP3305935B9/fr
Priority to PL14161606T priority patent/PL2924140T3/pl
Priority to SI201430572T priority patent/SI2924140T1/en
Priority to EP14161606.0A priority patent/EP2924140B1/fr
Priority to ES17191293T priority patent/ES2745046T3/es
Priority to PL17191293T priority patent/PL3305935T3/pl
Priority to ES14161606.0T priority patent/ES2659544T3/es
Priority to SI201431325T priority patent/SI3305935T1/sl
Priority to UAA201610736A priority patent/UA117959C2/uk
Priority to RU2016141474A priority patent/RU2675183C2/ru
Priority to PCT/EP2015/055685 priority patent/WO2015144529A1/fr
Priority to KR1020167029332A priority patent/KR20160137588A/ko
Priority to CA2941202A priority patent/CA2941202C/fr
Priority to JP2016558769A priority patent/JP6603669B2/ja
Priority to CN201580016149.1A priority patent/CN106133154A/zh
Priority to US15/127,529 priority patent/US10280477B2/en
Priority to BR112016022053-6A priority patent/BR112016022053B1/pt
Priority to MX2016012491A priority patent/MX2016012491A/es
Publication of EP2924140A1 publication Critical patent/EP2924140A1/fr
Application granted granted Critical
Publication of EP2924140B1 publication Critical patent/EP2924140B1/fr
Priority to US16/294,468 priority patent/US10934602B2/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • 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
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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 process for producing a flat steel product with a yield strength of at least 700 MPa and with at least 70% by volume bainitic structure.
  • Flat steel products of the type in question are typically rolled products, such as steel strips or sheets, as well as blanks and blanks made therefrom.
  • the invention relates to a method for producing high-strength so-called "heavy plates” which have a thickness of at least 3 mm.
  • High-strength flat steel products in particular in the field of commercial vehicle construction an increasing importance, as they reduce the dead weight of the vehicle and a Increase the payload.
  • a low weight not only contributes to the optimal use of the technical performance of the respective drive unit, but also supports resource efficiency, cost optimization and climate protection.
  • a significant reduction in the dead weight of steel sheet constructions can be achieved by increasing the mechanical properties, in particular the strength of each processed flat steel product.
  • modern toughened steel products intended for commercial vehicle construction are also expected to have good toughness properties, good brittle fracture resistance behavior and optimum suitability for cold forming and welding.
  • the steel slab After pouring and solidification of the melt in the known method, the steel slab is reheated to a temperature range whose lower limit is determined depending on the C and Nb contents of each potted steel and whose upper limit is 1170 ° C. Subsequently, the reheated slab is pre-rolled at a final temperature which is 1080-1150 ° C. After a pause of 30-150 seconds, during which the pre-rolled slab is maintained at 1000-1080 ° C, the pre-rolled slab is then hot-rolled to a hot-rolled strip. The degree of deformation of the last pass of the hot rolling should be 3 - 15%.
  • the hot rolling is completed at a hot rolling end temperature which is at least the Ar3 temperature of the processed steel and is at most 950 ° C.
  • the hot strip obtained is cooled at a cooling rate of more than 15 ° C / s to a coiling temperature of 450 - 550 ° C, where it is coiled into a coil.
  • the grain boundary density of the carbon present in solid solution should be 1 - 4.5 atoms / nm 2 and the size of the grains of cement precipitated at the grain boundaries should not be more than 1 ⁇ m.
  • the flat steel products produced in this way and produced by the known method should have tensile strengths of more than 780 MPa and have yield strengths of up to 726 MPa at sufficiently high-dose alloy contents.
  • the hot strip produced in the known manner should have a combination of properties which is particularly suitable for use in automobile construction. Optimum surface finish is achieved by limiting the reheat temperature to which the slab is heated prior to hot rolling to the above-mentioned temperature range and thus avoiding excessive scale formation which would be incorporated into the hot strip surface during hot rolling.
  • a high strength steel sheet comprising (in mass%) 0.03 to 0.10% C, 0.01 to 1.5% Si, 1.0 to 2.5% Mn, 0.1% or less P, 0.02% or less S, 0.01-1.2% Al, 0.06-0.15% Ti, 0.01% or less N and the balance iron and unavoidable impurities, its tensile strength being 590 MPa or is more and the ratio of tensile strength and yield strength is 0.80 or more.
  • the steel sheet should have a microstructure with at least 40 area% bainite, the remainder ferrite and martensite.
