EP4200450A1 - Procédé de fabrication d'un produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium, et produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium - Google Patents

Procédé de fabrication d'un produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium, et produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium

Info

Publication number
EP4200450A1
EP4200450A1 EP21765866.5A EP21765866A EP4200450A1 EP 4200450 A1 EP4200450 A1 EP 4200450A1 EP 21765866 A EP21765866 A EP 21765866A EP 4200450 A1 EP4200450 A1 EP 4200450A1
Authority
EP
European Patent Office
Prior art keywords
steel
weight
silicon
corrosion coating
alloyed
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.)
Pending
Application number
EP21765866.5A
Other languages
German (de)
English (en)
Inventor
Janko Banik
Dirk Rosenstock
Axel Ralf SCHROOTEN
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 EP4200450A1 publication Critical patent/EP4200450A1/fr
Pending legal-status Critical Current

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Classifications

    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/42—Induction heating
    • 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
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface 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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0457—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 with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • C21D8/0478—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 involving a particular surface 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • 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
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • 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
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • 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
    • 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
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the invention relates to a method for producing a flat steel product with a pre-alloyed anti-corrosion coating.
  • the invention also relates to a flat steel product with a pre-alloyed anti-corrosion coating.
  • the invention relates to a method for producing a steel component with a thoroughly alloyed anti-corrosion coating.
  • the invention relates to a steel component with an alloyed anti-corrosion coating.
  • flat steel product includes all rolled products whose length is much greater than their thickness. This includes steel strips and sheets as well as blanks and blanks made from them.
  • Percentages of structural components and proportions of phases in the layer relate to the volume (% by volume) unless otherwise stated. However, the values are determined as an area percentage in the metallographic microsection.
  • a pre-alloyed anti-corrosion coating is a coating into which a certain amount of iron has diffused, but complete alloying has not yet been achieved.
  • a pre-alloyed anti-corrosion coating is therefore characterized in that the Fe content is between 30 and 45% by weight, preferably between 30 and 40% by weight, particularly preferably between 35 and 40% by weight.
  • the Fe content in the thoroughly alloyed anti-corrosion coating is significantly higher and is at least 45% by weight, in particular at least 50% by weight, preferably 50% by weight to 70% by weight.
  • the anti-corrosion coating optionally comprises different layers and phases. The Fe content of the anti-corrosion coating is then averaged over the various layers and phases.
  • the steel substrate of flat steel products according to the invention consists in particular of so-called "MnB steel". Steels of this type are standardized in EN 10083-3. These steels have good hardenability and allow safe process control during hot pressing, which makes it possible to effect martensite hardening in the tool without additional cooling in an economical manner during hot forming.
  • Typical steels suitable for hot press hardening are steels A-E, the chemical composition of which is listed in Table 2.
  • the steel substrate can also be designed as a composite material with, for example, three steel layers, of which at least one layer can be tempered, in particular hardened, cf. EP 2 886 332 Bl.
  • EP 0 971 044 B1 specifies an alloy specification according to which an MnB steel, in addition to iron and unavoidable impurities (in wt.
  • a manganese content of more than 0.5% but less than 3% A silicon content of more than 0.1% but less than 0 .5%, a chromium content of more than 0.01% but less than 1%, a titanium content of less than 0.2%, an aluminum content of less than 0.1%, a phosphorus content of less than 0.1%, should have a sulfur content of less than 0.05% and a boron content of more than 0.0005% but less than 0.08%.
  • the aluminium-based anti-corrosion coating is a so-called AlSi coating which contains 3 - 15% by weight Si and up to 3.5% by weight iron.
  • the anti-corrosion coating preferably contains 9-10% by weight Si and 2-3.5% by weight iron. The percentages relate to the anti-corrosion coating before the heat treatment.
  • the corrosion coating contains only aluminum and unavoidable impurities in addition to the alloying elements Si and Fe mentioned. So the rest is aluminum and unavoidable impurities.
  • the flat steel products produced and coated in this way are heated to a heating temperature above the Acl temperature, then placed in a compression molding tool, where they are hot-formed into the steel component and directly connected to the ten of the compression mold cools so quickly that a hardened structure is created in the steel substrate of the steel flat product.
  • Fe diffuses from the steel substrate into the Al coating. So Fe is alloyed in, causing the coating to harden.
  • DE 10 2008 006 771 B3 therefore proposes a two-stage process in which the coated steel substrate is subjected to a first heating step and a second heating step.
  • the first heating step the aluminum-based coating is pre-alloyed.
  • the steel flat products can then be transported from the steel producer to the processor.
  • the processor then carries out the second heating step with hot press form hardening. By dividing the process into two, the processing time for the second heating step can be significantly reduced by the processor.
  • the first heating step lasts one hour or more and takes place at temperatures of 550-723 °C.
  • DE 10 2014 112 448 B4 also proposes a method which, however, aims to completely alloy a hardenable sheet steel with an aluminum-silicon coating.
  • the alloying process is carried out until the coating is saturated with iron from the steel, which means that there is only a small process window for heating later, as this creates thick layers that have a negative effect on the weldability of the hardened sheet steel component.
  • the object of the present invention is to further develop the aforementioned methods in such a way that the entire process time can be shortened and at the same time a flat steel product with improved properties is produced.
  • This object is achieved by a method for producing a flat steel product with a pre-alloyed anti-corrosion coating comprising at least the following steps:
  • This process window has several advantages.
  • the relatively short residence time in the furnace, combined with the high furnace temperatures, means that the anti-corrosion coating is reliably pre-alloyed, while at the same time the mechanical and technological parameters of the steel product are not impaired and the basic structure of the steel substrate is preserved in its components.
  • the heating rate is measured close to the surface, for example with a thermocouple close to the surface, since the temperature of the layer or the temperature of the contact area between layer and substrate is relevant for the underlying processes and not the core temperature of the steel substrate.
