EP2767602B1 - Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung - Google Patents

Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung Download PDF

Info

Publication number
EP2767602B1
EP2767602B1 EP13155226.7A EP13155226A EP2767602B1 EP 2767602 B1 EP2767602 B1 EP 2767602B1 EP 13155226 A EP13155226 A EP 13155226A EP 2767602 B1 EP2767602 B1 EP 2767602B1
Authority
EP
European Patent Office
Prior art keywords
cold
annealing
content
rolled
hot
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
EP13155226.7A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP2767602A1 (de
Inventor
Dorothée Dr. Dorner
Christian Höckling
Harald Dr.-Ing. Hofmann
Magnus Miller
Matthias Dipl.-Ing. Schirmer
Jonas Dipl.-Ing. Schwabe
Alexander Dipl.-Ing. Zimmermann
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel Europe AG
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
Priority to ES13155226T priority Critical patent/ES2736303T3/es
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to EP13155226.7A priority patent/EP2767602B1/de
Priority to PL13155226T priority patent/PL2767602T3/pl
Priority to PCT/EP2014/052811 priority patent/WO2014125017A1/de
Priority to KR1020157024980A priority patent/KR20150119231A/ko
Priority to CN201480022034.9A priority patent/CN105121674B/zh
Priority to US14/767,770 priority patent/US10131976B2/en
Priority to BR112015019535-0A priority patent/BR112015019535B1/pt
Priority to JP2015557423A priority patent/JP6388881B2/ja
Publication of EP2767602A1 publication Critical patent/EP2767602A1/de
Application granted granted Critical
Publication of EP2767602B1 publication Critical patent/EP2767602B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following 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
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Definitions

