EP3899059A1 - Procédé de fabrication de produits de type feuillard à chaud profilés obtenus par voie thermomécanique - Google Patents

Procédé de fabrication de produits de type feuillard à chaud profilés obtenus par voie thermomécanique

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Publication number
EP3899059A1
EP3899059A1 EP19832074.9A EP19832074A EP3899059A1 EP 3899059 A1 EP3899059 A1 EP 3899059A1 EP 19832074 A EP19832074 A EP 19832074A EP 3899059 A1 EP3899059 A1 EP 3899059A1
Authority
EP
European Patent Office
Prior art keywords
steel
temperature
rolling
hot
hardening
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.)
Pending
Application number
EP19832074.9A
Other languages
German (de)
English (en)
Inventor
Wolfgang Ernst
Helmut Spindler
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.)
Voestalpine Stahl GmbH
Original Assignee
Voestalpine Stahl GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Voestalpine Stahl GmbH filed Critical Voestalpine Stahl GmbH
Publication of EP3899059A1 publication Critical patent/EP3899059A1/fr
Pending legal-status Critical Current

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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/42—Induction heating
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/008—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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/085—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • 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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    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the invention relates to a method for producing thermo-mechanically produced and profiled or formed hot-rolled products according to the preamble of claim 1.
  • a hot-rolled strip is a steel strip which is produced by first melting a steel melt of a desired alloy with unavoidable impurities that are inherent in the steel melting process, as a rule in a converter. The melt is then usually placed in a metallurgical pan, in which further processing, in particular alloy setting, takes place. In addition, a wide variety of fresh processes are carried out in the converter in order to reduce unwanted accompanying elements.
  • the steel from the ladle is usually fed through a tundish of a continuous casting plant, in which the molten steel is cast into a theoretically endless slab.
  • the solidified steel strip is cut in the continuous casting plant into so-called slabs, which are tabular, with a thickness of several decimeters, a width of, for example, 1.5 m and a length of, for example, 6 m to 12 m.
  • Such slabs can then be further processed in rolling mills.
  • Such slabs are first preheated to the rolling temperature in a reheating oven and then reach the so-called hot (wide) strip mill.
  • the hot strip mill consists of a sequence of rolling stands, whereby a so-called reversing roughing stand is initially available, in which the slab is roughed.
  • the still very hot, bright-glowing steel strip is then introduced into the actual roll stands and passes through these roll stands, the strip being given a target thickness and width.
  • hot strips of this type can either be processed further directly as hot strips or further processed into thin sheet metal via a cold rolling mill.
  • hot strip is not only produced for further processing into thin sheet metal, but also represents a special steel specialty that can be directly processed with modifications.
  • Thermomechanical steel is a microalloyed steel material that is manufactured using a thermomechanical process. In the thermomechanical rolling process, a final temperature is maintained in a certain range. Material properties of the steel are achieved which cannot be achieved with heat treatment alone. This process cannot be repeated.
  • Thermomechanical steels have high strength and toughness and can be processed very well and in particular are particularly suitable for welding.
  • Thermomechanical rolling is a process in which certain usage properties of the steel, namely usually the strength and toughness, are improved by the combination of thermal action and plastic deformation.
  • thermal treatment There are various methods that involve thermal treatment and then forming, with a distinction being made at high and low temperatures.
  • the material is first formed at a certain temperature, followed by thermal treatment.
  • Micro-alloying elements are often added to thermally treated steels. These should precipitate as carbides and nit rides during hot forming in order to inhibit recrystallization. This leads to better mechanical properties by means of a grain change.
  • the tendency of titanium to form high-temperature stable nitrides is also used to prevent grain growth during austenite formation.
  • the precipitates formed later on during cooling also contribute to particle hardening.
  • the austenite In normal thermomechanical hot rolling processes, the austenite is deformed in a temperature range just above A 3 (iron-carbon diagram). The austenite form hardening takes place, steel-specific, about 500 ° C below the recrystallization temperature in the austenite. After conversion, this becomes extremely fine-needle martensite. In thermomechanical rolling during forming, for example in the pearlite stage, the strength is increased by refining the microstructure and possibly by precipitation hardening.
  • Thermomechanical rolling below 800 ° C forces micro-alloyed fine-grain structural steels to convert the non-crystallized austenite into an extremely fine-grained ferrite-pearlite structure. Subsequent accelerated cooling can even enable conversion to bainite or martensite, which leads to a further increase in strength.
