WO2009084793A1 - Tôle d'acier revêtue à haute teneur en manganèse à résistance et ductilité élevées, et son procédé de fabrication - Google Patents

Tôle d'acier revêtue à haute teneur en manganèse à résistance et ductilité élevées, et son procédé de fabrication Download PDF

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WO2009084793A1
WO2009084793A1 PCT/KR2008/004536 KR2008004536W WO2009084793A1 WO 2009084793 A1 WO2009084793 A1 WO 2009084793A1 KR 2008004536 W KR2008004536 W KR 2008004536W WO 2009084793 A1 WO2009084793 A1 WO 2009084793A1
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steel sheet
slab
temperature
high manganese
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Il Ryoung Sohn
Sun Ho Jeon
Gyo Sung Kim
Kwang Geun Chin
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Posco
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    • 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
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    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • 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
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    • 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
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    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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    • 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
    • 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
    • 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
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    • 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
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling

Definitions

  • the present invention relates to a high manganese galvanized steel sheet having high ductility and strength as well as excellent corrosion resistance and workability, in which high manganese steel containing 15 to 30 wt% manganese (Mn) is plated with zinc (Zn) so as to form a single galvanized layer or a plated layer composed of 5 wt% or less Mn, 5 to 15 wt% iron (Fe), balance Zn, and inevitable impurities introduced from a base metal when plated.
  • Mn manganese steel containing 15 to 30 wt% manganese
  • Zn zinc
  • an embodiment of the present invention is directed to provide a plating method for endowing high manganese steel, a kind of high-quality steel, with corrosion resistance. Disclosure of Invention Technical Problem
  • Embodiments of the present invention provide high manganese steel containing a great deal of Mn through an optimum alloy design, and a galvanizing and/or gal- vannealing method as a processing technique suitable for the high manganese steel.
  • a high manganese plated steel sheet which contains, by weight, 0.3% to 0.9% carbon (C), 15% to 30% manganese (Mn), 0.1% to 5.0% aluminum (Al), 0.04% or less nitrogen (N), 0.03% or less sulfur (S), 0.1% or less phosphor (P), one or two or more selected from the group consisting of 1.0% or less chrome (Cr), 1.0% or less molybdenum (Mo), 0.5% or less copper (Cu), 5.0% or less silicon (S), 0.0005% to 0.04% boron (B), 2.0% or less nickel (M), 0.5% or less niobium (Nb), 0.5% of less vanadium (V), 0.005% to 0.1% antimony (Sb), 0.001% to 0.3% titanium (Ti), 0.0005% to 0.04% lanthanum (La), 0.0005% to 0.04% cesium (Ce), 0.005% to 0.10% zirconium (Zr), and 0.0005% to 0.03
  • An oxide film of Zn alone or Zn-Fe-Mn composite may be formed on a surface of the steel sheet.
  • the oxide film of Zn-Fe-Mn composite contains, by weight, 5% or less Mn, and 5% to 15% Fe, inevitable impurities, and balance Zn on a basis of the oxide film.
  • a method of manufacturing a high manganese plated steel sheet includes: a heating step of heating a continuously cast slab at a temperature of 1050 0 C to 1300 0 C, the continuously cast slab containing, by weight, 0.3% to 0.9% carbon (C), 15% to 30% manganese (Mn), 0.1% to 5.0% aluminum (Al), 0.04% or less nitrogen (N), 0.03% or less sulfur (S), 0.1% or less phosphor (P), one or two or more selected from the group consisting of 1.0% or less chrome (Cr), 1.0% or less molybdenum (Mo), 0.5% or less copper (Cu), 5.0% or less silicon (S), 0.0005% to 0.04% boron (B), 2.0% or less nickel (M), 0.5% or less niobium (Nb), 0.5% of less vanadium (V), 0.005% to 0.1% antimony (Sb), 0.001% to 0.3% titanium (Ti), 0.0005% to 0.04%
  • the method may further include a galvannealing step so as to introduce Mn, Fe, etc. of base metal into the plated layer to form a stable composite oxide plated layer, thereby providing the high manganese plated steel sheet having high strength and toughness and improving corrosion resistance.
  • the high manganese plated steel sheet has Zn-Fe-Mn composite hot-dip galvanized layer that secures high ductility and strength and that has corrosion resistance better than existing hot-dip galvanized steel. Best Mode for Carrying out the Invention
