EP3658307A1 - Pièce en tôle fabriquée par formage à chaud d'un produit plat en acier et procédé pour sa fabrication - Google Patents

Pièce en tôle fabriquée par formage à chaud d'un produit plat en acier et procédé pour sa fabrication

Info

Publication number
EP3658307A1
EP3658307A1 EP17754271.9A EP17754271A EP3658307A1 EP 3658307 A1 EP3658307 A1 EP 3658307A1 EP 17754271 A EP17754271 A EP 17754271A EP 3658307 A1 EP3658307 A1 EP 3658307A1
Authority
EP
European Patent Office
Prior art keywords
sheet metal
metal component
steel
content
hot
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
EP17754271.9A
Other languages
German (de)
English (en)
Other versions
EP3658307B8 (fr
EP3658307B9 (fr
EP3658307B1 (fr
Inventor
Brigitte Hammer
Harald Hofmann
Thomas Heller
Sebastian STILLE
Georg Parma
Janko Banik
Jonas SCHWABE
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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
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Application filed by ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP3658307A1 publication Critical patent/EP3658307A1/fr
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Publication of EP3658307B1 publication Critical patent/EP3658307B1/fr
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Anticipated expiration legal-status Critical

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Classifications

    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • 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
    • C23C2/06—Zinc or cadmium 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
    • C23C2/04—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
    • 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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling

