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EP3512968B1 - 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 Download PDF

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Publication number
EP3512968B1
EP3512968B1 EP17768090.7A EP17768090A EP3512968B1 EP 3512968 B1 EP3512968 B1 EP 3512968B1 EP 17768090 A EP17768090 A EP 17768090A EP 3512968 B1 EP3512968 B1 EP 3512968B1
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particularly preferably
hot
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cold
weight
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German (de)
English (en)
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EP3512968A1 (fr
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Peter PALZER
Thomas Dr. Evertz
Manuel Dr. Otto
Kai Dr. KÖHLER
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Salzgitter Flachstahl GmbH
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Salzgitter Flachstahl GmbH
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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
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
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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
    • C21D8/0236—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
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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
    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • 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
    • 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
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    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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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
    • 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
    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
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    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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    • 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
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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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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a method for producing a flat steel product from a medium-manganese steel with a TRIP / TWIP effect, and a use for a flat steel product produced by this method.
  • a flat steel product made from a 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 steel melt): C: up 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 plus the remainder 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 equal to 0.5.
  • This steel is said to be characterized by the fact that it is more cost-effective to manufacture than steels with a high manganese content and at the same time has high elongation at break and, as a result, significantly improved formability.
  • TRIP steels have already been described, which have a predominantly ferritic basic structure with embedded retained austenite, which can convert to martensite during forming (TRIP effect). Because of its strong work hardening, TRIP steel achieves high values of uniform elongation and tensile strength. TRIP steels are suitable for use in structural, chassis and crash-relevant components of vehicles, as sheet metal blanks and as welded blanks.
  • German patent application DE 10 2015 111 866 A1 discloses a formable lightweight steel with a manganese content of 3 to 30% by weight and TRIP / TWIP properties, which is obtained by adding up to 0.8% by weight of antimony (Sb) and targeted heat treatment at 480 to 770 ° C exhibits improved material properties for 1 minute to 48 hours.
  • this steel has, in addition to improved tensile strength and elongation at break, increased resistance to hydrogen-induced cracking and hydrogen embrittlement.
  • This forming process with high elongation should have the advantage that, despite the high strength values, a plasticity reserve is retained, which enables subsequent final shaping into a finished component using conventional forming technology.
  • the steels selected for this are characterized by an Mn content in% by weight of 10 to 30.
  • Such high-manganese alloyed steels are more costly than medium-manganese steels due to their high alloying element content.
  • the present invention is based on the object of creating a method for producing a flat steel product from a steel with medium manganese content, and a use for a flat steel product produced by this method, which is achieved by improving the yield point while maintaining a sufficient residual deformability of the flat steel product produced distinguish.
  • a method for producing a flat steel product from a medium-manganese steel with a manganese content of 4 to 12, preferably greater than 5 to less than 10, wt .-% and with TRIP / TWIP effect comprising the steps: Cold strip, - Annealing the cold-rolled hot or cold strip at 500 to 840 ° C for 1 min. To 24 h, - Rerolling or skin-passing the annealed hot or cold strip to a flat steel product with a degree of deformation between 0.3% and 60% and with a yield point that is at least 50 MPa higher than that achieved before re-rolling or skin-passing, so that the re-rolling or skin-passing of the flat steel product increases its yield point.
  • the degree of deformation is usually related to the thickness direction of the flat steel product. By increasing the yield point, this flat steel product can be converted into optimized components with lower Sheet thickness can be produced.
  • the rerolling or skin passage causes a partial conversion of the metastable austenite of the annealed hot or cold strip into deformation twins (TWIP effect) and martensite (TRIP effect), whereby at least 3% of the austenite has to be converted into martensite and at least a proportion of 10% of the austenite is retained as a face-centered cubic phase.
  • the annealed hot or cold strip is re-rolled with a degree of deformation between 10 to 40%.
  • the annealed hot or cold strip is passaged with a degree of deformation between 0.6 and 2.2%.
  • the annealed hot or cold strip is re-rolled or skin-pass at a temperature of 0 to 400 ° C.
