EP3535431A1 - Produit en acier au manganèse moyen pour utilisation à basse température et son procédé de fabrication - Google Patents

Produit en acier au manganèse moyen pour utilisation à basse température et son procédé de fabrication

Info

Publication number
EP3535431A1
EP3535431A1 EP17798132.1A EP17798132A EP3535431A1 EP 3535431 A1 EP3535431 A1 EP 3535431A1 EP 17798132 A EP17798132 A EP 17798132A EP 3535431 A1 EP3535431 A1 EP 3535431A1
Authority
EP
European Patent Office
Prior art keywords
steel product
steel
weight
optional
rolling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP17798132.1A
Other languages
German (de)
English (en)
Other versions
EP3535431B1 (fr
Inventor
Peter PALZER
Manuel Otto
Kai Köhler
Thomas Evertz
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzgitter Flachstahl GmbH
Original Assignee
Salzgitter Flachstahl GmbH
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 Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Publication of EP3535431A1 publication Critical patent/EP3535431A1/fr
Application granted granted Critical
Publication of EP3535431B1 publication Critical patent/EP3535431B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • 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
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B21C37/08—Making tubes with welded or soldered seams
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B21C37/12—Making tubes or metal hoses with helically arranged seams
    • B21C37/122—Making tubes or metal hoses with helically arranged seams with welded or soldered seams
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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

