EP3899063B1 - Superaustenitischer werkstoff - Google Patents

Superaustenitischer werkstoff Download PDF

Info

Publication number
EP3899063B1
EP3899063B1 EP19829563.6A EP19829563A EP3899063B1 EP 3899063 B1 EP3899063 B1 EP 3899063B1 EP 19829563 A EP19829563 A EP 19829563A EP 3899063 B1 EP3899063 B1 EP 3899063B1
Authority
EP
European Patent Office
Prior art keywords
superaustenitic
material according
detection limit
nitrogen
weight
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
EP19829563.6A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3899063A1 (de
EP3899063C0 (de
Inventor
Rainer FLUCH
Andreas KEPLINGER
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.)
Voestalpine Boehler Edelstahl GmbH and Co KG
Original Assignee
Voestalpine Boehler Edelstahl GmbH and Co KG
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 Voestalpine Boehler Edelstahl GmbH and Co KG filed Critical Voestalpine Boehler Edelstahl GmbH and Co KG
Publication of EP3899063A1 publication Critical patent/EP3899063A1/de
Application granted granted Critical
Publication of EP3899063C0 publication Critical patent/EP3899063C0/de
Publication of EP3899063B1 publication Critical patent/EP3899063B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • C22C38/54—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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/38—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
    • C22C38/44—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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • C22C38/18—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

