WO2009004425A1 - Process for manufacturing a galvannealed steel sheet by dff regulation - Google Patents

Process for manufacturing a galvannealed steel sheet by dff regulation Download PDF

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Publication number
WO2009004425A1
WO2009004425A1 PCT/IB2008/001462 IB2008001462W WO2009004425A1 WO 2009004425 A1 WO2009004425 A1 WO 2009004425A1 IB 2008001462 W IB2008001462 W IB 2008001462W WO 2009004425 A1 WO2009004425 A1 WO 2009004425A1
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WO
WIPO (PCT)
Prior art keywords
steel sheet
oxide
temperature
process according
zinc
Prior art date
Application number
PCT/IB2008/001462
Other languages
English (en)
French (fr)
Inventor
Jean-Michel Mataigne
Florence Bertrand
Original Assignee
Arcelormittal France
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
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=38608886&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2009004425(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Arcelormittal France filed Critical Arcelormittal France
Priority to CA2701091A priority Critical patent/CA2701091C/en
Priority to KR1020107001332A priority patent/KR101273308B1/ko
Priority to PL08762800T priority patent/PL2171116T3/pl
Priority to AT08762800T priority patent/ATE521726T1/de
Priority to EP08762800A priority patent/EP2171116B1/en
Priority to JP2010514160A priority patent/JP5713673B2/ja
Priority to US12/666,702 priority patent/US20100193081A1/en
Priority to BRPI0813687A priority patent/BRPI0813687B1/pt
Priority to CN200880025372.2A priority patent/CN101809182B/zh
Publication of WO2009004425A1 publication Critical patent/WO2009004425A1/en

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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/52—Methods of heating with flames
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/11—Making amorphous alloys
    • 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
    • C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
    • 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
    • C23C2/261—After-treatment in a gas atmosphere, e.g. inert or reducing atmosphere
    • 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
    • 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

