EP3658307B9 - 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 Download PDF

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Publication number
EP3658307B9
EP3658307B9 EP17754271.9A EP17754271A EP3658307B9 EP 3658307 B9 EP3658307 B9 EP 3658307B9 EP 17754271 A EP17754271 A EP 17754271A EP 3658307 B9 EP3658307 B9 EP 3658307B9
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EP
European Patent Office
Prior art keywords
flat steel
steel product
steel
metal sheet
content
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EP17754271.9A
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German (de)
English (en)
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EP3658307B1 (fr
EP3658307A1 (fr
EP3658307B8 (fr
Inventor
Brigitte Hammer
Harald Hofmann
Thomas Heller
Sebastian STILLE
Georg Parma
Janko Banik
Jonas SCHWABE
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • 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
    • C21D8/0205—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
    • C22C38/02—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
    • C22C38/06—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
    • 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
    • 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 rolled products, such as steel strips, steel sheets or products made from them Blanks and blanks whose thickness is significantly less than their width and length.
  • these steels contain 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%, and optionally one or more elements from the group "V, Nb, Ti", the sum of the contents of these elements not exceeding 0.5%.
  • the EP 2 383 353 A2 presented a process for the production of a coated or uncoated hot or cold strip.
  • a molten steel composed as described above is cast into a billet or strip, which is then subjected to a heat treatment to heat it up to a hot rolling start temperature of 1150 - 1000 °C to produce a starting product.
  • the respective starting product is then hot-rolled into a hot strip.
  • the finished hot strip is then wound into a coil.
  • This work step can optionally be followed by annealing of the hot strip, cold rolling of the annealed hot strip, annealing of the cold strip and coating of the surface of the hot or cold strip.
  • From the EP 2 778 247 A1 is a method of manufacturing a component by hot press forming a steel sheet after heating in Two-phase region, ie after heating to a temperature between the Ac1 and the Ac3 temperature of the respective steel alloy, is known.
  • the hot-rolled strip obtained is coiled, annealed and then cold-rolled.
  • the hot strip is then heated to a temperature between the Ac1 and Ac3 temperatures of the respective steel alloy and hot press formed.
  • the structure of the component obtained in this way consists of 5 - 50% by volume of retained austenite and the remainder of martensite, tempered martensite, bainite or ferrite.
  • a component is also known that is hot-formed from a steel sheet made of a steel which, in % by weight, contains 0.02 - 0.45% C, 3.50 - 9.0% Mn, at most 0.020% P , at most 0.020% S, the rest Fe and unavoidable impurities.
  • the steel can additionally contain 0.1 - 3.0% Ni, 0.2 - 3.0% Cr, 0.1 - 0.8% Mo, 0.3 - 2.3% Si, 0.5 - 2.0 % Cu, 0.0005 - 0.0050% B, 0.02 - 0.30% Nb, 0.002 - 0.250% N, 0.05 - 0.25% Ti, 0.02 - 0.25% V, 0.015 - 3.0% Al, 0.002 - 0.005% REM and 0.005 - 0.03% Ca included.
  • the manufacturing process envisaged for this includes the following steps: heating of the steel sheet, transfer of the steel sheet, pre-cooling of the steel sheet, forming of the part and cooling of the part.
  • the task was to create a sheet metal component which, compared to conventionally produced sheet metal components, enables energy savings through lower forming temperatures, allows increased residual elongation at high strengths and which has the highest possible potential for a cathodic protection against corrosion is maintained.
  • a sheet metal component that achieves this object has at least the features specified in claim 1 .
  • a sheet metal component according to the invention is accordingly produced by hot forming of a steel flat product consisting of (in % by weight) C: 0.02-0.5%, Si: 0.05-1%, Mn: 4-12%, Cr: 0 .1 - 4%, AI: up to 3.5%, N: up to 0.05%, P: up to 0.05%, S: up to 0.01%, in total > 0.04% up to 2% Cu and/or Ni, up to 0.5% in total of Ti, Nb or V, rare earths: up to 0.1% and the remainder consists of Fe and unavoidable impurities.
