EP1865086B1 - Use of a steel flat product produced from a manganese boron steel and method of its production - Google Patents

Use of a steel flat product produced from a manganese boron steel and method of its production Download PDF

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Publication number
EP1865086B1
EP1865086B1 EP06115075A EP06115075A EP1865086B1 EP 1865086 B1 EP1865086 B1 EP 1865086B1 EP 06115075 A EP06115075 A EP 06115075A EP 06115075 A EP06115075 A EP 06115075A EP 1865086 B1 EP1865086 B1 EP 1865086B1
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EP
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Prior art keywords
hot
steel
rolled strip
cold
rolling
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EP06115075A
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German (de)
French (fr)
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EP1865086A1 (en
Inventor
Dr.-Ing Jian Bian
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Priority to AT06115075T priority Critical patent/ATE477348T1/en
Priority to DE502006007636T priority patent/DE502006007636D1/en
Priority to EP06115075A priority patent/EP1865086B1/en
Priority to PCT/EP2007/055130 priority patent/WO2007141152A1/en
Publication of EP1865086A1 publication Critical patent/EP1865086A1/en
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • 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
    • C22C38/04—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
    • C23C10/02—Pretreatment of the material to be coated
    • 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
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/021—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material including at least one metal alloy layer
    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/023—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material only coatings of metal elements only
    • C23C28/025—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material only coatings of metal elements only with at least one zinc-based layer

Definitions

  • the invention relates to a use of a steel flat product produced from a manganese-boron steel, and a method for its production.
  • MnB steels of the type used according to the invention are used in particular in the field of automobile construction for the production of components which are said to have a high strength in addition to a low weight.
  • Manganese-boron steels of the type in question which are standardized in EN 10083-3, have proven particularly suitable for the hot-pressing deformation. These steels have a good hardenability, which allows safe process control during hot pressing and by which it is economically possible to effect a martensite hardening in the mold without additional cooling during the hot deformation.
  • 22MnB5 steel A MnB steel proven in practice for the purposes summarized above is known as "22MnB5" and has been given the material number 1.5528 in the steel key, 2004 edition.
  • 22MnB5 steel on the market contains, in addition to iron and unavoidable impurities (in wt%), 0.220-0.250% C, 1.2-1.4% Mn, 0.2-2.3% Si, up to 0 , 02% P, up to 0.005% S, 0.020-0.050% Al, 0.020-0.050% Ti, 0.11-0.2% Cr, 0.002-0.0035% B and in each case up to 0.1% Mo, Cu and Ni (Material Data Sheet 11-112 of Salzgitter Flachstahl GmbH, November 2005 edition).
  • a MnB steel in addition to iron and unavoidable impurities (in% by weight), has a carbon content of more than 0.20%, but less than 0.5%, 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%.
  • An Indian EP 0 971 044 B1 As an exemplary embodiment, provided with an Al coating steel sheet has accordingly (in wt .-%) 0.21% C, 1.14% Mn, 0.020% P, 0.0038% S, 0.25% Si, 0, 04% Al, 0.009% Cu, 0.020% Ni, 0.18% Cr, 0.0040% N, 0.032% Ti, 0.003% B and 0.0050% Ca. After a heat treatment, the strength of this steel sheet should be more than 1500 MPa.
  • the residual fracture strain of the known steels is typically only 5-6%.
  • steels are needed, in addition to a high strength and an improved elongation behavior of the manufactured from such a steel component after hot pressing.
  • the steel sheet consists of a steel, which in addition to iron and unavoidable impurities (in wt .-%) C: 0.05 to 0.2%, Si: 0.2 to 2.0%, Mn: 0.2 to 2 , 5%, Al: 0.01 to 1.5%, Ni: 0.73 to 5.0%, P: ⁇ 0.03% and S: ⁇ 0.02%, and optionally one or more of the following ingredients Cu: ⁇ 0.2%, B: 0.0002 to 0.01%, Co: ⁇ 0.3%, Sn: ⁇ 0.3%, Mo: ⁇ 0.5%, Cr: ⁇ 1%, V : ⁇ 0.3%, Ti: ⁇ 0.06%, Nb: ⁇ 0.06%, rare earth metals ⁇ 0.05%, Ca: ⁇ 0.05%, Zr: ⁇ 0.05%,
  • the ratio of Si to Al should be set so that the Condition 0.4 (%) ⁇ Si + 0.8 Al (%) ⁇ 2.0% is satisfied.
  • the volume percentage of retained austenite in the steel sheet should be 2 to 20%.
  • the ratio of Ni, Cu, Co, Sn and Si, Al in 0.5 ⁇ m of the steel sheet surface layer is set so that the condition Ni + Cu + Co + Sn (%) ⁇ 1/4 Si + 1/3 Al (%), a Zn-plated layer specifically alloyed should adhere particularly well to the flat steel product.
  • the plating layer comprises Al: ⁇ 1%, optionally Fe: 8 to 15% and optionally one or more constituents selected from Mn: ⁇ 0.02%, Pb: ⁇ 0.01%, Fe: ⁇ 0.2% ,
  • the Zn layer may also be Sb: ⁇ 0.01%, Ni: ⁇ 3.0%, Cu: ⁇ 1.5%, Sn: ⁇ 0.1%, Co: ⁇ 0.1%, Cd: ⁇ 0.01%, and Cr: ⁇ 0.05%.
  • the principle used according to this prior art thus presupposes certain minimum contents of Si and Al, whereas the combination of the Mn and B contents plays only a minor role. Instead, like the one in the EP 1 160 346 A1 specified embodiments and explanations show, the Cu content of particular importance.
  • a method for producing a higher strength plate which is at least 70 mm thick and which is composed of a steel containing (in% by weight) 0.04-0.20% C, 0, 0002-0.0-03 % B and 0, 0003 - 0, 0025% Ca, balance iron and unavoidable impurities, the carbon content being C% in relation to the boron content B% of Steel is set so that the condition 0.1 ⁇ C% + 100 x B% ⁇ 0.32 is met. At the same time certain conditions are to be met for the bainite content of the steel sheet.
  • the addition of Ca is intended to improve the toughness in the heat-affected zone of a weld, which is produced when welding the heavy plate. It is obvious that heavy plates of this type are neither suitable for their range of characteristics nor their dimensions for hot pressing.
  • the invention therefore an object of the invention to provide a use of a flat steel product, which is due to its composition and properties particularly suitable for the production of components that in terms of in practice from such flat steel products , like steel strips or steel sheets, manufactured components certainly meet requirements.
  • a method for producing such a flat steel product should be specified.
  • this object has been achieved by using a manganese-boron steel according to the invention for the production of a hot-pressed component, which contains (in% by weight) 0.1-0.20% C, 0.05 - 0.30% Si, 0.8 - 1.8% Mn, 0.5 - 1.8% Ni, up to 0.015% P, up to 0.003% S, 0.0002 - 0.0080% B and the remainder contains iron and unavoidable impurities.
  • the MnB steel of the present invention may optionally contain 0.01-0.1% Ti, 0.01-0.05% Al, 0.002-0.005% N each in combination or alone.
  • a component which is hot-pressed under the use of such a flat steel product according to the invention has a tensile strength R m of at least 1,000 MPa and has an elongation at break A 80 of more than 10%.
  • MnB steel used according to the invention contains contents of Ni in order to significantly increase the elongation at break and toughness of components obtained from the steel used according to the invention after a hardened state obtained by hot press forming.
  • the presence of Ni improves the hardenability of MnB steels used according to the invention, so that the Mn contents could be reduced and the addition of critical Cr in terms of its influence on the residual ductility could be dispensed with.
  • the C content of steels used according to the invention has also been modified in such a way that the martensite hardness produced in the course of hot pressing is reduced or the components obtained after hot pressing have a bainitic structure in favor of improved extensibility, by virtue of the toughness and elongation at break of steel used according to the invention produced components is also positively influenced. If emphasis is placed on increased strength of the steel used according to the invention, in the Under the invention, the C content in the range of 0.15 to 0.20 wt .-% can be adjusted. In contrast, C contents of 0.10-0.15% by weight have proved to be useful for a less solid, but particularly good residual ductility and toughness, even after the hot-pressing molding and the steel having hardened therein.
  • Mn content By modifying the Mn content, it is also possible to influence the residual elongation and hardenability of the steel used according to the invention. Reduced Mn contents in the range of 0.8-1.6% by weight of improved residual extensibility are beneficial, while at Mn contents of 1.0-1.8% by weight improved hardenability of the inventively used Steel is present.
  • the residual elongation and the hardenability of the steel used according to the invention can be adjusted.
  • lower Ni contents lying in the range of 0.5-1.8% by weight, in particular in the range of 0.8-1.5% by weight lead to higher hardenability and at the same time to improved toughness, whereby together an improved residual elongation is achieved.
  • a steel used according to the invention with lower strength but with further improved residual elongation after hardening achieved during hot deformation has (in% by weight) 0.10-0.15% C, 0.05-0.30% Si , 0 - 1.8% Mn, 0.8 - 1.8% Ni, max. 0.015% P, max. 0.003% S, 0.0002 - 0.0080% B and the remainder iron and unavoidable impurities.
  • the hardening effect of boron in a steel used according to the invention occurs in particular when the B content is at least 0.0008% by weight.
  • the flat steel product used according to the invention may be a hot-rolled or cold-rolled steel strip or sheet.
  • composite steel strips or steel sheets used according to the invention are outstandingly suitable for surface refinement by application of a metallic coating. This can be applied for example by Feueralumtechnik or hot dip galvanizing and by a combination of these methods.
  • the corrosion protection respectively obtained by the metallic coating can additionally be improved by additionally providing the flat steel product used according to the invention with an organic or inorganic coating.
  • the resulting hot strip can be descaled for further processing in a conventional manner, for example by pickling. If the resulting flat steel product is to be fed directly as a hot strip of the forming to a component, can now be applied as corrosion protection, a metallic coating in the manner already described above. Alternatively, the hot strip may be cold rolled after the pickling, if necessary, to cold strip. The degrees of cold rolling achieved during cold rolling, preferably without intervening intermediate annealing, should be at least 40% in order to ensure complete recrystallization.
  • the steel melts S1, S2 have subsequently been cast into thin slabs in a likewise conventional cast roll mill.
  • Hot strips were then hot rolled from the resulting thin slabs.
  • the hot rolling end temperature was 850 ° C.
  • the obtained hot strips were coiled at a coiling temperature which was 560 ° C.
  • cold rolling degree reduction in thickness / thickness of the cold rolled hot strip achieved by the cold rolling
  • samples separated from the obtained cold tapes were coated with a metallic coating by fire aluminizing.
  • the metallic coating consisted of 89-92% by weight of Al, balance Si.
  • a second sample was fire-aluminized with a coating containing 55% by weight of Al, 43.4% by weight of Zn and 1.6% by weight of Si.
  • the samples thus treated have been hot stamped into body parts.
  • the components thus obtained had tensile strengths of more than 1,000 MPa and an elongation at break A 80 of at least 10%.
  • the lower yield strength could be increased by at least 80 MPa, without the strength and elongation at break of the components changed.
  • a martensitic, a bainitic or a mixed martensitic-bainitic structure was present in the components obtained.

