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EP2855717B1 - Tôle d'acier et méthode pour son obtention - Google Patents

Tôle d'acier et méthode pour son obtention Download PDF

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Publication number
EP2855717B1
EP2855717B1 EP13726583.1A EP13726583A EP2855717B1 EP 2855717 B1 EP2855717 B1 EP 2855717B1 EP 13726583 A EP13726583 A EP 13726583A EP 2855717 B1 EP2855717 B1 EP 2855717B1
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EP
European Patent Office
Prior art keywords
cold
temperature
steel product
flat steel
rolled
Prior art date
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EP13726583.1A
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German (de)
English (en)
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EP2855717A1 (fr
Inventor
Andreas Bongards
Sigrun Voss
Sebastian FELDHAUS
Udo Paul
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
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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
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    • 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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    • 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
    • C—CHEMISTRY; METALLURGY
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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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    • 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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    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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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 and a method for producing such a flat steel product.
  • Dual-phase steels have been used in automotive engineering for some time.
  • a large number of alloy concepts for such steels are known, each of which is composed in such a way that it meets a wide variety of requirements.
  • Many of the known concepts are based on an alloy with molybdenum or require complex manufacturing processes, in particular very rapid cooling in cold strip annealing, in order to produce the desired structure of the steel.
  • the price of molybdenum in the market fluctuates widely is subject to, the production of steels that contain high proportions of Mo is associated with a high cost risk. This contrasts with the positive effects that molybdenum has on the mechanical properties of dual-phase steels.
  • Sufficiently high Mo contents delay the formation of pearlite during cooling and thus ensure the formation of a structure that is favorable for the requirements of the respective steel.
  • a method for producing a hot strip from a dual-phase steel which (in% by weight) 0.03-0.15% C, up to 1.5% Si, 0.05-2.5% Mn, up to 0.05% P, 0.005-0.5% Al, 0.02-2% Cr, up to 0.01% N, up to 0.03% Ti, up to 0.06% Nb and the remainder contains iron and unavoidable impurities.
  • the contents of Mn and Cr should meet the condition Cr + Mn ⁇ 3.5 and the contents of Ti and Nb the condition 0.005% ⁇ 2 x Ti + Nb ⁇ 0.06%.
  • the hot strip should have a structure that (in area%) consists of 55 - 95% polygonal ferrite and 5 - 45% hard phases that are formed at low temperatures.
  • an appropriately assembled steel is cast into slabs, which are cooled to 1280 ° C and then hot rolled to a hot strip with a hot rolling temperature of Ar3 ⁇ 50 ° C.
  • the hot strip obtained is then coiled at a coiling temperature of up to 250 ° C.
  • the low reel temperature leads to the formation of the strength-increasing phases and thus to one very strong hot strip. However, this is difficult to process further. This is particularly evident in the attempt to produce cold-rolled steel strip from hot strips produced in this way.
  • the steel consists of (in% by weight) 0.07-0.2% C, 0.3-1.5% Si and Al, 1.0-3.0% Mn, bis to 0.02% P, up to 0.005% S, 0.1 - 0.5% Cr and 0.001 - 0.008% N and additionally 0.002 - 0.05% Ti or 0.002 - 0.05% Nb.
  • the hot-rolled steel sheet has a structure which (in area%) consists of 7-35% ferrite with a particle diameter of 0.5-3.0 ⁇ m and the rest of bainite ferrite or bainite and martensite. High levels of at least 0.5% Si contribute to increasing the strength of the steel, while aluminum is only added to calm the steel during its production. A low reel temperature of less than 430 ° C is also prescribed here in order to ensure the formation of a sufficient amount of strength-increasing hard phases in the hot strip.
  • the setting of the structure in the hot strip also has the consequence here that the hot strip produced in this known manner is also difficult to process into cold-rolled steel strip.
  • the steel strip consists of a steel which, in addition to iron and unavoidable impurities, consists of (in% by weight) 0.10 - 0.18% C, 1.90 - 2.50% Mn, 0.30 - 0, 50% Si, 0.50-0.70% Al, 0.10-0.50% Cr, 0.001-0.10% P, 0.01-0.05% Nb, up to 0.004% Ca, up to 0.05% S, up to 0.007% N, and optionally at least one of the following: 0.005 - 0.50% Ti, 0.005 - 0.50% V, 0.005 - 0.50% Mo, 0.005 - 0.50% Contains Ni, 0.005-0.50% Cu and up to 0.005% B.