  • Exemplary embodiments of the present invention provide a high manganese galvanized steel sheet having high ductility and strength as well as excellent corrosion resistance and workability, in which high manganese steel containing 15 to 30 wt% of manganese (Mn) is plated with zinc (Zn) so as to form a single galvanized layer or a galvannealed layer composed of 5 wt% or less Mn, 5 to 15 wt% iron (Fe), balance Zn, and inevitable impurities introduced from a base metal during plating, and a method of manufacturing the same.
  • Mn manganese
  • Zn zinc
  • Snce C contributes to stabilization of an austenite phase, it is favorable to increase an added amount of C.
  • the added amount of C is less than 0.3%, austenite stability is not maintained, and thus the fraction of a ferrite phase or an ⁇ - martensite phase other than the austenite phase is increased.
  • the added amount of C exceeds 0.9%, the austenite stability is greatly increased, and thus workability is reduced by transition of a deformation behavior caused by slip deformation.
  • the added amount of C is limited to a range of 0.3% to 0.9%.
  • Mn Manganese (Mn): 15% to 30%
  • Mn is an essential element that stabilizes an austenite phase as well as an important element that serves as a source that supplies Mn from a base metal to a plated layer in a galvannealing process during plating, and is added to a level of 15% to 30% for high manganese steel to which an embodiment of the present invention is applied.
  • Mn is added at an amount less than 15%, the fraction of a ferrite phase or an ⁇ - martensite phase other than the austenite phase is increased.
  • Mn is added at an amount exceeding 30%, high-temperature oxidation sharply occurs in a reheating process for hot rolling due to a high content of Mn, and thus deteriorates a quality of surface of a final product. Further, since a great deal of expensive Mn is added to increase production costs of the steel sheet, the added amount of Mn has an upper limit of 30%.
  • Al is typically added for deoxidation of steel, but for improvement of ductility in an embodiment of the present invention.
  • Al is an element for stabilizing a ferrite phase, but increases stacking fault energy in a slip plane, thereby inhibiting creation of an ⁇ -martensite phase to improve the ductility.
  • Mn when the added amount of Mn is low, Al inhibits the creation of the ⁇ -martensite phase. As such, Al goes far toward minimizing the added amount of Mn and improving formability.
  • Al is added at an amount of 0.1% or more.
  • the added amount of Al when the added amount of Al is more than 5.0%, creation of twins is inhibited to reduce ductility and continuous castability, and surface oxidation becomes serious to deteriorate the surface quality of a product when hot rolling.
  • the added amount of Al has an upper limit of 5.0%.
  • S is typically known that, when added excessively, S forms a S oxide layer on a surface of steel to degrade hot dip coating characteristics.
  • Mn- enriched steel when S is added at an appropriate amount, the S oxide layer is formed on the surface of the steel to inhibit oxidation in air.
  • the steel sheet after cold-rolled, the steel sheet can be prevented from forming a thick Mn oxide layer.
  • the cold rolled steel sheet After annealed, the cold rolled steel sheet can be prevented from corrosion, and thus the surface quality of the cold rolled steel sheet, particularly the base steel sheet, can be improved. Snce the thick Mn oxide layer is inhibited from being formed when hot dip coating is carried out, the hot dip coating characteristics are greatly improved.
  • the added amount of S has an upper limit of 5.0%.
  • S has a content of 0.04% or more in the steel, a desired purpose can be accomplished without separately adding S in an embodiment of the present invention.
  • Cr has an effect of forming a passivation film in air to inhibit corrosion.
  • Cr prevents decarburization of the steel, thereby inhibiting creation of an a - martensite phase from the surface of the steel sheet to improve formability of steel.
  • an added amount of Cr, a ferrite stabilizing element is increased, the creation of the a -martensite phase is accelerated to reduce ductility of steel. For this reason, the added amount of Cr has an upper limit of 1.0%.
  • Cu is a component added to increase corrosion resistance and strength. When an added amount of Cu exceeds 0.5%, red brittleness occurs to damage hot workability. Thus, the added amount of Cu is preferably limited to 0.5% or less.
  • M increases stability of an austenite phase to inhibit creation of an ⁇ '-martensite phase damaging formability, and thus is favorable in terms of improving workability of steel.
  • M is expensive.
  • the added amount of M is limited to 2.0% or less.
  • Mo is an element added to improve secondary working embrittlement resistance and platability. However, when an added amount of Mo exceeds 1.0%, Mo reduces the improving effect and is made economically unfavorable. Thus, the added amount of Mo is limited to 1.0% or less.
  • Nb and/or V are components added to increase strength. When an added amount of
  • Nb is more than 0.5%
  • Nb causes cracks during hot working.
