EP3292228A1 - Produit laminé plat en acier et son procédé de fabrication - Google Patents

Produit laminé plat en acier et son procédé de fabrication

Info

Publication number
EP3292228A1
EP3292228A1 EP16723293.3A EP16723293A EP3292228A1 EP 3292228 A1 EP3292228 A1 EP 3292228A1 EP 16723293 A EP16723293 A EP 16723293A EP 3292228 A1 EP3292228 A1 EP 3292228A1
Authority
EP
European Patent Office
Prior art keywords
steel
flat
content
temperature
product
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
EP16723293.3A
Other languages
German (de)
English (en)
Other versions
EP3292228B1 (fr
Inventor
Richard G. Thiessen
Thomas Heller
Karsten MACHALITZA
Roland Sebald
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.)
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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 ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP3292228A1 publication Critical patent/EP3292228A1/fr
Application granted granted Critical
Publication of EP3292228B1 publication Critical patent/EP3292228B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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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
    • 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
    • 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
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • 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 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
    • C21D8/0247—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
    • 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
    • C22C38/12—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
    • C22C38/18—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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
    • 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

Definitions

  • the invention relates to a flat steel product having an optimized combination of strength and elongation.
  • the invention relates to a method for producing such a product.
  • CA 2 734 976 A1 discloses a steel with good toughness and deformability, which should have a tensile strength of at least 980 MPa.
  • the steel contains in addition to iron and unavoidable
  • Impurities 0.17-0.73% C, up to 3.0% Si, 0.5-3.0% Mn, up to 0.1% P, up to 0.07% S, up to 3.0% Al and up to 0.010% N.
  • the sum of the Al and Si contents should be at least 0.7%.
  • Microstructure constituents the martensite in the structure of the steel is 10 - 90%, the proportion of retained austenite in the range of 5 - 50% and the proportion of ferritic bainite derived from "upper bainite” is at least 5% while a bainite called, in the fine carbide grains are evenly distributed, as they are not found in "lower bainite”
  • Steel flat product which has a tensile strength R m of at least 1200 MPa and consists of a steel, in addition to Fe and unavoidable impurities (in
  • C 0.10-0.50%
  • Si 0.1-2.5%
  • Mn 1.0-3.5%
  • Al up to 2.5%
  • P to to 0.020%
  • S up to 0.003%
  • N up to 0.02%
  • the flat steel product has a structure with (in area%) less than 5% ferrite, less than 10% bainite, 5-70% unan Stammten martensite, 5 - 30%
  • iron carbides have a size of less than 500 nm. Due to its minimized share of
  • Superior martensite has such a nature
  • composition with a heating rate ⁇ ⁇ ⁇ , ⁇ ⁇ 2 of at least 3 ° C / s heated to above the A 3 temperature of the steel of the flat steel product and at most 960 ° C amount austenitizing temperature T HZ .
  • Austenitmaschinesdauer t H z of 20 - kept s to be then cooled to a cooling stop temperature 180th This is greater than the martensite stop temperature and less than the martensite start temperature, wherein the cooling takes place at a cooling rate which is at least equal to one depending on the
  • Partitioning temperature to be heated This can be an isothermal hold the steel flat product in the
  • Carbon enriched from the supersaturated martensite This process is also known in the jargon as
  • Partitioning the Carbon or “Partitioning”.
  • the partitioning can already during the heating as so-called “Ramped Partitioning", by the holding carried out after heating at the
  • Partitioning temperature (so-called “isothermal")
  • Partitioning compared to the isothermal partitioning desired slower heating rate allows a particularly accurate control of each predetermined partitioning temperature with reduced energy use.
  • the steels obtained and processed in the above-mentioned manner belong to the so-called “AHSS steels” (Advanced High Strength Steel).
  • the invention has achieved this object in that a
  • the solution according to the invention of the abovementioned object consists in that at least the steps mentioned in claim 9 are completed in the production of a flat steel product according to the invention.
