EP3225702A1 - Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier - Google Patents

Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier Download PDF

Info

Publication number
EP3225702A1
EP3225702A1 EP16162652.8A EP16162652A EP3225702A1 EP 3225702 A1 EP3225702 A1 EP 3225702A1 EP 16162652 A EP16162652 A EP 16162652A EP 3225702 A1 EP3225702 A1 EP 3225702A1
Authority
EP
European Patent Office
Prior art keywords
steel
content
weight
flat
product
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.)
Granted
Application number
EP16162652.8A
Other languages
German (de)
English (en)
Other versions
EP3225702B1 (fr
Inventor
Hans-Günter KRULL
Frank van Soest
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.)
Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
Original Assignee
Deutsche Edelstahlwerke 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 Deutsche Edelstahlwerke GmbH filed Critical Deutsche Edelstahlwerke GmbH
Priority to ES16162652T priority Critical patent/ES2791887T3/es
Priority to EP16162652.8A priority patent/EP3225702B1/fr
Priority to US16/089,616 priority patent/US20190119771A1/en
Priority to PCT/EP2017/057359 priority patent/WO2017167778A1/fr
Publication of EP3225702A1 publication Critical patent/EP3225702A1/fr
Application granted granted Critical
Publication of EP3225702B1 publication Critical patent/EP3225702B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • 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
    • C21D8/0231—Warm 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
    • 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
    • C22C38/02—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • 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
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to a steel with a reduced density due to its high Al content and to a process for producing a flat or long product from such a steel.
  • references to alloying rules or compositions of materials refer to "%", which always refers to weight. If, on the other hand, information is given on the proportions of certain microstructural constituents, these always refer to the respective volume considered.
  • flat steel product or “flat product” are referred to herein rolled products whose thickness is much smaller than their length and width.
  • the flat steel products or flat products in question are sheets, strips or boards obtained from these sheets or strips.
  • long products of steel or “long products” refer to products obtained by forming a precursor whose length is significantly greater than their width and thickness but which are usually of comparable width and thickness.
  • Typical examples of long products are bars, bars, profiles and the like.
  • aluminum is one of the elements that has a ferrite-stabilizing effect and can even completely suppress the austenite-ferrite transformation.
  • the object of the invention was to provide a density-reduced iron-based material whose mechanical properties make it suitable for a wide range of applications Make the range of applications particularly suitable in the automotive industry.
  • the invention has achieved the object mentioned above in that the processing steps specified in claim 9 are used in the processing of steels according to the invention into flat or long products.
  • the required strength of more than 500 MPa is formed in addition to the known mixed crystal strengthening elements chromium, molybdenum, silicon and manganese via precipitation phases. These phases are predominantly excreted intracrystalline.
  • Strength-enhancing intermetallic phases such as the Laves phase, consist essentially of iron, titanium and optionally of molybdenum, Ni (Mn, Al, Ti), Ni 2 MnAl, Ni 3 Ti and Cu. But also fine carbides, fine nitrides and fine carbonitrides make a contribution to the strength level.
  • alloying with carbon according to the invention was largely dispensed with alloying with carbon and the freedom of conversion was accepted.
  • the carbon and nitrogen contents in the steel according to the invention are instead limited to the lowest possible values such that at most isolated carbides or carbonitrides are formed upon solidification.
  • the C content of the steel according to the invention is at most 0.2% by weight.
  • the formation of undesirable carbides can be prevented particularly reliably if the C content is less than 0.1% by weight, in particular not more than 0.02% by weight or not more than 0.01% by weight.
  • the N content is limited to not more than 0.020% by weight, in particular not more than 0.005% by weight.
  • the Al content of steels according to the invention is 6 to 25% by weight, in particular at least 10% by weight.
  • the invention provides that the contents of Cr, Mo, Mn, Si, V, W, Ni, Nb, Ti satisfy the following conditions: (% Cr + 2 *% Mo +% Mn +% Si +% V +% W +% Ni +% Nb +% Ti)> 0.05 *% Al with% Cr: Cr content of the steel,% Mo: Mo content of the steel,% Mn: Mn content of the steel,% Si: Si content of the steel,% V: V content of the steel,% W: W Content of Steel,% Ni: Ni content of the steel,% Nb: Nb content of the steel,% Ti: Ti content of the steel, and% Al: Al content of the steel.
  • Sulfur may be added to the steel of the present invention to improve its machinability in levels of up to 0.40 weight percent, with optimum effects at levels of up to 0.28 weight percent.
  • the S content of a steel according to the invention can be set to at least 0.01% by weight.
