EP2864517B1 - 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 - Google Patents

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 Download PDF

Info

Publication number
EP2864517B1
EP2864517B1 EP13732078.4A EP13732078A EP2864517B1 EP 2864517 B1 EP2864517 B1 EP 2864517B1 EP 13732078 A EP13732078 A EP 13732078A EP 2864517 B1 EP2864517 B1 EP 2864517B1
Authority
EP
European Patent Office
Prior art keywords
approx
steel
strip
hot
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
EP13732078.4A
Other languages
German (de)
English (en)
Other versions
EP2864517A1 (fr
Inventor
Thomas Schulz
Marion BECHTOLD
Norbert KWIATON
Alexander GEORGIEW
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 EP2864517A1 publication Critical patent/EP2864517A1/fr
Application granted granted Critical
Publication of EP2864517B1 publication Critical patent/EP2864517B1/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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D1/84—Controlled slow cooling
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C21D8/0221—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
    • 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
    • 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
    • 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
    • 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
    • C23C2/04—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 multi-phase steel according to the preamble of claim 1.
  • the invention relates to a method for producing a hot and / or cold rolled strip from such a steel according to claim 6.
  • the invention relates to steels with a tensile strength in the range from at least 580MPa to a maximum of 700MPa with low yield strength ratios of less than 66% for the production of components which have excellent formability and improved welding properties.
  • the hotly contested automotive market is forcing manufacturers to constantly look for solutions to reduce fleet consumption while maintaining the greatest possible comfort and occupant protection.
  • the weight saving of all vehicle components plays a decisive role, on the other hand, the best possible behavior of the individual components with high static and dynamic stress during operation and in the event of a crash.
  • the raw material suppliers try to take this need into account by making it possible to reduce the weight of the vehicles by providing high-strength to ultra-high-strength steels and reducing the sheet thickness, while at the same time improving the forming and component behavior during production and operation.
  • High-strength to ultra-high-strength steels enable lighter vehicle components, which means lower fuel consumption and less environmental pollution due to the reduced CO 2 content.
  • These steels must therefore meet comparatively high requirements with regard to their strength and ductility, energy absorption and processing, such as for example in stamping, hot and cold forming, welding and / or surface treatment, for example a metallic finish, organic coating or painting.
  • Newly developed steels must therefore meet the required weight reduction, the increasing material requirements for yield strength, tensile strength, strengthening behavior and elongation at break with good formability, as well as the component requirements for high toughness, edge crack resistance, energy absorption as well as strengthening and the bake hardening effect, but also improved suitability for joining in the form of e.g. better weldability.
  • Improved edge crack resistance means increased hole expansion capacity during forming and is known by synonyms such as Low Edge Crack (LEC) or known as High Hole Expansion (HHE).
  • LEC Low Edge Crack
  • HHE High Hole Expansion
  • Improved weldability is among other things achieved by a lowered carbon equivalent. This is synonymous with subperitectical (UP) or the already known low carbon equivalent (LCE).
  • UP subperitectical
  • LCE low carbon equivalent
  • the aim of the steel according to the invention is also to reduce the thickness of the steels used in automobile construction (e.g. micro-alloyed LA steels or LAD steels) in order to save weight.
  • the steels used in automobile construction e.g. micro-alloyed LA steels or LAD steels
  • a high-strength steel e.g. Dual phase steel (DP) can be used to ensure sufficient strength of the automotive components.
  • DP Dual phase steel
  • Dual-phase steels are therefore increasingly being used in vehicle construction, which consist of a ferritic basic structure in which a martensitic second phase and possibly another phase with bainite and residual austenite is embedded.
  • the bainite can exist in different forms.
  • Multi-phase steels are increasingly being used, e.g. complex-phase steels, ferritic-bainitic steels, bainitic steels, martensitic steels, TRIP steels, as well as the dual-phase steels described above, which are characterized by different microstructural compositions are characterized as described in EN 10346 (standard of European steel manufacturers) or VDA239-100 (standard of an automotive steel user) and described below.
  • Complex phase steels are steels that contain small amounts of martensite, residual austenite and / or pearlite in a ferritic / bainitic structure, whereby extreme grain refinement is caused by delayed recrystallization or by excretion of microalloying elements.
  • Ferritic-bainitic steels are steels that contain bainite or solidified bainite in a matrix of ferrite and / or solidified ferrite.
  • the strength of the matrix is brought about by a high dislocation density, grain refinement and the excretion of microalloying elements.
  • Bainitic steels are steels that are characterized by a very high yield strength and tensile strength with sufficient elongation for cold forming processes. Due to the chemical composition, it is easy to weld.
  • the structure typically consists of bainite. Small portions of other phases, such as martensite and ferrite, may occasionally be contained.
  • Martensitic steels are steels that contain small amounts of ferrite and / or bainite in a basic structure made of martensite through thermomechanical rolling. This steel grade is characterized by a very high yield strength and tensile strength with sufficient elongation for cold forming processes. Within the group of multi-phase steels, the martensitic steels have the highest tensile strength values.
  • Dual-phase steels are steels with a ferritic basic structure in which a martensitic second phase is embedded in an island, possibly with bainite as the second phase. With high tensile strength, dual-phase steels show a low yield ratio and strong strain hardening.
  • TRIP steels are steels with a predominantly ferritic structure, in which residual austenite is embedded, which can convert to martensite during the forming process (TRIP effect). Due to its strong strain hardening, the steel achieves high values of uniform elongation and tensile strength.
  • multi-phase steels are used, among other things, in structural, chassis and crash-relevant components, as sheet metal blanks, tailored blanks (welded blanks) and as flexible cold-rolled strips, so-called TRBs.
  • T ailor R olled B lank lightweight technology enables a significant weight reduction through a load-adjusted sheet thickness over the component length and / or steel grade.