  • the steel substrate is typically a steel with a ferritic-pearlitic structure, preferably a manganese-boron steel with a ferritic-pearlitic structure, particularly preferably a manganese-boron steel with a ferritic-pearlitic structure, which by heat treatment in the form of a thermal Hardening treatment can be converted into a martensitic structure.
  • the steel material consists of a hardenable steel material.
  • the steel material preferably has the following chemical composition in % by weight:
  • N up to 0.1% by weight, and optionally one or more alloying elements from the group (Al, Ti, V, Nb, B, Cr, Mo, Cu, Ni, Ca):
  • the steel substrate is particularly preferably a steel from the group of steels AE, the chemical analysis of which is given in Table 2.
  • Table 2 is to be understood in such a way that for each Steel from the group of steels AE the element proportions are given in percent by weight. A minimum and a maximum weight percentage is given here. For example, steel A therefore has a carbon content C: 0.05% by weight-0.10% by weight. If the lower bound is 0, the element is considered optional. No entry in the table means that there is no restriction for the item. For the elements chromium and molybdenum, steels C-E only have an upper limit for the sum of the element contents of chromium and molybdenum.
  • the steels AE can contain other optional elements, eg Cu, N, Ni, V, Sn, Ca. The remainder consists of iron.
  • the aluminum-based anti-corrosion coating is preferably a so-called AISi coating containing 0.5-15% by weight Si, optionally up to 5% by weight iron, optionally up to 5% by weight alkali or alkaline earth metals , preferably up to 1.0 wt .-% alkali or alkaline earth metals, and optionally up to 15 wt .-% Zn, preferably up to 10 wt .-% Zn and optional other components, the total content of which is at most 2.0 Wt .-% are limited, and the balance contains aluminum.
  • AISi coating containing 0.5-15% by weight Si, optionally up to 5% by weight iron, optionally up to 5% by weight alkali or alkaline earth metals , preferably up to 1.0 wt .-% alkali or alkaline earth metals, and optionally up to 15 wt .-% Zn, preferably up to 10 wt .-% Zn and optional other components, the total content of which
  • the optional content of alkali metals or alkaline earth metals in the melt can include, in particular, at least 0.0015% by weight of Ca, in particular at least 0.01% by weight of Ca.
  • the aluminium-based anti-corrosion coating is preferably a so-called AISi coating containing 0.5-15% by weight Si, optionally up to 5% by weight iron, optionally up to 5% by weight magnesium, the remainder being aluminium contains.
  • the anti-corrosion coating preferably contains 3-15% by weight Si, in particular 5-11% by weight Si, in particular 7-10% by weight Si and 2-3.5% by weight iron.
  • the magnesium content is preferably 0.05 to 1% by weight, in particular 0.1 to 0.5% by weight.
  • the division of the first heat treatment into a first sub-step, in which the steel flat product is heated and a second sub-step, in which the steel flat product is kept at a temperature above Ac3, has the advantage that accidental overheating of the anti-corrosion coating can be avoided. Overheating can lead to reduced spot weldability and paint adhesion of the hot press form hardened steel component. Therefore the coated flat steel product is preferably kept at a temperature between Ac3 and 950° C. in the second partial step.
  • the use of a two-stage process with the first heat treatment described and a second heat treatment during the actual hot press form hardening has the advantage that in the second step, which is carried out by the processor of the flat steel product, a flat steel product with a pre-alloyed anti-corrosion coating is already present.
  • the heat treatment is carried out by the processor of the steel flat product in a roller hearth furnace.
  • Untreated, aluminium-based coatings have the disadvantage that they assume a semi-liquid state during the heat treatment and lead to deposits on the furnace rollers. This in turn leads to unstable heating processes, increased rejects due to incorrect positioning of the heated flat steel products and increased maintenance costs due to defective furnace rollers.
  • the heating rate of more than 10 K/s in the temperature range from 500°C to 700°C also has the advantage that a silicon-poor phase and a silicon-rich phase form in the anti-corrosion coating.
  • the silicon-rich phase is distributed in islands in the silicon-poor phase.
  • the heating rate of more than 10 K/s results in an even distribution of the island-shaped, silicon-rich phase in the silicon-poor phase. This ensures that the hot-press form-hardened steel component has evenly distributed silicon-rich areas within a silicon-poor phase even in the region of the corrosion protection coating near the surface. This results in improved spot weldability of the steel component.
  • the roughness of the pre-alloyed steel flat product reliably results with an average roughness value R a in the range from 0.3 ⁇ m to 2.0 ⁇ m, preferably from 0.5 ⁇ m to 1.6 ⁇ m. This ensures that the hot-press form-hardened steel component also has a sufficiently large roughness to achieve good paint adhesion.
  • R a average roughness value
  • island-shaped is understood to mean an arrangement in which discrete unconnected areas are surrounded by another material—that is, “islands” of a specific material are located in another material.
  • a low-silicon phase is understood to mean a phase whose silicon content is 1-10% by weight, preferably 1-6% by weight.
  • a silicon-rich phase is understood to mean a phase whose silicon content is greater than 10% by weight, preferably 10-15%.
  • the heating rate in the temperature range from 500°C to 700°C is less than 20 K/s. This results in a stable process window, so that the desired flat steel product is reliably obtained even with a slight variation in the residence time.
  • the anti-corrosion coating is arranged on both sides of the steel substrate and has a coating weight r between 50 ⁇ and 200 ⁇ on both sides. The following then preferably applies to the residence time t v : whereby
  • a coating weight on both sides is the sum of the coating weights on both coated sides.
  • the numerical value is not the coating weight per coated side, but the sum of the two coating weights on each side.
  • the thickness of the flat steel product is in particular 0.5-3.5 mm, preferably 0.8-2.8 mm.
  • the flat steel product provided with the anti-corrosion coating pre-alloyed according to the invention can then be cooled to room temperature and stored until it is sent for further processing into the respective steel component. This is usually done by cooling in ambient air.