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

Abstract

Manganese-boron-steel (I) comprises (in wt.%): carbon (0.1-0.2); silicon (0.05-0.3), manganese (0.8-1.8), nickel (0.5-.8); phosphorus (= 0.015), sulfur (= 0.003), boron (0.0002-0.008), optionally titanium (0.01-0.1), optionally aluminum (0.01-0.05), optionally nitrogen (0.002-0.005) and rest of iron and unavoidable impurities. Independent claims are included for: (1) a flat steel product comprising (I); and (2) a process for the preparation of the steel product comprising smelting a steel melt containing (I), pouring the melt to slabs or thin slabs, thermally-rolling the slabs or thin slabs at 850-900[deg]C to form a hot-rolled strip and hasping the hot-rolled strip at 560-600[deg]C.

Description

Die Erfindung betrifft eine Verwendung eines aus einem Mangan-Bor-Stahl hergestellten Stahlflachprodukts, und ein Verfahren zu dessen Herstellung.The invention relates to a use of a steel flat product produced from a manganese-boron steel, and a method for its production.

MnB-Stähle der erfindungsgemäß verwendeten Art werden insbesondere im Bereich des Automobilbaus für die Herstellung von Bauteilen verwendet, die neben einem geringen Gewicht eine hohe Festigkeit besitzen sollen.MnB steels of the type used according to the invention are used in particular in the field of automobile construction for the production of components which are said to have a high strength in addition to a low weight.

Die an das Verformungsverhalten von modernen Automobilen im Crash-Fall gestellten hohen Sicherheitsanforderungen können heutzutage durch Verwendung von höherfesten Stählen zur Herstellung der bei einem Unfall für das Verformungsverhalten der Fahrzeug-Karosserie und der besonders kritischen Bauteile erfüllt werden. Problematisch ist dabei allerdings, dass hochfeste Stähle in der Regel eine unzureichende Umformbarkeit aufweisen und zum Rückfedern bei ihrer Kaltverformung zu dem jeweiligen Bauteil neigen.The high safety requirements placed on the deformation behavior of modern automobiles in the event of a crash today can be met by using higher-strength steels for producing the deformation behavior of the vehicle bodywork and the particularly critical components in the event of an accident. The problem is, however, that high-strength steels usually have insufficient formability and tend to spring back in their cold deformation to the respective component.

Dieses Problem wird in der Praxis dadurch bewältigt, dass aus höherfesten Stählen erzeugte Bleche im warmen Zustand in so genannten "Warmpressen" zum jeweiligen Bauteil verformt werden. Diese Vorgehensweise hat sich bewährt und erlaubt die Erzeugung auch von komplexer geformten Karosserie- und Fahrwerksteilen aus hochfesten Stählen.This problem is overcome in practice by the fact that sheets produced from higher-strength steels are deformed to the respective component in the warm state in so-called "hot pressing". This approach has been proven and allows the production of complex shaped body and chassis parts made of high-strength steels.

