EP2855718A1 - Acier, produit en acier plat et procédé de fabrication d'un produit en acier plat - Google Patents

Acier, produit en acier plat et procédé de fabrication d'un produit en acier plat

Info

Publication number
EP2855718A1
EP2855718A1 EP13726805.8A EP13726805A EP2855718A1 EP 2855718 A1 EP2855718 A1 EP 2855718A1 EP 13726805 A EP13726805 A EP 13726805A EP 2855718 A1 EP2855718 A1 EP 2855718A1
Authority
EP
European Patent Office
Prior art keywords
cold
temperature
steel
product
rolled steel
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.)
Granted
Application number
EP13726805.8A
Other languages
German (de)
English (en)
Other versions
EP2855718B1 (fr
Inventor
Ekatherina BOCHAROVA
Sigrun EBEST
Dorothea MATTISSEN
Roland Sebald
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
Original Assignee
ThyssenKrupp Steel Europe AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP2855718A1 publication Critical patent/EP2855718A1/fr
Application granted granted Critical
Publication of EP2855718B1 publication Critical patent/EP2855718B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
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    • 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
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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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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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
    • C21D8/0247—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
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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
    • C21D8/0405—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—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
    • 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
    • C21D8/0421—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
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    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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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 cost-producible, higher-strength steel.
  • the invention likewise relates to a flat steel product produced from such a steel and to a method for producing the same
  • 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 desired structure of the steel. Since 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.
  • molybdenum has on the mechanical properties of dual-phase steels. For example, sufficiently high Mo contents retard perlite formation during cooling and
  • the object of the invention was to provide a steel and a flat steel product, which have optimized mechanical properties and can be produced inexpensively, without being expensive, in terms of their procurement costs
  • this object has been achieved in relation to the steel in that such a steel has the composition given in claim 1.
  • the flat steel product the
  • a steel according to the invention which solves the abovementioned objects accordingly has the following composition (in% by weight):
  • Contaminants to which levels of phosphorus, sulfur, nitrogen or molybdenum are included provided that the levels of P, S, N or Mo are:
  • Carbon allows the formation of martensite in the microstructure and is therefore in the steel of the invention for setting the desired high strength
  • the steel of the invention contains at least 0.11 wt .-% C. Too high a C content, however, has a negative effect on the welding behavior. In general, the weldability of a steel decreases with the level of its carbon content. To negative influences of the C content on his
  • steel of the invention limited the maximum carbon content to 0.16 wt .-%.
  • Silicon is also used to increase strength by increasing the hardness of the ferrite.
  • the minimum content of silicon of a steel according to the invention is 0.1% by weight. Too high a content of silicon, however, leads to both the undesirable
  • Grain boundary oxidation which is the surface of a Steel flat product produced according to the invention steel negatively affected, as well as to difficulties when a flat steel product according to the invention to improve its corrosion resistance with a metallic coating is to be dip-coated.
  • the upper limit of the Si content of a steel according to the invention is 0.3% by weight.
  • the upper limit of the content range of Mn of a steel according to the invention is 1.9% by weight.
  • Aluminum is used in a steel according to the invention.
  • 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 steel according to the invention 0.02 - 0.1 wt .-%, in particular 0.02 - 0.05 wt .-%, is.
  • Chromium is in the steel according to the invention such as manganese for
  • the required Cr content is at least 0.45 wt .-%. Too high
  • chromium content can promote grain boundary oxidation.
  • the Cr content of a steel according to the invention is limited to a maximum of 0.85 wt .-%.
  • Titanium is a steel according to the invention for
  • provided steel according to the invention B can fully unfold its strength-increasing effect.
  • the upper limit of the titanium content is limited to 0.06 wt .-%, in particular 0.055 wt%, with levels of up to 0.045 wt. -% have been found to be particularly practical.
  • a content of at least 0.0008 wt .-% B is necessary.
  • a B content of more than 0.002 wt .-% leads to an undesirable
  • Phosphorus, sulfur, nitrogen and molybdenum are present in the steel according to the invention at most as impurities in such low levels that they have no influence on the properties of the steel and one of them
  • Impurities are present, the production-related, for example by scraping, into the steel
  • the method according to the invention for the production of a flat steel product according to the invention comprises the following steps: a) casting a composite according to the invention
  • the precursor may be a slab or a thin slab; b) hot rolling the precursor into a hot strip having a thickness of 2 to 5.5 mm, wherein the
  • the cold-rolled steel flat product is cooled at the end of the annealing period at a cooling rate of 0.5 - 110 K / s.
  • the precursor should continue either while still hot
  • the respective precursor can, if necessary, in an oven over a period of up to 500 minutes at a
  • the reel temperature is set according to the invention to 480-650 ° C, because a lower reel temperature to a much firmer hot-rolled steel flat product
  • 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.
  • the hot strip is placed in one or more
  • Cold rolling steps rolled to a cold-rolled steel flat product (“cold strip”). Starting from the inventively predetermined thickness of the hot strip is doing with a Total cold rolling degree of 35 - 80% cold rolled to achieve the desired cold rolled 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
  • Hot dip coating plant to be performed.
  • the glowing can also be a
  • 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
  • Holding level in which it, provided its preheating temperature is less than the respective targeted maximum
  • Annealing temperature is, with further heating the respective maximum annealing temperature of 750 - 870 ° C.