  • the cooling rate is preferably less than 5 K/s, in particular less than 3.5 K/s, between the oven temperature and 200°C. Since the anti-corrosion coating is only incompletely alloyed in the first heating stage described (ie less than 5% Fe content in the area adjacent to the surface with a thickness of 1.0 ⁇ m, i.e.
  • the anti-corrosion coating has a low susceptibility to corrosion even after the first heating stage, so that its storage, its transport and the other work steps carried out in the run-up to the second heating stage can be carried out without any additional measures being necessary.
  • the pre-alloyed anti-corrosion coating retains properties which, even after the first heating stage, still allow the flat steel products obtained to be divided or trimmed with simple cutting operations, without causing any lasting damage to the coating layer.
  • the invention further relates to a flat steel product with a pre-alloyed anti-corrosion coating, comprising a steel substrate with a pre-alloyed, aluminum-based anti-corrosion coating present at least on one side of the steel substrate.
  • the martensite content of the steel substrate is preferably less than 10% by volume, preferably less than 5% by volume, and the average Fe content of the anti-corrosion coating is 30-45% by weight.
  • the anti-corrosion coating comprises: a low-silicon phase which, in addition to unavoidable impurities, contains 1-10% by weight Si, 10-50% by weight Fe, up to 1% by weight Mn and 40-80% by weight aluminum, the sum of the ingredients present being 100% by weight, and - A silicon-rich phase which, in addition to unavoidable impurities, contains 10-15% by weight Si, 25-50% by weight Fe, up to 1% by weight Mn and 40-80% by weight aluminum, the sum of present components is 100% by weight and wherein the silicon-rich phase is distributed in islands in the silicon-poor phase.
  • Such a flat steel product with a pre-alloyed anti-corrosion coating can be produced, for example, using the method described above and has the advantages described above.
  • the mean roughness value R a of the pre-alloyed flat steel product is in the range from 0.3 ⁇ m to 2.0 ⁇ m, preferably from 0.5 ⁇ m to 1.6 ⁇ m. This ensures that the hot-press form-hardened steel component also has a sufficiently large roughness to achieve good paint adhesion.
  • the thickness of the flat steel product is in particular 0.5-3.5 mm, preferably 0.8-2.8 mm.
  • the island-shaped distribution of the silicon-rich phase in the silicon-poor phase is in particular such that the silicon-rich phase has discrete discontinuous regions which are surrounded by the silicon-poor phase.
  • Discrete, non-connected areas in the micrograph with a surface area of less than 100 ⁇ m 2 make up more than 80% of the entire silicon-rich phase.
  • discrete discontinuous regions with an area of less than 50 ⁇ m 2 account for more than 50% of the total silicon-rich phase.
  • more than 80% of the silicon-rich phase is in the form of small "islands” with an area of less than lOOpm 2 and preferably more than 50% of the silicon-rich phase is in the form of small "islands” with an area of less than 50pm 2am .
  • the insular distribution of the silicon-rich phase in the silicon-poor phase is such that the regions with silicon-rich phase are distributed over an area having at least a thickness perpendicular to the surface that is greater than 50% of the thickness of the anti-corrosion coating.
  • a single narrow strip with areas of silicon-rich phases does not form, but the silicon-rich areas are distributed in islands over a strip that takes up at least half of the corrosion protection coating.
  • the anti-corrosion coating in particular the region of the anti-corrosion coating near the surface, has between 10% by volume and 25% by volume of the silicon-rich phase.
  • hot-press form-hardened steel component has evenly distributed silicon-rich areas within a silicon-poor phase in the near-surface area of the corrosion protection coating. This results in improved spot weldability of the steel component.
  • the proportion of the silicon-rich phase in the pre-alloyed anti-corrosion coating is greater than 5% by volume, preferably greater than 10% by volume.
  • the Fe content of the anti-corrosion coating is more than 10% by weight Fe at every point. This has the advantage that the melting point at each point is set sufficiently high to prevent parts of the anti-corrosion coating from being liquefied during the subsequent hot press form hardening.
  • the flat steel product comprises a diffusion layer comprising Fe3Al and Fe2Al5 with a thickness between 1 pm and 6 pm, which is arranged adjacent to the steel substrate.
  • the diffusion layer is therefore directly adjacent to the steel substrate and contacts the steel substrate.
  • the diffusion layer is also often referred to as a ferrite fringe.
  • Such a diffusion layer improves the cutting behavior when cutting the flat steel product with a pre-alloyed anti-corrosion coating due to the smooth transition between the hard coating and the (comparatively) softer substrate.
  • the steel flat product comprises a layer of the silicon-rich phase with a thickness between 1 pm and 3 pm, which is arranged adjacent to the diffusion layer.
  • the layer of the silicon-rich phase is therefore directly adjacent to the diffusion layer and makes contact with the diffusion layer.
  • the silicon-rich phase layer has the same chemical composition as the island-like distributed silicon-rich phase regions.
  • the silicon-rich phase layer grows as does the diffusion layer during the master alloying process.
  • a further developed variant of the steel flat product with a pre-alloyed anti-corrosion coating comprises an oxide layer on the surface of the anti-corrosion coating.
  • the oxide layer is formed spontaneously through a reaction with atmospheric oxygen and essentially comprises aluminum oxide Al2O3 or, in the variant with magnesium, in the anti-corrosion coating MgO and Al2O3.
  • the proportion of MgO in the oxide layer is 55 to 65% and the proportion of aluminum oxide is about 35 to 45%.
  • the thickness of the oxide layer is typically 20 nm to 300 nm, preferably 50 nm to 200 nm, and additionally protects the flat steel product from corrosion.
  • the invention further relates to a method for producing a steel component with a thoroughly alloyed anti-corrosion coating, comprising at least the following steps:
  • the process of heating the flat steel product for a heating period t E includes increasing the temperature to the forming temperature Tu in the stated temperature range and holding the flat steel product at this forming temperature Tu.
