EP3512968A1 - Method for producing a flat steel product made of a manganese-containing steel, and such a flat steel product - Google Patents

Method for producing a flat steel product made of a manganese-containing steel, and such a flat steel product

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Publication number
EP3512968A1
EP3512968A1 EP17768090.7A EP17768090A EP3512968A1 EP 3512968 A1 EP3512968 A1 EP 3512968A1 EP 17768090 A EP17768090 A EP 17768090A EP 3512968 A1 EP3512968 A1 EP 3512968A1
Authority
EP
European Patent Office
Prior art keywords
hot
particularly preferably
flat steel
steel product
cold
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP17768090.7A
Other languages
German (de)
French (fr)
Other versions
EP3512968B1 (en
Inventor
Peter PALZER
Thomas Dr. Evertz
Manuel Dr. Otto
Kai Dr. KÖHLER
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzgitter Flachstahl GmbH
Original Assignee
Salzgitter Flachstahl GmbH
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Publication date
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Application filed by Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Publication of EP3512968A1 publication Critical patent/EP3512968A1/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/0242—Flattening; Dressing; Flexing
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
    • 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
    • C21D2211/008—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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys

Definitions

  • the invention relates to a method for producing a flat steel product from a medium manganese steel with TRI P / TW IP effect, a flat steel product produced by this method and a use thereof.
  • a steel flat product made of manganese-containing steel which has a tensile strength of 900 to 1500 MPa and consists of the following elements (contents in percent by weight and based on the molten steel): C: to 0.5 ; Mn: 4 to 12.0; Si: up to 1, 0; AI: up to 3.0; Cr: 0.1 to 4.0; Cu: up to 4.0; Ni: up to 2.0; N: up to 0.05; P: up to 0.05; S: up to 0.01 as well as balance iron and unavoidable impurities.
  • one or more elements from the group "V, Nb, Ti" are provided, the sum of the contents of these elements being at most 0.5.
  • This steel should be characterized in that it is less expensive to produce than
  • German Laid-Open Specification DE 10 2012 013 1 13 A1 also describes so-called TRIP steels which have a predominantly ferritic basic structure with embedded retained austenite which can convert to martensite during a transformation (TRIP effect). Because of its high work hardening, the TRIP steel achieves high levels of uniform elongation and tensile strength. TRIP steels are suitable for use. a. in structural, chassis and crash-relevant components of vehicles, as sheet metal blanks, as well as welded blanks.
  • German patent application DE 10 2015 1 1 1 866 A1 discloses a
  • deformable lightweight structural steel with a manganese content of 3 to 30 wt .-% and TRIP / TWIP properties, which by alloying up to 0.8 wt .-%
  • Antimony (Sb) and a targeted heat treatment at 480 to 770 ° C for 1 minute to 48 hours has improved material properties.
  • this steel in addition to improved tensile strength and elongation at break, this steel has increased resistance to hydrogen-induced cracking and cracking
  • German patent application DE 10 2005 052 774 A1 discloses a method for producing hot strips with TRIP and / or TWIP properties and high tensile strengths.
  • the lightweight structural steel consisting of the main elements Fe, Mn, Si and Al is encapsulated under protective gas close to the final dimensions to form a preliminary strip, which subsequently passes through a homogenization zone. This is followed by hot rolling until reaching the predetermined total degree of deformation of greater than 70%. Then the hot strip is before the cold forming
  • the finished hot strip is cooled and cold rolled several times, between the individual cold rolling processes, if necessary, intermediate anneals are performed.
  • German Patent DE 10 2004 054 444 B3 discloses a method for producing metal components or semi-finished products with high strength and plasticity by cold forming of steels. Their cold forming should lead to solidification by TWIP (Twinning Induced Plasticity) or SIP
  • Adjustment of strength of at least 30% of the initial value sets and the remaining tensile strain of the metal drops to not less than 20%.
  • Forming process with high elongation should have the advantage that, in spite of the high strength values, a plasticity reserve is maintained, which enables a downstream final shaping to a finished component by means of conventional forming technology.
  • the steels selected for this purpose are characterized by a Mn content in wt .-% of 10 to 30. Such high manganese alloyed steels are more expensive than due to the high alloy element contents
  • the present invention based on the object, a method for producing a flat steel product from a medium manganese steel, a flat product produced by this method and a
  • a process for producing a steel flat product from a medium manganese steel with TRIP / TWIP effect comprising the steps: - cold rolling a hot or cold strip, - annealing the cold-rolled hot or cold strip at 500 to 840 ° C for 1 min. to 24 h, - rolling or tempering of the annealed hot or cold strip to a flat steel product with a degree of deformation between 0.3% and 60% achieved that the yield strength is increased by the rolling or tempering of the flat steel product.
  • the degree of deformation is based on the thickness direction of the flat steel product.
  • Reworking or temper rolling causes partial transformation of the metastable austenite of the annealed hot or cold strip into twisted twins (TWIP effect) and martensite (TRIP effect), with at least a 3% share of austenite being required to convert to martensite and a minimum of 10% austenite is maintained as a cubic face-centered phase.
  • the annealed hot or cold strip is re-rolled with a degree of deformation of between 10 and 40%.
  • the annealed hot or cold strip is dressed with a degree of deformation of between 0.6 and 2.2%. It is preferably provided that the annealed hot or cold strip is re-rolled or dressed at a temperature of 0 to 400 ° C. As a result, deformation twins are formed (TWIP effect), which increase the yield and / or yield strength analogously to the dislocation density of other types of steel.
  • the annealed hot or cold strip is so far rolled or dressed into a flat steel product such that the flat steel product has a yield strength which is increased by at least 50 MPa compared with the state before the rolling or the skin pass.
  • the flat steel product via a
  • the hot or cold strip is cold rolled with a first pass at a temperature of the hot or cold strip of 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C.
  • the hot or cold strip between the first Walzstich following further rolling passes to temperatures of 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C, interposed or intercooled.
  • Increasing the temperature before the first pass also involves a reduction in the requisite forming forces.
  • an increase in the residual workability of the cold-rolled hot or cold strip is effected with tensile strengths of greater than 800 MPa to 2000 MPa with elongations at break greater than 3% in the most highly deformed areas.
  • the preheating of the hot or cold strip can be done for a coil or unwound strip or sheet material.
  • Cold rolling with preheating of the hot or cold strip prior to the first forming step completely or partially suppresses transformation of metastable austenite into martensite (TRIP effect) during the rolling process, whereby twining twists (TWIP effect) can form in the austenite. This results in an advantageous reduction of
  • the flat steel product having the following chemical composition is prepared in order to achieve in particular the advantages described: C: 0.0005 to 0.9, preferably 0.05 to 0.35
  • Mn 4 to 12, preferably greater than 5 to less than 10
  • Al 0 to 10, preferably 0.05 to 5, particularly preferably greater than 0.5 to 3
  • Nb 0 to 1, preferably 0.005 to 0.4, particularly preferably 0.01 to 0.1
  • V 0 to 1, 5, preferably 0.005 to 0.6, particularly preferably 0.01 to 0.3
  • Ti 0 to 1.5, preferably 0.005 to 0.6, particularly preferably 0.01 to 0.3
  • Mo 0 to 3, preferably 0.005 to 1.5, particularly preferably 0.01 to 0.6
  • Sn 0 to 0.5, preferably less than 0.2, particularly preferably less than 0.05
  • Cu 0 to 3, preferably less than 0.5, particularly preferably less than 0.1
  • W 0 to 5, preferably 0.01 to 3, particularly preferably 0.2 to 1.5
  • Co 0 to 8, preferably 0.01 to 5, particularly preferably 0.3 to 2
  • Zr 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.2
  • Ta 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.1
  • Te 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.1
  • N less than 0.1, preferably less than 0.05.
  • This semi-manganese TRIP (TRANSformation Induced Plasticity) and TWIP (TWinning Induced Plasticity) steel sheet is characterized by excellent cold and warm forging, increased resistance to hydrogen-induced delayed fracture
  • Continuous annealing plant bell annealing plant or other continuous or discontinuous annealing plants.
  • Typical thickness ranges for pre-strip are 1 mm to 35 mm and for slabs and thin slabs 35 mm to 450 mm.
  • the slab or thin slab is hot rolled to a hot strip having a thickness of 20 mm to 0.8 mm, or the final near cast cast slab is hot rolled to a hot strip with a thickness of 8 mm to 0.8 mm.
  • the cold strip has a thickness of usually less than 3 mm, preferably 0.1 to 1.4 mm.
  • the cold rolling of the hot strip may take place at room temperature or advantageously at elevated temperature with heating prior to the first pass and / or heating in another pass or between several passes.
  • Cold rolling at elevated temperature is advantageous to reduce rolling forces and promote the formation of twinned twins (TWIP effect).
  • Advantageous temperatures of the rolling stock before the first pass are 60 ° C to below Ac3 temperature, preferably 60 to 450 ° C.
  • Temperature preferably 60 ° C to 450 ° C, or between
  • Heating of the material during rapid rolling and high degrees of deformation be made.
  • the steel strip After cold rolling of the hot strip at room temperature, the steel strip is to restore sufficient forming properties in a continuous annealing, bell annealing or other continuous or discontinuous
  • Annealing plant advantageous with an annealing time of 1 min. to glow for 24 h and temperatures of 500 to 840 ° C. If necessary to achieve certain material properties, this annealing process can also be carried out at the elevated temperature rolled steel strip. After the annealing treatment, the steel strip is advantageously cooled to a temperature of 250 ° C to room temperature and then, if necessary, to adjust the required mechanical properties in the course of a
  • the Aging treatment reheated to a temperature of 300 to 450 ° C, at this temperature for up to 5 min. kept and then cooled to room temperature.
  • the aging treatment can advantageously be carried out in a continuous annealing plant.
  • the steel flat product produced in this way can optionally be electrolytically galvanized or hot-dip galvanized.
  • the steel strip thus produced receives a coating on an organic or inorganic basis instead of or after the electrolytic galvanizing or hot-dip galvanizing.
  • These may be, for example, organic coatings, plastic coatings or paints or other inorganic coatings such as iron oxide layers.
  • a flat steel product produced by the process according to the invention advantageously has a yield strength Rp0.2 of 300 to 1350 MPa, a tensile strength Rm of 1100 to 2200 MPa and an elongation at break A80 of more than 4 to 41%, with high strengths tending to be associated with lower elongations at break and vice versa:
  • the sample form 2 with an initial measuring length of A80 was used according to DIN 50 125.
  • Connections are versatile and complex.
  • the effect of the alloying elements in the alloy according to the invention will be discussed in more detail.
  • Carbon C needed to form carbides, stabilizes austenite and increases strength. Higher contents of C deteriorate the welding properties and lead to the deterioration of the elongation and toughness properties, therefore, a maximum content of 0.9 wt%, preferably 0.35 wt%, is determined.
  • a minimum addition of 0.0005 wt .-%, preferably 0.05 wt .-% is required.
  • Manganese Mn Stabilizes austenite, increases strength and toughness, and allows for strain-induced martensite and / or twin formation in the alloy of the present invention. Contents less than 4 wt .-% are not sufficient to stabilize the austenite and thus worsen the elongation properties, while at levels of 12 wt .-% and more, the austenite is too strong stabilized and thereby the strength properties, in particular the 0.2% proof stress, be reduced.