  • a precursor cast from an appropriately alloyed steel is heated to 1150 - 1280 ° C, at a Hot rolling end temperature, which is between the Ar3 temperature and 1050 ° C, hot rolled and cooled at a high cooling rate, for example, 45 ° C / s to a coiler temperature of less than 600 ° C, with a reel temperature of 300 - 500 ° C is set, if a purely bainitic structure is desired.
  • a method of producing a steel sheet comprising 0.05-0.15% C, 0.2-1.2% Si, 1.0-2.0% Mn, not more than 0.04% P, not more than 0.0030% S, 0.005 - 0.10% Al, not more than 0.005% N and 0.03 - 0.13% Ti, and the remainder being Fe and unavoidable impurities. It should consist of less than 80 area% of the structure of bainite and the rest of ferrite.
  • a correspondingly composed melt is cast into a precursor, which is hot rolled at a hot rolling end temperature of 800 - 1000 ° C and then cooled first at least 55 ° C / s and then at least 120 ° C / s to at most 500 ° C.
  • the tensile strength of the steel sheet thus obtained should be 780 MPa.
  • the object of the invention was to provide a method with which high-strength steel sheets can be produced in a practical manner with mechanical properties optimized with regard to use in automobile construction and with an equally optimized surface finish.
  • the method according to the invention is based on a steel alloy whose alloying constituents and alloy contents are matched to one another within narrow limits in such a way that maximized mechanical properties and optimized surface textures are achieved in a procedure which must be carried out safely.
  • Cu, Ni, V, Mo and Sb occur as accompanying elements, which enter the steel processed according to the invention as a technically unavoidable impurity in the steelmaking process. Their contents are limited to amounts which are ineffective in relation to the properties of the steel processed according to the invention.
  • the Cu content is limited to max. 0.12 wt .-%, the Ni content to less than 0.1 wt%, the V content to at most 0.01 wt .-%, the Mo content to less than 0.004 wt .-%, and the Sb content is also limited to less than 0.004 wt%.
  • the slab After the slab has been cast, it is reheated to an austenitizing temperature which is 1200-1300 ° C.
  • the upper limit of the temperature range to which the slab is heated to austenitise should not be exceeded in order to avoid coarsening of the austenite grain and increased scale formation.
  • the rewarming temperature range of 1200 - 1300 ° C does not yet result in the increased formation of Rotzunder that would reduce the surface quality of the steel flat product produced according to the invention.
  • Rotzunder forms in the processing according to the invention composite slabs exclusively during the hot rolling process (steps d), e) of the method according to the invention), if after Reheating too much primary scale is present on the slab surface.
  • the lower limit of the reheating temperature is set so that the desired homogenization of the structure is ensured with a uniform temperature distribution. From this temperature, a largely complete dissolution of the coarse Ti and Nb carbonitride precipitates present in the respective slab begins in the austenite.
  • fine Ti or Nb carbonitride precipitations can then be newly formed, which, as explained, make a significant contribution to increasing the strength properties. In this way, it is ensured that the flat steel products produced and assembled according to the invention regularly have a minimum yield strength of 700 MPa.
  • the reheating temperature during austenitisation of the respective slab is at least 1200 ° C., in order to achieve the desired effect of the most complete possible dissolution of the TiC and NbC precipitates.
  • the austenitizing temperature is below 1200 ° C.
  • the amount of carbide precipitates of Ti and Nb dissolved in austenite is so small that the effects used according to the invention do not occur.
  • a rewarming temperature below 1200 ° C. would therefore have in the processing of flat steel products, which corresponds to the optimized alloy selection according to the invention are composed, with the result that the required strength properties are not achieved.
  • the most complete possible dissolution of the TiC and NbC precipitates can be ensured with particular certainty if the reheating temperature is at least 1250 ° C.
  • a flat steel product meeting the highest quality requirements for its surface finish can be produced by completely removing the scale present on the slab before rough rolling. This can be done by completely descaling the slab surface after the furnace discharge and, if possible, immediately before the rough rolling. For this purpose, the slab can go through a conventional scale scrubber.
  • the time t_1 In order to produce a flat steel product with optimized surface finish, the time t_1, the transfer of the slab from the workstation ("reheating (step c)") or the optional "post-reheating” removal of the primary scale (step c ') "to start of finish hot rolling (step e)) is required, limited to a maximum of 300 s. This optimally includes pre-rolling. In such a short transfer time, only such a small amount of primary scale is newly formed that the red scale forming therefrom during hot rolling is harmless to the quality of the surface of the flat steel product obtained after hot rolling. In the case that descaling is carried out before roughing, the transport time between the descaling unit and the roughing stand should not exceed 30 s. With a so short transport time can thus form no or at most a harmless thin oxide layer on the previously descaled slab.