  • V creates a low-melting-point compound to damage hot workability.
  • the added amounts of Nb and V are each limited to 0.5% or less.
  • N precipitates fine nitride in austenite grains in reaction with Al in the solidification process, thereby facilitating generating twins to improve strength and ductility when the steel sheet is formed.
  • an added amount of N exceeds 0.04%, the nitride is excessively precipitated to reduce hot workability and elongation.
  • the added amount of N is limited to 0.04% or less.
  • S is an element that is inevitably added on manufacturing steel. Thus, an added amount of S is limited to 0.03% or less. Particularly, S forms coarse Mn sulfide (MnS) to generate defects such as flange cracks, and reduces stretch flangability (hole expandability). Thus, the added amount of S is preferably limited to 0.03% or less.
  • MnS coarse Mn sulfide
  • P has a significant role in improving pickling characteristics of a hot rolled steel sheet.
  • P is an element that causes interfacial precipitation, and forms scales and chemically unstable Fe-P compounds precipitated on interfaces of the steel sheet to facilitate removal of the scales when pickling is carried out.
  • a content of P increases, a superficial shape becomes uniform, and the pickling characteristics are improved.
  • the added amount of P is preferably limited to 0.1% or less.
  • B is resolved in columnar grain boundaries at a temperature of 1000 0 C or more, and thus inhibits creation and movement of vacancies to strengthen the columnar grain boundaries.
  • B has little effect.
  • B creates a large quantity of carbide and nitride to act as a nucleus for precipitation of Al nitride, thereby promoting the precipitation of coarse Al nitride to embrittle the grain boundaries.
  • the proper added amount of B ranges from 0.0005% to 0.040%.
  • Ti is an element that is effective for an increase in strength of steel and grain refinement. When a content of Ti is less than 0.001%, it is difficult to obtain this effect. In contrast, when the content of Ti exceeds 0.3%, manufacturing costs are increased, and ductility of ferrite can be reduced due to excessive precipitates. Thus, the content of Ti is preferably limited to a range from 0.001% to 0.3%.
  • Zr is resolved in columnar grain boundaries, thereby increasing a melting temperature of an Al-enriched low-melting-point compound to prevent a liquid phase film from being formed at a temperature of 1300 0 C. Further, Zr has high affinity for nitrogen (N) to act as a nucleus for precipitation of coarse Al nitride that is attributable to embrittlement of the columnar grain boundaries, thereby strengthening the columnar grain boundaries.
  • N nitrogen
  • Zr is less than 0.005%, these effects are insignificant.
  • the added amount of Zr exceeds 0.10%, Zr is segregated in the grain boundaries, thereby causing embrittlement of the grain boundaries.
  • the added amount of Zr is limited to a range from 0.005% to 0.10%.
  • La and Ce are rare earth elements that serve to create a nucleus of a dendrite structure when molten steel is solidified, thereby refining a dendrite to inhibit growth of a columnar grain structure and facilitate creation of an equiaxed grain structure.
  • La and CE reduces size and amount of columnar grains attributable to grain boundary embrittlement, and increases an amount of equiaxed grains having excellent high-temperature ductility to improve hot workability.
  • La and Ce form compounds with P and S which are segregated in the grain boundaries to reduce rupture strength of a grain boundary, thereby reducing adverse influence of P and S.
  • added amounts of La and Ce are less than 0.0005%, this effect is insignificant.
  • La and Ce exceed 0.040%, La and Ce are saturated.
  • the added amounts of La and Ce are preferably limited to a range from 0.0005% to 0.040%.
  • Ca forms compounds with non-metallic inclusions such as Al O , MnO, MnS, etc. in molten steel to spheroidize the non-metallic inclusions, thereby increasing rupture strength of a columnar grain boundary, releasing sensitivity of generating flange cracks from the steel sheet, and increasing stretch flangability (hole expandability) of the steel sheet.
  • non-metallic inclusions such as Al O , MnO, MnS, etc.
  • Sb contributes to inhibition of growth of various sub-scales generated in a hot-rolling process. Alloy elements such as S, Mn, Al, etc. show a selective oxidation behavior along an interface of the surface of the hot-rolled steel sheet, whereas Sb is segregated at the interfaces or the surface of the steel sheet without oxidation in a hot-rolling process, thereby effectively inhibiting growth of sub-scales.
  • Sb is excessively added, an amount of Sb precipitated from the interfaces is increased, and there is a possibility of the interfaces being mechanically weakened.
  • an added amount of Sb is less than 0.005%, it is difficult to produce a desired effect.
  • Sb exceeds 0.1% there is a possibility of causing working embrittlement of material.