  • the steel thus composed is said to improve deformability offer high strength and at the same time have good weldability and surface quality together with good manufacturability and coatability.
  • the object of the invention was to provide a flat steel product which has optimized mechanical properties and can be produced inexpensively without having to resort to expensive alloy elements which are subject to large fluctuations in their procurement costs.
  • the solution according to the invention to the above-mentioned object consists in the fact that such a flat steel product is in the cold-rolled state as specified in claim 1.
  • Carbon enables the formation of martensite in the structure and is therefore an essential element in the steel according to the invention for setting the desired high strength.
  • the steel according to the invention contains at least 0.12% by weight C.
  • an excessively high C content has a negative effect on the welding behavior.
  • the general rule here is that the weldability of a steel decreases with its carbon content.
  • the maximum carbon content in the steel according to the invention is therefore limited to 0.18% by weight.
  • Silicon is also used to increase strength by increasing the hardness of the ferrite.
  • the minimum silicon content of a steel according to the invention is 0.05% by weight. Too high a silicon content leads both to undesirable grain boundary oxidation, which negatively influences the surface of a flat steel product produced from steel according to the invention, and to difficulties if 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 steel according to the invention is 0.2% by weight.
  • Manganese prevents the formation of pearlite on cooling. As a result, the desired formation of martensite is promoted in the steel according to the invention and the strength of the steel is increased. A sufficiently high manganese content to suppress pearlite formation is 1.9% by weight. Manganese also has the negative property of forming segregations or reducing sweat suitability. In addition, the presence of higher Mn contents causes an increased expenditure of energy when melting a steel according to the invention. In order to avoid the negative effects of Mn in the steel according to the invention, the upper limit is that provided for Mn Content range of a steel according to the invention at 2.2 wt .-%.
  • Aluminum is of particular importance in the alloy according to the invention. Used at low levels, it is used for deoxidation. The amount of at least 0.2% by weight provided according to the invention promotes the formation of residual austenite. Similar to known TRIP steels, this has a positive effect on the elongation at break and the n-value of flat steel products made from steel according to the invention. However, a content of more than 0.5% by weight of Al deteriorates the slab properties in the event that the steel according to the invention is cast as a preliminary product into slabs or thin slabs and possibly leads to crack formation. In addition, high aluminum contents in the steel have a negative effect on the coating behavior. The Al contents in a steel according to the invention are therefore limited to 0.5% by weight.
  • Chromium is present in the steel according to the invention, such as manganese, to increase the strength.
  • the presence of Cr increases the hardenability and thus the proportion of martensite in the steel.
  • the Cr content required for this is at least 0.05% by weight.
  • the Cr content of a steel according to the invention is simultaneously limited to a maximum of 0.2% by weight.
  • Niobium forms very fine precipitates in the steel according to the invention and thereby also increases the strength.
  • An Nb content of at least 0.01% by weight is required for this. Too high levels would increase the positive influence of Nb too much and negatively influence the elongation at break.
  • the Nb content in a steel according to the invention is therefore limited to 0.06% by weight, the effect of Nb occurring particularly reliably when the Nb content is 0.01-0.04% by weight.
  • Phosphorus, sulfur, nitrogen, molybdenum, boron, titanium, nickel and copper are at most present in the steel according to the invention as impurities in such low contents that they have no influence on the properties of the steel and a steel flat product according to the invention produced therefrom. Accordingly, in a steel according to the invention at most 0.02% by weight of P, at most 0.003% by weight of S, at most 0.008% by weight of N, at most 0.1% by weight of Mo, at most 0.0007% by weight.
  • the sum of the contents of the alloying elements C, Si, Mn, Al, Cr and Nb present in effective amounts is at least 2.5% by weight and does not exceed 3.5% by weight. If the sum of the alloy contents is too low, there is a risk that the desired mechanical properties will not be achieved. If, on the other hand, the sum of the alloy contents is too high, a very high strength of over 900 MPa, which is not desired here, is achieved with poor deformation behavior.
  • the respective preliminary product can, if necessary, remain in a furnace for up to 500 minutes at a sufficient furnace temperature. Alternatively, you can the respective preliminary product can also be fed to hot rolling directly while it is still sufficiently hot.