  • the invention relates to a cold-rolled steel flat product for thermoforming applications, which has a reduced weight as a result of a density reduction with optimized mechanical properties and an optimized deformability. Likewise, the invention relates to a method for producing such a flat steel product.
  • Al-containing deep-drawing steels may contain a maximum of 6.5% by weight of Al (cf. U. Brüx "Thermoformable iron-aluminum lightweight steels", construction April 4, 2002 ).
  • the steel sheet is made of a steel containing (in% by weight) 0.001-0.01% C, ⁇ 3.0% Si,> 0.2-3.0% Mn, ⁇ 0.02% P, ⁇ 0 , 02% S, 5.0-10.0% Al, 0.001-0.05% N, and the remainder contains Fe and unavoidable impurities, the Mn and S content of the slab having the condition up to 20 ⁇ (Mn / S).
  • rare earth metals may be present in the alloy of the steel to aid in the desulfurization of the steel by sulfide formation.
  • this known steel sheet consists of a steel containing (in% by weight) ⁇ 0.01% C, 0.01-2.0% Si, 0.05-2.5% Mn, ⁇ 0.02% P , 5 - 10% Al, ⁇ 0.010% S and ⁇ 0.010% N, balance iron and unavoidable impurities.
  • ⁇ 0.01% C, 0.01-2.0% Si, 0.05-2.5% Mn, ⁇ 0.02% P 5 - 10% Al, ⁇ 0.010% S and ⁇ 0.010% N, balance iron and unavoidable impurities.
  • Ti, Nb, Mo and V in total 0.01-0.2% by weight of La, Ce, Nd and Y, 1-8% Cr and 0.0002 - 0.002% B be present in the steel.
  • the Rare earth metals should form a protective Al oxide film on the surface of the flat steel product to ensure high resistance of the steel sheet to high temperature oxidation.
  • the object of the invention was to provide a flat steel product which, with a significant weight reduction, has optimized deformation suitability and likewise optimized mechanical properties.
  • this object is achieved with regard to the cold-rolled flat steel product by providing a product having the features specified in claim 1.
  • a cold-rolled steel flat product according to the invention for deep-drawing applications consists of a steel which, in addition to iron and unavoidable impurities (in% by weight) C: up to 0.1%, Al: 6.5-11%, at least one rare earth metal from the group "Ce "La” with the proviso the content of rare earth metals is 0.02-0.2%, P: up to 0.1%, S: up to 0.03%, N: up to 0.1%, and optionally one or more elements from the group "Mn, Si, Nb, Ti, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" with the proviso contains, Mn: up to 6%, Si: up to 1%, Nb: up to 0.3%, Ti: up to 0.3%, Zr: up to 1%, V: up to 1%, W: up to 1%, Mo: up to 1%, Cr: up to 3%, Co: up to 1%, Ni: up to 2%, B: up to 0.1%, Cu: up
  • the cold rolled flat steel product according to the invention has an r-value which is at least 1, and a structure which is largely free of ⁇ -carbides. Accordingly, the ⁇ -carbide content of a flat steel product according to the invention is from 0% by volume (completely ⁇ -carbide-free state) to at most 0.1% by volume. Due to the minimized ⁇ -carbide content, the processability of the flat steel product according to the invention is reliably ensured.
  • the steel processed according to the invention contains at least 6.5-11% Al, up to 0.1% C and a content of 0.02-0.2% of one or more Elements of the group of rare earth metals.
  • the cold-rolled steel strip according to the invention is distinguished by r values of at least 1, with flat steel products according to the invention regularly achieving r values greater than 1.
  • the high r-value stands for a good thermoformability of the cold-rolled flat steel product according to the invention, since with increasing r-value, the tendency to thinning during deep drawing is reduced and, consequently, greater degrees of deep drawing are made possible. Otherwise there would be a risk of component failure at the thinned area.
  • a cold-rolled flat steel product according to the invention not only has high r values, but also achieves an elongation A50 of regularly more than 15%, in particular at least 18%. It is characteristic of the structure of a flat steel product according to the invention that it is completely ferritic and, as stated above, typically largely free of ⁇ -carbides (Fe-Al-C-carbides).
  • the high aluminum content of flat steel products according to the invention causes not only a decrease in density and weight but also an increase in the energy absorption capacity and, consequently, an improvement in the crash behavior.
  • the invention provides such reduced-density flat steel products with improved crash properties and a comparatively high modulus of elasticity, which can be produced in a simple manner and offer optimum conditions for use in vehicle construction.
  • the steel according to the invention may contain a large number of further alloying elements in order to set certain properties.
  • the relevant elements are summarized in the group "Mn, Si, Nb, Ti, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N".
  • Each of these optionally added Alloying elements can be present in the steel according to the invention or completely absent, wherein the respective element is to be regarded as "not present” if it is present in the steel flat product according to the invention in an amount in which it is ineffective and therefore attributable to the production-unavoidable impurities.
  • Aluminum is present in the steel of the present invention at levels of 6.5-11 wt.%, With Al contents of greater than 6.5 wt.%, More preferably greater than 6.7 wt.% Or greater than 7 wt. -%, are advantageous in view of the desired density reduction.
  • the presence of high Al contents reduces the density of the steel and significantly improves its corrosion and oxidation resistance.
  • Al increases the tensile strength at these levels.