  • a special heat treatment takes place for the defined structure adjustment, where e.g. due to comparatively soft components such as ferrite or bainitic ferrite, the steel has its low yield strength and due to its hard components such as martensite or carbon-rich bainite, its strength.
  • the untreated or pickled hot strip in typical thicknesses between 1.50 to 4.00 mm or cold strip in typical thicknesses from 0.50 to 3.00 mm is heated to such a temperature in a continuous annealing furnace that the required temperature increases during cooling Structure formation sets.
  • a steel with complex phase structure, martensitic, ferritic-bainitic and purely bainitic structure is heated to such a temperature in a continuous annealing furnace that the required temperature increases during cooling Structure formation sets.
  • a constant temperature is difficult to achieve, especially with different thicknesses in the transition area from one belt to another belt.
  • this can lead to e.g. the thinner strip is either passed through the furnace too slowly, which reduces productivity, or the thicker strip is passed through the furnace too quickly and the necessary annealing temperatures and cooling gradients are not achieved to achieve the desired structure.
  • the consequences are increased committee.
  • TRB®s with a multi-phase structure is not without additional effort with today's known alloys and available continuous annealing systems for widely varying strip thicknesses, e.g. an additional heat treatment before the Kaitwaizen, possible.
  • strip thicknesses e.g. an additional heat treatment before the Kaitwaizen.
  • a homogeneous multi-phase structure cannot be set in cold as well as hot-rolled steel strips due to a temperature gradient occurring in the usual alloy-specific narrow process windows.
  • a method for producing a steel strip with different thicknesses over the length of the strip is described, for example, in DE 100 37 867 A1 described.
  • the annealing treatment is usually carried out in a continuous annealing furnace upstream of the galvanizing bath.
  • the required strip is only set for the hot strip only during the annealing treatment in the continuous furnace in order to achieve the required mechanical properties.
  • Crucial process parameters are therefore the setting of the annealing temperatures and the speed, as well as the cooling rate (cooling gradient) in continuous annealing, since the phase change takes place depending on the temperature and time.
  • the areas with a smaller strip thickness due to the conversion processes during cooling either have too high strengths due to excessively high martensite contents or the areas with greater strip thickness achieve insufficient strengths due to insufficiently low martensite contents due to the process window being too small.
  • Homogeneous mechanical-technological properties across the strip length or width can practically not be achieved with the known alloy concepts for continuous annealing.
  • the goal of achieving the resulting mechanical-technological properties in a narrow range across 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 multi-phase steels are characterized by a too narrow process window and are therefore unsuitable for solving the problem at hand, particularly in the case of flexibly rolled strips. With the known alloy concepts, only steels of a strength class with defined cross-sectional areas (strip thickness and bandwidth) can currently be produced, so that different alloy classes are necessary for different strength classes and or cross-sectional areas.
  • the material processing properties are increasingly deteriorating, for example in welding, forming and hot-dip finishing, but also industrial production in all process stages, such as steel production, hot rolling, pickling, cold rolling and heat treatment with / without hot-dip coating, places greater demands on the individual systems.
  • the hole expansion test according to ISO 11630 is used as one of several possible test methods for the description and quantification of cold processing, in particular the edge crack behavior.
  • Silicon plays a subordinate role in the calculation of the carbon equivalent. This is crucial in relation to the invention.
  • the lowering of the carbon equivalent through lower levels of carbon and manganese is to be compensated for by increasing the silicon content. Thus, the edge crack resistance and the weldability are improved with the same strength.
  • a low yield strength ratio (Re / Rm) is typical for a dual-phase steel and is primarily used for the formability during stretching and deep-drawing processes. It gives the designer information about the distance between the onset of plastic deformation and failure of the material under quasi-static stress. Ask accordingly lower yield strength ratios represent a greater safety margin from component failure.
  • a higher yield strength ratio (Re / Rm), as is typical for complex phase steels, is also characterized by the resistance to edge cracks. This can be attributed to the smaller differences in the strength of the individual structural components, which has a favorable effect on a homogeneous deformation in the area of the cut edge.
  • the analytical landscape for achieving multi-phase steels with a minimum tensile strength of 580MPa is very diverse and shows very large alloy ranges for the strength-increasing elements carbon, silicon, manganese, phosphorus, aluminum as well as chromium and / or molybdenum, as well as in the addition of microalloys such as titanium, Niobium, vanadium and / or boron, as well as in the material characterizing properties.
  • the range of dimensions is wide and lies in the thickness range of about 0.50 to 4.00mm. Tapes up to around 1850mm are predominantly used, but also split tape dimensions, which are caused by lengthwise splitting of the tapes. Sheets or sheets are made by cross-cutting the strips.
  • the invention is therefore based on the object of creating a new alloy concept for high-strength multi-phase steel with a minimum tensile strength of 580MPa to 700MPa along and across the rolling direction, preferably with a dual-phase structure and a yield ratio of less than 66%, with which the process window for the Continuous annealing of hot or cold strips can be expanded so that in addition to strips with different cross-sections, steel strips with thicknesses that vary over strip length and possibly strip width and the correspondingly varying degrees of cold rolling can be produced with the most homogeneous mechanical and technological properties.
  • the hot-dip galvanizability of the steel is to be ensured and a method for producing a strip produced 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 0.600 to ⁇ 0.800 Mn 1,000 to ⁇ 2,250 Cr 0.280 to ⁇ 0.480 al 0.010 to ⁇ 0.06O P ⁇ 0,020 N ⁇ 0,0100 S ⁇ 0,0150
  • a steel with partially overlapping grades is made of DE 10161465 known.
  • the steel according to the invention is very well suited for hot-dip coating and has a significantly enlarged process window compared to the known steels. This results in increased process reliability when continuous annealing cold and hot strip with dual or multi-phase structure. Therefore, for continuously annealed hot or cold strips, more homogeneous mechanical and technological properties can be set in the strip, even with different cross sections and otherwise the same process parameters.