Als besonders gut geeignet für die Warmpressverformung haben sich Mangan-Bor-Stähle der hier in Rede stehenden Art erwiesen, die in der EN 10083-3 genormt sind. Diese Stähle besitzen eine gute Härtbarkeit, die beim Warmpressen eine sichere Prozessführung erlaubt und durch die es auf wirtschaftliche Weise möglich ist, im Zuge der Warmverformung eine Martensithärtung noch im Werkzeug ohne zusätzliche Kühlung zu bewirken.Manganese-boron steels of the type in question, which are standardized in EN 10083-3, have proven particularly suitable for the hot-pressing deformation. These steels have a good hardenability, which allows safe process control during hot pressing and by which it is economically possible to effect a martensite hardening in the mold without additional cooling during the hot deformation.

Ein für die voranstehend zusammengefassten Zwecke in der Praxis bewährter MnB-Stahl ist unter der Bezeichnung "22MnB5" bekannt und hat im Stahlschlüssel, Ausgabe 2004, die Werkstoffnummer 1.5528 erhalten. Typischerweise enthält auf dem Markt erhältlicher 22MnB5-Stahl neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) 0,220 - 0,250 % C, 1, 2 - 1,4 % Mn, 0, 2 - 0,3 % Si, bis zu 0,02 % P, bis zu 0,005 % S, 0,020 - 0,050 % Al, 0,020 - 0,050 % Ti, 0,11 - 0,2 % Cr, 0,002 - 0,0035 % B sowie jeweils bis zu 0,1 % Mo, Cu und Ni (Werkstoffdatenblatt 11-112 der Salzgitter Flachstahl GmbH, Ausgabe November 2005).A MnB steel proven in practice for the purposes summarized above is known as "22MnB5" and has been given the material number 1.5528 in the steel key, 2004 edition. Typically, 22MnB5 steel on the market contains, in addition to iron and unavoidable impurities (in wt%), 0.220-0.250% C, 1.2-1.4% Mn, 0.2-2.3% Si, up to 0 , 02% P, up to 0.005% S, 0.020-0.050% Al, 0.020-0.050% Ti, 0.11-0.2% Cr, 0.002-0.0035% B and in each case up to 0.1% Mo, Cu and Ni (Material Data Sheet 11-112 of Salzgitter Flachstahl GmbH, November 2005 edition).

Für entsprechend zusammengesetzte, warmgewalzte und mit einer Al-Beschichtung versehene Stahlbleche ist in der EP 0 971 044 B1 eine Legierungsvorschrift angegeben, gemäß der ein MnB-Stahl neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) einen Kohlenstoffgehalt von mehr als 0,20 %, jedoch weniger als 0,5 %, einen Mangangehalt von mehr als 0,5 %, jedoch weniger als 3 %, einen Siliziumgehalt von mehr als 0,1 %, jedoch weniger als 0,5 %, einen Chromgehalt von mehr als 0,01 % jedoch weniger als 1 %, einen Titangehalt von weniger als 0,2 %, einen Aluminiumgehalt von weniger als 0,1 %, einen Phosphorgehalt von weniger als 0,1 %, einen Schwefelgehalt von weniger als 0,05 % und einen Borgehalt von mehr als 0,0005 %, jedoch weniger als 0,08 % aufweisen soll. Ein in der EP 0 971 044 B1 als Ausführungsbeispiel angegebenes, mit einer Al-Beschichtung versehenes Stahlblech weist dementsprechend (in Gew.-%) 0,21 % C, 1,14 % Mn, 0,020 % P, 0,0038 % S, 0,25 % Si, 0,04 % Al, 0,009 % Cu, 0,020 % Ni, 0,18 % Cr, 0,0040 % N, 0,032 % Ti, 0,003 % B und 0,0050 % Ca auf. Nach einer Wärmebehandlung soll die Festigkeit dieses Stahlblechs mehr als 1500 MPa betragen.For appropriately composite, hot-rolled and provided with an Al-coated steel sheets is in the EP 0 971 044 B1 an alloying specification according to which a MnB steel, in addition to iron and unavoidable impurities (in% by weight), has a carbon content of more than 0.20%, but less than 0.5%, 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%. An Indian EP 0 971 044 B1 As an exemplary embodiment, provided with an Al coating steel sheet has accordingly (in wt .-%) 0.21% C, 1.14% Mn, 0.020% P, 0.0038% S, 0.25% Si, 0, 04% Al, 0.009% Cu, 0.020% Ni, 0.18% Cr, 0.0040% N, 0.032% Ti, 0.003% B and 0.0050% Ca. After a heat treatment, the strength of this steel sheet should be more than 1500 MPa.

Des Weiteren ist aus der JP 2004-211197 ein Stahlblech für Strukturbauteile von Automobilkarosserien bekannt, das neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) 0, 20 - 0,35 % C, 0, 01 - 1,0 % Si, 0,3 - 2,0 % Mn, 0,01 - 0,10 % Al, mehr als 1 - 5 % Ni, 0,005 - 0,1 % Ti, 0,0005 - 0,005 % B, 0,001 - 0,01 % N, bis zu 0,02 % P, bis zu 0,01 % S, bis zu 0,01 % O aufweist. In dem bei dieser Legierung für die Ti- und N-Gehalte die Bedingung "Ti/47.88 - N/14.01 ≤ 0,001", für die Al- und N-Gehalte die Bedingung "0 ≤ Al/26.98 - N/14.01 ≤ 0,0015" sowie für die C-, Si-, Mn-, Ni-, Cr-, Cu-, S- und P-Gehalte die Bedingung "-28.8 x C2 + 38.0 x C + 1.7 x Si + 7.5 x Mn + 1.4 x Ni + 43.2 x Cr + 8.7 x Cu + 53.5 x S + 57.1 x P + 17.9 ≥ 35" eingehalten werden, soll das betreffende Stahlblech eine besonders gute Härtbarkeit nach der Warmverformung bei gleichzeitig besonders gutem Verhalten bei einem schlagartigen Stoß besitzen.Furthermore, from the JP 2004-211197 a steel sheet for structural components of automobile bodies, which in addition to iron and unavoidable impurities (in wt .-%) 0, 20 - 0.35% C, 0, 01 - 1.0% Si, 0.3 - 2.0% Mn , 0.01-0.10% Al, more than 1-5% Ni, 0.005-0.1% Ti, 0.0005-0.005% B, 0.001-0.01% N, up to 0.02% P , up to 0.01% S, up to 0.01% O. In the case of this alloy, for the Ti and N contents, the condition "Ti / 47.88 - N / 14.01 ≤ 0.001", for the Al and N contents, the condition "0 ≤ Al / 26.98 - N / 14.01 ≤ 0, 0015 "and for the C, Si, Mn, Ni, Cr, Cu, S and P contents the condition" -28.8 x C 2 + 38.0 x C + 1.7 x Si + 7.5 x Mn + 1.4 x Ni + 43.2 x Cr + 8.7 x Cu + 53.5 x S + 57.1 x P + 17.9 ≥ 35 ", the steel sheet in question should have a particularly good hardenability after hot deformation with at the same time particularly good behavior in the event of a sudden impact.