  • the strength of the material can be adjusted.
  • this effect of Ti can be achieved particularly reliably by the presence of at least 0.60% by weight of Ti in the steel according to the invention.
  • Optimum effects of Ti result when the Ti content is at least 0.90 wt% or at most 2.0 wt%.
  • Chromium in amounts of up to 6.0 wt .-% contributes to the avoidance of the superstructure D03 and solid solution hardening.
  • the Cr content can be set to at least 0.30% by weight. Optimal effects arise when at least 0.50 wt .-% or at most 3.5 wt .-% Cr in the steel according to the invention are present.
  • Mo at levels of up to 3.0% by weight assists in avoiding superstructure D03, contributes to solid solution strengthening, and promotes the formation of desired precipitates.
  • the Mo content can be set to at least 0.1 wt .-%, with optimum effects of the presence of Mo in the steel according to the invention occur when its Mo content is at least 0.25 wt .-% or at most 2.8 wt .-%.
  • V is present in amounts of up to 1.0% by weight in the steel according to the invention, superstructure D03 can likewise be avoided.
  • the V content can be set to at least 0.10 wt%, with optimum effects of the presence of V in the inventive steel when its V content is at least 0.20 or at most 0.50 wt .-% is.
  • Tungsten at levels of up to 1.0% by weight also has a positive effect on avoiding superstructure D03.
  • the W content can be set to at least 0.20% by weight.
  • Optimum effects result when at least 0.40 wt .-% or at most 1.0 wt .-% W are present in the steel according to the invention. If W is to be added as an alternative to Mo, twice as much tungsten as molybdenum must be added to achieve the same effectiveness.
  • Copper in amounts of up to 4 wt .-% causes in the steel of the invention that the strength is increased over copper precipitates. This effect can be safely used, that the Cu content is at least 0.5 wt .-%, with contents of at most 3.50 wt .-% have been found to be particularly positive. In order to ensure hot workability, approximately the same amount of nickel should be added to the material.
  • the addition of up to 0.08% by weight of boron in the steel according to the invention can suppress the precipitation behavior of the hardening phases on the grain boundaries. This can certainly be achieved by the presence of at least 0.0005% by weight of B in the steel according to the invention. B contents of By contrast, more than 0.08% by weight have a negative effect on the formability of the steel. To avoid this, the B content of the steel according to the invention can be limited to at most 0.0030% by weight.
  • Nb is present in amounts of up to 1.5% by weight in the steel according to the invention, Nb also contributes to the avoidance of the superstructure D03 and strength-increasing precipitation phases are formed.
  • the Nb content can be set to at least 0.05% by weight, with optimum effects of the presence of Nb in the steel of the present invention if its Nb content is at least 0.10% by weight or more 0.30 wt .-% is.
  • the matrix of the steel according to the invention is largely, i. at least 85% by volume of ferrite, with higher ferrite contents of at least 90% by volume being particularly favorable.
  • austenite content of up to 10% by volume in the microstructure can also have a positive effect on the toughness of the steel. Therefore, it may be expedient to adjust the alloy of the steel according to the invention so that at least 2% by volume of austenite are present in the structure of the steel. If the austenite content is greater than 10% by volume, this has a negative effect on the precipitation behavior of the intermetallic phases.
  • the remaining constituents not taken up by ferrite or austenite are contents of intermetallic phases as well as fractions of carbide, nitride, bainite or perlite.
  • the proportions of these remaining constituents in the microstructure of the steel according to the invention are so low that they have at best negligible effects on its properties. Excessive undesirable austenite contents exceeding 10% by volume can be prevented by suitably adjusting the Mn and Ni contents of the steel according to the invention.
  • the Mn content of a steel according to the invention is limited to at most 3.5% by weight and the Ni content to at most 4.0% by weight.
  • Optimized use can be made of the positive influence of Mn and Ni on the nature of the steel according to the invention, when the sum of the contents of Mn and Ni is at most 5 wt .-%. It proves to be particularly advantageous if the Mn content is set to at most 1.0% by weight or the Ni content to at most 1.5 times the optionally present copper content.
  • the positive effects of the presence of Mn or Ni, such as the maintenance of optimized mechanical properties enabled by the deliberate addition of Ni or Mn, in the steel according to the invention can be particularly utilized in that the Mn content of the steel is at least 0.20% by weight. is.
  • Negative effects of the invention specifically approved S-content can be avoided by the ratio% Mn /% S of the manganese content% Mn to sulfur content% S is set to more than 2.0.
  • the hot forming in the temperature range of 700-1280 ° C a complete solution of any existing precipitates, adequate Forming forces, sufficient Rekristallistaionskinetik and minimal grain growth achieved.
  • the hot forming temperature is 850 to 1050 ° C.