  • processing in selected thickness ranges is possible (e.g. smaller 1mm tape thickness, 1 to 2mm tape thickness and 2 to 4mm tape thickness).
  • the material produced can be produced both as cold and hot strip via a hot-dip galvanizing line or a pure continuous annealing system in the trained and undressed, in the stretch-bending and non-stretch-bending direction and also in the heat-treated state (intermediate annealing).
  • steel strips can be produced by an intercritical annealing between A c1 and A c3 or in the case of an austenitizing annealing over A c3 with a final controlled cooling, which leads to a dual or multi-phase structure.
  • Annealing temperatures of approximately 700 to 950 ° C. have proven to be advantageous. Depending on the overall process, there are different approaches to realizing the heat treatment.
  • the strip is cooled from the annealing temperature with a cooling rate of approx. 15 to 100 ° C / s to an intermediate temperature of approx. 200 to 250 ° C.
  • the cooling down to room temperature is then carried out at a cooling rate of approx. 2 to 30 ° C / s.
  • Cooling as described above is stopped before entering the molten bath and only continued after leaving the bath until the intermediate temperature of about 200 to 250 ° C. has been reached.
  • the holding temperature is approx. 420 to 470 ° C. Cooling down to room temperature takes place again at a cooling rate of approx. 2 to 30 ° C / s.
  • the second variant of the temperature control for hot-dip coating includes maintaining the temperature for approx. 1 to 20s at the intermediate temperature of approx. 200 to 250 ° C and then reheating to the temperature required for hot-dip coating of approx. 420 to 470 ° C. After finishing, the strip is cooled again to approx. 200 to 250 ° C. The cooling to room temperature takes place again with a cooling rate of approx. 2 to 30 ° C / s.
  • the carbon equivalent can be reduced, which improves weldability and prevents excessive hardening during welding. In the case of resistance spot welding, the electrode service life can also 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 structured in such a way that alloy elements are combined with and without micro-alloy elements. Accompanying elements are inevitable and their effects are taken into account in the analysis concept if necessary.
  • Hydrogen (H) is the only element that can diffuse through the iron lattice without generating lattice strain. This causes the hydrogen in the iron lattice to be relative is movable and can be taken up relatively easily during processing of the steel. Hydrogen can only be absorbed into the iron lattice in an atomic (ionic) form.
  • Hydrogen has a strong embrittlement effect and diffuses preferentially to energetically favorable places (defects, grain boundaries etc.). Defects act as water stalls and can significantly increase the length of time that hydrogen stays in the material.
  • Recycle to molecular hydrogen can result in cold cracks. This behavior occurs with hydrogen embrittlement or with hydrogen-induced stress corrosion cracking. Hydrogen is also often mentioned as the reason for the delayed crack, the so-called delayed fracture, which occurs without external stresses.
  • a more even structure which among other things in the steel according to the invention. achieved through its widened process window, 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 amounts. Analogous to hydrogen, oxygen can only diffuse into the material in an atomic form. Due to the strong embrittlement effect and the negative effects on the aging resistance, attempts are made to reduce the oxygen content as much as possible during manufacture.
  • the oxygen content in the steel should therefore be as low as possible.
  • Nitrogen (N) is also an accompanying element from steel production. Steels with free nitrogen tend to have a strong aging effect. The nitrogen diffuses at dislocations even at low temperatures and blocks them. It causes an increase in strength combined with a rapid loss of toughness.
  • the nitrogen can be set in the form of nitrides by alloying with aluminum or titanium.
  • the nitrogen content is limited to ⁇ 0.0100%, advantageously to ⁇ 0.0090% or optimally to ⁇ 0.0080% or to quantities unavoidable in the steel production.
  • sulfur is bound as a trace element in iron ore. It is undesirable in steel (with the exception of free-cutting steels) because it tends to segregate strongly and is highly embrittling. An attempt is therefore made to achieve the smallest possible amount of sulfur in the melt (for example by means of a vacuum treatment). Furthermore, the sulfur present is converted into the relatively harmless compound manganese sulfide (MnS) by adding manganese.
  • MnS manganese sulfide
  • the manganese sulfides are often rolled out in rows during the rolling process and act as germination points for the conversion. This leads especially to diffusion-controlled conversion to a line structure and can lead to deteriorated mechanical properties if the line structure is very pronounced (e.g. pronounced marten seat lines instead of distributed martensite islands, anisotropic material behavior, reduced elongation at break).
  • the sulfur content is limited to ⁇ 0.0150%, advantageously to ⁇ 0.0050% or optimally to ⁇ 0.0030% or to quantities unavoidable in the steel production.
  • Phosphorus (P) is a trace element from iron ore and is dissolved in the iron lattice as a substitute atom . Phosphorus increases hardness through solid-solution hardening and improves hardenability.
  • the phosphorus content is limited to ⁇ 0.020% or to quantities unavoidable in the steel production.
  • Alloy elements are usually added to the steel in order to influence certain properties.
  • An alloy element in different steels can influence different properties. The effect generally depends strongly on the amount and the state of the solution in the material.
  • Carbon (C) is the most important alloying element in steel. Through its targeted introduction of up to 2.06%, iron only becomes steel. The carbon content is often drastically reduced during steel production. In the case of dual-phase steels for continuous hot-dip coating, its share is a maximum of 0.230%, a minimum value is not specified.
  • carbon is dissolved interstitially in the iron lattice.
  • the solubility is a maximum of 0.02% in ⁇ -iron and a maximum of 2.06% in ⁇ -iron.
  • carbon significantly increases the hardenability of steel and is therefore essential for the formation of a sufficient amount of martensite. Too high a carbon content, however, increases the difference in hardness between ferrite and martensite and limits weldability.
  • the steel according to the invention is underperitectic.
  • Carbon also forms carbides.
  • a representative in almost every steel is cementite (Fe 3 C).
  • much harder special carbides can form with other metals such as chromium, titanium, niobium, vanadium.
  • the minimum C content is set at 0.075% and the maximum C content at 0.105%.
  • Silicon (Si) binds oxygen during casting and thus reduces segregation and contamination in the steel.
  • the segregation coefficient is significantly lower than, for example, with manganese (0.16 compared to 0.87).