  • excessive contents of Al can lead to a deterioration of the forming behavior, which is expressed in a decrease in the r value.
  • the Al content is limited to a maximum of 11 wt .-%.
  • An optimally balanced ratio of reduced density and processability arises when 8-11 wt.% Al, in particular at least 9 wt.% Al, are present in the steel according to the invention.
  • the C content in steel according to the invention is limited to at most 0.1% by weight, in particular 0.07% by weight, low C contents of less than 0.05%, in particular 0.01% by weight, or less, especially cheap. Above 0.1 wt.% C contents, the formation of undesirable brittle kappa carbides (" ⁇ carbides”) on the Grain limits and a consequent reduction in hot and cold workability cause. In practice, it has proven expedient in this regard to adjust the C content of the steel according to the invention in the range of up to 0.05% by weight, with a steel according to the invention typically containing up to 0.008% by weight.
  • ⁇ -carbides Fe-Al-C compounds
  • ⁇ -carbides are formed early in the processing of generic steels during hot processing at high temperatures on the grain boundaries and cause embrittlement of the material.
  • the steel according to the invention comprises at least one element from the group of rare earth metals in amounts of 0.02-0.2% by weight, in particular up to 0.15 Wt .-%, wherein the rare earth metal content is typically at least 0.03 wt .-%.
  • Cerium and lanthanum are comparably inexpensive and available in sufficient quantities.
  • the presence of rare earth metals contributes to improved oxidation resistance and strength of a flat steel product according to the invention and acts desulfurizing as well as deoxidizing.
  • rare earth metals can be particularly targeted in the steel according to the invention, when the contents of rare earth metals are at least 0.03 wt .-%, wherein in the range of 0.06 - 0.12 wt .-%, in particular 0.06 - 0.10 wt .-%, lying rare earth
  • the S content to a maximum of 0.03 wt .-%, preferably at most 0.01 wt .-%, and the P content to a maximum of 0 , 1 wt .-%, preferably at most 0.05 wt .-%, limited.
  • the N content of the flat steel product according to the invention is limited to at most 0.1% by weight, in particular at most 0.02% by weight, preferably at most 0.001% by weight, in order to avoid the formation of relatively large amounts of Al nitrides. These would degrade the mechanical properties.
  • Ti, Nb, V, Zr, W and Mo can each be added individually or in different combinations to the steel according to the invention as carbide formers in order to bind off the existing C content.
  • carbides formed by the addition of one or more of the elements Ti, Nb, V, Zr, W, Mo additionally contribute to increasing the strength of the steel according to the invention.
  • Ti and Nb in amounts of up to 0.3 wt .-%, in particular in each case up to 0.1 wt .-%, V, W and Zr in amounts of up to 1 wt .-%, in particular in each case up to 0.5% by weight, and Mo in contents of up to 1% by weight in the steel according to the invention.
  • Mo also contributes to increasing the tensile strength, creep resistance and fatigue strength of a flat steel product of the present invention.
  • the carbides formed by Mo with C are particularly fine and thus improve the fineness of the structure of the flat steel product according to the invention. High levels of Mo, however, degrade the hot and cold workability. In order to avoid this particularly reliably, the optionally present Mo content of a steel according to the invention can be limited to 0.5% by weight.
  • Mn By adding Mn in amounts of up to 6% by weight, in particular up to 3% by weight or up to 1% by weight, the hot workability and weldability of the steel according to the invention can be improved.
  • Mn aids in deoxidation during melting and contributes to increasing the strength of the steel.
  • Si in amounts of up to 1 wt .-%, in particular up to 0.5 wt .-%, supported during the melting also the deoxidation and increases the strength and corrosion resistance of the steel according to the invention. At too high a content, however, the presence of Si reduces the ductility of the steel and its weldability.
  • the Co content of the steel according to the invention is limited to max. 1% by weight, preferably max. 0.5% by weight, limited.
  • B can also lead to the formation of a fine, the deformability of the steel according to the invention favoring structure.
  • excessive contents of B may impair cold workability and oxidation resistance. Therefore, the B content of the steel of the present invention is limited to 0.05% by weight, especially up to 0.01% by weight.
  • Cu in amounts of up to 3% by weight improves corrosion resistance in the steel of the present invention, but at higher levels may also deteriorate hot workability and weldability. If present, therefore, the Cu content in a practical embodiment of the invention is limited to at most 1 wt .-%.
  • oxygen is taken up in the steel according to the invention and forms precipitates with the rare earth metals present in the strip. If the rare earth metal is Ce, then cerium oxide precipitates are present in the steel flat product produced according to the invention.
  • strip casting Another positive aspect of strip casting is the fact that the cast strip is exposed to at most low mechanical stresses until it cools, so that the risk of cracking in the high-temperature region is minimized.
  • a waiting time of at least about 15 minutes should elapse between the last addition of alloy and the casting, in order to ensure thorough mixing of the molten steel.
  • Typical effluent temperatures are in the range of about 1590 ° C.
  • the hot-rolled strip can be cold-rolled despite its high Al contents, without severe edge tears or even ribbon tears occurring.