Definitions

  • the invention relates to a medium manganese steel product for use at low temperatures and a process for its preparation in the form of a
  • the invention relates to the production of a steel product from a medium manganese steel with excellent low temperature toughness and / or high strength, for use in temperature ranges to at least minus
  • steel products such as steel strips (hot or cold rolled), are considered as steel products
  • the steel has a notched impact strength of 70 J at -196 ° C and consists of the elements (contents in% by weight and based on the
  • Molten steel C: to 0.01 to 0.06; Mn: 2.0 to 8.0; Ni: 0.01 to 6.0; Mo: 0.02 to 0.6; Si: 0.03 to 0.5; AI: 0.003 to 0.05; N: 0.0015 to 0.01; P: up to 0.02; S: up to 0.01; as well as residual iron and unavoidable impurities.
  • This steel should be distinguished by the fact that it is cheaper to produce than the steels previously used for this purpose up to 9% by weight of nickel.
  • a method for producing a flat steel product from the above-described high-strength medium manganese steel comprises the following steps: - heating a steel slab to a temperature of 1000 ° C to 1250 ° C, - rolling the slab with a rolling temperature of 950 ° C or less with a reduction rate (Rolling degree) of 40% or less, - cooling the rolled steel to a temperature of 400 ° C or less at a cooling rate of 2 ° K / s or more, - and after cooling, tempering the steel for 0.5 to 4 hours at a temperature between 550 ° C and 650 ° C.
  • the structure of the steel points as
  • a door booster tube containing, in addition to iron, the following elements: C: 0.15 to 0.25%; Mn: 3.4 to 6.1%; P: max. 0.03%; S: max. 0.03%; Si: max. 0.6%; AI: 0.05%; Ni, Cr, Mo: 0 to 1%; V: 0 to 0.15%.
  • a structural composition of the steel is not described.
  • U.S. Patent No. 5,310,431 discloses a corrosion-resistant martensitic steel containing, in addition to iron and impurities, the following elements: C: 0.05 to 0.15%; Cr: 2 to 15%; Co: 0.1 to 10%; Ni: 0.1 to 4%, Mo: 0.1 to 2%; Ti: 0.1 to 0.75%; B: ⁇ 0.1%; N: ⁇ 0.02%.
  • the described steel may also contain, for example, ⁇ 5% Mn.
  • the publication US 2014/0230971 A1 discloses a high-strength steel sheet with excellent deformation properties and a method for its production.
  • the steel sheet consists of the following elements (in weight%): C: 0.03 to 0.35; Si: 0.5 to 3; Mn: 3.5 to 10; P: ⁇ 0.1; S: ⁇ 0.01; N: ⁇ 0.08.
  • a microstructure is given with more than 30% ferrite and more than 10% residual austenite.
  • the publication WO 2006/01 1503 A1 also describes a steel sheet whose chemical composition in% by weight is given as follows: C: 0.0005 to 0.3; Si: ⁇ 2.5; Mn: 2.7 to 5; P: ⁇ 0.15; S: ⁇ 0.015; Mo: 0.15 to 1.5; B: 0.0006 to 0.01; AI: ⁇ 0.15 and balance iron and unavoidable impurities. Characteristic of such a steel strip is a high modulus of elasticity of greater than 230 Gpa in the rolling direction.
  • European Patent Application EP 2 055 797 A1 relates to a ferromagnetic, iron-based alloy whose composition contains one or more of the following elements in% by weight: Al: 0.01 to 1: 1; Si: 0.01 to 7; Cr: 0.01 to 26 and balance iron and unavoidable impurities.
  • the alloy can also contain 0.01 to 5 wt .-% Mn and other elements.
  • TRIP steels which have a predominantly ferritic basic structure with embedded retained austenite, which during a forming too Can convert martensite (TRIP effect). Because of its high work hardening, the TRIP steel achieves high levels of uniform elongation and tensile strength. TRIP steels are used, among other things, in structural, chassis and crash-relevant components of vehicles as sheet metal blanks as well as welded blanks.
  • WO 2005/061 152 A1 discloses hot strips made of TRIP / TWIP steels with manganese contents of 9 to 30% by weight, wherein the melt is poured over a horizontal strip casting plant to a preliminary strip of between 6 and 15 mm and subsequently is rolled to a hot strip.
  • the present invention based on the object to provide a steel product from a manganese-containing steel, which is inexpensive to produce and an advantageous combination of strength and
  • the equation 0.1 1 ⁇ C + Al ⁇ 3 is satisfied with optional addition of one or more of the following elements: Ti, V, Cr, Cu, Nb, B, Co, W, Zr, Ca and Sn,
  • the alloy composition contains at least one or more of the elements B, V, Nb, Co, W or Zr in addition to Ni, with optional addition of one or more of the following elements: Ti, Cr, Cu, Ca and Sn,
  • Martensite an excellent low-temperature toughness at temperatures below room temperature to at least -196 ° C and a good combination of strength, elongation and forming properties.
  • Medium manganese steel product (medium manganese steel) on the basis of the alloying elements C, Mn, Al, Mo and Si cost-effective because of an increased addition of nickel of up to 9% by weight to achieve the
  • Low temperature toughness can generally be dispensed with.
  • Steel product according to the invention has a stable austenite at low temperatures to at least - 196 ° C, which converts at the earliest at a deformation at low temperatures, but otherwise present metastable to stable.
  • the steel product according to the invention can be used as a substitute for high-Ni-containing steels in low-temperature applications, such as in the fields of shipbuilding, boiler construction / container construction, construction machinery, transport vehicles, crane construction, mining, mechanical and plant engineering, power plant industry, oilfield pipes, Petrochemicals, wind turbines, penstocks, precision tubes, tubes in general and for the substitution of high-alloy steels, in particular Cr, CrN, CrMnN, CrNi, CrMnNi steels.
  • the optionally alloyed elements advantageously have the following contents in% by weight: Ti: 0.002 to 0.5; V: 0.006 to 0.1; Cr: 0.05 to 4; Cu: 0.05 to 2; Nb: 0.003 to 0.1; B: 0.0005 to 0.014; Co: 0.003 to 3; W: 0.03 to 2; Zr: 0.03 to 1; Ca: ⁇ 0.004 and Sn: ⁇ 0.5
  • the steel product according to the invention in particular in the form of a seamless tube, has a multiphase structure consisting of 2 to 90% by volume, preferably up to 80% by volume or up to 70% by volume austenite, less than 40% by volume, preferably less than 20% by volume of ferrite and / or bainite and the remainder martensite or tempered martensite and optionally a TRIP and / or TWIP effect.
  • Part of the martensite is present as tempered martensite and part of the austenite of up to 90% may be in the form of annealing or deformation twins.
  • the steel may optionally comprise both a TRIP and TWIP an effect, wherein a portion of the austenite during subsequent deformation / ⁇ indentation /