  • WO2017 / 016582 A1 discloses a high-strength steel with a high minimum yield strength and a method for securing such a steel.
  • This steel has a composition that is summarized as follows:
  • Pcm [C] + [Si] / 30 + [Mn] / 20 + [Cu] / 20 + [Ni] / 60 + [Cr] / 20 + [Mo] / 15 + [V] / 10 + 5 [ B]; where [C], [Si], [Mn], [Cu], [Ni], [Cr], [Mo], [V], and [B] are the mass fractions of the respective elements in high-strength steel in% by weight and where the following applies to Pcm:
  • the hydrogen content is reduced by vacuum treatment of the steel melt, after which the steel melt is cast into a slab.
  • the slab is then heated to a temperature in the range from 1100 to 1250 °, descaled and then hot-rolled to a flat steel product.
  • the product is then coiled, the coiling temperature being at least 800 ° C, whereby when the slab is hot-rolled into a flat steel product, the initial rolling temperature is in the range from 1050 ° C to 1250 ° C and the final rolling temperature is> 880 ° C, and for the Pcm applies: 0.38% by weight ⁇ Pcm ⁇ 0.44% by weight.
  • the flat steel product is preferably subjected to a hardening treatment after hot rolling, the hardening treatment being at least 40 Kelvin above the A C 3 temperature of the steel alloy and the flat steel product then being quickly quenched, so that the cooling rate is at least 25 K / s to one is below 200 ° C.
  • Lower austenitization temperatures of ⁇ 860 ° C in combination with the coordinated chemical composition of this steel alloy lead to undesired partial austenitization, which is not desirable.
  • the austenizing temperature should preferably be ⁇ 920 ° C.
  • EP 2 267 177 Al discloses a high-strength steel sheet which is used as a structural element in industrial machines and which on the one hand is said to have excellent resistance to delayed breakage and on the other hand has good welding behavior.
  • This steel sheet has a minimum yield strength of 1300 MPa or higher and a tensile strength of 1400 MPa or higher.
  • the thickness of this steel sheet should be equal to or greater than 4.5 mm or equal to or less than 25 mm.
  • a high-strength, hot-rolled steel product and a method for producing the same are known from EP 2 789 699 A1.
  • the method comprises the steps of melting a steel having the following composition: C 0.25 to 0.45%, Si 0.01 to 1.5%, Mn 0.4 to 3.0%, Ni 0.5 to 4%, AI 0.01 to 1.2%, Cr ⁇ 2%, Mo ⁇ 1%, Cu ⁇ 1.5%, V ⁇ 0.5%, Nb ⁇ 0.2%, Ti ⁇ 0.2% , B ⁇ 0.01%, Ca ⁇ 0.01%, balance iron and unavoidable contamination, wherein the molten steel is poured into a slab and the slab is heated to a temperature in the range from 950 to 1350 °, followed by heating step, in which the slab is then hot rolled in a temperature range from Ar3 to 1300 ° C and then directly cooled, the cooling temperature being below the Ms temperature and the austenite grain structure of the steel product being stretched in the rolling direction, so that the length / width Ratio is 1.2.
  • a hot-rolled product is known from US 2007/0272333 A1, which is said to have high strength, the steel having a composition with 0.03 to 0.1% carbon, 0.2 to 2% silicon, 0.5 to 2 , 5% manganese, 0.02 to 0.1% aluminum, 0.2 to 1.5% chromium and 0.1 to 0.5% molybdenum, 80% by area having at least in the longitudinal direction a martensitic structure.
  • thermomechanical treatment method for heavy plates is known from EP 2 340 897 A1. This method serves to increase the toughness, especially the low-temperature toughness.
  • the heavy plate is heated, partially and finally formed by rolling and cooled faster than cooling at ambient temperature, the heavy plate being heated for partial forming to A C 3 temperature being cooled faster after its final forming.
  • the heavy plate between the partial and the final forming is cooled to below ar3 temperature and then inductively heated to above Ac3 temperature.