  • the reel temperature is set at 480-610 ° C. because a lower reel temperature would lead to a much firmer hot-rolled steel flat product (“hot strip”), which could only be processed under difficult conditions.
  • a reel temperature above 610 ° C in combination with the chromium content provided according to the invention would increase the risk of grain boundary oxidation.
  • the coiled hot strip cools to room temperature in the coil. After cooling, it can optionally be pickled to remove scale and dirt adhering to it.
  • the hot strip is rolled in one or more cold rolling steps to a cold-rolled flat steel product ("cold strip").
  • cold rolling is carried out with a total cold rolling degree of 40-80% in order to achieve the desired cold strip thickness of 0.6-2.4 mm.
  • the cold strip is subjected to continuous annealing. This first serves to set the desired mechanical properties.
  • the cold-rolled flat steel product can be used to prepare the cold-rolled flat steel product for subsequent coating with a metallic coating, which protects the cold-rolled flat steel product from corrosive attacks in later use.
  • a metallic coating which protects the cold-rolled flat steel product from corrosive attacks in later use.
  • Such a coating can be applied on an industrial scale in a particularly cost-effective manner by hot-dip coating.
  • the annealing provided according to the invention can be carried out in a conventional, hot-dip coating system that is carried out in one pass. Alternatively, electrolytic galvanizing can also follow the annealing.
  • both the heating to the respective maximum annealing temperature and the subsequent cooling can take place in one or more steps.
  • the heating takes place initially in a preheating stage at a rate of 0.2 K / s to 45 K / s to a preheating temperature of up to 870 ° C, in particular 690 - 860 ° C or 690 - 840 ° C.
  • the flat steel product then goes into a holding stage in which, provided that its preheating temperature is less than the target maximum annealing temperature, it reaches the maximum annealing temperature of 750 - 870 ° C with further heating.
  • the flat steel product is held at the respective maximum annealing temperature until the end of the holding stage is reached.
  • the annealing time within which the flat steel product in the holding stage on the maximum annealing temperature is 8 - 260 s. If the temperature is too low or the time is too short, the material would not recrystallize. As a result, on the one hand, there would not be enough austenite available for the transformation of the structure during cooling to form martensite. On the other hand, unrecrystallized steel would result in pronounced anisotropy.
  • a too long annealing time or a too high temperature lead to a very coarse structure and thus to poorer mechanical properties.
  • the cold-rolled steel flat product is cooled at a cooling rate of 0.5 - 110 K / s.
  • the cooling rate is set within this window so that pearlite formation is largely avoided.
  • the cold-rolled steel flat product is to be hot-dip coated after annealing, it is cooled to a temperature of 455 - 550 ° C in the course of cooling.
  • the cold-rolled flat steel product tempered in this way then passes through a Zn melt bath which has a temperature of 450-480.degree. If the temperature of the cold-rolled flat steel product falls within the range intended for the zinc bath, the steel strip can be held for up to 100 s before entering the zinc bath.
  • the temperature of the steel strip is greater than 480 ° C
  • the flat steel product is cooled until it enters the zinc bath at a cooling rate of up to 10 K / s until its Temperature falls in the temperature range provided for the zinc bath, in particular is equal to the zinc bath temperature.
  • the thickness of the Zn-based protective layer present on the flat steel product is adjusted in a known manner by means of a stripping device.
  • a further heat treatment can optionally follow the hot-dip coating, in which the hot-dip coated steel flat product is heated to up to 550 ° C. in order to burn in the zinc layer.
  • the cold-rolled flat steel product obtained is cooled to room temperature.
  • the method according to the invention for producing flat steel products according to the invention consequently comprises the following variants:
  • the cold-rolled flat steel product (“cold strip”) is heated in a preheating furnace at a heating rate of 10-45 K / s to a preheating temperature of 660-840 ° C.
  • the preheated cold strip is then passed through an oven zone, in which the cold strip is held at a temperature of 760 - 860 ° C for a holding time of 8 - 24 s.
  • further heating occurs with a heating rate of 0.2 - 15 K / s.
  • the cold-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 at most 45 s.
  • the molten zinc bath has a temperature of 455 - 465 ° C.