Definitions

  • the invention relates to a super-austenitic material and a method for its production.
  • Such materials are z. B. used in chemical plant construction or in oil field or gas field technology.
  • a requirement for such materials is that they withstand corrosive attack, in particular attack in media with high chloride concentrations.
  • Such materials are, for example, from the CN 107876562A , the CN 104195446A or DE 43 42 188 known.
  • WO 02/02837 A1 is a corrosion-resistant material for use in media with a high chloride concentration in oil field technology. This is a chromium-nickel-molybdenum superaustenite that has a comparatively low nitrogen content but very high chromium and very high nickel contents.
  • the JP 2005 179733 A discloses a super austenitic material.
  • chromium-nickel-molybdenum steels usually have improved corrosion behavior compared to the previously mentioned chromium-manganese-nitrogen steels.
  • chromium manganese nitrogen steels are a more economical alloy composition that nonetheless offers an excellent combination of strength, toughness and corrosion resistance.
  • the chromium-nickel-molybdenum steels mentioned achieve significantly higher corrosion resistance than chromium manganese nitrogen steels, but are associated with significantly higher costs due to the very high nickel content.
  • PREN 16 % Cr + 3.3 x % Mo + 16 x % N.
  • MARC % Cr + 3.3 x % Mo + 20 x % N + 20 x % C - 0.25 x % Ni - 0.5 x % Mn.
  • Comparable steel grades are also known for use as shipbuilding steels for submarines, these being chromium-nickel manganese nitrogen steels which are also alloyed with niobium to stabilize the carbon, but this degrades the impact strength. These steels are generally low in manganese and therefore have relatively good corrosion resistance, but do not achieve the strength of drill collar grades.
  • the object of the invention is to create a super-austenitic, high-strength and tough material that can be produced in a comparatively simple and cost-effective manner.
  • the material is to be used, in particular in the measuring device industry and especially in the watchmaking industry, in particular as a housing for highly sensitive measuring devices and for screw support axle drives, pumps, flexible pipes, wire guides, chemical apparatus construction and seawater treatment plants. It should have a completely austenitic structure even after an optional cold forming after strain hardening the yield point should be R p0.2 >1000 MPa.
  • the alloy according to the invention has the following composition: elements preferred more preferred carbon (C) 0.01 - 0.20 0.01 - 0.1 Silicon (Si) ⁇ 0.5 ⁇ 0.5 Manganese (Mn) 4.0 - 7.0 5.0 - 6.0 Phosphorus (P) ⁇ 0.05 ⁇ 0.05 Sulfur (S) ⁇ 0.005 ⁇ 0.005 iron (Fe) rest rest Chromium (Cr) 24.0 - 28.0 26.0 - 28.0 Molybdenum (Mo) 2.5 - 3.5 2.5 - 3.5 Nickel (Ni) 12.0 - 15.5 13.0 - 15.0 vanadium (V) ⁇ 0.3 Below detection limit Tungsten (W) ⁇ 0.1 Below detection limit copper (Cu) ⁇ 0.15 Below detection limit cobalt (Co) ⁇ 0.5 Below detection limit Titanium (Ti) ⁇ 0.05 Below detection limit Aluminum (Al) ⁇ 0.1 ⁇ 0.1 niobium (Nb) ⁇ 0.025 Below detection limit boron
  • the steel according to the invention should be free of precipitation, since precipitation has a negative impact on toughness and corrosion resistance.
  • the yield point is R p0.2 >450 MPa and can easily reach values >500 MPa, with the impact work at 20°C being greater than 350 J and values of up to 440 J being reached.
  • the yield point is definitely R p0.2 >1000 MPa and values of up to 1100 MPa are achieved in practice, with strain hardened the impact work at 20°C being certainly greater than 80J, with values of 200 J being achieved in practice .
  • the notch impact work was determined according to DIN EN ISO 148-1.
  • values for the product of tensile strength Rm with notched impact strength KV of more than 100,000 MPa J, preferably >200,000 MPa J, particularly preferably >300,000 MPa J, can be achieved.
  • Carbon is contained in contents from 0.01 up to 0.25%. Carbon is an austenite former and has a favorable effect in terms of high mechanical parameters. With a view to avoiding carbidic precipitations, the carbon content should be set to between 0.01 and 0.20% by weight, in particular between 0.01 and 0.10% by weight.
  • silicon are ⁇ 0.5% by weight and are mainly used for deoxidizing the steel.
  • the specified upper limit reliably avoids the formation of intermetallic phases. Since silicon is also a ferrite former, the upper limit is also selected with a safety range in this regard. In particular, silicon can be provided in contents of 0.1-0.3% by weight.
  • Manganese is contained in amounts of 3.0 - 8.0% by weight. This is an extremely low value compared to materials according to the prior art. Up to now it has been assumed that manganese contents of more than 19% by weight, if possible more than 20% by weight, are necessary for high nitrogen solubility. Surprisingly, it has been found with the present alloy that even with the low manganese contents according to the invention, a nitrogen solubility is achieved which is above what is possible according to the prevailing expert opinion. In addition, it was previously assumed that good corrosion resistance goes hand in hand with very high manganese contents, but it has been found according to the invention that this is apparently not necessary due to unexplained synergistic effects in the present alloy.
  • the lower limit for manganese can be chosen at 3.5 or 4.0 or 4.5 or 5.0%.
  • the upper limit for manganese can be chosen at 6.0 or 6.5 or 7.0 or 7.5%.
  • Chromium levels of 17% by weight or more are found to be necessary for higher corrosion resistance. According to the invention, at least 24.0% and at most 30% chromium are included. Up to now it was assumed that contents higher than 24% by weight have an adverse effect on the magnetic permeability, because chromium is one of the ferrite-stabilizing elements. On the other hand, it was found with the alloy according to the invention that even very high chromium contents above 23% do not negatively affect the magnetic permeability in the present alloy, but the resistance to pitting and stress corrosion cracking is known to be optimally influenced.
  • the lower limit for chromium can be chosen at 25 or 26%.
  • the upper limit for chromium can be chosen at 28 or 29%.
  • Molybdenum is an element which contributes significantly to corrosion resistance in general and pitting corrosion resistance in particular, the effect of molybdenum being enhanced by nickel. According to the invention, 2.0 to 4% by weight of molybdenum are added. The lower limit for molybdenum can be chosen at 2.1 or 2.2 or 2.3 or 2.4 or 2.5%. The upper limit for molybdenum can be chosen at 3.5 or 3.6 or 3.7 or 3.8 or 3.9%. Higher molybdenum contents make an ESR treatment absolutely necessary in order to rule out segregation. Remelting processes are very complex and expensive. Therefore, according to the invention, DESU or ESU routes should be avoided.