  • the steel product of the present invention is also characterized by increased resistance to delayed fracture and hydrogen embrittlement. This is achieved mainly by a precipitation of molybdenum carbide, which acts as a hydrogen trap.
  • the steel has a high resistance to
  • Liquid metal embrittlement (LME) during welding Liquid metal embrittlement (LME) during welding.
  • the steel according to the invention is particularly suitable for the production of heavy plate or of hot and cold strip and welded and seamless tubes, which can be provided with metallic or non-metallic, organic or other inorganic coatings.
  • the steel product at room temperature has a yield strength Rp0.2 of 450-1,150 MPa, a tensile strength Rm of 500-2,100 MPa and an elongation at break A50 of more than 6% to 45%, with higher tensile strengths tend to be associated with lower elongations at break and vice versa.
  • a flat specimen with an initial measuring length A50 was used in accordance with DIN 50 125. Alloying elements are usually added to the steel in order to specifically influence certain properties. An alloying element in different steels can influence different properties. The effect and interaction generally depends substantially on the amount, the presence of other alloying elements and the dissolution state in the material.
  • Carbon C is required for the formation of carbides, stabilizes the austenite and increases the strength. Higher contents of C deteriorate the welding properties and lead to the deterioration of the elongation and toughness properties, therefore, a maximum content of less than 0.3% by weight is set. In order to achieve a fine precipitation of carbides, a minimum addition of 0.01% by weight is required. For an optimal combination of mechanical
  • the C content is advantageously set to 0.03 to 0.15% by weight.
  • Mn stabilizes the austenite, increases strength and toughness, and optionally allows deformation-induced martensite and / or twin formation in the alloy of the present invention. Contents less than 4% by weight are not sufficient to stabilize the austenite and thus worsen the
  • a range of 4 to ⁇ 8% by weight is preferred.
  • Aluminum AI AI serves to deoxidize the melt.
  • An AI content of 0.003 Weight% and more serves to deoxidize the melt. This results in a higher cost when casting.
  • Al contents of more than 2.9% by weight deteriorate the elongation properties.
  • higher Al contents significantly worsen the casting behavior in continuous casting. Therefore, a maximum content of 2.9% by weight and a minimum content of more than 0.003% by weight are set.
  • the steel has an Al content of 0.03 to 0.4% by weight.
  • a minimum content (in% by weight) of more than 0.1 1 and less than 3 should be maintained, whereby the strength of the austenite in particular increased by C, but the rejection of undesirable coarse carbides is suppressed by AI.
  • a content of C + Al of 3% by weight or more deteriorates the
  • Silicon Si Addition of Si at levels greater than 0.02% by weight inhibits carbon diffusion, reduces specific gravity, and increases strength and elongation and toughness properties. Furthermore, an improvement in cold rollability by alloying Si could be observed. Contents of more than 0.8% by weight lead to embrittlement of the material and negatively influence the hot and cold rollability as well as the coatability, for example by galvanizing. Therefore, a maximum content of 0.8% by weight and a minimum content of 0.02% by weight are set. Levels of 0.08 to 0.3% by weight have been found to be optimal.
  • Mo acts as a carbide former, increasing strength and increasing resistance to hydrogen induced delayed cracking and cracking
  • Phosphorus P is a trace element or trace element from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphor boosts
  • Solid solution solidifies the hardness and improves the hardenability.
  • it is usually attempted to lower the phosphorus content as much as possible, since it is highly susceptible to segregation, among other things, by its low diffusion rate and greatly reduces the toughness.
  • the addition of phosphorus to the grain boundaries can cause cracks along the grain boundaries during hot rolling.
  • phosphorus increases the transition temperature from tough to brittle behavior by up to 300 ° C.
  • Phosphorus content is limited to values less than 0.04% by weight.
  • S S, like phosphorus, is bound as a trace element or accompanying element in iron ore or is introduced by coke during production via the blast furnace route. It is generally undesirable in steel, as it tends to segregate severely and has a strong embrittlement, which increases the elongation and elongation
  • N is also a companion element of steelmaking. In the dissolved state, it improves the strength and toughness properties of steels containing more than or equal to 4% by weight of Mn. Low Mn-alloyed steels of less than 4% by weight tend to have a strong aging effect in the presence of free nitrogen. The nitrogen diffuses even at low
  • the nitrogen in the form of nitrides is possible, for example, by alloying aluminum and / or titanium and Nb, V, B, aluminum nitrides in particular having a negative effect on the forming properties of the alloy according to the invention.
  • the nitrogen content is less than 0.02% by weight. limited.
  • Titanium Ti When added as an option, Ti acts as a fine grain carbide former, enhancing its strength, toughness, and elongation properties. Furthermore, Ti reduces intergranular corrosion. Contents of Ti exceeding 0.5% by weight deteriorates the elongation properties, therefore, a maximum content of Ti of 0.5% by weight is set. Optionally, a minimum content of 0.002 is set to advantageously precipitate nitrogen with Ti. Vanadium V: If added as an option, V acts as a carbide-forming agent that refines grain, thereby improving its strength, toughness, and elongation properties. Contents of V of more than 0.1% by weight give no further advantages, which is why a maximum content of 0.1% by weight is determined. Optionally, a minimum content of 0.006% by weight is set, which is necessary for a separation of very fine carbides.
  • Chromium Cr With optional addition Cr increases the strength and reduces the
  • Corrosion rate retards ferrite and pearlite formation and forms carbides.
  • the maximum content is set at 4% by weight, as higher contents are one
  • Efficacy Minimum Cr content is set at 0.05% by weight.
  • Nickel Ni The optional addition of at least 0.005 wt.%, Preferably 0.01 wt.% Nickel stabilizes the austenite, especially at lower temperatures, and improves strength and
  • the maximum content is set here for cost reasons to 3% by weight.
  • a maximum content of Ni of 1% by weight has been found.