  • the cold strip in the molten zinc bath cools down to a temperature 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 adjusted in a manner known per se on the cold strip emerging from the molten zinc bath and now provided with a zinc coating. Finally, the coated cold strip is cooled to room temperature.
  • the cold rolled flat steel product is in an entrance heating zone of a continuous furnace with a Heating rate of up to 25 K / s brought to a target temperature that is 760 - 860 ° C.
  • the cold-rolled flat steel product thus heated is held at an annealing temperature of 750-870 ° C., in particular 780-870 ° C., for 35-150 s.
  • an annealing temperature 750-870 ° C., in particular 780-870 ° C., for 35-150 s.
  • it is during the holding time, i.e. H. within this holding zone, heated to the respective annealing temperature with a heating rate of up to 3 K / s.
  • a two-stage cooling takes place, in which the cold-rolled flat steel product is first slowly cooled with a cooling rate of 0.5-10 K / s to an intermediate temperature which is 640-730 ° C, and then with a cooling rate of 5 - 110 K / s accelerated to a temperature of 455 - 550 ° C is cooled.
  • the cold-rolled flat steel product cooled to the relevant temperature then passes through a molten zinc bath.
  • the molten zinc bath has a temperature of 450 - 480 ° C.
  • the coating thickness is adjusted in a manner known per se on the cold-rolled flat steel product emerging from the molten zinc bath and now provided with a zinc coating.
  • an annealing treatment (“galvannealing") can be carried out in order to cause alloying in the zinc coating.
  • the cold strip 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 can be subjected to skin pass rolling in order to improve its mechanical properties and the surface quality of the coating.
  • the degree of skin pass set in this case is typically in the range of 0.1-2.0%, in particular 0.1-1.0%.
  • the cold-rolled flat steel product which is composed and produced according to the invention, can also undergo a heat treatment in a conventional annealing furnace as an alternative to the possibility of hot-dip coating described above, in which the heating (working step e.1)) and the annealing at the respective annealing temperature (working step e.2) are carried out in the manner described above, but in which step e.3 is carried out at least in two stages, in that the cold-rolled flat steel product is first cooled to a temperature range of 250-500 ° C. and then stays in this temperature range for up to 760 s and subsequently is further cooled. In this way, the residual austenite in the structure of the steel flat product according to the invention is stabilized.
  • the following heat treatment steps are then carried out in a continuous furnace:
  • the cold-rolled flat steel 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 cold-rolled flat steel product thus heated is then passed through an oven zone in which the cold-rolled flat steel product is held for a holding time of 70-260 s at an annealing temperature of 750-870 ° C., in particular 750-850 ° C. Depending on the preheating temperature reached in the previous step, further heating occurs with a heating rate of up to 5 K / s.
  • the cold-rolled flat steel product that has been annealed in this way is then subjected to a two-stage cooling, in which it is first cooled to an intermediate temperature of 450-570 ° C. at a rate of 3-30 K / s.
  • This cooling can be carried out as air and / or gas cooling.
  • This is followed by a slower cooling, in which the cold rolled Flat steel product is cooled to 400-500 ° C. at a cooling rate of 1-15 K / s.
  • the respective cooling can be followed by an aging treatment, in which the cold-rolled flat steel product is kept at a temperature of 250-500 ° C., in particular 250-330 ° C., for a holding time of 150-760 s. Depending on the respective inlet temperature, the cold-rolled flat steel product cools down at a cooling rate of up to 1.5 K / s.
  • the cold-rolled flat steel product heat-treated in the manner described above can also be subjected to skin pass rolling in order to further improve its mechanical properties.
  • the levels of skin pass set here are typically in the range of 0.1-2.0%, in particular 0.1-1.0%.
  • the heat-treated and optionally skin-rolled, cold-rolled flat steel product can then pass through a coating system for electrolytic coating, in which the respective metallic protective layer, for. B. a zinc alloy layer, is deposited in a known manner electro-chemically ("electrolytically") on the cold-rolled flat steel product.
  • the flat steel product is characterized by a structure consisting of 50-90% by volume of ferrite including bainitic ferrite, 5-40% by volume of martensite, up to 15% by volume of residual austenite and up to 10 Vol .-% consists of other structural components that are unavoidable due to the manufacturing process, the residual austenite content optimally being in the range of 6 - 12 Vol .-%.
  • flat steel products according to the invention can be produced reliably using the method according to the invention.