  • the hot strip annealing serves to produce a sufficiently recrystallized recovered core band area, lowering the cold rolling resistance and increasing the maximum achievable degree of cold rolling.
  • a texture selection effected by the hot-band annealing and a high degree of cold deformation promote the formation of a suitable cold-rolled texture with the desired property profile.
  • the hot strip annealing in particular the crucible annealing process with peak temperatures above 650 ° C. set in accordance with the variants explained above is suitable.
  • inventive melts E1, E2, E3, E4 and three comparative melts V1, V2, V3, have been melted, whose compositions are given in Table 1.
  • the steel melts E1 - E3 have been cast into precursors in the form of blocks.
  • the blocks have then been heated through a preheating period VD to a preheating temperature VT and converted into slabs.
  • the reheated slabs are hot rolled at a hot rolling end temperature WET to a hot strip and the resulting hot strip was wound at a reel temperature HT in each case into a coil.
  • a cast strip was produced as a precursor via a two-roll strip casting plant, which was then also hot-rolled into a hot strip with a hot rolling end temperature WET.
  • the processing to the hot strip was carried out in a continuous process sequence without interruption following the strip casting, so that the precursor already had a temperature lying in the range of inventively predetermined preheating temperatures when entering the hot rolling device and the preheating could be omitted.
  • the hot strip produced from the steel E4 has been coiled after hot rolling at a reel temperature HT to form a coil.
  • the so annealed hot strips were cold rolled with a cold rolling grade KWG each to a cold rolled steel strip.
  • the resulting cold-rolled steel strips were then each subjected to a final annealing at a final annealing temperature SGT and a final annealing time SGD.
  • the final annealing has been carried out either as a continuous annealing or as a bell annealing.
  • the cold-rolled steel strips produced from the steels E1-E4 produced according to the invention in accordance with the invention have yield strengths which are regularly greater than 400 MPa, in particular greater than 420 MPa and thereby reach values of 500 MPa and more, and tensile strengths which are regularly greater 500 MPa, in particular greater than 520 MPa, while achieving values of 600 MPa and more, and having elongation values A50 of at least 16%, always having r values of 1 or greater.
  • the cold-rolled steel strips produced from the steels according to the invention in a manner according to the invention contain, in addition to a Fe (Al) mixed-crystal matrix, a hardening precursor state.
  • a hardening precursor state In common hot rolling parameters, rolling is carried out in the fully ferrite phase region and hot strip is obtained with a typical three-layer structure, the again characterized by recrystallized globulitic margins and the only recovered core region with stem crystals.
  • a texture favorable for thermoformability which ensures r values of more than 1 is achieved here. At rare earth metal contents below 200 ppm, this effect does not occur, which can be used particularly reliably with rare-earth metal contents of at least 300 ppm.
  • the hot strip annealing performed according to the invention reduces the dislocation density in the recovered area and facilitates subsequent cold rolling processing.
  • the hot strips which are assembled according to the invention are not only hot-rollable in the full-ferrite phase region, but can be cold-rolled in spite of the existence of the Fe3Al intermetallic phase at room temperature, in contrast to the non-inventive rare earth-metal steels V1-V3.
  • suitable final annealing parameters an extremely solid and density-reduced steel can be produced, which has high r-values and correspondingly optimized forming properties.
  • Cold-rolled steel strips not assembled according to the invention do not achieve such r-values even if these steel strips have been produced taking into account production parameters that are closely related to the parameters set in the production of the cold-rolled steel flat products according to the invention. Accordingly, the steel strips produced according to the invention have, despite their high Al contents, a superior deep-drawing capability, without the need for elaborate alloying or process technology Measures are required.
  • the cold-rolled steel strips produced from the steels V1, V2, V3 which are not composed according to the invention also contain a hardening precursor state in addition to a Fe (Al) mixed-crystal matrix. A hot strip annealing also facilitates cold rolling processing here.
  • the cold-rolled steel strips not assembled according to the invention do not achieve the r-values required for a good deep drawing behavior.
  • precursors produced from the non-inventive steel S3 are hot-rollable in the fully ferrite phase region, they can not be cold-cracked at room temperature due to the existence of the intermetallic phase Fe3Al.
  • Table 1 stolen C Si Mn P S Cr Mo Ni al Ce La Ce + La N Ti Nb V E1 0,008 0.09 0.15 0,003 0.005 0.01 0.00 0.01 8.20 0.073 0,040 .1130 0.0032 0.001 0,003 0,002 E2 0,007 0.09 0.25 0,003 0.005 0.40 0.01 0.02 8.30 0.048 0.019 0.0670 0.0510 0,003 0,002 0,002 E3 0,004 0.09 0.15 0,003 0,004 0.01 0.00 0.01 10.10 0.067 0.034 .1010 0.0048 0.001 0.001 0,003 E4 0.026 0.43 0.38 0.011 ⁇ 0.001 1.16 0.06 0.35 6.7 0.0258 0.0152 0.0410 0.0009 0.22 0.12 0.009 V1 0,004 0.14 0.09 0,007 0,003 0.04 0.00 0.03 8.10 0.0004 0.0002 0.0006 0.0048 0,004 0,004 0.016 V2 0.005 0.11 0.11