  • step d the respectively processed slab is pre-rolled at a rough rolling temperature of 950-1250 ° C.
  • the total reduction in pre-rolling amounts to at least 50%.
  • the lower limit of the predetermined for the rough rolling temperature range and the minimum value of the total stitch decrease ⁇ hv are set so that the recrystallization processes in the respective pre-rolled slab can run completely. In this way, the formation of a fine-grained austenitic structure is ensured before the finish rolling, whereby optimized toughness and elongation at break properties of the steel flat product produced according to the invention are achieved.
  • the dwell and pause time t_2 between rough rolling and finish rolling is limited to 50 seconds to avoid undesirable austenite grain growth.
  • Pre-rolling is followed, in step e), by hot rolling of the pre-rolled slab into a hot-rolled flat steel product having a hot strip thickness of typically 3-15 mm.
  • Flat steel products with such thicknesses are referred to in the jargon as "heavy plate”.
  • the final temperature of hot rolling is 800 - 880 ° C.
  • the comparatively low hot rolling end temperature enhances the effect of hot rolling.
  • the upper limit of the range of the hot rolling finish temperature is set so that no recrystallization of the austenite takes place during rolling in the hot rolling finishing line. This also contributes to the expression of a fine-grained structure.
  • the lower limit temperature is at least 800 ° C, so that no ferrite forms during rolling.
  • the cooling break after hot rolling is at most 10 seconds to prevent undesirable microstructural changes between hot rolling and controlled accelerated cooling.
  • the choice of reel temperature has a decisive influence on precipitation hardening.
  • the reel temperature range according to the invention is chosen so that it is on the one hand below the Bainitstarttemperatur, on the other hand in the excretion maximum for the formation of Karbonitridausscheidept.
  • a reel temperature which is too low would mean that the precipitation potential would no longer be usable and thus the required minimum yield strength would no longer be reached.
  • the cooling conditions are inventively chosen so that the hot rolled flat steel product immediately before reeling a bainitic structure having a phase content of at least 70 vol .-%. A further bainite formation then takes place in the reel.
  • the microstructure of the hot-rolled flat steel product produced according to the invention after coiling, consists entirely of bainite in the technical sense. This is achieved by observing the inventively predetermined range of reel temperature.
  • the high cooling rate avoids the formation of unwanted phase components.
  • the cooling rate of the cooling after hot rolling can be limited to 150 K / s.
  • the yield strength of the hot-rolled flat steel products produced according to the invention in the manner explained above is reliably 700-850 MPa. Their elongation at break is in each case at least 12%. Equally regularly, steel flat products according to the invention achieve tensile strengths of 750-950 MPa.
  • the notched impact work determined for products according to the invention is in the range from 50 to 110 J at -20 ° C. and in the range from 30 to 110 J at -40 ° C.
  • Steel flat products produced according to the invention have a fine-grained structure with a mean grain size of at most 20 ⁇ m, in order to achieve good elongation at break and toughness.
  • the abovementioned properties lie with a hot-rolled flat steel product in the rolling state after Reel in front.
  • a further heat treatment for the adjustment or expression of certain important properties for the intended use as a high-strength sheet in commercial vehicle construction is not necessary.
  • the reheated slabs have been transported in less than 30 s to a scale washer in which the primary scale adhering to them has been removed from the slabs.
  • the slabs emerging from the scale scrubber have then been transported to a roughing stand, where they have been pre-rolled with a rough-rolling temperature TVW and a total reduction in stitches ⁇ hv over the rough-rolling.
  • the pre-rolled slabs were finished hot rolled in a finished hot rolling mill to hot strip with a thickness of BD and a width BB.
  • the hot rolling has been completed with a total decrease in the finished heat transfer scale ⁇ hf at a hot rolling end temperature TEW.
  • the finished hot-rolled flat steel product exiting from the last stand has been cooled to a coiling temperature HT by intensive cooling with water at a cooling rate dT of 50-120 K / s after a pause t_p of 1-7 seconds in which it has cooled slowly in air , After cooling, the flat steel products already had at least 70% by volume bainitic structure.