  • the steel melts A-I were cast into slabs and, after cooling in an oven, were heated to the respective hot rolling starting temperature WAT.
  • the slabs entering the hot rolling stack with the hot rolling start temperature WAT were hot rolled to a hot rolled steel strip with a thickness WBD at a final temperature WET.
  • the hot-rolled steel strips were cooled to a coiling temperature HT, at which they were then wound into a coil and cooled to room temperature.
  • the hot-rolled steel strips obtained in this way are closed with a respective overall degree of deformation KWG cold rolled steel strip with a thickness KBD has been cold rolled.
  • the cold-rolled steel strips thus obtained have been subjected to various annealing tests.
  • the steel strips in a holding zone were first heated to a maximum annealing temperature TG at a heating rate RF, at which they were then held.
  • a heating rate RF for the passage of the entire holding zone, i.e. H. including the paver heating and holding, an annealing time tG was required.
  • the cold-rolled steel strips are then also in one step with a cooling rate RE cooled to a temperature TE.
  • the steel strips emerging from the melt pool had a Zn alloy coating, which protects them against corrosion.
  • heating rate RV heating temperature TV
  • preheating rate RF heating temperature TG
  • annealing time tG heating time tE
  • temperature TE temperature TE
  • holding time tE The operating parameters "heating rate RV”, “preheating temperature TV”, “preheating rate RF”, “annealing temperature TG”, “annealing time tG”, “cooling rate rE”, “temperature TE”, “holding time tE” are taken into account in the production of the hot and cold rolled steel strips "," Cooling rate RB “and” Bath temperature TB “are given in Table 4.
  • the steel strips are comparable to one low cooling rate RE 'have been cooled to an intermediate temperature TE'.
  • the intermediate temperature TE 'is reached the respective steel strips have been rapidly cooled to the respective temperature TE with an increased cooling rate RE.
  • the steel strips emerging from the melt pool had a Zn alloy coating, which protects them against corrosion.
  • cooling rate RV The operating parameters "heating rate RV”, "preheating temperature TV”, “heating rate RF”, "annealing temperature TG”, “annealing time tG”, “cooling rate RE '”, “intermediate temperature TE'”, “taken into account in the production of the hot and cold rolled steel strips” Cooling rate RE “,” temperature TE “,” holding time tE “,” cooling rate RB “and” temperature TB “are given in Table 5.
  • the cold-rolled steel strips were then cooled in two stages in the uninterrupted connection.
  • the steel strips were cooled to an intermediate temperature TZ 'with a comparable high cooling rate RZ' by using gas jet cooling.
  • the intermediate temperature TZ ' was reached, the gas jet cooling was ended and roller cooling took place with a reduced cooling rate RZ "to an intermediate temperature TZ".
  • the two-stage cooling was followed by an aging treatment, by means of which the respective steel strip was cooled from the intermediate temperature TZ "to the aging temperature TU at a cooling rate RU.
  • cooling rate RV heating rate
  • preheating temperature TV heating rate RG
  • annealing temperature TG heating rate RG
  • annealing time tG heating rate RZ '
  • intermediate temperature TZ' intermediate temperature TZ
  • taken into account in the production of the hot and cold rolled steel strips Cooling rate RZ "”, “intermediate temperature TZ” ",” cooling rate RU “and” aging temperature TU "are given in Table 6.
  • the yield strength Rp0.2, the tensile strength Rm, the elongation A80, the n-value (10-20 / Ag) and the composition of the structure were determined on the cold-rolled steel strips produced in the manner described above, these properties in each case on samples have been determined lengthways to the rolling direction.
  • the behavior in the V-bend has been determined in accordance with DIN EN ISO 7438.
  • the ratio of the minimum bending radius, i.e. the radius at which there is no visible crack, to the sheet thickness should be at most 1.5 here and ideally does not exceed 1.0.
  • the minimum bending dome diameter at which no visible damage occurs was determined in the bending test according to DIN EN ISO 7438 (sample dimension sheet thickness * 20mm ⁇ 120mm). It should be 2 ⁇ sheet thickness, ideally 1.5 ⁇ sheet thickness. In relation to the present invention, this means that the maximum bending mandrel diameter should not exceed 4.8 mm.