  • Manganter is a range of greater than 5 to less than 10 wt .-% is preferred.
  • Aluminum AI improves the strength and elongation properties, reduces the specific gravity and influences the conversion behavior of the
  • Carbon diffusion reduces specific gravity and increases strength and elongation and toughness properties. Furthermore, could a
  • Chromium Cr The optional addition of Cr improves strength and reduces corrosion rate, retards ferrite and pearlite formation, and forms carbides. Higher contents lead to a deterioration of the elongation properties. Therefore, a Cr content of 0 to 6 wt .-%, preferably 0.1 to 4 wt .-%, more preferably from greater than 0.5 to 2.5 wt .-% determined.
  • Ivlikroleg michingsetti are usually added only in very small quantities. They work in contrast to the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion formation but can also in a dissolved state the alloying elements mainly by excretion
  • Micro-alloying elements significantly influence the processing and final properties. In particular affect in hot forming
  • Typical micro-alloying elements are vanadium, niobium and titanium. These elements can be dissolved in the iron grid and form carbides, nitrides and carbonitrides with carbon and nitrogen. Vanadium V and niobium Nb: These act in particular through the formation of carbides Grain-refining, which at the same time strength, toughness and
  • Elongation properties are improved. Contents of over 1, 5 wt .-% and 1 wt .-% bring no further advantages.
  • Titanium Ti As a carbide former, it refines grain, improving its strength, toughness, and elongation properties while reducing intergranular corrosion. Contents of Ti of above 1, 5 wt .-% deteriorate the elongation properties, which is why optionally a maximum content of 1, 5 wt .-%, preferably 0.6 wt .-%, particularly preferably 0.3 wt .-%, is determined ,
  • Molybdenum Mo acts as a carbide former, increases strength and increases
  • Tin Sn Tin increases strength but, similar to copper, accumulates at higher temperatures below the scale and grain boundaries. It leads by penetration into the grain boundaries to the formation of low-melting phases and associated with cracks in the structure and solder brittleness, which is why an optional
  • Maximum content of 0.5 wt .-% preferably of less than 0.2 wt .-%, more preferably of less than 0.05 wt .-%, is provided.
  • Copper Cu Reduces the corrosion rate and increases strength. Contents above 3 wt .-% deteriorate the manufacturability by forming low-melting phases during casting and hot rolling, which is why a maximum optional content of 3 wt .-%, preferably less than 0.5 wt .-%, particularly preferably less than 0.1 wt. -%, is set.
  • Tungsten W acts as a carbide former and increases strength and heat resistance.
  • Contents of W of more than 5% by weight deteriorate the elongation properties, therefore, optionally, a maximum content of 5% by weight is determined.
  • a content of 0.01 wt .-% to 3 wt .-% is provided and more preferably from 0.2 to 1, 5 wt .-%.
  • Cobalt Co Increases the strength of the steel, stabilizes the austenite and improves the heat resistance. Contents of over 8 wt .-% worsen the
  • the Co content is therefore determined with a maximum of 8 wt .-%, preferably from 0.01 to 5 wt .-%, particularly preferably from 0.3 to 2 wt .-%.
  • Zirconium Zr acts as a carbide former and improves strength. Zr contents exceeding 0.5% by weight deteriorate the elongation properties. Therefore, a Zr content of 0 to 0.5 wt .-%, preferably 0.005 to 0.3 wt .-%, particularly preferably from 0.01 to 0.2 wt .-%, set.
  • Tantalum Ta Like niobium, tantalum acts as a carbide-forming agent that refines grain, thereby improving its strength, toughness and elongation properties. Contents of over 0.5 wt .-% cause no further improvement in the properties. Therefore, a maximum content of 0.5 wt .-% is optionally set. Preferably, a minimum content of 0.005 and a maximum content of 0.3 wt .-% are set, in which the grain refining can be advantageously effected. In order to improve the economy and optimize the grain refinement, a content of from 0.01% by weight to 0.1% by weight is particularly preferred.
  • Tellurium Te improves corrosion resistance and mechanical properties as well as machinability. Furthermore, Te increases the strength of manganese sulfides (MnS), which is less elongated in the rolling direction during hot and cold rolling. Contents above 0.5% by weight
  • Maximum content of 0.5 wt .-% is set.
  • a minimum content of 0.005 wt.% And a maximum content of 0.3 wt.% are set, which advantageously improves the mechanical properties and increases the strength of existing MnS.
  • Boron B Boron delays the austenite transformation, improves the
  • Phosphorus P Is a trace element, comes mainly from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphor boosts
  • Solid solution solidifies the hardness and improves the hardenability.
  • the addition of phosphorus to the grain boundaries can cause cracks along the grain boundaries during hot rolling.
  • phosphorus increases the transition temperature from tough to brittle behavior by up to 300 ° C.
  • Sulfur S Like phosphorus as a trace element in iron ore, but especially in the production route, it is bound in the coke via the blast furnace process. It is generally undesirable in steel because it tends to segregate and has a strong embrittlement, thereby degrading the elongation and toughness properties. It is therefore an attempt to achieve the lowest possible amounts of sulfur in the melt (for example, by deep desulphurisation). From the above
  • the sulfur content is limited to values of less than 0.1% by weight, preferably less than 0.02% by weight.
  • N is also a companion element of steelmaking. It improves in the dissolved state with steels containing more than 4 manganese steels with higher manganese content %
  • Mn the strength and toughness properties.
  • Low Mn-alloyed steels of less than 4% by weight tend to have a strong aging effect in the presence of free nitrogen.
  • the nitrogen diffuses at low temperatures at dislocations and blocks them. It causes an increase in strength combined with a rapid loss of toughness. Curing of the nitrogen in the form of nitrides is possible, for example, by alloying of titanium or aluminum, with aluminum nitrides in particular adversely affecting the
  • the nitrogen content is limited to less than 0.1% by weight, preferably less than 0.05% by weight.

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Abstract

The invention relates to a method for producing a flat steel product made of a medium manganese steel having a TRIP/TWIP effect. The aim of the invention is to achieve an improvement in the yield strength when a sufficient residual deformability of the produced flat steel product is obtained. This aim is achieved by the following steps: cold rolling a hot or cold strip, annealing the cold-rolled hot or cold strip at 500 to 840 °C for 1 minute to 24 hours, temper rolling or finishing the annealed hot or cold strip to form a flat steel product having a degree of deformability between 0.3 % and 60 %. The invention further relates to a flat steel product produced according to said method and to a use thereof.

Description

VERFAHREN ZUR HERSTELLUNG EINES STAHLFLACHPRODUKTS AUS EINEM MANGANHALTIGEN STAHL UND EIN DERARTIGES STAHLFLACHPRODUKT  METHOD FOR PRODUCING A STEEL FLAT PRODUCT FROM A MANGANIZED STEEL AND A SUITABLE STEEL FLAT PRODUCT
Die Erfindung betrifft ein Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl mit TRI P/TW IP-Effekt, ein nach diesem Verfahren hergestelltes Stahlflachprodukt und eine Verwendung hierfür. The invention relates to a method for producing a flat steel product from a medium manganese steel with TRI P / TW IP effect, a flat steel product produced by this method and a use thereof.
Aus der europäischen Patentanmeldung EP 2 383 353 A2 ist ein Stahlflachprodukt aus einem manganhaltigen Stahl bekannt, der eine Zugfestigkeit von 900 bis 1500 MPa aufweist und aus den folgenden Elementen (Gehalte in Gewichtsprozent und bezogen auf die Stahlschmelze) besteht: C: bis 0,5; Mn: 4 bis 12,0; Si: bis zu 1 ,0; AI: bis zu 3,0; Cr: 0,1 bis 4,0; Cu: bis zu 4,0; Ni: bis zu 2,0; N: bis zu 0,05; P: bis zu 0,05; S: bis zu 0,01 sowie Rest Eisen und unvermeidbare Verunreinigungen. Optional sind ein oder mehrere Elemente aus der Gruppe„V, Nb, Ti" vorgesehen, wobei die Summe der Gehalte dieser Elemente höchstens gleich 0,5 ist. Dieser Stahl soll sich dadurch auszeichnen, dass dieser kostengünstiger herzustellen ist als From the European patent application EP 2 383 353 A2 a steel flat product made of manganese-containing steel is known, which has a tensile strength of 900 to 1500 MPa and consists of the following elements (contents in percent by weight and based on the molten steel): C: to 0.5 ; Mn: 4 to 12.0; Si: up to 1, 0; AI: up to 3.0; Cr: 0.1 to 4.0; Cu: up to 4.0; Ni: up to 2.0; N: up to 0.05; P: up to 0.05; S: up to 0.01 as well as balance iron and unavoidable impurities. Optionally, one or more elements from the group "V, Nb, Ti" are provided, the sum of the contents of these elements being at most 0.5. This steel should be characterized in that it is less expensive to produce than
hochmanganhaltige Stähle und gleichzeitig hohe Bruchdehnungswerte und damit einhergehend eine deutlich verbesserte Umformbarkeit besitzt. Auch sind in der deutschen Offenlegungsschrift DE 10 2012 013 1 13 A1 bereits sogenannte TRIP-Stähle beschrieben, die ein überwiegend ferritisches Grundgefüge mit eingelagertem Restaustenit aufweisen, der während einer Umformung zu Martensit umwandeln kann (TRIP-Effekt). Wegen seiner starken Kaltverfestigung erreicht der TRIP-Stahl hohe Werte der Gleichmaßdehnung und Zugfestigkeit. TRIP- Stähle eignen sich für den Einsatz u. a. in Struktur-, Fahrwerks- und crashrelevanten Bauteilen von Fahrzeugen, als Blechplatinen, sowie als geschweißte Platinen. high manganese steels and at the same time has high elongation at break and, consequently, a significantly improved formability. German Laid-Open Specification DE 10 2012 013 1 13 A1 also describes so-called TRIP steels which have a predominantly ferritic basic structure with embedded retained austenite which can convert to martensite during a transformation (TRIP effect). Because of its high work hardening, the TRIP steel achieves high levels of uniform elongation and tensile strength. TRIP steels are suitable for use. a. in structural, chassis and crash-relevant components of vehicles, as sheet metal blanks, as well as welded blanks.