  • the tensile tests for determining the yield strength ReH, the tensile strength Rm and the elongation at break A were carried out according to DIN EN ISO 6892-1 on longitudinal samples of the hot strips.
  • the notched bar impact tests to determine the impact energy Av at -20 ° C and -40 ° C and -60 ° C were carried out on longitudinal samples according to DIN EN ISO 148-1.
  • the structural investigations were carried out by light microscope and scanning electron microscope. For this purpose, the samples were taken from a quarter of the bandwidth, prepared as a longitudinal section and etched with Nital (ie alcoholic nitric acid containing a proportion of 3% by volume of nitric acid) or sodium disulfite.
  • Nital ie alcoholic nitric acid containing a proportion of 3% by volume of nitric acid
  • the determination of the structural components was carried out by means of area analysis in sample position 1/3 sheet thickness, as in H. Schumann and H. Oettel "Metallography” 14th edition, 2005 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim described.
  • the mechanical properties and the structural constituents of the hot strips produced according to the invention are given in Table 3.
  • the band sheets produced according to the method of the present invention have high strength properties with good toughness properties and good elongation at break.
  • the yield strengths of the hot strips produced in the above manner are between 700 MPa and 790 MPa.
  • the elongation at break is at least 12% and the Tensile strength 750 - 880 MPa.
  • the notch impact work at -20 ° C is in the range 60 to 100 J.
  • the notch impact work is 40 to 75 J and at -60 ° C, the impact energy is at 30 - 70 J.
  • Table 1 stolen C Si Mn P S al N Cr Nb B Ti Cu Ni V Not a word sb A 0,060 0.42 1.77 0,012 0.0010 0.034 0.0046 0.04 0.062 0.0020 0,110 0.02 0.03 0,010 0,004 0,004 B 0.053 0.49 1.75 0,015 0.0014 0.034 0.0049 0.06 0.066 0.0020 0.091 0.02 0.03 0.005 0,004 0,004 C 0,061 0.22 1.79 0,014 0.0021 0,050 0.0047 0.04 0.063 0.0019 0.097 0.02 0.02 0,003 0,004 0,004 D 0,065 0.20 1.8 0,014 0.0021 0,040 0.0047 0.04 0,065 0.0005 0,110 0.02 0.02 0,003 0,004 0,004 e 0,070 0.03 1.89 0.011 0.0014 0,042 0.0051 0.04 0,060 0.0005 0.130 0.02 0.03 0,008 0,004 0,004 Data in wt .-%,

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Claims (13)

  1. Procédé de génération d'un produit plat en acier présentant une limite d'élasticité d'au moins 700 MPa et une microstructure bainitique d'au moins 70 % en volume, ledit procédé comportant les étapes de travail suivantes consistant à :
    a) faire fondre une masse d'acier contenant (% en poids) du
    C : 0,05 - 0,08 %,
    Si : 0,015 - 0,500 %,
    Mn : 1,60 - 2,00 %,
    P : jusqu'à 0,025 %,
    S : jusqu'à 0,010 %,
    Al : 0,020 - 0,050 %,
    N : jusqu'à 0,006 %,
    Cr : jusqu'à 0,40 %,
    Nb : 0,060 - 0,070 %,
    B : 0,0005 - 0,0025 %,
    Ti : 0,090 - 0,130 %,
    ainsi que des impuretés techniquement inévitables parmi lesquelles l'on compte jusqu'à 0,12 % Cu, jusqu'à 0,100 % Ni, jusqu'à 0,010 % V, jusqu'à 0,004 % Mo et jusqu'à 0,004 % Sb,
    et
    le reste étant du Fe ;
    b) couler la masse en fusion pour former une brame ;
    c) chauffer à nouveau la brame à une température de réchauffement de 1200 -1300 °C ;
    d) pré-laminer la brame à une température de pré-laminage de 950 -1250 °C et à obtenir une réduction d'épaisseur totale d'au moins 50 % lors du pré-laminage ;
    e) soumettre la brame pré-laminée à un laminage de finition à chaud, où le laminage de finition à chaud est terminé lors d'une température finale de laminage à chaud de 800 -880 °C ;
    f) refroidir intensément le produit plat en acier, qui a été soumis à un laminage de finition à chaud, dans un laps de temps tout au plus de 10s après avoir terminé le laminage de finition à chaud, à une température d'enroulement de 550 - 620 °C avec une vitesse de refroidissement d'au moins 40 K/s ;
    g) enrouler le produit plat en acier qui a été soumis à un laminage de finition à chaud,
    où l'allongement à la rupture du produit plat en acier laminé à chaud, obtenu après l'enroulement, est au moins de 12 %.