  • tungsten is present in amounts below 0.5% and contributes to the increase in corrosion resistance.
  • the upper limit for tungsten can be chosen at 0.4 or 0.3 or 0.2 or 0.1% or below the detection limit (i.e. without any deliberate addition).
  • nickel is present in contents of 10 to 16%, as a result of which a high resistance to stress corrosion cracking is achieved in media containing chloride.
  • the lower limit for nickel can be chosen at 11 or 12 or 13%.
  • the upper limit for nickel can be chosen at 15 or 15.5%.
  • the alloying of copper is described as advantageous for the resistance in sulfuric acid, it is found according to the invention that copper at values >0.5% increases the tendency to precipitate chromium nitrides, which has a negative effect on the corrosion properties.
  • the upper limit value for copper was set at ⁇ 0.5%, preferably below 0.15%, most preferably below the detection limit.
  • Cobalt can be provided in amounts of up to 5% by weight, in particular to replace nickel.
  • the upper limit for cobalt can be chosen at 5 or 3 or 1 or 0.5 or 0.4 or 0.3 or 0.2 or 0.1% or below the detection limit (i.e. without any intentional addition).
  • Nitrogen is included at levels of 0.50 to 0.90% by weight to ensure high strength. Furthermore, nitrogen contributes to corrosion resistance and is a strong austenite former, which is why higher contents than 0.50% by weight, in particular higher than 0.52% by weight, are favorable. In order to avoid nitrogen-containing precipitates, in particular chromium nitride, the upper limit of nitrogen is limited to 0.90% by weight. It has been shown that despite the very low manganese content, in contrast to known alloys, these high nitrogen contents can be achieved in the alloy . Due to the good nitrogen solubility on the one hand and the disadvantages that are obtained with higher nitrogen contents, in particular over 0.90%, any pressure increase is even out of the question as part of a DESU route.
  • the ratio of nitrogen to carbon is greater than 15.
  • the lower limit for nitrogen can be chosen at 0.52 or 0.54 or 0.60 or 0.65%.
  • the upper limit for nitrogen can be selected at 0.80 or 0.85%.
  • boron, aluminum and sulfur can be included as further alloy components, but only optionally.
  • the alloy components vanadium and titanium are not necessarily contained in the present steel alloy. Although these elements contribute positively to the solubility of nitrogen, the high nitrogen solubility of the present invention can be provided even in their absence.
  • the alloy according to the invention should not contain niobium, since it can form precipitates which reduce toughness. Historically, niobium has only been used to bind carbon, which is not necessary in the alloy of the present invention. The niobium content is still tolerable up to 0.1%, but should not exceed the content of unavoidable impurities.
  • the components are melted under atmospheric conditions and then further treated with secondary metallurgy. Blocks are then cast, which are immediately hot-formed.
  • ESR Electroslag remelting
  • DESU pressure electroslag remelting
  • MARC opt 40 ⁇ wt%Cr + 3.3 x wt%Mo + 20 x wt%C + 20 x wt%N - 0.5 x wt%Mn
  • MARC formula is optimized by finding that the otherwise usual deduction of nickel does not apply to the system according to the invention and the limit value of 40 is necessary.
  • FIG 2 the possible process routes for the production of the alloy composition according to the invention are shown as examples.
  • a possible one is now used as an example Route described.
  • VID vacuum induction melting unit
  • melted material is simultaneously melted and treated for secondary metallurgy.
  • the melt is then poured into molds (ingot) and solidifies there into blocks.
  • molds ingot
  • These are then hot-formed in several steps. For example, pre-forged on the rotary forging machine and brought to final dimensions in the multi-line rolling mill.
  • a heat treatment step can also be carried out.
  • the cold forming step can be carried out by means of wire drawing.
  • a super-austenitic material according to the invention can not only have the described (and in particular in figure 2 illustrated) production routes are produced, the advantageous properties of the alloy according to the invention can also be achieved by a powder-metallurgical production route.
  • figure 4 are the three alloys made figure 3 produced by a method according to the invention and subjected to strain hardening.
  • R p0.2 was around 1000 MPa for all three materials and the tensile strength Rm was between 1100 MPa and 1250 MPa.
  • the impact energy was excellent at 270 J to even over 300 J (alloy C - 329.5 J).
  • the advantage of the invention is that an austenitic, high-strength material with increased corrosion resistance and a low nickel content is created, which at the same time shows high strength and paramagnetic behavior.
  • a completely austenitic structure is also present after cold forming, so that it has been possible to combine the positive properties of a cost-effective CrMnNi steel with the outstanding technical properties of a CrNiMo steel.
  • a special feature of the invention is that, due to the high nitrogen content, the work hardening rate is higher than with other super austenites in order to be able to achieve tensile strengths (R m ) of 2500 MPa.
  • R m tensile strengths
  • Typical areas of application for the materials according to the invention are shipbuilding and here in particular submarine construction, chemical apparatus construction, seawater treatment plants, the paper industry, screws and bolts, flexible pipes, so-called wirelines, completion tools, springs, valves, umbilicals, axle drives, pumps. Depending on the area of application, there may be minor alloy adjustments which figure 5 are shown.
  • the strength can be further increased by cold forming, as already described.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
  • Conductive Materials (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Articles (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Soft Magnetic Materials (AREA)
EP19829563.6A 2018-12-20 2019-12-19 Superaustenitischer werkstoff Active EP3899063B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102018133255.6A DE102018133255A1 (de) 2018-12-20 2018-12-20 Superaustenitischer Werkstoff
PCT/EP2019/086384 WO2020127788A1 (de) 2018-12-20 2019-12-19 Superaustenitischer werkstoff

