EP2855718B1 - Produit en acier plat et procédé de fabrication d'un produit en acier plat - Google Patents

Produit en acier plat et procédé de fabrication d'un produit en acier plat Download PDF

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Publication number
EP2855718B1
EP2855718B1 EP13726805.8A EP13726805A EP2855718B1 EP 2855718 B1 EP2855718 B1 EP 2855718B1 EP 13726805 A EP13726805 A EP 13726805A EP 2855718 B1 EP2855718 B1 EP 2855718B1
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Prior art keywords
cold
temperature
flat steel
steel product
rolled flat
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EP13726805.8A
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German (de)
English (en)
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EP2855718A1 (fr
Inventor
Ekatherina BOCHAROVA
Sigrun Voss
Dorothea MATTISSEN
Roland Sebald
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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    • 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
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    • 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
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    • 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
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21D8/0236—Cold rolling
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    • 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
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    • 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
    • C21D8/0405—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 of ferrous alloys
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    • 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
    • C21D8/0421—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 working steps
    • C21D8/0426—Hot rolling
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    • C21—METALLURGY OF IRON
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    • 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
    • C21D8/0421—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 working steps
    • C21D8/0436—Cold rolling
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    • 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
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    • 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
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    • 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
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D7/00—Electroplating characterised by the article coated
    • C25D7/06—Wires; Strips; Foils
    • C25D7/0614—Strips or foils
    • 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
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a flat steel product produced from a cost-producible, high-strength steel and a method for producing such a flat steel product.
  • Dual-phase steels have been used in automotive engineering for some time.
  • alloying concepts for such steels known, each of which is composed so that they meet a wide variety of requirements.
  • Many of the known concepts are based on an alloy with molybdenum or require complex manufacturing processes, in particular a very rapid cooling in the cold strip annealing in order to produce the respectively desired structure of the steel.
  • the price of molybdenum in the market is subject to strong fluctuations, the production of steels containing high levels of Mo is associated with a high cost risk.
  • sufficiently high Mo contents retard the formation of perlite during cooling and thus ensure the formation of a favorable structure for the requirements imposed on the respective steel.
  • WO 03/018858 A1 discloses an ultra high strength steel composition, a process for producing an ultra-high strength steel product, and the resulting product, wherein the steel composition disclosed in this document does not contain niobium and molybdenum.
  • the object of the invention was to specify a flat steel product which has optimized mechanical properties and can be produced inexpensively without having to resort to expensive alloying elements that are subject to great variations in their procurement costs.
  • this object has been achieved with respect to the flat steel product in that such a flat steel product has the composition and properties specified in claim 1.
  • the flat steel product according to the invention contains at least 0.11% by weight C.
  • an excessively high C content has a negative effect on the welding behavior.
  • the weldability of a steel decreases with the level of its carbon content.
  • the maximum carbon content is limited to 0.16 wt .-% in the flat steel product according to the invention.
  • Silicon is also used to increase strength by increasing the hardness of the ferrite.
  • the minimum content of silicon of a flat steel product according to the invention is 0.1% by weight.
  • too high a content of silicon leads both to undesired grain boundary oxidation, which adversely affects the surface of a flat steel product according to the invention, and to difficulties when a flat steel product according to the invention is to be hot-dip coated with a metallic coating to improve its corrosion resistance.
  • the upper limit of the Si content of a flat steel product according to the invention is 0.3% by weight.
  • Manganese prevents the formation of perlite during cooling. As a result, the desired martensite formation is promoted in the flat steel product according to the invention and the strength of the flat steel product is increased. A sufficiently high manganese content to suppress perlite formation is 1.4% by weight here. Manganese, however, also has the negative property of forming segregations or reducing its suitability for welding. To avoid these effects, the upper limit of Mn intended content range of a flat steel product according to the invention at 1.9 wt .-%.
  • Aluminum is added to a flat steel product according to the invention for deoxidizing.