  • a rolled steel tube which is produced from a plurality of welded strips, the tube comprising metallic base areas, welding shocks and heat-affected zones, and having a tensile strength of more than 80 ksi, in addition to iron 0.17 to 0.35 wt% carbon, 0.3 to 2 wt% manganese, 0.1 to 0.3 %
  • silicon, 0.01 to 0.04% by weight aluminum, up to 9.01% sulfur and up to 0.015% by weight phosphorus can be present, the microstructure containing more than 90% by volume annealed martensite, wherein the microstructure should be homogeneous over all areas, namely the metallic base areas, the welding surges and the heat-affected zones, the microstructure should have a uniform distribution of carbides.
  • chromium 0.5% by weight molybdenum, 0.003% by weight boron, up to 0.03% by weight titanium, up to 0.5% copper, up to 0.5% nickel, up to 0 , 1 wt .-% niobium, 0.15 wt .-% vanadium and 0.05 wt .-% calcium with a maximum oxygen content of 0.005 wt .-%.
  • hot-rolled ultra-high-strength or wear-resistant steels for all possible forms of use are known from the prior art, which have a high strength with high toughness and good processability.
  • Products of this type are made available as broadband sheets or sheet products, these being produced in particular on broadband roads.
  • the rolling processes used are conventional hot rolling (WW) and thermo-mechanical rolling (TM).
  • WW hot rolling
  • TM thermo-mechanical rolling
  • the hot strips produced in conventional hot rolling processes or in the thermomechanical rolling process are produced after rolling either by slow cooling or quenching or direct hardening (DQ).
  • Pipes or profiles can also be produced using the rolling process, either using seamless tube rolling mills or so-called roll profiling lines.
  • the shaping processes used here are conventional hot rolling, thermo-mechanical rolling and roll profiling. Even with such pipes, there is a subsequent heat treatment, this heat treatment being either conventional flashing, i.e. pipe hardening, conventional tempering, i.e. pipe tempering and local weld post-treatment after welding processes, inductive heat treatments for normalizing clarifying and tempering are not unknown are.
  • the object of the invention is to provide a process for the production of thermo-mechanically manufactured and profiled hot-rolled products which, compared to conventionally produced thermo-mechanical hot-rolled products, have outstanding strength-toughness combinations and a fine isotropic structure.
  • thermo-mechanically produced and profiled hot-rolled products with the features of claim 1.
  • TM rolling In TM rolling, a substantial part of the forming takes place below the recrystallization stop temperature, which causes the austenite to stretch as shown in Figures 2 and 3.
  • TM rolling there is a finer end structure with a higher dislocation density.
  • the finer grain and the increased dislocation density increase the strength.
  • the finer grain structure also increases the toughness.
  • the hot strip product according to the invention has a predominantly martensitic structure, which is formed from globular, fine austenite grains and thus has homogeneous isotropic properties. This also applies to existing welds.
  • a hot strip is thermo-mechanically rolled and produced directly hardened, so that a predominantly martensitic structure is formed from an elongated austenite grain with a homogeneous carbon distribution.
  • the heat treatment is carried out differently than previously as a short-term heat treatment.
  • the short-term heat treatment according to the invention can be inductive hardening or induction hardening (hardening and tempering).
  • inductive hardening or induction hardening (hardening and tempering).
  • all forms of heating are suitable which allow a brief, preferably rapid, heating, with hardening at least once and tempering being optional.
  • a globular, fine austenite grain is obtained which, after conversion into a predominantly martensitic structure, has maximum strength and toughness values.
  • the heat treatment takes place after cooling to room temperature from the rolling. This means that no further work is carried out directly from the rolling heat and, in particular, hardening.
  • a short-term heat treatment is according to the invention, for example, a hardening ver, which is carried out one or more times, the heating rates depending on the cross section of the material to be heated up to 1000 K / s, this heating rate can decrease with increasing cross section.
  • the maximum temperature here is above A C 3, which means 800 ° C. to 1000 ° C., in particular 820 ° C. to 970 ° C.
  • the holding time at which the maximum temperature is maintained is 0.5 to 60 seconds, after which cooling is carried out, the cooling rates being between 10 K / s and over 60 K / s.
  • An optional tempering is carried out at temperatures below A ci , the temperatures being in particular between 300 ° C and 700 ° C.
  • a tempering temperature of between 500 ° C and 700 ° C can be advantageous to improve the weld seam properties, but a lower tempering temperature of 300 ° C to 450 ° C can be particularly advantageous to increase the yield strength.
