EP2803743B1 - Acier faiblement allié - Google Patents

Acier faiblement allié Download PDF

Info

Publication number
EP2803743B1
EP2803743B1 EP12865286.4A EP12865286A EP2803743B1 EP 2803743 B1 EP2803743 B1 EP 2803743B1 EP 12865286 A EP12865286 A EP 12865286A EP 2803743 B1 EP2803743 B1 EP 2803743B1
Authority
EP
European Patent Office
Prior art keywords
less
content
low alloy
alloy steel
ssc
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
EP12865286.4A
Other languages
German (de)
English (en)
Other versions
EP2803743A1 (fr
EP2803743A4 (fr
Inventor
Hiroyuki Hirata
Kenji Kobayashi
Tomohiko Omura
Kaori Kawano
Kota TOMATSU
Kazuhiro Ogawa
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.)
Nippon Steel Corp
Original Assignee
Nippon Steel and Sumitomo Metal Corp
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 Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Publication of EP2803743A1 publication Critical patent/EP2803743A1/fr
Publication of EP2803743A4 publication Critical patent/EP2803743A4/fr
Application granted granted Critical
Publication of EP2803743B1 publication Critical patent/EP2803743B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • 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
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—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
    • C22C38/18—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
    • C22C38/32—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
    • C22C38/38—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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • E—FIXED CONSTRUCTIONS
    • E21—EARTH OR ROCK DRILLING; MINING
    • E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
    • E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings
    • E—FIXED CONSTRUCTIONS
    • E21—EARTH OR ROCK DRILLING; MINING
    • E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
    • E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings
    • E21B17/01—Risers
    • 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
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints

Definitions

  • the present invention relates to a low alloy steel.
  • a steel pipe called a riser, flowline, or trunkline is used for transmission of crude oil or natural gas between an oil well or gas well located at the bottom of the sea and a platform on the sea or between the platform and a refinery station on the land.
  • a riser, flowline, or trunkline is used for transmission of crude oil or natural gas between an oil well or gas well located at the bottom of the sea and a platform on the sea or between the platform and a refinery station on the land.
  • HIC hydrogen induced cracking
  • SSC sulfide stress cracking
  • Patent Document 1 JP5-255746A proposes a steel provided with excellent HIC resistance by defining the heat history and heat treatment conditions at the production time without substantially containing Ni, Cu and Ca.
  • Patent Document 2 JP6-336639A proposes a steel provided with HIC resistance and SSC resistance by essentially adding Cr, Ni and Cu.
  • Patent Document 3 JP2002-60894A proposes a steel in which the HIC resistance and SSC resistance are enhanced by defining the specific ranges of amounts of C, Ti, N, V and O.
  • Patent Document 4 JP2010-24504A
  • a high-strength steel in which, by reducing the amounts of C and Mn and by adding 0.5% or more of Mo, the hardening of weld heat affected zone is restrained, and both of HIC resistance and SSC resistance of base metal and HAZ are achieved.
  • Patent Document 5 describes a resistance welded tube for hollow stabilizer having a composition containing C: 0.03 to 0.10 weight%, Si: 0.20 to 1.0 weight%, Mn: 1.0-2.5 weight%, P: 0.03 weight% or less, S: 0.005 weight% or less, N+O: 150 ppm or less, Al: 0.01 to 0.1 weight%, B: 0.0050 weight% or less, Ti: 0.02-0.20 weight%, Nb: 0.02-0.10 weight% and Ca: 0.0050 weight% or less.
  • An objective of the present invention is to provide a low alloy steel in which a HAZ has excellent hydrogen embrittlement resistance in wet hydrogen sulfide environments or the like without requiring much cost.
  • HZ Heat Affected Zone
  • the reason why the HAZ is highly susceptible to hydrogen embrittlement is as follows.
  • hydrogen intrudes into the steel on account of corrosion reaction.
  • This hydrogen can move freely in the crystal lattice of the steel.
  • This hydrogen is so-called diffusible hydrogen.
  • This hydrogen accumulates in a dislocation or a vacancy, which is one kind of defects in the crystal lattice to embrittle the steel.
  • the HAZ is an as-quenched structure being heated to a high temperature by the heat history of welding, and cooled rapidly. Therefore, in the HAZ, the dislocations and vacancies in which hydrogen is trapped exist densely as compared with a thermally refined base metal. As a result, it is considered that the HAZ is highly susceptible to hydrogen embrittlement as compared with the base metal.
  • a low alloy steel in which a HAZ has excellent resistance to embrittlement attributable to hydrogen such as stress corrosion cracking in wet hydrogen sulfide environments.
  • This low alloy steel is best suitable as a starting material of a steel pipe for the transmission of crude oil or natural gas.
  • C carbon
  • C is an element effective in enhancing the hardenability of steel and increasing the strength thereof. In order to achieve these effects, 0.01% or more of C must be contained. However, if the content of C exceeds 0.15%, the hardness in the quenched state increases too much, and the HAZ is hardened, so that the hydrogen embrittlement susceptibility of HAZ is enhanced. Therefore, the C content is set to 0.01 to 0.15%.
  • the lower limit of the C content is preferably 0.02%, further preferably 0.03%.
  • the C content is preferably 0.12% or less, further preferably less than 0.10%.
  • Si silicon is an element effective for deoxidation, but brings about a decrease in toughness if being contained excessively. Therefore, the Si content is set to 3% or less.
  • the Si content is preferably 2% or less.
  • the lower limit of the Si content is not particularly defined; however, even if the Si content is decreased, the deoxidizing effect decreases, the cleanliness of steel is deteriorated, and an excessive decrease in the Si content leads to an increase in production cost. Therefore, the Si content is 0.01% or more.
  • Mn manganese
  • Mn manganese
  • the Mn content is set to 3% or less.
  • the lower limit of the Mn content is not particularly defined; however, in order to achieve the strength increasing effect of Mn, 0.2% or more of Mn is contained.
  • the lower limit thereof is further preferably 0.4%, and the preferable upper limit thereof is 2.8%.
  • B (boron) is an element that constitutes the findings, which are the basis of the present invention. As described before, B occupies the accumulation site of hydrogen, such as the dislocation or vacancy in the HAZ. Therefore, B is an element effective in enhancing the hydrogen embrittlement resistance. Furthermore, when a steel material is produced, B segregates at grain boundaries, thereby enhancing the hardenability indirectly, and contributes to the improvement in strength. In order to achieve these effects, 0.005% or more of B must be contained. On the other hand, if B is contained excessively, borides precipitate in large amounts in the HAZ, the interface between a matrix and borides acts as the accumulation site of hydrogen, and inversely embrittlement is produced. Therefore, the B content is set to 0.006 to 0.050%. The lower limit of the B content is preferably 0.008%. The upper limit thereof is preferably 0.045%, further preferably 0.040%.
  • the lower limit of the B content be controlled according to the highest hardness of HAZ. That is to say, in order to attain sufficient hydrogen embrittlement resistance, the B content is in the range satisfying Formula (1) in the relationship with the maximum value of Vickers hardness of HAZ: 0.005 ⁇ Hv / 300 + 0.0023 ⁇ B where, "Hv” in the formula means the maximum value of Vickers hardness of HAZ, and "B” means the content of B (mass%).
  • the maximum value of Vickers hardness of HAZ is a value that is determined by a Vickers test in which the test force is 98.07N in conformity to JIS Z2244.