  • a content of at most 0.1 wt .-% is required.
  • an Al content of at most 0.05 wt .-% has proven to be particularly favorable. From a content of 0.02 wt .-%, the desired effect of Al safely occurs, so that the Al content of a flat steel product according to the invention 0.02 to 0.1 wt .-%, in particular 0.02 to 0.05 wt .-%, is.
  • Chromium is present in the flat steel product according to the invention such as manganese for increasing the strength.
  • the presence of Cr increases the hardenability and thus the proportion of martensite in the flat steel product.
  • the required Cr content is at least 0.45 wt .-%.
  • too high a content of chromium may promote grain boundary oxidation.
  • the Cr content of a flat steel product according to the invention is limited to a maximum of 0.85% by weight.
  • Titanium is added to a flat steel product according to the invention for increasing the strength through the formation of ultrafine precipitates.
  • Ti binds nitrogen in the steel flat product and thus prevents the undesired formation of boron nitrides.
  • the B provided in the flat steel product according to the invention can thus fully develop its strength-increasing effect.
  • a minimum content of 0.025 wt .-% Ti is essential for this. At higher titanium contents, the recrystallization is greatly delayed in the annealing. In extreme cases, this can be accompanied by a decrease in stretch.
  • the upper limit of the titanium content is limited to 0.06% by weight, in particular 0.055% by weight, with contents of up to 0.045% by weight having proven to be particularly practical.
  • Boron is also used to increase the strength in the flat steel product according to the invention.
  • a content of at least 0.0008 wt .-% B is necessary.
  • a B-content of more than 0.002 wt .-% leads to an undesirable embrittlement.
  • Phosphorus, sulfur, nitrogen and molybdenum are present in the flat steel product of the invention at most as impurities in such low levels that they have no influence on the properties of the flat steel product. Accordingly, in a flat steel product according to the invention in each case at most 0.02 wt .-% P, at most 0.003 wt .-% S, at most 0.008 wt .-% N and at most 0.1 wt .-% Mo, with the content of molybdenum preferred is below 0.05% by weight.
  • further impurities may be present which, for production-related reasons, enter the flat steel product, for example by scrap insertion. However, these impurities are also present in such small amounts that they do not affect the properties of the flat steel product.
  • the precursor should be further processed either while still hot, so kept at a temperature after casting be at least 300 ° C, or at a cooling rate of at most 60 ° C / h, in particular 50 ° C / h, slowly cooled.
  • the respective precursor may, if necessary, dwell in an oven for a period of up to 500 minutes at a sufficient oven temperature.
  • the reel temperature is set according to the invention to 480-650 ° C, because a lower coiler temperature would lead to a much firmer hot rolled steel flat product ("hot strip"), which could be further processed only under difficult conditions.
  • a coiler temperature above 650 ° C. in combination with the chromium content provided according to the invention would increase the risk of grain boundary oxidation.
  • the coiled hot-rolled coil cools to room temperature in the coil.
  • it can be pickled after cooling to remove scale and debris adhering to it.
  • cold rolling is carried out with a total cold rolling degree of 35-80% in order to achieve the desired cold strip thickness of 0.6-2.4 mm.
  • the cold strip is subjected to a continuous annealing. This is used first to set the desired mechanical properties.
  • the cold-rolled steel flat product can be used to prepare the cold-rolled steel flat product for subsequent coating with a metallic coating that protects the cold-rolled steel flat product from corrosive attack in later use.
  • a metallic coating that protects the cold-rolled steel flat product from corrosive attack in later use.
  • a coating can be applied by hot-dip coating.
  • the annealing provided according to the invention can be carried out in a pass-through, conventionally formed hot-dip coating installation. Alternatively, electrolytic galvanizing may also follow the annealing.
  • both the heating to the respective maximum annealing temperature, as well as the subsequent cooling in one or more steps can take place.
