EP1113085B1 - Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte - Google Patents

Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte Download PDF

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Publication number
EP1113085B1
EP1113085B1 EP99870267A EP99870267A EP1113085B1 EP 1113085 B1 EP1113085 B1 EP 1113085B1 EP 99870267 A EP99870267 A EP 99870267A EP 99870267 A EP99870267 A EP 99870267A EP 1113085 B1 EP1113085 B1 EP 1113085B1
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Prior art keywords
steel
content
temperature
cold
rolled
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EP99870267A
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English (en)
French (fr)
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EP1113085A1 (de
Inventor
Serge Claessens
Dirk Vanderschueren
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Sidmar SA
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Sidmar SA
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Priority to AT99870267T priority Critical patent/ATE241022T1/de
Priority to DE69908151T priority patent/DE69908151T2/de
Priority to EP99870267A priority patent/EP1113085B1/de
Priority to ES99870267T priority patent/ES2200492T3/es
Priority to US09/733,424 priority patent/US6641931B2/en
Publication of EP1113085A1 publication Critical patent/EP1113085A1/de
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    • 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
    • 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
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22C38/18—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
    • 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
    • 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
    • C23C2/26—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the present invention is related to a method of production of a high strength cold-rolled metal coated steel product.
  • the present invention is also related to the direct products obtained by the method mentioned her above.
  • Those steels are also commonly called multi-phase steels or preferably dual phase steels.
  • Documents US-A-4394186 and BE-A-886583 are describing dual phase steel sheets having as major constituents a phase being ferrite and at least another phase being either martensite or bainite or retained austenite. These steel sheets have a low yield ratio, of approximately 0.6, and are free from yield point elongation.
  • the production method for obtaining uncoated steel sheets is to heat the steel in a continuous annealing line at a temperature within the intercritical region followed by a quenching in one step(called primary cooling R1) from the annealing temperature to a temperature lower than 200°C with an average cooling rate comprised between 1°C and 30°C per second.
  • the composition of the steel has a carbon content comprised between 0.01 to 0.3% with a manganese content comprised between 0.7 and 1.7%.
  • the production method for obtaining a hot dip coated steel is to heat the steel in a continuous annealing line at a temperature within the intercritical region followed by a quenching in two steps: in the first quenching step, the strip is quenched (primary cooling R1) down to a temperature between 420°C and 700°C (molten zinc bath temperature) at a cooling rate comprised within the range of 1°C/sec ⁇ R1 ⁇ 30°C/sec, the second quenching step (secondary cooling R2) consists in a quenching from the molten bath temperature to a temperature lower than 200°C at a cooling rate within the range of 100°C/sec ⁇ R2 ⁇ 300°C/sec.
  • primary cooling R1 molten zinc bath temperature
  • the first quenching step is to avoid the transformation of austenite to perlite
  • the second quenching step is performed to obtain the transformation of the austenite into martensite.
  • the described high (between 100°C and 300°C per second) secondary cooling rate (R2) of the steel strip which is still covered with molten metal is probably feasible at laboratory scale, but in the industrial technology of today this quenching is not feasible. Indeed, after the molten metal coating bath the coated strip (with molten metal at its surface) is cooled in open air (no forced air cooling) during its vertical transfer to the wiping knifes (regulation of the layer thickness) and is then cooled in a vertical cooling device, to ensure the same layer thickness on both sides.
  • a cooling rate, higher than 50°C per second can only be achieved by roll quenching, which is not applicable in said method due to the molten layer, or by water quenching, which is impossible to apply in said method on a molten metal surface and above a molten metal bath.
  • Those two quenching methods are applied on uncoated steel surfaces. So far in the state of the art, no industrial galvanising line has been equipped with such quenching devices used for secondary quenching.
  • EP-A-0501605 describes a galvanised steel sheet, which has a tensile strength not less than 800Mpa and a yield ratio lower than 0.6.