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)
  • Heat Treatment Of Sheet Steel (AREA)
EP13155226.7A 2013-02-14 2013-02-14 Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung Active EP2767602B1 (de)

Priority Applications (9)

Application Number Priority Date Filing Date Title
EP13155226.7A EP2767602B1 (de) 2013-02-14 2013-02-14 Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung
PL13155226T PL2767602T3 (pl) 2013-02-14 2013-02-14 Walcowany na zimno płaski wyrób stalowy do zastosowań w głębokim tłoczeniu i sposoby jego wytwarzania
ES13155226T ES2736303T3 (es) 2013-02-14 2013-02-14 Producto plano de acero laminado en frío para aplicaciones de embutición profunda y procedimiento para su fabricación
KR1020157024980A KR20150119231A (ko) 2013-02-14 2014-02-13 딥드로잉 적용을 위한 냉간압연 평강 제품 및 그 제조 방법
PCT/EP2014/052811 WO2014125017A1 (de) 2013-02-14 2014-02-13 Kaltgewalztes stahlflachprodukt für tiefziehanwendungen und verfahren zu seiner herstellung
CN201480022034.9A CN105121674B (zh) 2013-02-14 2014-02-13 用于深冲应用的冷轧扁平钢产品及其制造方法
US14/767,770 US10131976B2 (en) 2013-02-14 2014-02-13 Cold-rolled flat steel product for deep drawing applications and method for production thereof
BR112015019535-0A BR112015019535B1 (pt) 2013-02-14 2014-02-13 Produto de aço laminado a frio para estampagem profunda
JP2015557423A JP6388881B2 (ja) 2013-02-14 2014-02-13 深絞り加工に用いる冷間圧延平鋼製品及びその製造方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP13155226.7A EP2767602B1 (de) 2013-02-14 2013-02-14 Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung

Publications (2)

Publication Number Publication Date
EP2767602A1 EP2767602A1 (de) 2014-08-20
EP2767602B1 true EP2767602B1 (de) 2019-04-17

Family

ID=47757330

Family Applications (1)

Application Number Title Priority Date Filing Date
EP13155226.7A Active EP2767602B1 (de) 2013-02-14 2013-02-14 Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung

Country Status (9)

Country Link
US (1) US10131976B2 (pl)
EP (1) EP2767602B1 (pl)
JP (1) JP6388881B2 (pl)
KR (1) KR20150119231A (pl)
CN (1) CN105121674B (pl)
BR (1) BR112015019535B1 (pl)
ES (1) ES2736303T3 (pl)
PL (1) PL2767602T3 (pl)
WO (1) WO2014125017A1 (pl)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102015116186A1 (de) 2015-09-24 2017-03-30 Thyssenkrupp Ag Halbzeug und Verfahren zur Herstellung einer Fahrzeugkomponente, Verwendung eines Halbzeugs und Fahrzeugkomponente
DE102016211411A1 (de) * 2016-06-24 2017-12-28 Thyssenkrupp Ag Fahrzeugrad und Verwendung
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
DE102017201068A1 (de) * 2017-01-24 2018-07-26 Thyssenkrupp Ag Fahrzeugrahmen und Verwendung
CN107254636B (zh) * 2017-05-02 2019-02-22 嘉禾福顺机械实业有限公司 一种泵用合金钢材料及其制备方法
CN113684413B (zh) * 2020-05-18 2022-06-28 宝山钢铁股份有限公司 一种深冲内胆用冷轧搪瓷钢及其制造方法