  • Another important effect is that silicon postpones the formation of ferrite at shorter times and temperatures, thus allowing sufficient ferrite to form before quenching. In hot rolling, this creates a basis for improved cold rolling.
  • the accelerated ferrite formation enriches the austenite with carbon and thus stabilizes it. Because silicon hinders carbide formation, the austenite is additionally stabilized. The accelerated cooling can thus suppress the formation of bainite in favor of martensite.
  • silicon also increases the strength and the yield strength ratio of the ferrite with solid crystal strengthening with only a slightly lower elongation at break.
  • silicon reduces the difference in hardness between the structural components of ferrite and martensite, since it increases the solubility for carbon in ferrite.
  • the furnace atmosphere can be reducing for iron, but oxidizing for the alloying elements.
  • the oxides of the alloy elements remain in the RTF at the former iron / iron oxide boundary layer, i.e. well below the surface of the steel strip (internal oxidation).
  • the dew point in the area between the furnace and zinc pot transition zone should be selected (preferably below -30 ° C) so that the strip is not oxidized before it is immersed in the zinc bath. Dew points of -35 or -40 ° C have proven to be advantageous.
  • the internal oxidation can be promoted by slightly increasing the oxygen content in the furnace atmosphere. This is accomplished by regulating the dew point (preferably> -30 ° C, advantageously -25 or -20 ° C). Due to the higher oxygen partial pressure, the oxygen can diffuse into the steel strip and oxidize the alloying elements. If, on the other hand, there is only a little oxygen in the atmosphere, the less noble alloy elements diffuse to the strip surface and form non-wettable oxides there. Here, too, it is important to avoid oxidation of the iron in the RTF and in the area of the proboscis.
  • the minimum Si content is set at 0.600% and the maximum silicon content at 0.800%.
  • Manganese (Mn) is added to almost all steels for desulfurization in order to convert the harmful sulfur into manganese sulfides.
  • manganese increases the strength of the ferrite through solidification of the crystal and shifts the ⁇ - / ⁇ -conversion to lower temperatures.
  • a main reason for alloying manganese in dual-phase steels is the significant improvement in hardenability. Due to the diffusion hindrance, the pearlite and bainite transformation is postponed for longer periods and the martensite start temperature is lowered.
  • the addition of manganese increases the hardness ratio between martensite and ferrite.
  • the structure of the structure is strengthened. A high difference in hardness between the phases and the formation of marten seat ropes result in a lower hole expansion capacity, which has an adverse effect on the edge crack resistance.
  • manganese tends to form oxides on the steel surface during the annealing treatment.
  • manganese oxides eg MnO
  • Mn mixed oxides eg Mn 2 SiO 4
  • Si / Mn or Al / Mn ratio manganese is to be regarded as less critical, since globular oxides form rather than oxide films. Nevertheless, high manganese levels can have a negative impact on the appearance of the zinc layer and the zinc adhesion.
  • the manganese content is set at 1,000 to 2,250% for the reasons mentioned.
  • the manganese content is preferably ⁇ 1.50%, with strip thicknesses from 1 to 2mm at ⁇ 1.75% and with strip thicknesses> 2mm at ⁇ 1.50%.
  • Chromium (Cr) on the one hand, can significantly increase the hardenability of steel in small quantities in dissolved form.
  • Cr Cr
  • chromium carbides causes particle solidification.
  • the associated increase in Number of germ sites with a simultaneously reduced carbon content leads to a reduction in hardenability.
  • chromium In dual-phase steels, the addition of chromium mainly improves hardenability. When dissolved, chromium shifts the pearlite and bainite transformation for longer times and at the same time lowers the martensite start temperature.
  • Chromium is also a carbide former. If chromium-iron mixed carbides are present, the austenitizing temperature before hardening must be selected high enough to dissolve the chromium carbides. Otherwise, the increased number of bacteria can lead to a deterioration in the hardenability.
  • Chromium also tends to form oxides on the steel surface during the annealing treatment, which can degrade the galvanizing quality.
  • the chromium content is therefore set at values from 0.280 to 0.480%.
  • the total content of Mn + Si + Cr must also be observed according to the sheet thickness, according to the invention.
  • a total content of ⁇ 1.88 to ⁇ 2.60% has been found to be favorable for sheet thicknesses of ⁇ 1mm, a total content of ⁇ 2.20 to ⁇ 3.00% for sheet thicknesses of 1 to 2mm and a total content of for sheet thicknesses ⁇ 2mm ⁇ 2.50 to ⁇ 3.53%.
  • Aluminum (Al) is usually alloyed to the steel in order to bind the oxygen and nitrogen dissolved in the iron. The oxygen and nitrogen are thus converted into aluminum oxides and aluminum nitrides. These excretions can cause grain refinement by increasing the number of germs and thus increase the toughness properties and strength values.
  • Titanium nitrides have a lower enthalpy of formation and are formed at higher temperatures.
  • the aluminum content is therefore limited to 0.010 to a maximum of 0.060% and is added to calm the steel.
  • Niobium (Nb) For cost reasons, niobium is not added and the content is limited to the unavoidable amounts accompanying steel.
  • the annealing temperatures for the dual-phase structure to be achieved for the steel according to the invention are between approximately 700 and 950 ° C., so that depending on the temperature range, a partially austenitic (two-phase area) or a fully austenitic structure (austenite area) is achieved.
  • the hot-dip coated material can be used as hot strip as well as cold-rolled hot strip or cold strip in trained (cold-rolled) or undressed condition and / or stretch-bend or not stretch-bend condition are manufactured.
  • Steel strips in the present case as hot strip, cold-rolled hot strip or cold strip made from the alloy composition according to the invention are also distinguished in the further processing by a high resistance to crack formation close to the edge.
  • the hot strip is produced according to the invention with finish rolling temperatures in the austenitic region above A r3 and coiling temperatures above the bainite start temperature.
  • the hot strip is produced according to the invention with finish rolling temperatures in the austenitic region above A r3 and coiling temperatures below the bainite start temperature.
  • Example 1 (cold-rolled hot strip according to FIG. 7c )
  • a steel according to the invention with 0.101% C; 0.605% Si; 1.374% Mn; 0.327% Cr; 0.039% Al; 0.012% P; 0.0035% Nb; 0.003% Mo; 0.0063% N; 0.0009% S was melted in a converter steel mill, hot-rolled in a hot strip mill at a final rolling temperature of 911 ° C and wound at a reel temperature of 484 ° C with a thickness of 2.37mm. After pickling with hydrochloric acid, the cold rolling was carried out on a five-stand tandem mill with a cold rolling degree of 16% from 2.37 mm to 1.99 mm.