  2. Procédé selon la revendication 1, caractérisé en ce que selon la formule CE = % C + % Mn / 6 + % Cr + % Mo + % V / 5 + % Cu + % Ni / 15
    Figure imgb0008
    avec % C = teneur respective en C % en poids
    % Mn = teneur respective en Mn % en poids
    % Cr = teneur respective en Cr % en poids
    % Mo = teneur respective en Mo % en poids
    % V = teneur respective en V % en poids
    % Cu = teneur respective en Cu % en poids
    % Ni = teneur respective en Ni % en poids
    pour l'équivalent en carbone calculé CE de la masse d'acier en fusion dans l'étape de travail a) la formule suivante s'applique : CE ≤ 0 , 5 % en poids
    Figure imgb0009
  3. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la température de réchauffement est de 1250 - 1300 °C.
  4. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que dans une étape de travail c') traversée entre le réchauffement (étape de travail c)) et le pré-laminage (étape de travail d)), l'étape primaire adhérente sur la brame respectivement transformée est retirée.
  5. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le temps de transport requis pour le transport de la brame depuis le poste de travail traversé précédemment (étape de travail c) ou étape de travail optionnelle c')) jusqu'au laminage de finition à chaud (étape de travail e)) est limité tout au plus à 300 s.
  6. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le temps de séjour s'écoulant entre le pré laminage (étape de travail d)) et le laminage de finition à chaud (étape de travail e)) est tout au plus de 50 s.
  7. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la vitesse de refroidissement lors du refroidissement dans l'étape de travail f) est tout au plus de 150 K/s.
  8. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'épaisseur du produit plat en acier laminé à chaud obtenu après le laminage à chaud est de 3 - 15 mm.
  9. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la limite d'élasticité des produits plats en acier laminés à chaud obtenus après l'enroulement est de 700 - 850 MPa.
  10. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la résistance à la traction des produits plats en acier laminés à chaud obtenus après l'enroulement est de 750 - 950 MPa.
  11. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'indice de résilience des produits plats en acier laminés à chaud obtenus après l'enroulement se situe dans une plage de 50 - 110 J par -20 °C.
  12. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que les produits plats en acier laminés à chaud obtenus après l'enroulement possèdent exclusivement une microstructure bainitique outre d'autres constituants structurels techniquement inévitables.
  13. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le diamètre de grain moyen de la microstructure des produits plats en acier obtenus après l'enroulement est tout au plus de 20 µm.
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SI201430572T SI2924140T1 (en) 2014-03-25 2014-03-25 A process for the manufacture of a high-strength steel flat product
EP14161606.0A EP2924140B1 (fr) 2014-03-25 2014-03-25 Procédé de génération d'un produit plat en acier haute résistance
ES17191293T ES2745046T3 (es) 2014-03-25 2014-03-25 Producto plano de acero altamente resistente y uso de un producto plano de acero altamente resistente
PL17191293T PL3305935T3 (pl) 2014-03-25 2014-03-25 Płaski produkt stalowy o wysokiej wytrzymałości i zastosowanie płaskiego produktu stalowego o wysokiej wytrzymałości
ES14161606.0T ES2659544T3 (es) 2014-03-25 2014-03-25 Procedimiento para la fabricación de un producto plano de acero altamente resistente
SI201431325T SI3305935T1 (sl) 2014-03-25 2014-03-25 Ploščat jekleni proizvod visoke trdnosti in uporaba takega ploščatega jeklenega proizvoda visoke trdnosti
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PCT/EP2015/055685 WO2015144529A1 (fr) 2014-03-25 2015-03-18 Procédé pour fabriquer un produit plat en acier très résistant
KR1020167029332A KR20160137588A (ko) 2014-03-25 2015-03-18 고강도 평강 제품을 제조하기 위한 방법
CA2941202A CA2941202C (fr) 2014-03-25 2015-03-18 Procede pour fabriquer un produit plat en acier tres resistant
JP2016558769A JP6603669B2 (ja) 2014-03-25 2015-03-18 高強度の平鋼製品を製造するための方法
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RU2016141474A RU2675183C2 (ru) 2014-03-25 2015-03-18 Способ получения высокопрочного стального прокатного плоского изделия
BR112016022053-6A BR112016022053B1 (pt) 2014-03-25 2015-03-18 Método para a produção de um produto plano de aço
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