Definitions

  • the present invention relates to a process for manufacturing a hot-dip galvannealed steel sheet having a TRIP microstructure.
  • TRIP steels (the term TRIP standing for transformation-induced plasticity), which combine very high mechanical strength with the possibility of very high levels of deformation.
  • TRIP steels have a microstructure comprising ferrite, residual austenite and optionally martensite and/or bainite, which allows them to achieve tensile strength from 600 to 1000 MPa.
  • This type of steel is widely used for production of energy-absorbing parts, such as for example structural and safety parts such as longitudinal members and reinforcements.
  • TRIP steel sheets are obtained by adding a large amount of silicon to steel. Silicon stabilizes the ferrite and the austenite at room temperature, and prevents residual austenite from decomposing to form carbide.
  • TRIP steel sheets containing more than 0.2% by weight of silicon are galvanized with difficulty, because silicon oxides are formed on the surface of the steel sheet during the annealing taking place just before the coating. These silicon oxides show a poor wettability toward the molten zinc, and deteriorate the plating performance of the steel sheet.
  • TRIP steel having low silicon content (less than 0.2% by weight).
  • this has a major drawback: a high level of tensile strength, that is to say about 800 MPa, can be achieved only if the content of carbon is increased. But, this has the effect to lower the mechanical resistance of the welded points.
  • the TRIP effect is observed when the TRIP steel sheet is being deformed, as the residual austenite is transformed into martensite under the effect of the deformation, and the strength of the TRIP steel sheet increases.
  • the purpose of the present invention is therefore to remedy the aforementioned drawbacks and to propose a process for hot-dip galvannealing a steel sheet having a high silicon content (more than 0.5% by weight) and a
  • TRIP microstructure showing high mechanical characteristics, that guarantees a good wettability of the surface steel sheet and no non-coated portions, and thus guarantees a good adhesion and a nice surface appearance of the zinc alloy coating on the steel sheet, and that preserves the TRIP effect.
  • the first subject of the invention is a process for manufacturing a hot-dip galvannealed steel sheet having a TRIP microstructure comprising ferrite, residual austenite and optionally martensite and/or bainite, said process comprising the steps consisting in:
  • the interlamellar austenite is progressively enriched with carbon without any carbides being precipitated. This enrichment is such that the austenite is stabilized, that is to say the martensitic transformation of this austenite does not take place upon cooling down to room temperature.
  • Manganese with a content between 0.50 and 2.0% by weight. Manganese promotes hardenability, making it possible to achieve a high yield strength R e . Manganese promotes the formation of austenite, contributes to reducing the martensitic transformation start temperature Ms and to stabilizing the austenite. However, it is necessary to avoid the steel having too high a manganese content in order to prevent segregation, which may be demonstrated during heat treatment of the steel sheet. Furthermore, an excessive addition of manganese causes the formation of a thick internal manganese oxide layer which causes brittleness, and the adhesion of the zinc based coating will not be sufficient.
  • Silicon with a content of more than 0.5% by weight, preferably more than 0.6% by weight, and less or equal to 2.0% by weight. Silicon improves the yield strength R e of the steel. This element stabilizes the ferrite and the residual austenite at room temperature. Silicon inhibits the precipitation of cementite upon cooling from austenite, considerably retarding the growth of carbides. This stems from the fact that the solubility of silicon in cementite is very low and the fact that silicon increases the activity of the carbon in austenite. Thus, any cementite nucleus that forms will be surrounded by a silicon-rich austenitic region, and rejected to the precipitate-matrix interface.
  • This silicon-enriched austenite is also richer in carbon, and the growth of the cementite is slowed down because of the reduced diffusion resulting from the reduced carbon activity gradient between the cementite and the neighbouring austenitic region.
  • This addition of silicon therefore contributes to stabilizing an amount of residual austenite sufficient to obtain a TRIP effect.
  • internal silicon oxides and complex oxide comprising silicon and/or manganese and/or aluminium are formed and dispersed under the surface of the sheet.
  • an excessive addition of silicon causes the formation of a thick internal silicon oxide layer and possibly complex oxide comprising silicon and/or manganese and/or aluminium which causes brittleness and the adhesion of the zinc based coating will not be sufficient.
  • aluminium with a content between 0.005 and 2.0% by weight. Like the silicon, aluminium stabilizes ferrite and increases the formation of ferrite as the steel sheet cools down. It is not very soluble in cementite and can be used in this regard to avoid the precipitation of cementite when holding the steel at a bainitic transformation temperature and to stabilize the residual austenite. A minimum amount of aluminium is required in order to deoxidize the steel.
  • Chromium with a content not exceeding 1.0% by weight.
  • the chromium content must be limited in order to avoid surface appearance problems when galvanizing the steel
  • Phosphorus with a content not exceeding 0.02% by weight, and preferably less than 0.010% by weight. Phosphorus in combination with silicon increases the stability of the residual austenite by suppressing the precipitation of carbides.
  • - Titanium with a content not exceeding 0.20% by weight. Titanium improves the yield strength of R e , however its content must be limited to 0.20% by weight in order to avoid degrading the toughness.
  • Vanadium with a content not exceeding 0.40% by weight. Vanadium improves the yield strength of R e by grain refinement, and improves the weldability of the steel. However, above 0.40% by weight, the toughness of the steel is degraded and there is a risk of cracks appearing in the weld zones.
  • Nickel with a content not exceeding 1.0% by weight. Nickel increases the yield strength of R e . Its content is generally limited to 1.0% by weight because of its high cost.
  • Niobium with a content not exceeding 0.20% by weight. Niobium promotes the precipitation of carbonitrides, thereby increasing the yield strength of R e . However, above 0.20% by weight, the weldability and the hot formability are degraded.
  • the balance of the composition consists of iron and other elements that are usually expected to be found and impurities resulting from the smelting of the steel, in proportions that have no influence on the desired properties.
  • the steel sheet having the above composition is first subjected to an oxidation followed by a reduction, before being hot-dip galvanized in a bath of molten zinc and heat-treated to form said galvannealed steel sheet.