Definitions

  • the invention relates to a sheet metal component produced by hot forming a flat steel product.
  • the invention relates to a method for producing a component according to the invention.
  • the flat steel products according to the invention are:
  • Mn-containing steels are known from EP 2 383 353 A2 which, as a coated or uncoated hot or cold strip, have an elongation at break A80 of at least 4% and a tensile strength of 900-1500 MPa. These steels contain besides iron and
  • C up to 0.5
  • Mn from 4 to 12%
  • Si up to 1, 0%
  • Al up to 3%
  • Cr from 0.1 to 4%
  • Cu up to 2.0%
  • Ni up to 2.0%
  • N up to 0.05%
  • P up to 0.05%
  • S up to 0.01%
  • Hot rolling start temperature 1150 - 1000 ° C to warm. Following this, the respective starting product becomes a hot strip
  • the finished hot strip is then coiled into a coil.
  • This step can optionally each annealing of
  • Hot strip cold rolling the annealed hot strip, annealing the cold strip and coating the surface of the hot strip or cold strip.
  • From EP 2 778 247 A1 is a method for producing a component by hot press forming a steel sheet after heating in Two-phase region, that is, after heating to a temperature which is between the Ac1 and the Ac3 temperature of the respective steel alloy known.
  • the obtained a slab made of iron, unavoidable impurities and (in% by weight) C: 0.01-0.5%, Si: up to 3.0%, Mn: 3-15%, P: 0.0001 - 0.1%, S: 0.0001 -0.03%, Al:
  • Hot rolled strip is coiled, annealed and then cold rolled. Subsequently, the hot strip is heated to a temperature between the Ad and the Ac3 temperature of the respective steel alloy, and hot press formed.
  • the structure of the component thus obtained consists of 5 to 50% by volume of retained austenite and the remainder of martensite, tempered martensite, bainite or ferrite.
  • Hot press hardening of conventional hot-forming steels From these steels existing boards are for the hot press forming on such a high
  • the object was to provide a sheet metal component which, compared to conventionally produced sheet metal components enables energy savings through lower forming temperatures, allows for increased residual elongation at high strengths and in which the highest possible potential for a cathodic Corrosion protection is ensured.
  • Sheet metal component can be specified.
  • a sheet-metal component according to the invention is accordingly produced by hot-forming a flat steel product which consists of (in% by weight) C: up to 0.5%, Si: 0.05-1%, Mn: 4-12%, Cr: 0.1 - 4%, Al: up to 3.5%, N: up to 0.05%, P: up to 0.05%, S: up to 0.01%, in total up to 2% Cu or Ni, in
  • the content% C of C and the content% Cr of Cr of the steel of the flat steel product satisfy the following condition: (10x% C) +% Cr ⁇ 5.5 wt%.
  • Hot forming to the sheet metal component according to VDA 238-100: 2010-12 determined bending angle of more than 60 °.
  • the microstructure of the hot-formed sheet-metal component according to the invention consists of austenite at 5% -50% by volume and the remainder martensite, tempered martensite or ferrite, whereby the ferrite content can also be 0.
  • the mean grain diameters of the grains of the microstructure are lower 5 ⁇ m, preferably less than 2 ⁇ m.
  • the flat steel product formed according to the invention into the sheet metal component consists of a steel which belongs to the class of the so-called "medium manganese steels", which usually contain Mn contents of 4 to 12% by weight,
  • Hot working can be reduced.
  • the advantages obtained are further enhanced by holding and hot working in the two-phase area.
  • the Mn contents of a flat steel product processed according to the invention are set at 4-12% by weight in such a way that the required minimum strengths of a steel according to the invention are reliably achieved and at the same time a high retained austenite content is maintained which ensures optimum elongation properties.
  • Carbon "C” determines in the steel of a steel flat product formed according to the invention to the component on the one hand the strength of martensite and on the other hand the amount and the stability of the retained austenite. Too high
  • Carbon content is the weldability and toughness of the steel, z. B. by formation of Cr carbides, adversely affected. Therefore, the amount is
  • the C content of a steel according to the invention is at least 0.02% by weight.
  • Aluminum "AI” and silicon “Si” are strong ferrite formers. Both elements counteract the influence of austenite formers C and Mn.
  • the essential object of the elements Si and Al consists in the steel according to the invention to the
  • Sheet metal component of hot-formed steel flat product is to suppress the carbide precipitation and thus promote the stability of the retained austenite.
  • Si and Al result in solid solution hardening and reduce the specific gravity of the steel. If the Si and AI content is too low, the
  • the invention provides, the Si content to max. 1 wt .-%, wherein the positive effects of the presence of Si can already be effectively used if the Si content of the steel of the flat steel product from which the component according to the invention is thermoformed, at least 0.05 wt .-% ,
  • Cr contributes to the increase in strength. Furthermore, Cr also lowers the Ms temperature (martensite start temperature) and thus supports retained austenite stabilization. From a content of 0.1% by weight Cr, but in particular from Cr contents of at least 2.2% by weight, these positive effects can be observed. From Cr contents of 2.2% by weight, the scale resistance is also improved in the uncoated state. at
  • Flat steel products provided with a metallic anti-corrosive coating can benefit from a positive effect on the layer, such as the effect as a diffusion barrier for the diffusion of iron into the protective coating.
  • thermoformed steel flat product is limited to max. 4 wt .-% limited, because at higher levels Cr carbides could occur, which would adversely affect the ductility of the steel.
  • the invention stipulates that the content "% C” of carbon “C” and the content “% Cr” of chromium “Cr” of the steel of a molded according to the invention to the component Flat steel product the condition (10x% C) +% Cr ⁇ 5.5 wt .-% must comply.
  • micro-alloying elements Ti, Nb and V can be found in the steel of the
  • the austenitic structure can be additionally stabilized. If the content of N is too high, the processability during continuous casting is impaired and a
  • the contents of phosphorus "P" of the steel of a component according to the invention are limited to a maximum of 0.05% by weight in order to reliably exclude negative influences of this element.
  • the sulfur content "S" of a steel according to the invention is limited to max. 0.01 wt% limited.
  • Rare earths "REM” can contribute to grain refining in the steel of the component according to the invention by forming oxides and improve the isotropy of the mechanical-technological properties via the texture.
  • the two rare earths cerium and lanthanum are chemically almost identical and therefore always occur in nature, communitized. Due to their chemical similarity, they are very heavy and therefore difficult to separate. They have the same thing
  • the rare earths can be freely substituted for use in steel. At levels above 0.1% by weight, however, the danger of so-called "clogging" arises, inter alia, in the large-scale casting of the steel. the clogging of the casting mold by locally solidifying melt. Nevertheless, the advantages of the presence of the SEM can be safely used by the fact that the content of the steel of a component according to the invention
  • the bending angle determined in accordance with VDA 238-100: 2010-12 is a measure of the folding behavior of the material in the event of a crash and thus an indicator of the ductility possessed by a hot-formed component.
  • Inventive components are characterized by a high bending angle of at least 60 °, in particular
  • Hot working at temperatures that are in the two-phase mixing zone of the steel (or deeper) that makes up the steel flat product from which the part is formed has beneficial effects.
  • Components according to the invention are characterized in that they have a structure which consists of at least 5% by volume of austenite, it being possible for the austenite content of the structure to be up to 50% by volume.
  • the remaining structure of the component consists of strength-increasing proportions of martensite and tempered martensite.
  • ferrite may be included.
  • the amount of other technically unavoidable structural constituents is so small that they are ineffective with regard to the properties of the component according to the invention.
  • the inventive method for producing a sheet metal component according to the preceding claims comprises the following steps: a) providing a steel flat product made of a steel, the (in wt .-%) of