Die deutsche Offenlegungsschrift DE 10 2015 1 1 1 866 A1 offenbart einen German patent application DE 10 2015 1 1 1 866 A1 discloses a
umformbaren Leichtbaustahl mit einem Mangan-Gehalt von 3 bis 30 Gew.-% und TRIP/TWIP-Eigenschaften, welcher durch Zulegierung von bis zu 0,8 Gew.-% deformable lightweight structural steel with a manganese content of 3 to 30 wt .-% and TRIP / TWIP properties, which by alloying up to 0.8 wt .-%
Antimon (Sb) und einer gezielten Wärmebehandlung bei 480 bis 770°C für 1 Minute bis 48 Stunden verbesserte Werkstoffeigenschaften aufweist. Insbesondere weist dieser Stahl neben einer verbesserten Zugfestigkeit und Bruchdehnung einen erhöhten Widerstand gegenüber wasserstoffinduzierter Rissbildung und  Antimony (Sb) and a targeted heat treatment at 480 to 770 ° C for 1 minute to 48 hours has improved material properties. In particular, in addition to improved tensile strength and elongation at break, this steel has increased resistance to hydrogen-induced cracking and cracking
Wasserstoffversprödung auf. Aus der deutschen Offenlegungsschrift DE 10 2005 052 774 A1 ist ein Verfahren zum Erzeugen von Warmbändern mit TRIP- und/oder TWIP- Eigenschaften sowie hohen Zugfestigkeiten bekannt. Der aus den Hauptelementen Fe, Mn, Si und AI bestehende Leichtbaustahl wird unter Schutzgas endabmessungsnah zu einem Vorband vergossen, welches im Anschluss eine Homogenisierungszone durchläuft. Danach folgt ein Warmwalzen bis zum Erreichen des vorgegebenen Gesamt-Umformgrades von größer 70%. Sodann wird das Warmband vor der Kaltumformung Hydrogen embrittlement on. German patent application DE 10 2005 052 774 A1 discloses a method for producing hot strips with TRIP and / or TWIP properties and high tensile strengths. The lightweight structural steel consisting of the main elements Fe, Mn, Si and Al is encapsulated under protective gas close to the final dimensions to form a preliminary strip, which subsequently passes through a homogenization zone. This is followed by hot rolling until reaching the predetermined total degree of deformation of greater than 70%. Then the hot strip is before the cold forming
rekristallisierend geglüht. Im Anschluss daran wird das fertige Warmband abgekühlt und mehrfach kaltgewalzt, wobei zwischen den einzelnen Kaltwalzprozessen erforderlichenfalls Zwischenglühungen durchgeführt werden. annealed recrystallizing. Subsequently, the finished hot strip is cooled and cold rolled several times, between the individual cold rolling processes, if necessary, intermediate anneals are performed.
Des Weiteren ist aus der deutschen Patentschrift DE 10 2004 054 444 B3 ein Verfahren zum Herstellen von Metallbauteilen oder Halbzeugen mit hoher Festigkeit und Plastizität durch Kaltumformung von Stählen bekannt. Deren Kaltumformung soll zu einer Verfestigung durch TWIP- (Twinning Induced Plasticity) oder SIP-Furthermore, German Patent DE 10 2004 054 444 B3 discloses a method for producing metal components or semi-finished products with high strength and plasticity by cold forming of steels. Their cold forming should lead to solidification by TWIP (Twinning Induced Plasticity) or SIP
(Shearband Induced Plasticity) Effekte führen. Hierbei liegen die Umformgrade bei einer gesamten Dehnung im Bereich von 10 bis 70%. Die Umformung findet nach einem Schluss- oder Kristallisationsglühen so weit statt, bis sich ein (Shearband Induced Plasticity) effects. Here, the degrees of deformation at a total elongation in the range of 10 to 70%. The forming takes place after a final or crystallization annealing so far until a
Festigkeitszuwachs von mindestens 30% des Ausgangswertes einstellt und die verbleibende Zugdehnung des Metalls auf nicht unter 20% absinkt. Dieser Adjustment of strength of at least 30% of the initial value sets and the remaining tensile strain of the metal drops to not less than 20%. This
Umformprozess mit hoher Dehnung soll den Vorteil haben, dass trotz der hohen Festigkeitswerte eine Plastizitätsreserve erhalten bleibt, die eine nachgelagerte Endformgebung zu einem fertigen Bauteil mittels konventioneller Umformtechnik ermöglicht. Die hierfür gewählten Stähle zeichnen sich durch einen Mn-Gehalt in Gew.-% von 10 bis 30 aus. Derartige hochmanganhaltige legierte Stähle sind aufgrund der hohen Legierungselementgehalte kostenintensiver als  Forming process with high elongation should have the advantage that, in spite of the high strength values, a plasticity reserve is maintained, which enables a downstream final shaping to a finished component by means of conventional forming technology. The steels selected for this purpose are characterized by a Mn content in wt .-% of 10 to 30. Such high manganese alloyed steels are more expensive than due to the high alloy element contents
Mittelmanganstähle. Central manganese steels.
Hiervon ausgehend liegt der vorliegenden Erfindung die Aufgabe zu Grunde, ein Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl, ein nach diesem Verfahren hergestelltes Stahlflachprodukt und eine On this basis, the present invention based on the object, a method for producing a flat steel product from a medium manganese steel, a flat product produced by this method and a
Verwendung hierfür zu schaffen, die sich durch eine Verbesserung der Streckgrenze bei Erhalt eines ausreichenden Restumformvermögens des hergestellten To use for this purpose, which is characterized by an improvement in the yield strength while maintaining a sufficient Resumformvermögens of the produced
Stahlflach produkts auszeichnen. Diese Aufgabe wird durch ein Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl mit TRI P/TW IP-Effekt mit den Merkmalen des Anspruchs 1 , ein nach diesem Verfahren hergestelltes Stahlflachprodukt mit den Merkmalen des Anspruchs 12 und eine Verwendung für dieses Stahlflachprodukt gemäß Anspruch 13 gelöst. Vorteilhafte Ausgestaltungen der Erfindung sind in den Unteransprüchen angegeben. Distinguish flat steel products. This object is achieved by a method for producing a steel flat product from a medium manganese steel with TRI P / TW IP effect with the features of claim 1, a produced by this method flat steel product having the features of claim 12 and a use for this flat steel product according to claim 13 solved. Advantageous embodiments of the invention are specified in the subclaims.
Erfindungsgemäß wird durch ein Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl mit TRIP/TWIP-Effekt, umfassend die Schritte: - Kaltwalzen eines Warm- oder Kaltbands, - Glühen des kaltgewalzten Warm- oder Kaltbands bei 500 bis 840 °C für 1 min. bis 24 h, - Nachwalzen oder Dressieren des geglühten Warm- oder Kaltbands zu einem Stahlflachprodukt mit einem Umformgrad zwischen 0,3 % und 60 % erreicht, dass durch das Nachwalzen oder Dressieren des Stahlflach produkts dessen Streckgrenze erhöht wird. In üblicher weise ist der Umformgrad auf die Dickenrichtung des Stahlflachprodukts bezogen. Über dieAccording to the invention, by a process for producing a steel flat product from a medium manganese steel with TRIP / TWIP effect, comprising the steps: - cold rolling a hot or cold strip, - annealing the cold-rolled hot or cold strip at 500 to 840 ° C for 1 min. to 24 h, - rolling or tempering of the annealed hot or cold strip to a flat steel product with a degree of deformation between 0.3% and 60% achieved that the yield strength is increased by the rolling or tempering of the flat steel product. In the usual way, the degree of deformation is based on the thickness direction of the flat steel product. About the
Erhöhung der Streckgrenze, können aus diesem Stahlflachprodukt optimierte Bauteile mit geringerer Blechdicke hergestellt werden. Das Nachwalzen oder Dressieren bewirkt eine teilweise Umwandlung des metastabilen Austenits des geglühten Warmoder Kaltbands in Verformungszwillinge (TWIP-Effekt) und Martensit (TRIP-Effekt), wobei mindestens ein Anteil von 3 % des Austenits in Martensit umwandeln muss und mindestens ein Anteil von 10 % des Austenits als kubisch-flächenzentrierte Phase erhalten bleibt. Increasing the yield strength, can be made of this flat steel product optimized components with lower sheet thickness. Reworking or temper rolling causes partial transformation of the metastable austenite of the annealed hot or cold strip into twisted twins (TWIP effect) and martensite (TRIP effect), with at least a 3% share of austenite being required to convert to martensite and a minimum of 10% austenite is maintained as a cubic face-centered phase.
In Bezug auf das Nachwalzen ist bevorzugt vorgesehen, dass das geglühte Warm- oder Kaltband mit einem Umformgrad zwischen 10 bis 40 % nachgewalzt wird. With respect to the rolling, it is preferably provided that the annealed hot or cold strip is re-rolled with a degree of deformation of between 10 and 40%.
In Bezug auf das Dressieren ist bevorzugt vorgesehen, dass das geglühte Warmoder Kaltband mit einem Umformgrad zwischen 0,6 bis 2,2 % dressiert wird. Vorzugsweise ist vorgesehen, dass das geglühte Warm- oder Kaltband bei einer Temperatur von 0 bis 400 °C nachgewalzt oder dressiert wird. Hierdurch werden Verformungszwillinge gebildet (TWIP-Effekt), welche analog der Versetzungsdichte anderer Stahlsorten die Streck- und/oder Dehngrenze erhöhen. In einer bevorzugten Ausgestaltung wird das geglühte Warm- oder Kaltband so weit zu einem Stahlflachprodukt nachgewalzt oder dressiert, dass das Stahlflachprodukt eine um mindestens 50 MPa erhöhte Streckgrenze gegenüber dem Zustand vor dem Nachwalzen oder Dressieren aufweist. Besonders bevorzugt ist vorgesehen, dass das Stahlflachprodukt über eine With regard to the temper rolling, it is preferably provided that the annealed hot or cold strip is dressed with a degree of deformation of between 0.6 and 2.2%. It is preferably provided that the annealed hot or cold strip is re-rolled or dressed at a temperature of 0 to 400 ° C. As a result, deformation twins are formed (TWIP effect), which increase the yield and / or yield strength analogously to the dislocation density of other types of steel. In a preferred embodiment, the annealed hot or cold strip is so far rolled or dressed into a flat steel product such that the flat steel product has a yield strength which is increased by at least 50 MPa compared with the state before the rolling or the skin pass. Particularly preferably, it is provided that the flat steel product via a
Zugfestigkeit von größer 1300 MPa und über eine Bruchdehnung A80 von größer 3 % verfügt.  Tensile strength greater than 1300 MPa and has an elongation at break A80 of greater than 3%.
In einer vorteilhaften Ausgestaltung des Verfahrens wird das Warm- oder Kaltband mit einem ersten Walzstich bei einer Temperatur des Warm- oder Kaltbands von 60 °C bis unterhalb Ac3, vorzugsweise von 60 °C bis 450 °C, kaltgewalzt. Optional wird dann das Warm- oder Kaltband zwischen den dem ersten Walzstich folgenden weiteren Walzstichen auf Temperaturen von 60 °C bis unterhalb Ac3, vorzugsweise von 60 °C bis 450 °C, zwischenerwärmt oder zwischengekühlt. Mit der Erhöhung der Temperatur vor dem ersten Walzstich geht auch eine Verringerung der erforderlichen Umformkräfte einher. Auch wird eine Erhöhung des Restumformvermögens des kaltgewalzten Warm- oder Kaltbands mit Zugfestigkeiten von größer 800 MPa bis 2000 MPa bei Bruchdehnungen von größer 3 % in den am stärksten umgeformten Bereichen bewirkt. Das Vorwärmen des Warm- oder Kaltbands kann für ein Coil oder abgewickeltes Band- oder Tafelmaterial erfolgen. Durch das Kaltwalzen mit dem Vorwärmen des Warm- oder Kaltbands vor dem ersten Umformschritt wird während des Walzvorgangs eine Umwandlung von metastabilen Austenit in Martensit (TRIP- Effekt) ganz oder teilweise unterdrückt, wobei sich im Austenit Verformungszwillinge (TWIP-Effekt) bilden können. Hierdurch wird eine vorteilhafte Reduktion der In an advantageous embodiment of the method, the hot or cold strip is cold rolled with a first pass at a temperature of the hot or cold strip of 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C. Optionally, the hot or cold strip between the first Walzstich following further rolling passes to temperatures of 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C, interposed or intercooled. Increasing the temperature before the first pass also involves a reduction in the requisite forming forces. Also, an increase in the residual workability of the cold-rolled hot or cold strip is effected with tensile strengths of greater than 800 MPa to 2000 MPa with elongations at break greater than 3% in the most highly deformed areas. The preheating of the hot or cold strip can be done for a coil or unwound strip or sheet material. Cold rolling with preheating of the hot or cold strip prior to the first forming step completely or partially suppresses transformation of metastable austenite into martensite (TRIP effect) during the rolling process, whereby twining twists (TWIP effect) can form in the austenite. This results in an advantageous reduction of
Walzkräfte erreicht und das Gesamtumformvermögen erhöht. Durch die weiteren Walzstiche bei erhöhten Temperaturen werden gezielt Verformungszwillinge eingebracht, welche bei Raumtemperatur weiter in Martensit umwandeln und dadurch das Energieaufnahmevermögen erhöhen und einen höheren Umformgrad zulassen. Unter dem erfindungsgemäßen Stahlflachprodukt ist ein kaltnachgewalztes Achieved rolling forces and increased the total forming capacity. Due to the further rolling passes at elevated temperatures, deformation twins are deliberately introduced, which at room temperature continue to convert into martensite, thereby increasing the energy absorption capacity and allowing a higher degree of deformation. Under the flat steel product according to the invention is a cold rolled
Grobblech, Warm- und/oder Kaltband zu verstehen. Heavy plate, hot and / or cold strip to understand.