  • Heating can be carried out using a short roller hearth furnace, chamber furnace or rapid heating (conductive, inductive or contact heating).
  • the steel flat product with a pre-alloyed anti-corrosion coating By using the steel flat product with a pre-alloyed anti-corrosion coating, it is sufficient to carry out the subsequent heating in the short heating time described. No additional time needs to be set aside to allow the anti-corrosion coating to fully alloy. It is therefore sometimes even possible to synchronize the process steps following the heating, such as transfer to the press, forming, press hardening, possibly cutting, transfer to storage, with the duration of the heating, so that there is no or minimal time delay. Furthermore, the use of the steel flat product with a pre-alloyed anti-corrosion coating has the advantage that the heating can be carried out in a roller hearth furnace without having to worry about deposits on the furnace rollers.
  • the melting point of the anti-corrosion coating has increased, so that liquefaction no longer occurs during the subsequent heating process for hot press form hardening. Consequently, deposition on kiln rollers is also avoided.
  • the thickness of the flat steel product is in particular 0.5-3.5 mm, preferably 0.8-2.8 mm.
  • the lower limit for the heating duration ensures that the already existing or newly forming diffusion layer adjoining the steel substrate has a thickness of at least 1 pm.
  • a diffusion layer thickness greater than lpm is a good indicator that the alloying penetration has reached a sufficient level.
  • the method described for producing a steel component with a thoroughly alloyed anti-corrosion coating also includes the step:
  • the steel flat product is not only formed into the steel component, but is also quenched to the target temperature at the same time.
  • the cooling rate in the forming tool to the target temperature is in particular at least 20 K/s, preferably at least 30 K/s, in particular at least 50 K/s, particularly preferably at least 100 K/s.
  • the target temperature is below 400°C, preferably below 300°C.
  • the target temperature is preferably at least 50°C. This achieves a martensite content in the substrate of more than 50% by volume, preferably more than 80% by volume, in particular more than 90% by volume, in particular more than 95% by volume.
  • the steel component After the steel component has been removed from the forming tool, the steel component is cooled to a cooling temperature T of less than 50° C. within a cooling period of 0.5 to 600 s. This is usually done by air cooling.
  • the invention further relates to a steel component with a fully alloyed anti-corrosion coating comprising a steel substrate with a fully alloyed, aluminium-based anti-corrosion coating present on at least one side of the steel substrate.
  • a steel component can in particular be produced according to the method described above.
  • the fully alloyed anti-corrosion coating includes:
  • - % aluminum contains,
  • a silicon-rich phase (R) which, in addition to unavoidable impurities, contains 10-15% by weight Si, 40-70% by weight Fe, up to 1% by weight Mn and 40-80% by weight aluminum, wherein the silicon-rich phase is distributed in islands in the silicon-poor phase
  • the Fe content in the thoroughly alloyed anti-corrosion coating is at least 45% by weight, in particular at least 50% by weight, preferably 50% by weight to 70% by weight.
  • the insular distribution of the silicon-rich phase in the silicon-poor phase is such that the anti-corrosion coating, in particular the region of the anti-corrosion coating near the surface, has between 10% by volume and 25% by volume of the silicon-rich phase.
  • the silicon-rich islands ensure good spot weldability.
  • they increase the roughness of the steel component, resulting in an average roughness value R a greater than lpm.
  • the mean roughness value is preferably greater than 1.2 pm, particularly preferably greater than 1.5 pm. This ensures good paint adhesion.
  • the martensite content in the steel substrate is more than 50% by volume, preferably more than 80% by volume, in particular more than 90% by volume, in particular more than 95% by volume.
  • the anti-corrosion coating optionally comprises up to 5% by weight of magnesium, preferably 0.05 to 1% by weight, in particular 0.1 to 0.5% by weight of magnesium.
  • the magnesium content of the anti-corrosion coating is 0.1 to 0.5% by weight of magnesium.
  • areas of the silicon-poor phase and the silicon-rich phase that are at a distance from the surface of the anti-corrosion coating that is greater than 1.0 ⁇ m each have a magnesium content of up to 0.5% by weight. Since magnesium accumulates in the surface area during forming, the proportion of magnesium in the two phases close to the surface can be above 0.5% by weight. However, in the deeper phases described, the magnesium content is a maximum of 0.5% by weight.
  • a further developed variant of the steel component with an alloyed anti-corrosion coating includes an oxide layer on the surface of the anti-corrosion coating.
  • the oxide layer is formed spontaneously by reaction with atmospheric oxygen and essentially comprises aluminum oxide Al2O3 or, in the variant with magnesium in the anti-corrosion coating, MgO and Al2O3.
  • MgO and Al2O3 aluminum oxide
  • the proportion of MgO in the oxide layer is 55 to 65% and the proportion of aluminum oxide is about 35 to 45%.
  • the thickness of the oxide layer is typically 20 nm to 300 nm, preferably 50 nm to 200 nm, and additionally protects the steel component from corrosion.
  • the near-surface area of the (pre-alloyed or thoroughly alloyed) anti-corrosion coating is understood to mean the area down to a depth of 200 nm below the surface of the anti-corrosion coating.
  • the surface of the anti-corrosion coating is understood to mean the contact area with the ambient atmosphere or with the oxide layer.
  • the proportion of the silicon-rich phase in the fully alloyed anti-corrosion coating is less than 20% by volume, preferably less than 15% by volume.
  • the insular distribution of the silicon-rich phase in the silicon-poor phase is, in the case of the steel component with a thoroughly alloyed anti-corrosion coating, in particular such that the silicon-rich phase has discrete, non-connected areas which are surrounded by the silicon-poor phase.
  • Discrete, non-connected areas with a surface area of less than 100 ⁇ m 2 make up more than 80% of the entire silicon-rich phase.
  • discrete discontinuous regions with an area of less than 50 ⁇ m 2 account for more than 50% of the total silicon-rich phase.