  • the hole expansion according to ISO 16630 with a hole diameter of 10 mm and a drawing speed of 0.8 mm / s was determined on punched samples from the cold-rolled steel strips produced in the manner described above. It is at least 14%, ideally at least 16%.
  • Table 7 shows for the total of 58 tests carried out in the manner described above, which of the steels specified in Table 1 was processed, which of the hot rolling variants specified in Table 2 was used, and which of the cold rolling variants specified in Table 3 were used and which of the annealing process variants indicated in Tables 4, 5 and 6 has been run through by the respective cold-rolled steel strip.
  • Table 7 shows the respective skin level DG, the mechanical properties and the composition of the structure as well as the properties determined in accordance with DIN EN ISO 7438 ("V-bend", "U-bend”) and DIN ISO 16630 ("Hole expansion”) specified.

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Claims (12)

  1. Produit plat en acier laminé à froid, qui présente la composition suivante en % en poids : C : 0,12 à 0,18% ; Si : 0,05 à 0,2% ; Mn : 1,9 à 2,2% ; Al : 0,2 à 0,5% ; Cr : 0,05 à 0,2% ; Nb : 0,01 à 0,06% ;
    le reste étant du Fe et des impuretés inévitables liées au processus de fabrication, qui comprennent les teneurs en phosphore, soufre, azote, molybdène, bore, titane, nickel et cuivre, à condition que leurs teneurs satisfassent respectivement : P : ≤ 0,02 %, S : ≤ 0,003 %, N : ≤ 0,008 %, Mo : ≤ 0,1 %, B : ≤ 0,0007 %, Ti : ≤ 0,01 %, Ni : ≤ 0,1 %, Cu : ≤ 0,1 %,
    la somme des teneurs en C, Si, Mn, Al, Cr et Nb étant de 2,5 à 3,5 % en poids, et qui présente une structure qui est constituée par 50 à 90 % en volume de ferrite, y compris la ferrite bainitique, 5 à 40 % en volume de martensite, jusqu'à 15 % en volume d'austénite résiduelle et jusqu'à 10 % en volume d'autres constituants de structure inévitables liés au processus de fabrication, sa limite d'élasticité Rp0,2 étant d'au moins 440 MPa, sa résistance à la traction Rm étant d'au moins 780 MPa, son allongement à la rupture A80 étant d'au moins 14 %, son n10-20/Ag étant d'au moins 0,1 et sa valeur BH2 étant d'au moins 25 MPa, à chaque fois déterminés lors de l'essai de traction selon DIN EN ISO 6892, forme d'éprouvette 2, éprouvette longitudinale.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que sa teneur en Mo est d'au plus 0,05 % en poids.
  3. Produit plat en acier selon la revendication 1 ou 2, caractérisé en ce que sa teneur en austénite résiduelle est de 6 à 12 % en volume.
  4. Procédé de fabrication d'un produit plat en acier laminé à froid selon l'une quelconque des revendications 1 à 3, comprenant les étapes de travail suivantes :
    a) le coulage d'un acier de la composition suivante en % en poids pour former un produit préliminaire : C : 0,12 à 0,18 %, Si : 0,05 à 0,2 %, Mn : 1,9 à 2,2 %, Al : 0,2 à 0,5 %, Cr : 0,05 à 0,2 %, Nb : 0,01 à 0,06 %, le reste étant du Fe et des impuretés inévitables, qui comprennent les teneurs en phosphore, soufre, azote, molybdène, bore, titane, nickel et cuivre, à condition que leurs teneurs satisfassent respectivement : P : ≤ 0,02 %, S : ≤ 0,003 %, N : ≤ 0,008 %, Mo : ≤ 0,1 %, B : ≤ 0,0007 %, Ti : ≤ 0,01 %, Ni : ≤ 0,1 %, Cu : ≤ 0,1 %, la somme des teneurs en C, Si, Mn, Al, Cr et Nb étant de 2,5 à 3,5 % en poids ;
    b) le laminage à chaud du produit préliminaire pour former une bande chaude d'une épaisseur de 2 à 5,5 mm, la température initiale du laminage à chaud étant de 1 000 à 1 300 °C, et la température finale du laminage à chaud étant de 840 à 950 °C ;
    c) le bobinage de la bande chaude en une bobine à une température de dévidoir de 480 à 610 °C ;
    d) le laminage à froid de la bande chaude pour former un produit plat en acier laminé à froid d'une épaisseur de 0,6 à 2,4 mm, le degré de laminage à froid obtenu par le laminage à froid étant de 40 à 80 % ;
    e) le recuit en passage continu du produit plat en acier laminé à froid,
    e.1) le produit plat en acier laminé à froid étant tout d'abord chauffé lors d'une étape de préchauffage avec un taux de chauffage de 0,2 à 45 °C/s à une température de préchauffage de jusqu'à 870 °C,
    e.2) le produit plat en acier laminé à froid étant ensuite maintenu lors d'une étape de maintien pendant une durée de recuit de 8 à 260 s à une température de recuit de 750 à 870 °C, le produit plat en acier préchauffé étant éventuellement soumis à un chauffage final pendant l'étape de maintien à la température de recuit respective,
    e.3) le produit plat en acier laminé à froid étant refroidi après la fin de la durée de recuit à un taux de refroidissement de 0,5 à 110 K/s.