  • the steel according to the invention has a structure which consists of ferrite, martensite, bainite and residual austenite.
  • This steel shows the following characteristic values (specifications in brackets, cross values according to EN 10346 and longitudinal values according to VDA239-100): - yield strength (Rp0.2) transversely 419MPa (340MPa-420MPa) longitudinal direction 408MPa (330MPa-430MPa) - tensile strength (Rm) transversely 646MPa (min.600MPa) longitudinal direction 636MPa (590MPa-700MPa) - elongation at break (A80) transversely 23.6% (min. 20%) longitudinal direction 27.0% (min.
  • the yield point ratio Rp0.2 / Rm is 64% in the transverse direction with respect to the rolling direction and 65% in the longitudinal direction.
  • Example 2 (cold strip according to FIG. 7b )
  • a steel according to the invention with 0.101% C; 0.605% Si; 1.374% Mn; 0.327% Cr; 0.039% Al; 0.012% P; 0.0035% Nb; 0.003% Mo; 0.0063% N; 0.0009% S was melted in a converter steel mill, hot-rolled in a hot strip mill at a final rolling temperature of 902 ° C and wound at a reel temperature of 676 ° C with a thickness of 2.02mm. After pickling with hydrochloric acid, the cold rolling was carried out on a five-stand tandem mill with a degree of cold rolling of 50% from 2.02 mm to 0.99 mm.
  • the steel according to the invention has a structure which consists of ferrite, martensite, bainite and residual austenite.
  • the yield point ratio Re / Rm is 58% in both the longitudinal and transverse directions (based on the rolling direction).
  • Example 3 (hot strip according to FIG. 7b )
  • a steel according to the invention with 0.101% C; 0.605% Si; 1.374% Mn; 0.327% Cr; 0.039% Al; 0.012% P; 0.0035% Nb; 0.003% Mo; 0.0063% N; 0.0009% S was melted in a converter steel mill, hot-rolled in a hot strip mill at a final rolling temperature of 916 ° C and wound at a reel temperature of 485 ° C with a thickness of 2.02mm.
  • the steel according to the invention has a structure which consists of ferrite, martensite, bainite and residual austenite.
  • the yield strength ratio Re / Rm is 58.4% both in the transverse direction and in the longitudinal direction (based on the rolling direction).
  • Example 4 hot strip and cold-rolled hot strip according to FIG. 7c .
  • the steel according to the invention from example 2 (reel temperature 676 ° C.) and from example 3 (reel temperature 485 ° C.) was further processed after pickling under conditions close to the company.
  • the cold rolling was carried out in a test cold rolling mill.
  • the degrees of cold rolling tested were 0% and 10%.
  • the hot-dip galvanizing cycle was carried out using a glow simulator Figure 7c readjusted.
  • Figure 1 shows schematically the process chain for the production of the steel according to the invention.
  • the different process routes relating to the invention are shown.
  • the process route is the same for all steels according to the invention up to position 5 (pickling), after which process routes differ depending on the desired results.
  • the pickled hot strip can be galvanized or cold rolled and galvanized with different degrees of rolling.
  • soft-annealed hot strip or soft-annealed cold strip can be cold-rolled and galvanized.
  • Figure 2 shows results of a hole expansion test (relative values for comparison quality). The results of the hole expansion tests for a steel according to the invention are shown compared to the comparison quality, the standard quality process 2 serves as a reference.
  • Process 2 corresponds to annealing, for example on hot-dip galvanizing with a combined direct-fired furnace and radiant tube furnace, as shown in Figure 7b is described.
  • Figure 3 shows the relevant alloying elements of the steel according to the invention, exemplifies compared to the comparative quality.
  • the main difference in the comparison steel lies in the carbon content, which is in the overperitectic range, but also in the elements silicon and chromium.
  • the standard quality is phosphorus microalloyed.
  • the steel according to the invention is clearly silicon alloyed.
  • Figure 4 shows the mechanical characteristics transverse to the rolling direction of the steel according to the invention for comparison quality. All characteristic values achieved by annealing in a two-phase area correspond to the normative specifications of an HCT600X or HDT580X.
  • Figure 5 shows schematically the time-temperature profile of the process steps hot rolling and continuous annealing of strips from the alloy composition according to the invention. The time and temperature dependent conversion for the hot rolling process as well as for a heat treatment after the cold rolling is shown.
  • Figure 6 shows the positive result of the ball impact test (according to SEP1931) on a hot-dip galvanized material made from the steel according to the invention.
  • the Figures 7 schematically show three variants of the temperature-time profiles according to the invention in the annealing treatment and cooling and in each case different austenitizing conditions.
  • Procedure 1 shows the annealing and cooling of the cold or hot rolled steel strip produced in a continuous annealing plant.
  • First the strip is heated to a temperature in the range of approx. 700 to 950 ° C.
  • the annealed steel strip is then cooled from the annealing temperature with a cooling rate between approx. 15 and 100 ° C / s to an intermediate temperature of approx. 200 to 250 ° C.
  • This schematic representation does not show a second intermediate temperature (approx. 300 to 500 ° C).
  • the steel strip is then cooled in air at a cooling rate of between approx. 2 and 30 ° C / s until room temperature is reached, or cooling is maintained at room temperature until the cooling rate is between approx. 15 and 100 ° C / s.
  • Procedure 2 shows the process according to method 1, however the cooling of the steel strip for the purpose of hot-dip coating is briefly interrupted when passing through the hot-dip tank, in order to then cool with a cooling rate between approx. 15 and 100 ° C / s up to an intermediate temperature of approx. 200 continue up to 250 ° C.
  • the steel strip is then cooled in air at a cooling rate between approx. 2 and 30 ° C / s until room temperature is reached.
  • Procedure 3 ( Figure 7c ) also shows the process according to method 1 for hot-dip coating, but the cooling of the steel strip is interrupted by a short pause (approx. 1 to 20 s) at an intermediate temperature in the range from approx. 200 to 400 ° C and up to the temperature, which is necessary for hot-dip coating (approx. 420 to 470 ° C) reheated.
  • the steel strip is then cooled again to an intermediate temperature of approx. 200 to 250 ° C. With a cooling rate of approx.
  • the final cooling of the steel strip takes place at 2 and 30 ° C / s until the room temperature is reached in air.
  • Figure 8 shows the mechanical characteristics of a steel according to the invention (example! 4), which according to method 3 ( Figure 7c ) was annealed or cold-rolled and annealed.
  • the values are mean values from two longitudinal samples, which were determined in the tensile test.
  • the low yield strength values are due to the fact that the samples are undressed.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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 (12)