  • the added amount of Sb is limited to a range from 0.005% to 0.1%.
  • a hot-rolled steel sheet of high manganese steel is manufactured using continuous casting as in the process of manufacturing ordinary steel sheet.
  • Steel melted with the above-mentioned composition is homogenized at a temperature of 1050 0 C to 1300 0 C similar to typical conditions, and a homogenized sample is subjected to finish hot rolling at a temperature of 85O 0 C to 95O 0 C under typical conditions, hot rolling for coiling at a temperature of 65O 0 C or less, and pickling.
  • the heating temperature of a continuously cast slab is set to 1300 0 C as its upper limit. This is because a trace of alloy element strengthening a columnar grain boundary is added to increase the melting point of a low-melting-point compound of the columnar grain boundary up to about 1300 0 C.
  • a liquid phase film is generated from the columnar gain boundary of the continuously cast slab, and thus cracks occur during hot rolling.
  • the heating temperature is set to 1050 0 C as its lower limit.
  • a typical finish rolling temperature is about 900 0 C in a hot rolling process.
  • the steel sheet according to an embodiment of the present invention is subjected to hot rolling at this temperature.
  • a rolling load is increased, which not only overloads a rolling mill but also exerts a bad influence on a quality of the interior of the steel sheet.
  • Hot Rolling and Coiling temperature 750 c or less
  • the coiling temperature of the hot rolled steel sheet is preferably low.
  • the coiling temperature is limited to 75O 0 C or less that is a sufficiently low temperature.
  • the steel sheet After the hot rolling, the steel sheet is subjected to pickling in a solution of HCl in order to remove oxidized scales formed on the surface thereof. If necessary, the steel sheet is subjected to cold rolling in order to adjust shape and thickness thereof.
  • the pickling is preferably carried out at HCl concentration of 5% to 25% within a range from 6O 0 C to 9O 0 C for 20 seconds or more.
  • the annealing temperature is limited to 600 0 C or more. Snce the high manganese steel according to an embodiment of the present invention is austenite steel free of phase transformation, workability can be sufficiently secured when the steel is heated at a recrystallization temperature or more. As such, the annealing is carried out under typical annealing conditions.
  • the hot galvanizing bath is a typical galvanizing bath based on a composition of Zn-
  • the plating is carried out in a plating bath of Zn-0.013%Al by weight.
  • the plated layer does not undergo a great change in physical properties and corrosion resistance.
  • the steel sheet is subjected to galvannealing at a temperature of 44O 0 C to 58O 0 C, thereby forming a galvannealed layer.
  • the galvannealed layer is created in such a manner that Mn, Fe or the other components contained in base metal during galvannealing are diffused to react with a plating element of Zn.
  • a composition of the galvannealed layer includes, by weight, 5% or less Mn, 5% to 15% Fe, balance Zn, and a trace of other impurities introduced in the plating process among constituent elements of steel.
  • a oxide film formed after annealing The oxide film consit of Al alone or Mn-Al composite. An average thickness of the oxide film is 500 nm or less. Further, the oxide film is required not to continuously formed 10/M (micrometer) or more when its thickness is 50nm or more. [96] [97] Now, the high manganese galvanized steel sheet according to Examples of the present invention will be described in detail. [98]
  • Plating was performed in the following two methods.
  • the cold rolled steel sheet was annealed under N -10%H atmosphere at a temperature of 62O 0 C to 88O 0 C, and was immersed into Zn-0.021%Al bath maintained at a temperature of 46O 0 C, thereby forming a zinc plated layer on a surface thereof.
  • the cold rolled steel sheet was annealed under N -10%H atmosphere at a temperature

Abstract

L'invention porte sur un procédé de fabrication d'une tôle d'acier plaquée à haute teneur en manganèse. Le procédé consiste à chauffer une brame de coulée continue à une température de 1050°C à 1300°C ; à effectuer un laminage à chaud de finition sur la brame à une température de 850°C à 950°C ; à effectuer un laminage à chaud et un bobinage sur la brame à une température de 750°C ou moins ; à décaper la brame dans une solution de HCl ayant une concentration de 5 % à 25 % pendant 20 secondes ou plus ; à recuire la brame à une température de recristallisation de 600°C ; à immerger la brame dans un bain de galvanisation par immersion à chaud de façon à créer une couche plaquée sur une surface de la tôle d'acier.
PCT/KR2008/004536 2007-12-27 2008-08-05 Tôle d'acier revêtue à haute teneur en manganèse à résistance et ductilité élevées, et son procédé de fabrication WO2009084793A1 (fr)

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KR10-2007-0138538 2007-12-27

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