  • the content %C of C and the content %Cr of Cr in the steel of the steel flat product fulfill the following condition: (10x%C)+%Cr ⁇ 5.5% by weight.
  • the flat steel product according to the invention has a bending angle of more than 60°, determined according to VDA 238-100: 2010-12, after hot forming to form the sheet metal component.
  • the microstructure of the hot-formed sheet metal component according to the invention consists of 5-50% by volume of austenite and the remainder of martensite, tempered martensite or ferrite, it also being possible for the ferrite proportion to be “0”.
  • the average grain diameter of the grains of the structure is less than 5 ⁇ m, preferably less than 2 ⁇ m.
  • the flat steel product formed into the sheet metal component according to the invention consists of a steel which belongs to the class of so-called "middle manganese steels" which usually have Mn contents of 4-12% by weight, in particular 4-9% by weight.
  • Manganese "Mn” lowers the austenitization temperature and delays the transformation of ferrite, pearlite and bainite. This also allows the holding temperature in the furnace before hot forming to be reduced. The advantages obtained are further enhanced by holding and hot working in the two-phase region. During the subsequent cooling, a high proportion of austenite is retained. This leads to a very high residual elongation at break and a high possible bending angle up to the first cracks and thus higher energy absorption in the event of a crash.
  • the Mn content of a steel flat product processed according to the invention is set at 4-12 wt.
  • carbon “C” determines the strength of martensite on the one hand and others the amount and stability of the retained austenite. If the carbon content is too high, the weldability and toughness of the steel, e.g. B. negatively affected by the formation of Cr carbides. Therefore, the carbon content of Mn steels of the type selected according to the invention is at most 0.5% by weight, with lower C contents of less than 0.5% by weight, in particular of up to 0.3% by weight prove particularly favorable. However, if the carbon content is too low, the amount and stability of the retained austenite will be affected. The carbon content of a steel according to the invention is therefore at least 0.02% by weight.
  • Aluminum "AI” and silicon “Si” are strong ferrite formers. Both elements counteract the influence of the austenite formers C and Mn.
  • the main task of the elements Si and Al in the steel of a steel flat product hot-formed to form the sheet metal component according to the invention is to suppress carbide precipitation and thus promote the stability of the retained austenite.
  • Si and Al lead to solid solution hardening and reduce the specific weight of the steel.
  • the Si and Al content is too low, carbide precipitation may not be effectively suppressed.
  • the Si and Al contents are too high, processing is made more difficult both in the case of production using a continuous casting method and in the case of production using a strip casting method.
  • the invention therefore provides for the Si content to be limited to a maximum of 1% by weight, with the positive effects of the presence of Si already being able to be used effectively if the Si content of the steel of the flat steel product from which the inventive component is thermoformed is at least 0.05% by weight.
  • chromium “Cr” in amounts of 0.1-4% by weight specifically reduces the risk of stress corrosion cracking in a steel according to the invention.
  • Cr and Al hinder hydrogen-induced cracking.
  • Cr contributes to the increase in strength.
  • Cr also lowers the Ms temperature (martensite start temperature) and thus supports the stabilization of retained austenite.
  • the Cr content of the steel of a flat steel product hot-formed to form the component according to the invention is limited to a maximum of 4% by weight, because higher contents could produce Cr carbides which would adversely affect the ductility of the steel.
  • the invention stipulates that the carbon “C” content “%C” and the chromium “Cr” content “%Cr” of the steel of a component formed according to the invention must be taken into account Steel flat product must comply with the condition (10x%C) + %Cr ⁇ 5.5% by weight.
  • micro-alloying elements Ti, Nb and V can be present in the steel of the flat steel product from which the component according to the invention is formed in amounts totaling up to 0.5% by weight. These micro-alloying elements contribute to grain refinement and increased strength. However, contents of Ti, Nb and V above 0.5% by weight do not increase this effect, whereas the positive effects of Ti, Nb and V in the steel of the component according to the invention can be safely used if their in total is at least 0.05% by weight.