  • a particularly inexpensive alloy system can be achieved if, in combination with manganese, the following condition is met: 6 ⁇ 1.5 Mn + Ni ⁇ 8.
  • Copper Cu reduces the corrosion rate and increases the strength. Contents of more than 2% by weight deteriorate the manufacturability by forming low-melting phases during casting and hot rolling, which is why a maximum content of 2% by weight. In order to achieve a strength-increasing effect by Cu, a minimum of 0.05% by weight is set.
  • Niob Nb acts as a carbide former to fine grain, thereby improving strength, toughness, and elongation properties. Contents of Nb of more than 0.1% by weight give no further advantages, which is why a maximum content of 0.1% by weight is determined. Optionally, a minimum content of 0.003% by weight is set, which is necessary for a precipitation of very fine carbides.
  • Co increases the strength of the steel and stabilizes the austenite. Contents of more than 3% by weight deteriorate the elongation properties, which is why optionally a maximum content of 3% by weight is determined. Preferably, an optional minimum content of 0.003% by weight is provided, which in addition to the
  • Tungsten W acts as a carbide former and increases strength. Contents of W of more than 2% by weight deteriorate the elongation properties, therefore, one
  • Zirconium Zr acts as a carbide former and improves strength. Contents of Zr of more than 1% by weight deteriorate the elongation properties, therefore, a
  • Ca is used to modify non-metallic oxide inclusions, which could otherwise result in undesirable alloy failure due to inclusions in the structure which act as stress concentration sites and weaken the metal composite. Furthermore, Ca improves the
  • Sn Sn increases strength but, similar to copper, accumulates at higher temperatures below the scale and grain boundaries. It leads by penetration into the grain boundaries to the formation of low-melting phases and associated with cracks in the structure and solder brittleness, which is why an optional
  • a steel product in the form of a flat steel product, such as hot strip, cold strip or plate, is delivered according to the invention by a method comprising the steps:
  • Weight% Ti: 0.002 to 0.07; V: 0.006 to 0.1; Cr: 0.05 to 4; Ni: 0.01 to 3; Cu: 0.05 to 2; Nb: 0.003 to 0.1; B: 0.0005 to 0.014; Co: 0.003 to 3; W: 0.03 to 2; Zr: 0.03 to 1; Ca: less than 0.004; Sn: less than 0.5 on the process route
  • Blast furnace steel plant or electric arc furnace steelworks each with optional vacuum treatment of the melt Pouring the molten steel into a preliminary strip by means of a horizontal or vertical continuous strip casting process, or casting the molten steel into a slab or thin slab by means of a horizontal or vertical slab or thin slab casting process,
  • annealing the cold strip in an annealing plant with an annealing time of 0.3 to 24 h and temperatures of 500 ° C. to 840 ° C., preferably 520 ° C. to 600 ° C. with an annealing time of 0.5 to 6 h,
  • the flat steel product having excellent low temperature toughness at temperatures below -196 ° C and a good combination of strength, elongation and forming properties.
  • Endge sleepges not already on the hot or cold strip but optionally only after the tube made, wherein the annealing of the tube in an annealing at an annealing time of 0.3 to 24 h and temperatures of 500 ° C to 840 ° C, preferably 520 ° C to 600 ° C with an annealing time of 0.5 to 6 h.
  • the tube may have a one- or two-sided organic or inorganic
  • Typical 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 heavy plate having a thickness of about 3 mm to 200 mm or a hot strip having a thickness of 0.8 mm to 28 mm, or the preliminary near-cast cast slab into a hot strip having a thickness of 0.8 mm to 3 mm is hot rolled.
  • the cold strip according to the invention has a thickness of at most 3 mm, preferably 0.1 mm to 1, 4 mm.
  • the cold rolling of the hot strip may take place at room temperature or advantageously at elevated temperature before the first pass, in one or more rolling passes.
  • Cold rolling at elevated temperature is advantageous to reduce rolling forces and promote the formation of twinned twins (TWIP effect).
  • Advantageous temperatures of the rolling stock before the first pass are 60 ° C to 450 ° C.
  • the steel strip can be dressed after cold rolling, thereby adjusting the surface texture (topography) needed for the final application.
  • the casting can be done for example by means of the Pretex® method.
  • the flat steel product thus produced receives a surface refinement, for example by electrolytic galvanizing or hot-dip galvanizing and instead of galvanizing or additively a coating on an organic or inorganic basis.
  • the coating systems may, for example, organic coatings, plastic coatings or paints or other inorganic coatings such as iron oxide layers be.
  • the flat steel product produced according to the invention can be used both as sheet metal,
  • Sheet metal section or board used or further processed to a longitudinal or spiral seam welded pipe used or further processed to a longitudinal or spiral seam welded pipe.
  • Ti 0.002 to 0.07
  • V 0.006 to 0.1
  • Cr 0.05 to 4
  • Cu 0.05 to 2
  • Nb 0.003 to 0.1
  • B 0.0005 to 0.014
  • Co 0.003 to
  • the equation 0.1 1 ⁇ C + Al ⁇ 3 is satisfied, with optional addition of one or more of the following elements: Ti: 0.002 to 0.07; V: 0.006 to 0.1; Cr: 0.05 to 4; Cu: 0.05 to 2; Nb: 0.003 to 0.1; B: 0.0005 to 0.014; Co: 0.003 to 3; W: 0.03 to 2; Zr: 0.03 to 1; Ca: less than 0.004; Sn: less than 0.5,
  • the alloy composition contains, besides Ni, at least one or more of the elements B, V, Nb, Co, W or Zr, with optional addition of one or more of the following elements: Ti: 0.002 to 0.07; Cr: 0.05 to 4; Cu: 0.05 to 2; Ca: less than 0.004; Sn: less than 0.5 via the process route blast furnace steelworks or electric arc furnace steelworks each with optional vacuum treatment of the melt;
  • Hot rolling into a seamless tube for example in a plug mill, cross-rolling mill, release mill, die mill, rolling mill, continuous rolling mill, Pilger rolling mill or a bumper system with, for example, the following procedure: Production of a hollow block from a bloom, subsequent elongation
  • Hydroforming optionally at a temperature from room temperature to below Ac3 temperature, preferably 60 ° C to 450 ° C.
  • a solid block (round cast bar) is essentially understood to mean a continuous casting section produced by round continuous casting which already has a desired length.
  • the elongation at break A50 of the X8Ni9 was converted according to DIN ISO 2566/1 from the breaking elongation A5,65 according to the standard to a sample cross section of 20 mm.
  • the elongation characteristics stand for the elongation in the rolling direction.