  • a particularly fine-grained microstructure, grain size according to ASTM E 112 4 and finer, is achieved.
  • the flat product or long product obtained according to the invention can undergo different heat treatments in order to adjust its mechanical properties.
  • An advantageous way of such a heat treatment in terms of energy utilization may be that the obtained after hot working steel flat or long product after the hot forming with a cooling rate of max. 3.0 K / min, in particular 1.5 K / min is slowly cooled, and from the economic point of view, the cooling rate should not be less than 1.0 K / min.
  • the final strength of the steel is achieved directly by precipitation of the precipitation phases, such as Laves, Heussler, copper, Ni3Ti and / or Ni3Al phases.
  • This procedure is particularly advantageous if the Ti content of the steel according to the invention is more than 0.60% by weight.
  • the tensile strength of the resulting flat or long product is typically in the range of 700-1150 MPa.
  • the flat or long product thermoformed from the steel according to the invention first to a solution annealing at more than 700 ° C., in particular 700-1250 ° C. or 700-1000 ° C., and then at a cooling rate of at least 25 K. / min to suppress the formation of excreta. After the respective cooling, there is an intermediate which is comparatively soft and readily machinable with a tensile strength of less than 900 MPa.
  • the product obtained can be stored at temperatures of 150-700 ° C over a period of 15 minutes to 30 hours to positively influence the state of precipitation of its microstructure.
  • precipitation of the Ti-containing precipitation phases occurs here, which in particular causes an increase in strength.
  • a steel S1 with the composition given in Table 1 was melted and cast into a block. This precursor has been heated to a hot forming temperature of 1050 ° C and formed at this temperature by pressing to a semi-finished product (long product).
  • the product thus obtained was solution annealed at a solution annealing temperature of 1050 ° C over a period of 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 800 MPa and could be easily machined with this comparatively low strength.
  • the machined product was aged at 500 ° C for 4 hours to set its final strength. After this aging, the steel of the product had a tenacity of 1070 MPa. It was found that the removal treatment led to minimal distortion of the product at most. An aging at a temperature of 550 ° C and a duration of 1 h gave a strength of 1200 MPa. At a Temperature of 600 ° C and the same aging time of 1 h, a strength of 1300 MPa could be achieved.
  • the density of the steel S1 used in Example 1 was 6.9 kg / dm 3 .
  • a steel S2 with the composition given in Table 1 was melted and cast into a block.
  • the precursor in question has been formed by pressing at a hot working temperature of 1050 ° C.
  • the product thus obtained was solution annealed at a solution annealing temperature of 1050 ° C over a period of 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 920 MPa and could be easily machined with this comparatively low strength.
  • the product was removed after mechanical processing at 500 ° C for 4 hours. After this aging, the steel of the product had a strength of 1175 MPa. It was also evident here that the aging treatment led to at most minimal distortion of the product.
  • the density of the steel S2 used in Example 2 was 6.9 kg / dm 3 .
  • a steel S3 with the composition given in Table 1 was melted and cast into a block.
  • the precursor in question has been converted to a block at a hot forming temperature of 1000 ° C by pressing.
  • the product thus obtained was solution annealed at a solution annealing temperature of 1075 ° C over a period of 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 860 MPa and could be easily machined with this comparatively low strength.
  • the product was aged to set its final strength at 550 ° C for 1 hour. After this aging, the steel of the product had a strength of 1540 MPa. It was found that the removal treatment led to minimal distortion of the product at most.
  • the density of the steel S3 used in Example 3 was 6.7 kg / dm 3 .
  • a steel S4 with the composition given in Table 1 was melted and cast into a block. Chromium and molybdenum were added to the melt to avoid a damaging superstructure (D03) and solid solution hardening.
  • the precursor in question has been formed by pressing at a hot working temperature of 1075 ° C.
  • the product thus obtained was solution annealed at a solution annealing temperature of 1050 ° C over a period of 1 h and then quenched by immersion in water.
  • the steel After quenching, the steel had a tensile strength of 805 MPa and could be easily machined with this comparatively low strength.
  • the product was aged at 550 ° C for 1 hour. After this aging, the steel of the product had a strength of 1260 MPa. It was found that the removal treatment led to minimal distortion of the product at most.
  • the density of the steel S4 used in Example 4 was 6.1 kg / dm 3 .
  • His structure consisted of more than 99 vol .-% of ferrite and precipitated phase.
  • Table 1 stolen al Ti C Si Mn N Cr Not a word S1 8th 1.25 0.04 0.59 0.56 0.001 S2 8th 1.25 0.01 1.43 1.50 0,002 S3 10 2.15 0.01 0.51 0.49 0,002 S4 18 1.31 0.01 0.5 0.47 0,002 2 0.24 Data in wt .-%, balance iron and unavoidable impurities