  • the cooling rate at which the obtained hot-formed component is cooled is subject to no restrictions.
  • EP 2 383 353 A2 The basic possibilities of producing flat steel products suitable for the purposes according to the invention and provided in step a) of the method according to the invention are described in EP 2 383 353 A2, the content of which is incorporated by reference in the present application.
  • Typical protective layers which are present on components according to the invention and with which the flat steel products from which components according to the invention are formed can be coated with zinc-based protective coatings applied by hot-dip coating, such as Zn coatings ("Z"), zinc-iron coatings. Coatings ("ZF”), zinc-magnesium-aluminum coatings ("ZM”), zinc-aluminum coatings ("ZA”). Furthermore, aluminum-based protective coatings such as aluminum-zinc coatings (“AZ”), aluminum-silicon coatings (“AS”) can be used.
  • electrolytically applied protective coatings based on Zn such as pure zinc “ZE” coatings or zinc-nickel coatings (“ZN”).
  • metallic corrosion protection coatings which are known per se and which are applied by deposition methods, such as PVD, CVD or steam spraying, are also possible.
  • thermoforming a component can be produced that has optimal mechanical properties after its hot forming and due to these properties and its other
  • the high manganese content of flat steel products processed according to the invention enables lower hot forming temperatures than usual
  • the warming temperatures for hot working should not be more than 60 ° C above the Ac3 temperature of the respective steel of the flat steel product to obtain the desired positive properties.
  • the heating temperatures can be particularly low when the
  • the hot forming according to the invention takes place here at heating temperatures
  • Temperature range lie in which a two-phase structure in the
  • Flat steel product is present, it may be the heating temperature below the Ac1 temperature of the respective steel from which the
  • Heating temperatures of Austenitanteil before hot forming is not relevant, the desired proportion must be set in forming under Ac1 in a previous annealing step.
  • the heating temperature at this additional annealing should be at least so high that the forming forces stand out positively from those of the cold forming.
  • the heating temperature in this case should be set so that the forming forces of the hot forming a maximum of 85% of
  • the annealing times which are typically required for the heating in step b), are usually up to 60 minutes, with annealing times of up to 20 minutes, in particular up to 10 minutes, having proved to be particularly economical in practice.
  • the heating can be carried out in conventional chamber furnaces or roller kilns in which the
  • compositions of the deformed to the component steel flat product properties are formed almost independent of heating and cooling, but it may also prove to be beneficial if the heating is carried out by conductive or inductive heating, or for example by means of solid state contact or in a fluidized bed.
  • Alternative methods to conventional furnace heating can achieve shorter annealing times compared to pure radiant heating in conventional ovens. At the same time, the alternative methods allow more accurate heating cycles, as they affect the course of the
  • step c) The hot forming (step c)) of the respective
  • the component according to the invention can be made in conventional thermoforming tools available for this purpose in the prior art.
  • the hot forming is carried out as directly as possible subsequent to the heating (step b)), so that the temperature at which the flat steel product enters the thermoforming corresponds to a technically insignificant difference in the heating temperature. Indeed is also a stronger cooling allowed, as long as the forming forces and
  • the cooling of the component after the hot forming can be done in a manner known per se in the hot forming tool. Alternatively, however, after thermoforming, the component may be cooled outside the tool at a suitably short interval from the thermoforming tool. Since the cooling rate is not limited, it can even be less than 10K / s.
  • the invention has a particularly positive effect on the production of components made of flat steel products, which are metallic
  • Protective layer are used to protect them from corrosion or other attacks.
  • thermoforming of the component according to the invention can be carried out, a Auflegieren the protective coating by diffusion of alloying constituents from the steel substrate takes place at most reduced, so that the protective coating even after the
  • Thermoforming of the component maintains its cathodic protection.
  • the protective layers present on the steel flat product processed in accordance with the invention in each case, which are hot-deformed to the component according to the invention, typically have a surface near to the hot-forming prior to hot-forming
  • the parameters of the procedure according to the invention make it possible to obtain the cathodic protective effect of a Zn-containing layer present on the flat steel product and to avoid critical cracks during hot forming of more than 10 ⁇ m.
  • the comparative steel V conventionally used in hot working typically contributes to the adjustment of the mechanical target properties
  • Target properties additionally consist of the distinctly Zn-richer ⁇ -phase, which leads to an improved corrosion protection potential. Due to the
  • the layer system is sufficiently temperature stable, so that in inventive
  • Hot forming temperatures to no critical cracking over 10 ⁇ depth comes through liquid Zn, in which a crack propagation would be expected under stress of the component.
  • a manganese-containing layer is formed on the free surface of the protective coating in a manner known per se (see EP 2 290 133 B1)
  • components produced according to the invention have temperatures which are below a maximum limit, which are the
  • the product Rm x A80 in components according to the invention is likewise regularly in the range from 13,000 to 35,000 MPa%.
  • the tensile strengths Rm are at components that out
  • compositions are given in each case in wt .-% in Table 1.
  • Table 1 lists the Ad and Ac3 temperatures in ° C determined for steels S1-S3 and V according to SEP 1680: 1990-12.
  • the comparative melt V is due to their low Mn content and the presence of B outside the specifications of the invention.
  • Hot strips have been cut from a conventionally produced precursor to a thickness "d” hot rolled (state “WW”) and then under a hood (state “HG”) or in a continuous furnace (state “DO”) have been annealed
  • state "WW" hot rolled
  • HG hood
  • DO continuous furnace
  • Hot rolled strips which have additionally been cold-rolled to a thickness "d" (state "KW) Before the blanking, some of the cold-rolled strips are partially hood-annealed, as in examples 3, 6, 12 (state “HG”). ) or, as in Examples 7, 9, 10, 13-16, in a continuous furnace ("DO" state) Some of the sheet blanks are also electrolytically ("ZE") or fire-coated (“ZE”) or fire-coated with a pure zinc layer (“ Z "), with a zinc-iron layer (“ ZF ”) or with an aluminum-silicon layer (“ AS ").
  • ZE electrolytically
  • Z fire-coated
  • ZF pure zinc-iron layer
  • AS " aluminum-silicon layer
  • the blanks are each heated to a heating temperature Tew in a conventional oven, then hot worked into a hat profile in a conventional thermoforming tool and then cooled in air.
  • the determined on each component obtained tensile strength Rm, the
  • Yield strength Rp0.2, the elongation at break A80, the product Rm x A80 and the bending angle are given in Table 2.
  • structural parameters of the respectively obtained component are specified there.
  • Elongation at break A80 is above 10% and the products Rm x A80 are more than 14,000 MPa%. At the same time, the examples have bending angles of more than 60 °.
  • austenitic structure is set, which largely converts to martensite during cooling, which leads to the high strengths.
  • a particularly fine structure can be achieved by adding
  • Microalloying elements and rare earth metals are achieved.
  • Sheet metal cutting headed glowing in the two phase field set When hot forming below Ac1, essentially only the martensite is tempered.
  • the latter method has, in addition to good mechanical properties, particular advantages with respect to the coating. Since the temperatures are below the melting temperature of the coating, cracks in the substrate can be largely avoided by penetrating zinc during hot working.
  • the coating is such that cracks remain within an acceptable range of at most 10 ⁇ .