  • the heating takes place first in a preheating stage at a rate of 0.2 K / s to 45 K / s to a preheating temperature which is at most equal to the maximum annealing temperature, in particular in the range of 690-860 ° C or 690-840 ° C. , lies.
  • the flat steel product enters a holding stage in which, if its preheating temperature is less than the respectively targeted maximum annealing temperature, the respective maximum annealing temperature of 750-870 ° C. is reached with further heating.
  • the respective maximum annealing temperature the flat steel product is held until the end of the holding stage is reached.
  • the annealing time within which the flat steel product in the holding stage is kept at the maximum annealing temperature, is 8 - 260 s.
  • the material would not recrystallize.
  • unrecrystallized steel would result in a pronounced anisotropy.
  • a too long annealing time or an excessively high temperature lead to a very coarse microstructure and thus to poorer mechanical properties.
  • the cooling of the cold-rolled steel flat product takes place at a cooling rate of 0.5-110 K / s.
  • the cooling rate is set within this window so that a Perlit Struktur is largely avoided.
  • the cold-rolled steel flat product is to be dip-coated after heat treatment, it is cooled to a temperature of 455-550 ° C. in the course of cooling.
  • the thus tempered cold-rolled steel flat product then passes through a Zn-melt bath, which has a temperature of 450-480 ° C.
  • the steel strip can be held for up to 100 seconds before entering the zinc bath.
  • the temperature of the steel strip is greater than 480 ° C, the steel flat product is cooled until it enters the zinc bath at a cooling rate of up to 10 K / s until its temperature falls within the temperature range envisaged for the zinc bath, in particular equal to the zinc bath temperature is.
  • the thickness of the Zn-based protective layer present on the flat steel product is adjusted in a known manner by a stripping device.
  • the hot dip coating may be followed by another galvannealing, in which the hot dip coated steel flat product is heated up to 550 ° C to burn in the zinc layer.
  • the resulting cold rolled steel flat product is cooled to room temperature.
  • the process according to the invention for producing flat steel products according to the invention consequently comprises the following variants:
  • the cold-rolled steel flat product (“cold strip”) is heated in a preheating oven at a heating rate of 10 - 45 K / s to a preheating temperature of 660 - 840 ° C.
  • the preheated cold strip is passed through a furnace zone, in which the cold strip is maintained at a temperature of 760-860 ° C over a holding time of 8 - 24 s.
  • further heating occurs at a heating rate of 0.2 - 15 K / s.
  • the annealed cold strip is then cooled at a cooling rate of 2.0 - 30 K / s to an inlet temperature of 455 - 550 ° C, with which it then passes through a molten zinc bath and is held for a holding time of more than 45 s.
  • the zinc melt bath has a temperature of 455-465 ° C.
  • the cold strip in the molten zinc bath cools at a cooling rate of up to 10 K / s to the respective temperature of the molten zinc bath or is kept at a constant temperature.
  • the coating thickness is set in a conventional manner. Finally, the coated cold-rolled strip is cooled to room temperature.
  • the cold-rolled flat steel product is brought to a target temperature in an input heating zone of a continuous furnace at a heating rate of up to 25 K / s, which is 760-860 ° C.
  • a holding of the thus-heated cold-rolled steel flat product takes place at a 750-870 ° C., in particular 780-870 ° C., amounting annealing temperature.
  • a heating rate of up to 3 K / s to the respective annealing temperature is thereby during the holding time, i. heated within this holding zone, with a heating rate of up to 3 K / s to the respective annealing temperature.
  • a two-stage cooling is performed, in which the cold rolled steel flat product is first cooled slowly at a cooling rate of 0.5 - 10 K / s to an intermediate temperature of 640 - 730 ° C and a cooling rate of 5 - 110 K / s accelerated to a temperature of 455 - 550 ° C is cooled.
  • the cooled to the temperature in question cold-rolled steel flat product then passes through a molten zinc bath.
  • the zinc melt bath has a temperature of 450-480 ° C.
  • the coating thickness is set in a conventional manner.