  1. Acier multiphasé à haute résistance avec des résistances à la traction minimums de 580 MPa pour une bande d'acier laminée à froid ou laminée à chaud ayant des propriétés de formage améliorées, en particulier pour la construction automobile légère, composé des éléments suivants (teneurs en % en masse) : C 0,075 à ≤ 0,105 Si 0,600 à ≤ 0,800 Mn 1,000 à ≤ 2,250 Cr 0,280 à ≤ 0,480 Al 0,010 à ≤ 0,060 P ≤ 0,020 N ≦ 0,0100 S ≤ 0,0150
    le reste est constitué de fer et d'impuretés résultant de la fusion, à condition que,
    pour des épaisseurs de bandes jusqu'à 1 mm, la teneur en Mn soit ≤ 1,500 % et la somme des teneurs en Mn+Si+Cr soit ≥ 1,88 et ≤ 2,60 %,
    pour des épaisseurs de bandes de 1 à 2 mm, la teneur en Mn soit ≤ 1,750 % et la somme des teneurs en Mn+Si+Cr soit ≥ 2,20 et ≤ 3,00 %, et
    pour des épaisseurs de bande ≥ 2mm, la teneur en Mn soit ≥ 1,500 % et la somme des teneurs en Mn+Si+Cr soit ≥ 2,50 et ≤ 3,53 %.
  2. Acier selon la revendication 1,
    caractérisé en ce que,
    la teneur en N est ≤ 0,0090 %.
  3. Acier selon la revendication 1,
    caractérisé en ce que,
    la teneur en N est ≤ 0,0080 %.
  4. Acier selon la revendication 1,
    caractérisé en ce que,
    la teneur en S est ≤ 0,0050 %.
  5. Acier selon la revendication 1,
    caractérisé en ce que,
    la teneur en S est ≤ 0,0030 %.
  6. Procédé de fabrication d'une bande d'acier laminée à froid ou à chaud à partir d'un acier produit selon l'une quelconque des revendications 1 à 5, dans lequel une structure à deux phases est produite pendant un recuit continu,
    caractérisé en ce que,
    la bande d'acier laminée à froid ou laminée à chaud est chauffée à une température dans la plage d'environ 700 à 950 °C pendant le recuit continu, et en ce que la bande d'acier recuite est ensuite refroidie à une vitesse de refroidissement comprise entre environ 15 et 100 °C/s jusqu'à une première température intermédiaire comprise entre environ 300 et 500 °C, puis à une seconde vitesse de refroidissement comprise entre environ 15 et 100 °C/s jusqu'à une seconde température intermédiaire comprise entre environ 200 et 250 °C, et en ce que, lors du recuit continu, la bande d'acier recuite est chauffée à une température comprise entre environ 200 à 250 °C, puis la bande d'acier est refroidie à l'air à une vitesse de refroidissement comprise entre environ 2 et 30 °C/s jusqu'à ce que la température ambiante soit atteinte, ou le refroidissement est maintenu à une vitesse comprise entre environ 15 et 100 °C/s de la première température intermédiaire jusqu'à la température ambiante, dans lequel par un processus de transformation par galvanisation à chaud après le chauffage et ensuite de refroidissement, le refroidissement est interrompu avant l'entrée dans le bain de fusion et, après la transformation par galvanisation à chaud, le refroidissement se poursuit à une vitesse comprise entre environ 15 et 100 °C/s jusqu'à une température intermédiaire d'environ 200 à 250 °C, puis la bande d'acier est refroidie à l'air à une vitesse de refroidissement d'environ 2 et 30 °C/s jusqu'à atteindre la température ambiante.
  7. Procédé selon la revendication 6,
    caractérisé en ce que,
    dans une transformation par galvanisation à chaud, après chauffage et refroidissement ultérieur à la température intermédiaire comprise entre environ 200 et 250 °C avant l'entrée dans le bain de fusion, la température est maintenue pendant environ 1 à 20 s, puis la bande d'acier est à nouveau chauffée jusqu'à la température comprise entre environ 420 et 470 °C et, après transformation par galvanisation à chaud, le refroidissement s'effectue à une vitesse de refroidissement comprise entre environ 15 et 100 °C/s jusqu'à une température intermédiaire comprise entre environ 200 et 250 °C, puis à l'air à une vitesse de refroidissement comprise entre environ 2 et 30 °C/s jusqu'à la température ambiante.
  8. Procédé selon l'une des revendications 6 à 7,
    caractérisé en ce que,
    le potentiel d'oxydation lors d'un recuit avec une configuration d'installation constituée d'une zone de four directement chauffée (NOF) et d'un four à tubes d'acier (RTF) est augmenté par une teneur en CO inférieure à 4 %, dans lequel l'atmosphère du four dans le RTF est réglée pour réduire, et pour éviter une oxydation de la bande avant son immersion dans le bain de zinc, le point de rosée est établi à -30 °C ou moins.
  9. Procédé selon l'une quelconque des revendications 6 ou 7,
    caractérisé en ce que,
    le point de rosée dans l'atmosphère du four est de -30 °C ou plus, par exemple -25 ou -20 °C, lors du recuit uniquement avec un four à tubes d'acier.
  10. Procédé selon l'une des revendications 6 à 9,
    caractérisé en ce que,
    en ajustant la vitesse de passage de l'installation à différentes épaisseurs de bandes au cours du traitement thermique, des états de structure et des valeurs caractéristiques mécaniques comparables des bandes sont définis.
  11. Procédé selon l'une des revendications 6 à 10,
    caractérisé en ce que,
    la bande d'acier est dressée après le traitement thermique.
  12. Procédé selon au moins l'une quelconque des revendications 6 à 11,
    caractérisé en ce que,
    la bande d'acier est redressé par étirage après le traitement thermique.
EP13732078.4A 2012-06-22 2013-05-24 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 Active EP2864517B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102012013113A DE102012013113A1 (de) 2012-06-22 2012-06-22 Hochfester Mehrphasenstahl und Verfahren zur Herstellung eines Bandes aus diesem Stahl mit einer Mindestzugfestigkleit von 580MPa
PCT/DE2013/000299 WO2013189474A1 (fr) 2012-06-22 2013-05-24 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