Besonders bevorzugt ist vorgesehen, dass das Stahlflachprodukt mit folgender chemischer Zusammensetzung (in Gew.-%) hergestellt wird, um insbesondere die beschriebenen Vorteile zu erreichen: C: 0,0005 bis 0,9, vorzugsweise 0,05 bis 0,35 It is particularly preferred that the flat steel product having the following chemical composition (in% by weight) is prepared in order to achieve in particular the advantages described: C: 0.0005 to 0.9, preferably 0.05 to 0.35
Mn: 4 bis 12, vorzugsweise größer 5 bis kleiner 10 Mn: 4 to 12, preferably greater than 5 to less than 10
Rest Eisen einschließlich unvermeidbarer stahlbegleitender Elemente, Remainder of iron including unavoidable steel-accompanying elements,
mit optionaler Zulegierung von: with optional addition of:
AI: 0 bis 10, bevorzugt 0,05 bis 5, insbesondere bevorzugt größer 0,5 bis 3 Al: 0 to 10, preferably 0.05 to 5, particularly preferably greater than 0.5 to 3
Si: 0 bis 6, bevorzugt 0,05 bis 3, insbesondere bevorzugt 0,1 bis 1 ,5 Si: 0 to 6, preferably 0.05 to 3, particularly preferably 0.1 to 1.5
Cr: 0 bis 6, bevorzugt 0,1 bis 4, insbesondere bevorzugt größer 0,5 bis 2,5 Cr: 0 to 6, preferably 0.1 to 4, particularly preferably greater than 0.5 to 2.5
Nb: 0 bis 1 , bevorzugt 0,005 bis 0,4, insbesondere bevorzugt 0,01 bis 0,1 Nb: 0 to 1, preferably 0.005 to 0.4, particularly preferably 0.01 to 0.1
V: 0 bis 1 ,5, bevorzugt 0,005 bis 0,6, insbesondere bevorzugt 0,01 bis 0,3 V: 0 to 1, 5, preferably 0.005 to 0.6, particularly preferably 0.01 to 0.3
Ti: 0 bis 1 ,5, bevorzugt 0,005 bis 0,6, insbesondere bevorzugt 0,01 bis 0,3 Ti: 0 to 1.5, preferably 0.005 to 0.6, particularly preferably 0.01 to 0.3
Mo: 0 bis 3, bevorzugt 0,005 bis 1 ,5, insbesondere bevorzugt 0,01 bis 0,6 Mo: 0 to 3, preferably 0.005 to 1.5, particularly preferably 0.01 to 0.6
Sn: 0 bis 0,5, bevorzugt kleiner 0,2, insbesondere bevorzugt kleiner 0,05 Sn: 0 to 0.5, preferably less than 0.2, particularly preferably less than 0.05
Cu: 0 bis 3, bevorzugt kleiner 0,5, insbesondere bevorzugt kleiner 0,1 Cu: 0 to 3, preferably less than 0.5, particularly preferably less than 0.1
W: 0 bis 5, bevorzugt 0,01 bis 3, insbesondere bevorzugt 0,2 bis 1 ,5 W: 0 to 5, preferably 0.01 to 3, particularly preferably 0.2 to 1.5
Co: 0 bis 8, bevorzugt 0,01 bis 5, insbesondere bevorzugt 0,3 bis 2 Co: 0 to 8, preferably 0.01 to 5, particularly preferably 0.3 to 2
Zr: 0 bis 0,5, bevorzugt 0,005 bis 0,3, insbesondere bevorzugt 0,01 bis 0,2  Zr: 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.2
Ta: 0 bis 0,5, bevorzugt 0,005 bis 0,3, insbesondere bevorzugt 0,01 bis 0,1 Ta: 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.1
Te: 0 bis 0,5, bevorzugt 0,005 bis 0,3, insbesondere bevorzugt 0,01 bis 0,1 Te: 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.1
B: 0 bis 0,15, bevorzugt 0,001 bis 0,08, insbesondere bevorzugt 0,002 bis 0,01 P: kleiner 0,1 , bevorzugt kleiner 0,04 B: 0 to 0.15, preferably 0.001 to 0.08, particularly preferably 0.002 to 0.01 P: less than 0.1, preferably less than 0.04
S: kleiner 0,1 , bevorzugt kleiner 0,02 S: less than 0.1, preferably less than 0.02
N: kleiner 0,1 , bevorzugt kleiner 0,05. N: less than 0.1, preferably less than 0.05.
Dieses Stahlflachprodukt aus dem mittel-manganhaltigen TRIP(TRansformation Induced Plasticity)- und/oder TWIP (TWinning Induced Plasticity)-Stahl weist eine hervorragender Kalt- und Halbwarmumformbarkeit, erhöhten Widerstand gegen wasserstoffinduzierte verzögerte Rissbildung (delayed fracture), gegen This semi-manganese TRIP (TRANSformation Induced Plasticity) and TWIP (TWinning Induced Plasticity) steel sheet is characterized by excellent cold and warm forging, increased resistance to hydrogen-induced delayed fracture
Wasserstoffversprödung (hydrogen embrittlement) sowie gegen Hydrogen embrittlement (hydrogen embrittlement) as well as against
Flüssigmetallversprödung beim Schweißen im verzinkten Zustand auf. Liquid metal embrittlement during welding in the galvanized state.
In üblicher Weise wird das vorbeschriebene Stahlflachprodukt mit einer nachfolgend angeführten Erzeugungsroute hergestellt: In the usual way, the above-described flat steel product is produced by a production route given below:
- Erschmelzen einer Stahlschmelze mit der vorstehend beschriebenen chemischen Zusammensetzung in einem über die Prozessroute Hochofen-Stahlwerk oder Elektrolichtbogenofen-Stahlwerk mit optionaler Vakuumbehandlung der Schmelze; - Vergießen der Stahlschmelze zu einem Vorband mittels eines endabmessungsnahen horizontalen oder vertikalen Bandgießverfahrens oder Vergießen der Stahlschmelze zu einer Bramme oder Dünnbramme mittels eines horizontalen oder vertikalen Brammen- oder Dünnbrammengießverfahrens, Melting a molten steel having the above-described chemical composition in an over the process route blast furnace steel mill or electric arc furnace steel mill with optional vacuum treatment of the melt; Pouring the molten steel into a preliminary strip by means of a horizontal or vertical continuous strip casting process, or casting the molten steel into a slab or thin slab by means of a horizontal or vertical slab or thin slab casting process,
- Erwärmen des Vorbandes auf eine Walztemperatur von 1050 bis 1250°C oder Inlinewalzen aus der Gießhitze (erste Hitze) heraus, Heating the pre-strip to a rolling temperature of 1050 to 1250 ° C or inline rolling from the casting heat (first heat),
- Warmwalzen des Vorbandes oder der Bramme oder der Dünnbramme zu einem Warmband mit einer Dicke von 20 bis 0,8 mm mit einer Walzendtemperatur von 1050 bis 800°C,  Hot rolling of the pre-strip or slab or thin slab into a hot strip having a thickness of 20 to 0.8 mm and a final rolling temperature of 1050 to 800 ° C,
- Aufhaspeln des Warmbandes bei einer Temperatur von mehr als 100 bis 800°C,- coiling of the hot-rolled strip at a temperature of more than 100 to 800 ° C,
- Beizen des Warmbandes, Pickling of the hot strip,
- Glühen des Warmbandes in einer Durchlauf- oder Haubenglühanlage  - Annealing the hot strip in a continuous or annealing annealing plant
beziehungsweise in einer kontinuierlichen oder diskontinuierlichen Glühanlage bei einer Glühzeit von 1 min. bis 24 h und Temperaturen von 500 °C bis 840°C, or in a continuous or discontinuous annealing plant with an annealing time of 1 min. up to 24 h and temperatures from 500 ° C to 840 ° C,
- Kaltwalzen des Warmbandes bei Raumtemperatur, bevorzugt mit einem Vorwärmen auf 60 °C bis unterhalb Ac3-Temperatur, bevorzugt 60 °C bis 450 °C vor dem ersten Walzstich zur Verringerung der Walzkräfte und Bildung von Verformungszwillingen im Austenit und bedarfsweisem Kühlen oder Erwärmen zwischen den Walzstichen auf 60 °C bis unterhalb der Ac3-Temperatur, bevorzugt 60 °C bis 450 °C, - Cold rolling of the hot strip at room temperature, preferably with a preheating to 60 ° C to below Ac3 temperature, preferably 60 ° C to 450 ° C before the first pass to reduce the rolling forces and formation of twist twists in austenite and as needed cooling or heating between the Rolling passes at 60 ° C. to below the Ac 3 temperature, preferably 60 ° C. to 450 ° C.,
- Glühen des kaltgewalzten Warm- oder Kaltbands bei 500 bis 840 °C für 1 min bis 24 h über Durchlauf- oder Haubenglühung, Annealing the cold-rolled hot or cold strip at 500 to 840 ° C. for 1 minute to 24 hours by continuous or bell annealing,
- Nachwalzen oder Dressieren des geglühten Warm- oder Kaltbands zur Erhöhung der Streckgrenze mit glatten oder texturierten Walzen (beispielsweise mit  - rolling or tempering the annealed hot or cold strip to increase the yield strength with smooth or textured rollers (for example with
P retexTextu ri e ru n g ) ,  P retexTextu ri e ru n g),
- optionales elektrolytisches Verzinken oder Feuerverzinken des Stahlbandes oder Aufbringen einer anderweitigen organischen oder anorganischen Beschichtung,optional galvanizing or hot-dip galvanizing of the steel strip or application of another organic or inorganic coating,
- optionales Glühen bei 500 bis 840 °C für 1 min bis 24 h in einer - Optional annealing at 500 to 840 ° C for 1 min to 24 h in one
Durchlaufglühanlage, Haubenglühanlage oder sonstigen kontinuierlichen oder diskontinuierlichen Glühanlagen. Continuous annealing plant, bell annealing plant or other continuous or discontinuous annealing plants.