  • the annealing time within which the flat steel product in the holding stage is kept at the maximum annealing temperature, is 8 - 260 s. At too low a temperature or too little time, the material would not recrystallize. As a result, not enough austenite for martensite formation would be available for the structural transformation during cooling. On the other hand unrecrystallized steel would result in a pronounced anisotropy. On the other hand, 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 is carried out at a cooling rate of 0.5-110 K / s
  • Heat treatment are dip-coated, it is cooled in the course of cooling to a temperature of 455 - 550 ° C.
  • the thus tempered cold-rolled steel flat product then passes through a Zn melt bath, which has a temperature of 450 - 480 ° C. If the
  • the steel flat product is cooled to a temperature of up to 10 K / s until it enters the zinc bath until its temperature is within that of the zinc bath
  • Zinc bath temperature is.
  • the thickness of the Zn-based protective layer present on the flat steel product 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.
  • flat steel products according to the invention comprise 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 over a
  • Holding time of 8 - 24 s at a temperature of 760 - 860 ° C is maintained.
  • further heating occurs at a heating rate of 0.2 - 15 K / s.
  • the thus 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
  • Zinc melt bath is passed through and held for a maximum holding time of 45 s.
  • the zinc melt bath has a temperature of 455-465 ° C. Depending on its inlet temperature, the cold strip cools
  • Zinc melt bath with 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.
  • Zinc coating provided cold strip is set in a conventional manner, the coating thickness.
  • the cold-rolled steel flat product is in one
  • Heating rate of up to 25 K / s brought to a target temperature 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 holding zone of the furnace over 35-150 s, 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.
  • Holding zone with a heating rate of up to 3 K / s heated to the respective annealing temperature.
  • Steel flat product is first cooled slowly at a cooling rate of 0.5 - 10 K / s to an intermediate temperature which is 640 - 730 ° C, and with a cooling rate of 5 - 110 K / s accelerated to a temperature of 455 - 550 ° C. is cooled.
  • the zinc melt bath has a temperature of 450-480 ° C. At the from the
  • Zinc coating provided cold-rolled Flat steel product is set in a conventional manner, the coating thickness.
  • 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.
  • Treatment is carried out, after Galvannealing- treatment, the zinc-coated cold-rolled a
  • Temper rolling are subjected to its mechanical properties and the surface finish of the
  • Dressing grades are typically in the range of
  • Hot dip coating also undergo a heat treatment in a conventional annealing furnace, in which the heating (step el)) and the annealing at the respective annealing temperature (step e.2) are completed in the manner described above, but in which the step e.3) at least is carried out in two stages by the cold rolled
  • Temperature range lingers up to 760 s to one
  • 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 thus annealed cold-rolled steel flat product is then subjected to a two-stage cooling in which it is first cooled at a cooling rate of 3 - 30 K / s accelerated to an intermediate temperature of 450 - 570 ° C.
  • This cooling can be carried out as air and / or gas cooling. This is followed by one slower cooling at which the cold rolled
  • At the respective cooling can be a
  • cold-rolled steel flat product over a holding time of 150 - 760 s at a temperature of 250 - 500 ° C, in particular 250 - 330 ° C, is maintained.
  • cooling of the cold-rolled steel flat product occurs at a cooling rate of up to 1.5 K / s.
  • Heat-treated cold-rolled flat steel product may finally be subjected to temper rolling in order 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%.
  • Cold-rolled flat rolled steel can subsequently be coated with a coating machine
  • An inventive flat steel product has a composite in the manner explained above
  • alloy according to the invention is also characterized by a structure containing 60-90 vol% of ferrite including bainitic ferrite, 10 to 40% by volume of martensite, up to 5% by volume of retained austenite and up to 5 vol -% due to manufacturing unavoidable
  • R p0 , 2 is at least 440 MPa, in particular up to 550 MPa, R m is at least 780 MPa, in particular up to 900 MPa,
  • nio-20 / Ag at least 0.10
  • BH2 at least 25 MPa, in particular at least 30 MPa.
  • Hot dip coating passes through: Preheating to a preheating temperature TV by means of a heating rate RV;
  • the temperature TE optionally holding at the temperature TE for a duration tH when the respective temperature TE falls within the temperature range provided for the temperature TB of the melt bath, in particular equal to the temperature TB, (FIG. 1) or further cooling proceeding from the temperature TE ' to a temperature TE "when the temperature TE 'is greater than the upper limit of the temperature range envisaged for the molten bath, the temperature TE" reached in the second cooling step being equal to the temperature TB of the molten bath Temperature range falls, in particular equal to the
  • 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.
  • hot rolled steel strips were cooled to a reeling temperature HT at which they were then wound into a coil.
  • the resulting hot-rolled steel strips are KWG with a respective overall degree of deformation cold rolled steel strip with a thickness KBD cold rolled.
  • the steel strips are in a holding zone, first with a
  • Heating rate RF has been finished to a maximum annealing temperature TG on which they have subsequently been held.
  • an 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 Hot melt steel strips exhibited a Zn alloy coating that protects them from corrosion.
  • Preheating temperature TV has been heated. Immediately after preheating, the steel strips have run into a second zone of the respective furnace.
  • the steel strips were finished with a heating rate RF to the required maximum annealing temperature TG finished.
  • the cold-rolled steel strips were then cooled in two stages. In the first stage of cooling are the
  • RV heating rate preheating temperature TV, heating rate RF, annealing temperature TG, annealing time tG, cooling rate RE ', intermediate temperature TE', cooling rate RE '
  • Preheating temperature TV has been heated. Immediately after preheating, the steel strips have run into a second zone of the respective furnace.
  • Annealing temperature TG heated steel strips were then kept at this temperature. The Finished heating and holding also took place during a total annealing period.
  • the cold-rolled steel strips were then cooled in two stages.
  • RV heating rate preheating temperature TV, heating rate RG, annealing temperature TG, annealing time tG, cooling rate RZ ', intermediate temperature TZ', cooling rate RZ
  • 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 ,
  • the behavior in V-bend has been determined according to DIN EN ISO 7438.
  • the sheet thickness should be here 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 a total of 32 in the