Publications (2)

Publication Number Publication Date
EP2864517A1 EP2864517A1 (fr) 2015-04-29
EP2864517B1 true EP2864517B1 (fr) 2020-01-22

Family

ID=48700231

Family Applications (1)

Application Number Title Priority Date Filing Date
EP13732078.4A Active EP2864517B1 (fr) 2012-06-22 2013-05-24 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

Country Status (6)

Country Link
US (1) US20150337408A1 (fr)
EP (1) EP2864517B1 (fr)
KR (1) KR102079611B1 (fr)
DE (1) DE102012013113A1 (fr)
RU (1) RU2627068C2 (fr)
WO (1) WO2013189474A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102020110319A1 (de) 2020-04-15 2021-10-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit einem Mehrphasengefüge und Stahlband hinzu

Families Citing this family (32)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3132063B1 (fr) 2014-04-15 2021-01-13 ThyssenKrupp Steel Europe AG Procédé de production d'un produit plat en acier laminé à froid à limite d'élasticité élevée et produit plat en acier laminé à froid
CN106232851B (zh) * 2014-04-23 2018-01-05 新日铁住金株式会社 连续变截面板用热轧钢板、连续变截面板、及它们的制造方法
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
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
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
DE102015111177A1 (de) * 2015-07-10 2017-01-12 Salzgitter Flachstahl Gmbh Höchstfester Mehrphasenstahl und Verfahren zur Herstellung eines kaltgewalzten Stahlbandes hieraus
DE102015112889A1 (de) 2015-08-05 2017-02-09 Salzgitter Flachstahl Gmbh Hochfester manganhaltiger Stahl, Verwendung des Stahls für flexibel gewalzte Stahlflachprodukte und Herstellverfahren nebst Stahlflachprodukt hierzu
WO2017109540A1 (fr) * 2015-12-21 2017-06-29 Arcelormittal Procédé de fabrication d'une tôle d'acier à haute résistance ayant une ductilité et une aptitude au formage améliorées et tôle d'acier ainsi obtenue
DE102016110661A1 (de) 2016-06-09 2017-12-14 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines kaltgewalzten Stahlbandes aus einem hochfesten, manganhaltigen Stahl
JP6737338B2 (ja) 2016-08-08 2020-08-05 日本製鉄株式会社 鋼板
CN109642263B (zh) 2016-08-23 2021-02-26 德国沙士基达板材有限公司 一种用于制造在进一步加工过程中具有改进性能的高强度钢带的方法以及这种钢带
DE102016115618A1 (de) 2016-08-23 2018-03-01 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines höchstfesten Stahlbandes mit verbesserten Eigenschaften bei der Weiterverarbeitung und ein derartiges Stahlband
RU2725939C1 (ru) 2016-09-16 2020-07-07 Зальцгиттер Флахшталь Гмбх Способ изготовления подвергнутой повторному формованию детали из плоского стального продукта с содержанием марганца и деталь такого типа
DE102016117502A1 (de) 2016-09-16 2018-03-22 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Warm- oder Kaltbandes und/oder eines flexibel gewalzten Stahlflachprodukts aus einem hochfesten manganhaltigen Stahl und Stahlflachprodukt hiernach
DE102016117508B4 (de) 2016-09-16 2019-10-10 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlflachprodukts aus einem mittelmanganhaltigen Stahl und ein derartiges Stahlflachprodukt
DE102016117494A1 (de) 2016-09-16 2018-03-22 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines umgeformten Bauteils aus einem mittelmanganhaltigen Stahlflachprodukt und ein derartiges Bauteil
CN109923233A (zh) 2016-11-02 2019-06-21 德国沙士基达板材有限公司 用于低温应用的中锰钢产品及其制造方法
WO2018083028A1 (fr) 2016-11-02 2018-05-11 Salzgitter Flachstahl Gmbh Tube sans soudure en acier au manganèse moyen et procédé de fabrication
WO2018151974A2 (fr) 2017-02-17 2018-08-23 Goff Omega Holdings, Llc Procédé de test de fragilisation par l'hydrogène
DE102017223633A1 (de) 2017-12-21 2019-06-27 Voestalpine Stahl Gmbh Kaltgewalztes Stahlflachprodukt mit metallischer Korrosionsschutzschicht und Verfahren zur Herstellung eines solchen
KR102031454B1 (ko) * 2017-12-24 2019-10-11 주식회사 포스코 저온 밀착성과 가공성이 우수한 용융아연도금강판 및 그 제조방법
RU2691809C1 (ru) * 2018-05-25 2019-06-18 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Способ производства толстолистового высокопрочного износостойкого проката (варианты)
CN110616303A (zh) * 2018-06-19 2019-12-27 宝山钢铁股份有限公司 一种980MPa级以上冷轧或镀锌双相钢板的制造方法
CN109136739B (zh) * 2018-06-29 2020-08-04 唐山钢铁集团有限责任公司 双相钢冷轧高强汽车板可涂装性能表面质量的控制方法
WO2020058330A1 (fr) * 2018-09-19 2020-03-26 Sms Group Gmbh Acier avancé à haute limite d'élasticité, bande en acier composée de cet acier ainsi que procédé pour la fabrication d'une bande en acier
KR102648242B1 (ko) * 2018-12-19 2024-03-18 주식회사 포스코 전기 저항 점용접성이 우수한 고강도 아연도금강판 및 그 제조방법
DE102019108457B4 (de) * 2019-04-01 2021-02-04 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit verbesserter Haftung metallischer Schmelztauchüberzüge
DE102020203564A1 (de) 2020-03-19 2021-09-23 Sms Group Gmbh Verfahren zum Herstellen eines gewalzten Mehrphasenstahlbandes mit Sondereigenschaften
EP4139492A1 (fr) 2020-04-22 2023-03-01 ThyssenKrupp Steel Europe AG Produit d'acier plat laminé à chaud et son procédé de fabrication
CA3146647A1 (fr) * 2021-01-29 2022-07-29 Algoma Steel Inc. Tole d'acier lamine a froid
CN113957349B (zh) * 2021-10-26 2022-09-06 江苏沙钢集团有限公司 一种600MPa级热成形钢及其生产方法
WO2023129088A2 (fr) * 2021-12-30 2023-07-06 Ereğli̇ Demi̇r Ve Çeli̇k Fabri̇kalari T.A.Ş. Tôle d'acier revêtue d'un alliage fer-zinc (galvanneal) à haute résistance et procédé de production pour l'industrie automobile