  • This steel contains carbon, manganese, niobium, titanium and boron and has a dual phase structure. After annealing at a temperature comprised between Ac3-30°C to Ac3+70°C the steel sheet is cooled at a rate higher than 50°C per second down to a temperature comprised between 450°C and 550°C. This controlled cooling step should avoid that the perlite transformation occurs.
  • the addition of manganese and chrome as alloying elements as a way of obtaining quenching structures is well known. Those elements have however a very detrimental effect on the adhesion of the coating metal on the steel surface.
  • JP-A-4350152 describes the manufacture of a galvanised steel sheet having a molybdenum content comprised between 0.005 and 0.5%, a boron-content comprised between 4 and 50 ppm, a silicon-content less than 0.5% and a carbon-content comprised between 0.01 and 0.2% with the presence of some Mn, Al and Ti elements.
  • the annealing temperature at the galvanising line lies higher than Ac3.
  • the cooling is performed at a cooling rate higher than 50°C per second.
  • This method has two main disadvantages: the high annealing temperature of above Ac3 is very expensive and the high cooling rate (> 50°C/second) in the secondary cooling, is hardly feasible industrially .
  • JP-A-56047555 is describing the manufacture of a galvanised steel plate by annealing a cold rolled steel strip through a continuous hot dip galvanising line.
  • the steel composition consists of 0.02-0.07% C, 1.5-2.5% Mn, 0.5-1%Cr, 0.01-0.1% Al, 0.07% or less Si, and the remaining is Fe.
  • the Mn, Cr and C-contents are defined by the following relation: C + 0,06 Mn + 0.03 Cr > 0.17%.
  • the steel strip is soaked between the transformation temperatures Ac1 and Ac3, and soon passed through the hot galvanising bath of the said hot dip galvanising line to obtain the galvanised steel plate having a low yield ratio of approx. 0.7 or less and a tensile strength of approx. 450MPa or more.
  • the high Mn(>1.5%) and Cr (>0.5%) concentrations have such a detrimental effect on the zinc adhesion that it is virtually impossible to obtain a defect free zinc layer for industrial applications. This is due to the heavy manganese and chrome oxides formed at the strip surface before entering the zinc bath.
  • JP-A-56163219 is describing a cold rolled high-tensile galvanised steel strip whereby a slab of the steel consisting of 0.02-0.15%C, 1.6-3.0% Mn, 0.1-1.0% Cr, less than 0.1% Si, 0.01-0.10% Al and the balance Fe with unavoidable impurities and satisfying the following relation : Mn%+1/2Cr% higher than or equal to 1.9%, is hot-rolled, pickled and cold-rolled to obtain a cold-rolled steel strip. Then, the slab is heated at an annealing temperature between Ac1 and Ac3 with an in-line annealing type continuous galvanising device and is immediately passed through a galvanising bath, whereby it is plated.
  • the average cooling rates up to the execution of the hot dipping after the in-line annealing are preferably about 2-8°C/sec and the average cooling rates down to about 350 °C after the plating are preferably about 3-8 °C/sec.
  • the high Mn (>1.5%) and Cr (>0.5%) concentrations have such a detrimental effect on the zinc adhesion that it is virtually impossible to obtain a defect free zinc layer for industrial applications. This is due to the heavy manganese and chrome oxides formed at the strip surface before entering the zinc bath.
  • Aluminising steel according to the above described process of annealing and cooling in two steps is also a known technique.
  • a combination of a good adhesion of the coating, together with a low decrease in strength because of the use at high temperature is necessary.
  • Aluminium coatings on standard commercial sheet steels show a poor temperature corrosion resistance above 650°C, because of the formation of brittle Al-Fe-Si-compounds.
  • aluminised steel grades have been made commercially available in the past with a high temperature corrosion resistance up to 800°C.
  • One commercial steel grade is known to have a good behaviour at 900°C.
  • a weakness of those steels is the continuous decrease in strength during the use time, related to the time spent at high temperature. To thwart the decrease in strength in this existing grade considerable amounts of Ti and Nb are added to the steel in order to inhibit the ferrite grain growth. However, by doing this, the decrease in strength is only retarded.
  • the present invention aims to produce a cold-rolled hot-dip metal coated multi-phase steel, having a tensile strength of at least 500 MPa, and a yield ratio (Re/Rm) lower than 0.65 in skinned condition and lower than 0.60 in unskinned condition.
  • the present invention aims to suggest a high strength steel with good formability and good metal coating adhesion behaviour, which are required for instance by the automobile industry for unexposed and exposed parts.
  • a further aim is to suggest an aluminised steel having a high temperature corrosion resistance up to 900°C, good coating adhesion and good strength properties during and after its use at these high temperatures.
  • the present invention relates to a method and a composition for producing a cold-rolled steel sheet with multi-phase structure and more particularly to a method and a composition for producing a cold-rolled metal coated steel sheet having excellent formability, high strength, low yield ratio and high ductility.