  • more than 80% of the silicon-rich phase is in the form of small "islands” with an area of less than 100 pm 2 and preferably more than 50% of the silicon-rich phase is in the form of small "islands” with an area of less than 50pm 2am .
  • the steel component comprises a diffusion layer, in particular comprising Fe3Al and Fe2Al5, with a thickness between 1 pm and 20 pm, which is arranged adjacent to the steel substrate.
  • the diffusion layer is therefore directly adjacent to the steel substrate and contacts the steel substrate.
  • the thickness of the diffusion layer is at least 3 ⁇ m. In particular, the thickness is no more than 16 pm, particularly preferably no more than 12 pm.
  • the thickness of the diffusion layer is a good indicator of the degree of alloying. It has been shown that the desired alloying penetration is achieved in the specified thickness ranges.
  • the proportion of pores in the anti-corrosion coating is less than 5% by volume.
  • the proportion of pores based on the anti-corrosion coating and the diffusion layer is less than 5% by volume.
  • the proportion of pores is determined by measuring the surface area in the micrograph.
  • the steel component comprises a layer of the silicon-rich phase with a thickness between 1 pm and 3 pm, which is arranged adjacent to the diffusion layer. The layer of the silicon-rich phase is therefore directly adjacent to the diffusion layer on the side facing away from the substrate and makes contact with the diffusion layer. On the other side, the diffusion layer contacts the anti-corrosion coating.
  • the silicon-rich phase layer has the same chemical composition as the island-like distributed silicon-rich phase regions.
  • FIG. 1a shows a cross section of a flat steel product with a pre-alloyed anti-corrosion coating in a first variant
  • FIG. 2a shows a cross section of a steel flat product with a pre-alloyed anti-corrosion coating in a second variant
  • FIG. 2b shows a cross section of a steel component with a fully alloyed anti-corrosion coating in a second embodiment variant
  • 3a shows a cross section of a flat steel product with a pre-alloyed anti-corrosion coating in a third variant
  • 3b shows a cross section of a steel component with a fully alloyed anti-corrosion coating in a third embodiment variant
  • 4a shows a cross section of a flat steel product with a pre-alloyed anti-corrosion coating in a fourth variant
  • 4b shows a cross section of a steel component with a fully alloyed anti-corrosion coating in a fourth variant.
  • Shaped blanks were cut from a 1.8 mm thick strip of steel grade D according to Table 2 with a 25 ⁇ m thick aluminum-based anti-corrosion coating on both sides. Both a punching tool and a laser were used as cutting methods.
  • the initial composition of the protective coating was 8 wt% Si, 3 wt% Fe, 0.3 wt% Mg, balance Al.
  • the run weight was 70 ⁇ on each side. In a 2-zone continuous furnace, these blanks were first heated in the first zone at a furnace temperature of 1100°C to over 900°C in 105 seconds. The heating rate between 500°C and 700°C was 12 K/s.
  • the blank was then held at 920°C for 35 seconds, which is above the Ac3 temperature, which is around 860°C for the selected steel grade. During this time, the anti-corrosion coating was pre-alloyed. The Fe content in the anti-corrosion coating was then between 35% by weight and 40% by weight. In addition, the Fe content of the anti-corrosion coating was more than 10% by weight Fe at each point.
  • the mean roughness value R a is 0.9 pm in this variant.
  • the cross section of the flat steel product 9 produced in this way is shown in FIG.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the regions with a silicon-rich phase 15 are distributed over an area which has a thickness perpendicular to the surface which corresponds to approximately 80% of the thickness of the anti-corrosion coating 13 .
  • a single, narrow strip with areas of silicon-rich phases 15 does not form, but the silicon-rich areas are distributed in islands over a strip that occupies about 80% of the anti-corrosion coating. This ensures that the proportion of the silicon-rich phase 15 in the anti-corrosion coating in the hot-press-formed steel component is between 10% by volume and 25% by volume.
  • the flat steel product includes a diffusion layer 19 comprising Fe3Al and Fe2Al5 with a thickness of 3 ⁇ m, which is arranged adjacent to the steel substrate 11 .
  • the diffusion layer 19 is therefore bordering directly to the steel substrate 11 and contacts the steel substrate 11.
  • the anti-corrosion coating 13 comprises a layer 21 of the silicon-rich phase 15 with a thickness of 1 pm, which is arranged adjacent to the diffusion layer 19.
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the flat steel product also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 60 nm, which is not visible due to the resolution in FIG.
  • the shaped blanks treated in this way were further processed elsewhere on a hot forming line. Further processing took place in a short hot forming furnace at a forming temperature of 920°C. A heating period of 150 seconds, during which the treated blanks were brought to the forming temperature and held there, was sufficient for complete austenitization and thorough alloying of the coating. The furnace rollers of the hot-forming furnace showed no Al contamination even after throughput of several 500 blanks.
  • the anti-corrosion coating contained an average of 51% by weight Fe and had silicon-rich areas with Si contents between 10% and 14%.
  • the anti-corrosion coating does not show a clear stratification of the silicon-rich and silicon-poor areas. Instead, the silicon-rich phase is distributed in islands in the silicon-poor phase. As a result, both silicon-poor and silicon-rich phases are also present in the near-surface area. Both the joining properties and the paint adhesion properties were therefore better than with commercially available aluminium-based anti-corrosion coatings, in which a layer with a continuous low-silicon layer is formed in the area close to the surface.
  • the cross section of the steel component 23 produced in this way is shown in FIG.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the area close to the surface has approximately 18% by volume of the silicon-rich phase 15 .
  • the anti-corrosion coating 13 and the diffusion layer 19 together have a porosity of 1.1%.
  • the proportion of the silicon-rich phase in Anti-corrosion coating is 14% by volume.
  • About 85% of the silicon-rich phase is in the form of small "islands" with an area of less than 100 pm 2 .
  • the steel component 23 also includes a diffusion layer 19 with Fe3Al and Fe2Al5, which is arranged adjacent to the steel substrate 11 below the anti-corrosion coating 13.
