EP2171116B1 - Verfahren zur herstellung eines verzinkten und dann wärmebehandelten stahlblechs durch dff-regulierung - Google Patents

Verfahren zur herstellung eines verzinkten und dann wärmebehandelten stahlblechs durch dff-regulierung Download PDF

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Publication number
EP2171116B1
EP2171116B1 EP08762800A EP08762800A EP2171116B1 EP 2171116 B1 EP2171116 B1 EP 2171116B1 EP 08762800 A EP08762800 A EP 08762800A EP 08762800 A EP08762800 A EP 08762800A EP 2171116 B1 EP2171116 B1 EP 2171116B1
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Prior art keywords
steel sheet
oxide
temperature
process according
zinc
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English (en)
French (fr)
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EP2171116A1 (de
Inventor
Jean-Michel Mataigne
Florence Bertrand
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ArcelorMittal France SA
Nippon Steel Corp
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ArcelorMittal France SA
Nippon Steel Corp
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Priority to EP08762800A priority Critical patent/EP2171116B1/de
Priority to PL08762800T priority patent/PL2171116T3/pl
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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 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°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.
  • 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. If the temperature T1 is below 680°C, the internal oxidation of silicon, manganese and aluminium will not be favoured, and the galvanizability of the steel sheet will be insufficient.
  • An atmosphere having a ratio air-to-fuel less than 1 leads to the formation of superficial oxidation of silicon, manganese and aluminium, and thus a superficial layer of oxides selected from the group consisting of silicon oxide, manganese oxide, aluminium oxide, and complex oxide comprising silicon and/or manganese and/or aluminium, possibly in combination with iron oxide is formed, and the wettability is impaired.
  • a ratio air-to-fuel above 1.2 the layer of iron oxide is too thick, and will not be completely reduced. Thus, the wettability will also 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 850°C.
  • T2 When the steel sheet is at the temperature T2, a dual phase microstructure composed of ferrite and austenite is formed.
  • T2 When T2 is above 850°C, the volume ratio of austenite grows too much, and external selective oxidation occurs on the steel surface. But when T2 is below 770°C, the time required to form a sufficient volume ratio of austenite is too high.
  • 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.
  • the reduced steel sheet is finally cooled at a cooling temperature T3 near the temperature of the bath of molten zinc, in order to avoid the cooling or the re-heating of said bath.
  • T3 is thus preferably between 460 and 510°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°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°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°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°C) to 750°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°C, then they are soaked at 800°C for 60 s, and finally they are cooled to 460 °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 °C.
  • the thickness of the zinc-based coating is 7 ⁇ m.
  • the aim is to compare the wettablilty 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.
  • the wettability is visually controlled by an operator.
  • the adherence of the coating is also visually controlled after a 180° bending test of samples.
  • Table I chemical composition of the steel of samples A and B, in % by weight, the balance of the composition being iron and unavoidable impurities (sample A and B).
  • Table I C Mn Si Al Mo Cr P Ti V Ni Nb 0.20 1.73 1.73 0.01 0.005 0.02 0.01 0.005 0.005 0.01 0.005
  • Table II Wettabilty Adherence Aspect of the surface Sample A** Bad Bad Bad Sample B* Good Good Good Good * according to the invention ** according to the conventional process
  • 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 480°C, 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)
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  • Crystallography & Structural Chemistry (AREA)
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  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (11)