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 Steel (AREA)
EP16162652.8A 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier Active EP3225702B1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
ES16162652T ES2791887T3 (es) 2016-03-29 2016-03-29 Acero con densidad reducida y procedimiento para la fabricación de un producto plano de acero o un producto alargado de acero a partir de un acero de este tipo
EP16162652.8A EP3225702B1 (fr) 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier
US16/089,616 US20190119771A1 (en) 2016-03-29 2017-03-29 Steel with Reduced Density and Method for Producing a Flat Steel or Long Steel Product from Such a Steel
PCT/EP2017/057359 WO2017167778A1 (fr) 2016-03-29 2017-03-29 Acier de masse volumique réduite et procédé de fabrication d'un produit acier plat ou d'un produit acier allongé réalisé dans un acier de ce type

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP16162652.8A EP3225702B1 (fr) 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier

Publications (2)

Publication Number Publication Date
EP3225702A1 true EP3225702A1 (fr) 2017-10-04
EP3225702B1 EP3225702B1 (fr) 2020-03-25

Family

ID=55637294

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16162652.8A Active EP3225702B1 (fr) 2016-03-29 2016-03-29 Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier

Country Status (4)

Country Link
US (1) US20190119771A1 (fr)
EP (1) EP3225702B1 (fr)
ES (1) ES2791887T3 (fr)
WO (1) WO2017167778A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113718161A (zh) * 2021-09-01 2021-11-30 新疆八一钢铁股份有限公司 一种防止20Ni2MoA齿轮钢加工开裂的控制方法

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3719158B9 (fr) * 2019-04-01 2022-07-27 Deutsche Edelstahlwerke Specialty Steel GmbH & Co. KG Utilisation d'une poudre d'acier, procédé de fabrication d'un composant d'acier selon un procédé de fabrication additive