  • a steel which has the following composition (all values in% by weight) is particularly suitable for the process according to the invention:
  • the following alloy composition is particularly suitable (all values in% by weight): 0.055 to 0.195 carbon,
  • the invention has the advantage that ultra-high-strength, profiled hot-rolled products with significantly improved properties in terms of toughness and isotropy can be produced, with good processability and, in particular, good weldability, and conventionally tempered profiles can be replaced here.
  • Inline in the invention is understood to mean that the entire heat treatment process takes place in one pass and that separate manipulation of lumpy profiles can advantageously be dispensed with.
  • the welding process step or production step results in a local change in the structure and the mechanical properties due to the energy (heat and / or pressure) introduced. Products therefore have inhomogeneous properties in the area of the weld seam.
  • the short-term heat treatment according to the invention is used in the course of production after a process step “welding”, as shown in FIG. 14 b for a fusion welding process, the microstructure in the weld seam area is homogenized aligned with that of the rest of the product.
  • welded pipes For pipes, the relatively inexpensive to manufacture welded pipes can be used as a replacement for seamless construction pipes, whereby there is little manufacturing effort and narrower thickness tolerances can be guaranteed.
  • the steel products are heated to greater than A C 3, for example 920 ° C., and are kept there in the minute range (for example 10 minutes), and then accelerated and cooled.
  • a tempering treatment is carried out after the hardening step, where the temperature is below A ci, for example at 570 ° C, and the tempering time is in the minute range (e.g. 15 minutes).
  • the curing takes place at z. B. 950 ° C, but only z. B. a second hold time is available, while the first heat treatment at 950 ° C for z. B. a second and the compensation step at z. B. 650 ° C also for z. B. takes a second.
  • the heating rate also affects the duration of the heat treatment, especially above the Ac3 point, and can also be interchangeable in a predictable way (more time, lower temperature and vice versa), the Hollomon-Jaffee parameter ( HJP), which maps both influencing factors.
  • HJP Hollomon-Jaffee parameter
  • the applicant then further developed it to provide meaningful results for continuous heat treatment processes, i.e. for heating up, maintaining at a maximum temperature and cooling down (Hubmer G., Ernst W., Klein M., Sonnleitner M., Spindler H.: A TRI- BUTE TO HOLLOMON & JAFFE -THE 70TH BIRTHDAY OF A BRILLIANT EQUATION,
  • Particularly advantageous mechanical properties in particular for the product of impact energy KV and tensile strength Rm, can result if the HJ parameters of the hardening process with heating to a maximum temperature of 800 ° C. to 1000 ° C., in particular 820 ° C. to 970 ° C. between 18000 and 23000 is preferably set between 18500 and 22000.
  • pipes or profiles can be produced which have a particularly good combination of high tensile strength Rm and high notched bar impact bending KV, particularly at low temperatures.
  • the product of Rm * KV can be> 70,000 MPaJ, preferably> 80,000 MPaJ, particularly preferably> 90,000 MPaJ, in particular> 100,000 MPaJ.
  • the invention thus relates to a method for producing thermo-mechanically manufactured hot strip products, wherein a steel alloy is melted, the steel alloy being set so that recrystallization during hot rolling is suppressed, the melted steel alloy being poured into slabs and the slabs after heating above AC 3 to a desired degree of forming a desired strip thickness are hot rolled, the strip after rolling to room temperature is cooled and briefly heated to> Ac3 and cooled again for the purpose of hardening, characterized in that the heating with a temperature increase of more than 5 K / s preferably with more than 10 K / s, particularly preferably with more than 50 K.
  • / s takes place in particular at more than 100 K / s and is held at a desired target temperature of 0.5 to 60 s and then cooling takes place, the steel strip or the blank, which was produced by thermo-mechanical rolling, in a forming pro is profiled into a component.
  • a steel alloy is melted, which contains the following elements and iron as well as unavoidable impurities, all details being in% by weight
  • a steel alloy is melted, which in particular contains the following elements and iron as well as inevitable impurities, all details being in% by weight
  • the short-term heating with all suitable forms of heating e.g. done inductively.
  • the target temperature during brief heating for hardening can be> AC3, which means 800 ° C. to 1000 ° C., in particular 820 ° C. to 970 ° C.
  • the target temperature during brief heating for tempering can be ⁇ Aci, the temperatures being in particular between 300 ° C. and 700 ° C.