Übliche Dickenbereiche für Vorband sind 1 mm bis 35 mm sowie für Brammen und Dünnbrammen 35 mm bis 450 mm. Vorzugsweise ist vorgesehen, dass die Bramme oder Dünnbramme zu einem Warmband mit einer Dicke von 20 mm bis 0,8 mm warmgewalzt wird oder das endabmessungsnah gegossene Vorband zu einem Warmband mit einer Dicke von 8 mm bis 0,8 mm warmgewalzt wird. Das Kaltband hat eine Dicke von üblicherweise unter 3 mm, vorzugsweise 0,1 bis 1 ,4 mm. Typical thickness ranges for pre-strip are 1 mm to 35 mm and for slabs and thin slabs 35 mm to 450 mm. Preferably, it is provided that the slab or thin slab is hot rolled to a hot strip having a thickness of 20 mm to 0.8 mm, or the final near cast cast slab is hot rolled to a hot strip with a thickness of 8 mm to 0.8 mm. The cold strip has a thickness of usually less than 3 mm, preferably 0.1 to 1.4 mm.
Im Zusammenhang mit dem vorstehenden erfindungsgemäßen Verfahren wird ein endabmessungsnah mit dem Zwei-Rollen Gießverfahren erzeugtes Vorband mit einer Dicke von kleiner gleich 3 mm, vorzugsweise 1 mm bis 3 mm, bereits als Warmband verstanden. Das so als Warmband produzierte Vorband weist, bedingt durch die eingebrachte Umformung der beiden gegenläufigen Walzen, keine Gussstruktur auf. Ein Warmwalzen findet somit bereits inline während des Zwei-Rollen-Gießverfahrens statt, so dass ein separates Erwärmen und Warmwalzen optional entfallen kann. In connection with the above method according to the invention, a preliminary strip close to the final dimensions produced by the two-roller casting method with a thickness of less than or equal to 3 mm, preferably 1 mm to 3 mm, is already considered a hot strip. Due to the introduced deformation of the two counter-rotating rolls, the pre-strip produced as a hot strip has no cast structure. Hot rolling thus already takes place inline during the two-roll casting process, so that separate heating and hot rolling can optionally be dispensed with.
Das Kaltwalzen des Warmbandes kann bei Raumtemperatur oder vorteilhaft bei erhöhter Temperatur mit einer Erwärmung vor dem ersten Walzstich und/oder Erwärmungen in einem weiteren oder zwischen mehreren Walzstichen stattfinden. Das Kaltwalzen bei erhöhter Temperatur ist vorteilhaft, um die Walzkräfte zu reduzieren und die Bildung von Verformungszwillingen (TWIP-Effekt) zu begünstigen. Vorteilhafte Temperaturen des Walzgutes vor dem ersten Walzstich betragen 60°C bis unterhalb Ac3-Temperatur, bevorzugt 60 bis 450°C. The cold rolling of the hot strip may take place at room temperature or advantageously at elevated temperature with heating prior to the first pass and / or heating in another pass or between several passes. Cold rolling at elevated temperature is advantageous to reduce rolling forces and promote the formation of twinned twins (TWIP effect). Advantageous temperatures of the rolling stock before the first pass are 60 ° C to below Ac3 temperature, preferably 60 to 450 ° C.
Erfolgt das Kaltwalzen in mehreren Walzstichen ist es vorteilhaft, das Stahlband zwischen den Walzstichen auf eine Temperatur von 60°C bis unterhalb Ac3-If cold rolling is carried out in several rolling passes, it is advantageous to allow the steel strip between the rolling passes to a temperature of 60 ° C to below Ac3.
Temperatur, bevorzugt 60 °C bis 450°C, zwischenzuerwärmen bzw. Temperature, preferably 60 ° C to 450 ° C, or between
herunterzukühlen, da der TWIP-Effekt in diesem Bereich besonders vorteilhaft zumto cool down, since the TWIP effect in this area is particularly advantageous for
Tragen kommt. Je nach Walzgeschwindigkeit und Umformgrad kann sowohl einWear comes. Depending on the rolling speed and degree of deformation, both a
Zwischenerwärmen, bspw. bei sehr niedrigen Umformgraden und Intermediate heating, eg. At very low degrees of deformation and
Walzgeschwindigkeiten, als auch eine zusätzliche Kühlung, bedingt durch die Rolling speeds, as well as additional cooling, due to the
Erwärmung des Werkstoffs beim schnellen Walzen und hohen Umformgraden, vorgenommen werden.  Heating of the material during rapid rolling and high degrees of deformation, be made.
Nach einem Kaltwalzen des Warmbandes bei Raumtemperatur ist das Stahlband zur Wiederherstellung ausreichender Umformeigenschaften in einer Durchlaufglühanlage, Haubenglühanlage oder sonstigen kontinuierlichen oder diskontinuierlichen After cold rolling of the hot strip at room temperature, the steel strip is to restore sufficient forming properties in a continuous annealing, bell annealing or other continuous or discontinuous
Glühanlage vorteilhaft bei einer Glühzeit von 1 min. bis 24 h und Temperaturen von 500 bis 840°C zu glühen. Falls zur Erzielung bestimmter Werkstoffeigenschaften erforderlich, kann dieser Glühvorgang auch bei dem bei erhöhter Temperatur gewalzten Stahlband erfolgen. Nach der Glühbehandlung wird das Stahlband vorteilhaft auf eine Temperatur von 250°C bis Raumtemperatur abgekühlt und anschließend, falls erforderlich, zur Einstellung der geforderten mechanischen Eigenschaften, im Zuge einer Annealing plant advantageous with an annealing time of 1 min. to glow for 24 h and temperatures of 500 to 840 ° C. If necessary to achieve certain material properties, this annealing process can also be carried out at the elevated temperature rolled steel strip. After the annealing treatment, the steel strip is advantageously cooled to a temperature of 250 ° C to room temperature and then, if necessary, to adjust the required mechanical properties in the course of a
Alterungsbehandlung, auf eine Temperatur von 300 bis 450°C wieder erwärmt, bei dieser Temperatur für bis zu 5 min. gehalten und anschließend auf Raumtemperatur abgekühlt. Die Alterungsbehandlung kann vorteilhaft in einer Durchlaufglühanlage durchgeführt werden. Aging treatment, reheated to a temperature of 300 to 450 ° C, at this temperature for up to 5 min. kept and then cooled to room temperature. The aging treatment can advantageously be carried out in a continuous annealing plant.
Das so hergestellte Stahlflachprodukt kann optional elektrolytisch verzinkt oder feuerverzinkt werden. In einer vorteilhaften Weiterbildung erhält das so hergestellte Stahlband anstelle oder nach dem elektrolytischen Verzinken oder Feuerverzinken eine Beschichtung auf organischer oder anorganischer Basis. Dies können zum Beispiel organische Beschichtungen, Kunststoffbeschichtungen oder Lacke oder anderweitige anorganische Beschichtungen wie beispielsweise Eisenoxidschichten sein. The steel flat product produced in this way can optionally be electrolytically galvanized or hot-dip galvanized. In an advantageous development, the steel strip thus produced receives a coating on an organic or inorganic basis instead of or after the electrolytic galvanizing or hot-dip galvanizing. These may be, for example, organic coatings, plastic coatings or paints or other inorganic coatings such as iron oxide layers.
Erfindungsgemäß bietet sich vorteilhaft eine Verwendung eines nach dem In accordance with the invention, it is advantageous to use one after the
vorbeschriebenen Verfahren hergestellten Bauteils im Kraftfahrzeugbau, above-described method in automotive engineering,
Schienenfahrzeugbau, Schiffsbau, Anlagenbau, Infrastrukturbau, in der Luft- und Raumfahrt, Hausgerätetechnik und in geschweißten Platinen (tailored welded blanks) an. Rail vehicle construction, shipbuilding, plant construction, infrastructure construction, in the aerospace industry, household appliance technology and in tailored welded blanks.
Ein nach dem erfindungsgemäßen Verfahren hergestelltes Stahlflachprodukt weist vorteilhaft eine Dehngrenze Rp0,2 von 300 bis 1350 MPa, eine Zugfestigkeit Rm von 1 100 bis 2200 MPa und eine Bruchdehnung A80 von mehr als 4 bis 41 % auf, wobei hohen Festigkeiten tendenziell niedrigere Bruchdehnungen zuzuordnen sind und umgekehrt: A flat steel product produced by the process according to the invention advantageously has a yield strength Rp0.2 of 300 to 1350 MPa, a tensile strength Rm of 1100 to 2200 MPa and an elongation at break A80 of more than 4 to 41%, with high strengths tending to be associated with lower elongations at break and vice versa:
Rm von über 1 100 bis 1200 MPa Rm x A80 > 25000 bis zu 45000 Rm of over 1 100 to 1200 MPa Rm x A80> 25000 up to 45000
Rm von über 1200 bis 1400 MPa Rm x A80 > 20000 bis zu 42000  Rm of over 1200 to 1400 MPa Rm x A80> 20,000 to 42,000
Rm von über 1400 bis 1800 MPa Rm x A80 > 10000 bis zu 40000  Rm of over 1400 to 1800 MPa Rm x A80> 10000 to 40000
Rm von über 1800 MPa: Rm x A80 > 7200 bis zu 20000  Rm of over 1800 MPa: Rm x A80> 7200 up to 20000
Für die Bruchdehnungsuntersuchungen wurde gemäß DIN 50 125 die Probenform 2 mit einer Anfangsmesslänge von A80 verwendet. Die Verwendung des Begriffs„bis" in der Definition der Gehaltsbereiche, wie beispielsweise 0,01 bis 1 Gew.-%, bedeutet, dass die Eckwerte - im Beispiel 0,01 und 1 - mit eingeschlossen sind. Legierungselemente werden dem Stahl in der Regel zugegeben, um gezielt bestimmte Eigenschaften zu beeinflussen. Dabei kann ein Legierungselement in verschiedenen Stählen unterschiedliche Eigenschaften beeinflussen. Die Wirkung und Wechselwirkung hängt im Allgemeinen stark von der Menge, der Anwesenheit weiterer Legierungselemente und dem Lösungszustand im Werkstoff ab. Die For the elongation at break tests the sample form 2 with an initial measuring length of A80 was used according to DIN 50 125. The use of the term "bis" in the definition of content ranges, such as 0.01 to 1% by weight, means that the benchmarks - in the example 0.01 and 1 - are included in. Alloying elements usually become the steel In addition, an alloying element in different steels may affect different properties, the effect and interaction of which are generally highly dependent on the amount, the presence of other alloying elements and the state of dissolution in the material
Zusammenhänge sind vielseitig und komplex. Im Folgenden soll auf die Wirkung der Legierungselemente in der erfindungsgemäßen Legierung näher eingegangen werden. Nachfolgend werden die positiven Effekte der erfindungsgemäß verwendeten Legierungselemente beschrieben. Kohlenstoff C: Wird benötigt zur Bildung von Karbiden, stabilisiert den Austenit und erhöht die Festigkeit. Höhere Gehalte an C verschlechtern die Schweißeigenschaften und führen zur Verschlechterung der Dehnungs- und Zähigkeitseigenschaften, weshalb ein maximaler Gehalt von 0,9 Gew.-%, bevorzugt 0,35 Gew.-%, festgelegt wird. Um die gewünschte Kombination von Festigkeits- und Dehnungseigenschaften des Werkstoffs zu erreichen, ist eine Mindestzugabe von 0,0005 Gew.-%, bevorzugt 0,05 Gew.-%, erforderlich. Connections are versatile and complex. In the following, the effect of the alloying elements in the alloy according to the invention will be discussed in more detail. The following describes the positive effects of the alloying elements used according to the invention. Carbon C: needed to form carbides, stabilizes austenite and increases strength. Higher contents of C deteriorate the welding properties and lead to the deterioration of the elongation and toughness properties, therefore, a maximum content of 0.9 wt%, preferably 0.35 wt%, is determined. In order to achieve the desired combination of strength and elongation properties of the material, a minimum addition of 0.0005 wt .-%, preferably 0.05 wt .-%, is required.