Landscapes

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

Abstract

L'invention concerne un produit en acier pour utilisation à basse température présentant une énergie absorbée minimale à -196 °C dans le sens transversal ≥ 50 j/cm2 et ayant la composition chimique suivante en % en poids : C : 0,01 à < 0,3, de préférence 0,03 à 0,15 ; Mn : 4 à < 10, de préférence 4 à < 8 ; Al : 0,003 à 2,9, de préférence 0,03 à 0,4 ; Mo : 0,01 à 0,8, de préférence 0,1 à 0,5 ; Si : 0,02 à 0,8, de préférence 0,08 à 0,3 ; Ni : 0,005 à 3, de préférence 0,01 à 3 ; P : < 0,04 ; S : < 0,02 ; N : < 0,02 ; le reste étant du fer, y compris des éléments inévitables accompagnant l'acier, - pour la composition de l'alliage, l'équation 6 < 1,5 Mn + Ni < 8 étant satisfaite, avec ajout facultatif d'un ou de plusieurs des éléments suivants : Ti, V, Cr, Cu, Nb, B, Co, W, Zr, Ca et Sn, - ou pour la composition de l'alliage, l'équation 0,11 < C + Al < 3 étant satisfaite, avec ajout facultatif d'un ou de plusieurs des éléments suivants : Ti, V, Cr, Cu, Nb, B, Co, W, Zr, Ca et Sn, - ou la composition de l'alliage contenant, outre Ni, au moins un ou plusieurs des éléments B, V, Nb, Co, W ou Zr, avec ajout facultatif d'un ou de plusieurs des éléments suivants : Ti, Cr, Cu, Ca et Sn, ledit produit en acier présentant une structure constituée de 2 à 90 % en volume d'austénite, de moins de 40 % en volume de ferrite et/ou de bainite, le reste étant du martensite. Ce produit en acier peut être fabriqué à faible coût et présente une combinaison avantageuse de caractéristiques mécaniques et d'allongement à basses températures ainsi qu'éventuellement un effet TRIP et/ou TWIP. L'invention concerne également un procédé de fabrication d'un produit en acier sous la forme d'un produit plat ou d'un tube sans soudure.
EP17798132.1A 2016-11-02 2017-10-27 Produit d'acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication Active EP3535431B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102016120895 2016-11-02
PCT/EP2017/077628 WO2018083035A1 (fr) 2016-11-02 2017-10-27 Produit en acier au manganèse moyen pour utilisation à basse température et son procédé de fabrication