  • deformation twins are formed (TWIP effect) which, analogous to the dislocation density of other types of steel, increase the yield strength and / or yield strength.
  • the flat steel product has a tensile strength of greater than 1300 MPa and an elongation at break A80 of greater than 3%.
  • the hot or cold strip is cold-rolled with a first rolling pass at a temperature of the hot or cold strip from 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C.
  • the hot or cold strip is then intermediately heated or intermediately cooled between the further rolling passes following the first rolling pass to temperatures from 60 ° C to below Ac3, preferably from 60 ° C to 450 ° C.
  • the increase in temperature before the first rolling pass there is also a reduction in the required forming forces.
  • An increase in the residual deformability of the cold-rolled hot or cold strip with tensile strengths of greater than 800 MPa to 2000 MPa with elongations at break of greater than 3% is brought about in the most heavily formed areas.
  • the hot or cold strip can be preheated 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 converts metastable austenite into martensite (TRIP effect) during the rolling process. completely or partially suppressed, whereby deformation twins (TWIP effect) can form in the austenite. This results in an advantageous reduction in the rolling forces and increases the overall formability.
  • deformation twins are specifically introduced, which further convert to martensite at room temperature and thus increase the energy absorption capacity and allow a higher degree of deformation.
  • the flat steel product mentioned is to be understood as meaning cold re-rolled heavy plate, hot and / or cold strip.
  • This flat steel product made from the medium-manganese-containing TRIP (TRansformation Induced Plasticity) and / or TWIP (TWinning Induced Plasticity) steel has excellent cold and warm formability, increased resistance to hydrogen-induced delayed fracture, and hydrogen embrittlement. as well as against liquid metal embrittlement when welding in the galvanized state.
  • the usual thickness ranges for pre-strip are 1 mm to 35 mm and for slabs and thin slabs 35 mm to 450 mm. It is preferably provided that the slab or thin slab is hot rolled into a hot strip with a thickness of 20 mm to 0.8 mm or the pre-strip cast close to its final dimensions is hot rolled into 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.
  • a pre-strip produced near net dimensions using the two-roll casting method with a thickness of less than or equal to 3 mm, preferably 1 mm to 3 mm, is already understood as hot strip.
  • the pre-strip produced in this way as hot strip does not have a cast structure due to the reshaping of the two counter-rotating rolls. Hot rolling thus already takes place inline during the two-roll casting process, so that separate heating and hot rolling can optionally be omitted.
  • the cold rolling of the hot strip can take place at room temperature or advantageously at an elevated temperature with heating before the first rolling pass and / or heating in a further or between several rolling passes.
  • Cold rolling at elevated temperatures is advantageous in order to reduce the rolling forces and to promote the formation of deformation twins (TWIP effect).
  • Advantageous temperatures of the rolling stock before the first rolling pass are 60 ° C to below the Ac3 temperature, preferably 60 to 450 ° C.
  • the cold rolling takes place in several rolling passes, it is advantageous to temporarily heat or cool the steel strip between the rolling passes to a temperature of 60 ° C to below Ac3 temperature, preferably 60 ° C to 450 ° C, since the TWIP effect in this area particularly advantageous for Carry comes.
  • both intermediate heating e.g. at very low degrees of deformation and rolling speeds, as well as additional cooling, due to the heating of the material during fast rolling and high degrees of deformation, can be carried out.
  • the steel strip After cold rolling the hot strip at room temperature, the steel strip should be annealed in a continuous annealing plant, hood annealing plant or other continuous or discontinuous annealing plant with an annealing time of 1 min. To 24 h and temperatures of 500 to 840 ° C to restore sufficient forming properties. If necessary to achieve certain material properties, this annealing process can also be carried out with the steel strip rolled at an elevated temperature.
  • the steel strip is advantageously cooled to a temperature of 250 ° C to room temperature and then, if necessary, to set the required mechanical properties, in the course of an aging treatment, heated again to a temperature of 300 to 450 ° C at this temperature held for up to 5 minutes and then cooled to room temperature.