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11.
  • the diffusion layer has a thickness of 7 ⁇ m.
  • the steel component 23 includes a layer 21 of the silicon-rich phase 15 with a thickness of 2 ⁇ m, which is arranged adjacent to the diffusion layer 19 below the anti-corrosion coating 13 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the steel component also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 100 nm, which is not visible in FIG. 1b due to the resolution.
  • Shaped blanks were cut from a 1.5 mm thick strip of steel grade E according to Table 2 with a 20 ⁇ m thick aluminum-based anti-corrosion coating on both sides.
  • a laser was used as the cutting method.
  • the initial composition of the protective coating was 10 wt% Si, 3 wt% Fe, balance Al.
  • the run weight was 60 ⁇ on each side.
  • these molded blanks were initially heated in the first zone at a furnace temperature of 1050°C to over 900°C in 90 seconds.
  • the heating rate between 500°C and 700°C was 11 K/s.
  • This part of the furnace had an O 2 -containing atmosphere with a dew point TP of -10°.
  • the blank was then held at 920°C for 60 seconds, which is above the Ac3 temperature, which is around 845°C for the selected steel grade. This part of the oven did not have a dew point control.
  • FIG. 2a The cross section I iff picture Id of the steel flat product 9 produced in this way is shown in FIG. 2a.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17. The insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the regions with a silicon-rich phase 15 are distributed over an area which has a thickness perpendicular to the surface which corresponds to approximately 90% of the thickness of the anti-corrosion coating 13 .
  • a single, narrow strip with regions of silicon-rich phases 15 does not form, but rather the silicon-rich regions are distributed in islands over a strip that occupies about 90% of the anti-corrosion coating. This ensures that in the case of the hot-press formed steel component, the region of the anti-corrosion coating close to the surface has between 10% by volume and 25% by volume of the silicon-rich phase.
  • the flat steel product includes a diffusion layer comprising Fe3Al and Fe2Al5 with a thickness of 2 ⁇ m, which is arranged adjacent to the steel substrate 11 .
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the flat steel product also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 60 nm, which is not visible due to the resolution in FIG.
  • the shaped blanks treated in this way were further processed in a separate process step in an inductive rapid heating line.
  • the heating time to 900°C was 15 seconds.
  • the circuit boards were then kept at this temperature for a further 30 seconds at this temperature using infrared radiation. This resulted in complete austenitization of the base material and full alloying of the coating.
  • the heating time was 45 seconds.
  • the anti-corrosion coating contained an average of 56% by weight Fe and had silicon-rich areas with Si contents between 10% by weight and 13.5% by weight.
  • the anti-corrosion coating did not show a clear stratification of the silicon-rich and silicon-poor regions above the diffusion layer. Instead, the silicon-rich phase is distributed in islands in the silicon-poor phase. As a result, both silicon-poor and silicon-rich phases are present in the near-surface area.
  • the region of the anti-corrosion coating near the surface contained 18% by volume of the silicon-rich phase.
  • the anti-corrosion coating 13 and the diffusion layer 19 together have a porosity of 2.3%. Both the joining properties and the paint adhesion properties were therefore better than with commercially available aluminium-based anti-corrosion coatings, in which a layer with a continuous low-silicon layer forms in the area close to the surface.
  • the cross section of the steel component 23 produced in this way is shown in FIG. 2b. shown.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the area close to the surface has approximately 23% by volume of the silicon-rich phase 15 .
  • the proportion of the silicon-rich phase in the anti-corrosion coating is 11% by volume. More than 90% of the silicon-rich phase is in the form of small “islands” with an area of less than 100 pm 2 .
  • the steel component 23 also includes a diffusion layer 19 with Fe3Al and Fe2Al5, which is arranged adjacent to the steel substrate 11 below the anti-corrosion coating 13.
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11.
  • the diffusion layer has a thickness of 6 ⁇ m.
  • the steel component 23 comprises a layer 21 of the silicon-rich phase 15 with a thickness of 1 ⁇ m, which is arranged adjacent to the diffusion layer 19 below the anti-corrosion coating 13 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the steel component also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 110 ⁇ m, which is not visible due to the resolution in FIG. 2b.
  • Example 3
  • Shaped blanks were cut from a 1.2 mm thick strip of steel grade D according to Table 2 with a 20 ⁇ m thick aluminum-based anti-corrosion coating on both sides.
  • a laser was used as the cutting method.
  • the initial composition of the protective coating was 6 wt% Si, 3 wt% Fe, 0.3 wt% Mg, balance Al.
  • the run weight was 60 ⁇ on each side.
  • these molded blanks were first heated in the first zone at a furnace temperature of 1000°C to over 900°C in 90 seconds.
  • the heating rate between 500°C and 700°C was 13 K/s.
  • This part of the furnace had an O 2 -containing atmosphere with a dew point of -15°C.
  • the blank was then held at 920°C for 30 seconds, which is above the Ac3 temperature, which is around 860°C for the selected steel grade.
  • the anti-corrosion coating was pre-alloyed.
  • the Fe content in the anti-corrosion coating was then between 35% by weight and 40% by weight.
  • the Fe content of the anti-corrosion coating was more than 10% by weight Fe at each point.
  • the mean roughness value R a is 1.2 pm in this variant.
  • FIG. 3a The cross section I iffbi Id of the steel flat product 9 produced in this way is shown in FIG. 3a.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the regions with a silicon-rich phase 15 are distributed over an area which has a thickness perpendicular to the surface which corresponds to approximately 80% of the thickness of the anti-corrosion coating 13 .
  • a single, narrow strip with areas of silicon-rich phases 15 does not form, but rather the silicon-rich areas are distributed in islands over a strip that occupies about 80% of the anti-corrosion coating. In this way it is ensured that in the case of the hot-press-formed steel component of the anti-corrosion coating, in particular the region of the anti-corrosion coating near the surface, has between 10% by volume and 25% by volume
  • the flat steel product includes a diffusion layer comprising Fe3Al and Fe2Al5 with a thickness of 2.5 pm arranged adjacent to the steel substrate 11.