Publications (3)

Publication Number Publication Date
EP3899063A1 EP3899063A1 (de) 2021-10-27
EP3899063C0 EP3899063C0 (de) 2023-08-30
EP3899063B1 true EP3899063B1 (de) 2023-08-30

Family

ID=69063782

Family Applications (2)

Application Number Title Priority Date Filing Date
EP19829563.6A Active EP3899063B1 (de) 2018-12-20 2019-12-19 Superaustenitischer werkstoff
EP19829564.4A Active EP3899064B1 (de) 2018-12-20 2019-12-19 Superaustenitischer werkstoff

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP19829564.4A Active EP3899064B1 (de) 2018-12-20 2019-12-19 Superaustenitischer werkstoff

Country Status (11)

Country Link
US (2) US20220145436A1 (es)
EP (2) EP3899063B1 (es)
JP (2) JP2022514920A (es)
CN (2) CN113544295A (es)
BR (2) BR112021011844A8 (es)
CA (2) CA3124189C (es)
DE (1) DE102018133255A1 (es)
EA (2) EA202191412A1 (es)
ES (2) ES2957403T3 (es)
PL (2) PL3899064T3 (es)
WO (2) WO2020127789A1 (es)

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN116121667A (zh) * 2021-11-14 2023-05-16 重庆三爱海陵实业有限责任公司 气门及其耐高温合金
CN115261718B (zh) * 2022-03-28 2023-06-06 江西宝顺昌特种合金制造有限公司 一种超级奥氏体不锈钢s34565板材及其制备方法
CN115992330B (zh) * 2023-02-17 2024-04-19 东北大学 一种高氮低钼超级奥氏体不锈钢及其合金成分优化设计方法