  • A1 (aluminum) is an element effective for deoxidation, but if being contained excessively, the effect is saturated, and also the toughness is decreased. Therefore, the Al content is set to 0.08% or less.
  • the Al content is preferably 0.06% or less.
  • the lower limit of the Al content is not particularly defined; however, an excessive decrease in the Al content does not sufficiently achieve the deoxidizing effect, deteriorates the cleanliness of steel, and also increases the production cost. Therefore, 0.001% or more of Al is contained.
  • the Al content in the present invention means the content of acid soluble Al (so-called "sol.Al").
  • the low alloy steel in accordance with the present invention contains the above-described elements, and the balance consists of Fe and impurities.
  • the "impurities” mean components that are mixed on account of various factors including raw materials such as ore or scrap when a steel material is produced on an industrial scale. Of the impurities, concerning the elements described below, the content thereof must be restricted stringently.
  • N nitrogen
  • the N content must be restricted to 0.01% or less.
  • the N content is preferably 0.008% or less.
  • the lower limit of the N content is not particularly defined; however, an excessive decrease in the N content leads to a remarkable increase in production cost. Therefore, the lower limit of the N content is preferably 0.0001%.
  • P phosphorus
  • HAZ tungsten carbide
  • the P content is restricted to 0.05% or less.
  • the lower limit of the P content is not particularly defined; however, an excessive decrease in the P content leads to a remarkable increase in production cost. Therefore, the lower limit of the P content is preferably 0.001%.
  • S sulfur
  • S sulfur
  • the lower limit of the S content is not particularly defined; however, an excessive decrease in the S content leads to a remarkable increase in production cost. Therefore, the lower limit of the S content is preferably 0.0001%.
  • the O content exists in the steel as an impurity. If much O is contained, large amounts of oxides are formed, and the workability and ductility are deteriorated. Therefore, the O content must be set to 0.03% or less.
  • the O content is preferably 0.025% or less.
  • the lower limit of the O content need not particularly be defined; however, an excessive decrease in the O content leads to a remarkable increase in production cost. Therefore, the O content is preferably 0.0005% or more.
  • the low alloy steel in accordance with the present invention may contain the elements described below in lieu of a part of Fe.
  • One or more elements selected from Cr (chromium), Mo (molybdenum), Ni (nickel) and Cu (copper) may be contained because these elements enhance the hardenability and contribute to the improvement in strength. However, if the contents thereof are excessively high, the HAZ is hardened remarkably, and therefore the hydrogen embrittlement susceptibility may be enhanced. Therefore, if one or more elements of these elements are contained, the contents thereof are set to 1.5% or less in total.
  • the lower limit of the contents of these elements is preferably 0.02%, further preferably 0.05%.
  • the upper limit thereof is preferably 1.2%.
  • One or more elements selected from Ti (titanium), V (vanadium) and Nb (niobium) may be contained because these elements are elements that form fine carbo-nitrides and contribute to the improvement in strength, and also stably supplement diffusible hydrogen, and bring about a considerable effect of reducing the hydrogen embrittlement susceptibility.
  • the contents thereof are excessively high, the formation of carbo-nitrides becomes excessive, and therefore the toughness may be decreased. Therefore, if one or more elements of these elements are contained, the contents thereof are set to 0.2% or less in total.
  • the lower limit of the contents of these elements is preferably 0.001%, further preferably 0.003%.
  • the upper limit thereof is preferably 0.15%.
  • At least one of Ca (calcium) and Mg (magnesium) may be contained because these elements improve the hot workability of steel. However, if the contents thereof are excessively high, these elements combine with oxygen to remarkably decrease the cleanliness, so that the hot workability may rather be deteriorated. Therefore, if at least one kind of these elements is contained, the contents thereof are set to 0.05% or less in total.
  • the lower limit of the contents of Ca and/or Mg is preferably 0.0005%, further preferably 0.001%.
  • the upper limit thereof is preferably 0.03%.
  • test material was prepared by machining a 12 mm-thick low alloy steel plate having the chemical composition given in Table 1 into a 12 mm square and a 100 mm length. This test material was subjected to HAZ-simulated thermal cycle in which the test material was heated to a temperature of 1350°C, at which the hardening of HAZ was remarkable, for 3 seconds by high-frequency induction heating, and thereafter was rapidly cooled. By using this test material, the tests described below were conducted.
  • test specimen having a thickness of 2 mm, a width of 10 mm, and a length of 75 mm was sampled from the obtained test material, and the SCC resistance was evaluated by a four-point bending test in conformity to EFC16 specified by the European Federation of Corrosion.
  • the test specimen was immersed in a 5% common salt + 0.5% acetic acid aqueous solution of normal temperature (24°C), in which 1 atm hydrogen sulfide gas is saturated, for 336 hours, whereby the presence of occurrence of SSC was examined.
  • a low alloy steel in which a HAZ has excellent resistance to embrittlement attributable to hydrogen such as stress corrosion cracking in wet hydrogen sulfide environments.
  • This low alloy steel is best suitable as a starting material of a steel pipe for the transmission of crude oil or natural gas.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Geology (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Mining & Mineral Resources (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Environmental & Geological Engineering (AREA)
  • Fluid Mechanics (AREA)
  • General Life Sciences & Earth Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Claims (8)