  • the aging treatment can advantageously be carried out in a continuous annealing plant.
  • the flat steel product produced in this way can optionally be electrolytically galvanized or hot-dip galvanized.
  • the steel strip produced in this way receives a coating on an organic or inorganic basis instead of or after electrolytic galvanizing or hot-dip galvanizing.
  • These can be, for example, organic coatings, plastic coatings or lacquers or other inorganic coatings such as iron oxide layers.
  • a component manufactured according to the above-described method can advantageously be used in motor vehicle construction, rail vehicle construction, shipbuilding, plant construction, infrastructure construction, in aerospace, domestic appliance technology and in welded blanks (tailored welded blanks).
  • 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 from over 1100 to 1200 MPa: Rm x A80 ⁇ 25,000 up to 45,000 - Rm from over 1200 to 1400 MPa: Rm x A80 ⁇ 20,000 up to 42,000 - Rm from over 1400 to 1800 MPa: Rm x A80 ⁇ 10,000 up to 40,000 - Rm of over 1800 MPa: Rm x A80 ⁇ 7200 up to 20000
  • specimen form 2 with an initial gauge length of A80 was used in accordance with DIN 50 125.
  • Alloy elements are usually added to steel in order to specifically influence certain properties.
  • An alloy element can influence different properties in different steels. The effect and interaction generally depends heavily on the amount, the presence of other alloying elements and the state of solution in the material. The relationships are varied 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 positive effects of the alloying elements used according to the invention are described below.
  • Carbon C Is required for the formation of carbides, stabilizes the austenite and increases the strength. Higher contents of C worsen the welding properties and lead to a deterioration in the elongation and toughness properties, which is why a maximum content of 0.9% by weight, preferably 0.35% by weight, is specified. In order to achieve the desired combination of strength and elongation properties of the material, a minimum addition of 0.0005% by weight, preferably 0.05% by weight, is required.
  • Manganese Mn Stabilizes austenite, increases strength and toughness and enables deformation-induced martensite and / or twin formation in the alloy according to the invention. Contents of less than 4% by weight are not sufficient to stabilize the austenite and thus worsen the elongation properties, while with contents of 12% by weight and more the austenite is too strongly stabilized and thus the strength properties, in particular the 0.2% yield strength, be reduced. For the manganese steel according to the invention with medium manganese contents, a range from greater than 5 to less than 10% by weight is preferred.
  • Aluminum Al improves the strength and elongation properties, lowers the specific density and influences the transformation behavior of the alloy according to the invention. Too high a content of Al worsens the elongation properties. Higher Al contents also significantly worsen the casting behavior in continuous casting. This results in a higher effort when potting. High Al contents delay the precipitation of carbides in the alloy according to the invention.
  • Silicon Si The optional addition of Si in higher contents hinders the carbon diffusion, reduces the specific density and increases the strength and the elongation and toughness properties. Furthermore, an improvement in cold rollability could be observed through the addition of Si. Higher Si contents lead to embrittlement of the material and have a negative effect on hot and cold rollability and coatability, for example through galvanizing.
  • Chromium Cr The optional addition of Cr improves the strength and reduces the corrosion rate, delays the formation of ferrite and pearlite and forms carbides. Higher contents lead to a deterioration in the elongation properties.
  • Micro-alloy elements are usually only used in very small quantities admitted. In contrast to the alloying elements, they work mainly through the formation of precipitates, but can also influence the properties in a dissolved state. Even small amounts of the micro-alloying elements have a considerable influence on the processing and final properties. In hot forming in particular, micro-alloy elements have an advantageous effect on the recrystallization behavior and cause grain refinement.
  • Typical micro-alloy elements are vanadium, niobium and titanium. These elements can be dissolved in the iron lattice and form carbides, nitrides and carbonitrides with carbon and nitrogen.
  • Vanadium V and niobium Nb These have a grain-refining effect due to the formation of carbides, which at the same time improves strength, toughness and elongation properties. Contents of more than 1.5% by weight or 1% by weight have no further advantages.