  5. Procédé selon la revendication 4, caractérisé en ce que le produit préliminaire est chauffé avant l'étape de travail b) pendant une durée de chauffage de jusqu'à 500 minutes à la température initiale de laminage à chaud respective.
  6. Procédé selon la revendication 4, caractérisé en ce que le produit préliminaire est refroidi après l'étape de travail a) à la température initiale de laminage à chaud respective, puis introduit directement dans le laminage à chaud.
  7. Procédé selon l'une quelconque des revendications 4 à 6, caractérisé en ce que le produit plat en acier laminé à froid traverse un revêtement par immersion en masse fondue, qui suit en passage continu l'étape de travail e.3), et en ce que la température à laquelle le produit plat en acier laminé à froid est refroidi à l'étape de travail e.3) est de 455 à 550 °C.
  8. Procédé selon l'une quelconque des revendications 4 à 6, caractérisé en ce que le produit plat en acier laminé à froid est refroidi à la température ambiante à l'étape de travail e.3).
  9. Procédé selon la revendication 8, caractérisé en ce que le produit plat en acier laminé à froid est refroidi en au moins deux étapes de refroidissement à l'étape de travail e.3).
  10. Procédé selon la revendication 8 ou 9, caractérisé en ce que le produit plat en acier laminé à froid est refroidi à une température de 250 à 500 °C à l'étape de travail e.3), et maintenu dans cette plage de température pendant jusqu'à 760 s, afin de réaliser un traitement de vieillissement, et en ce que le produit plat en acier laminé à froid est ensuite soumis à un refroidissement final.
  11. Procédé selon l'une quelconque des revendications 8 à 10, caractérisé en ce que le produit plat en acier laminé à froid est revêtu électrolytiquement avec un revêtement protecteur métallique après le refroidissement à température ambiante.
  12. Procédé selon l'une quelconque des revendications 4 à 10, caractérisé en ce que le produit plat en acier laminé à froid est enfin écroui avec un degré d'écrouissage de 0,1 à 2,0 %.
EP13726583.1A 2012-06-05 2013-06-05 Tôle d'acier et méthode pour son obtention Active EP2855717B1 (fr)

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PCT/EP2013/061628 WO2013182621A1 (fr) 2012-06-05 2013-06-05 Acier, produit en acier plat et procédé de fabrication d'un produit en acier plat

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KR102073442B1 (ko) 2020-02-04
JP6374864B2 (ja) 2018-08-15
KR20150028267A (ko) 2015-03-13
CN104520448B (zh) 2017-08-11
WO2013182621A1 (fr) 2013-12-12
JP2015525292A (ja) 2015-09-03
KR102073441B1 (ko) 2020-02-04
JP6310452B2 (ja) 2018-04-11
KR20150023566A (ko) 2015-03-05
WO2013182622A1 (fr) 2013-12-12
US20150122377A1 (en) 2015-05-07
CN104583424B (zh) 2017-03-08
EP2855717A1 (fr) 2015-04-08
US20150152533A1 (en) 2015-06-04
CN104583424A (zh) 2015-04-29
US9976205B2 (en) 2018-05-22
EP2855718B1 (fr) 2019-05-15
EP2855718A1 (fr) 2015-04-08
JP2015525293A (ja) 2015-09-03
CN104520448A (zh) 2015-04-15

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