Family Cites Families (38)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB778597A (en) * 1955-02-15 1957-07-10 Ford Motor Co Improvements in or relating to the manufacture of nitrogen-rich wrought austenitic alloys
AT277302B (de) * 1963-05-24 1969-12-29 Boehler & Co Ag Geb Austenitischer korrosionsbeständiger Stahl
JPS5521547A (en) * 1978-08-01 1980-02-15 Hitachi Metals Ltd Austenite stainless steel having high strength and pitting corrosion resistance
DE3407307A1 (de) * 1984-02-24 1985-08-29 Mannesmann AG, 4000 Düsseldorf Verwendung einer korrosionsbestaendigen austenitischen eisen-chrom-nickel-stickstoff-legierung fuer mechanisch hoch beanspruchte bauteile
DE3837456C1 (en) * 1988-05-17 1990-03-29 Thyssen Edelstahlwerke Ag, 4000 Duesseldorf, De Use of a fully austenitic steel for components which are severely stressed corrosion-chemically and mechanically
NO891969L (no) * 1988-05-17 1989-11-20 Thyssen Edelstahlwerke Ag Korrosjonsbestandig austenittisk staal.
DE3837457C1 (en) * 1988-05-17 1989-12-21 Thyssen Edelstahlwerke Ag, 4000 Duesseldorf, De Steel for components of plants or equipment for the conveying, storage and transport of oil or gas
JPH03285050A (ja) * 1990-03-30 1991-12-16 Aichi Steel Works Ltd 高温特性の優れた排気バルブ用鋼
JP2591256B2 (ja) * 1990-05-21 1997-03-19 住友金属工業株式会社 高強度非磁性鋼
DE4342188C2 (de) 1993-12-10 1998-06-04 Bayer Ag Austenitische Legierungen und deren Verwendung
JPH08239735A (ja) * 1995-02-28 1996-09-17 Sumitomo Metal Mining Co Ltd オーステナイト系ステンレス鋳鋼
JP3546421B2 (ja) * 1995-03-31 2004-07-28 大同特殊鋼株式会社 高強度・高耐食含窒素オーステナイ ト系ステンレス鋼
US6129999A (en) * 1995-09-27 2000-10-10 Sumitomo Metal Industries, Ltd. High-strength welded steel structures having excellent corrosion resistance
JP3347582B2 (ja) * 1996-04-12 2002-11-20 大同特殊鋼株式会社 メタルガスケット用オーステナイト系ステンレス鋼 及びその製造方法
AT407882B (de) 1999-07-15 2001-07-25 Schoeller Bleckmann Oilfield T Verfahren zur herstellung eines paramagnetischen, korrosionsbeständigen werkstoffes u.dgl. werkstoffe mit hoher dehngrenze, festigkeit und zähigkeit
DE29921813U1 (de) * 1999-12-12 2000-02-24 Friederich, Heinrich, Dr.-Ing., 68649 Groß-Rohrheim Hochfester korrosionsbeständiger Edelstahl-Profilstab
AT408889B (de) 2000-06-30 2002-03-25 Schoeller Bleckmann Oilfield T Korrosionsbeständiger werkstoff
KR100445246B1 (ko) * 2001-12-28 2004-08-21 김영식 공식저항성이 우수한 고니켈 2상 스테인리스강
US20040258554A1 (en) * 2002-01-09 2004-12-23 Roman Radon High-chromium nitrogen containing castable alloy
US6761777B1 (en) * 2002-01-09 2004-07-13 Roman Radon High chromium nitrogen bearing castable alloy
JP4210999B2 (ja) * 2003-12-19 2009-01-21 大同特殊鋼株式会社 無段変速機用リング材料及びその製造方法、並びに無段変速機用リング
JP2005281855A (ja) * 2004-03-04 2005-10-13 Daido Steel Co Ltd 耐熱オーステナイト系ステンレス鋼及びその製造方法
SE528008C2 (sv) * 2004-12-28 2006-08-01 Outokumpu Stainless Ab Austenitiskt rostfritt stål och stålprodukt
US20090129967A1 (en) * 2007-11-09 2009-05-21 General Electric Company Forged austenitic stainless steel alloy components and method therefor
CN102414764B (zh) * 2009-09-29 2014-06-04 古河电气工业株式会社 用于超导线材的基板、超导线材及其制造方法
JP5056985B2 (ja) * 2009-11-18 2012-10-24 住友金属工業株式会社 オーステナイト系ステンレス鋼板およびその製造方法
KR101543938B1 (ko) * 2011-03-28 2015-08-11 신닛테츠스미킨 카부시키카이샤 고압 수소 가스용 고강도 오스테나이트 스테인리스강
SG192478A1 (en) * 2011-05-26 2013-08-30 United Pipelines Asia Pacific Pte Ltd Austenitic stainless steel
US9347121B2 (en) * 2011-12-20 2016-05-24 Ati Properties, Inc. High strength, corrosion resistant austenitic alloys
US10329649B2 (en) * 2012-01-20 2019-06-25 Solu Stainless Oy Austenitic stainless steel product and a method for manufacturing same
US9869003B2 (en) * 2013-02-26 2018-01-16 Ati Properties Llc Methods for processing alloys
CN104195446A (zh) 2014-08-06 2014-12-10 张家港市飞浪泵阀有限公司 用于泵阀产品上的超级奥氏体不锈钢
EP3214194B1 (en) * 2014-10-29 2019-12-04 Nippon Steel Corporation Austenitic stainless steel and manufacturing method therefor
CA3019892C (en) * 2016-04-07 2020-12-22 Nippon Steel & Sumitomo Metal Corporation Austenitic stainless steel material
CN106244940A (zh) * 2016-08-26 2016-12-21 天津新伟祥工业有限公司 一种铬锰氮系奥氏体耐热钢及其制备方法
CN107876562A (zh) 2017-11-23 2018-04-06 海盐中达金属电子材料有限公司 一种超级奥氏体不锈钢钢带及其加工用热轧机
CN108396223B (zh) * 2018-03-29 2020-09-29 东北大学 一种超级奥氏体不锈钢及其合金成分优化设计方法
CN108642409A (zh) * 2018-05-08 2018-10-12 江苏理工学院 一种耐腐蚀超级奥氏体不锈钢及其制造工艺

