EP2836614B1 - Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier - Google Patents

Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier Download PDF

Info

Publication number
EP2836614B1
EP2836614B1 EP13717417.3A EP13717417A EP2836614B1 EP 2836614 B1 EP2836614 B1 EP 2836614B1 EP 13717417 A EP13717417 A EP 13717417A EP 2836614 B1 EP2836614 B1 EP 2836614B1
Authority
EP
European Patent Office
Prior art keywords
steel
strip
temperature
cooling
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP13717417.3A
Other languages
German (de)
English (en)
Other versions
EP2836614A1 (fr
Inventor
Thomas Schulz
Andreas WEDEMEIER
Michael Pohl
Hans-Joachim KRATZ
Matthias Geler
Oliver Meyer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzgitter Flachstahl GmbH
Original Assignee
Salzgitter Flachstahl GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Publication of EP2836614A1 publication Critical patent/EP2836614A1/fr
Application granted granted Critical
Publication of EP2836614B1 publication Critical patent/EP2836614B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C21D8/0284—Application of a separating or insulating coating
    • 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
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • 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
    • 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
    • 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

Definitions

  • the invention relates to a high-strength multiphase steel according to the preamble of claim 1.
  • the invention relates to a method for producing a hot or cold rolled strip of such a steel according to claim 6.
  • the invention relates to steels with tensile strengths in the range of 580-900 MPa with low yield ratio of less than 67% for the production of components which have excellent formability and welding properties.
  • the hotly contested automotive market is forcing manufacturers to constantly seek solutions to reduce fleet consumption while maintaining maximum comfort and occupant safety.
  • the weight saving of all vehicle components plays a decisive role, on the other hand, but also a most favorable behavior of the individual components with high static and dynamic stress during operation as well as in the event of a crash.
  • the suppliers of raw material suppliers are trying to meet this need by reducing the weight of the vehicles by providing high-strength and ultra-high-strength steels and reducing the sheet thickness, while at the same time improving forming and component behavior during production and operation.
  • High-strength and higher-strength steels enable lighter vehicle components (eg cars, trucks), which consequently results in lower fuel consumption.
  • the reduced CO 2 content reduces the environmental impact.
  • These steels must therefore meet relatively high requirements in terms of their strength and ductility, energy absorption and in their processing, such as punching, hot and cold forming, welding and / or surface finishing (e.g., metallized, organically coated, painted).
  • Newly developed steels must therefore meet the requirements for the required weight reduction, the increasing material requirements for yield strength, Tensile strength and elongation at break with good formability, as well as the component requirements for high toughness, edge crack resistance, energy absorption and strength on the work-hardening effect and the bake-hardening effect, but also improved joining suitability in the form of eg improved weldability.
  • Improved edge tear resistance means increased hole widening and is known by synonyms such as High Hole Expansion (HHE) and Low Edge Crack (LEC).
  • HHE High Hole Expansion
  • LEC Low Edge Crack
  • LCE Low Carbon Equivalent
  • UP Under Peritectical
  • dual-phase steels consist of a ferritic basic structure in which a martensitic second phase and possibly a further phase with bainite and retained austenite are incorporated.
  • the bainite can be present in different forms.
  • the steel grades determining processing characteristics of dual-phase steels such as a very low yield ratio and at the same time very high tensile strength, a strong work hardening and a good cold workability, are well known.
  • Multiphase steels such as complex-phase steels, ferritic-bainitic steels, bainitic steels and martensitic steels, which are characterized by different microstructural compositions as described in EN 10346, are also used with increasing tendency.
  • Complex-phase steels are steels which contain small amounts of martensite, retained austenite and / or pearlite in a ferritic / bainitic matrix, whereby extreme grain refinement is brought about by delayed recrystallization or by precipitation of micro-alloying elements.
  • Ferritic-bainitic steels are steels that contain bainite or solidified bainite in a matrix of ferrite and / or solidified ferrite.
  • the solidification of the matrix is effected by a high dislocation density, by grain refining and the excretion of micro-alloying elements.
  • Bainitic steels are steels that are characterized by a very high yield strength and tensile strength at a sufficiently high elongation for cold forming processes. Due to the chemical composition a good weldability is given.
  • the microstructure typically consists of bainite. Occasionally, small amounts of other phases, such as. As martensite and ferrite.
  • Martensitic steels are steels that contain small amounts of ferrite and / or bainite in a matrix of martensite due to thermomechanical rolling.
  • the steel grade is characterized by a very high yield strength and tensile strength at a sufficiently high elongation for cold forming processes. Within the group of multiphase steels, the martensitic steels have the highest tensile strength values.
  • T Ailor R olled B lank lightweight technology allows a significant weight reduction by the load customized choice of thickness greater than the length of the component.
  • TRB®s with multiphase structure are not without limitations, however, with currently known alloys and available continuous annealing equipment for widely varying tape thicknesses. for the heat treatment before cold rolling, possible. In areas of different tape thickness, i. in the presence of different Kaltabwalzgrade, due to a temperature gradient occurring in the common process windows no homogeneous multi-phase microstructure can be set in cold- as well as hot-rolled steel strips.
  • the hot strip in typical thicknesses between 1.50 mm to 4.00 mm or cold strip, in typical thicknesses of 0.50 mm to 3.00 mm, heated in a continuous annealing furnace to a temperature such that during cooling the required microstructure established.
  • a continuous annealing furnace heated in a continuous annealing furnace to a temperature such that during cooling the required microstructure established.
  • a special heat treatment takes place, where e.g.
  • comparatively soft components such as ferrite or bainitic ferrite
  • the steel its low yield strength and its hard constituents, such as martensite or carbon-rich bainite its strength.
  • the annealing treatment is usually carried out in a continuous annealing furnace upstream of the galvanizing bath.
  • the required microstructure of the hot strip may also be adjusted in the continuous furnace during the annealing treatment, in order to achieve the required mechanical properties.