  • the holding times at the target temperature during hardening and / or tempering and / or tempering can be less than 5 seconds.
  • the cooling after the heating step or steps can further advantageously take place with cooling rates of> 10 ° K / s. It is also advantageous if the cooling rate is> 30K / s and in particular> 60K / s.
  • hardening can be carried out directly from a rolling area (DQ).
  • DQ rolling area
  • the sheet thickness is 1.5 mm to 20 mm, in particular 3 mm to 15 mm.
  • the Hollomon-Jaffee parameter of the short-term curing process is between 18000 and 23000, preferably between 18500 and 22000.
  • the invention also relates to a profiled component produced with one of the prescribing NEN, at least one of the following mechanical properties being present:
  • the invention relates to the use of the components according to the invention for the manufacture of cranes for stationary and mobile applications on trucks, ships and Panze stanchions and wear applications in the automotive sector and in trailers and semitrailers for trucks, as well as for automotive support structures and frames.
  • Figure 1 shows the influence of conventional hot rolling on the structure
  • Figure 2 shows the influence of thermomechanical rolling on the structure
  • FIG. 3 the difference in the microstructure between recrystallized austenite and non-recrystallized austenite
  • Figure 4 shows the steel phases, based on the temperature curves driven
  • thermomechanically rolled and conventionally tempered product shows the comparison of the heat treatment routes for a thermomechanically rolled and conventionally tempered product, for a thermomechanically rolled product and for a thermomechanically rolled product according to the invention
  • FIG. 7 shows a detail of the structure in a thermomechanically rolled and tempered steel after the short-term heat treatment according to the invention
  • Figure 8a selected properties of a steel heat-treated according to the invention
  • Figure 8b product of tensile strength Rm and notched bar impact work KV as a function of the Hol-Imon-Jaffee parameter of the hardening process for short-term hardening according to the invention and conventional hardening of the steel (material A);
  • FIG. 9b product of tensile strength Rm and notched bar impact work KV as a function of the Hol-Imon-Jaffee parameter of the hardening process for short-term hardening according to the invention and conventional hardening of the steel (material B);
  • FIG. 10a shows the possible temperature-time profiles in the method according to the invention with the structure resulting in the individual manufacturing steps
  • FIG. 10b shows the possible temperature-time profiles in the method according to the invention with the structure of welded joints resulting from the individual manufacturing steps.
  • steel is rolled thermomechanically to increase the properties of toughness and isotropy as well as further properties.
  • conventionally hot-rolled steels are steels in which the rolling stock is first heated to the hot forming temperature and then rolled, whereby the undeformed grain is steered in the rolling direction, with recrystallization already taking place after the rolling pass, at the end of which the respective austenite grain is globular.
  • thermomechanically rolled steels contain higher levels of carbide formers, which form precipitates even during hot rolling.
  • the excretions or the dissolved microalloy elements delay or suppress the recrystallization after the rolling passes. Accordingly, there is no recrystallization and corresponding grain growth, so that, according to FIG. 2, a globular structure according to FIG. 1 is not formed, but the austenite is present in an elongated form.
  • thermomechanically rolled steels with the non-globular, stretched and deformed austenite grain results in a much finer structure after the transformation.
  • the forming has a significant impact on the structure and the properties, the properties cannot be achieved by the heat treatment alone.
  • thermomechanically rolled steels used are so-called micro-alloyed steels.
  • FIG. 4 shows schematically how different structures or microstructures can be achieved from the austenite area using different cooling curves. This shows that martensitic steels, complex phase steels, dual phase steels and ferritic-bainitic steels can be reached via different cooling paths. Conventional previous heat treatment routes are shown in Figure 5, lines 1 and 2.
  • thermomechanical rolling and a conventional tempering step a plate tempering that is used for sheet metal and thermomechanical rolling that can be combined with a direct hardening step (DQ) and a tempering step (A).
  • thermomechanical rolling an optional direct hardening (with an optional tempering step)
  • the hot strip Before this brief inductive hardening or tempering step, the hot strip is allowed to cool to room temperature or hardened (eg after direct hardening). Further processing from the rolling heat does not take place.
  • the temperature time profiles according to the prior art are shown in FIGS. 6a and 6b.
  • the differences in the structures can be seen in comparison to known structures according to FIGS. 6a and 6b and the structure according to the invention produced according to FIG. 10a.