  • the present invention makes it possible to obtain an increase in strength by using it at high temperature, in combination with a good coating adhesion and a low yield ratio. Furthermore, because of the metallurgy of the steel, the mechanical values are reconditioned through its use at high temperature.
  • multiphase designates that the major constituent phases of the steel are a ferrite phase and a martensite phase.
  • a low amount of a bainite phase and of a retained austenite phase could be present.
  • yield ratio designates the ratio: yield strength/tensile strength i.e. Re/Rm.
  • the present invention is more particularly related to a steel composition
  • a steel composition comprising:
  • the invention also 5 relates to a method of producing a cold-rolled, metal coated, multi-phase steel having the above composition, said method comprising the steps of:
  • the invention also relates to the end product, which is a steel product having said composition, which is produced by said method and which is characterised by :
  • Figure 1 represents a schematic view of the annealing treatment at the hot dip coating line according to the method of the present invention. Additions of Cr and Mo retard the austenite transformation into perlite and bainite.
  • Figure 2 represents the influence of Cr-addition on the formation of Cr 2 O 3 on the surface of the steel sheet after soaking and before hot dip coating.
  • Figures 3a and 3b are representing industrial trial results, for the galvanised steel product according to the present invention, wherein :
  • Figure 4 represents the influence of the skin-pass reduction on the yield ratio of the galvanised steel product according to the present invention.
  • Figure 5 represents the temperature resistance of aluminised steel according to the present invention, compared to existing steels.
  • Figure 6 represents the strength in terms of yield strength Re and tensile strength Rm as a function of the number of hours spent at a high temperature.
  • Figure 7 compares the coating quality of an aluminised steel according to the present invention to that of an existing steel, after a prolonged exposure to 800°C.
  • Figure 8 illustrates the ability of the aluminised steel according to the present invention to retain its mechanical properties after cooling from a high temperature (reconditioning of the steel).
  • the following description is related to two embodiments of the method according to the present invention, namely for the production of a preferred galvanised steel sheet and for the production of a preferred aluminised steel sheet.
  • Mn and Cr, also Ti are essential in avoiding the formation of brittle Fe-Al-Si compounds during the use at high temperatures, which are detrimental for the coating adhesion.
  • Mn, Cr and Ti is beneficial for the phenomenon of interdiffusion of Fe and Al, which causes the coating to dissolve in the steel, leaving a ferrite phase at the surface with a high Al-content and an excellent high temperature corrosion resistance.
  • the steel composition for a 600 MPa strength combined with a yield ratio lower than 0.65, is defined by the following contents:
  • the C-content is determined by the desired strength level.
  • the Si-content is essentially important for hardness and for the flash butt weldability, but has to be limited to ensure sufficient coating adhesion and surface quality.
  • the process is preferably characterised by the following steps:
  • Figures 5 to 8 represent laboratory results for the aluminised steel according to the invention.
  • Figure 5 illustrates the temperature resistance of the present steel, by way of its weight increase as a function of temperature.
  • the reference 'High Ti ULC steel' refers to a commercially available Al-coated steel with a temperature resistance up to 800 °C.
  • the weight increase of the new steel is significantly lower at 900 °C, which is a consequence of the interdiffusion of Al and Fe, avoiding the formation of a brittle Fe-Al-Si layer and direct oxidation of the steel sheet.
  • Figure 6 illustrates the conservation and even the slight rise in the mechanical properties (Re and Rm) of the aluminised steel as a function of the number of hours spent at a temperature of 900°C.
  • Figure 7 illustrates the superior surface quality of the aluminised steel according to the present invention (no flaking at the surface (a) nor cracks in the coating layer (b)).
  • Figure 8 illustrates the ability of the aluminised steel according to the invention to undergo a reconditioning during cooling, after an exposure to the high temperature. This phenomenon allows to retain the good mechanical properties of the steel, after repeated use at high temperature. Influence of steel composition on the amount of bare spots (#/cm 2 ) detected after galvanising, using the thermal cycle as described within this document Cast N° Cr Mn Si Mo Bare spots #/cm 2 1 0 1.54 0.12 0 None 2 0.25 1.44 0.12 0.2 None 3 0.25 1.47 0.12 0.2 None 4 0.26 1.39 0.12 0.2 None 5 0.5 1.5 0.08 0 None 6 0.7 1.5 0 0 > 20 7 0 1.9 0 0 > 10 Obtained industrial results of the galvanised steel product according to the present invention.