  • a homogeneous temperature distribution is difficult to achieve, especially at different thicknesses in the transition region from one belt to another. This can result in alloy compositions with too small process windows in the continuous annealing, e.g. the thinner belt is either driven too slowly through the furnace and thereby the productivity is lowered, or that the thicker belt is driven too fast through the furnace and the necessary annealing temperatures and cooling gradients to achieve the desired structure is not achieved. The consequences are increased rejects with corresponding costs of misconduct.
  • the decisive process parameter is thus the setting of the speed in the continuous annealing, since the phase transformation takes place depending on temperature and time.
  • a method for producing a steel strip with different thickness over the strip length is z. B. in the DE 100 37 867 A1 described.
  • the goal of achieving the resulting mechanical and technological properties in a narrow range over bandwidth and strip length by the controlled adjustment of the volume fractions of the structural phases has top priority and is therefore only possible through an enlarged process window.
  • the known alloy concepts for multiphase steels are characterized by too narrow a process window and therefore unsuitable for solving the present problem, in particular in flexibly rolled strips.
  • At present, only steels of a strength class with defined cross-sectional areas (strip thickness and strip width) can be represented with the known alloy concepts, so that altered alloy concepts are necessary for different strength classes and / or cross-sectional areas.
  • the state of the art is that an increase in strength is achieved by the increase in the quantity of carbon and / or silicon and / or manganese and an increase in the strength via the microstructural adjustments and the solid solution hardening (mixed crystal hardening) with adapted temperature control.
  • the hole expansion test according to ISO 11630 is used as one of several possible test methods.
  • a low yield ratio (Re / Rm) is typical for a dual-phase steel and is used primarily for formability in drawing and deep drawing operations. This gives the designer information about the distance between onset of plastic deformation and failure of the material under quasistatic stress. Ask accordingly lower yield ratio ratios provide a greater safety margin for component failure.
  • a higher yield ratio (Re / Rm), which is typical for complex phase steels, is also distinguished by resistance to edge cracks. This can be attributed to the smaller differences in the strengths of the individual structural components, which has a favorable effect on a homogeneous deformation in the area of the cutting edge.
  • the analytical landscape for achieving multi-phase steels with minimum tensile strengths of 580 MPa has become very diverse and shows very large alloy areas in the strength-increasing elements carbon, silicon, manganese, phosphorus, aluminum and chromium and / or molybdenum, as well as in the addition of microalloys such Titanium and vanadium, as well as in the material-characterizing properties.
  • the range of dimensions is broad and lies in the thickness range of about 0.50 to 4.00 mm. It can be found mainly bands up to about 1850mm application, but also slit strip dimensions caused by longitudinal parts of the bands. Sheets or sheets are made by cutting the strips.
  • the invention is therefore based on the object, a new alloy concept for a high-strength multiphase steel with a minimum tensile strength of 580 MPa longitudinal and transverse to the rolling direction, preferably with dual-phase structure and a yield ratio of less than 67%, with the process window for the continuous annealing of hot or Cold bands can be extended so that in addition to bands with different cross sections and steel bands with over tape length and possibly bandwidth varying thickness, and thus the correspondingly varying degrees of cold rolling, can be produced with the most homogeneous mechanical and technological properties.
  • a method for producing a strip made from this steel is to be specified.
  • this object is achieved by a steel with the following contents in% by weight: C 0.075 to ⁇ 0.105 Si 0.200 to ⁇ 0.300 Mn 1,000 to ⁇ 2,000 Cr 0.280 to ⁇ 0.480 al 0.010 to ⁇ 0.060 P ⁇ 0.020 Nb ⁇ 0.005 to ⁇ 0.025 N ⁇ 0.0100 S ⁇ 0.0050
  • the steel according to the invention offers the advantage of a significantly enlarged process window in comparison to the known steels. This results in an increased process reliability in the continuous annealing of cold and hot strip with dual-phase structure. Thus, homogenized mechanical-technological properties in the strip can be ensured for pass-annealed hot or cold strips even with different cross sections and otherwise identical process parameters.
  • stress-optimized components can be produced by forming technology.
  • the material produced can be produced both as a cold strip and as a hot strip via a hot-dip galvanizing line or a pure continuous annealing plant in the dressed and undressed and also in the heat-treated state (intermediate annealing).
  • the steel strips produced with the alloy composition according to the invention are characterized in the production of a dual-phase steel by a much wider compared to the standard process window in terms of temperature and flow rate in the intercritical annealing between A c1 and A c3 or in a Austenitizing annealing over A c3 with final controlled cooling or annealing below the beginning of the two-phase region (eg A c1 - about 20 ° C) in comparison to the known alloy concepts of (see FIG. 9a . 9b . 9c ).
  • Annealing temperatures of about 700 to 950 ° C have proved to be advantageous. Depending on the overall process, there are different approaches to realize the heat treatment.
  • the strip is cooled starting from the annealing temperature at a cooling rate of 15 to 100 ° C / s to an intermediate temperature of 200 to 250 ° C.
  • the cooling to room temperature is finally carried out at a cooling rate of 2 to 30 ° C / s.
  • the cooling as described above is stopped before entering the molten bath and continued until after leaving the bath until reaching the intermediate temperature of 200 to 250 ° C. Depending on the molten bath temperature results in a holding temperature of about 420 to 470 ° C.
  • the cooling to room temperature is again at a cooling rate of 2 to 30 ° C / s.
  • the second variant of the temperature control in the hot dip finishing involves holding the temperature for about 1 to 20 seconds at the intermediate temperature of 200 to 250 ° C and then reheating to the temperature required for hot dipping refinement of about 420 to 470 ° C.
  • the strip is cooled after refining again to 200 to 250 ° C.
  • the cooling to room temperature is again at a cooling rate of 2 to 30 ° C / s.
  • the basis for achieving a broad process window is the microalloying according to the invention exclusively with niobium, taking into account the above-mentioned. classical composition carbon / silicon / manganese / chromium, with a graded and defined manganese content to be displayed according to the strip thickness.