  1. Tube d'acier servant à transmettre du pétrole brut ou du gaz naturel, sachant que le tube d'acier est fait d'acier faiblement allié constitué de, en pourcentage massique,
    C : 0,01 à 0,15 %,
    Si : 0,01 % à 3 %,
    Mn : 0,2 % à 3 %,
    B : 0,006 à 0,050 %,
    Al : 0,001 % à 0,08 %,
    optionellement
    un ou plusieurs éléments sélectionnés parmi Cr, Mo, Ni et Cu : 1,5 % ou moins au total ;
    un ou plusieurs éléments sélectionnés parmi Ti, V et Nb : 0,2 % ou moins au total ; et
    Ca et/ou Mg : 0,05 % ou moins au total ;
    l'équilibre étant en Fe et en impuretés,
    sachant que dans les impuretés,
    N : 0,01 % ou moins,
    P : 0,05 % ou moins,
    S : 0,03 % ou moins, et
    O : 0,03 % ou moins, sachant que
    la teneur en B satisfait la Formule (1) : 0,005 × Hv / 300 + 0,0023 ≤ B
    Figure imgb0006
     la valeur « Hv » de la formule indiquant la valeur maximum de la dureté de Vickers dans une zone affectée par la chaleur et « B » indiquant la teneur en B en % massique.
  2. Tube d'acier servant à transmettre du pétrole brut ou du gaz naturel selon la revendication 1, sachant que l'acier faiblement allié contient, en pourcentage en masse,
    un ou plusieurs éléments sélectionnés parmi Cr, Mo, Ni et Cu : de 0,02 à 1,5 % au total.
  3. Tube d'acier servant à transmettre du pétrole brut ou du gaz naturel selon la revendication 1 ou 2, sachant que l'acier faiblement allié contient, en pourcentage massique,
    un ou plusieurs éléments sélectionnés parmi Ti, V et Nb : 0,001 à 0,2 % au total.
  4. Tube d'acier servant à transmettre du pétrole brut ou du gaz naturel selon l'une des revendications de 1 à 3, sachant que l'acier faiblement allié contient, en pourcentage massique,
    Ca et/ou Mg : 0,0005 à 0,05 % au total.
  5. Utilisation d'un acier faiblement allié pour un tube d'acier servant à transmettre du pétrole brut ou du gaz naturel,
    l'acier faiblement allié étant constitué de, en pourcentage massique,
    C : 0,01 à 0,15 %,
    Si : 0,01 % à 3 %,
    Mn : 0,2 % à 3 %,
    B : 0,006 à 0,050 %,
    Al : 0,001 % à 0,08 %,
    optionnellement
    un ou plusieurs éléments sélectionnés parmi Cr, Mo, Ni et Cu : 1,5 % ou moins au total ;
    un ou plusieurs éléments sélectionnés parmi Ti, V et Nb : 0,2 % ou moins au total ; et
    Ca et/ou Mg : 0,05 % ou moins au total ;
    l'équilibre étant en Fe et en impuretés,
    sachant que dans les impuretés,
    N : 0,01 % ou moins,
    P : 0,05 % ou moins,
    S : 0,03 % ou moins, et
    O : 0,03 % ou moins, sachant que
    la teneur en B satisfait la Formule (1) : 0,005 × Hv / 300 + 0,0023 ≤ B
    Figure imgb0007
     la valeur « Hv » de la formule indiquant la valeur maximum de la dureté de Vickers dans une zone affectée par la chaleur et « B » indiquant la teneur en B en % massique.
  6. Utilisation d'un acier faiblement allié pour un tube d'acier servant à transmettre du pétrole brut ou du gaz naturel selon la revendication 5, où l'acier faiblement allié contient, en pourcentage massique,
    un ou plusieurs éléments sélectionnés parmi Cr, Mo, Ni et Cu : 0,02 à 1,5 % au total.
  7. Utilisation d'un acier faiblement allié servant à transmettre du pétrole brut ou du gaz naturel selon la revendication 5 ou 6, où l'acier faiblement allié contient, en pourcentage massique,
    un ou plusieurs éléments sélectionnés parmi Ti, V et Nb : 0,001 à 0,2 % au total.
  8. Utilisation d'un acier faiblement allié pour un tube d'acier servant à transmettre du pétrole brut ou du gaz naturel selon une des revendications 5 à 7, où l'acier faiblement allié contient, en pourcentage massique,
    Ca et/ou Mg : 0,0005 à 0,05 % au total.
EP12865286.4A 2012-01-12 2012-12-17 Acier faiblement allié Active EP2803743B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2012004103 2012-01-12
PCT/JP2012/082606 WO2013105395A1 (fr) 2012-01-12 2012-12-17 Acier faiblement allié