Mangan Mn: Stabilisiert den Austenit, erhöht die Festigkeit und die Zähigkeit und ermöglicht eine verformungsinduzierte Martensit- und/oder Zwillingsbildung in der erfindungsgemäßen Legierung. Gehalte kleiner 4 Gew.-% sind nicht ausreichend zur Stabilisierung des Austenits und verschlechtern somit die Dehnungseigenschaften, während bei Gehalten von 12 Gew.-% und mehr der Austenit zu stark stabilisiert wird und dadurch die Festigkeitseigenschaften, insbesondere die 0,2 % Dehngrenze, verringert werden. Für den erfindungsgemäßen Manganstahl mit mittleren Manganese Mn: Stabilizes austenite, increases strength and toughness, and allows for strain-induced martensite and / or twin formation in the alloy of the present invention. Contents less than 4 wt .-% are not sufficient to stabilize the austenite and thus worsen the elongation properties, while at levels of 12 wt .-% and more, the austenite is too strong stabilized and thereby the strength properties, in particular the 0.2% proof stress, be reduced. For manganese manganese according to the invention with medium
Mangangehalten wird ein Bereich von größer 5 bis kleiner 10 Gew.-% bevorzugt. Mangangehalten is a range of greater than 5 to less than 10 wt .-% is preferred.
Aluminium AI: AI verbessert die Festigkeits- und Dehnungseigenschaften, senkt die spezifische Dichte und beeinflusst das Umwandlungsverhalten der Aluminum AI: AI improves the strength and elongation properties, reduces the specific gravity and influences the conversion behavior of the
erfindungsgemäßen Legierung. Zu hohe Gehalte an AI verschlechtern die alloy according to the invention. Too high levels of AI worsen the
Dehnungseigenschaften. Auch verschlechtern höhere AI-Gehalte das Gießverhalten im Strangguss deutlich. Hierdurch entsteht ein höherer Aufwand beim Vergießen. Hohe AI-Gehalte verzögern die Ausscheidung von Karbiden in der Elongation properties. Also, higher Al contents deteriorate the casting behavior in continuous casting clearly. This results in a higher cost when casting. High Al contents retard the precipitation of carbides in the
erfindungsgemäßen Legierung. Daher wird ein AI-Gehalt von 0 bis 10 Gew.-%, bevorzugt 0,05 bis 5 Gew.-%, besonders bevorzugt von größer 0,5 bis 3 Gew.-%, festgelegt. alloy according to the invention. Therefore, an Al content of 0 to 10 wt .-%, preferably 0.05 to 5 wt .-%, particularly preferably greater than 0.5 to 3 wt .-% determined.
Silizium Si: Die optionale Zugabe von Si in höheren Gehalten behindert die Silicon Si: The optional addition of Si at higher levels hinders the
Kohlenstoffdiffusion, verringert die spezifische Dichte und erhöht die Festigkeit und die Dehnungs- sowie Zähigkeitseigenschaften. Des Weiteren konnte eine Carbon diffusion reduces specific gravity and increases strength and elongation and toughness properties. Furthermore, could a
Verbesserung der Kaltwalzbarkeit durch Zulegieren von Si beobachtet werden. Improvement of the cold rollability can be observed by alloying Si.
Höhere Si-Gehalte führen zu einer Versprödung des Werkstoffs und beeinflussen die Warm- und Kaltwalzbarkeit sowie die Beschichtbarkeit beispielsweise durch  Higher Si contents lead to embrittlement of the material and influence hot and cold rollability as well as coatability, for example
Verzinken negativ. Daher wird ein Si-Gehalt von 0 bis 6 Gew.-%, bevorzugt 0,05 bis 3 Gew.-%, besonders bevorzugt von 0,1 bis 1 ,5 Gew.-%, festgelegt. Galvanize negatively. Therefore, an Si content of 0 to 6 wt .-%, preferably 0.05 to 3 wt .-%, particularly preferably from 0.1 to 1, 5 wt .-%, determined.
Chrom Cr: Die optionale Zugabe von Cr verbessert die Festigkeit und verringert die Korrosionsrate, verzögert die Ferrit- und Perlitbildung und bildet Karbide. Höhere Gehalte führen zu einer Verschlechterung der Dehnungseigenschaften. Daher wird ein Cr-Gehalt von 0 bis 6 Gew.-%, bevorzugt 0,1 bis 4 Gew.-%, besonders bevorzugt von größer 0,5 bis 2,5 Gew.-%, festgelegt. Chromium Cr: The optional addition of Cr improves strength and reduces corrosion rate, retards ferrite and pearlite formation, and forms carbides. Higher contents lead to a deterioration of the elongation properties. Therefore, a Cr content of 0 to 6 wt .-%, preferably 0.1 to 4 wt .-%, more preferably from greater than 0.5 to 2.5 wt .-% determined.
Ivlikrolegierungselemente werden in der Regel nur in sehr geringen Mengen zugegeben. Sie wirken im Gegensatz zu den Legierungselementen hauptsächlich durch Ausscheidungsbildung können aber auch in gelöstem Zustand die Ivlikrolegierungselemente are usually added only in very small quantities. They work in contrast to the alloying elements mainly by excretion formation but can also in a dissolved state the
Eigenschaften beeinflussen. Bereits geringe Mengenzugaben der Affect properties. Even small additions of the
Mikrolegierungselemente beeinflussen die Verarbeitungs- und Endeigenschaften erheblich. Insbesondere bei der Warmumformung beeinflussen  Micro-alloying elements significantly influence the processing and final properties. In particular affect in hot forming
Mikrolegierungselemente das Rekristallisationsverhalten vorteilhaft und bewirken eine Kornfeinung. Micro-alloying the recrystallization advantageous and cause a grain refinement.
Typische Mikrolegierungselemente sind Vanadium, Niob und Titan. Diese Elemente können im Eisengitter gelöst werden und bilden mit Kohlenstoff und Stickstoff Carbide, Nitride und Carbonitride. Vanadium V und Niob Nb: Diese wirken insbesondere durch die Bildung von Karbiden kornfeinend, wodurch gleichzeitig die Festigkeit, Zähigkeit und Typical micro-alloying elements are vanadium, niobium and titanium. These elements can be dissolved in the iron grid and form carbides, nitrides and carbonitrides with carbon and nitrogen. Vanadium V and niobium Nb: These act in particular through the formation of carbides Grain-refining, which at the same time strength, toughness and
Dehnungseigenschaften verbessert werden. Gehalte von über 1 ,5 Gew.-% beziehungsweise 1 Gew.-% bringen keine weiteren Vorteile. Für Vanadium und Niob wird optional bevorzugt ein Mindestgehalt von 0,005 Gew.-% und ein Maximalgehalt von 0,6 Gew.-% beziehungsweise 0,4 Gew.-%, besonders bevorzugt ein Elongation properties are improved. Contents of over 1, 5 wt .-% and 1 wt .-% bring no further advantages. For vanadium and niobium, a minimum content of 0.005 wt.% And a maximum content of 0.6 wt.% Or 0.4 wt.%, More preferably, is preferably preferred
Mindestgehalt von 0,01 Gew.-% und ein Maximalgehalt von 0,3 Gew.-% Minimum content of 0.01% by weight and a maximum content of 0.3% by weight
beziehungsweise 0,1 Gew.-%, vorgesehen. or 0.1 wt .-%, provided.
Titan Ti: Wirkt als Karbidbildner kornfeinend, wodurch gleichzeitig die Festigkeit, Zähigkeit und Dehnungseigenschaften verbessert werden und vermindert die interkristalline Korrosion. Gehalte an Ti von über 1 ,5 Gew.-% verschlechtern die Dehnungseigenschaften, weshalb optional ein Maximalgehalt von 1 ,5 Gew.-%, bevorzugt 0,6 Gew.-%, besonders bevorzugt 0,3 Gew.-%, festgelegt wird. Titanium Ti: As a carbide former, it refines grain, improving its strength, toughness, and elongation properties while reducing intergranular corrosion. Contents of Ti of above 1, 5 wt .-% deteriorate the elongation properties, which is why optionally a maximum content of 1, 5 wt .-%, preferably 0.6 wt .-%, particularly preferably 0.3 wt .-%, is determined ,
Mindestgehalte von 0,005 Gew.-%, bevorzugt von 0,01 Gew.-%, können vorgesehen werden, um Stickstoff abzubinden und Ti vorteilhaft auszuscheiden. Minimum contents of 0.005 wt .-%, preferably of 0.01 wt .-%, can be provided to bind off nitrogen and Ti advantageously excrete.
Molybdän Mo: Wirkt als Karbidbildner, erhöht die Festigkeit und erhöht den Molybdenum Mo: acts as a carbide former, increases strength and increases
Widerstand gegen verzögerte Rissbildung und Wasserstoffversprödung. Hohe Gehalte an Mo verschlechtern die Dehnungseigenschaften. Daher wird optional ein Mo-Gehalt von 0 bis 3 Gew.-%, bevorzugt 0,005 bis 1 ,5 Gew.-%, besonders bevorzugt von größer 0,01 bis 0,6 Gew.-%, festgelegt. Resistance to delayed cracking and hydrogen embrittlement. High levels of Mo degrade the elongation properties. Therefore, an Mo content of 0 to 3 wt .-%, preferably 0.005 to 1, 5 wt .-%, particularly preferably greater than 0.01 to 0.6 wt .-%, optionally set.
