EP3512968A1 - Procédé pour fabriquer un produit plat en acier à partir d'un acier au manganèse et produit plat en acier résultant - Google Patents

Procédé pour fabriquer un produit plat en acier à partir d'un acier au manganèse et produit plat en acier résultant

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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)
English (en)
Other versions
EP3512968B1 (fr
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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Application filed by Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Publication of EP3512968A1 publication Critical patent/EP3512968A1/fr
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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
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
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    • 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
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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
    • C21D8/0273—Final recrystallisation annealing
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    • 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
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • 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
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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
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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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • 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
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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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
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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
    • C21D8/0205—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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  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne un procédé pour fabriquer un produit plat en acier à partir d'un acier à teneur moyenne en manganèse à effet TRI P/TW IP. Afin d'améliorer limite d'élasticité apparente lors tout en conservant le potentiel de déformation résiduelle du produit plat en acier obtenu, les étapes suivantes sont proposées: laminage à froid d'une bande à chaud ou à froid, recuit de la bande à chaud ou à froid laminée à froid à une température de 500 à 840 °C pendant une durée de 1 min à 24 h, écrouissage ou planage de la bande à chaud ou à froid après recuit pour former un produit plat en acier avec un taux de réduction compris entre 0,3 % et 60 %. L'invention concerne également un produit plat en acier réalisé selon ce procédé et une utilisation de celui-ci.
EP17768090.7A 2016-09-16 2017-09-13 Procédé pour fabriquer un produit plat en acier à partir d'un acier au manganèse et produit plat en acier résultant Active EP3512968B1 (fr)

Applications Claiming Priority (2)

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DE102016117508.0A DE102016117508B4 (de) 2016-09-16 2016-09-16 Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl und ein derartiges Stahlflachprodukt
PCT/EP2017/072994 WO2018050683A1 (fr) 2016-09-16 2017-09-13 Procédé pour fabriquer un produit plat en acier à partir d'un acier au manganèse et produit plat en acier résultant

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EP3512968A1 true EP3512968A1 (fr) 2019-07-24
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US (1) US11261503B2 (fr)
EP (1) EP3512968B1 (fr)
KR (1) KR102298180B1 (fr)
DE (1) DE102016117508B4 (fr)
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WO (1) WO2018050683A1 (fr)

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CN108504959B (zh) * 2018-06-04 2019-11-12 福州大学 一种复合合金化处理的奥氏体中锰钢及其制备方法
CN109440010B (zh) * 2018-12-20 2021-08-13 唐山钢铁集团高强汽车板有限公司 一种1100MPa级高强捆带钢及其生产方法
US11827961B2 (en) * 2020-12-18 2023-11-28 Vacuumschmelze Gmbh & Co. Kg FeCoV alloy and method for producing a strip from an FeCoV alloy

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KR20190052683A (ko) 2019-05-16
WO2018050683A1 (fr) 2018-03-22
US20190203311A1 (en) 2019-07-04
RU2734216C9 (ru) 2020-11-12
EP3512968B1 (fr) 2021-08-25
WO2018050683A8 (fr) 2018-05-11
RU2734216C1 (ru) 2020-10-13
KR102298180B1 (ko) 2021-09-07
DE102016117508A1 (de) 2018-03-22
DE102016117508B4 (de) 2019-10-10
US11261503B2 (en) 2022-03-01

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