  • the structure of the steel treated according to the invention, thermomechanically rolled and briefly heat-treated, differs significantly from that of conventionally treated steels, the smaller size and more isotropic shape of the grain structure being particularly noticeable.
  • the remuneration step is to be explained again, the conventional remuneration step being shown in FIG. 6a.
  • thermomechanically rolled and completely cooled With conventional tempering, a product is first heated in a reheating furnace and then thermomechanically rolled and completely cooled.
  • the mixture is then heated again to approx. 900 ° C and then subjected to rapid cooling in water and then a tempering step is carried out at approx. 600 ° C with subsequent cooling in air.
  • the conventional heat treatments not according to the invention are thus conventional heating (H) or table hardening, conventional tempering (H-i-A) or table hardening, conventional tempering (A) as table annealing or bonnet annealing.
  • thermomechanical rolling the anisotropy of the properties is generated by the stretching of the structure, whereby an annealing can create very good strength / toughness ratios, but only sheets and no strip heat can be treated.
  • thermomechanically produced hot strip (TM + DQ) which results in an elongated austenite grain and a homogeneous carbon distribution in the microstructure.
  • the subsequent heat treatments are carried out as short-term heat treatments.
  • the heating according to the invention is briefly heated briefly, the heat source being, for example, inductive heating, but not necessarily. According to the invention, it can be hardened at least once and optionally tempered once. This results in a globular fine austenite grain with maximized strength and maximized toughness.
  • Hardening can be carried out once or twice according to the invention, the heating rates being very high at 100 to 1000 ° K / s, the maximum temperature being set to> AC3. According to the invention, these are 800 ° C to 1000 ° C, in particular between 820 and 970 ° C.
  • the holding time is extremely short compared to the prior art and can be from 0.5 to 60 seconds and in particular from 0.5 to 5 seconds.
  • the heating rate can also be lower and be about 5 K / s or 10 K / s or 15 K / s.
  • the short holding times of 0.5 to 60 seconds are preferred, but not essential, further preferably 0.5 to 20 seconds, in particular 0.5 to 5 seconds.
  • the subsequent cooling rates are set at> 10 ° K / s to over 60 ° K / s.
  • the optional tempering is carried out at a maximum temperature below Aci, which is usually 300 ° C to 700 ° C.
  • a tempering temperature of between 500 ° C and 700 ° C can be advantageous, but a lower tempering temperature of 300 ° C to 450 ° C can be particularly advantageous to increase the yield point.
  • the short-term heat treatments according to the invention are thus on the one hand hardening or tempering treatments.
  • thermomechanically rolled, directly hardened and tempered steel has an elongated structure
  • steel produced according to the invention (TM + DQ + A + HKZ / HKZ + AKZ) has an isotropic globular structure.
  • the structure consists of 90% martensite (not tempered or tempered), the rest being austenite and bainite.
  • the former austenite grain is globular, with the grain size below 20 pm and in particular below 10 pm.
  • Figures 8a, 8b and 9a, 9b show examples of two alloy compositions (material A and material B) the achievable mechanical properties depending on the heat treatment routes and parameters. If a steel with the chemical composition shown in FIG. 8a is conventionally hardened, that is, austenitized, ie held at 920 ° C. for 10 minutes, the HJ parameter is 23380.
  • the mechanical properties for R p o. 2 are 907 MPa.
  • the R m at 1174 MPa and the notched bar impact work KV at 23 joules.
  • the product of Rm with KV is 27.002 MPaJ.
  • the R p o, 2 is 879 MPa
  • the R m is 934 MPa
  • the notched bar impact work is 23 Joules.
  • the product of Rm with KV is 21,482 MPaJ.
  • FIG. 8b the product of tensile strength and impact energy at -40 ° C. is plotted as a function of the HJ parameter for different hardening processes.
  • the light point corresponds to the previously described example A according to the invention with a HJ of 21,879 and the dark point to the prior art.
  • the HJ value should be between 18000 and 22000 and the maximum temperature in the range of 800 - 1000 ° C. If the HJP is too small and the maximum temperatures are too low, there is no complete austenitization and the material cannot be fully hardened.
  • the HJP and the maximum temperature of the hardening process should not be too high either, HJP should be below 23000 in particular, as otherwise the mechanical properties (especially the product of Rm and KV) can drop drastically.