Den voranstehend genannten, konventionellen MnB-Stählen gemeinsam ist, dass sie zwar jeweils hohe Festigkeiten und eine gute Härtbarkeit aufweisen. Ihre hohe Festigkeit nach dem Warmpressen ergibt sich dabei durch den im Martensitgitter gelösten Kohlenstoff, während ihre gute Härtbarkeit maßgeblich durch die Mn- und Cr- Gehalte und ergänzt durch B bestimmt wird.What is common to the above-mentioned conventional MnB steels is that they each have high strengths and good hardenability. Their high strength after hot pressing results from the carbon dissolved in the martensite grid, while their good hardenability is largely determined by the Mn and Cr contents and supplemented by B.

Die Restbruchdehnung der bekannten Stähle liegt allerdings typischerweise nur bei 5 - 6 %. Um den immer weiter steigenden Anforderungen an das Crash-Verhalten von Fahrzeugkarosserien gerecht zu werden, werden jedoch Stähle benötigt, die neben einer hohen Festigkeit auch ein verbessertes Dehnungsverhalten des aus einem solchen Stahl gefertigten Bauteils nach dem Warmpressen aufweisen.The residual fracture strain of the known steels, however, is typically only 5-6%. In order to meet the ever-increasing demands on the crash behavior of vehicle bodies, however, steels are needed, in addition to a high strength and an improved elongation behavior of the manufactured from such a steel component after hot pressing.

Neben dem voranstehend diskutierten Stand der Technik sind aus der EP 1 160 346 A1 ein hochfestes feuerverzinktes Stahlblech mit ausgezeichneter Plattierungshaftung und Pressformbarkeit sowie ein Verfahren zur Herstellung eines solchen Stahlblechs beschrieben. Das Stahlblech besteht dabei aus einem Stahl, der neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) C: 0,05 bis 0,2 %, Si: 0,2 bis 2,0 %, Mn: 0,2 bis 2,5 %, Al: 0,01 bis 1,5 %, Ni: 0,73 bis 5,0 %, P: < 0,03 % und S: < 0,02 %, sowie optional einen oder mehrere der folgenden Bestandteile Cu: < 0,2 %, B: 0,0002 bis 0,01 %, Co: < 0,3 %, Sn: < 0,3 %, Mo: < 0,5 %, Cr: < 1 %, V: < 0, 3. %, Ti: < 0,06 %, Nb: < 0,06 %, Seltenerdmetalle < 0,05 %, Ca: < 0,05 %, Zr: < 0,05 %, Mg: < 0,05 %, Zn: < 0,02 %, W: < 0,05 %, As: < 0,02 %, N: < 0,03 % und O: < 0,05 % enthält. Gleichzeitig soll das Verhältnis von Si zu Al so eingestellt sein, dass die Bedingung 0,4 (%) ≤ Si + 0,8 Al (%) ≤ 2,0 % erfüllt ist. Ebenso soll der Volumenprozentsatz von Restaustenit im Stahlblech 2 bis 20 % betragen. Indem dann an der Stahlblechoberfläche das Verhältnis von Ni, Cu, Co, Sn und Si, Al in 0,5 µm der Stahlblech-Oberflächenschicht so eingestellt ist, dass die Bedingung Ni + Cu + Co + Sn (%) ≥ 1/4 Si + 1/3 Al (%) gilt, soll eine in bestimmter Weise legierte Zn-Plattierungsschicht besonders gut auf dem Stahlflachprodukt haften. Dazu weist die Plattierungsschicht Al: ≤ 1 %, optional Fe: 8 bis 15 % sowie optional einen oder mehrere Bestandteile, ausgewählt aus Mn: < 0,02 %, Pb: < 0,01 %, Fe: < 0,2 % auf. Wenn die optionalen 8 bis 15 % Fe nicht in der Zn-Plattierungsschicht enthalten sind, kann die Zn-Schicht auch Sb: < 0, 01 %, Ni: < 3,0 %, Cu: < 1,5 %, Sn: < 0,1 %, Co: < 0,1 %, Cd: < 0,01 % und Cr: < 0,05 % aufweisen. Das gemäß diesem Stand der Technik genutzte Prinzip setzt folglich gewisse Mindestgehalte an Si und Al voraus, wogegen die Kombination der Mn- und B-Gehalte nur eine untergeordnete Rolle spielt. Stattdessen kommt, wie die in der EP 1 160 346 A1 angegebenen Ausführungsbeispiele und Erläuterungen zeigen, dem Cu-Gehalt eine besondere Bedeutung zu.In addition to the above-discussed prior art are from the EP 1 160 346 A1 A high-strength hot-dip galvanized steel sheet excellent in plating adhesion and press-formability, and a method for producing such a steel sheet are described. The steel sheet consists of a steel, which in addition to iron and unavoidable impurities (in wt .-%) C: 0.05 to 0.2%, Si: 0.2 to 2.0%, Mn: 0.2 to 2 , 5%, Al: 0.01 to 1.5%, Ni: 0.73 to 5.0%, P: <0.03% and S: <0.02%, and optionally one or more of the following ingredients Cu: <0.2%, B: 0.0002 to 0.01%, Co: <0.3%, Sn: <0.3%, Mo: <0.5%, Cr: <1%, V : <0.3%, Ti: <0.06%, Nb: <0.06%, rare earth metals <0.05%, Ca: <0.05%, Zr: <0.05%, Mg: < 0.05%, Zn: <0.02%, W: <0.05%, As: <0.02%, N: <0.03%, and O: <0.05%. At the same time, the ratio of Si to Al should be set so that the Condition 0.4 (%) ≦ Si + 0.8 Al (%) ≦ 2.0% is satisfied. Likewise, the volume percentage of retained austenite in the steel sheet should be 2 to 20%. Then, on the steel sheet surface, the ratio of Ni, Cu, Co, Sn and Si, Al in 0.5 μm of the steel sheet surface layer is set so that the condition Ni + Cu + Co + Sn (%) ≥ 1/4 Si + 1/3 Al (%), a Zn-plated layer specifically alloyed should adhere particularly well to the flat steel product. For this purpose, the plating layer comprises Al: ≦ 1%, optionally Fe: 8 to 15% and optionally one or more constituents selected from Mn: <0.02%, Pb: <0.01%, Fe: <0.2% , When the optional 8 to 15% Fe is not contained in the Zn plating layer, the Zn layer may also be Sb: <0.01%, Ni: <3.0%, Cu: <1.5%, Sn: < 0.1%, Co: <0.1%, Cd: <0.01%, and Cr: <0.05%. The principle used according to this prior art thus presupposes certain minimum contents of Si and Al, whereas the combination of the Mn and B contents plays only a minor role. Instead, like the one in the EP 1 160 346 A1 specified embodiments and explanations show, the Cu content of particular importance.