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1044801A (en) * 1963-01-30 1966-10-05 Yawata Iron & Steel Co Improvements in or relating to aluminum steels
US4334923A (en) * 1980-02-20 1982-06-15 Ford Motor Company Oxidation resistant steel alloy
DE19634524A1 (de) * 1996-08-27 1998-04-09 Krupp Ag Hoesch Krupp Leichtbaustahl und seine Verwendung für Fahrzeugteile und Fassadenverkleidungen
JP3790398B2 (ja) 1999-12-10 2006-06-28 新日本製鐵株式会社 加工部断面耐食性に優れた被覆鋼
JP4458610B2 (ja) 2000-03-27 2010-04-28 日新製鋼株式会社 耐高温酸化性に優れた溶融アルミニウムめっき鋼板
JP2001271148A (ja) * 2000-03-27 2001-10-02 Nisshin Steel Co Ltd 耐高温酸化性に優れた高Ａｌ鋼板
JP4472015B2 (ja) * 2003-06-18 2010-06-02 新日本製鐵株式会社 延性に優れた高強度低比重鋼板およびその製造方法
JP4324072B2 (ja) * 2004-10-21 2009-09-02 新日本製鐵株式会社 延性に優れた軽量高強度鋼とその製造方法
JP4797807B2 (ja) 2006-05-30 2011-10-19 Ｊｆｅスチール株式会社 高剛性低密度鋼板およびその製造方法
EP1995336A1 (fr) * 2007-05-16 2008-11-26 ArcelorMittal France Acier à faible densité présentant une bonne aptitude à l'emboutissage
CN101082107B (zh) * 2007-06-29 2010-06-16 武汉钢铁(集团)公司 超低碳冷轧深冲搪瓷钢及其生产方法

Non-Patent Citations (1)

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

Also Published As

Publication number Publication date
WO2014125017A1 (de) 2014-08-21
PL2767602T3 (pl) 2019-10-31
CN105121674A (zh) 2015-12-02
EP2767602A1 (de) 2014-08-20
ES2736303T3 (es) 2019-12-27
JP2016513178A (ja) 2016-05-12
JP6388881B2 (ja) 2018-09-12
BR112015019535B1 (pt) 2020-09-15
CN105121674B (zh) 2018-08-28
BR112015019535A2 (pt) 2017-07-18
US10131976B2 (en) 2018-11-20
KR20150119231A (ko) 2015-10-23
US20150376751A1 (en) 2015-12-31

Similar Documents

Publication Publication Date Title
EP2767601B1 (de) Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung
EP1309734B1 (de) Höherfester, kaltumformbarer stahl und stahlband oder -blech, verfahren zur herstellung von stahlband und verwendungen eines solchen stahls
DE10259230B4 (de) Verfahren zum Herstellen eines Stahlprodukts
EP1918406B1 (de) Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Bor mikrolegierten Mehrphasenstahl
EP2767602B1 (de) Kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen und Verfahren zu seiner Herstellung
EP1918402B1 (de) Verfahren zum Herstellen von Stahl-Flachprodukten aus einem ein Komplexphasen-Gefüge bildenden Stahl
DE69935125T2 (de) Hochfestes, kaltgewalztes stahlblech und verfahren zu dessen herstellung
EP1807542A1 (de) Höherfestes, twip-eigenschaften aufweisendes stahlband oder -blech und verfahren zu dessen herstellung mittels "direct strip casting "
WO2010029012A1 (de) Nichtrostender stahl, aus diesem stahl hergestelltes kaltband und verfahren zur herstellung eines stahlflachprodukts aus diesem stahl
DE60207591T2 (de) Verfahren zur herstellung von geschweissten röhren und dadurch hergestelltes rohr
EP2840159B1 (de) Verfahren zum Herstellen eines Stahlbauteils
WO2008052918A1 (de) Verfahren zum herstellen von stahl-flachprodukten aus einem ein martensitisches gefüge bildenden stahl
WO2015117934A1 (de) Hochfestes stahlflachprodukt mit bainitisch-martensitischem gefüge und verfahren zur herstellung eines solchen stahlflachprodukts
DE102015111866A1 (de) Umformbarer Leichtbaustahl mit verbesserten mechanischen Eigenschaften und Verfahren zur Herstellung von Halbzeug aus diesem Stahl
EP1918405B1 (de) Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Silizium legierten Mehrphasenstahl
DE69230447T2 (de) Hochfeste,kaltgewalzte stahlplatte mit exzellenter umformbarkeit,feurverzinktes,kaltgewalztes stahlblech und verfahren zur herstellung dieser bleche
EP1399598B1 (de) Verfahren zum herstellen von hochfesten, aus einem warmband kaltverformten stahlprodukten mit guter dehnbarkeit
EP3658307B9 (de) Blechbauteil, hergestellt durch warmumformen eines stahlflachprodukts und verfahren zu dessen herstellung
EP1398390B1 (de) Ferritisch/martensitischer Stahl mit hoher Festigkeit und sehr feinem Gefüge
EP3847284B1 (de) Warmgewalztes stahlflachprodukt und verfahren zu seiner herstellung
EP1918404B1 (de) Verfahren zum Herstellen von Stahl-Flachprodukten aus einem mit Aluminium legierten Mehrphasenstahl
EP3771746A1 (de) Stahl, stahlflachprodukt, verfahren zur herstellung eines stahlflachprodukts und verwendung
EP3405593B1 (de) Stahlflachprodukt und verfahren zu seiner herstellung
WO2017211952A1 (de) Verfahren zur herstellung eines kaltgewalzten stahlbandes mit trip-eigenschften aus einem hochfesten, manganhaltigen stahl
EP1411140B1 (de) Verfahren zum Herstellen eines besonders gut verformbaren kaltgewalzten Stahlbands oder -blechs