  1. Prozess zum Herstellen eines schmelzgetauchten galvanisch getemperten (galvannealed) Stahlblechs, das eine durch Transformation induzierte Plastizitäts-(TRIP)-Mikrostruktur hat, die Ferrit, Restaustenit und optional Martensit und/oder Balnit umfasst, wobei der Prozess die Schritte umfasst, die aus Folgendem bestehen:
    - Bereitstellen eines Stahlblechs, dessen Zusammensetzung Folgendes in Gewichts-% umfasst:
    0,01 ≤ C ≤ 0,22%
    0,50 ≤ Mn ≤ 2,0%
    0,5 < Si ≤ 2,0%
    0,005 ≤ A1 ≤ 2,0
    Mo < 0,01%
    Cr ≤ 1,0%
    P < 0,02%
    T2 ≤ 0,20%
    V ≤ 0,40%
    Ni ≤ 1,0%
    Nb ≤ 0,20%,
    wobei der Rest der Zusammensetzung Eisen und unvermeidliche Verunreinigungen sind, die aus dem Verhütten herrühren,
    - Oxidieren des Stahlblechs durch Erwärmen desselben von Umgebungstemperatur auf eine Temperatur T1 zwischen 680 und 800°C im Direktflammenofen, in dem die Atmosphäre Luft und Brennstoff in einem Luft-Brennstoff-Verhältnis zwischen 1,0 und 1,2 umfasst, um eine Schicht von Eisenoxid auf der Oberfläche des Stahlblechs zu bilden und um ein inneres Oxid des mindestens einen Typs von Oxid zu bilden, das aus der Gruppe bestehend Si-Oxid, Mn-Oxid, Al-Oxid, Komplexoxid, das Si und Mn umfasst, Komplexoxid, das Si und Al umfasst, Komplexoxid, das Al und Mn umfasst, und Komplexoxid, das Si, Mn und Al umfasst, ausgewählt ist,
    - Reduzieren des oxidierten Stahlblechs, um die Schicht von Eisenoxid zu reduzieren,
    - Feuermetallisieren des reduzierten Stahlblechs, um ein zinkbasiertes beschichtetes Stahlblech zu bilden, und
    - Einwirkenlassen einer Legierungsbehandlung auf das zinkbasierte beschichtete Stahlblech, um ein galvannealed Stahlblech zu erhalten.
  2. Prozess nach Anspruch 1, wobei das Stahlblech P < 0,010% in Gewichts-% umfasst.
  3. Prozess nach Anspruch 1 oder 2, wobei das Stahlblech Mo≤ 0,006% in Gewichts-% umfasst.
  4. Prozess nach einem der Ansprüche 1 bis 3, wobei das Reduzieren des oxidierten Stahlblechs aus einer Wärmebehandlung besteht, die in einer Atmosphäre ausgeführt wird, welche mehr als 15 Volumen-% Wasserstoff umfasst, wobei der Rest Stickstoff und unvermeidliche Verunreinigungen sind, wobei die Wärmebehandlung eine Heizphase von der Temperatur T1 bis zu einer Haltetemperatur T2, eine Haltephase bei der Haltetemperatur T2 für eine Haltezeit t2 und eine Kühlungsphase von der Haltetemperatur T2 bis zu einer Kühltemperatur T3 umfasst.
  5. Prozess nach Anspruch 4, wobei die Haltetemperatur T2 zwischen 770 und 850°C liegt.
  6. Prozess nach Anspruch 4 oder 5, wobei die Haltezeit t2 zwischen 20 und 180 s liegt.
  7. Prozess nach einem der Ansprüche 4 bis 6, wobei die Kühltemperatur T3 zwischen 460 und 510°C liegt.
  8. Prozess nach einem der Ansprüche 3 bis 7, wobei das Reduzieren in einem Strahlrohrofen oder in einem Widerstandsofen ausgeführt wird.
  9. Prozess nach einem der Ansprüche 1 bis 8, wobei das Feuermetallisieren durch Schmelztauchen des reduzierten Stahlblechs in ein Schmelzbad ausgeführt wird, das 0,08 bis 0,135 Gewichts-% Aluminium umfasst, wobei der Rest Zink und unvermeidliche Verunreinigungen sind.
  10. Prozess nach Anspruch 9, wobei die Temperatur des Schmelzbades zwischen 450 und 500°C liegt.
  11. Prozess nach einem der Ansprüche 1 bis 10, wobei die Legierungsbehandlung durch Erwärmen des zinkbasierten beschichteten Stahlblechs auf eine Temperatur T4 zwischen 460 und 510°C für eine Haltezeit t4 zwischen 10 und 30 s ausgeführt wird.
EP08762800A 2007-06-29 2008-06-06 Verfahren zur herstellung eines verzinkten und dann wärmebehandelten stahlblechs durch dff-regulierung Active EP2171116B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP08762800A EP2171116B1 (de) 2007-06-29 2008-06-06 Verfahren zur herstellung eines verzinkten und dann wärmebehandelten stahlblechs durch dff-regulierung
PL08762800T PL2171116T3 (pl) 2007-06-29 2008-06-06 Proces produkcji blachy stalowej cynkowanej zanurzeniowo z krótkotrwałym wyżarzaniem przez regulację DFF

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP07290816A EP2009129A1 (de) 2007-06-29 2007-06-29 Verfahren zur Herstellung eines galvanisierten oder Galvanneal-Stahlblechs durch DFF-Regulierung
EP08762800A EP2171116B1 (de) 2007-06-29 2008-06-06 Verfahren zur herstellung eines verzinkten und dann wärmebehandelten stahlblechs durch dff-regulierung
PCT/IB2008/001462 WO2009004425A1 (en) 2007-06-29 2008-06-06 Process for manufacturing a galvannealed steel sheet by dff regulation

Publications (2)

Publication Number Publication Date
EP2171116A1 EP2171116A1 (de) 2010-04-07
EP2171116B1 true EP2171116B1 (de) 2011-08-24

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ATE521726T1 (de) 2011-09-15
RU2451107C2 (ru) 2012-05-20
EP2009129A1 (de) 2008-12-31
JP5713673B2 (ja) 2015-05-07
KR101273308B1 (ko) 2013-06-11
CA2701091A1 (en) 2009-01-08
RU2010102924A (ru) 2011-08-10
PL2171116T3 (pl) 2012-01-31
WO2009004425A1 (en) 2009-01-08
BRPI0813687B1 (pt) 2018-10-30
CN101809182B (zh) 2015-08-05
CN101809182A (zh) 2010-08-18
EP2171116A1 (de) 2010-04-07
US20100193081A1 (en) 2010-08-05
BRPI0813687A8 (pt) 2015-12-15
ES2371985T3 (es) 2012-01-12
JP2015078438A (ja) 2015-04-23
AR067339A1 (es) 2009-10-07
BRPI0813687A2 (pt) 2014-12-30
CA2701091C (en) 2012-04-17
JP2010532820A (ja) 2010-10-14
KR20100055389A (ko) 2010-05-26

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