Zinn Sn: Zinn steigert die Festigkeit, reichert sich jedoch ähnlich Kupfer bei höheren Temperaturen unter der Zunderschicht und an den Korngrenzen an. Es führt durch Eindringen in die Korngrenzen zur Bildung niedrig schmelzender Phasen und damit verbunden zu Rissen im Gefüge und zu Lotbrüchigkeit, weshalb optional ein Tin Sn: Tin increases strength but, similar to copper, accumulates at higher temperatures below the scale and grain boundaries. It leads by penetration into the grain boundaries to the formation of low-melting phases and associated with cracks in the structure and solder brittleness, which is why an optional
Maximalgehalt 0,5 Gew.-%, bevorzugt von kleiner 0,2 Gew.-%, besonders bevorzugt von kleiner 0,05 Gew.-%, vorgesehen ist. Kupfer Cu: Verringert die Korrosionsrate und steigert die Festigkeit. Gehalte oberhalb 3 Gew.-% verschlechtern die Herstellbarkeit durch Bildung niedrig schmelzender Phasen beim Vergießen und Warmwalzen weshalb optional ein Maximalgehalt von 3 Gew.-%, bevorzugt von kleiner 0,5 Gew.-%, besonders bevorzugt von kleiner 0,1 Gew.-%, festgelegt wird. Wolfram W: Wirkt als Karbidbildner und erhöht die Festigkeit und Warmfestigkeit. Gehalte an W von über 5 Gew.-% verschlechtern die Dehnungseigenschaften, weshalb optional ein Maximalgehalt von 5 Gew.-% festgelegt wird. Bevorzugt ist ein Gehalt von 0,01 Gew.-% bis 3 Gew.-% vorgesehen und besonders bevorzugt von 0,2 bis 1 ,5 Gew.-%. Maximum content of 0.5 wt .-%, preferably of less than 0.2 wt .-%, more preferably of less than 0.05 wt .-%, is provided. Copper Cu: Reduces the corrosion rate and increases strength. Contents above 3 wt .-% deteriorate the manufacturability by forming low-melting phases during casting and hot rolling, which is why a maximum optional content of 3 wt .-%, preferably less than 0.5 wt .-%, particularly preferably less than 0.1 wt. -%, is set. Tungsten W: acts as a carbide former and increases strength and heat resistance. Contents of W of more than 5% by weight deteriorate the elongation properties, therefore, optionally, a maximum content of 5% by weight is determined. Preferably, a content of 0.01 wt .-% to 3 wt .-% is provided and more preferably from 0.2 to 1, 5 wt .-%.
Kobalt Co: Erhöht die Festigkeit des Stahls, stabilisiert den Austenit und verbessert die Warmfestigkeit. Gehalte von über 8 Gew.-% verschlechtern die Cobalt Co: Increases the strength of the steel, stabilizes the austenite and improves the heat resistance. Contents of over 8 wt .-% worsen the
Dehnungseigenschaften. Der Co-Gehalt wird daher mit maximal 8 Gew.-%, bevorzugt von 0,01 bis 5 Gew.-%, besonders bevorzugt von 0,3 bis 2 Gew.-%, festgelegt. Elongation properties. The Co content is therefore determined with a maximum of 8 wt .-%, preferably from 0.01 to 5 wt .-%, particularly preferably from 0.3 to 2 wt .-%.
Zirkonium Zr: Wirkt als Karbidbildner und verbessert die Festigkeit. Gehalte an Zr von über 0,5 Gew-% verschlechtern die Dehnungseigenschaften. Daher wird ein Zr- Gehalt von 0 bis 0,5 Gew.-%, bevorzugt 0,005 bis 0,3 Gew.-%, besonders bevorzugt von 0,01 bis 0,2 Gew.-%, festgelegt. Zirconium Zr: acts as a carbide former and improves strength. Zr contents exceeding 0.5% by weight deteriorate the elongation properties. Therefore, a Zr content of 0 to 0.5 wt .-%, preferably 0.005 to 0.3 wt .-%, particularly preferably from 0.01 to 0.2 wt .-%, set.
Tantal Ta: Tantal wirkt ähnlich wie Niob als Karbidbildner kornfeinend und verbessert dadurch gleichzeitig die Festigkeit, Zähigkeit und Dehnungseigenschaften. Gehalte von über 0,5 Gew.-% bewirken keine weitere Verbesserung der Eigenschaften. Daher wird optional ein Maximalgehalt von 0,5 Gew.-% festgelegt. Bevorzugt werden ein Minimalgehalt von 0,005 und ein Maximalgehalt von 0,3 Gew.-% festgelegt, in welchem die Kornfeinung vorteilhaft bewirkt werden kann. Zur Verbesserung der Wirtschaftlichkeit und Optimierung der Kornfeinung wird insbesondere bevorzugt ein Gehalt von 0,01 Gew.-% bis 0,1 Gew.-% angestrebt. Tantalum Ta: Like niobium, tantalum acts as a carbide-forming agent that refines grain, thereby improving its strength, toughness and elongation properties. Contents of over 0.5 wt .-% cause no further improvement in the properties. Therefore, a maximum content of 0.5 wt .-% is optionally set. Preferably, a minimum content of 0.005 and a maximum content of 0.3 wt .-% are set, in which the grain refining can be advantageously effected. In order to improve the economy and optimize the grain refinement, a content of from 0.01% by weight to 0.1% by weight is particularly preferred.
Tellur Te: Tellur verbessert die Korrosionsbeständigkeit und die mechanischen Eigenschaften sowie die spanende Bearbeitbarkeit. Des Weiteren erhöht Te die Festigkeit von Mangansulfiden (MnS), welches dadurch beim Warm- und Kaltwalzen weniger stark in Walzrichtung gelängt wird. Gehalte oberhalb 0,5 Gew.-% Tellurium Te: Tellurium improves corrosion resistance and mechanical properties as well as machinability. Furthermore, Te increases the strength of manganese sulfides (MnS), which is less elongated in the rolling direction during hot and cold rolling. Contents above 0.5% by weight
verschlechtern die Dehnungs- und Zähigkeitseigenschaften, weshalb ein deteriorate the elongation and toughness properties, which is why a
Maximalgehalt von 0,5 Gew.-% festgelegt wird. Optional wird ein Minimalgehalt von 0,005 Gew.-% und ein Maximalgehalt von 0,3 Gew.-% festgelegt, welche die mechanischen Eigenschaften vorteilhaft verbessern und die Festigkeit vorhandener MnS erhöht. Weiterhin wird ein Minimalgehalt von 0,01 Gew.-% und ein  Maximum content of 0.5 wt .-% is set. Optionally, a minimum content of 0.005 wt.% And a maximum content of 0.3 wt.% Are set, which advantageously improves the mechanical properties and increases the strength of existing MnS. Furthermore, a minimum content of 0.01 wt .-% and a
Maximalgehalt von 0,1 Gew.-% bevorzugt, welche eine Optimierung der mechanischen Eigenschaften bei gleichzeitiger Reduktion der Legierungskosten ermöglichen. Maximum content of 0.1 wt .-% preferred, which is an optimization of allow mechanical properties while reducing alloying costs.
Bor B: Bor verzögert die Austenitumwandlung, verbessert die Boron B: Boron delays the austenite transformation, improves the
Warmumformeigenschaften von Stählen und erhöht die Festigkeit bei Hot forming properties of steels and increases strength
Raumtemperatur. Es entfaltet seine Wirkung bereits bei sehr geringen Room temperature. It unfolds its effect even at very low levels
Legierungsgehalten. Gehalte oberhalb 0,15 Gew.-% verschlechtern die Dehnungsund Zähigkeitseigenschaften stark, weshalb der Maximalgehalt auf 0,15 Gew.-% festgelegt wird. Optional wird ein Minimalgehalt von 0,001 Gew.-% und Maximalgehalt von 0,08, vorzugsweise ein Minimalgehalt von 0,002 Gew.-% und Maximalgehalt von 0,01 festgelegt, um die festigkeitssteigernde Wirkung von Bor vorteilhaft zu nutzen. Alloy contents. Contents above 0.15 wt% greatly deteriorate the elongation and toughness properties, and therefore the maximum content is set at 0.15 wt%. Optionally, a minimum content of 0.001% by weight and maximum content of 0.08, preferably a minimum content of 0.002% by weight and a maximum content of 0.01 are set in order to make advantageous use of the strength-increasing effect of boron.
Phosphor P: Ist ein Spurenelement, stammt überwiegend aus dem Eisenerz und wird im Eisengitter als Substitutionsatom gelöst. Phosphor steigert durch Phosphorus P: Is a trace element, comes mainly from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphor boosts
Mischkristallverfestigung die Härte und verbessert die Härtbarkeit. Es wird allerdings in der Regel angestrebt, den Phosphorgehalt soweit wie möglich abzusenken, da er unter anderem durch seine geringe Diffusionsgeschwindigkeit stark seigerungsanfällig ist und im hohen Maße die Zähigkeit vermindert. Durch die Anlagerung von Phosphor an den Korngrenzen können Risse entlang der Korngrenzen beim Warmwalzen auftreten. Zudem setzt Phosphor die Übergangstemperatur von zähem zu sprödem Verhalten um bis zu 300 °C herauf. Aus vorgenannten Gründen ist der Solid solution solidifies the hardness and improves the hardenability. However, it is generally desirable to lower the phosphorus content as much as possible, since it is highly susceptible to segregation, among other things due to its low diffusion rate, and to a great extent reduces its toughness. The addition of phosphorus to the grain boundaries can cause cracks along the grain boundaries during hot rolling. In addition, phosphorus increases the transition temperature from tough to brittle behavior by up to 300 ° C. For the above reasons is the
Phosphorgehalt auf werte kleiner 0,1 Gew.-%, bevorzugt kleiner 0,04 Gew.-%, begrenzt. Schwefel S: Ist wie Phosphor als Spurenelement im Eisenerz aber insbesondere bei der Erzeugungsroute über den Hochofenprozess im Koks gebunden. Er ist im Stahl im Allgemeinen unerwünscht, da er zu starker Seigerung neigt und stark versprödend wirkt, wodurch die Dehnungs- und Zähigkeitseigenschaften verschlechtert werden. Es wird daher versucht, möglichst geringe Mengen an Schwefel in der Schmelze zu erreichen (beispielsweise durch eine Tiefentschwefelung). Aus vorgenannten Phosphorus content to values less than 0.1 wt .-%, preferably less than 0.04 wt .-% limited. Sulfur S: Like phosphorus as a trace element in iron ore, but especially in the production route, it is bound in the coke via the blast furnace process. It is generally undesirable in steel because it tends to segregate and has a strong embrittlement, thereby degrading the elongation and toughness properties. It is therefore an attempt to achieve the lowest possible amounts of sulfur in the melt (for example, by deep desulphurisation). From the above
Gründen ist der Schwefelgehalt auf Werte kleiner 0,1 Gew.-%, bevorzugt kleiner 0,02 Gew.-%, begrenzt.  The sulfur content is limited to values of less than 0.1% by weight, preferably less than 0.02% by weight.
Stickstoff N: N ist ebenfalls ein Begleitelement aus der Stahlherstellung. Er verbessert im gelösten Zustand bei höher manganhaltigen Stählen mit größer oder gleich 4 Gew.-% Mn die Festigkeits- und Zähigkeitseigenschaften. Niedriger Mn-Iegierte Stähle mit weniger als 4 Gew.-% neigen in Gegenwart von freiem Stickstoff zu einem starken Alterungseffekt. Der Stickstoff diffundiert schon bei geringen Temperaturen an Versetzungen und blockiert diese. Er bewirkt damit einen Festigkeitsanstieg verbunden mit einem rapiden Zähigkeitsverlust. Ein Abbinden des Stickstoffes in Form von Nitriden ist beispielsweise durch Zulegieren von Titan oder Aluminium möglich, wobei sich insbesondere Aluminiumnitride negativ auf die Nitrogen N: N is also a companion element of steelmaking. It improves in the dissolved state with steels containing more than 4 manganese steels with higher manganese content % By weight Mn the strength and toughness properties. Low Mn-alloyed steels of less than 4% by weight tend to have a strong aging effect in the presence of free nitrogen. The nitrogen diffuses at low temperatures at dislocations and blocks them. It causes an increase in strength combined with a rapid loss of toughness. Curing of the nitrogen in the form of nitrides is possible, for example, by alloying of titanium or aluminum, with aluminum nitrides in particular adversely affecting the
Umformeigenschaften der erfindungsgemäßen Legierung auswirken. Aus Forming properties of the alloy according to the invention effect. Out
vorgenannten Gründen ist der Stickstoffgehalt auf weniger als 0,1 Gew.-%, bevorzugt kleiner 0,05 Gew.-%, begrenzt. For the aforementioned reasons, the nitrogen content is limited to less than 0.1% by weight, preferably less than 0.05% by weight.