Publications (3)

Publication Number Publication Date
EP2803743A1 EP2803743A1 (fr) 2014-11-19
EP2803743A4 EP2803743A4 (fr) 2016-03-09
EP2803743B1 true EP2803743B1 (fr) 2018-08-22

Family

ID=48781354

Family Applications (1)

Application Number Title Priority Date Filing Date
EP12865286.4A Active EP2803743B1 (fr) 2012-01-12 2012-12-17 Acier faiblement allié

Country Status (11)

Country Link
US (1) US20140348695A1 (fr)
EP (1) EP2803743B1 (fr)
JP (1) JP5418702B2 (fr)
CN (1) CN104053803B (fr)
AU (1) AU2012365128B2 (fr)
BR (1) BR112014017178A8 (fr)
CA (1) CA2856247C (fr)
ES (1) ES2689229T3 (fr)
IN (1) IN2014DN05913A (fr)
MX (1) MX2014008504A (fr)
WO (1) WO2013105395A1 (fr)

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011096510A1 (fr) * 2010-02-04 2011-08-11 新日本製鐵株式会社 Tuyau en acier soudé à haute résistance et procédé pour sa production

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5255746A (en) 1975-10-30 1977-05-07 Mitsubishi Heavy Ind Ltd Build up process of high speed winder driving roll
JPS55122820A (en) * 1979-03-13 1980-09-20 Kawasaki Steel Corp Manufacture of alloyed zinc-plated high tensile steel sheet with superior workability
JPS6336639A (ja) 1986-07-31 1988-02-17 Nec Corp デ−タ交換方式
JPH05320759A (ja) * 1992-05-19 1993-12-03 Nippon Steel Corp 微細な亜粒界を有する鋳片および微細な金属組織を有する厚鋼板の製造法
JP3793253B2 (ja) * 1995-08-11 2006-07-05 新日本製鐵株式会社 加工性に優れた熱延鋼板の製造方法
JP4272284B2 (ja) * 1998-12-11 2009-06-03 日新製鋼株式会社 疲労耐久性に優れた中空スタビライザー用電縫溶接鋼管
JP5229300B2 (ja) * 2000-03-31 2013-07-03 Ｊｆｅスチール株式会社 溶接部靱性に優れた高強度厚肉溶接ベンド鋼管用の素管およびその製造方法
JP3714136B2 (ja) 2000-08-18 2005-11-09 Ｊｆｅスチール株式会社 電子ビーム溶接特性および耐サワー性能に優れた鋼
JP4171281B2 (ja) * 2002-10-17 2008-10-22 新日本製鐵株式会社 加工性に優れた鋼板及びその製造方法
JP5042744B2 (ja) * 2007-08-23 2012-10-03 新日本製鐵株式会社 エレクトロスラグ溶接方法
JP5547368B2 (ja) * 2007-09-12 2014-07-09 関西ペイント株式会社 水性塗料組成物
JP2010024504A (ja) 2008-07-22 2010-02-04 Sumitomo Metal Ind Ltd ラインパイプ用継目無鋼管およびその製造方法
JP5000619B2 (ja) * 2008-10-14 2012-08-15 新日本製鐵株式会社 溶接金属の靭性に優れた１パス大入熱溶接継手およびその製造方法