  • a flat steel product according to the invention consists of a steel which, in addition to iron and unavoidable impurities, consists of (in% by weight)
  • the invention is based on the recognition that by choosing a suitable alloy, a flat steel product can be obtained in which a high strength is achieved by a structure comprising at most minimal retained austenite contents and by a high proportion of tempered martensite and by finely divided non-tempered martensite is paired with a very good formability.
  • Flat steel products are at 950 - 1300 MPa with a yield strength of at least 800 MPa and can reach to the respective tensile strength.
  • the elongation A50 of flat steel products according to the invention lies
  • the factor ⁇ should not be less than 1.5. Excessive levels of silicon or aluminum would negatively affect the coatability (silicon) or castability (aluminum) of the steel. With insufficient contents of carbon, manganese or chromium, the required strength would not be achieved. Higher values for the factor ⁇ of at least 1.6 have proved to be advantageous for setting a stable production process, with values for the factor ⁇ of at least 1.8 having proven particularly advantageous for production stability. Too much carbon and manganese can increase one
  • Carbon has several important functions in the steel of the present invention.
  • the C content plays a major role in the formation of austenite and
  • Carbon equivalent CE has American Welding
  • the carbon equivalent should be CE
  • CE value is not more than 1.1 wt .-% to ensure good weldability.
  • a particularly good weldability can be ensured by the fact that the CE value is limited to at most 1.0 wt .-%.
  • the CE value should not be less than 0.254% by weight, and in particular not less than 0.29% by weight, in order to calculate the effect of the present invention Carbon equivalent CE incorporated alloying elements.
  • flat steel product is the production of cementite suppressed, would be bound by the carbon, which then no longer for the stabilization of the
  • the Si content is 0.2-1.5 wt%, and Si contents of at least 0.25 wt% or at most 0.95 wt% are practical for the practice favorable and of at most 0.63 wt .-% have been found to be particularly favorable.
  • Aluminum is added to the steel of a flat steel product according to the invention in the steelmaking process for deoxidizing and for setting any nitrogen present.
  • AI can also be used for the suppression of cementite.
  • the austenitizing temperature also increases. Therefore, the Al content is one for an invention
  • Steel flat product provided steel limited to 0.01 to 1.5 wt .-%. If low austenitizing temperatures are to be ensured, it may be expedient to limit the Al content to a maximum of 0.44% by weight, in particular to 0.1% by weight. In addition, higher Al contents have a negative impact on castability in steelmaking. Al contents of not more than 1.0% by weight, in particular not more than 0.44% by weight, have proved favorable for ensuring particularly good castability. In addition, aluminum can be bound by nitrogen to aluminum nitride. In the flat steel product present
  • Aluminum nitride precipitations can adversely affect the formability of the flat steel product. So it may be in terms of optimizing the formability
  • Al content can be appropriate to limit the Al content to at most 1.0 wt .-%, in particular to at most 0.44 wt .-%.
  • Manganese is important for the hardenability of the steel of a flat steel product according to the invention and also prevents the formation of unwanted perlite during the process
  • Mn content a range of 1.0 to 3.0 wt .-%, in particular at least 1.5 wt .-% or at most 2.4 wt .-% provided.
  • Phosphorus has an unfavorable effect on the weldability of a flat steel product according to the invention.
  • the P content should be as low as possible, in any case not exceed 0.02 wt .-%, in particular less than 0.02 wt .-% or less than 0.018 wt .-% amount.
  • the presence of effective levels of sulfur in the steel of a flat steel product according to the invention would lead to the formation of sulphides, in particular MnS or (Mn, Fe) S, which would have a negative effect on the elongation.
  • the S content of the steel should be kept as low as possible, but in any case not higher than 0.005 wt .-%, in particular less than 0.005 wt .-% or less than 0.003 wt .-% amount.
  • the N content of the steel of a flat steel product according to the invention is limited to at most 0.008 wt .-%.