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne une pièce en tôle et un procédé pour la fabrication de telles pièces en tôle qui, par rapport à des pièces en tôle fabriquées de manière classique, permet une économie d'énergie par des températures de formage plus basses, admet une dilatation résiduelle plus élevée à des résistances élevées et pour lequel un potentiel le plus élevé possible pour une protection cathodique contre la corrosion est assuré. La pièce en tôle selon l'invention est constituée par (en % en poids) C : jusqu'à 0,5 %, Si : 0,05-1 %, Mn : 4-12 %, Cr : 0,1-4 %, AI : jusqu'à 3,5 %, N : jusqu'à 0,05 %, P : jusqu'à 0,05 %, S : jusqu'à 0,01 %, Cu, Ni : au total jusqu'à 2 %, Ti, Nb, V : au total jusqu'à 0,5 %, terres rares : jusqu'à 0,1 %, et le reste est constitué par du Fe et des impuretés inévitables, la teneur % C en C et la teneur % Cr en Cr remplissant la condition suivante : (10 x %C) + %Cr < 5,5 %. Pour la fabrication d'une pièce en tôle, selon l'invention, le produit plat en acier est chauffé à une température de réchauffement qui est d'au moins 200°C et d'au plus 800°C et il est ensuite façonné, par formage à chaud du produit plat en tôle chauffé à température de réchauffement, en pièce, la structure de la pièce en tôle façonnée à chaud étant constituée à raison de 5-50 % en volume d'austénite et, comme reste, de martensite, de martensite trempée ou de ferrite, la proportion de ferrite pouvant également être de "0" et le diamètre moyen des grains de la structure étant inférieur à 5 pm.
EP17754271.9A 2017-07-25 2017-07-25 Pièce en tôle fabriquée par formage à chaud d'un produit plat en acier et procédé pour sa fabrication Active EP3658307B9 (fr)