Schließlich ist aus der JP 2005-336541 ein Verfahren zur Herstellung eines höherfesten Grobblechs bekannt, das mindestens 70 mm dick ist und das aus einem Stahl zusammengesetzt ist, der (in Gew.-%) 0,04 - 0,20 % C, 0, 0002 - 0, 0-03 % B und 0, 0003 - 0, 0025 % Ca, Rest Eisen und unvermeidbare Verunreinigungen aufweist, wobei der Kohlenstoffgehalt C% im Verhältnis zum Borgehalt B% des Stahls so eingestellt ist, dass die Bedingung 0,1 ≤ C% + 100 x B% ≤ 0,32 erfüllt ist. Gleichzeitig sollen für den Bainit-Anteil des Stahlblechs bestimmte Bedingungen erfüllt sein. Durch die Zugabe von Ca soll dabei die Zähigkeit in der Wärmeeinflusszone einer Schweißnaht verbessert sein, die beim Verschweißen des Grobblechs entsteht. Es ist offensichtlich, dass Grobbleche dieser Art weder von ihrem Eigenschaftsspektrum noch von ihren Abmessungen zum Warmpressen geeignet sind.Finally, out of the JP 2005-336541 a method is known for producing a higher strength plate which is at least 70 mm thick and which is composed of a steel containing (in% by weight) 0.04-0.20% C, 0, 0002-0.0-03 % B and 0, 0003 - 0, 0025% Ca, balance iron and unavoidable impurities, the carbon content being C% in relation to the boron content B% of Steel is set so that the condition 0.1 ≤ C% + 100 x B% ≤ 0.32 is met. At the same time certain conditions are to be met for the bainite content of the steel sheet. The addition of Ca is intended to improve the toughness in the heat-affected zone of a weld, which is produced when welding the heavy plate. It is obvious that heavy plates of this type are neither suitable for their range of characteristics nor their dimensions for hot pressing.

Ausgehend von dem voranstehend erläuterten Stand der Technik lag der Erfindung daher die Aufgabe zugrunde, eine Verwendung eines Stahlflachprodukts anzugeben, , das sich aufgrund seiner Zusammensetzung und Eigenschaften besonders zur Herstellung von Bauteilen eignet, die den im Hinblick auf die in der Praxis an aus solchen Stahlflachprodukten, wie Stahlbändern oder Stahlblechen, hergestellten Bauteilen gestellten Anforderungen sicher genügen. Darüber hinaus sollte ein Verfahren zur Herstellung eines solchen Stahlflachproduktes angegeben werden.Based on the above-described prior art, the invention therefore an object of the invention to provide a use of a flat steel product, which is due to its composition and properties particularly suitable for the production of components that in terms of in practice from such flat steel products , like steel strips or steel sheets, manufactured components certainly meet requirements. In addition, a method for producing such a flat steel product should be specified.

In Bezug auf die Verwendung ist diese Aufgabe dadurch gelöst worden, dass zur Herstellung eines warmgepressten Bauteils, erfindungsgemäß ein Mangan-Bor-Stahl verwendet wird, der (in Gew.-%) 0,1 - 0,20 % C, 0,05 - 0,30 % Si, 0,8 - 1,8 % Mn, 0,5 - 1,8 % Ni, bis zu 0,015 % P, bis zu 0,003 % S,
0,0002 - 0,0080 % B und als Rest Eisen und unvermeidbare Verunreinigungen enthält. Zusätzlich kann der erfindungsgemäße MnB-Stahl wahlweise 0,01 - 0,1 % Ti, 0,01 - 0,05 % Al, 0,002 - 0,005 % N jeweils in Kombination oder alleine enthalten. Ein unter erfindungsgemäßer Verwendung eines solchen Stahlflachprodukts warmgepresstes Bauteil weist eine Zugfestigkeit Rm von mindestens 1.000 MPa auf und besitzt eine Bruchdehnung A80 von mehr als 10 %.With regard to use, this object has been achieved by using a manganese-boron steel according to the invention for the production of a hot-pressed component, which contains (in% by weight) 0.1-0.20% C, 0.05 - 0.30% Si, 0.8 - 1.8% Mn, 0.5 - 1.8% Ni, up to 0.015% P, up to 0.003% S,
0.0002 - 0.0080% B and the remainder contains iron and unavoidable impurities. In addition, the MnB steel of the present invention may optionally contain 0.01-0.1% Ti, 0.01-0.05% Al, 0.002-0.005% N each in combination or alone. A component which is hot-pressed under the use of such a flat steel product according to the invention has a tensile strength R m of at least 1,000 MPa and has an elongation at break A 80 of more than 10%.

Im Gegensatz zu den konventionell für das Warmpressen verwendeten MnB-Stählen, bei denen die mechanischen Eigenschaften maßgeblich durch die C-, Mn- und Cr-Gehalte bestimmt werden, ist bei dem erfindungsgemäßen Legierungskonzept auf Gehalte an Cr verzichtet worden.In contrast to the MnB steels conventionally used for hot pressing, in which the mechanical properties are largely determined by the C, Mn and Cr contents, contents of Cr have been dispensed with in the alloying concept according to the invention.

Stattdessen enthält erfindungsgemäß verwendeter MnB-Stahl Gehalte an Ni, um die Bruchdehnung und Zähigkeit von aus dem erfindungsgemäß verwendeten Stahl hergestellten Bauteilen nach einem Warmpressverformen erhaltenen gehärteten Zustand maßgeblich zu steigern. Gleichzeitig verbessert die Anwesenheit von Ni die Härtbarkeit erfindungsgemäß verwendeter MnB-Stähle, so dass die Mn-Gehalte reduziert und auf die Zugabe von hinsichtlich seines Einflusses auf die Restdehnbarkeit kritischem Cr verzichtet werden konnte.Instead, MnB steel used according to the invention contains contents of Ni in order to significantly increase the elongation at break and toughness of components obtained from the steel used according to the invention after a hardened state obtained by hot press forming. At the same time, the presence of Ni improves the hardenability of MnB steels used according to the invention, so that the Mn contents could be reduced and the addition of critical Cr in terms of its influence on the residual ductility could be dispensed with.

Der C-Gehalt erfindungsgemäß verwendeter Stähle ist zudem so modifiziert worden, dass zu Gunsten einer verbesserten Dehnbarkeit die im Zuge des Warmpressens erzeugte Martensithärte vermindert oder das nach dem Warmpressen erhaltene Bauteile ein bainitisches Gefüge aufweist, durch dass die Zähigkeit und Bruchdehnung von aus erfindungsgemäß verwendetem Stahl erzeugten Bauteilen ebenfalls positiv beeinflusst wird. Wird auf eine erhöhte Festigkeit des erfindungsgemäß verwendeten Stahls Wert gelegt, kann im Rahmen der Erfindung der C-Gehalt im Bereich von 0,15 - 0,20 Gew.-% eingestellt werden. Für einen weniger festen, jedoch eine besonders gute Restdehnbarkeit und Zähigkeit auch nach der Warmpressverfomung und der in deren Zuge bewirkten Härtung aufweisenden Stahl haben sich demgegenüber C-Gehalte von 0,10 - 0,15 Gew.-% als zweckmäßig erwiesen.The C content of steels used according to the invention has also been modified in such a way that the martensite hardness produced in the course of hot pressing is reduced or the components obtained after hot pressing have a bainitic structure in favor of improved extensibility, by virtue of the toughness and elongation at break of steel used according to the invention produced components is also positively influenced. If emphasis is placed on increased strength of the steel used according to the invention, in the Under the invention, the C content in the range of 0.15 to 0.20 wt .-% can be adjusted. In contrast, C contents of 0.10-0.15% by weight have proved to be useful for a less solid, but particularly good residual ductility and toughness, even after the hot-pressing molding and the steel having hardened therein.