  • the aim is to form an oxidized steel sheet having an outer layer of iron oxide with a controlled thickness which will protect the steel from the selective outer oxidation of silicon, manganese and aluminium, while the steel sheet is annealed before the hot-dip galvanization.
  • Said oxidation of the steel sheet is performed under conditions that allow the formation, on the surface of the steel sheet, of a layer of iron oxide containing no superficial oxides selected from the group consisting of silicon oxide, manganese oxide, aluminium oxide, complex oxide comprising silicon and/or manganese and/or aluminium.
  • a layer of iron oxide containing no superficial oxides selected from the group consisting of silicon oxide, manganese oxide, aluminium oxide, complex oxide comprising silicon and/or manganese and/or aluminium.
  • a layer of an internal oxide of at least one type of oxide selected from the group consisting of silicon oxide, manganese oxide, aluminium oxide, complex oxide comprising Si and Mn, complex oxide comprising Si and Al, complex oxide comprising Mn and Al and complex oxide comprising Si, Mn and Al is thus formed.
  • the oxidation is preferably performed by heating said steel sheet from ambient temperature to a heating temperature T1 which is between 680 and 800 0 C, in a direct flame furnace where the atmosphere comprises air and fuel, with a ratio air-to-fuel preferably between 1 and 1.2.
  • T1 is above 800 0 C
  • the iron oxide layer formed on the surface of the steel sheet will contain manganese coming from the steel, and the wettability will be impaired.
  • the oxidized steel sheet When leaving the direct flame furnace, the oxidized steel sheet is reduced in conditions permitting the achievement of the complete reduction of the iron oxide into iron.
  • This reduction step can be performed in a radiant tube furnace or in a resistance furnace.
  • Said oxidized steel sheet is thus heat treated in an atmosphere comprising preferably more than 15% by volume of hydrogen, the balance being nitrogen and unavoidable impurities. Indeed, if the content of hydrogen in the atmosphere is less than 15% by volume, the layer of iron oxide can be insufficiently reduced and the wettability is impaired.
  • Said oxidized steel sheet is heated from the heating temperature T1 to a soaking temperature T2, then it is soaked at said soaking temperature T2 for a soaking time t2, and is finally cooled from said soaking temperature T2 to a cooling temperature T3.
  • Said soaking temperature T2 is preferably between 770 and 85O 0 C.
  • sufficient austenite must be formed during the soaking step, so that sufficient residual austenite is maintained during the cooling step.
  • the soaking is performed for a time t2, which is preferably between 20 and 180s. If the time t2 is longer than 180s, the austenite grains coarsen and the yield strength R e of the steel after forming will be limited. Furthermore, the hardenability of the steel is low. However, if the steel sheet is soaked for a time t2 less than 20s, the proportion of austenite formed will be insufficient and sufficient residual austenite and bainite will not form when cooling.
  • T3 is thus preferably between 460 and 510 0 C. Therefore, a zinc-based coating having a homogenous microstructure can be obtained.
  • the steel sheet When the steel sheet is cooled, it is hot dipped in the bath of molten zinc whose temperature is preferably between 450 and 500 0 C.
  • This bath can contain 0.08 to 0.135% by weight of dissolved aluminium, the balance being zinc and unavoidable impurities.
  • Aluminium is added in the bath in order to deoxidize the molten zinc, and to make it easier to control the thickness of the zinc-based coating. In that condition, precipitation of delta phase (FeZn 7 ) is induced at the interface of the steel and of the zinc-based coating.
  • the steel sheet When leaving the bath, the steel sheet is wiped by projection of a gas, in order to adjust the thickness of the zinc-based coating. This thickness, which is generally between 3 and 10 ⁇ m, is determined according to the required resistance to corrosion.
  • the hot-dip galvanized steel sheet is finally heat-treated so that a coating made of a zinc-iron alloy is obtained, by diffusion of the iron from steel to the zinc of the coating.
  • This alloying treatment can be performed by maintaining said steel sheet at a temperature T4 between 460 and 510 0 C for a soaking time t4 between 10 and 30s. Thanks to the absence of external selective oxidation of silicon, manganese and aluminium, this temperature T4 is lower than the conventional alloying temperatures. For that reason, large quantities of molybdenum to the steel are not required, and the content of molybdenum in the steel can be limited to less than 0.01% by weight. If the temperature T4 is below 460 0 C, the alloying of iron and zinc is not possible.
  • the time t4 is adjusted so that the average iron content in the alloy is between 8 and 12% by weight, which is a good compromise for improving the weldability of the coating and limiting the powdering while shaping.
  • Samples A and B are pre-heated from ambient temperature (20 0 C) to 750 0 C, in a direct flame furnace. They are subsequently and continuously annealed in a radiant tube furnace, where they are heated from 750° to 800 0 C, then they are soaked at 800°C for 60 s, and finally they are cooled to 460 0 C.
  • the atmosphere in the radiant tube furnace comprises 30% by volume of hydrogen, the balance being nitrogen and unavoidable impurities.
  • samples A and B are hot dip galvanized in a molten zinc- based bath comprising 0.12% by weight of aluminium, the balance being zinc and unavoidable impurities.
  • the temperature of said bath is 460 0 C.
  • the thickness of the zinc-based coating is 7 ⁇ m.
  • the aim is to compare the wettability and the adherence of these samples, when the air-to-fuel ratio in the direct flame furnace fluctuates.
  • the air-to-fuel ratio is 0.90 for sample A, and 1.05 according to the invention for sample B.
  • the results are shown in table II.
  • Figure 1 is a photography of sample A after the pre-heating step and before the annealing step
  • figure 2 is a photography of sample B after the pre-heating step and before the annealing step.
  • the aim is to show the effect of the internal selective oxidation of silicon and manganese on the temperature of alloying.
  • the temperature of alloying treatment applied to sample B in order to obtain a galvannealed steel sheet according to the invention is compared with the temperature of alloying of sample A.
  • Sample B which has been hot dip galvanized is then subjected to an alloying treatment by heating it to 48O 0 C 1 and by maintaining it at this temperature for 19 s .
  • the inventors have checked that the TRIP microstructure of the obtained hot dip galvannealed steel sheet according to the invention was not lost by this alloying treatment.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
PCT/IB2008/001462 2007-06-29 2008-06-06 Process for manufacturing a galvannealed steel sheet by dff regulation WO2009004425A1 (en)