  • niobium retards the recrystallization in the annealing treatment, thereby stabilizing the austinite grain size and achieving a broader process window in the final annealing treatment.
  • Material characteristic is also that the addition of manganese with increasing weight percent of the ferrite is shifted to longer times and lower temperatures during cooling.
  • the proportions of ferrite are more or less reduced by increased amounts of bainite.
  • niobium enables the previously described process robustness.
  • the manganese variation compensates for the cross-sectional influence in the time-temperature conversion behavior.
  • the carbon equivalent can be reduced, thereby improving weldability and avoiding too much hardening during welding. In resistance spot welding, moreover, the electrode life can be significantly increased.
  • the effect of the elements in the alloy according to the invention is described in more detail below.
  • the multiphase steels are typically chemically designed to combine alloying elements with and without micro-alloying elements.
  • Accompanying elements are unavoidable and are considered in the analysis concept with regard to their effect if necessary.
  • Hydrogen (H) is the only element that can generate diffraction through the iron grid without creating lattice strains. As a result, the hydrogen in the iron grid is relatively mobile and can be absorbed relatively easily during production. Hydrogen can only be taken up in atomic (ionic) form in the iron lattice.
  • Hydrogen has a strong embrittlement and preferably diffuses to energy-favorable sites (defects, grain boundaries, etc.). In this case, defects act as hydrogen traps and can significantly increase the residence time of the hydrogen in the material.
  • a more uniform structure which in the steel according to the invention u.a. achieved by its microalloying reduces the susceptibility to hydrogen embrittlement.
  • the hydrogen content in the steel should be as low as possible.
  • Oxygen (O) In the molten state, the steel has a relatively high absorption capacity for gases, but at room temperature, oxygen is only soluble in very small quantities. Similar to hydrogen, oxygen can only diffuse into the material in atomic form. Due to the strong embrittling effect and the negative effects on the aging resistance, as much as possible is attempted during production to reduce the oxygen content.
  • the oxygen content in the steel should be as low as possible.
  • Nitrogen (N) is also a companion element of steelmaking. Steels with free nitrogen tend to have a strong aging effect. The nitrogen diffuses at low temperatures at dislocations and blocks them. It causes an increase in strength combined with a rapid loss of toughness. Nitrogen bonding in the form of nitrides is possible by alloying aluminum or titanium.
  • the nitrogen content is limited to ⁇ 0.0100%, advantageously ⁇ 0.0090% or optimally ⁇ 0.0080% or amounts unavoidable in steel production.
  • S Sulfur
  • MnS manganese sulfide
  • the manganese sulfides are often rolled in rows during the rolling process and act as nucleation sites for the transformation. This leads to a line-shaped structure, especially in the case of diffusion-controlled conversion, and can lead to impaired mechanical properties in the case of pronounced bristleness (for example, pronounced Martensitile instead of distributed martensite islands, anisotropic material behavior, reduced elongation at break).
  • the sulfur content is limited to ⁇ 0.0050% or unavoidable amounts in steelmaking.
  • Phosphorus (P) is a trace element from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphorus increases hardness by solid solution strengthening and improves hardenability.
  • the phosphorus content is limited to ⁇ 0.020% or to unavoidable amounts in steelmaking.
  • Alloying elements are usually added to the steel in order to specifically influence certain properties.
  • an alloying element in different steels affect different characteristics. The effect generally depends strongly on the amount and the solution state in the material.
  • Carbon (C) considered the most important alloying element in steel. Through its targeted introduction of up to 2.06% iron is only steel. Often the carbon content is drastically lowered during steelmaking. In the case of dual-phase steels for continuous hot-dip refinement, its maximum proportion is 0.23%; a minimum value is not specified.
  • Carbon is also required to form carbides.
  • a representative occurring almost in every steel is the cementite (Fe 3 C).
  • significantly harder special carbides with other metals such as chromium, titanium, niobium, vanadium can form.
  • the minimum C content is set to 0.075% and the maximum C content to 0.105%.
  • silicon increases the strength and yield ratio of the ferrite with only a slight decrease Elongation at break.
  • Another important effect is that silicon shifts the formation of ferrite to shorter times, thus allowing the formation of sufficient ferrite before quenching.
  • the austenite is carbon enriched and stabilized.
  • silicon stabilizes austenite markedly in the lower temperature range, especially in the area of bainite formation by preventing carbide formation.
  • highly adherent scale may form at high silicon contents, which may affect further processing.
  • silicon may diffuse to the surface during annealing and form film-like oxides alone or together with manganese. These oxides deteriorate the galvanizability by adversely affecting the galvanizing reaction (iron solution and inhibiting layer formation) when the steel strip is immersed in the molten zinc. This manifests itself in a poor zinc adhesion and unpigmented areas.
  • a suitable kiln operation with adjusted moisture content in the annealing gas and / or by a low Si / Mn ratio and / or by the use of moderate amounts of silicon, however, a good galvanizability of the steel strip and a good zinc adhesion can be ensured.
  • the minimum Si content is set at 0.200% and the maximum silicon content at 0.300%.
  • Manganese (Mn) is added to almost all steels for desulfurization to convert the harmful sulfur into manganese sulfide. In addition, manganese increases the strength of the ferrite by solid solution strengthening and shifts the ⁇ / ⁇ conversion to lower temperatures.
  • manganese tends to form oxides on the steel surface during annealing. Depending on the annealing parameters and the contents of other alloying elements (in particular silicon and aluminum), manganese oxides (eg MnO) and / or Mn mixed oxides (eg Mn 2 SiO 4 ) may occur. However, manganese is at one low Si / Mn or Al / Mn ratio to be considered as less critical, since forming more globular oxides instead of oxide films. However, high levels of manganese can negatively affect the appearance of the zinc layer and zinc adhesion.
  • the manganese content is therefore set to 1,000 to 2,000% depending on the cross section (tape thickness at the same bandwidth).
  • a manganese content 1.00-1.50 wt.%
  • a manganese content of 1.50-2.00 wt.% Exposed.
  • Chromium (Cr) On the one hand chromium in dissolved form can considerably increase the hardenability of steel even in small amounts. On the other hand, chromium causes particle hardening with appropriate temperature control in the form of chromium carbides. The associated increase in the number of seed sites with simultaneously reduced content of carbon leads to a reduction in the hardenability.