  • a galvannealing may be performed to alloy in the zinc coating.
  • the cold strip provided with the zinc coating can be heated to 470-550 ° C. and kept at this temperature for a sufficient time.
  • the zinc coated cold strip may be subjected to temper rolling to improve its mechanical properties and surface finish of the coating.
  • the case-setting degrees are typically in the range of 0.1-2.0%, in particular 0.1-1.0%.
  • the cold rolled flat steel product assembled and produced according to the invention may alternatively undergo a heat treatment in a conventional annealing furnace in which the heating (step e.1)) and the annealing at the respective annealing temperature (step e.2) be completed in the manner described above, but in which the step e.3) is at least carried out in two stages by the cold-rolled steel flat product First cooled to a temperature range of 250 - 500 ° C, then dwells in this temperature range up to 760 s to perform an overaging treatment, and then cooled to room temperature. In this way, the retained austenite is stabilized in the microstructure of the flat steel product according to the invention.
  • the following heat treatment steps are then carried out in a continuous furnace:
  • the cold-rolled steel flat product is first heated in a heating zone at a heating rate of 1-8 K / s to 750-870, in particular 750-850 ° C.
  • the so-warmed cold-rolled steel flat product is passed through a furnace zone, in which the cold-rolled steel flat product over a holding time of 70 - 260 s at an annealing temperature of 750 - 870 ° C, in particular 750 - 850 ° C, is maintained.
  • a heating rate of up to 5 K / s.
  • the thus annealed cold-rolled steel flat product is then subjected to a two-stage cooling, in which it is first accelerated at a cooling rate of 3 - 30 K / s cooled to an intermediate temperature of 450 - 570 ° C.
  • This cooling can be carried out as air and / or gas cooling.
  • This is followed by a slower cooling, in which the cold-rolled steel flat product is cooled to 400-500 ° C at a cooling rate of 1-15 K / s.
  • the respective cooling can be followed by an over-aging treatment in which the cold-rolled steel flat product is maintained at a temperature of 250-500 ° C., in particular 250-330 ° C., over a holding time of 150-760 s.
  • cooling of the cold-rolled steel flat product occurs at a cooling rate of up to 1.5 K / s.
  • the cold-rolled flat steel product heat-treated in the above-described manner may be finally subjected to temper rolling to further improve its mechanical properties.
  • the applied skin passages are typically in the range of 0.1-2.0%, in particular 0.1-1%.
  • the thus heat-treated and optionally temper rolled cold-rolled steel flat product can then pass through a coating system for electrolytic coating, in which the respective metallic protective layer, for.
  • a coating system for electrolytic coating in which the respective metallic protective layer, for.
  • electrochemical electrochemical
  • a flat steel product according to the invention has an alloy according to the invention assembled in the manner described above and is additionally characterized by a structure comprising 60-90% by volume of ferrite including bainitic ferrite, 10% -40% by volume of martensite, up to 5% Vol% of retained austenite and up to 5% by volume due to production-related unavoidable other microstructural constituents.
  • the characteristic values determined in the tensile test according to DIN EN ISO 6892 lie in the following ranges: R p0,2 at least 440 MPa, in particular up to 550 MPa, R m at least 780 MPa, in particular up to 900 MPa, A 80 at least 14%, n 10-20 / Ag at least 0.10, Bra 2 at least 25 MPa, in particular at least 30 MPa.
  • flat steel products according to the invention can be reliably produced by using the method according to the invention.
  • the steel melts A - I, X, Y have been cast into slabs.
  • the cooling of the slabs was carried out so that a maximum cooling rate of 60 K / h was not exceeded.
  • the slabs were then heated in an oven to the respective hot rolling start temperature WAT.
  • the slabs entering the hot rolling scale at the hot rolling start temperature WAT were hot rolled at a final temperature WET into hot rolled steel strips having a thickness WBD.
  • the hot rolled steel strips cooled to a reeling temperature HT at which they have subsequently been wound into a coil.