  • the austenitic structure can be additionally stabilized by adding nitrogen "N" in amounts of up to 0.05% by weight. If the N content is too high, processability during continuous casting is impaired and an brittle amount of nitrides is formed.
  • the content of phosphorus "P" in the steel of a component according to the invention is limited to a maximum of 0.05% by weight in order to reliably rule out negative influences from this element.
  • the sulfur "S" content of a steel according to the invention is limited to a maximum of 0.01% by weight.
  • Rare earths "REM” can contribute to grain refinement in the steel of the component according to the invention through the formation of 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 come in the Nature always communitized before. Due to their chemical similarity, they are very difficult and therefore difficult to separate. They have the same effect.
  • Rare earths can be freely substituted for use in steel. With contents above 0.1% by weight, however, there is, among other things, the risk of so-called "clogging" in industrial-scale casting of the steel, ie the clogging of the casting mold by locally solidifying melt.
  • the advantages of the presence of the REM can nevertheless be safely used in that the steel content of a component according to the invention is at least 0.0005% by weight.
  • 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 is therefore an indicator of the ductility that a hot-formed component has.
  • Components according to the invention are characterized by a high bending angle of at least 60°, in particular at least 80° or more than 80°, such as at least 85°, after hot forming.
  • the uniform, very fine structure plays a supporting role here.
  • High austenite content such as that present when hot working occurs at temperatures in the two-phase mixing region (or lower) of the steel making up the flat steel product from which the component is formed, has beneficial effects.
  • Components according to the invention are distinguished by the fact that they have a structure which consists of at least 5% by volume of austenite, with the proportion of austenite in the structure being able 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 also be included.
  • the amount of other structural components that are technically unavoidable is so small that they are ineffective with regard to the properties of the component according to the invention.
  • the method according to the invention for producing a sheet metal component according to the preceding claims comprises the following work steps: a) Providing a flat steel product made from a steel which, in % by weight, consists of C: 0.02 - 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%, a total of 0.04% up to 2% Cu and/or Ni, a total of up to 0.5% Ti, Nb or V, SEM: up to 0.1% and the balance being Fe and unavoidable impurities, where the %C content of C and the %Cr content of Cr satisfies the following condition: 10 ⁇ %C + %Cr ⁇ 5 .5% , b) through heating the steel flat product to a heating temperature which is at least 200 °C and at most 800 °C; c) Hot forming of the flat steel product
  • the cooling rate at which the hot-formed component obtained is cooled is not subject to any restrictions.
  • EP 2 383 353 A2 The basic possibilities of producing steel flat products that are suitable for the purposes of the invention and are provided in step a) of the method of the invention are in EP 2 383 353 A2 described.
  • the diagram reproduced there and the associated sections [0031] to [0040] of EP 2 383 353 A2 are the different in methods available in practice for producing flat steel products which are suitable for producing components according to the invention.
  • Typical protective coatings present on components of the present invention are hot dip zinc-based protective coatings such as Zn (“Z”) coatings, zinc-iron coatings ("ZF”), Zinc-Magnesium-Aluminum Coatings ("ZM”), Zinc-Aluminum Coatings ("ZA”).
  • zinc-based protective coatings such as Zn (“Z") coatings, zinc-iron coatings (“ZF”), Zinc-Magnesium-Aluminum Coatings (“ZM”), Zinc-Aluminum Coatings (“ZA”).
  • aluminum-based protective coatings can be used, such as aluminum-zinc coatings ("AZ”), aluminum-silicon coatings ("AS”).
  • Electrolytically applied Zn-based protective coatings such as pure zinc “ZE” coatings or zinc-nickel (“ZN”) coatings can also be provided.
  • metallic anti-corrosion coatings which are known per se and are applied by deposition processes such as PVD, CVD or vapor spraying are also possible.
  • the invention shows a way in which resource-saving hot forming can be used to produce a component that has optimal mechanical properties after hot forming and, due to these properties and its other functional properties, can also meet high requirements in the event of a crash load on the component.