  • chromium In dual phase steels, the addition of chromium mainly improves the hardenability. Chromium, when dissolved, shifts perlite and bainite transformation to longer times, while decreasing the martensite start temperature.
  • Chromium is also a carbide former. If chromium is in carbide form, the austenitizing temperature must be high enough before curing to dissolve the chromium carbides. Otherwise, the increased germ count may lead to a deterioration of the hardenability.
  • Chromium also tends to form oxides on the steel surface during the annealing process, which may degrade zinc-plating quality.
  • the chromium content is therefore set to values of 0.280 to 0.480%.
  • Molybdenum (Mo) The addition of molybdenum is similar to chromium to improve hardenability. The perlite and bainite transformation is pushed to longer times and the martensite start temperature is lowered.
  • molybdenum considerably increases the tempering resistance, so that no loss of strength is to be expected in the zinc bath and, as a result of solid solution hardening, increases the strength of the ferrite.
  • the content of molybdenum is limited to the unavoidable, steel-accompanying amounts.
  • Copper (Cu): The addition of copper can increase the tensile strength and hardenability. In combination with nickel, chromium and phosphorus, copper can form a protective oxide layer on the surface, which can significantly reduce the corrosion rate.
  • copper When combined with oxygen, copper can form harmful oxides at the grain boundaries, which can be detrimental to hot working processes in particular.
  • the content of copper is therefore limited to quantities that are unavoidable in steel production.
  • alloying elements such as nickel (Ni) or tin (Sn) are limited in their contents to unavoidable amounts in steelmaking.
  • Microalloying elements are usually added only in very small amounts ( ⁇ 0.1%). They act in contrast to the alloying elements mainly by excretion formation but can also affect the properties in a dissolved state. Despite the small quantity additions, micro-alloying elements strongly influence the production conditions as well as the processing and final properties.
  • micro-alloying elements carbide and nitride formers which are generally soluble in the iron lattice are used. Formation of carbonitrides is also possible because of the complete solubility of nitrides and carbides in one another. The tendency to form oxides and sulfides is usually most pronounced in the case of the micro-alloying elements, but as a rule it is purposefully prevented on account of other alloying elements.
  • This property can be used positively by binding the generally harmful elements sulfur and oxygen.
  • the setting may also have negative effects, if there are not enough micro-alloying elements for the formation of carbides available.
  • Typical micro-alloying elements are aluminum, vanadium, titanium, niobium and boron. These elements can be dissolved in the iron lattice and form carbides and nitrides with carbon and nitrogen.
  • Aluminum (Al) is usually added to the steel to bind the dissolved oxygen in the iron and nitrogen.
  • the oxygen and nitrogen is thus converted into aluminum oxides and aluminum nitrides. These precipitations can cause a grain refining by increasing the germination sites and thus increase the toughness properties and strength values.
  • Titanium nitrides have a lower formation enthalpy and are formed at higher temperatures.
  • aluminum such as silicon shifts ferrite formation to shorter times, allowing the formation of sufficient ferrite in dual phase steel. It also suppresses carbide formation and thus leads to a delayed transformation of austenite. For this reason, aluminum is also used as an alloying element in retained austenitic steels to substitute part of the silicon with aluminum. The reason for this approach is that aluminum is somewhat less critical to the galvanizing reaction than silicon.
  • the aluminum content is therefore limited to 0.010 to a maximum of 0.060%.
  • Niobium (Nb) In addition to the above-described effect of widening the process window by delayed phase transformation in continuous annealing, niobium causes a high grain refining because it most effectively retards recrystallization of all the micro-alloying elements and also inhibits austenite grain growth.
  • the strength-enhancing effect is qualitatively higher than that of titanium, as evidenced by the increased grain refining effect and the greater amount of strength-enhancing particles (bonding of the titanium to TiN at high temperatures).
  • Niobium carbides form at temperatures below 1200 ° C. In the case of nitrogen bonding with titanium, niobium can be effective in forming small and effective ones Carbides in the lower temperature range (smaller carbide sizes) increase its strength-increasing effect.
  • niobium Another effect of niobium is the retardation of the ⁇ / ⁇ conversion and the lowering of the martensite start temperature in the dissolved state. On the one hand this happens through the solute drag effect and on the other hand through the grain refining. This causes an increase in strength of the structure and thus a higher resistance to the increase in volume during martensite formation.
  • the precipitation hardening can thus be effectively effective especially for steels with a low carbon content (greater supersaturation possible) and in hot forming processes (deformation-induced precipitation).
  • the niobium content is therefore limited to values between 0.005 and 0.025%, wherein the contents are advantageously limited to ⁇ 0.005 to ⁇ 0.020% for cost reasons.
  • vanadium content is limited to unavoidable steel accompanying amounts.
  • the annealing temperatures for the dual-phase structure to be achieved are between about 700 and 950 ° C. for the steel according to the invention, thus achieving a recrystallized (single-phase region), partially austenitic (two-phase) or fully austenitic microstructure (austenite region) depending on the temperature range.
  • the hot-dip coated material can be produced both as a hot strip and as a cold rolled hot strip or cold strip in the dressed (cold rolled) or undressed state and / or stretch bending or non-stretch bent state.
  • Steel strips in the present case as hot strip, cold rolled hot strip or cold strip made of the alloy composition according to the invention are also characterized in the further processing by a high resistance to near-edge cracking.
  • the hot strip according to the invention with Endwalztemperaturen in austenitic area above A c3 and reel temperatures above the bainite start temperature generated.
  • FIG. 1 shows schematically the process chain for the production of the steel according to the invention. Shown are the different process routes relating to the invention. Up to position 5 (pickle) the process route is the same for all steels according to the invention, after which deviating process routes take place depending on the desired results.
  • the pickled hot strip can be galvanized or cold rolled and galvanized. Or it can be annealed cold-rolled and galvanized.