  • the N content should be avoided to avoid any negative
  • Chromium in amounts of up to 1.0 wt .-% can in
  • Steel provided according to the invention can optionally be used as an effective inhibitor of perlite and also contributes to the strength.
  • contents of more than 1.0% by weight Cr there is the danger of pronounced grain boundary oxidation.
  • To be able to use the positive effect of Cr are at least 0.05 wt .-% required.
  • the presence of Cr in the steel has a particularly favorable effect
  • flat molybdenum product also contain molybdenum in amounts of 0.05 to 0.2 wt .-%. Mo in these grades
  • the steel of a flat steel product according to the invention may further optionally contain levels of one or more
  • Ti contents of at least 0.005 wt .-% and Nb contents of at least 0.001 wt .-% lead each alone or in combination with each other to freeze the grain and
  • Ti may also be used to set the nitrogen present in the steel to allow for the action of other alloying elements, particularly boron.
  • Ti contents of at least 0.02 wt .-% have been found to be particularly
  • the boron also optionally present in the steel of a flat steel product according to the invention segregates on the
  • the steel provided according to the invention must contain at least 0.0001% by weight of B. At levels greater than 0.005% by weight, no increase in the beneficial effect of B can be detected.
  • the flat steel product according to the invention can be provided with a metallic protective coating. This can be applied in particular by hot dip coating.
  • coatings based on Zn are suitable for a flat steel product according to the invention.
  • the method according to the invention for producing a high-strength steel flat product comprises the following
  • Austenitizing temperature T HZ wherein the heating up to 200-400 ° C draw forming inflection point temperature T w at a heating rate ⁇ ⁇ ⁇ 5-25 K / s, and then up to the austenitization temperature T HZ with a heating rate ⁇ ⁇ 2 of at least 2 - taken 10 ° K / s; c) holding the flat steel product in the
  • Cooling time t k from 50 - 300 s to one
  • Cooling stop temperature T Q for which applies:
  • Total treatment time t B of 10 - 1000 s at a treatment temperature T B which is at least equal to the cooling stop temperature T Q and not higher than 550 ° C, In particular, not higher than 500 ° C, is held. or g.2) the flat steel product starting from the
  • Cooling stop temperature T Q is heated to a 450 - 500 ° C treatment treatment temperature T B , the steel flat product is then optionally held isothermally at this treatment temperature T B over a holding time t B i, wherein the heating to the treatment temperature T B with a heating rate ⁇ ⁇ ⁇ of less than 80 ° K / s and takes place as the sum of the time required for the heating heating time t BR and the holding time t B i total treatment time t BT 10 - 1000 s, and wherein the
  • Steel flat product is passed through a melt bath after being treated to coat it with a Zn-based metallic protective coating; h) from the treatment temperature T B outgoing cooling at a cooling rate ⁇ ⁇ 2 of more than 5 K / s.
  • step a) becomes a flat steel product
  • provided flat steel product may be
  • Austenitizing temperature T HZ (step b)) are basically two interruption-free successive steps possible, the steel flat product is heated in the first step with a heating rate ⁇ ⁇ ⁇ from 5 - 25 K / s up to a point of inflection temperature T w , the 200 - 400 ° C is. Values for ⁇ of at least 5 K / s have been favorable for the
  • the heating rate ⁇ ⁇ 2 it has proved advantageous to limit the heating rate ⁇ ⁇ 2 to a maximum of 10 K / s.
  • values for the heating rate ⁇ ⁇ 2 of less than 2 K / s have proved to be unfavorable for the economy of the process.
  • the Heating velocities ⁇ ⁇ ⁇ , ⁇ ⁇ 2 areas mentioned overlap the heating on the
  • Heating rates ⁇ ⁇ ⁇ and ⁇ ⁇ 2 in step b) are then the same.
  • the austenitizing temperature T H z must be above the A 3 temperature.