Also Published As

Publication number Publication date
WO2020127788A1 (de) 2020-06-25
ES2957403T3 (es) 2024-01-19
DE102018133255A1 (de) 2020-06-25
EP3899063A1 (de) 2021-10-27
CA3124189A1 (en) 2020-06-25
WO2020127789A1 (de) 2020-06-25
EA202191413A1 (ru) 2021-09-28
EP3899064C0 (de) 2023-08-30
EA202191412A1 (ru) 2021-09-28
ES2956332T3 (es) 2023-12-19
EP3899064A1 (de) 2021-10-27
BR112021011849A2 (pt) 2021-09-08
US20220145436A1 (en) 2022-05-12
PL3899064T3 (pl) 2023-11-20
EP3899064B1 (de) 2023-08-30
EP3899063C0 (de) 2023-08-30
JP2022522092A (ja) 2022-04-14
PL3899063T3 (pl) 2023-12-04
CA3124189C (en) 2023-10-31
CN113544294A (zh) 2021-10-22
BR112021011844A2 (pt) 2021-08-31
JP2022514920A (ja) 2022-02-16
US20240052469A2 (en) 2024-02-15
BR112021011844A8 (pt) 2023-05-09
US20230332282A1 (en) 2023-10-19
CA3122044A1 (en) 2020-06-25
CN113544295A (zh) 2021-10-22

Similar Documents

Publication Publication Date Title
DE602004000140T2 (de) Rostfreier austenitischer Stahl
AT412727B (de) Korrosionsbeständige, austenitische stahllegierung
EP3535431B1 (de) Mittelmanganstahlprodukt zum tieftemperatureinsatz und verfahren zu seiner herstellung
DE69329004T2 (de) Hochfester und korrosionsbeständiger rostfreier Stahl und Behandlungsverfahren
EP3899063B1 (de) Superaustenitischer werkstoff
EP3504349B1 (de) Verfahren zur herstellung eines höchstfesten stahlbandes mit verbesserten eigenschaften bei der weiterverarbeitung und ein derartiges stahlband
DE60124227T2 (de) Duplex rostfreier stahl
WO2019121879A1 (de) Verfahren zum additiven fertigen eines gegenstandes aus einem maraging-stahlpulver
EP3325678B1 (de) Umformbarer leichtbaustahl mit verbesserten mechanischen eigenschaften und verfahren zur herstellung von halbzeug aus diesem stahl
EP3512968B1 (de) Verfahren zur herstellung eines stahlflachprodukts aus einem manganhaltigen stahl und ein derartiges stahlflachprodukt
DE60300561T3 (de) Verfahren zur Herstellung eines warmgewalzten Stahlbandes
DE102015222183A1 (de) Warmumformstahl und Verfahren zum Herstellen desselben
DE69601340T2 (de) Hochfester, hochzaher warmebestandiger stahl und verfahren zu seiner herstellung
DE2927091A1 (de) Nichtmagnetischer manganhartstahl mit ausgezeichneter schweissbarkeit und verarbeitbarkeit und verwendung dieses stahls
DE10019042A1 (de) Stickstofflegierter, sprühkompaktierter Stahl, Verfahren zu seiner Herstellung und Verbundwerkstoff hergestellt aus dem Stahl
EP3899065A1 (de) Bohrstrangkomponente mit hoher korrosionsbeständigkeit und verfahren zu ihrer herstellung
AT407882B (de) Verfahren zur herstellung eines paramagnetischen, korrosionsbeständigen werkstoffes u.dgl. werkstoffe mit hoher dehngrenze, festigkeit und zähigkeit
DE69015394T2 (de) Rostfreier ferritischer Stahl und Verfahren zur Herstellung dieses Stahls.
EP3469108B1 (de) Verfahren zur herstellung eines kaltgewalzten stahlbandes mit trip-eigenschften aus einem hochfesten, manganhaltigen stahl
EP3225702B1 (de) Stahl mit reduzierter dichte und verfahren zur herstellung eines stahlflach- oder -langprodukts aus einem solchen stahl
DE69708574T2 (de) Verwendung eines schweissbaren ferritischen Gussstahls mit niedrigem Chromgehalt und mit sehr gute Warmfestigkeit
EP3728674A1 (de) Verfahren zum herstellen eines gegenstands aus einem maraging-stahl
DE102018108173A1 (de) Austenitische Legierung und Verfahren zum Herstellen einer stickstoffhaltigen austenitischen Legierung
EP2809818B1 (de) Duplexstahl mit verbesserter kerbschlagzähigkeit und zerspanbarkeit
DE2118697B2 (de) Verfahren zur Herstellung eines hxxochfesten, kohlenstoffarmen Baustahles mit guter Schweißbarkeit