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the flat steel product also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 70 nm, which is not visible due to the resolution in FIG. 3a.
  • the shaped blanks treated in this way were further processed elsewhere in a contact heating line.
  • the heating time to the forming temperature of 900° was 20 seconds.
  • the circuit board was then kept at this temperature for a further 75 seconds via the infrared radiation of the contact plates, in that the plates took up a distance of approx. 5 mm from the surface of the circuit board. This resulted in complete austenitization of the steel substrate and thorough alloying of the anti-corrosion coating.
  • the heating time was therefore 95 seconds. Due to the pre-alloyed anti-corrosion coating, there was no adhesion to the contact plates. The layer thickness of the anti-corrosion coating also remained constant over the panel surface.
  • the anti-corrosion coating contained an average of 60% by weight Fe and had silicon-rich areas with Si contents between 11% and 15%.
  • the anti-corrosion coating did not show a clear stratification of the silicon-rich and silicon-poor regions above the diffusion layer. Instead, the silicon-rich phase is distributed in islands in the silicon-poor phase. As a result, both silicon-poor and silicon-rich phases are present in the near-surface area. Both the joining properties and the paint adhesion properties were therefore better than with commercially available aluminium-based anti-corrosion coatings, in which a layer with a continuous low-silicon layer is formed in the area close to the surface.
  • the cross section of the steel component 23 produced in this way is shown in FIG. 3b. shown.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular phase is clear Distribution of the silicon-rich phase 15 in the silicon-poor phase 17 to recognize.
  • the area close to the surface has approximately 15% by volume of the silicon-rich phase 15 .
  • the anti-corrosion coating 13 and the diffusion layer 19 together have a porosity of 1.3%.
  • the proportion of the silicon-rich phase in the anti-corrosion coating is approx. 13% by volume.
  • Over 90% of the silicon-rich phase is in the form of small “islands” with an area of less than 100 pm 2 .
  • the steel component 23 also includes a diffusion layer 19 with Fe3Al and Fe2Al5, which is arranged adjacent to the steel substrate 11 below the anti-corrosion coating 13.
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11.
  • the diffusion layer has a thickness of 9 ⁇ m.
  • the steel component 23 includes a layer 21 of the silicon-rich phase 15 with a thickness of 2 ⁇ m, which is arranged adjacent to the diffusion layer 19 below the anti-corrosion coating 13 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the steel component also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 220 nm, which is not visible due to the resolution in FIG. 3b.
  • Shaped blanks were cut from a 1.6 mm thick strip of steel grade D according to Table 2 with a 25 ⁇ m thick aluminum-based anti-corrosion coating on both sides.
  • a laser was used as the cutting method.
  • the initial composition of the protective coating was 8 wt% Si, 3 wt% Fe, 0.3 wt% Mg, balance Al.
  • the run weight was 75j ⁇ on each side.
  • the chemical composition was identical to example 3.
  • the cross section I iff picture Id of the steel flat product 9 produced in this way is shown in FIG. 4a.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the regions with a silicon-rich phase 15 are distributed over an area which has a thickness perpendicular to the surface which corresponds to approximately 80% of the thickness of the anti-corrosion coating 13 .
  • a single, narrow strip with areas of silicon-rich phases 15 does not form, but the silicon-rich areas are distributed in islands over a strip that occupies about 80% of the anti-corrosion coating. This ensures that in the case of the hot-press formed steel component, the region of the anti-corrosion coating close to the surface has between 10% by volume and 25% by volume of the silicon-rich phase.
  • the flat steel product includes a diffusion layer comprising Fe3Al and Fe2Al5 with a thickness of 3 ⁇ m, which is arranged adjacent to the steel substrate 11 .
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the flat steel product also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 110 ⁇ m, which is not visible due to the resolution in FIG. 4a.
  • the molded blanks treated in this way were further processed in a separate process step in a contact heating process using heat conduction.
  • the heating time to the forming temperature of 900° was 12 seconds.
  • the blank was then held at this temperature in a roller hearth oven for a further 110 seconds. There it came for complete austenitization of the steel substrate and for thorough alloying of the anti-corrosion coating.
  • the heating time was therefore 122 seconds. Due to the pre-alloyed anti-corrosion coating, there was no adhesion to the contact plates or furnace rollers. The layer thickness of the anti-corrosion coating also remained constant over the panel surface.
  • the anti-corrosion coating contained an average of 58% by weight Fe and had silicon-rich areas with Si contents between 11% and 16%.
  • the anti-corrosion coating did not show a clear stratification of the silicon-rich and silicon-poor regions above the diffusion layer. Instead, the silicon-rich phase is distributed in islands in the silicon-poor phase. As a result, both silicon-poor and silicon-rich phases are present in the near-surface area. Both the joining properties and the paint adhesion properties were therefore better than with commercially available aluminium-based anti-corrosion coatings, in which a layer with a continuous low-silicon layer is formed in the area close to the surface.
  • the cross section of the steel component 23 produced in this way is shown in FIG. 4b. shown.
  • An anti-corrosion coating 13 is arranged on a steel substrate 11 .
  • the anti-corrosion coating 13 comprises a silicon-rich phase 15 and a silicon-poor phase 17.
  • the insular distribution of the silicon-rich phase 15 in the silicon-poor phase 17 can be clearly seen.
  • the area close to the surface has approximately 17% by volume of the silicon-rich phase 15 .
  • the anti-corrosion coating 13 and the diffusion layer 19 together have a porosity of 1.2%.
  • the proportion of the silicon-rich phase in the anti-corrosion coating is 10.5% by volume.
  • Over 90% of the silicon-rich phase is in the form of small “islands” with an area of less than 100 pm 2 .