  • the high manganese content of flat steel products processed according to the invention enables lower hot forming temperatures than with conventional hot forming steels.
  • the invention thus makes it possible to save energy and costs.
  • the heating temperatures for hot forming should not be more than 60° C. above the Ac3 temperature of the respective steel of the steel flat product in order to obtain the desired positive properties.
  • the heating temperatures can be particularly low if the deformation is to take place in the two-phase region or at temperatures below that. In this case, the proportion of residual austenite in the resulting component is over 20% by volume and the elongation at break A80 is over 15%.
  • the hot forming according to the invention takes place here at heating temperatures that are typically above the Ac1 temperature and below the Ac3 temperature of the respective steel of the steel flat product, with heating temperatures that are at least 10 °C higher proving to be particularly favorable in the case of deformation in the two-phase region are lower than the Ac1 temperature and at least 50 °C lower than the Ac3 temperature of the respective steel of the steel flat product.
  • the heating temperature can be below the Ac1 temperature of the respective steel from which the flat steel product hot-formed according to the invention consists.
  • the proportion of austenite before hot forming is not important for anneals with heating temperatures above the Ac1 temperature, the desired proportion for forming below Ac1 must be set in a preceding annealing step.
  • the heating temperature during this additional annealing should be at least so high that the forming forces stand out positively from those of cold forming. Accordingly, in this case the heating temperature should be set in such a way that the forming forces during hot forming amount to a maximum of 85% of the forming forces at room temperature. This is at Heating temperatures of over 200 °C, in particular over 400 °C, secured.
  • the procedure according to the invention results in a structure which is characterized by optimized proportions of austenite and, as a result, has very good mechanical properties, in particular high residual elongation and high energy absorption in the event of a crash load.
  • the comparatively low heating temperatures in this range, at which the hot forming of the component according to the invention takes place, also prove to be particularly advantageous if the flat steel product processed according to the invention is to have cathodic corrosion protection.
  • the annealing times typically required for thorough 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 proven to be particularly economical in practice.
  • Thorough heating can be carried out in conventional chamber furnaces or roller furnaces, in which the flat steel products to be hot-formed are brought to the heating temperature in a continuous flow or in batches. Since the properties of the flat steel product formed into the component are formed almost independently of the heating and cooling rate in compositions according to the invention, it can also prove advantageous if the heating is carried out by conductive or inductive heating, or also, for example, by means of solid-body contact or in a fluidized bed .
  • the alternative methods to conventional furnace heating mean that shorter annealing times can be achieved in comparison to pure radiation heating in a conventional furnace. At the same time, the alternative methods allow for more precisely controlled heating cycles since the course of the heating can follow precise specifications. Another advantage of using the alternative heating process is that it is possible to react quickly to production changes, which are typical for small batch production with different sheet metal thicknesses.
  • the hot forming (work step c)) of the steel flat product heated to the respective heating temperature to form the component according to the invention can be carried out in conventional hot forming tools available for this purpose in the prior art.
  • the hot forming takes place as soon as possible after the through heating (work step b)), so that the temperature at which the steel flat product enters the hot forming corresponds to the heating temperature with the exception of a technically insignificant difference.
  • stronger cooling is also permissible as long as the forming forces and springback are advantageous compared to cold forming.
  • the cooling of the component after the hot forming can also take place in a manner known per se in the hot forming tool.
  • the component can also be removed from the hot forming tool and cooled outside of the tool at a suitably short time interval. Since the cooling speed is not limited, it can even be less than 10K/s.
  • the invention has a particularly positive effect when producing components from flat steel products that are coated with a metallic protective layer to protect them from corrosion or other attacks.
  • each of the protective layers processed according to the invention and hot-formed into the component according to the invention typically have a surface-near boundary layer adjoining the steel substrate of the flat steel product prior to the hot-forming, which consists of metallic and/or oxidic iron and, if necessary, metallic and/or oxidic manganese and the other alloy components of the base material.
  • the parameters of the procedure according to the invention make it possible to maintain the cathodic protective effect of a layer containing Zn present on the flat steel product and to avoid critical cracks of more than 10 ⁇ m during hot forming.