Durch eine Modifizierung des Mn-Gehaltes kann zudem die Restdehnung und Härtbarkeit des erfindungsgemäß verwendeten Stahls beeinflusst werden. Dabei sind reduzierte, im Bereich von 0,8 - 1,6 Gew.-% liegende Mn-Gehalte einer verbesserten Restdehnbarkeit zuträglich, während bei Mn-Gehalten von 1,0 - 1,8 Gew.-% eine verbesserte Härtbarkeit des erfindungsgemäß verwendeten Stahls vorliegt.By modifying the Mn content, it is also possible to influence the residual elongation and hardenability of the steel used according to the invention. Reduced Mn contents in the range of 0.8-1.6% by weight of improved residual extensibility are beneficial, while at Mn contents of 1.0-1.8% by weight improved hardenability of the inventively used Steel is present.

Ebenso kann durch eine geeignete Einstellung des Nickel-Gehalts die Restdehnung und die Härtbarkeit des erfindungsgemäß verwendeten Stahls eingestellt werden. So führen niedrigere, im Bereich von 0,5 - 1,8 Gew.-%, insbesondere im Bereich von 0,8 - 1,5 Gew.-%, liegende Ni-Gehalte zu einer höheren Härtbarkeit und zugleich zu einer verbesserten Zähigkeit, wodurch zusammen eine verbesserte Restdehnung erzielt wird.Likewise, by a suitable adjustment of the nickel content, the residual elongation and the hardenability of the steel used according to the invention can be adjusted. Thus, lower Ni contents lying in the range of 0.5-1.8% by weight, in particular in the range of 0.8-1.5% by weight, lead to higher hardenability and at the same time to improved toughness, whereby together an improved residual elongation is achieved.

Ein erfindungsgemäß verwendeter Stahl mit hoher Festigkeit und verbesserter Restdehnung nach einer im Zuge einer Warmverformung erzielten Härtung weist dementsprechend (in Gew.-%) 0,15 - 0,2 % C, 0,05 - 0,30 % Si, 0,8- 1,6 % Mn, 0,5 - 1,0 % Ni, max. 0,015 % P, max. 0,003 % S, 0,0002 - 0,0080 % B sowie als Rest Eisen und unvermeidbare Verunreinigungen auf.A steel used according to the invention with high strength and improved residual elongation after hardening achieved during hot deformation accordingly has (in% by weight) 0.15-0.2% C, 0.05-0.30% Si, 0.8 - 1.6% Mn, 0.5 - 1.0% Ni, max. 0.015% P, max. 0.003% S, 0.0002 - 0.0080% B and the remainder iron and unavoidable impurities.

Ein erfindungsgemäß verwendeter Stahl mit geringerer Festigkeit, jedoch weiter verbesserter Restdehnung nach einer im Zuge einer Warmverformung erzielten Härtung weist demgegenüber (in Gew.-%) 0,10 - 0,15 % C, 0, 05 - 0,30 % Si, 1, 0 - 1,8 % Mn, 0,8 - 1,8 % Ni, max. 0,015 % P, max. 0,003 % S, 0,0002 - 0,0080 % B sowie als Rest Eisen und unvermeidbare Verunreinigungen auf.In contrast, a steel used according to the invention with lower strength but with further improved residual elongation after hardening achieved during hot deformation has (in% by weight) 0.10-0.15% C, 0.05-0.30% Si , 0 - 1.8% Mn, 0.8 - 1.8% Ni, max. 0.015% P, max. 0.003% S, 0.0002 - 0.0080% B and the remainder iron and unavoidable impurities.

Unabhängig davon, welche der verschiedenen im Rahmen der erfindungsgemäß verwendeten Legierung möglichen Varianten zur Anwendung kommen, tritt die härtesteigernde Wirkung von Bor in einem erfindungsgemäß verwendeten Stahl insbesondere dann ein, wenn der B-Gehalt mindestens 0,0008 Gew.-% beträgt.Regardless of which of the various possible variants of the alloy used according to the invention are used, the hardening effect of boron in a steel used according to the invention occurs in particular when the B content is at least 0.0008% by weight.

Bei dem erfindungsgemäß verwendeten Stahlflachprodukt kann es sich um ein warm- oder kaltgewalztes Stahlband oder - blech handeln. Dabei eignen sich erfindungsgemäß verwendete zusammengesetzte Stahlbänder oder Stahlbleche hervorragend für eine Oberflächenveredelung durch Auftrag einer metallischen Beschichtung. Diese kann beispielsweise durch Feueraluminierung oder Feuerverzinkung sowie durch eine Kombination dieser Verfahren aufgebracht werden. Darüber hinaus kann der durch die metallische Beschichtung jeweils erhaltene Korrosionsschutz zusätzlich dadurch verbessert werden, dass das erfindungsgemäß verwendete Stahlflachprodukt zusätzlich mit einer organischen oder anorganischen Beschichtung versehen wird.The flat steel product used according to the invention may be a hot-rolled or cold-rolled steel strip or sheet. In this case, composite steel strips or steel sheets used according to the invention are outstandingly suitable for surface refinement by application of a metallic coating. This can be applied for example by Feueralumierung or hot dip galvanizing and by a combination of these methods. In addition, the corrosion protection respectively obtained by the metallic coating can additionally be improved by additionally providing the flat steel product used according to the invention with an organic or inorganic coating.

Hinsichtlich des Herstellverfahrens ist die oben genannte Aufgabe schließlich durch ein Verfahren zur Herstellung eines erfindungsgemäß verwendeten Stahlflachprodukts gelöst worden, bei dem folgende Arbeitschritte durchlaufen werden:

  • Erschmelzen einer der entsprechend der Zusammensetzung des erfindungsgemäß verwendeten Stahlflachproduktes zusammengesetzten Stahlschmelze,
  • Vergießen der Schmelze zu Brammen oder Dünnbrammen,
  • Warmwalzen der Brammen oder Dünnbrammen bei einer Warmwalzendtemperatur von 850 - 900 °C zu einem Warmband,
  • Haspeln des Warmbands bei Haspeltemperaturen von 560 - 600 °C.
With regard to the manufacturing process, the above object is finally achieved by a process for the preparation of a flat steel product used in accordance with the invention, in which the following working steps are carried out:
  • Melting one of the steel melt composed according to the composition of the flat steel product used according to the invention,
  • Casting the melt into slabs or thin slabs,
  • Hot rolling of the slabs or thin slabs at a hot rolling end temperature of 850 - 900 ° C into a hot strip,
  • Coiling of the hot strip at reel temperatures of 560 - 600 ° C.