  • FIG. 9a it can be seen from FIG. 9a that, in the case of a different alloy layer and the comparison of the values that can be achieved, the short-term heat treatment in turn leads to optimal property combinations.
  • FIG. 10a shows the temperature-time profile according to a possible embodiment of the invention together with the structures that arise.
  • thermomechanical rolling which is converted into a martensitic grain by the direct hardening, an annealing treatment being carried out if necessary.
  • this elongated grain enriched with dislocations due to the thermomechanical treatment and direct hardening, is converted into a fine, globular grain.
  • thermomechanical rolls according to the invention the subsequent heat treatments being carried out as short-term heat treatments, it is advantageous that a structure with improved properties is achieved, the short-term heat treatments also allowing these heat treatment processes to be carried out inline,
  • the welding process step or production step results in a local change in the structure and the mechanical properties due to the energy (heat and / or pressure) introduced. Products therefore have inhomogeneous properties in the area of the weld seam.
  • the short-term heat treatment according to the invention is used in the course of production after a process step “welding”, as shown in FIG. 10 b for a fusion welding process, the microstructure in the weld area becomes flomogenized.
  • the micro structure of the weld area and also its mechanical properties become aligned with that of the rest of the product. This applies to fusion welded connections such as laser welding as well as pressure welded connections such as high frequency welding.
  • the product according to the invention is produced by first melting a steel with the composition according to the invention, in particular that shown in figures. 8 or 9 specified chemical composition is melted in the steelworks and cast into a slab in a continuous casting plant after the secondary metal lurgic treatment.
  • the slab is then heated to a temperature in the range from 1100 ° C to 1300 ° C, in particular 1200 ° C to 1260 ° C, descaled and then thermomechanically hot-rolled into a steel strip, the rolling starting temperature being in the range from when the slab is hot-rolled 1000 ° C to 1250 ° C and the final roll temperature is greater than 800 ° C, in particular between 830 ° C and 930 ° C.
  • a significant part of the forming takes place below the recrystallization stop temperature, which causes the austenite to stretch, as shown in Figure 2.
  • the steel strip is cooled from the final rolling temperature to the coiling temperature by means of water application and coiled.
  • the reel temperature in the present example is below the martensite start temperature, which is less than 500 ° C, in particular less than 250 ° C, and is achieved with a cooling rate of greater than 25 ° C / s, in particular between 40 ° C / s and 100 ° C / s.
  • the steel strip is optionally subjected to a heat treatment, with or without an upstream cut (e.g. cross or longitudinal parts), the temperature being below the Al temperature, in particular below 700 ° C.
  • Blanks from steel strip produced according to the invention can optionally be connected by a welding process. These blanks can have different dimensions or chemical compositions.
  • the steel strip or the blank is formed into a component (profile, tube, edge part) in a forming process with an optionally integrated welding process (e.g. in a roll profiling or bending system).
  • either the steel strip is then subjected to a short-term heat treatment before the forming or the formed component (profile, tube, edge part).
  • the product is first heated at least once to a maximum temperature above Ac3, which is typically 800 ° C. to 1000 ° C., but in particular 820 ° C. to 970 ° C., briefly heated to temperature and then rapidly cooled.
  • the heating rates are more than 5 K / s, preferably more than 10 K / s, particularly preferably more than 50 K / s, in particular more than 100 K / s.
  • the holding time at the maximum temperature is 0.5 to 60 seconds, for example 1 to 10s, finally cooling with cooling rates between 10 K / s and over 60 K / s is carried out.
  • the steel strip before the forming or the formed component can be subjected to a tempering treatment after hardening.
  • the sheet is at a heating rate of up to 1000 K / s, in particular 400 ° C / s to 800 ° C / s to a maximum temperature below Acl, which is usually 300 ° C to 700 ° C, for example 550 ° C indicates, heated.
  • the holding time at the maximum temperature is 0.5 to 60 seconds, for example 1 to 10 s, and finally cooling with cooling rates between 10 K / s and up to over 60 K / s is carried out.
  • the product according to the invention is produced by first melting a steel melt with the composition according to the invention, in particular the chemical composition shown in FIG. 8, in the steelworks and casting it into a slab in a continuous casting plant after the secondary metallurgical treatment.