Priority Applications (9)

Application Number Priority Date Filing Date Title
CA2701091A CA2701091C (en) 2007-06-29 2008-06-06 Process for manufacturing a galvannealed steel sheet by dff regulation
KR1020107001332A KR101273308B1 (ko) 2007-06-29 2008-06-06 Ｄｆｆ 조절에 의한 합금화 아연도금 강판의 제조 방법
PL08762800T PL2171116T3 (pl) 2007-06-29 2008-06-06 Proces produkcji blachy stalowej cynkowanej zanurzeniowo z krótkotrwałym wyżarzaniem przez regulację DFF
AT08762800T ATE521726T1 (de) 2007-06-29 2008-06-06 Verfahren zur herstellung eines verzinkten und dann wärmebehandelten stahlblechs durch dff- regulierung
EP08762800A EP2171116B1 (en) 2007-06-29 2008-06-06 Process for manufacturing a galvannealed steel sheet by dff regulation
JP2010514160A JP5713673B2 (ja) 2007-06-29 2008-06-06 Ｄｆｆ調整によって合金化亜鉛めっき鋼板を製造する方法
US12/666,702 US20100193081A1 (en) 2007-06-29 2008-06-06 Process for manufacturing a galvannealed steel sheet by dff regulation
BRPI0813687A BRPI0813687B1 (pt) 2007-06-29 2008-06-06 processo para produção de uma chapa de aço galvanizada e recozida
CN200880025372.2A CN101809182B (zh) 2007-06-29 2008-06-06 通过dff调节制造锌镀层退火的钢片材的方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP07290816.3 2007-06-29
EP07290816A EP2009129A1 (en) 2007-06-29 2007-06-29 Process for manufacturing a galvannealed steel sheet by DFF regulation

Publications (1)

Publication Number Publication Date
WO2009004425A1 true WO2009004425A1 (en) 2009-01-08

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Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/IB2008/001462 WO2009004425A1 (en) 2007-06-29 2008-06-06 Process for manufacturing a galvannealed steel sheet by dff regulation

Country Status (13)

Country Link
US (1) US20100193081A1 (pt)
EP (2) EP2009129A1 (pt)
JP (2) JP5713673B2 (pt)
KR (1) KR101273308B1 (pt)
CN (1) CN101809182B (pt)
AR (1) AR067339A1 (pt)
AT (1) ATE521726T1 (pt)
BR (1) BRPI0813687B1 (pt)
CA (1) CA2701091C (pt)
ES (1) ES2371985T3 (pt)
PL (1) PL2171116T3 (pt)
RU (1) RU2451107C2 (pt)
WO (1) WO2009004425A1 (pt)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2906734B1 (fr) 2013-03-06 2022-06-01 Arcelormittal PROCÉDÉ DE RÉALISATION D'UNE TÔLE À REVÊTEMENT ZnAl AVEC UN ESSORAGE OPTIMISÉ, TÔLE, PIÈCE ET VÉHICULE CORRESPONDANTS

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ES2876258T3 (es) * 2009-12-29 2021-11-12 Posco Partes prensadas en caliente con chapadas con zinc y procedimiento de producción de las mismas
KR20120075260A (ko) * 2010-12-28 2012-07-06 주식회사 포스코 도금밀착성이 우수한 용융도금강판 및 그 제조방법
TWI504757B (zh) * 2011-09-30 2015-10-21 Nippon Steel & Sumitomo Metal Corp High strength molten galvanized steel sheet and its manufacturing method
KR20130076589A (ko) * 2011-12-28 2013-07-08 주식회사 포스코 도금표면 품질 및 도금밀착성이 우수한 고강도 용융아연도금강판 및 그 제조방법
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