  • FIG. 2 shows results of a hole expansion test (relative values in comparison). Shown are the results of the hole widening tests for a steel according to the invention (variant 1, see FIG. 3 ) compared to the standard grades, the standard grade is Process 1 as reference. All materials have a sheet thickness of 2.50mm. The results apply to the test according to ISO 16630. It can be seen that the steels according to the invention achieve better expansion values for punched holes than the standard grades with the same processing.
  • Process 1 here corresponds to annealing, for example, on a hot-dip galvanizing with a combined directly fired furnace and radiant tube furnace, as it is known in FIG. 9b is described.
  • the process 2 corresponds for example to a process control in a continuous annealing plant, as in FIG.
  • FIG. 3 shows the relevant alloying elements of the steel according to the invention over the standard grade, which exemplifies the state of the art.
  • the comparative steel which corresponds to the state of the art
  • the main difference lies in the carbon content, which lies in the super-architectural range, but also in the elements silicon, manganese and chromium.
  • the standard grade is phosphorus-microalloyed.
  • the steels of the invention are niobium-microalloyed and have a significantly increased manganese content.
  • FIG. 4a shows the mechanical characteristics transverse and longitudinal to the rolling direction of the steel according to the invention, for example in its variant 1, 2 and 3, in comparison with the standard grade, which represents the prior art by way of example. All characteristic values achieved by annealing in the two-phase area correspond to the normative specification of an HCT600X.
  • FIG. 4b Shows the mechanical characteristic values transverse to the rolling direction of the steel according to the invention, by way of example in its variants 1, 2 and 3, which was determined by a regression calculation. Shown are the mechanical characteristics depending on the band thickness related Mangangehaltvariationen (invention variants 1,2 and 3). All characteristic values correspond to the normative specification. The yield ratio is significantly below 67% for all variants.
  • Figure 4c shows the mechanical characteristics transverse to the rolling direction and the chemical composition of the steel according to the invention, in its variant 1, with a material thickness of 0.77 mm and an annealing below the beginning of the two-phase region (eg A c1 - about 20 ° C) in comparison with the Standard quality, which exemplifies the state of the art. All characteristic values correspond to the normative specification of a HCT780X, ie the next higher strength class with reference to the HCT600X.
  • FIG. 4d shows the mechanical characteristics transverse to the rolling direction and the chemical composition of the steel according to the invention (variant 1) with a material thickness of 2.50 mm and an annealing above A c3 . All characteristics correspond to the normative specification of a HDT580X.
  • FIG. 5 shows schematically the time-temperature curve of the process steps hot rolling and continuous annealing of strips of the alloy composition according to the invention. Shown is the time- and temperature-dependent conversion for the hot rolling process as well as for a heat treatment after cold rolling, by way of example for variant 1.
  • FIG. 6 Shows a schematic CCT diagram for the inventive steel, differentiated according to the variation 1, 2 and 3.
  • the calculated CCT diagram with the corresponding chemical composition (varying only by levels of manganese) and the A c1 and A c3 temperature shown By setting appropriate temperature-time profiles during cooling, it is advantageously possible to set a broad spectrum of microstructural compositions in the steel material.
  • Of particular interest here is the shift of ferrite nose, perlitnase and bainitic nose at later times in the staggered increase in manganese contents.
  • the potential is made possible to set similar microstructural proportions over the entire thickness spectrum considered at a system speed that depends on the strip thickness.
  • FIG. 7 shows the mechanical characteristics along the rolling direction with the same parameters of continuously annealed strips with varying degrees of rolling or different strip thickness in an exemplary consideration of variant 1. Shown are the characteristics of tensile strength, yield strength and elongation at break depending on selected degrees of reduction. Only the tensile strength increases with increasing Abwalzgrad. All values up to 30% reduction rate are in the range of the standard for a HCT600X. Higher degrees of finishing (greater than 75%) lead to a change in the steel grades towards HCT780X, with minimum strengths of 780 MPa.
  • FIG. 8 shows an overview of the strength classes that can be set using the alloy concept according to the invention (variant 1).
  • the alloy composition used corresponds to that in the FIG. 3 shown. Shown are the differently processed steel strips with their characteristics along the rolling direction and microstructural compositions. This clearly indicates the range of adjustable strength classes for hot and cold strip with the resulting microstructure constituents depending on the process steps carried out and the process parameters set.
  • the Figures 9 show schematically the temperature-time courses in the annealing and cooling with three different variants and each different austenitization conditions according to the claims for registered method.
  • the method 1 shows the annealing and cooling of the produced cold or hot rolled steel strip in a continuous annealing system.
  • a temperature in the range of 700 to 950 ° C we heated the strip to a temperature in the range of 700 to 950 ° C.
  • the annealed steel strip is then cooled from the annealing temperature at a cooling rate between 15 and 100 ° C / s to an intermediate temperature of approximately 200 to 250 ° C.
  • a second intermediate temperature about 300 to 500 ° C
  • the steel strip is cooled at a cooling rate between 2 and 30 ° C / s until it reaches room temperature in air or the cooling at a cooling rate between 15 and 100 ° C / s is maintained up to room temperature.
  • the method 2 ( FIG. 9b ) shows the process according to method 1, but the cooling of the steel strip for the purpose of a hot dipping refinement is briefly interrupted when passing through the hot dipping vessel, then the cooling at a cooling rate between 15 and 100 ° C / s up to an intermediate temperature of 200 to 250 ° C. continue. Subsequently, the steel strip is cooled at a cooling rate between 2 and 30 ° C / s until it reaches room temperature in air.
  • the method 3 ( FIG. 9c ) also shows the process according to method 1 in a hot dipping refinement, but the cooling of the steel strip is interrupted by a short break ( about 1 to 20 s) at an intermediate temperature in the range of 200 to 250 ° C and up to the temperature which refines to hot dipping necessary ( about 420 to 470 ° C) reheated. Subsequently, the steel strip is again cooled to an intermediate temperature of 200 to 250 ° C. At a cooling rate of 2 and 30 ° C / s, the final cooling of the steel strip takes place until air reaches the room temperature.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (13)