  • Titanium Ti Has a grain-refining effect as a carbide former, which at the same time improves strength, toughness and elongation properties and reduces intergranular corrosion. Contents of Ti of more than 1.5% by weight deteriorate the elongation properties, which is why a maximum content of 1.5% by weight, preferably 0.6% by weight, particularly preferably 0.3% by weight, is optionally specified . Minimum contents of 0.005% by weight, preferably 0.01% by weight, can be provided in order to bind nitrogen and advantageously precipitate Ti.
  • Molybdenum Mo Acts as a carbide former, increases the strength and increases the resistance against delayed crack formation and hydrogen embrittlement. High contents of Mo impair the elongation properties.
  • Tin Sn Tin increases the strength, but, like copper, accumulates under the scale and at the grain boundaries at higher temperatures. Penetrating into the grain boundaries leads to the formation of low-melting phases and the associated cracks in the structure and solder brittleness, which is why an optional maximum content of 0.5% by weight, preferably less than 0.2% by weight, particularly preferably less 0.05 wt%, is provided.
  • Copper Cu Reduces the rate of corrosion and increases strength. Contents above 3 wt .-% worsen the manufacturability by the formation of low-melting phases during casting and hot rolling, which is why optionally a maximum content of 3 wt .-%, preferably less than 0.5 wt .-%, particularly preferably less than 0.1 wt. -%, is determined.
  • Tungsten W Acts as a carbide former and increases strength and heat resistance. W contents of more than 5% by weight impair the elongation properties, which is why a maximum content of 5% by weight is optionally specified. A content of 0.01% by weight to 3% by weight is preferably provided, and particularly preferably 0.2 to 1.5% by weight.
  • Cobalt Co Increases the strength of the steel, stabilizes the austenite and improves the high temperature strength. Contents of more than 8% by weight impair the elongation properties.
  • the Co content is therefore set at a maximum of 8% by weight, preferably from 0.01 to 5% by weight, particularly preferably from 0.3 to 2% by weight.
  • Zirconium Zr Acts as a carbide former and improves strength. Zr contents of more than 0.5% by weight deteriorate the elongation properties. A Zr content of 0 to 0.5% by weight, preferably 0.005 to 0.3% by weight, particularly preferably 0.01 to 0.2% by weight, is therefore specified.
  • Tantalum Ta Like niobium, tantalum has a grain-refining effect as a carbide former and thereby improves strength, toughness and elongation properties at the same time. Contents of more than 0.5% by weight do not bring about any further improvement in the properties. A maximum content of 0.5% by weight is therefore optionally specified. A minimum content of 0.005 and a maximum content of 0.3% by weight are preferably specified, in which the grain refinement can advantageously be effected. To improve the A content of 0.01% by weight to 0.1% by weight is particularly preferred for economy and optimization of the grain refinement.
  • Tellurium Te improves the corrosion resistance and the mechanical properties as well as the 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 impair the elongation and toughness properties, which is why a maximum content of 0.5% by weight is specified. Optionally, a minimum content of 0.005% by weight and a maximum content of 0.3% by weight are specified, which advantageously improve the mechanical properties and increase the strength of the MnS present. Furthermore, a minimum content of 0.01% by weight and a maximum content of 0.1% by weight are preferred, which enable the mechanical properties to be optimized with a simultaneous reduction in alloy costs.
  • MnS manganese sulfides
  • Boron B Boron retards the austenite transformation, improves the hot forming properties of steels and increases the strength at room temperature. It develops its effect even with very low alloy contents. Contents above 0.15% by weight greatly impair the elongation and toughness properties, which is why the maximum content is set at 0.15% by weight.
  • a minimum content of 0.001% by weight and a maximum content of 0.08, preferably a minimum content of 0.002% by weight and a maximum content of 0.01, are specified in order to advantageously use the strength-increasing effect of boron.