Das erhaltene Warmband kann für die weitere Verarbeitung in an sich bekannter Weise beispielsweise durch Beizen entzundert werden. Sofern das erhaltene Stahlflachprodukt unmittelbar als Warmband der Umformung zu einem Bauteil zugeführt werden soll, kann nun als Korrosionsschutz eine metallische Beschichtung in der voranstehend bereits beschriebenen Weise aufgebracht werden. Alternativ kann das Warmband nach dem erforderlichenfalls durchgeführten Beizen zu Kaltband kaltgewalzt werden. Die beim Kaltwalzen bevorzugt ohne zwischengeschaltetes Zwischenglühen erzielten Kaltwalzgrade sollten mindestens 40 % betragen, um eine vollständige Rekristallisation zu gewährleisten.The resulting hot strip can be descaled for further processing in a conventional manner, for example by pickling. If the resulting flat steel product is to be fed directly as a hot strip of the forming to a component, can now be applied as corrosion protection, a metallic coating in the manner already described above. Alternatively, the hot strip may be cold rolled after the pickling, if necessary, to cold strip. The degrees of cold rolling achieved during cold rolling, preferably without intervening intermediate annealing, should be at least 40% in order to ensure complete recrystallization.

Nachfolgend wird die Erfindung anhand von Ausführungsbeispielen erläutert.The invention will be explained below with reference to exemplary embodiments.

In einem konventionellen Konverter sind zwei erfindungsgemäß verwendete Stahlschmelzen S1, S2 erschmolzen worden, deren Zusammensetzungen in Tabelle 1 angegeben sind. Zusätzlich ist in Tabelle 1 zum Vergleich die Zusammensetzung eines konventionellen 22MnB5-Stahls V angegeben.In a conventional converter, two molten steels S1, S2 used according to the invention have been melted, the compositions of which are given in Table 1. In addition, in Table 1, the composition of a conventional 22MnB5 steel V is shown for comparison.

Die Stahlschmelzen S1,S2 sind anschließend in einer ebenfalls konventionellen Gießwalzanlage zu Dünnbrammen vergossen worden.The steel melts S1, S2 have subsequently been cast into thin slabs in a likewise conventional cast roll mill.

Aus den so erhaltenen Dünnbrammen sind anschließend Warmbänder warmgewalzt worden. Die Warmwalzendtemperatur betrug dabei 850 °C. Anschließend sind die erhaltenen Warmbänder bei einer Haspeltemperatur gehaspelt worden, die bei 560 °C lag.Hot strips were then hot rolled from the resulting thin slabs. The hot rolling end temperature was 850 ° C. Subsequently, the obtained hot strips were coiled at a coiling temperature which was 560 ° C.

Nach dem Haspeln sind die Warmbänder gebeizt und zu Kaltbändern kaltgewalzt worden. Im Hinblick auf eine Minimierung der Produktionskosten erfolgte das Kaltwalzen ohne Zwischenglühung. Der im Zuge des Kaltwalzens erreichte Kaltverformungsgrad (Kaltwalzgrad = durch das Kaltwalzen erzielte Dickenabnahme / Dicke des kaltzuwalzenden Warmbands) lag bei 40 %.After coiling, the hot-rolled strips were pickled and cold-rolled to cold-rolled strips. With a view to minimizing production costs, cold rolling was carried out without intermediate annealing. The degree of cold deformation achieved in the course of cold rolling (cold rolling degree = reduction in thickness / thickness of the cold rolled hot strip achieved by the cold rolling) was 40%.

Anschließend wurden von den erhaltenen Kaltbändern abgeteilte Proben durch Feueraluminieren mit einer metallischen Beschichtung belegt. Bei einer ersten Probe bestand der metallische Überzug dabei aus 89 - 92 Gew.-% Al, Rest Si. Eine zweite Probe wurde mit einem Überzug, der 55 Gew.-% Al, 43,4 Gew.-% Zn und 1,6 Gew.-% Si enthielt, feueraluminiert.Subsequently, samples separated from the obtained cold tapes were coated with a metallic coating by fire aluminizing. In the case of a first sample, the metallic coating consisted of 89-92% by weight of Al, balance Si. A second sample was fire-aluminized with a coating containing 55% by weight of Al, 43.4% by weight of Zn and 1.6% by weight of Si.

Andere von den erhaltenen Kaltbändern abgeteilte Proben sind einer Feuerverzinkung unterzogen worden, bei der eine erste Probe mit einer Reinzinkschicht (Zn-Gehalt mindestens 99 Gew.-%) und eine zweite Probe mit einer Schicht aus 95 Gew.-% Zn, Rest Al belegt worden ist. Eine dritte Probe wurde in an sich ebenso bekannter Weise durch Galvanealing mit einer Reinzinkschicht beschichtet.Other samples separated from the obtained cold tapes were subjected to a hot-dip galvanizing process in which a first sample was coated with a zinc-zinc layer (Zn content at least 99% by weight) and a second sample with a layer of 95% by weight Zn, balance Al has been. A third sample was coated in a manner known per se by galvanic plating with a pure zinc coating.

Die so behandelten Proben sind durch Warmpressformen zu Karosseriebauteilen umgeformt worden. Die so erhaltenen Bauteile wiesen Zugfestigkeiten von jeweils mehr als 1.000 MPa und eine Bruchdehnung A80 von mindestens 10 % auf. Durch Auftrag eines durch Kataphorese-Tauch-Lackierung aufgebrachten Lackschicht mit anschließender Trocknung konnte die untere Streckgrenze um mindestens 80 MPa gesteigert werden, ohne dass die Festigkeit und Bruchdehnung der Bauteile sich änderte.The samples thus treated have been hot stamped into body parts. The components thus obtained had tensile strengths of more than 1,000 MPa and an elongation at break A 80 of at least 10%. By applying a paint layer applied by cataphoresis dip coating with subsequent drying, the lower yield strength could be increased by at least 80 MPa, without the strength and elongation at break of the components changed.

Abhängig von der jeweiligen Temperaturführung im für die Warmpressverformung verwendeten Werkzeug lag in den erhaltenen Bauteilen ein martensitisches, ein bainitisches oder ein gemischt martensitisches-bainitisches Gefüge vor.Depending on the respective temperature control in the tool used for the hot-pressing deformation, a martensitic, a bainitic or a mixed martensitic-bainitic structure was present in the components obtained.