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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)
  • Heat Treatment Of Sheet Steel (AREA)
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Claims (14)

  1. Stahlzusammensetzung, die enthält:
    einen C-Gehalt, zwischen 0,06% und 0,15%,
    einen Si-Gehalt, zwischen 0,1% und 0,4%,
    einen Mn-Gehalt, kleiner als 1,5%,
    einen Cr-Gehalt, zwischen 0,2% und 0,5%,
    einen Mo-Gehalt, zwischen 0,1% und 0,25%, so dass die folgende Bedingung erfüllt ist: Cr + 2Mo 0,7%,
    wobei der Rest aus Fe und aus zufälligen Verunreinigungen besteht.
  2. Stahlzusammensetzung gemäss Anspruch 1, wobei der Mn-Gehalt zwischen 1,35% und 1,50% liegt.
  3. Stahlzusammensetzung gemäss Anspruch 1, wobei der Cr-Gehalt zwischen 0,2% und 0,4% liegt und der Mo-Gehalt zwischen 0,15% und 0,25% liegt, so dass Cr + 2Mo 0,7%.
  4. Stahlzusammensetzung gemäss Anspruch 1, wobei der Cr-Gehalt zwischen 0,2% und 0,3% liegt und der Mo-Gehalt zwischen 0,2% und 0,25% liegt, so dass Cr + 2Mo 0,7%.
  5. Stahlzusammensetzung gemäss Anspruch 1, wobei der Si-Gehalt zwischen 0,1% und 0,15% liegt.
  6. Verfahren für die Herstellung eines kaltgewalzten, metallbeschichteten Mehrphasenstahls, das folgende Schritte umfasst:
    die Herstellung einer Bramme aus Stahl mit einer Zusammensetzung, die enthält:
    einen C-Gehalt, zwischen 0,06% und 0,15%,
    einen Si-Gehalt, zwischen 0,1% und 0,4%,
    einen Mn-Gehalt, kleiner als 1,5%,
    einen Cr-Gehalt, zwischen 0,2% und 0,5%,
    einen Mo-Gehalt, zwischen 0,1% und 0,25%, so dass die folgende Bedingung erfüllt ist: Cr + 2Mo 0,7%,
    wobei der Rest aus Fe und aus zufälligen Verunreinigungen besteht,
    die Herstellung eines Stahlbleches durch Wiedererwärmen, Warmwalzen und Kaltwalzen der Bramme,
    das Halten des besagten kaltgewalzten Stahlbleches während einer längeren Zeit auf einer zwischen Ac1 und Ac3 liegenden Temperatur,
    das Durchführen einer primären Abkühlung herunter auf die Temperatur des geschmolzenen Metallbades, mit einer Abkühlungsgeschwindigkeit, die höher als 25°C pro Sekunde ist,
    das Durchführen der Schmelztauchbeschichtung des besagten Stahlbleches mit Metall,
    das Durchführen einer sekundären Abkühlung des besagten Bleches herunter auf eine Temperatur, die kleiner als Ms ist, mit einer Abkühlungsgeschwindigkeit, die höher als 4°C pro Sekunde ist,
    das Durchführen eines Dressiergrades, der zwischen 0% und 0,4% liegt.
  7. Verfahren gemäss Anspruch 6, wobei die Abkühlungsgeschwindigkeit während des primären Abkühlungsschrittes höher als 40°C pro Sekunde ist.
  8. Verfahren gemäss Anspruch 6, bei welchem das Stahlblech verzinkt wird, wobei die Temperatur am Eingang des geschmolzenen Zinkbades zwischen 440°C und 475°C liegt.
  9. Verfahren gemäss Anspruch 6, bei welchem das Stahlblech aluminiert wird, wobei die Temperatur am Eingang des geschmolzenen Aluminiumbades zwischen 650°C und 720°C liegt.
  10. Verfahren gemäss Anspruch 6, wobei die Warmhaltetemperatur zwischen 780°C und 850°C liegt.
  11. Verfahren gemäss Anspruch 6, bei welchem das Stahlblech verzinkt wird, wobei der Dressiergrad 0,2% beträgt.
  12. Kaltgewalztes, metallbeschichtetes Mehrphasenprodukt mit einer Stahlzusammensetzung gemäss Anspruch 1, wobei das besagte Produkt durch eine Zugfestigkeit von mindestens 500 MPa und ein Streckgrenzenverhältnis von weniger als 0,65 im dressierten Zustand gekennzeichnet ist.
  13. Kaltgewalztes, metallbeschichtetes Mehrphasenprodukt mit einer Stahlzusammensetzung gemäss Anspruch 1, wobei der besagte Stahl durch eine Zugfestigkeit von mindestens 500 MPa und ein Streckgrenzenverhältnis von weniger als 0,6 im nicht dressierten Zustand gekennzeichnet ist.
  14. Aluminiertes Stahlprodukt gemäss Anspruch 12 oder 13 mit einer Korrosionsfestigkeit bis zu einer Temperatur von 900°C.
EP99870267A 1999-12-10 1999-12-17 Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte Expired - Lifetime EP1113085B1 (de)