  1. Acier polyphasé à haute résistance ayant une résistance minimale à la traction de 580 MPa pour une bande d'acier inoxydable laminé à froid ou à chaud et avec des propriétés de formage améliorées, notamment pour la construction facilitée de véhicules, constitué des éléments (teneur en % en masse) : C 0,075 à ≤ 0,105 Si 0,200 à ≤ 0,300 Mn 1,000 à ≤ 2,000 Cr 0,280 à ≤ 0,480 Al 0,010 à ≤ 0,060 P ≤ 0,020 Nb ≥ 0,005 à ≤ 0,025 N ≤ 0,0100 S ≤ 0,0050
    Reste de fer, y compris des impuretés résultant de la fusion, à condition que la teneur en Mn est ≥ 1,000 ≤ 1,500 %
    pour des épaisseurs de bande de 0,50-1,00 mm,
    que la teneur en Mn est ≥ 1,250 ≤ 1,750 %
    pour des épaisseurs de bande de 1,00-2,00 mm, et
    que la teneur en Mn est ≥ 1,500 ≤ 2,000 %
    pour des épaisseurs de bande de 2,00-4,00 mm.
  2. Acier selon la revendication 1,
    caractérisé en ce que
    pour atteindre une résistance minimale à la traction de 780 MPa, la teneur en Mn est ≥ 1,500 ≤ 2,000 % pour des épaisseurs de bande de 0,50-1,00 mm.
  3. Acier selon les revendications 1-2,
    caractérisé en ce que
    la teneur en Nb est ≤ 0,020 %.
  4. Acier selon l'une quelconque des revendications 1-3,
    caractérisé en ce que
    la teneur en N est ≤ 0,0090 %.
  5. Acier selon l'une quelconque des revendications 1-3,
    caractérisé en ce que
    la teneur en N est ≤ 0,0080 %.
  6. Procédé de production d'une bande d'acier laminé à froid ou à chaud à partir d'un acier produit selon l'une des revendications 1 à 5, dans lequel l'acier polyphasé requis est produit au cours d'un recuit continu, caractérisé en ce que la bande d'acier laminé à froid ou à chaud est chauffée dans le four de recuit continu à une température comprise entre 700 et 950 °C, et en ce que la bande d'acier recuite est alors refroidie à partir de la température de recuit avec une vitesse de refroidissement comprise entre 15 et 100 °C/s jusqu'à une première température intermédiaire de 300 à 500 °C, avant un refroidissement à une vitesse de refroidissement comprise entre 15 et 100 °C/s jusqu'à une seconde température intermédiaire de 200 à 250 °C, puis la bande d'acier est refroidie à l'air à une vitesse de refroidissement de 2 à 30 °C/s, jusqu'à atteindre la température ambiante, ou le refroidissement est maintenu à une vitesse de refroidissement comprise entre 15 et 100 °C/s entre la première température intermédiaire et la température ambiante.
  7. Procédé selon la revendication 6,
    caractérisé en ce que
    par l'intermédiaire d'une galvanisation au trempé après chauffage et refroidissement ultérieur, le refroidissement s'arrête avant l'entrée dans le bain de fusion, et après la galvanisation au trempé, le refroidissement survient à une vitesse de refroidissement comprise entre 15 et 100 °C/s jusqu'à une température intermédiaire de 200 à 250 °C, puis la bande d'acier est refroidie à l'air à une vitesse de refroidissement de 2 à 30 °C/s jusqu'à la température ambiante.
  8. Procédé selon la revendication 6,
    caractérisé en ce que
    par l'intermédiaire d'une galvanisation au trempé après chauffage et refroidissement ultérieur, la température est maintenue pendant 1 à 20 s à la température intermédiaire de 200 à 250 °C avant l'entrée dans le bain de fusion, puis la bande d'acier est chauffée à nouveau à la température de 420 à 470 °C, puis après la galvanisation au trempé, un refroidissement survient à une vitesse de refroidissement comprise entre 15 et 100 °C/s jusqu'à une température intermédiaire de 200 à 250 °C, avant un refroidissement à l'air à une vitesse de refroidissement de 2 et 30 °C/s jusqu'à la température ambiante.
  9. Procédé selon l'une quelconque des revendications 6 à 8,
    caractérisé en ce que
    afin d'obtenir une résistance minimale à la traction de 780 MPa, une bande d'acier selon la revendication 2 est traitée thermiquement en dessous du point de transformation Ac1.
  10. Procédé selon l'une quelconque des revendications 6 à 8,
    caractérisé en ce que
    afin d'obtenir une résistance minimale à la traction de 780 MPa, une bande d'acier selon la revendication 2 est traitée thermiquement avec des niveaux de laminage à froid supérieurs à 75 % entre Ac1 et Ac3.
  11. Procédé selon l'une quelconque des revendications 6 à 8,
    caractérisé en ce que
    il est possible d'ajuster les états structuraux comparables et les caractéristiques mécaniques des bandes en adaptant la vitesse de traitement du système à différentes épaisseurs de bande au cours du traitement thermique.
  12. Procédé selon l'une quelconque des revendications 6 à 11,
    caractérisé en ce que
    la bande d'acier est dressée après le traitement thermique.
  13. Procédé selon au moins l'une quelconque des revendications 6 à 12,
    caractérisé en ce que
    la bande d'acier est dressée par traction après le traitement thermique.
EP13717417.3A 2012-03-20 2013-02-27 Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier Active EP2836614B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102012006017A DE102012006017A1 (de) 2012-03-20 2012-03-20 Hochfester Mehrphasenstahl und Verfahren zur Herstellung eines Bandes aus diesem Stahl
PCT/DE2013/000125 WO2013139319A1 (fr) 2012-03-20 2013-02-27 Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier