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: UNKNOWN

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

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

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: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20210618

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

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 502019009199

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C21D0006000000

Ipc: C22C0038460000

Ref country code: DE

Ref legal event code: R079

Free format text: PREVIOUS MAIN CLASS: C21D0006000000

Ipc: C22C0038460000

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/00 20060101ALN20230317BHEP

Ipc: C22C 38/58 20060101ALN20230317BHEP

Ipc: C22C 38/48 20060101ALN20230317BHEP

Ipc: C22C 33/02 20060101ALN20230317BHEP

Ipc: C22C 38/50 20060101ALN20230317BHEP

Ipc: C22C 38/52 20060101ALN20230317BHEP

Ipc: C22C 38/54 20060101ALN20230317BHEP

Ipc: C21D 6/00 20060101ALI20230317BHEP

Ipc: C21D 7/02 20060101ALI20230317BHEP

Ipc: C21D 7/10 20060101ALI20230317BHEP

Ipc: C21D 8/02 20060101ALI20230317BHEP

Ipc: C21D 9/46 20060101ALI20230317BHEP

Ipc: C21D 9/08 20060101ALI20230317BHEP

Ipc: C22C 38/22 20060101ALI20230317BHEP

Ipc: C22C 38/38 20060101ALI20230317BHEP

Ipc: C22C 38/40 20060101ALI20230317BHEP

Ipc: C22C 38/42 20060101ALI20230317BHEP

Ipc: C22C 38/44 20060101ALI20230317BHEP

Ipc: C22C 38/46 20060101AFI20230317BHEP

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: 20230502

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

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230706

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: 502019009199

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

U01 Request for unitary effect filed

Effective date: 20230927

P04 Withdrawal of opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230929

U07 Unitary effect registered

Designated state(s): AT BE BG DE DK EE FI FR IT LT LU LV MT NL PT SE SI

Effective date: 20231005

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: 20231201

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

Ref country code: GB

Payment date: 20231227

Year of fee payment: 5

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2957403

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20240119

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: 20231230

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

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: 20230830

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: 20231130

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: 20231230

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: 20230830

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: 20231201

U20 Renewal fee paid [unitary effect]

Year of fee payment: 5

Effective date: 20231227

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

Ref country code: PL

Payment date: 20231211

Year of fee payment: 5

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

Ref country code: ES

Payment date: 20240102

Year of fee payment: 5

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: 20230830

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: 20230830

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: 20230830

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: 20230830

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

Ref country code: CH

Payment date: 20240102

Year of fee payment: 5

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502019009199

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

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

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

26N No opposition filed

Effective date: 20240603

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: 20230830

U1N Appointed representative for the unitary patent procedure changed [after the registration of the unitary effect]

Representative=s name: WSL PATENTANWAELTE PARTNERSCHAFT MBB; DE

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: 20230830