Citations (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1892316A (en) 1929-12-26 1932-12-27 Bonney Floyd Co Noncorrosive steel alloy
DE1208080B (de) 1963-08-02 1965-12-30 Yawata Iron & Steel Co Seewasserbestaendiger Stahl
DE1262613B (de) 1957-07-02 1968-03-07 Langley Alloys Ltd Verwendung einer Stahllegierung als Werkstoff fuer Gegenstaende mit hoher Festigkeit, Verschleissfestigkeit und verhaeltnismaessig geringem spezifischem Gewicht
DE2656076A1 (de) * 1975-12-12 1977-06-23 Hoogovens Ijmuiden Bv Stahllegierung mit verbesserter bestaendigkeit gegen insbesondere seewasserkorrosion und daraus zumindest teilweise gefertigte vorrichtungen bzw. einrichtungen
GB2186886B (en) 1986-02-25 1989-11-22 Nippon Steel Corp Steel composition
JPH05271873A (ja) * 1992-03-25 1993-10-19 Sumitomo Metal Ind Ltd 振動減衰特性に優れた鋼
DE19634524A1 (de) 1996-08-27 1998-04-09 Krupp Ag Hoesch Krupp Leichtbaustahl und seine Verwendung für Fahrzeugteile und Fassadenverkleidungen
JPH11350087A (ja) * 1998-06-11 1999-12-21 Nippon Steel Corp 耐食鋼
DE19900199A1 (de) 1999-01-06 2000-07-13 Ralf Uebachs Leichtbaustahllegierung
DE10035489A1 (de) 2000-07-21 2002-01-31 Schaeffler Waelzlager Ohg Reibpaarung
DE10231125A1 (de) 2001-09-28 2003-05-08 Daimler Chrysler Ag Hochfester Duplex-/Triplex-Leichtbaustahl und seine Verwendung
DE10359786A1 (de) 2003-12-19 2005-08-04 Daimlerchrysler Ag Rostfreie Rahmenkonstruktion für Kraftfahrzeuge
DE102005027258A1 (de) 2005-06-13 2006-12-21 Daimlerchrysler Ag Hochkohlenstoffhaltiger Stahl mit Superplastizität
DE102005024029B3 (de) 2005-05-23 2007-01-04 Technische Universität Bergakademie Freiberg Austenitischer Leichtbaustahl und seine Verwendung
DE102005030413B3 (de) 2005-06-28 2007-03-15 Technische Universität Bergakademie Freiberg Hochfester austenitisch-martensitischer Leichtbaustahl und seine Verwendung
DE102006030699A1 (de) 2006-06-30 2008-01-03 Daimlerchrysler Ag Gegossener Stahlkolben für Verbrennungsmotoren
DE102007047159A1 (de) 2007-08-29 2009-03-05 Volkswagen Ag Stahllegierung und Verwendung derselben in Ventilen
DE102007056144A1 (de) 2007-11-16 2009-05-20 Volkswagen Ag Abgaskrümmer oder Turboladergehäuse aus einer FeAl-Stahllegierung
DE102009031576A1 (de) 2008-07-23 2010-03-25 V&M Deutschland Gmbh Stahllegierung für einen ferritischen Stahl mit ausgezeichneter Zeitstandfestigkeit und Oxidationsbeständigkeit bei erhöhten Einsatztemperaturen
DE102010006800A1 (de) 2010-02-04 2011-03-17 Daimler Ag Aluminium-haltige Eisenlegierung und daraus hergestellter Turbolader
DE102010012718A1 (de) 2010-03-25 2011-09-29 Daimler Ag Dichtereduzierter UHC-Leichtbaustahl und dessen Verwendung
WO2013178629A1 (fr) * 2012-05-29 2013-12-05 Thyssenkrupp Steel Europe Ag Acier fe-al-cr résistant au fluage à chaud
EP2767601A1 (fr) 2013-02-14 2014-08-20 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication

Patent Citations (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1892316A (en) 1929-12-26 1932-12-27 Bonney Floyd Co Noncorrosive steel alloy
DE1262613B (de) 1957-07-02 1968-03-07 Langley Alloys Ltd Verwendung einer Stahllegierung als Werkstoff fuer Gegenstaende mit hoher Festigkeit, Verschleissfestigkeit und verhaeltnismaessig geringem spezifischem Gewicht
DE1208080B (de) 1963-08-02 1965-12-30 Yawata Iron & Steel Co Seewasserbestaendiger Stahl
DE2656076A1 (de) * 1975-12-12 1977-06-23 Hoogovens Ijmuiden Bv Stahllegierung mit verbesserter bestaendigkeit gegen insbesondere seewasserkorrosion und daraus zumindest teilweise gefertigte vorrichtungen bzw. einrichtungen
GB2186886B (en) 1986-02-25 1989-11-22 Nippon Steel Corp Steel composition
JPH05271873A (ja) * 1992-03-25 1993-10-19 Sumitomo Metal Ind Ltd 振動減衰特性に優れた鋼
DE19634524A1 (de) 1996-08-27 1998-04-09 Krupp Ag Hoesch Krupp Leichtbaustahl und seine Verwendung für Fahrzeugteile und Fassadenverkleidungen
JPH11350087A (ja) * 1998-06-11 1999-12-21 Nippon Steel Corp 耐食鋼
DE19900199A1 (de) 1999-01-06 2000-07-13 Ralf Uebachs Leichtbaustahllegierung
DE10035489A1 (de) 2000-07-21 2002-01-31 Schaeffler Waelzlager Ohg Reibpaarung
DE10231125A1 (de) 2001-09-28 2003-05-08 Daimler Chrysler Ag Hochfester Duplex-/Triplex-Leichtbaustahl und seine Verwendung
DE10359786A1 (de) 2003-12-19 2005-08-04 Daimlerchrysler Ag Rostfreie Rahmenkonstruktion für Kraftfahrzeuge
DE102005024029B3 (de) 2005-05-23 2007-01-04 Technische Universität Bergakademie Freiberg Austenitischer Leichtbaustahl und seine Verwendung
DE102005027258A1 (de) 2005-06-13 2006-12-21 Daimlerchrysler Ag Hochkohlenstoffhaltiger Stahl mit Superplastizität
DE102005030413B3 (de) 2005-06-28 2007-03-15 Technische Universität Bergakademie Freiberg Hochfester austenitisch-martensitischer Leichtbaustahl und seine Verwendung
DE102006030699A1 (de) 2006-06-30 2008-01-03 Daimlerchrysler Ag Gegossener Stahlkolben für Verbrennungsmotoren
DE102007047159A1 (de) 2007-08-29 2009-03-05 Volkswagen Ag Stahllegierung und Verwendung derselben in Ventilen
DE102007056144A1 (de) 2007-11-16 2009-05-20 Volkswagen Ag Abgaskrümmer oder Turboladergehäuse aus einer FeAl-Stahllegierung
DE102009031576A1 (de) 2008-07-23 2010-03-25 V&M Deutschland Gmbh Stahllegierung für einen ferritischen Stahl mit ausgezeichneter Zeitstandfestigkeit und Oxidationsbeständigkeit bei erhöhten Einsatztemperaturen
DE102010006800A1 (de) 2010-02-04 2011-03-17 Daimler Ag Aluminium-haltige Eisenlegierung und daraus hergestellter Turbolader
DE102010012718A1 (de) 2010-03-25 2011-09-29 Daimler Ag Dichtereduzierter UHC-Leichtbaustahl und dessen Verwendung
WO2013178629A1 (fr) * 2012-05-29 2013-12-05 Thyssenkrupp Steel Europe Ag Acier fe-al-cr résistant au fluage à chaud
EP2767601A1 (fr) 2013-02-14 2014-08-20 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
G. FROMMEYER; E. J. DREWES; B. ENGL: "Physical and mechanical properties of iron-aluminium-(Mn, Si) lightweight steels", REVUE DE METALLURGIE, vol. 97, October 2000 (2000-10-01), pages 1245 - 1253, XP001124154

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113718161A (zh) * 2021-09-01 2021-11-30 新疆八一钢铁股份有限公司 一种防止20Ni2MoA齿轮钢加工开裂的控制方法

Also Published As

Publication number Publication date
ES2791887T3 (es) 2020-11-06
US20190119771A1 (en) 2019-04-25
WO2017167778A1 (fr) 2017-10-05
EP3225702B1 (fr) 2020-03-25