Publications (2)

Publication Number Publication Date
EP3535431A1 true EP3535431A1 (fr) 2019-09-11
EP3535431B1 EP3535431B1 (fr) 2021-06-09

Family

ID=60331577

Family Applications (1)

Application Number Title Priority Date Filing Date
EP17798132.1A Active EP3535431B1 (fr) 2016-11-02 2017-10-27 Produit d'acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication

Country Status (10)

Country Link
US (1) US11352679B2 (fr)
EP (1) EP3535431B1 (fr)
JP (1) JP2020500262A (fr)
KR (1) KR20190082804A (fr)
CN (1) CN109923233A (fr)
AU (1) AU2017353259B2 (fr)
CA (1) CA3042120C (fr)
DK (1) DK3535431T3 (fr)
RU (1) RU2728054C1 (fr)
WO (1) WO2018083035A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4299768A1 (fr) * 2022-06-29 2024-01-03 Benteler Steel/Tube GmbH Procédé de fabrication d'un tube en acier et tube en acier

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20210062726A (ko) * 2017-03-01 2021-05-31 에이케이 스틸 프로퍼티즈 인코포레이티드 극도로 높은 강도를 갖는 프레스 경화 강
CN110184543B (zh) * 2019-07-04 2021-07-20 广西大学 一种低镍高强汽车钢板及其制造方法
CN110527908A (zh) * 2019-09-06 2019-12-03 武汉科技大学 一种中碳微纳结构贝氏体钢及其热处理方法
WO2022018504A1 (fr) 2020-07-24 2022-01-27 Arcelormittal Feuille d'acier laminée à chaud et traitée thermiquement et son procédé de fabrication
CN111961982B (zh) * 2020-09-15 2022-02-01 东北大学 高扩孔率高强度高延伸率的热轧中锰钢板及其制备方法
CN113502440A (zh) * 2021-02-26 2021-10-15 上海交通大学 一种节镍型超低温用高强钢及其热处理工艺
US20220314377A1 (en) * 2021-04-06 2022-10-06 GM Global Technology Operations LLC High-strength steel sheet blank having decarburized outer layers
CN113549745B (zh) * 2021-07-27 2022-09-13 内蒙古工业大学 一种低成本第三代汽车钢加工工艺
KR102699825B1 (ko) * 2022-03-15 2024-08-27 한양대학교 에리카산학협력단 니켈(Ni)-알루미늄(Al)계 석출물을 포함하는 중망간강과 그 제조 방법
CN118422057A (zh) * 2024-04-30 2024-08-02 武汉科技大学 一种具有良好冲击磨料磨损性能的中锰钢