  • Phosphorus P is a trace element, comes mainly from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphorus increases hardness through solid solution strengthening and improves hardenability. As a rule, however, the aim is to lower the phosphorus content as much as possible, since, among other things, due to its low diffusion rate, it is very susceptible to segregation and to a great extent reduces the toughness. The accumulation of phosphorus at the grain boundaries can cause cracks to appear 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 aforementioned reasons, the phosphorus content is less than 0.1% by weight, preferably less than 0.04% by weight, limited.
  • Sulfur S Like phosphorus, it is bound in coke as a trace element in iron ore but especially during the production route via the blast furnace process. It is generally undesirable in steel because it tends to segregate strongly and has a strong embrittling effect, as a result of which the elongation and toughness properties are impaired. Attempts are therefore made to achieve the lowest possible amounts of sulfur in the melt (for example by means of deep desulphurisation). For the reasons mentioned above, the sulfur content is limited to values less than 0.1% by weight, preferably less than 0.02% by weight.
  • N is also an accompanying element in steel production. In the dissolved state, it improves the strength and toughness properties of steels with a higher manganese content with greater than or equal to 4% by weight Mn. Lower Mn-alloyed steels with less than 4% by weight tend to have a strong aging effect in the presence of free nitrogen. The nitrogen diffuses at dislocations even at low temperatures and blocks them. It thus causes an increase in strength combined with a rapid loss of toughness.
  • the nitrogen can be set in the form of nitrides, for example, by adding titanium or aluminum to the alloy, with aluminum nitrides in particular having a negative effect on the forming properties of the alloy according to the invention. For the reasons mentioned above, the nitrogen content is limited to less than 0.1% by weight, preferably less than 0.05% by weight.

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Claims (11)

  1. Procédé d'obtention d'un produit plat en acier à partir d'un acier à teneur moyenne en manganèse dont la teneur en manganèse va de 4 à 12, de préférence de plus 5 à moins de 10, en % en poids et ayant un effet TRIP/TWIP, ledit procédé comprenant les étapes suivantes :
    - laminer à froid un feuillard à chaud ou à froid,
    - recuire le feuillard à chaud ou à froid laminé à froid à une température allant de 500 à 840°C pendant 1 min à 24 h,
    - passer le feuillard à chaud ou à froid recuit au laminoir d'écrouissage ou de dressage pour obtenir un produit plat en acier dont le degré de déformation est compris entre 0,3 % et 60 % et dont la limite d'élasticité est augmentée d'au moins 50 MPa par rapport à celle avant le passage au laminoir d'écrouissage ou de dressage.
  2. Procédé selon la revendication 1, caractérisé en ce que le feuillard à chaud ou à froid recuit est passé au laminoir d'écrouissage avec un degré de déformation compris entre 10 et 40 %.
  3. Procédé selon la revendication 1 ou 2, caractérisé en ce que le feuillard à chaud ou à froid recuit est passé au laminoir de dressage avec un degré de déformation compris entre 0,6 et 2,2 %.
  4. Procédé selon l'une au moins des revendications 1 à 3, caractérisé en ce que le feuillard à chaud ou à froid est laminé à froid avec une première passe de laminage à une température du feuillard à chaud ou à froid allant de 60°C à au-dessous de Ac3, de préférence de 60°C à 450°C.
  5. Procédé selon la revendication 4, caractérisé en ce que le feuillard à chaud ou à froid est chauffée intermédiairement ou refroidie intermédiairement à des températures allant de 60°C à au-dessous de Ac3, de préférence de 60°C à 450°C, entre les autres passes de laminage suivant la première passe de laminage.
  6. Procédé selon l'une au moins des revendications 1 à 5, caractérisé en ce que le feuillard à chaud ou à froid recuit est passé au laminoir d'écrouissage ou de dressage à une température de 0 à 400°C.
  7. Procédé selon l'une au moins des revendications 1 à 6, caractérisé en ce que le produit plat en acier a une résistance à la traction supérieure à 1300 MPa et un allongement à la rupture A80 supérieur à 3 %.