Priority Applications (5)

Application Number Priority Date Filing Date Title
AT99870267T ATE241022T1 (de) 1999-12-17 1999-12-17 Verfahren zum herstellen von kaltgewalzten metallbeschichteten stahlprodukte mit niedrigem streckgrenze-zugfestigkeit, und dabei erhaltene produkte
DE69908151T DE69908151T2 (de) 1999-12-17 1999-12-17 Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte
EP99870267A EP1113085B1 (de) 1999-12-17 1999-12-17 Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte
ES99870267T ES2200492T3 (es) 1999-12-17 1999-12-17 Procedimiento para producir productos de acero laminados en frio recubiertos de metal, y producto asi obtenido que presenta un bajo limite de alargamiento.
US09/733,424 US6641931B2 (en) 1999-12-10 2000-12-08 Method of production of cold-rolled metal coated steel products, and the products obtained, having a low yield ratio

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP99870267A EP1113085B1 (de) 1999-12-17 1999-12-17 Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte

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EP1113085A1 EP1113085A1 (de) 2001-07-04
EP1113085B1 true EP1113085B1 (de) 2003-05-21

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AT (1) ATE241022T1 (de)
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Publication number Priority date Publication date Assignee Title
DE102012006017A1 (de) 2012-03-20 2013-09-26 Salzgitter Flachstahl Gmbh Hochfester Mehrphasenstahl und Verfahren zur Herstellung eines Bandes aus diesem Stahl

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* Cited by examiner, † Cited by third party
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GB1287178A (en) * 1969-10-13 1972-08-31 Nippon Kokan Kk Process of manufacturing heat resisting steel sheet for deep drawing
JPS579831A (en) * 1980-05-21 1982-01-19 British Steel Corp Steel production
JP2616350B2 (ja) * 1992-08-07 1997-06-04 住友金属工業株式会社 超高張力冷延鋼板およびその製造方法

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ATE241022T1 (de) 2003-06-15
ES2200492T3 (es) 2004-03-01
EP1113085A1 (de) 2001-07-04
DE69908151D1 (de) 2003-06-26
DE69908151T2 (de) 2004-03-11

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