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100003161A1 (en) * 2002-06-19 2010-01-07 Nippon Steel Corporation Steel for Crude Oil Tank, Method for Producing the Same, Crude Oil Tank and Corrosion Prevention Method Thereof

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19610675C1 (de) 1996-03-19 1997-02-13 Thyssen Stahl Ag Mehrphasenstahl und Verfahren zu seiner Herstellung
EP2312008B1 (fr) * 1997-01-29 2012-03-14 Nippon Steel Corporation Aciers haute résistance ayant d'excellentes propriétés d'absorption d'énergie aux chocs.
KR100334949B1 (ko) * 1997-03-17 2002-05-04 아사무라 타카싯 동적변형 특성이 우수한 듀얼 페이즈형 고강도 강판 및 그 제조방법
JPH11293396A (ja) * 1998-04-15 1999-10-26 Nkk Corp 高強度溶融亜鉛めっき鋼板及び合金化溶融亜鉛めっき鋼板ならびにその製造方法
JP3956550B2 (ja) * 1999-02-02 2007-08-08 Ｊｆｅスチール株式会社 強度延性バランスに優れた高強度溶融亜鉛メッキ鋼板の製造方法
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
JP2003247043A (ja) 2001-07-06 2003-09-05 Jfe Steel Kk 強度−延性バランスに優れた高張力溶融亜鉛めっき冷延鋼板およびその製造方法
DE10161465C1 (de) * 2001-12-13 2003-02-13 Thyssenkrupp Stahl Ag Verfahren zum Herstellen von Warmband
FR2836930B1 (fr) * 2002-03-11 2005-02-25 Usinor Acier lamine a chaud a tres haute resistance et de faible densite
WO2005019487A1 (fr) * 2003-08-26 2005-03-03 Jfe Steel Corporation Tole d'acier lamine a froid a haute resistance a la traction et son procede de production
JP4337604B2 (ja) * 2004-03-31 2009-09-30 Ｊｆｅスチール株式会社 高張力鋼板の歪時効処理方法および高強度構造部材の製造方法
EP2009128A1 (fr) * 2007-06-29 2008-12-31 ArcelorMittal France Acier au silicium galvanisé ou recuit après galvanisation
JP5533144B2 (ja) * 2010-03-31 2014-06-25 新日鐵住金株式会社 溶融めっき冷延鋼板およびその製造方法
DE102012002079B4 (de) * 2012-01-30 2015-05-13 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines kalt- oder warmgewalzten Stahlbandes aus einem höchstfesten Mehrphasenstahl

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100003161A1 (en) * 2002-06-19 2010-01-07 Nippon Steel Corporation Steel for Crude Oil Tank, Method for Producing the Same, Crude Oil Tank and Corrosion Prevention Method Thereof

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102020110319A1 (de) 2020-04-15 2021-10-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit einem Mehrphasengefüge und Stahlband hinzu

Also Published As

Publication number Publication date
RU2015101783A (ru) 2016-08-20
DE102012013113A1 (de) 2013-12-24
WO2013189474A1 (fr) 2013-12-27
EP2864517A1 (fr) 2015-04-29
US20150337408A1 (en) 2015-11-26
KR20150023567A (ko) 2015-03-05
KR102079611B1 (ko) 2020-04-07
RU2627068C2 (ru) 2017-08-03

Similar Documents

Publication Publication Date Title
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
EP2809819B1 (fr) Acier multiphases très résistant, aux propriétés améliorées lors de sa fabrication et de son traitement
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
EP2836614B1 (fr) Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier
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
EP2366035B1 (fr) Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication
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
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
WO2017009192A1 (fr) Acier multiphase à haute résistance et procédé de fabrication d'une bande d'acier laminée à froid composée dudit 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
EP3692178B1 (fr) Procede de fabrication d'une bande d'acier a partir d'un acier multiphase a tres haute resistance
EP3535431B1 (fr) Produit d'acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication
EP4136265A1 (fr) Procédé de fabrication d'une bande d'acier à structure multiphasée et bande d'acier associée
DE102021108448A1 (de) Stahlband aus einem hochfesten Mehrphasenstahl und Verfahren zur Herstellung eines derartigen Stahlbandes

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: 20141205

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

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: 502013014245

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0038020000

Ipc: C21D0001740000

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: C21D 1/74 20060101AFI20190724BHEP

Ipc: C21D 8/02 20060101ALI20190724BHEP

Ipc: C22C 38/04 20060101ALI20190724BHEP

Ipc: C22C 38/18 20060101ALI20190724BHEP

Ipc: C22C 38/02 20060101ALI20190724BHEP

Ipc: C21D 6/00 20060101ALI20190724BHEP

Ipc: C21D 9/52 20060101ALI20190724BHEP

Ipc: C22C 38/06 20060101ALI20190724BHEP

Ipc: C23C 2/06 20060101ALI20190724BHEP

Ipc: C21D 11/00 20060101ALI20190724BHEP

Ipc: C22C 38/00 20060101ALI20190724BHEP

Ipc: C22C 38/22 20060101ALI20190724BHEP

Ipc: C21D 1/84 20060101ALI20190724BHEP

Ipc: C22C 1/02 20060101ALI20190724BHEP

Ipc: C22C 38/38 20060101ALI20190724BHEP

Ipc: C22C 38/26 20060101ALI20190724BHEP

INTG Intention to grant announced

Effective date: 20190822

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: 1226936

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200215

REG Reference to a national code

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: DE

Ref legal event code: R096

Ref document number: 502013014245

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20200122

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: 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: 20200122

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: 20200422

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: 20200614

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: 20200122

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: 20200122

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

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: 20200122

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: 20200423

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: 20200422

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: 20200122

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: 20200522

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: 20200122

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502013014245

Country of ref document: DE

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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

26N No opposition filed

Effective date: 20201023

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: 20200531

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: 20200122

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: 20200122

Ref country code: CH

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

Effective date: 20200531

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

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: 20200122

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: 20200122

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200531

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

Effective date: 20200524

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: 20200524

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

Ref country code: IE

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

Effective date: 20200524

Ref country code: GB

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

Effective date: 20200524

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: 20200531

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 1226936

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200524

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: 20200524

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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: 20200122

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

Ref country code: FR

Payment date: 20230526

Year of fee payment: 11

Ref country code: DE

Payment date: 20230519

Year of fee payment: 11