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  • Chemical & Material Sciences (AREA)
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  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
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  • Coating With Molten Metal (AREA)

Abstract

L'invention concerne un acier et un produit en acier plat fabriqué à partir de ce dernier, lesquels présentent des propriétés mécaniques optimisées et peuvent être obtenus de manière économique sans nécessiter d'éléments d'alliage onéreux dont les coûts d'achat sont soumis à d'importantes variations. L'acier et le produit en acier plat selon l'invention présentent 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 du Fe et des impuretés inévitables résultant du processus de fabrication et comprenant des teneurs en phosphore, en soufre, en azote ou en molybdène qui remplissent les conditions suivantes en ce qui concerne chacune de leurs teneurs : P : < 0,02 %, S : < 0,003 %, N : < 0,008 %, Mo : < 0,1 %. En outre, l'invention concerne un procédé de fabrication d'un produit en acier plat composé d'un acier selon l'invention.
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)

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WO2013182621A1 (fr) 2013-12-12
KR102073441B1 (ko) 2020-02-04
JP2015525292A (ja) 2015-09-03
EP2855717A1 (fr) 2015-04-08
KR20150028267A (ko) 2015-03-13
US9976205B2 (en) 2018-05-22
JP6310452B2 (ja) 2018-04-11
EP2855718B1 (fr) 2019-05-15
WO2013182622A1 (fr) 2013-12-12
EP2855717B1 (fr) 2020-01-22
CN104583424A (zh) 2015-04-29
KR20150023566A (ko) 2015-03-05
KR102073442B1 (ko) 2020-02-04
JP6374864B2 (ja) 2018-08-15
CN104520448B (zh) 2017-08-11
CN104583424B (zh) 2017-03-08
US20150122377A1 (en) 2015-05-07
US20150152533A1 (en) 2015-06-04
CN104520448A (zh) 2015-04-15
JP2015525293A (ja) 2015-09-03

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