Family Cites Families (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4257808A (en) * 1979-08-13 1981-03-24 The United States Of America As Represented By The United States Department Of Energy Low Mn alloy steel for cryogenic service and method of preparation
US5256219A (en) 1990-10-24 1993-10-26 Mannesmann Aktiengesellschaft Steel reinforcement tube
US5310431A (en) 1992-10-07 1994-05-10 Robert F. Buck Creep resistant, precipitation-dispersion-strengthened, martensitic stainless steel and method thereof
JP2001192773A (ja) 2000-01-13 2001-07-17 Sumitomo Metal Ind Ltd ラインパイプ用鋼
JP2005002385A (ja) * 2003-06-10 2005-01-06 Sumitomo Metal Ind Ltd 成形性と靱性に優れた鋼管とその製造方法
JP4079053B2 (ja) * 2003-08-18 2008-04-23 Ｊｆｅスチール株式会社 エアバッグ用高強度高靭性継目無鋼管の製造方法
WO2005061152A1 (fr) 2003-12-23 2005-07-07 Salzgitter Flachstahl Gmbh Procede pour produire des feuillards a chaud a partir d'un acier leger
WO2006011503A1 (fr) 2004-07-27 2006-02-02 Nippon Steel Corporation Plaque d'acier à module de young élevé, tôle d'acier galvanisé à chaud utilisant celle-ci, alliage de tôle d'acier galvanisé à chaud, tube d'acier à module de young élevé et procédé de fabrication de ceux-ci
RU2269588C1 (ru) 2004-10-25 2006-02-10 Федеральное Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Конструкционных Материалов "Прометей" (Фгуп "Цнии Км "Прометей") Хладостойкая сталь высокой прочности
JP5215855B2 (ja) 2006-08-23 2013-06-19 独立行政法人科学技術振興機構 Ｆｅ基合金及びその製造方法
KR101330903B1 (ko) 2008-11-05 2013-11-18 혼다 기켄 고교 가부시키가이샤 고강도 강판 및 그 제조 방법
RU2414520C1 (ru) 2009-06-29 2011-03-20 Открытое акционерное общество "Северсталь" (ОАО "Северсталь") Сталь конструкционная с высокой ударной вязкостью при криогенных температурах
JP5392717B2 (ja) * 2009-09-18 2014-01-22 東洋鋼鈑株式会社 給油パイプ
JP5287770B2 (ja) * 2010-03-09 2013-09-11 Ｊｆｅスチール株式会社 高強度鋼板およびその製造方法
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
JP5540885B2 (ja) * 2010-05-20 2014-07-02 新日鐵住金株式会社 溶融めっき熱延鋼板およびその製造方法
KR101271974B1 (ko) * 2010-11-19 2013-06-07 주식회사 포스코 극저온 인성이 우수한 고강도 강재 및 그 제조방법
PL2692895T3 (pl) * 2011-03-28 2018-07-31 Nippon Steel & Sumitomo Metal Corporation Blacha stalowa cienka walcowana na zimno i sposób jej wytwarzania
JP5440672B2 (ja) 2011-09-16 2014-03-12 Ｊｆｅスチール株式会社 加工性に優れた高強度鋼板およびその製造方法
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
KR101510505B1 (ko) * 2012-12-21 2015-04-08 주식회사 포스코 우수한 도금성과 초고강도를 갖는 고망간 용융아연도금강판의 제조방법 및 이에 의해 제조된 고망간 용융아연도금강판
CN103422017A (zh) 2013-08-01 2013-12-04 天津钢管集团股份有限公司 输送温度低于-130℃环境用无缝钢管及其制造方法
CN104131225B (zh) * 2014-07-30 2016-08-24 宝山钢铁股份有限公司 低成本超低温镍钢及其制造方法
MX2019001521A (es) * 2016-08-22 2019-05-15 Jfe Steel Corp Pieza automotriz con soldadura por resistencia.

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4299768A1 (fr) * 2022-06-29 2024-01-03 Benteler Steel/Tube GmbH Procédé de fabrication d'un tube en acier et tube en acier

Also Published As

Publication number Publication date
JP2020500262A (ja) 2020-01-09
DK3535431T3 (da) 2021-08-16
CN109923233A (zh) 2019-06-21
US11352679B2 (en) 2022-06-07
WO2018083035A1 (fr) 2018-05-11
EP3535431B1 (fr) 2021-06-09
AU2017353259A1 (en) 2019-05-09
AU2017353259B2 (en) 2022-12-22
KR20190082804A (ko) 2019-07-10
RU2728054C1 (ru) 2020-07-28
US20190264297A1 (en) 2019-08-29
CA3042120C (fr) 2022-08-09
CA3042120A1 (fr) 2018-05-11