Publications (2)

Publication Number Publication Date
EP2836614A1 EP2836614A1 (fr) 2015-02-18
EP2836614B1 true EP2836614B1 (fr) 2019-09-11

Family

ID=48142581

Family Applications (1)

Application Number Title Priority Date Filing Date
EP13717417.3A Active EP2836614B1 (fr) 2012-03-20 2013-02-27 Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier

Country Status (6)

Country Link
US (1) US10519525B2 (fr)
EP (1) EP2836614B1 (fr)
KR (1) KR102048792B1 (fr)
DE (1) DE102012006017A1 (fr)
RU (1) RU2615957C2 (fr)
WO (1) WO2013139319A1 (fr)

Families Citing this family (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102014017273A1 (de) 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102014017275A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
DE102014017274A1 (de) 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Höchstfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
CN104551441A (zh) * 2014-11-27 2015-04-29 宝山钢铁股份有限公司 一种含v的超高强气体保护焊丝及其制造方法
DE102015116186A1 (de) * 2015-09-24 2017-03-30 Thyssenkrupp Ag Halbzeug und Verfahren zur Herstellung einer Fahrzeugkomponente, Verwendung eines Halbzeugs und Fahrzeugkomponente
DE102016100648B4 (de) * 2015-12-23 2018-04-12 Benteler Automobiltechnik Gmbh Wärmebehandlungsofen sowie Verfahren zur Wärmebehandlung einer vorbeschichteten Stahlblechplatine und Verfahren zur Herstellung eines Kraftfahrzeugbauteils
BR112018073110A2 (pt) * 2016-08-08 2019-03-06 Nippon Steel & Sumitomo Metal Corp chapa de aço
RU2691809C1 (ru) * 2018-05-25 2019-06-18 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Способ производства толстолистового высокопрочного износостойкого проката (варианты)
RU2690076C1 (ru) * 2018-12-18 2019-05-30 Публичное акционерное общество "Северсталь" Листовой прокат и способ его получения
DE102020203564A1 (de) 2020-03-19 2021-09-23 Sms Group Gmbh Verfahren zum Herstellen eines gewalzten Mehrphasenstahlbandes mit Sondereigenschaften
DE102020110319A1 (de) 2020-04-15 2021-10-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit einem Mehrphasengefüge und Stahlband hinzu
US20230151468A1 (en) 2020-04-22 2023-05-18 Thyssenkrupp Steel Europe Ag Hot-Rolled Flat Steel Product and Method for the Production Thereof
CN111695271B (zh) * 2020-06-29 2023-07-25 武汉钢铁有限公司 一种钢坯表面金属在塑性变形中的追踪方法
CN113862580A (zh) * 2021-09-08 2021-12-31 唐山不锈钢有限责任公司 一种590MPa级冷轧双相钢用热轧钢带及其生产方法

Family Cites Families (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3806376A (en) * 1969-12-30 1974-04-23 Nippon Steel Corp Method for producing low-carbon cold rolled steel sheet having excellent cold working properties and an apparatus for continuous treatment thereof
JPS54163719A (en) * 1978-06-16 1979-12-26 Nippon Steel Corp Production of high tensile strength * low yield ratio and high extensibility composite textured steel panel with excellent workability
JPH03277743A (ja) * 1990-03-27 1991-12-09 Kawasaki Steel Corp 超高張力冷延鋼板およびその製造法
DE19610675C1 (de) 1996-03-19 1997-02-13 Thyssen Stahl Ag Mehrphasenstahl und Verfahren zu seiner Herstellung
DE19936151A1 (de) * 1999-07-31 2001-02-08 Thyssenkrupp Stahl Ag Höherfestes Stahlband oder -blech und Verfahren zu seiner Herstellung
DE10037867A1 (de) 1999-08-06 2001-06-07 Muhr & Bender Kg Verfahren zum flexiblen Walzen eines Metallbandes
DE69908151T2 (de) * 1999-12-17 2004-03-11 Sidmar N.V. Verfahren zum Herstellen von kaltgewalzten metallbeschichteten Stahlprodukte mit niedrigem Streckgrenze-Zugfestigkeit, und dabei erhaltene Produkte
WO2001081640A1 (fr) * 2000-04-21 2001-11-01 Nippon Steel Corporation Plaque d'acier presentant une excellente aptitude a l'ebarbage et une resistance elevee a la fatigue, et son procede de production
EP1375683B1 (fr) * 2001-03-29 2012-02-08 Sumitomo Metal Industries, Ltd. Tube en acier a haute resistance pour coussin d'air et procede pour la production de ce tube
EP1288322A1 (fr) * 2001-08-29 2003-03-05 Sidmar N.V. Acier à tres haute résistance mécanique, procédé pour la production de cet acier et le produit obtenu
FR2830260B1 (fr) * 2001-10-03 2007-02-23 Kobe Steel Ltd Tole d'acier a double phase a excellente formabilite de bords par etirage et procede de fabrication de celle-ci
JP4156889B2 (ja) * 2001-10-03 2008-09-24 株式会社神戸製鋼所 伸びフランジ性に優れた複合組織鋼板およびその製造方法
RU2256707C1 (ru) * 2004-07-15 2005-07-20 Липецкий государственный технический университет Способ производства стали с однородными свойствами
DE102004053620A1 (de) 2004-11-03 2006-05-04 Salzgitter Flachstahl Gmbh Hochfester, lufthärtender Stahl mit ausgezeichneten Umformeigenschaften
MXPA05008339A (es) * 2005-08-04 2007-02-05 Tenaris Connections Ag Acero de alta resistencia para tubos de acero soldables y sin costura.
DE102006054300A1 (de) * 2006-11-14 2008-05-15 Salzgitter Flachstahl Gmbh Höherfester Dualphasenstahl mit ausgezeichneten Umformeigenschaften
ES2387040T3 (es) * 2007-08-15 2012-09-12 Thyssenkrupp Steel Europe Ag Acero de doble fase, producto plano de un acero de doble fase de este tipo y procedimiento para la fabricación de un producto plano
CA2718304C (fr) * 2008-03-27 2012-03-06 Nippon Steel Corporation Tole d'acier galvanisee a haute resistance, tole galvanisee a chaud alliee a haute resistance et tole d'acier laminee a froid a haute resistance qui excellent en termes d'aptitude au moulage et au soudage, et procede de fabrication de toutes ces toles
CN101621006B (zh) * 2008-07-03 2011-01-12 中芯国际集成电路制造(上海)有限公司 利用锗预非晶处理来形成p-型轻度掺杂的漏极区的方法
US8128762B2 (en) * 2008-08-12 2012-03-06 Kobe Steel, Ltd. High-strength steel sheet superior in formability
JP4853575B2 (ja) 2009-02-06 2012-01-11 Ｊｆｅスチール株式会社 耐座屈性能及び溶接熱影響部靭性に優れた低温用高強度鋼管およびその製造方法
JP4924730B2 (ja) * 2009-04-28 2012-04-25 Ｊｆｅスチール株式会社 加工性、溶接性および疲労特性に優れる高強度溶融亜鉛めっき鋼板およびその製造方法
JP5740847B2 (ja) * 2009-06-26 2015-07-01 Ｊｆｅスチール株式会社 高強度溶融亜鉛めっき鋼板およびその製造方法
US20110000864A1 (en) * 2009-07-06 2011-01-06 Moore Lela K Cookware Holder and Method
US9822422B2 (en) * 2009-09-24 2017-11-21 Ati Properties Llc Processes for reducing flatness deviations in alloy articles
DE102011117572A1 (de) 2011-01-26 2012-08-16 Salzgitter Flachstahl Gmbh Höherfester Mehrphasenstahl mit ausgezeichneten Umformeigenschaften