  • the resulting hot-rolled steel strips were cold-rolled to a cold-rolled steel strip having a thickness KBD with a respective total deformation degree KWG.
  • hot rolling start temperature WAT hot rolling end temperature WET
  • hot rolled steel strip WBD hot rolled steel strip WBD
  • coiler temperature HT total deformation degree KWG
  • total deformation degree KWG total deformation degree KWG
  • the cold-rolled steel strips thus obtained have been subjected to different annealing tests.
  • the steel strips in a holding zone were first finished with a heating rate RF to a maximum annealing temperature TG, on which they were subsequently held.
  • a heating rate RF to a maximum annealing temperature TG, on which they were subsequently held.
  • a annealing time tG was required for the passage of the entire holding zone, d. H. including the finished heating and holding.
  • the cold-rolled steel strips were then cooled in one stage at a cooling rate RE to a temperature TE.
  • the from the melt bath Exiting steel strips had a Zn alloy coating which protects them against corrosion.
  • the operating parameters considered in the production of hot and cold rolled steel strip are "heating rate RV”, "preheating temperature TV”, “heating rate RF”, “annealing temperature TG”, “annealing time tG”, “cooling rate rE”, “temperature TE”, holding time tE “,” RB cooling rate “and” bath temperature TB “are given in Table 4.
  • heating rate RV heating temperature TV
  • heating rate RF heating temperature TG
  • annealing time tG annealing time tG
  • cooling rate rE cooling rate rE
  • heating rate RV preheating temperature TV
  • heating rate RF annealing temperature TG
  • annealing time tG cooling rate RE '
  • intermediate temperature TE' Cooling rate RE "
  • Temperature TE Holding time tE
  • Cooling rate RB and/or Temperature TB "are shown in Table 5.
  • the cold-rolled steel strips were then cooled in two stages.
  • the steel strips having a comparatively high cooling rate RZ ' have been cooled to an intermediate temperature TZ' by use of gas jet cooling.
  • the intermediate temperature TZ ' was the gas jet cooling ended and there was a roller cooling with a reduced cooling rate RZ "to an intermediate temperature TZ".
  • the two-stage cooling was followed by an over-aging treatment, via which the respective steel strip was cooled to the overaging temperature TU starting from the intermediate temperature TZ "at a cooling rate RU.
  • the yield strength Rp0.2, the tensile strength Rm, the elongation A80, the n value (10-20 / Ag) and the composition of the microstructure have been determined, these properties being determined on samples along the rolling direction ,
  • V-bend has been determined according to DIN EN ISO 7438.
  • the ratio of the minimum bending radius, ie the radius at which no visible crack occurs, to the sheet thickness should here be at most 2.0 and ideally does not exceed 1.7.
  • the minimum bending dome diameter has been determined at which no visible damage occurs. It should be 4 * sheet thickness, ideally 3 * sheet thickness. With respect to the present invention this means that the maximum bending dome diameter should not exceed 9.6 mm.
  • the hole expansion according to ISO 16630 with a hole diameter of 10 mm was determined with a drawing speed of 0.8 mm / s. It is at least 15%, ideally at least 18%.
  • Table 7 shows, for the total of 32 tests carried out in the manner described above, which of the steels specified in Table 1 has been used, which has been applied to the hot rolling variants indicated in Table 2, of which the cold rolling variants given in Table 3 have been used and which of the annealing process variants given in Tables 4, 5 and 6 has been passed through by the respective cold-rolled steel strip. Furthermore, Table 7 shows the mechanical properties and the composition of the microstructure as well as the properties determined according to DIN EN ISO 7438 ("V-bend", "U-bend”) and DIN ISO 16630 ("hole widening").