In Diag. 1 sind die für die Stähle S1,S2 die nach dem Jominiy-Test berechneten Härteverläufe dem Härteverlauf des konventionell zusammengesetzten Stahls V gegenüber gestellt. Dabei ist die jeweilige Härte H über den jeweiligen Abstand A zur abgeschreckten Fläche aufgetragen. Tabelle 1 S1 S2 V C 0,20 0,15 0,233 Si 0,24 0,24 0,24 Mn 1,00 1,00 1,23 P < 0,015 < 0,015 0,018 S < 0,001 < 0,001 0,001 Al 0,03 0,03 0,035 N 0,003 0,003 0,0031 Ni 0,65 0,65 0,023 Ti 0,033 0,033 0,033 B 0,0025 0,0025 0,0022 Cr < 0,05 < 0,05 0,14

Figure imgb0001
In Diag. 1, for the steels S1, S2, the hardness profiles calculated according to the Jominiy test are compared with the hardness curve of the conventionally assembled steel V. The respective hardness H is plotted over the respective distance A to the quenched surface. Table 1 S1 S2 V C 0.20 0.15 0.233 Si 0.24 0.24 0.24 Mn 1.00 1.00 1.23 P <0.015 <0.015 0,018 S <0.001 <0.001 0.001 al 0.03 0.03 0,035 N 0,003 0,003 0.0031 Ni 0.65 0.65 0.023 Ti 0.033 0.033 0.033 B 0.0025 0.0025 0.0022 Cr <0.05 <0.05 0.14
Figure imgb0001

Claims (17)

  1. Use of a steel flat product produced from a manganese boron steel which contains (in wt. %) C: 0.1 - 0.20 %, Si: 0.05 - 0.30 %, Mn: 0.8 - 1.8 %, Ni: 0.5 - 1.8 %, P: ≤ 0.015 %, S: ≤ 0,003 %, B: 0.0002 - 0.0080 %
    and optionally one or more of the following elements Ti, Al and N according to the following proportions: Ti: 0.01 - 0.1 %, Al: 0.01 - 0.05 %, N: 0.002 - 0.005 %,
    the remainder being iron and unavoidable impurities, for manufacturing a hot-pressed component which has a tensile strength Rm of at least 1,000 MPa and possesses an elongation at fracture A80 of more than 10 %.
  2. Use according to Claim 1, characterised in that the steel contains 0.15 - 0.20 wt. % of carbon.
  3. Use according to Claim 1, characterised in that the steel contains 0.10 - 0.15 wt. % of carbon.
  4. Use according to any one of the preceding claims, characterised in that the steel contains 0.8 - 1.6 wt. % of manganese.
  5. Use according to any one of Claims 1 to 3, characterised in that the steel contains 1.0 - 1.8 wt. % of manganese.
  6. Use according to any one of the preceding claims, characterised in that the steel contains 0.5 - 1.0 wt. % of nickel.
  7. Use according to any one of Claims 1 to 5, characterised in that the steel contains 0.8 - 1.8 wt. % of nickel.
  8. Use according to any one of the preceding claims, characterised in that the steel contains at least 0.0008 wt. % of boron.
  9. Method for manufacturing a steel flat product for use according to any one of Claims 1 to 8 comprising the following production steps:
    - smelting a manganese boron steel melt which contains (in wt. %): C: 0.1 - 0.20 %, Si: 0.05 - 0.30 %, Mn: 0.8 - 1.8 %, Ni: 0.5 - 1.8 %, P: ≤ 0.015 %, S: ≤ 0,003 %, B: 0.0002 - 0.0080 %
    and optionally one or more of the following elements Ti, Al and N according to the following proportions: Ti: 0.01 - 0.1 %, Al: 0.01 - 0.05 %, N: 0.002 - 0.005 %,
    the remainder being iron and unavoidable impurities,
    - casting the melt into slabs or thin slabs,
    - hot-rolling the slabs or thin slabs at a hot-rolling final temperature of 850 - 900 °C into a hot-rolled strip,
    - coiling the hot-rolled strip at coiling temperatures of 560 - 600 °C.
  10. Method according to Claim 9, characterised in that the hot-rolled strip is de-scaled after the hot-rolling.
  11. Method according to Claim 9 or 10, characterised in that the hot-rolled strip is cold-rolled into a cold-rolled strip after the hot-rolling.
  12. Method according to Claim 11, characterised in that the cold-rolling is carried out without intermediate annealing.
  13. Method according to Claim 11 or 12, characterised in that the cold-rolling degree obtained when cold-rolling is at least 40 %.
  14. Method according to any one of Claims 9 to 13, characterised in that the de-scaled, hot-rolled strip or the cold-rolled strip is surface-coated by a metallic coating.
  15. Method according to Claim 14, characterised in that the de-scaled, hot-rolled strip or the cold-rolled strip is hot-dip aluminium-coated.
  16. Method according to Claim 14, characterised in that the de-scaled, hot-rolled strip or the cold-rolled strip is hot-dip galvanized.
  17. Method according to any one of Claims 14 to 16, characterised in that the de-scaled, hot-rolled strip or cold-rolled strip provided with the metallic coating is provided with an organic or inorganic coating.
EP06115075A 2006-06-07 2006-06-07 Use of a steel flat product produced from a manganese boron steel and method of its production Not-in-force EP1865086B1 (en)

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AT06115075T ATE477348T1 (en) 2006-06-07 2006-06-07 USE OF A FLAT PRODUCT MADE FROM A MANGANEOUS-BORON STEEL AND METHOD FOR THE PRODUCTION THEREOF
DE502006007636T DE502006007636D1 (en) 2006-06-07 2006-06-07 Use of a flat product produced from manganese-boron steel and process for its production
EP06115075A EP1865086B1 (en) 2006-06-07 2006-06-07 Use of a steel flat product produced from a manganese boron steel and method of its production
PCT/EP2007/055130 WO2007141152A1 (en) 2006-06-07 2007-05-25 Manganese boron steel, flat products produced from such steel, and production method

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EP2390530B1 (en) * 2010-05-31 2012-03-28 iwis motorsysteme GmbH & Co. KG Articulated chain with chain links made of boron manganese steel
KR20180016980A (en) * 2015-06-03 2018-02-20 잘쯔기터 플래시슈탈 게엠베하 Deformation-hardened parts made of galvanized steel, method for making the same, and deformation of parts - Method for manufacturing steel strip suitable for hardening
WO2017006144A1 (en) 2015-07-09 2017-01-12 Arcelormittal Steel for press hardening and press hardened part manufactured from such steel
DE102016200518A1 (en) * 2016-01-18 2017-07-20 Ford Global Technologies, Llc Chassis subframe assembly to improve crash safety
WO2018220430A1 (en) 2017-06-02 2018-12-06 Arcelormittal Steel sheet for manufacturing press hardened parts, press hardened part having a combination of high strength and crash ductility, and manufacturing methods thereof
EP3814536A1 (en) 2018-06-26 2021-05-05 Tata Steel Nederland Technology B.V. Cold-rolled martensite steel with high strength and high bendability and method of producing thereof

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FR2780984B1 (en) 1998-07-09 2001-06-22 Lorraine Laminage COATED HOT AND COLD STEEL SHEET HAVING VERY HIGH RESISTANCE AFTER HEAT TREATMENT
AU744962B2 (en) 1999-02-22 2002-03-07 Nippon Steel & Sumitomo Metal Corporation High strength galvanized steel plate excellent in adhesion of plated metal and formability in press working and high strength alloy galvanized steel plate and method for production thereof
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