Similar Documents

Publication Publication Date Title
DE69426763T2 (de) hochfeste, HOCHDEHNBARER ROSTFREIER ZWEI-PHASEN STAHL UND VERFAHREN ZU DESSEN HERSTELLUNG
EP2383353B1 (fr) Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication
EP1309734B2 (fr) Acier et feuillard ou tole d'acier a resistance tres elevee, pouvant etre forme a froid, procede pour produire un feuillard d'acier et utilisations d'un tel acier
EP2366035B1 (fr) Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication
DE60216934T3 (de) Ultrahochfester stahl, produkt aus diesem stahl und verfahren zu seiner herstellung
AT394056B (de) Verfahren zur herstellung von stahl
DE112006003169B4 (de) Stahlbleche zum Warmpressformen mit ausgezeichneten Wärmebehandlungs- und Schlageigenschaften, daraus hergestellte Warmpressteile und Verfahren zu deren Herstellung
DE2124994C3 (de) Verfahren zur Herstellung starker, zähfester Stahlplatten
EP3332047B1 (fr) Procédé de fabrication d'un produit plat en acier laminé flexible et son utilisation
EP3504349B1 (fr) Procédé de fabrication d'une bande d'acier à résistance très élevée présentant des propriétés améliorées lors du traitement ultérieur et une telle bande d'acier
EP2059623A1 (fr) Acier moulé austénitique inoxydable, son procédé de fabrication et son utilisation
EP2905348B1 (fr) Produit en acier plat de haute résistance avec une structure bainitique-martensitique et procédé de fabrication d'un tel produit acier plat
EP2895635A1 (fr) Alliage d'acier pour un acier faiblement allié à haute résistance
EP3168312B1 (fr) Acier inoxydable de construction comprenant un joint bainitique, pièce forgée ainsi fabriquée et procédé de fabrication d'une pièce forgée
EP3325678B1 (fr) Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier
DE60300561T3 (de) Verfahren zur Herstellung eines warmgewalzten Stahlbandes
DE4040355A1 (de) Verfahren zur herstellung eines duennen stahlblechs aus stahl mit hohem kohlenstoffgehalt
EP3512968B1 (fr) Procédé pour fabriquer un produit plat en acier à partir d'un acier au manganèse et produit plat en acier résultant
EP1430161B1 (fr) Acier duplex/triplex a resistance elevee pour construction legere et son utilisation
EP3899064B1 (fr) Matériau superausténitique
DE2800444C2 (de) Verwendung eines Cr-Mo-Stahls
DE60315182T2 (de) Werkstück aus schweisbarem baustahl und verfahren zum herstellen
DE3113844A1 (de) "ferritfreier, ausscheidungshaertbarer rostfreier stahl"
EP3225702B1 (fr) Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier
DE102016115618A1 (de) Verfahren zur Herstellung eines höchstfesten Stahlbandes mit verbesserten Eigenschaften bei der Weiterverarbeitung und ein derartiges Stahlband

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

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

Free format text: STATUS: THE APPLICATION HAS BEEN PUBLISHED

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

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

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20180404

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

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: DEUTSCHE EDELSTAHLWERKE SPECIALTY STEEL GMBH & CO.

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20180906

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

INTG Intention to grant announced

Effective date: 20190814

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

GRAL Information related to payment of fee for publishing/printing deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR3

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

INTC Intention to grant announced (deleted)
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

INTG Intention to grant announced

Effective date: 20200128

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: DE

Ref legal event code: R096

Ref document number: 502016009234

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1248621

Country of ref document: AT

Kind code of ref document: T

Effective date: 20200415

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

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

Ref country code: FI

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

Effective date: 20200325

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: 20200625

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: 20200325

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

Ref country code: ES

Payment date: 20200520

Year of fee payment: 5

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: 20200626

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: 20200625

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: 20200325

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: 20200325

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: 20200325

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20200325

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: 20200325

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: 20200725

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: 20200325

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: 20200325

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: 20200325

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: 20200325

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: 20200325

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: 20200818

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

Ref country code: CZ

Payment date: 20200505

Year of fee payment: 5

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2791887

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20201106

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20200331

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

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: 20200325

Ref country code: LU

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

Effective date: 20200329

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502016009234

Country of ref document: DE

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: 20200329

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: 20200325

Ref country code: LI

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

Effective date: 20200331

Ref country code: CH

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

Effective date: 20200331

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: 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: 20200325

Ref country code: BE

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

Effective date: 20200331

26N No opposition filed

Effective date: 20210112

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

Ref country code: FR

Payment date: 20210318

Year of fee payment: 6

Ref country code: IT

Payment date: 20210324

Year of fee payment: 6

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: 20200325

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

Ref country code: GB

Payment date: 20210318

Year of fee payment: 6

Ref country code: DE

Payment date: 20210318

Year of fee payment: 6

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 NON-PAYMENT OF DUE FEES

Effective date: 20210329

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 1248621

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210329

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20220523

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: 20200325

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: 20200325

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: 20200325

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: 20200325

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: 20200325

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: 20210330

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: 20210329

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502016009234

Country of ref document: DE

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

Effective date: 20220329

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: 20220329

Ref country code: FR

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

Effective date: 20220331

Ref country code: DE

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

Effective date: 20221001

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: 20220329