  • Table 1 stolen C Si Mn P S al Cr Ti Mo N B total A 0,147 0.29 1.61 0.011 0.001 0.027 0.62 0.037 0,007 0,004 0.0008 2.76 B 0.130 0.20 1.60 0,010 0.001 0.031 0.73 0,038 0,020 0,007 0.0008 2.77 C 0.140 0.20 1.57 0,008 0.001 0.037 0.71 0.047 0,020 0,008 0.0012 2.74 D 0.140 0.18 1.65 0,007 0.001 0.034 0.49 0.047 0,010 0,006 0.0011 2.57 e 0.130 0.21 1.68 0,010 0.001 0.037 0.51 0,045 0,020 0,006 0.0010 2.65 F 0.158 0.25 1.54 0,015 0,003 0,029 0.75 0,039 0,040 0,007 0.0013 2.83 G 0,119 0.23 1.75 0.009 0.001 0.032 0.63 0,051 0,010 0.005 0.0013 2.84 I 0.130 0.14 1.57 0,013 0,002

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Claims (12)

  1. Produit plat en acier laminé à froid, ayant la composition suivante en % en poids
    C: 0,11 -0,16%;
    Si: 0,1 -0,3%;
    Mn: 1,4 - 1,9 % ;
    Al : 0,02- 0,1 % ;
    Cr : 0,45- 0,85 % ;
    Ti : 0,025 - 0,06 % ;
    B : 0,0008 - 0,002 % ;
    le reste étant constitué de Fe et d'inévitables impuretés dues à la fabrication, dont font partie des teneurs en phosphore, soufre, azote ou molybdène, avec la condition que pour chacune de leurs teneurs s'applique :
    P : ≤ 0,02 %,
    S : ≤ 0,003 %,
    N : ≤ 0,008 %,
    Mo : ≤ 0,05 % en poids,
    qui présente une structure qui est constituée à raison de 60 - 90 % en volume de ferrite y compris ferrite bainitique, de 10 - 40 % en volume de martensite, de jusqu'à 5 % en volume d'austénite résiduelle et de jusqu'à 5 % en volume d'autres composants structuraux inévitables dus à la fabrication, et sa limite élastique Rp0,2 est d'au moins 440 MPa, sa résistance à la traction est d'au moins 780 MPa, son allongement à la rupture A80 est d'au moins 14 %, sa valeur n10-20/Ag est d'au moins 0,11 et sa valeur BH2 est d'au moins 25 MPa, déterminés chaque fois dans l'essai de traction selon DIN EN ISO 6892, forme des éprouvettes 2, éprouvettes longitudinales.
  2. Produit plat en acier laminé à froid selon la revendication 1, caractérisé en ce que sa teneur en Al est d'au maximum 0,05 % en poids.
  3. Produit plat en acier laminé à froid selon l'une quelconque des revendications précédentes, caractérisé en ce que sa teneur en Ti est d'au maximum ≤ 0,055 % en poids.
  4. Produit plat en acier laminé à froid selon la revendication 3, caractérisé en ce que sa teneur en Ti est d'au maximum 0,045 % en poids.
  5. Procédé pour la fabrication d'un produit plat en acier laminé à froid constitué conformément à l'une quelconque des revendications 1 à 4, comprenant les étapes de travail suivantes :
    a) coulée d'un acier ayant la composition selon l'une quelconque des revendications 1 à 4, pour l'obtention d'un demi-produit ;
    b) laminage à chaud du demi-produit pour l'obtention d'un feuillard laminé à chaud ayant une épaisseur de 2 à 5,5 mm, la température initiale du laminage à chaud valant 1000 - 1300 °C et la température finale du laminage à chaud valant 840 - 950 °C ;
    c) bobinage du feuillard laminé à chaud en un rouleau à une température de bobinage de 480 - 650 °C ;
    d) laminage à froid du feuillard laminé à chaud pour l'obtention d'un produit plat en acier laminé à froid, d'une épaisseur de 0,6 - 2,4 mm, le degré de laminage à froid atteint par le laminage à froid valant 35 - 80 % ;
    e) traitement thermique, se déroulant en passage continu du produit plat en acier laminé à froid, dans lequel
    e.1) le produit plat en acier laminé à froid est d'abord chauffé à une température de préchauffage de jusqu'à 870 °C dans une étape de préchauffage à une vitesse de chauffage de 0,2 - 45 °C/s,
    e.2) le produit plat en acier laminé à froid est ensuite maintenu à une température de recuit de 750 - 870 °C, dans une étape d'arrêt, pendant une durée de recuit de 8 - 260 s, en option le produit plat en acier préchauffé étant porté à la température de recuit respective pendant l'étape d'arrêt,
    e.3) à la fin de la durée de recuit le produit plat en acier laminé à froid est refroidi à une vitesse de refroidissement de 0,5 -110 K/s.