  • the harmful consequences that would occur if the Zn layer were to melt are avoided. Due to the diffusion of Fe from the substrate into the layer, its melting point is raised sufficiently. However, in order to maintain cathodic protection against corrosion, the Fe content in the coating must be limited so that sufficient Zn-rich phases are retained after hot forming.
  • the Fe-Zn phases present in the coating were determined for the examples by X-ray diffractometry and are summarized in Table 3.
  • the comparison steel V which is conventionally used in hot forming, is typically annealed at 870 - 950 °C to set the target mechanical properties. This leads to the formation of a ⁇ / ⁇ 1 phase, which is comparatively temperature-stable, which limits the proportion of liquid Zn that forms and thus reduces the risk of liquid metal embrittlement occurring.
  • the high proportion of Fe contained in the ⁇ / ⁇ 1 phase severely limits the active corrosion protection of the layer.
  • the significantly higher Zn-rich ⁇ phase also remains due to the significantly lower oven temperature for setting the mechanical target properties, which leads to an improved corrosion protection potential.
  • the layer system Due to the layer structure caused by the alloying, the layer system is sufficiently temperature-stable so that no critical cracking of more than 10 ⁇ m depth occurs due to liquid Zn at hot forming temperatures according to the invention, at which crack propagation would be expected when the component is stressed.
  • components produced according to the invention have an optimized combination of high strength values, for which tensile strengths Rm of typically at least 1000 MPa stand, and optimized elongation properties, which are expressed in elongations at break A80 of regularly more than 10%.
  • the product Rm ⁇ A80 is accordingly also regularly in the range of 13,000-35,000 MPa%.
  • the tensile strengths Rm for components made from conventional steels for hot forming were produced at temperatures at which a fully austenitic structure is present, typically at least 1200 MPa, since they are fully martensitic after quenching.
  • these components only achieve significantly lower elongation at break values A80, so that the product Rm x A80 for these components is regularly only 6,000 - 11,000 MPa%.
  • Table 1 shows the Ac1 and Ac3 temperatures in °C determined for steels S1 - S3 and V in accordance with SEP 1680:1990-12.
  • the comparison melt V lies outside the specifications of the invention due to its low Mn content and the presence of B.
  • Sheet metal blanks were made from steels S1 - S3 and V.
  • the sheet metal blanks were each heated through in a conventional oven to a heating temperature Tew, then hot-formed in a conventional hot-forming tool to form a hat profile and then cooled in air.
  • the tensile strength Rm determined on the component obtained in each case, the yield point Rp0.2, the elongation at break A80, the product Rm ⁇ A80 and the bending angle are given in Table 2.
  • structural parameters of the component obtained are given there.
  • the austenite content of the respective component obtained and the estimated grain size as well as the crack depths at the most critical point of the hat profile are given there, as measured in the cross section under the light microscope.
  • the elongations at break A80 are more than 10% and the products Rm ⁇ A80 are more than 14,000 MPa%.
  • the examples have bending angles of more than 60°.
  • a particularly fine structure can be achieved by alloying micro-alloying elements and rare earth metals.
  • the austenite content was adjusted by annealing in the two-phase region prior to sheet metal cutting.

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Claims (13)

  1. Composant en tôle produit par formage à chaud d'un produit plat en acier, comprenant, en % en poids C : de 0,02 à 0,5 %, Si : de 0,05 à 1 %, Mn : de 4 à 12 %, Cr : de 0,1 à 4 %, Al : 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 %, la somme des teneurs en Cu et Ni étant > 0,04 %, Ti, Nb, V : en somme jusqu'à 0,5 %, Terres rares : jusqu'à 0,1 %,
    et le reste étant constitué de Fe et d'impuretés inévitables,
    où la teneur %C de C et la teneur %Cr de Cr satisfont la condition suivante: 10 × %C + %Cr < 5 ,5% ,
    Figure imgb0007
     où le produit plat en acier, après avoir été formé à chaud en composant en tôle, a un angle de pliage de plus de 60° déterminé selon la norme VDA 238-100 : 2010-12 et
    où la structure du composant en tôle formé à chaud est constituée de 5 à 50 % en volume d'austénite et le reste de martensite, de martensite tempérée ou de ferrite, où la teneur en ferrite peut également être "0", et où le diamètre moyen de grain des grains de la structure est inférieur à 5 µm.