  • the A 3 temperature is
  • the alloy of the steel selected according to the invention makes it possible to limit the austenitizing temperature T H z to a maximum of 950 ° C., and thus allows for the
  • Austenitizing t H z may be less than 15 s to avoid any unwanted grain growth.
  • step d) follows one of the
  • Cooling can be about 50 - 300 seconds and extend must end at an intermediate temperature T K, which is not lower than 680 ° C in order to avoid the undesirable formation of ferrite. Up is the
  • Intermediate temperature T K preferably to temperatures which are at most A 3 , and typically limited to 775 ° C, since at higher intermediate temperatures T K needed for the subsequent cooling
  • the steel flat product is quenched in step e) at a high cooling rate 9 Q to an analysis-dependent cooling stop temperature T Q.
  • the high cooling rate 9Q can be achieved, for example, with a modern gas cooling system.
  • the minimum cooling rate 9Q necessary to avoid the ferritic and bainitic transformation is more than 30 K / s.
  • the cooling rate 9Q is typically limited by the plant upwards and is typically not more than 200 K / s.
  • the martensite start temperature can be estimated by the following equation (alloy contents
  • T M s (° C) 539 ° C + (-423% C - 30.4% Mn - 7.5% Si + 30% A1) ° C / wt% with% C: C content of the steel .
  • step f the flat steel product over a holding time tQ of 10 - 60 seconds on the
  • the holding period t Q is at least 10 seconds in order to ensure a homogenization of the temperature in the flat steel product and thus a uniform structure. For longer holding periods of more than 60 seconds is the
  • Holding time t Q is at most 60 seconds to the
  • step g) completed heat treatment of
  • Essentially consists of two different types of martensite, namely tempered martensite and unannealed martensite.
  • step g) comprises two
  • the temperature control in both variants g.l), g.2) of step g) is in each case selected such that the retained austenite present in the structure with carbon from the supersaturated martensite is enriched.
  • treating the flat steel product in the step g) comprises an over the total processing time t B T extending holding the flat steel product at a treatment temperature T B which is at least equal to the cooling stop temperature T Q, and not higher than 550 ° C, wherein a cooling stop temperature T Q of at most 500 ° C has proven to be particularly favorable.
  • the treatment temperature T B may also be higher than the cooling stop temperature T Q.
  • the steel flat product starting from the cooling stop temperature T Q to the respective
  • Heating rate ⁇ ⁇ ⁇ should be done.
  • step g the flat steel product with a
  • the formation of carbides and the decomposition of retained austenite is targeted by the inventive limitation of the total treatment time t BT
  • Heating rate ⁇ ⁇ ⁇ can also be omitted isothermal holding, the holding time t BI so be equal to "0".
  • the flat steel product passes through the following
  • Treatment temperature T B a hot-dip coating in which it is coated with a Zn coating.
  • the treatment temperature T B can be chosen so that it corresponds to the inlet temperature with which the
  • Run flat steel product into the respective melt bath should. Typically, this is the
  • Treatment temperatures T B in the range of 450 - 500 ° C.
  • the melt bath typically contains in total up to 3.0% by weight of one or more elements of the group consisting of Al, Mg, Si, Pb, Ti, Ni, Cu, B and Mn.
  • ⁇ ⁇ 2 is more than 5 K / s to avoid the formation of pearlite and ferrite.
  • the flat steel product according to the invention has a structure that
  • Martensite of which at least, in particular more than 50 area% of tempered martensite from the first
  • microstructure of a flat steel product according to the invention is very fine with an average particle size of less than 2 ⁇ m and can scarcely be assessed by means of conventional optical microscopy. Therefore, a judgment by means of scanning electron microscopy (SEM) and a
  • the maximum permissible residual austenite content can only be determined with difficulty at high magnification by light microscopy or scanning electron microscopy. Therefore, a quantitative determination of retained austenite by means of X-ray diffraction (XRD) is recommended (according to ASTM E975), according to which the retained austenite content is given in% by volume.