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011096510A1 (fr) * 2010-02-04 2011-08-11 新日本製鐵株式会社 Tuyau en acier soudé à haute résistance et procédé pour sa production
EP2532765A1 (fr) * 2010-02-04 2012-12-12 Nippon Steel Corporation Tuyau en acier soudé à haute résistance et procédé pour sa production

Also Published As

Publication number Publication date
BR112014017178A8 (pt) 2017-07-04
WO2013105395A1 (fr) 2013-07-18
AU2012365128A1 (en) 2014-06-26
ES2689229T3 (es) 2018-11-12
JPWO2013105395A1 (ja) 2015-05-11
EP2803743A1 (fr) 2014-11-19
MX2014008504A (es) 2014-10-14
CA2856247A1 (fr) 2013-07-18
EP2803743A4 (fr) 2016-03-09
AU2012365128B2 (en) 2015-09-03
JP5418702B2 (ja) 2014-02-19
US20140348695A1 (en) 2014-11-27
CA2856247C (fr) 2017-08-01
IN2014DN05913A (fr) 2015-06-05
BR112014017178A2 (pt) 2017-06-13
CN104053803B (zh) 2016-08-24
CN104053803A (zh) 2014-09-17

Similar Documents

Publication Publication Date Title
EP2865777B1 (fr) Tuyau en acier inoxydable à forte résistance sans soudure ayant une excellente résistance à la corrosion pour des puits de pétrole, et son procédé de fabrication
JP4538094B2 (ja) 高強度厚鋼板およびその製造方法
US10233523B2 (en) Carburization resistant metal material
AU2014294080B2 (en) High-strength steel material for oil well and oil well pipes
CN110168124B (zh) 双相不锈钢及其制造方法
EP3575427B1 (fr) Acier inoxydable à deux phases plaquée et son procédé de production
WO2005017222A1 (fr) Tuyau en acier inoxydable a haute resistance a la corrosion utilise dans un puits de petrole et procede de production correspondant
WO2003044238A1 (fr) Acier inoxydable super-austenitique
KR20210072140A (ko) 고 Mn 강판 및 그 제조 방법
EP2803741B1 (fr) Procédé de traitement thermique après soudage d'un tuyau en acier faiblement allié
US20120003116A1 (en) Austenitic stainless steel
WO2005042793A1 (fr) Tuyau en acier inoxydable haute resistance pour une canalisation presentant une excellente resistance a la corrosion, et procede de production associe
WO2016079920A1 (fr) Tuyau sans soudure en acier inoxydable à haute résistance pour des puits de pétrole
KR20130133030A (ko) 2상 스테인리스강
JP4952708B2 (ja) マルテンサイト系ステンレス鋼およびその製造方法
US8747575B2 (en) 655 MPa grade martensitic stainless steel having high toughness and method for manufacturing the same
EP2803743B1 (fr) Acier faiblement allié
JP5890342B2 (ja) 二相系ステンレス鋼材および二相系ステンレス鋼管
EP4023785A1 (fr) Acier inoxydable austénitique hautement résistant à la corrosion ayant une excellente résistance au choc et une excellente aptitude au façonnage à chaud

Legal Events

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

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20140801

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

DAX Request for extension of the european patent (deleted)
RA4 Supplementary search report drawn up and despatched (corrected)