  • the slab is then heated to a temperature of 1225 ° C, descaled and then conventionally hot-rolled to a steel strip, the rolling starting temperature being 1110 ° C and the rolling end temperature 890 ° C when the slab is hot-rolled.
  • a major part of the deformation takes place below the recrystallization stop temperature, which causes the austenite to stretch, as shown in Figure 2.
  • the steel strip is cooled to the coiling temperature by means of water and reeled up.
  • the reel temperature in the present example is 125 ° C and is achieved with a cooling rate of 55 ° C / s.
  • the longitudinally divided steel strip with a thickness of 5 mm is formed in a roll profiling system with an integrated welding process into a closed profile with a square cross-section and the external dimensions of 50 mm by 50 mm. According to the invention, the profile is then subjected to a short-term heat treatment.
  • the profile is first heated to a maximum temperature above Ac3, in the present example at 950 ° C., briefly kept at temperature and then rapidly cooled.
  • the heating rates are 15 K / s.
  • the holding time at the maximum temperature is 1 second, after which cooling takes place at cooling rates of 20 K / s.
  • the Hollomon-Jaffee parameter of the short-term curing carried out is 21882.

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Abstract

L'invention concerne un procédé de fabrication de produits de type feuillard à chaud obtenus par voie thermomécanique, procédé selon lequel un alliage d'acier est fondu, cet alliage étant conçu de façon à empêcher une recristallisation pendant le laminage à chaud, l'alliage d'acier fondu étant coulé en brames, ces dernières étant laminées à chaud après avoir été chauffées à une température supérieure à Ac3 jusqu'à obtention d'un taux de déformation voulu et d'une épaisseur de feuillard voulue, le feuillard étant refroidi à température ambiante après le laminage et chauffé brièvement à une température > Ac3 puis refroidi en vue d'une trempe. L'invention est caractérisée que le chauffage est réalisé avec une augmentation de température de plus de 5 K/s, de préférence de plus de 10 K/s, de préférence encore de plus de 50 K/s, en particulier de plus de 100 K/s et maintenu à une température cible voulue pendant 0,5 à 60 s, puis un refroidissement est effectué, le feuillard d'acier ou la pièce découpée produit(e) par laminage thermomécanique étant profilé(e) selon un processus de déformation pour permettre l'obtention d'une pièce.
EP19832074.9A 2018-12-19 2019-12-18 Procédé de fabrication de produits de type feuillard à chaud profilés obtenus par voie thermomécanique Pending EP3899059A1 (fr)

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DE102018132816.8A DE102018132816A1 (de) 2018-12-19 2018-12-19 Verfahren zur Herstellung von thermo-mechanisch hergestellten profilierten Warmbanderzeugnissen
PCT/EP2019/086052 WO2020127555A1 (fr) 2018-12-19 2019-12-18 Procédé de fabrication de produits de type feuillard à chaud profilés obtenus par voie thermomécanique

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JP6630812B2 (ja) 2015-07-24 2020-01-15 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフトＴｈｙｓｓｅｎＫｒｕｐｐ Ｓｔｅｅｌ Ｅｕｒｏｐｅ ＡＧ 高い最小降伏限界を有する高強度鋼およびその種の鋼を製造する方法
DE102015112886A1 (de) 2015-08-05 2017-02-09 Salzgitter Flachstahl Gmbh Hochfester aluminiumhaltiger Manganstahl, ein Verfahren zur Herstellung eines Stahlflachprodukts aus diesem Stahl und hiernach hergestelltes Stahlflachprodukt
JP6762798B2 (ja) * 2016-08-03 2020-09-30 株式会社神戸製鋼所 高強度鋼板およびその製造方法
WO2018220430A1 (fr) 2017-06-02 2018-12-06 Arcelormittal Tôle d'acier destinée à la fabrication de pièces trempées à la presse, pièce trempée à la presse présentant une association de résistance élevée et de ductilité d'impact, et procédés de fabrication de cette dernière
DE102018132901A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von konventionell warmgewalzten Warmbanderzeugnissen
DE102018132908A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten Warmbanderzeugnissen
DE102018132860A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von konventionell warmgewalzten, profilierten Warmbanderzeugnissen

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN116555677A (zh) * 2023-03-31 2023-08-08 马鞍山钢铁股份有限公司 一种热成形用钢及其制造方法

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