  2. Composant en tôle selon la revendication 1, caractérisé en ce que sa teneur en C est de jusqu'à 0,3 % en poids.
  3. Composant en tôle selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cr est d'au moins 2,2 % en poids.
  4. Composant en tôle selon l'une des revendications précédentes, caractérisé en ce que le diamètre moyen de grain est inférieur à 2 µm.
  5. Composant en tôle selon l'une des revendications précédentes, caractérisé en ce que l'angle de pliage est supérieur à 80°.
  6. Composant en tôle selon l'une des revendications précédentes, caractérisé en ce qu'après formage à chaud, la résistance à la traction Rm du produit plat en acier est d'au moins 1000 MPa, son allongement à la rupture A80 est supérieur à 10% et le produit Rm*A80 formé de sa résistance à la traction Rm et de son allongement à la rupture A80 est supérieur à 13000 MPa%.
  7. Composant en tôle selon l'une des revendications précédentes, caractérisé en ce qu'il est pourvu d'un revêtement protecteur métallique.
  8. Procédé de fabrication d'un composant en tôle selon l'une des revendications précédentes, comprenant les étapes de travail suivantes:
    a) mise à disposition d'un produit plat en acier fabriqué à partir d'un acier constitué, en % en poids, de C : de 0,02 à 0,5 %, Si : de 0,05 à 1 %, Mn : de 4 à 12 %, Cr : de 0,1 à 4 %, Al : jusqu'à 3,5 %, N : jusqu'à 0,05 %, P : jusqu'à 0,05 %, S : jusqu'à 0,01 %, au total plus de 0,04 % et jusqu'à 2 % de Cu et/ou Ni, au total jusqu'à 0,5 % de Ti, Nb ou V, REM : jusqu'à 0,1 %,
    et le reste étant constitué de Fe et d'impuretés inévitables,
    la teneur %C de C et la teneur %Cr de Cr satisfaisant à la condition suivante: 10 × %C + %Cr < 5 ,5%
    Figure imgb0008
    b) chauffage à cœur du produit plat en acier à une température de chauffage, laquelle est au moins de 200°C et au plus égale à la température Ac3 + 60°C de l'acier dont le produit plat en acier est respectivement constitué;
    c) travail à chaud du produit en acier plat chauffé à la température de chauffage pour former le composant.
  9. Procédé selon la revendication 8, caractérisé en ce que la température de chauffage est au maximum de 800°C.
  10. Procédé selon la revendication 8, caractérisé en ce que la température de chauffage est supérieure à la température Ac1 et inférieure à la température Ac3 de l'acier dont est constitué respectivement le produit plat en acier.
  11. Procédé selon la revendication 8, caractérisé en ce que la température de chauffage est inférieure à la température Ac1 de l'acier dont est constitué respectivement le produit plat en acier.
  12. Procédé selon l'une quelconque des revendications 8 à 11, caractérisé en ce que le produit plat en acier mis à disposition à l'étape a) comporte une couche métallique anticorrosion.
  13. Procédé selon l'une quelconque des revendications 8 à 11, caractérisé en ce que le chauffage à cœur de l'étape de travail b) est effectué au moyen d'un procédé de chauffage par conduction ou par induction.
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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EP4151757A4 (fr) * 2020-05-13 2023-10-04 Nippon Steel Corporation 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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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
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EP2524970A1 (fr) * 2011-05-18 2012-11-21 ThyssenKrupp Steel Europe AG Produit plat en acier hautement résistant et son procédé de fabrication
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US20170218475A1 (en) * 2014-08-07 2017-08-03 Jfe Steel Corporation High-strength steel sheet and method for manufacturing same
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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
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