  8. Procédé selon l'une au moins des revendications 1 à 7, caractérisé en ce que le passage au laminoir d'écrouissage ou de dressage permet d'obtenir un produit plat en acier dont l'austénite métastable est partiellement transformée en macles de déformation (effet TWIP) et en martensite (effet TRIP), au moins une proportion de 3 % de l'austénite métastable étant convertie en martensite et au moins une proportion de 10 % de l'austénite métastable étant conservée sous forme de phases centrées sur les faces d'un cube.
  9. Procédé selon l'une au moins des revendications 1 à 8, caractérisé en ce que le produit plat en acier est obtenu avec la composition chimique suivante (en % en poids) :
    C : de 0,0005 à 0,9, de préférence de 0,05 à 0,35
    Mn : de 4 à 12, de préférence de plus de 5 à moins de 10
    le reste étant du fer, y compris des éléments d'accompagnement de l'acier inévitables,
    avec ajout optionnel par alliage de :
    Al : de 0 à 10, de préférence de 0,05 à 5, de manière particulièrement préférée plus de 0,5 à 3
    Si : de 0 à 6, de préférence de 0,05 à 3, de manière particulièrement préférée de 0,1 à 1,5
    Cr : de 0 à 6, de préférence de 0,1 à 4, de manière particulièrement préférée plus de 0,5 à 2,5
    Nb : de 0 à 1, de préférence de 0,005 à 0,4, de manière particulièrement de 0,01 à 0,1
    V : de 0 à 1,5, de préférence de 0,005 à 0,6, de manière particulièrement de 0,01 à 0,3
    Ti : de 0 à 1,5, de préférence de 0,005 à 0,6, de manière particulièrement de 0,01 à 0,3
    Mo : de 0 à 3, de préférence de 0,005 à 1,5, de manière particulièrement de 0,01 à 0,6
    Sn : de 0 à 0,5, de préférence moins de 0,2, de manière particulièrement préférée moins de 0,05
    Cu : de 0 à 3, de préférence moins de 0,5, de manière particulièrement préférée moins de 0,1
    W : de 0 à 5, de préférence 0,01 à 3, de manière particulièrement de 0,2 à 1,5
    Co : de 0 à 8, de préférence de 0,01 à 5, de manière particulièrement de 0,3 à 2
    Zr : de 0 à 0,5, de préférence de 0,005 à 0,3, de manière particulièrement de 0,01 à 0,2
    Ta : de 0 à 0,5, de préférence de 0,005 à 0,3, de manière particulièrement de 0,01 à 0,1
    Te : de 0 à 0,5, de préférence de 0,005 à 0,3, de manière particulièrement de 0,01 à 0,1
    B : de 0 à 0,15, de préférence de 0,001 à 0,08, de manière particulièrement de 0,002 à 0,01
    P : moins de 0,1, de préférence moins de 0,04
    S : moins de 0,1, de préférence moins de 0,02
    N : moins de 0,1, de préférence moins de 0,05.
  10. Procédé selon l'une des revendications 1 à 9, caractérisé en ce que le produit plat en acier est revêtu d'un revêtement métallique, minérale ou organique.
  11. Utilisation d'un produit plat en acier obtenu par un procédé selon l'une au moins des revendications précédentes 1 à 10 dans la construction automobile, la construction de véhicules ferroviaires, la construction navale, la construction d'usines, la construction d'infrastructures, l'exploitation minière, dans l'aérospatiale, la technologie de l'électroménager et dans des flans soudés.