  6. Procédé selon la revendication 5, caractérisé en ce qu'entre les étapes de travail a) et b) le demi-produit est maintenu à une température ≥ 300 °C.
  7. Procédé selon la revendication 5, caractérisé en ce qu'entre les étapes de travail a) et b) le demi-produit est refroidi jusqu'à la température ambiante à une vitesse de refroidissement ≤ 60 °C/h.
  8. Procédé selon la revendication 6 ou 7, caractérisé en ce qu'avant l'étape de travail b) le demi-produit est chauffé jusqu'à la température initiale de laminage à chaud respective pendant une durée de chauffage de jusqu'à 500 minutes.
  9. Procédé selon l'une quelconque des revendications 5 à 8, caractérisé en ce que le produit plat en acier laminé à froid passe par une galvanisation par immersion à chaud qui fait suite en passage continu à l'étape de travail e.3), et en ce que la température à laquelle le produit plat en acier laminé à froid est refroidi dans l'étape de travail e.3) vaut 455 - 550 °C.
  10. Procédé selon l'une quelconque des revendications 5 à 8, caractérisé en ce que dans l'étape de travail e.3) le produit plat en acier laminé à froid est refroidi jusqu'à la température ambiante.
  11. Procédé selon la revendication 10, caractérisé en ce que dans l'étape de travail e.3) le produit plat en acier laminé à froid est refroidi jusqu'à la température ambiante dans au moins deux étapes de refroidissement, en ce que dans la première étape de refroidissement le produit plat en acier laminé à froid est refroidi jusqu'à 250 - 500 °C et est maintenu dans cette plage de température pendant jusqu'à 760 s, et en ce que le produit plat en acier laminé à froid est ensuite refroidi jusqu'à la température ambiante.
  12. Procédé selon l'une quelconque des revendications 10 et 11, caractérisé en ce qu'après le refroidissement jusqu'à la température ambiante le produit plat en acier laminé à froid est recouvert d'un revêtement protecteur métallique par électrolyse.
EP13726805.8A 2012-06-05 2013-06-05 Produit en acier plat et procédé de fabrication d'un produit en acier plat Active EP2855718B1 (fr)

Applications Claiming Priority (2)

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DE102012104894 2012-06-05
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KR102073442B1 (ko) 2020-02-04
US20150122377A1 (en) 2015-05-07
US20150152533A1 (en) 2015-06-04
KR20150023566A (ko) 2015-03-05
KR20150028267A (ko) 2015-03-13
CN104583424B (zh) 2017-03-08
JP6374864B2 (ja) 2018-08-15
US9976205B2 (en) 2018-05-22
JP6310452B2 (ja) 2018-04-11
EP2855717A1 (fr) 2015-04-08
WO2013182621A1 (fr) 2013-12-12
EP2855717B1 (fr) 2020-01-22
CN104520448A (zh) 2015-04-15
WO2013182622A1 (fr) 2013-12-12
JP2015525293A (ja) 2015-09-03
EP2855718A1 (fr) 2015-04-08
CN104520448B (zh) 2017-08-11
KR102073441B1 (ko) 2020-02-04
JP2015525292A (ja) 2015-09-03
CN104583424A (zh) 2015-04-29

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