  • XRD X-ray diffraction
  • the distortion of the crystal lattice can also be used. This lattice distortion is very important for the initial resistance to plastic deformation.
  • Lattice distortion is the electron backscatter diffraction (EBSD).
  • EBSD electron backscatter diffraction
  • a threshold typically 5 °
  • adjacent points belong to the same (deformed) grain.
  • the neighboring points belong to
  • the KAM is evaluated by the third neighbor points.
  • An inventive flat steel product must have a KAM average of a
  • the invention is based on
  • CE % C + (% Si +% Mn) / 5 + (% Cr +% Mo) / 6 with% C the respective C-, with% Si the respective Si, with% Mn the respective Mn-, with% Cr of respective Cr, with% Mo the respective Mo and with% A1 of the respective Al content of the steels A - I have been calculated.
  • the steels E, F and G therefore did not fulfill the requirements for the coordination of the alloying elements and austenitic alloy elements which are determined by the factor ⁇ according to the invention.
  • Cooling speed 9 Q were used in which the samples 1 - 7, 11, 12, 16 - 23, 28 - 31, 33 - 35, 39, 40, 43 - 60 have been cooled to a cooling stop temperature T Q , which for the samples 1 - 7, 11, 12, 16, 17, 19 - 23, 28 - 31, 33 - 35, 39, 40, 43 - 60 were each up to 175 ° C lower and for sample 18 was higher than that
  • Samples 1 - 7, 11, 12, 16 - 23, 28 - 31, 33 - 35, 39, 40, 43-60 has been held for a holding period t Q of 10 - 60 s.
  • the samples 1 - 7, 11, 12, 16, 17, 19 - 23, 28 - 31, 33 - 35, 39, 40, 43 - 48 were then heated at a heating rate ⁇ ⁇ ⁇ via a
  • Heating time t B R heated to a treatment temperature T B , where they have been held in some experiments for an additional holding time t B i.
  • Sample 18 was cooled analogously thereto to the treatment temperature T B. Subsequently, the cooling took place
  • Elongation at break A 50 (according to DIN EN ISO 6892, sample form 1), the product R m * Aso, and the hole expansion ratios ⁇ , ⁇ 2 (according to ISO 16630).
  • the microstructural fractions of ferrite "F”, tempered martensite “AM”, retained austenite “RA”, unannealed martensite “M” and bainite “B”, and the kernel average misorientation value "KAM” were determined. The respective property values are given in Table 3 for each of the samples.
  • Austenitizing temperature T HZ Austenitizing temperature T HZ .
  • the microstructure has not been completely austenitized, so that too much ferrite forms in the structure. This leads to extremely localized damage and premature failure during forming.
  • Comparative Example D29 shows, as does too high austenitization at high temperatures
  • Formability can adversely affect.
  • Comparative Examples A3 and C19 show that if the cooling rates are too low, 9 Q the desired yield strength is not reached, which is due
  • the comparative example C18 which was generated with too high a cooling stop temperature T Q , shows a
  • Ferrite content is due to an insufficient prevention of carbide formation due to a low silicon content as well as to a low content of aluminum and silicon in relation to carbon, manganese and chromium and thus to a high ⁇ -factor.
  • Comparative Examples F39, F40, F59 and F60 show the effects of a too low ⁇ factor, which also leads to deviations from the desired microstructure. The minimum strength has been partially reached, but the yield strength and the hole widening are not in the target area here.
  • Comparative Example 148 illustrates that too low a cooling rate ⁇ ⁇ 2 leads to an increased ferrite formation and thus to low yield strengths.