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)

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Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ES2903435T3 (es) * 2016-09-29 2022-04-01 Outokumpu Oy Método para la deformación en frío de un acero austenítico
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
KR102699825B1 (ko) * 2022-03-15 2024-08-27 한양대학교 에리카산학협력단 니켈(Ni)-알루미늄(Al)계 석출물을 포함하는 중망간강과 그 제조 방법

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10259230A1 (de) * 2002-12-17 2004-07-15 Thyssenkrupp Stahl Ag Verfahren zum Herstellen eines Stahlprodukts

Family Cites Families (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5384206A (en) 1991-03-15 1995-01-24 Nippon Steel Corporation High-strength cold-rolled steel strip and molten zinc-plated high-strength cold-rolled steel strip having good formability and method of producing such strips
FR2796083B1 (fr) 1999-07-07 2001-08-31 Usinor Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites
DE102004054444B3 (de) 2004-08-10 2006-01-19 Daimlerchrysler Ag Verfahren zur Herstellung von Stahlbauteilen mit höchster Festigkeit und Plastizität
DE102005052774A1 (de) 2004-12-21 2006-06-29 Salzgitter Flachstahl Gmbh Verfahren zum Erzeugen von Warmbändern aus Leichtbaustahl
EP1846584B2 (fr) 2005-02-02 2022-12-14 Tata Steel IJmuiden B.V. Acier austénitique à haute résistance et procédé pour sa fabrication et son utilisation
KR20070085757A (ko) * 2007-06-04 2007-08-27 티센크루프 스틸 악티엔게젤샤프트 Ｔｗｉｐ 특성을 갖는 고강도 강 스트립 또는 박판 및 직접스트립 주조에 의한 상기 스트립 제조 방법
JP5365216B2 (ja) 2008-01-31 2013-12-11 Ｊｆｅスチール株式会社 高強度鋼板とその製造方法
CN102639742B (zh) * 2009-11-18 2016-03-30 新日铁住金株式会社 奥氏体系不锈钢板及其制造方法
EP2383353B1 (fr) 2010-04-30 2019-11-06 ThyssenKrupp Steel Europe AG Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication
JP6009438B2 (ja) 2010-06-10 2016-10-19 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ オーステナイト鋼の製造方法
JP5729211B2 (ja) * 2010-08-31 2015-06-03 Ｊｆｅスチール株式会社 冷延鋼板の製造方法、冷延鋼板および自動車部材
KR20120065464A (ko) * 2010-12-13 2012-06-21 주식회사 포스코 항복비 및 연성이 우수한 오스테나이트계 경량 고강도 강판 및 그의 제조방법
JP2013104114A (ja) 2011-11-15 2013-05-30 Jfe Steel Corp 曲げ加工性に優れた冷延鋼板およびその製造方法
JP2013224476A (ja) 2012-03-22 2013-10-31 Jfe Steel Corp 加工性に優れた高強度薄鋼板及びその製造方法
DE102012013113A1 (de) 2012-06-22 2013-12-24 Salzgitter Flachstahl Gmbh Hochfester Mehrphasenstahl und Verfahren zur Herstellung eines Bandes aus diesem Stahl mit einer Mindestzugfestigkleit von 580MPa
KR101480497B1 (ko) 2012-10-15 2015-01-09 주식회사 포스코 동적 재결정을 이용한 쌍정유기소성강판 제조 방법 및 이에 의해 제조되는 쌍정유기소성 강판
DE102013003516A1 (de) 2013-03-04 2014-09-04 Outokumpu Nirosta Gmbh Verfahren zur Herstellung eines ultrahochfesten Werkstoffs mit hoher Dehnung
FI126798B (en) * 2013-07-05 2017-05-31 Outokumpu Oy Delayed fracture resistant stainless steel and method for its production
JP6237365B2 (ja) 2014-03-17 2017-11-29 新日鐵住金株式会社 成形性と衝突特性に優れた高強度鋼板
MX2017005569A (es) * 2014-10-30 2017-06-23 Jfe Steel Corp Lamina de acero de alta resistencia y metodo para la fabricacion de la misma.
DE102015111866A1 (de) 2015-07-22 2017-01-26 Salzgitter Flachstahl Gmbh Umformbarer Leichtbaustahl mit verbesserten mechanischen Eigenschaften und Verfahren zur Herstellung von Halbzeug aus diesem Stahl
JP6635463B2 (ja) 2015-09-04 2020-01-22 トヨタ車体株式会社 拡散接合方法

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10259230A1 (de) * 2002-12-17 2004-07-15 Thyssenkrupp Stahl Ag Verfahren zum Herstellen eines Stahlprodukts

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