Similar Documents

Publication Publication Date Title
EP3535431B1 (fr) Produit d&#39;acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication
DE69617002T4 (de) Verfahren zur herstellung von hochfesten nahtlosen stahlrohren mit hervorragender schwefel induzierter spannungsrisskorossionsbeständigkeit
EP2383353B1 (fr) Acier à résistance élevée comprenant du Mn, produit plat en acier composé d&#39;un tel acier et son procédé de fabrication
EP3504349B1 (fr) Procédé de fabrication d&#39;une bande d&#39;acier à résistance très élevée présentant des propriétés améliorées lors du traitement ultérieur et une telle bande d&#39;acier
EP3332047B1 (fr) Procédé de fabrication d&#39;un produit plat en acier laminé flexible et son utilisation
EP3332046B1 (fr) Acier au manganèse à haute résistance contenant de l&#39;aluminium, procédé de fabrication d&#39;un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d&#39;après celui-ci
EP2905348B1 (fr) Produit en acier plat de haute résistance avec une structure bainitique-martensitique et procédé de fabrication d&#39;un tel produit acier plat
EP3512967B1 (fr) Procédé pour la fabrication d&#39;une pièce façonnée en un produit plat en acier contenant du manganèse et pièce correspondante
EP3512968B1 (fr) Procédé pour fabriquer un produit plat en acier à partir d&#39;un acier au manganèse et produit plat en acier résultant
WO2018083028A1 (fr) Tube sans soudure en acier au manganèse moyen et procédé de fabrication
EP3927862A1 (fr) Produit en acier constitué d&#39;acier léger de construction contenant du manganèse, et son procédé de fabrication
WO2019115551A1 (fr) Produit plat en acier laminé à chaud, à rigidité élevée, doté d&#39;une résistance à la fissuration de bords élevée ainsi que d&#39;une capacité de durcissement à la cuisson élevée, procédé de fabrication d&#39;un tel produit plat en acier
WO2022184580A1 (fr) Produit plat en acier laminé à froid et son procédé de production
WO2018050637A1 (fr) Procédé de fabrication d&#39;une bande laminée à chaud ou à froid et/ou d&#39;un produit plat en acier laminé de manière flexible constitué par un acier contenant du manganèse, hautement solide et produit plat en acier ainsi obtenu
WO2018050634A1 (fr) Procédé pour la fabrication d&#39;une pièce façonnée à partir d&#39;un produit plat en acier à teneur moyenne en manganèse et pièce correspondante
EP3469108B1 (fr) Procédé de fabrication d&#39;une bande d&#39;acier laminée à froid présentant des propriétés trip à partir d&#39;un acier à résistance élevée contenant du manganèse
DE102016115618A1 (de) Verfahren zur Herstellung eines höchstfesten Stahlbandes mit verbesserten Eigenschaften bei der Weiterverarbeitung und ein derartiges Stahlband
WO2024046913A1 (fr) Procédé de fabrication d&#39;un produit plat en acier laminé à froid

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: UNKNOWN

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20190521

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20200511

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: B21C 37/08 20060101ALN20210205BHEP

Ipc: C22C 38/16 20060101ALI20210205BHEP

Ipc: C21D 1/26 20060101ALI20210205BHEP

Ipc: C21D 8/10 20060101ALN20210205BHEP

Ipc: C22C 38/04 20060101ALI20210205BHEP

Ipc: C22C 38/22 20060101ALI20210205BHEP

Ipc: C22C 38/06 20060101ALI20210205BHEP

Ipc: C22C 38/08 20060101ALI20210205BHEP

Ipc: C22C 38/30 20060101ALI20210205BHEP

Ipc: C22C 38/14 20060101ALI20210205BHEP

Ipc: B21C 37/12 20060101ALN20210205BHEP

Ipc: C22C 38/02 20060101ALI20210205BHEP

Ipc: C22C 38/18 20060101ALI20210205BHEP

Ipc: C22C 38/20 20060101ALI20210205BHEP

Ipc: C22C 38/00 20060101AFI20210205BHEP

Ipc: C21D 8/02 20060101ALI20210205BHEP

Ipc: C21D 6/00 20060101ALI20210205BHEP

Ipc: C22C 38/10 20060101ALI20210205BHEP

Ipc: C21D 9/46 20060101ALN20210205BHEP

Ipc: C22C 38/12 20060101ALI20210205BHEP

Ipc: C21D 9/08 20060101ALN20210205BHEP

INTG Intention to grant announced

Effective date: 20210223

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1400557

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210615

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502017010631

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DK

Ref legal event code: T3

Effective date: 20210813

REG Reference to a national code

Ref country code: FI

Ref legal event code: FGE

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210909

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210910

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210909

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211011

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502017010631

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20220310

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20211027

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211027

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211027

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211031

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211031

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211027

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230513

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20171027

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20231019

Year of fee payment: 7

Ref country code: FR

Payment date: 20231026

Year of fee payment: 7

Ref country code: FI

Payment date: 20231020

Year of fee payment: 7

Ref country code: DK

Payment date: 20231024

Year of fee payment: 7

Ref country code: DE

Payment date: 20231020

Year of fee payment: 7

Ref country code: AT

Payment date: 20231020

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: BE

Payment date: 20231019

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210609