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Abstract

L'invention concerne un produit laminé plat en acier, possédant une résistance à la traction Rm ≥ 950 MPa, une limite d'élasticité ≥ 800 MPa et un allongement à la rupture A50 ≥ 8 %. Ce produit laminé plat en acier est constitué d'un acier qui contient (en % en poids) 0,05 - 0,20 % C, 0,2 - 1,5 % Si, 0,01 - 1,5 % Al, 1,0 - 3,0 % Mn, ≤ 0,02 % P, ≤ 0,005 % S, ≤ 0,008 % N, ainsi que respectivement de manière facultative 0,05 - 1,0 %, 0,05 - 0,2 % Mo, 0,005 - 0,2 % Ti, 0,001 - 0,05 % Nb, 0,0001 - 0,005 % B, le reste étant constitué de Fe et d'impuretés inévitables. Selon l'invention, 1,5 ≤ ψ ≤ 3, avec ψ=(%C+%Mn/5+%Cr/6)/(%Al+%Si) et %C, %Mn, %Cr, %Al, %Si représentant respectivement la teneur en C, Mn, Cr, Al et Si de l'acier. Ce produit laminé plat en acier présente une structure constituée de (en % surfacique) ≤ 5 % de bainite, ≤ 5 % de ferrite polygonale, ≥ 90 % de martensite et ≤ 2 % en volume d'austénite résiduelle, au moins la moitié de la martensite étant de la martensite revenue. L'invention concerne en outre un procédé de fabrication d'un tel produit laminé plat en acier.
EP16723293.3A 2015-05-06 2016-05-04 PRODUIT EN ACIER PLAT ET PROCÉDÉ DE FABRICATION DE
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EP3859041A4 (fr) * 2018-09-28 2021-12-15 Posco Tôle d'acier laminée à froid à haute résistance ayant un rapport d'expansion de trou élevé, tôle d'acier galvanisée à chaud par trempe à haute résistance, et procédés de fabrication associés
US11753693B2 (en) 2018-09-28 2023-09-12 Posco Co., Ltd High-strength cold rolled steel sheet having high hole expansion ratio, highstrength hot-dip galvanized steel sheet, and manufacturing methods therefor

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KR101917472B1 (ko) * 2016-12-23 2018-11-09 주식회사 포스코 항복비가 낮고 균일연신율이 우수한 템퍼드 마르텐사이트 강 및 그 제조방법
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WO2019063081A1 (fr) * 2017-09-28 2019-04-04 Thyssenkrupp Steel Europe Ag Produit plat en acier et son procédé de fabrication
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CN112585284A (zh) * 2018-05-22 2021-03-30 蒂森克虏伯钢铁欧洲股份公司 由钢形成的具有高抗拉强度的板材成型件及其制造方法
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EP3872206B1 (fr) * 2020-02-28 2023-06-21 ThyssenKrupp Steel Europe AG Procédé de fabrication d'un produit plan en acier laminé à froid, traité ultérieurement et produit plan en acier laminé à froid, traité ultérieurement
WO2021176249A1 (fr) * 2020-03-02 2021-09-10 Arcelormittal Tôle d'acier laminée à froid à haute résistance et recuite après galvanisation et son procédé de fabrication
CN114107794B (zh) * 2020-08-31 2023-08-11 宝山钢铁股份有限公司 一种980MPa级超低碳马氏体加残奥型超高扩孔钢及其制造方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3859041A4 (fr) * 2018-09-28 2021-12-15 Posco Tôle d'acier laminée à froid à haute résistance ayant un rapport d'expansion de trou élevé, tôle d'acier galvanisée à chaud par trempe à haute résistance, et procédés de fabrication associés
US11753693B2 (en) 2018-09-28 2023-09-12 Posco Co., Ltd High-strength cold rolled steel sheet having high hole expansion ratio, highstrength hot-dip galvanized steel sheet, and manufacturing methods therefor

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WO2016177763A1 (fr) 2016-11-10
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ZA201707321B (en) 2022-11-30
MX2017014090A (es) 2018-03-01
KR20180003581A (ko) 2018-01-09
ES2820348T3 (es) 2021-04-20
JP6788612B2 (ja) 2020-11-25
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US20190119774A1 (en) 2019-04-25
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