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: 20130214

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

R17P Request for examination filed (corrected)

Effective date: 20150220

RBV Designated contracting states (corrected)

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

17Q First examination report despatched

Effective date: 20160909

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

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 8/04 20060101AFI20180927BHEP

Ipc: C22C 38/00 20060101ALI20180927BHEP

Ipc: C21D 9/48 20060101ALI20180927BHEP

Ipc: C22C 38/06 20060101ALI20180927BHEP

INTG Intention to grant announced

Effective date: 20181030

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: DE

Ref legal event code: R096

Ref document number: 502013012632

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1121610

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190515

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: FP

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

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: 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: 20190417

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: 20190817

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: 20190717

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: 20190417

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: 20190417

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

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: 20190718

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: 20190417

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: 20190417

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: 20190717

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2736303

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20191227

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

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: 20190817

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502013012632

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: 20190417

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: 20190417

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: 20190417

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: 20190417

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: 20190417

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

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

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: 20190417

26N No opposition filed

Effective date: 20200120

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: 20190417

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

Ref country code: IT

Payment date: 20200224

Year of fee payment: 8

Ref country code: GB

Payment date: 20200218

Year of fee payment: 8

Ref country code: SE

Payment date: 20200219

Year of fee payment: 8

Ref country code: FI

Payment date: 20200220

Year of fee payment: 8

Ref country code: ES

Payment date: 20200320

Year of fee payment: 8

Ref country code: NL

Payment date: 20200218

Year of fee payment: 8

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: 20190417

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

Ref country code: BE

Payment date: 20200221

Year of fee payment: 8

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

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: 20200214

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: 20190417

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: IE

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

Effective date: 20200214

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

Ref country code: PL

Payment date: 20210209

Year of fee payment: 9

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

REG Reference to a national code

Ref country code: FI

Ref legal event code: MAE

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

Effective date: 20210214

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20210228

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 NON-PAYMENT OF DUE FEES

Effective date: 20210214

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

Ref country code: SE

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

Effective date: 20210215

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20210301

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 NON-PAYMENT OF DUE FEES

Effective date: 20210301

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: 20210214

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 NON-PAYMENT OF DUE FEES

Effective date: 20210214

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

Ref country code: DE

Payment date: 20220222

Year of fee payment: 10

Ref country code: AT

Payment date: 20220223

Year of fee payment: 10

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20220513

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

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: 20190417

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: 20190417

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

Ref country code: FR

Payment date: 20220222

Year of fee payment: 10

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: 20190417

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

Ref country code: ES

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

Effective date: 20210215

Ref country code: BE

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

Effective date: 20210228

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502013012632

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 1121610

Country of ref document: AT

Kind code of ref document: T

Effective date: 20230214

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: 20230214

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

Ref country code: FR

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

Effective date: 20230228

Ref country code: DE

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

Effective date: 20230901

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 NON-PAYMENT OF DUE FEES

Effective date: 20220214