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
EP2836614A1 (fr) 2015-02-18
RU2615957C2 (ru) 2017-04-11
US10519525B2 (en) 2019-12-31
WO2013139319A1 (fr) 2013-09-26
KR102048792B1 (ko) 2019-11-26
KR20140138990A (ko) 2014-12-04
RU2014142014A (ru) 2016-05-10
DE102012006017A1 (de) 2013-09-26
US20150034215A1 (en) 2015-02-05

Similar Documents

Publication Publication Date Title
EP2809819B1 (fr) Acier multiphases très résistant, aux propriétés améliorées lors de sa fabrication et de son traitement
EP2836614B1 (fr) Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier
EP2864517B1 (fr) Acier multiphase à haute résistance et procédé pour la fabrication d'une bande faite de cet acier présentant une résistance à la traction minimale de 580 mpa
EP3027784B1 (fr) Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier
EP2668302B1 (fr) Procédé de fabrication d'une bande d'acier à partir d'un acier multiphasé à haute résistance mécanique présentant d'excellentes propriétés de déformation
EP3221484B1 (fr) Procédé de production d'une bande en acier polyphasé, durcissant à l'air, ayant une haute résistance et ayant d'excellentes propriétés de mise en oeuvre
EP3320120A1 (fr) Acier multiphase à haute résistance et procédé de fabrication d'une bande d'acier laminée à froid composée dudit acier
EP3221478B1 (fr) Bande à chaud ou à froid d'un acier multiphasé à haute résistance durcissant à l'air qui présente d'excellentes propriétés de traitement et procédé de fabrication d'une bande à chaud ou à froid à partir de cet acier multiphasé à haute résistance durcissant à l'air
EP3221483B1 (fr) Acier multiphases autotrempant en profondeur à haute résistance mécanique avec excellent aptitude au faconnage et procédé de fabrication d'une bande de cet acier
WO2009021897A1 (fr) Acier biphasé, produit plat constitué d'un tel acier biphasé et procédé de fabrication d'un produit plat
DE102008035714A1 (de) Stahlblech zum Warmpreßformen, das Niedrigtemperatur-Vergütungseigenschaft hat, Verfahren zum Herstellen desselben, Verfahren zum Herstellen von Teilen unter Verwendung desselben, und damit hergestellte Teile
EP3692178B1 (fr) Procede de fabrication d'une bande d'acier a partir d'un acier multiphase a tres haute resistance
EP2855717A1 (fr) Acier, produit en acier plat et procédé de fabrication d'un produit en acier plat
WO2024068957A1 (fr) Procédé de fabrication d'une bande d'acier à partir d'un acier multiphase à haute résistance et bande d'acier correspondante
WO2022207913A1 (fr) Bande d'acier constituée d'un acier multiphase à haute résistance et procédé de production d'une telle bande d'acier

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20140709

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

RIN1 Information on inventor provided before grant (corrected)

Inventor name: KRATZ, HANS-JOACHIM

Inventor name: WEDEMEIER, ANDREAS

Inventor name: MEYER, OLIVER

Inventor name: SCHULZ, THOMAS

Inventor name: POHL, MICHAEL

Inventor name: GELER, MATTHIAS

DAX Request for extension of the european patent (deleted)
17Q First examination report despatched

Effective date: 20161010

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 502013013569

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C21D0008020000

Ipc: C21D0001260000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C23C 2/02 20060101ALI20190318BHEP

Ipc: C21D 1/26 20060101AFI20190318BHEP

Ipc: C21D 1/18 20060101ALI20190318BHEP

Ipc: C22C 38/00 20060101ALI20190318BHEP

Ipc: C21D 8/02 20060101ALI20190318BHEP

Ipc: C22C 38/04 20060101ALI20190318BHEP

Ipc: C22C 38/38 20060101ALI20190318BHEP

Ipc: C22C 1/02 20060101ALI20190318BHEP

Ipc: C22C 38/26 20060101ALI20190318BHEP

Ipc: C21D 9/46 20060101ALI20190318BHEP

Ipc: C22C 38/02 20060101ALI20190318BHEP

Ipc: C21D 9/56 20060101ALI20190318BHEP

Ipc: C22C 38/06 20060101ALI20190318BHEP

INTG Intention to grant announced

Effective date: 20190412

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1178521

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190915

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502013013569

Country of ref document: DE

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20190911

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20191211

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20191211

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20191212

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200113

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200224

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502013013569

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG2D Information on lapse in contracting state deleted

Ref country code: IS

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20200112

26N No opposition filed

Effective date: 20200615

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20200227

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200229

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200227

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200227

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200227

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200229

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 1178521

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200227

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20200227

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190911

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20240219

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20240221

Year of fee payment: 12