Claims

Patentansprüche claims
1 . Verfahren zur Herstellung eines Stahlflachprodukts aus einem 1 . Process for producing a flat steel product from a
mittelmanganhaltigen Stahl mit TRIP/TWIP-Effekt, umfassend die Schritte: Medium manganese steel with TRIP / TWIP effect, comprising the steps:
- Kaltwalzen eines Warm- oder Kaltbands, - cold rolling of a hot or cold strip,
- Glühen des kaltgewalzten Warm- oder Kaltbands bei 500 bis 840 °C für 1 min. bis 24 h,  - annealing the cold-rolled hot or cold strip at 500 to 840 ° C for 1 min. until 24 h,
- Nachwalzen oder Dressieren des geglühten Warm- oder Kaltbands zu einem  - rolling or passing the annealed hot or cold strip to a
Stahlflachprodukt mit einem Umformgrad zwischen 0,3 % und 60 %. Flat steel product with a degree of deformation between 0.3% and 60%.
2. Verfahren nach Anspruch 1 , dadurch gekennzeichnet, dass das geglühte Warmoder Kaltband mit einem Umformgrad zwischen 10 bis 40 % nachgewalzt wird. 2. The method according to claim 1, characterized in that the annealed hot or cold strip is re-rolled with a degree of deformation between 10 to 40%.
3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass das geglühte Warm- oder Kaltband mit einem Umformgrad zwischen 0,6 bis 2,2 % dressiert wird. 3. The method according to claim 1 or 2, characterized in that the annealed hot or cold strip is trained with a degree of deformation between 0.6 to 2.2%.
4. Verfahren nach mindestens einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass das Warm- oder Kaltband mit einem ersten Walzstich bei einer Temperatur des Warm- oder Kaltbands von 60 °C bis unterhalb Ac3, vorzugsweise von 60 °C bis 450 °C, kaltgewalzt wird. 4. The method according to at least one of claims 1 to 3, characterized in that the hot or cold strip with a first rolling pass at a temperature of the hot or cold strip of 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C. , cold rolled.
5. Verfahren nach Anspruch 4, dadurch gekennzeichnet, dass das Warm- oder Kaltband zwischen den dem ersten Walzstich folgenden weiteren Walzstichen auf Temperaturen von 60 °C bis unterhalb Ac3, vorzugsweise von 60 °C bis 450 °C, zwischenerwärmt oder zwischengekühlt wird. 5. The method according to claim 4, characterized in that the hot or cold strip between the first Walzstich following further rolling passes to temperatures of 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C, inter-heated or intercooled.
6. Verfahren nach mindestens einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass das geglühte Warm- oder Kaltband bei einer Temperatur von 0 bis 400 °C nachgewalzt oder dressiert wird. 6. The method according to at least one of claims 1 to 5, characterized in that the annealed hot or cold strip is re-rolled or dressed at a temperature of 0 to 400 ° C.
7. Verfahren nach mindestens einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass das geglühte Warm- oder Kaltband so weit zu einem Stahlflachprodukt nachgewalzt oder dressiert wird, dass das Stahlflachprodukt eine um mindestens 50 MPa erhöhte Streckgrenze gegenüber vor dem Nachwalzen oder Dressieren aufweist. 7. The method according to at least one of claims 1 to 6, characterized in that the annealed hot or cold strip is retreaded or trained so far to a flat steel product that the flat steel product has an increased by at least 50 MPa yield strength over before re-rolling or temper rolling.
8. Verfahren nach mindestens einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass das Stahlflachprodukt über eine Zugfestigkeit von größer 1300 MPa und über eine Bruchdehnung A80 von größer 3 % verfügt. 8. The method according to at least one of claims 1 to 7, characterized in that the flat steel product has a tensile strength of greater than 1300 MPa and a breaking elongation A80 of greater than 3%.
9. Verfahren nach mindestens einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass das geglühte Warm- oder Kaltband so weit zu einem Stahlflachprodukt nachgewalzt oder dressiert wird, dass dessen metastabiler Austenit teilweise in Verformungszwillinge (TWIP-Effekt) und Martensit (TRIP-Effekt) umgewandelt wird, wobei mindestens ein Anteil von 3 % des metastabiler Austenits in Martensit umwandelt und mindestens ein Anteil von 10 % des metastabilen Austenits als kubisch-flächenzentrierte Phase erhalten bleibt. 9. The method according to at least one of claims 1 to 8, characterized in that the annealed hot or cold strip is retreaded or trained so far to a flat steel product, that its metastable austenite partially in deformation twins (TWIP effect) and martensite (TRIP effect ), wherein at least a portion of 3% of the metastable austenite is converted to martensite and at least 10% of the metastable austenite is retained as a cubic face centered phase.
10. Verfahren nach mindestens einem der Ansprüche 1 bis 9, dadurch 10. The method according to at least one of claims 1 to 9, characterized
gekennzeichnet, dass das Stahlflachprodukt mit folgender chemischer characterized in that the flat steel product with the following chemical
Zusammensetzung (in Gew.-%) hergestellt wird: Composition (in wt .-%) is produced:
C: 0,0005 bis 0,9, vorzugsweise 0,05 bis 0,35 C: 0.0005 to 0.9, preferably 0.05 to 0.35
Mn: 4 bis 12, vorzugsweise größer 5 bis kleiner 10 Mn: 4 to 12, preferably greater than 5 to less than 10
Rest Eisen einschließlich unvermeidbarer stahlbegleitender Elemente, Remainder of iron including unavoidable steel-accompanying elements,
mit optionaler Zulegierung von: with optional addition of:
AI: 0 bis 10, bevorzugt 0,05 bis 5, insbesondere bevorzugt größer 0,5 bis 3 Al: 0 to 10, preferably 0.05 to 5, particularly preferably greater than 0.5 to 3
Si: 0 bis 6, bevorzugt 0,05 bis 3, insbesondere bevorzugt 0,1 bis 1 ,5 Si: 0 to 6, preferably 0.05 to 3, particularly preferably 0.1 to 1.5
Cr: 0 bis 6, bevorzugt 0,1 bis 4, insbesondere bevorzugt größer 0,5 bis 2,5 Cr: 0 to 6, preferably 0.1 to 4, particularly preferably greater than 0.5 to 2.5
Nb: 0 bis 1 , bevorzugt 0,005 bis 0,4, insbesondere bevorzugt 0,01 bis 0,1 Nb: 0 to 1, preferably 0.005 to 0.4, particularly preferably 0.01 to 0.1
V: 0 bis 1 ,5, bevorzugt 0,005 bis 0,6, insbesondere bevorzugt 0,01 bis 0,3 V: 0 to 1, 5, preferably 0.005 to 0.6, particularly preferably 0.01 to 0.3
Ti: 0 bis 1 ,5, bevorzugt 0,005 bis 0,6, insbesondere bevorzugt 0,01 bis 0,3 Ti: 0 to 1.5, preferably 0.005 to 0.6, particularly preferably 0.01 to 0.3
Mo: 0 bis 3, bevorzugt 0,005 bis 1 ,5, insbesondere bevorzugt 0,01 bis 0,6 Mo: 0 to 3, preferably 0.005 to 1.5, particularly preferably 0.01 to 0.6
Sn: 0 bis 0,5, bevorzugt kleiner 0,2, insbesondere bevorzugt kleiner 0,05 Sn: 0 to 0.5, preferably less than 0.2, particularly preferably less than 0.05
Cu: 0 bis 3, bevorzugt kleiner 0,5, insbesondere bevorzugt kleiner 0,1 Cu: 0 to 3, preferably less than 0.5, particularly preferably less than 0.1
W: 0 bis 5, bevorzugt 0,01 bis 3, insbesondere bevorzugt 0,2 bis 1 ,5 W: 0 to 5, preferably 0.01 to 3, particularly preferably 0.2 to 1.5
Co: 0 bis 8, bevorzugt 0,01 bis 5, insbesondere bevorzugt 0,3 bis 2 Co: 0 to 8, preferably 0.01 to 5, particularly preferably 0.3 to 2
Zr: 0 bis 0,5, bevorzugt 0,005 bis 0,3, insbesondere bevorzugt 0,01 bis 0,2  Zr: 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.2
Ta: 0 bis 0,5, bevorzugt 0,005 bis 0,3, insbesondere bevorzugt 0,01 bis 0,1 Ta: 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.1
Te: 0 bis 0,5, bevorzugt 0,005 bis 0,3, insbesondere bevorzugt 0,01 bis 0,1 Te: 0 to 0.5, preferably 0.005 to 0.3, particularly preferably 0.01 to 0.1
B: 0 bis 0,15, bevorzugt 0,001 bis 0,08, insbesondere bevorzugt 0,002 bis 0,01 P: kleiner 0,1 , bevorzugt kleiner 0,04 S: kleiner 0,1 , bevorzugt kleiner 0,02 B: 0 to 0.15, preferably 0.001 to 0.08, particularly preferably 0.002 to 0.01 P: less than 0.1, preferably less than 0.04 S: less than 0.1, preferably less than 0.02
N: kleiner 0,1 , bevorzugt kleiner 0,05. N: less than 0.1, preferably less than 0.05.
1 1 . Verfahren nach einem der Ansprüche 1 bis 10, dadurch gekennzeichnet, dass das Stahlflachprodukt metallisch, anorganisch oder organisch beschichtet wird.  1 1. Method according to one of claims 1 to 10, characterized in that the flat steel product is coated metallic, inorganic or organic.
12. Stahlflachprodukt hergestellt nach einem Verfahren nach mindestens einem der Ansprüche 1 bis 1 1 . 12. Flat steel product prepared by a process according to any one of claims 1 to 1 1st
13. Verwendung eines nach einem Verfahren nach mindestens einem der 13. Use of a method according to at least one of
vorgenannten Ansprüche 1 bis 1 1 hergestellten Stahlflachprodukts im the above-mentioned claims 1 to 1 1 produced flat steel product in
Kraftfahrzeugbau, Schienenfahrzeugbau, Schiffsbau, Anlagenbau, Infrastrukturbau, Bergbau, in der Luft- und Raumfahrt, Hausgerätetechnik und in geschweißten Platinen.  Automotive engineering, rail vehicle construction, shipbuilding, plant construction, infrastructure construction, mining, in the aerospace industry, home appliance technology and in welded circuit boards.
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US20190203311A1 (en) 2019-07-04
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US11261503B2 (en) 2022-03-01
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RU2734216C1 (en) 2020-10-13

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