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PCT/EP2017/068771 WO2019020169A1 (fr) 2017-07-25 2017-07-25 Pièce en tôle fabriquée par formage à chaud d'un produit plat en acier et procédé pour sa fabrication

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DE102020204356A1 (de) 2020-04-03 2021-10-07 Thyssenkrupp Steel Europe Ag Gehärtetes Blechbauteil, hergestellt durch Warmumformen eines Stahlflachprodukts und Verfahren zu dessen Herstellung
WO2021230149A1 (fr) * 2020-05-13 2021-11-18 日本製鉄株式会社 Corps moulé estampé à chaud
CN113913700B (zh) * 2021-10-26 2023-01-24 江苏沙钢集团有限公司 一种1700MPa级热成形钢及其生产方法

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ATE554190T1 (de) 2009-08-25 2012-05-15 Thyssenkrupp Steel Europe Ag Verfahren zum herstellen eines mit einem metallischen, vor korrosion schützenden überzug versehenen stahlbauteils und stahlbauteil
EP2383353B1 (fr) 2010-04-30 2019-11-06 ThyssenKrupp Steel Europe AG Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication
CN102127675B (zh) * 2011-02-21 2012-11-14 钢铁研究总院 高效率低能耗高质量的钢板温成形零件的生产方法
EP2524970A1 (fr) * 2011-05-18 2012-11-21 ThyssenKrupp Steel Europe AG Produit plat en acier hautement résistant et son procédé de fabrication
KR101382981B1 (ko) * 2011-11-07 2014-04-09 주식회사 포스코 온간프레스 성형용 강판, 온간프레스 성형 부재 및 이들의 제조방법
EP2690183B1 (fr) * 2012-07-27 2017-06-28 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à chaud et son procédé de fabrication
EP3093359A4 (fr) 2014-01-06 2017-08-23 Nippon Steel & Sumitomo Metal Corporation Élément formé à chaud et son procédé de fabrication
EP3132063B1 (fr) * 2014-04-15 2021-01-13 ThyssenKrupp Steel Europe AG Procédé de production d'un produit plat en acier laminé à froid à limite d'élasticité élevée et produit plat en acier laminé à froid
US10508317B2 (en) * 2014-07-18 2019-12-17 Nippon Steel Corporation Steel product and manufacturing method of the same
MX2017001526A (es) * 2014-08-07 2017-05-11 Jfe Steel Corp Lamina de acero de alta resistencia y metodo para fabricar la misma.
CN104846274B (zh) 2015-02-16 2017-07-28 重庆哈工易成形钢铁科技有限公司 热冲压成形用钢板、热冲压成形工艺及热冲压成形构件
US20160312323A1 (en) 2015-04-22 2016-10-27 Colorado School Of Mines Ductile Ultra High Strength Medium Manganese Steel Produced Through Continuous Annealing and Hot Stamping
KR101677398B1 (ko) * 2015-11-30 2016-11-18 주식회사 포스코 열간성형용 강재 및 이를 이용한 부재 제조방법
CN105483531A (zh) * 2015-12-04 2016-04-13 重庆哈工易成形钢铁科技有限公司 用于冲压成形的钢材及其成形构件与热处理方法

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CN110944765B (zh) 2022-02-25
EP3658307B8 (fr) 2021-11-03
US20210087662A1 (en) 2021-03-25
EP3658307B9 (fr) 2022-01-12
CN110944765A (zh) 2020-03-31
EP3658307B1 (fr) 2021-09-29
WO2019020169A1 (fr) 2019-01-31

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