Effective date: 20160208

17Q First examination report despatched

Effective date: 20161006

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/02 20060101ALI20171201BHEP

Ipc: C22C 38/24 20060101ALI20171201BHEP

Ipc: C22C 38/38 20060101ALI20171201BHEP

Ipc: C21D 9/14 20060101ALI20171201BHEP

Ipc: C22C 38/32 20060101ALI20171201BHEP

Ipc: C22C 38/42 20060101ALI20171201BHEP

Ipc: C22C 38/48 20060101ALI20171201BHEP

Ipc: C22C 38/46 20060101ALI20171201BHEP

Ipc: C22C 38/06 20060101ALI20171201BHEP

Ipc: C22C 38/58 20060101ALI20171201BHEP

Ipc: C22C 38/04 20060101ALI20171201BHEP

Ipc: C21D 9/00 20060101ALI20171201BHEP

Ipc: C22C 38/14 20060101ALI20171201BHEP

Ipc: C22C 38/44 20060101ALI20171201BHEP

Ipc: C22C 38/00 20060101AFI20171201BHEP

Ipc: C22C 38/12 20060101ALI20171201BHEP

Ipc: C21D 9/50 20060101ALI20171201BHEP

Ipc: C22C 38/54 20060101ALI20171201BHEP

Ipc: C21D 9/08 20060101ALI20171201BHEP

INTG Intention to grant announced

Effective date: 20171219

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

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTC Intention to grant announced (deleted)
INTG Intention to grant announced

Effective date: 20180406

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

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

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1032597

Country of ref document: AT

Kind code of ref document: T

Effective date: 20180915

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602012050261

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: NO

Ref legal event code: T2

Effective date: 20180822

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2689229

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20181112

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: 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: 20180822

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: 20180822

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: 20181222

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: 20181123

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: 20180822

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: 20181122

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1032597

Country of ref document: AT

Kind code of ref document: T

Effective date: 20180822

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

Ref country code: HR

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

Effective date: 20180822

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: 20180822

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: 20180822

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180822

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: 20180822

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: 20180822

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: 20180822

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: 20180822

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602012050261

Country of ref document: DE

Representative=s name: ZIMMERMANN & PARTNER PATENTANWAELTE MBB, DE

Ref country code: DE

Ref legal event code: R081

Ref document number: 602012050261

Country of ref document: DE

Owner name: NIPPON STEEL CORPORATION, JP

Free format text: FORMER OWNER: NIPPON STEEL & SUMITOMO METAL CORP., TOKYO, JP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602012050261

Country of ref document: DE

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: 20180822

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: 20180822

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: 20180822

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: 20190523

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

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

Effective date: 20181217

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

Ref country code: LU

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

Effective date: 20181217

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: 20180822

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: 20180822

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20181231

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: 20181217

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

Ref country code: BE

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

Effective date: 20181231

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

Ref country code: CH

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

Effective date: 20181231

Ref country code: GB

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

Effective date: 20181217

Ref country code: LI

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

Effective date: 20181231

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

Ref country code: MT

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

Effective date: 20181217

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

Ref country code: SE

Payment date: 20191210

Year of fee payment: 8

Ref country code: NL

Payment date: 20191114

Year of fee payment: 8

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: 20180822

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

Ref country code: ES

Payment date: 20200102

Year of fee payment: 8

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

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: 20180822

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

Ref country code: HU

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

Effective date: 20121217

Ref country code: MK

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

Effective date: 20180822

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: 20180822

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20210101

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

Ref country code: NL

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

Effective date: 20210101

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

Ref country code: SE

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

Effective date: 20201218

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20220412

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: 20201218

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

Ref country code: NO

Payment date: 20231212

Year of fee payment: 12

Ref country code: IT

Payment date: 20231110

Year of fee payment: 12

Ref country code: FR

Payment date: 20231108

Year of fee payment: 12

Ref country code: DE

Payment date: 20231031

Year of fee payment: 12