  • the steel component 23 also includes a diffusion layer 19 with Fe3Al and Fe2Al5, which is arranged adjacent to the steel substrate 11 below the anti-corrosion coating 13.
  • the diffusion layer 19 is therefore directly adjacent to the steel substrate 11 and makes contact with the steel substrate 11.
  • the diffusion layer has a thickness of 5 ⁇ m.
  • the steel component 23 comprises a layer 21 of the silicon-rich phase 15 with a thickness of 1 ⁇ m, which is arranged adjacent to the diffusion layer 19 below the anti-corrosion coating 13 .
  • the layer 21 of the silicon-rich phase 15 is therefore directly adjacent to the diffusion layer 19 and contacts the diffusion layer 19.
  • the steel component also includes an oxide layer on the surface of the anti-corrosion coating with a thickness of 170 nm, which is not visible due to the resolution in FIG. 4b.
  • the table below shows the process parameters for blanks of different thicknesses.
  • the steel grade of the steel substrate is also given in the table.
  • All molded blanks include a 25 ⁇ m thick aluminium-based anti-corrosion coating on both sides.
  • the initial composition of the protective coating was 9 wt% Si, 3 wt% Fe, balance AL.
  • the overlay weight was 70 ⁇ on each side.
  • the shaped blanks treated in this way were further processed elsewhere on a hot forming line. Further processing took place in a short hot forming furnace at a forming temperature of 900°C or 920°C. The thickness of the diffusion layer, weldability, paint adhesion and tool wear were then determined.
  • the weldability was determined as suitability for resistance spot welding according to SEP1220-2.
  • a stone impact test according to EN ISO 20567 was carried out to determine the paint adhesion.
  • the painted sample is bombarded with a defined amount of "corundum” and subjected to a VDA corrosion test.
  • the paint adhesion was also determined according to EN ISO 2409 (cross-cut test).
  • the painted sample is scratched in a defined cross pattern up to the metallic protective layer and also subjected to the VDA corrosion test.
  • the tool abrasion was determined by removing the powdery and adhering residues in the tool after a certain number of components had been produced and determining them gravimetrically.
  • Table 1 the mass of abrasion after 100 formed components is based on 1 square meter coated material specified. From 100 g abrasion per 1000 components (ie 10 g per 100 components) unscheduled cleaning actions could become necessary. Therefore, values below 10g / 100 components are considered acceptable.

Abstract

L'invention concerne un procédé de fabrication d'un produit plat en acier (9) présentant un revêtement préallié résistant à la corrosion (13), comprenant au moins les étapes suivantes consistant à : - fournir un produit plat en acier revêtu (9) comprenant un substrat en acier (11) comportant un revêtement résistant à la corrosion à base d'aluminium (13) sur au moins un côté du substrat en acier (11) ; - soumettre le produit plat en acier revêtu (9) à un traitement thermique impliquant les étapes partielles suivantes : i. chauffage du produit plat en acier revêtu (9) dans un four à une température de four T située dans la plage allant de 950 °C à 1 150 °C et à un temps de séjour de four t v situé dans la plage allant de 40 s à 150 s, la température du four étant choisie de sorte que la vitesse de chauffage du produit plat en acier revêtu (9) dans la plage de température de 500 °C à 700 °C soit supérieure à 10 K/s ; ii. maintient de produit plat en acier revêtu (9) à une température supérieure à Ac3 pendant un temps de maintien situé dans la plage allant de 20 s à 60 s.
EP21765866.5A 2020-08-19 2021-08-17 Procédé de fabrication d'un produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium, et produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium Pending EP4200450A1 (fr)

Applications Claiming Priority (2)

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EP2020073159 2020-08-19
PCT/EP2021/072833 WO2022038135A1 (fr) 2020-08-19 2021-08-17 Procédé de fabrication d'un produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium, et produit plat en acier ayant un revêtement résistant à la corrosion à base d'aluminium

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WO2023202765A1 (fr) * 2022-04-20 2023-10-26 Thyssenkrupp Steel Europe Ag Produit plat en acier pourvu d'un revêtement en al, son procédé de fabrication, composant en acier et son procédé de fabrication
DE102022115400A1 (de) * 2022-06-21 2023-12-21 Thyssenkrupp Steel Europe Ag Blechformteil mit verbesserten Schweißeigenschaften

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FR2780984B1 (fr) 1998-07-09 2001-06-22 Lorraine Laminage Tole d'acier laminee a chaud et a froid revetue et comportant une tres haute resistance apres traitement thermique
DE102008006771B3 (de) 2008-01-30 2009-09-10 Thyssenkrupp Steel Ag Verfahren zur Herstellung eines Bauteils aus einem mit einem Al-Si-Überzug versehenen Stahlprodukt und Zwischenprodukt eines solchen Verfahrens
WO2010085983A1 (fr) * 2009-02-02 2010-08-05 Arcelormittal Investigacion Y Desarrollo S.L. Procédé de fabrication de pièces estampées revêtues et pièces préparées à partir de ce procédé
KR20130132623A (ko) * 2011-04-01 2013-12-04 신닛테츠스미킨 카부시키카이샤 도장 후 내식성이 우수한 핫 스탬핑 성형된 고강도 부품 및 그 제조 방법
EP2886332B1 (fr) 2013-12-20 2018-11-21 ThyssenKrupp Steel Europe AG Produit en acier plat, et procédé de fabrication d'un composant d'une carrosserie de véhicule automobile et d'une carrosserie de véhicule automobile.
DE102014112448B4 (de) 2014-06-13 2016-11-24 Benteler Automobiltechnik Gmbh Herstellverfahren für Al-Si-beschichtete Stahlblechteile und Al-Si-beschichtetes Stahlblechband
ES2827455T3 (es) * 2016-02-25 2021-05-21 Benteler Automobiltechnik Gmbh Método de fabricación de un componente de automóvil con al menos dos zonas de resistencia mutuamente diferentes

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