EP2143815A1 - Austenitischer edelstahl mit hervorragender beständigkeit gegenüber korngrenzkorrosion und spannungsrisskorrosion sowie verfahren zur herstellung des austenitischen edelstahls - Google Patents

Austenitischer edelstahl mit hervorragender beständigkeit gegenüber korngrenzkorrosion und spannungsrisskorrosion sowie verfahren zur herstellung des austenitischen edelstahls Download PDF

Info

Publication number
EP2143815A1
EP2143815A1 EP08752039A EP08752039A EP2143815A1 EP 2143815 A1 EP2143815 A1 EP 2143815A1 EP 08752039 A EP08752039 A EP 08752039A EP 08752039 A EP08752039 A EP 08752039A EP 2143815 A1 EP2143815 A1 EP 2143815A1
Authority
EP
European Patent Office
Prior art keywords
stainless steel
less
austenitic stainless
temperature
steel material
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP08752039A
Other languages
English (en)
French (fr)
Other versions
EP2143815B1 (de
EP2143815A4 (de
Inventor
Kiyoshi Kiuchi
Ikuo Ioka
Chiaki Kato
Nobutoshi Maruyama
Ichiro Tsukatani
Makoto Tanabe
Jumpei Nakayama
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.)
Kobe Steel Ltd
Kobelco Research Institute Inc
Japan Atomic Energy Agency
Original Assignee
Kobe Steel Ltd
Kobelco Research Institute Inc
Japan Atomic Energy Agency
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 Kobe Steel Ltd, Kobelco Research Institute Inc, Japan Atomic Energy Agency filed Critical Kobe Steel Ltd
Publication of EP2143815A1 publication Critical patent/EP2143815A1/de
Publication of EP2143815A4 publication Critical patent/EP2143815A4/de
Application granted granted Critical
Publication of EP2143815B1 publication Critical patent/EP2143815B1/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
    • 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • the present invention relates to an austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance even under severe intergranular corrosion environments such as a corrosion environment for a boiling heat transfer surface in a high-concentration nitric acid solution containing highly oxidizing metal ions and an environment in high-temperature high-pressure water under neutron irradiation, and relates to a method for producing an austenitic stainless steel material excellent in intergranular corrosion resistance and stress corrosion cracking resistance even under the severe intergranular corrosion environments.
  • austenitic stainless steels generally show corrosion resistance even in environments containing strong oxidizing acids such as nitric acid by forming a passive film on the surface.
  • the austenitic stainless steels have been used, for example: as a structural material in nitric acid production plants; and as a material for dissolvers for dissolving the spent nuclear fuels with high-concentration nitric acid and acid recovery evaporators for recovery of nitric acid by distillation of the solution in the dissolver in plants for reprocessing spent nuclear fuels.
  • the austenitic stainless steels are also used as a material for light water reactor cores under the environment in high-temperature high-pressure water under neutron irradiation.
  • an austenitic stainless steel material is used as a material for the dissolver or the acid recovery evaporator in plants for reprocessing spent nuclear fuels
  • metal ions such as cerium ion (Ce 4+ ), ruthenium ion (Ru 3+ ) and chromium ion (Cr 6+ ) are released into the nitric acid from the spent nuclear fuels and thus, the nitric acid solution becomes more oxidative than that in the nitric acid production plant. For that reason, the austenitic stainless steel is more susceptible to corrosion accompanied by intergranular corrosion.
  • the following measures are taken, for use of an austenitic stainless steel material under environments of high-temperature nitric acid containing highly oxidizing metal ions: First, the carbon content in the austenitic stainless steel is reduced as much as possible, for prevention of generation of Cr-depletion layer, which is the cause of intergranular corrosion. Nb is added as needed in small amount to the austenitic stainless steel. In addition, the austenitic stainless steel material is subjected to solution treatment.
  • Patent Document 1 disclosed an austenitic stainless steel containing C at 0.005 wt% or less, Si at 0.4 wt% or less, Mn at 0.1 to 12 wt%, P at 0.005 wt% or less, Ni at 7 to 28 wt%, Cr at 15 to 30 wt%, N at 0.06 to 0.30 wt% and the balance of essentially Fe.
  • the intergranular corrosion resistance of the austenitic stainless steel is improved, by suppressing aggregation of P in grain boundaries, while the P content in the austenitic stainless steel is restricted.
  • Patent Document 3 discloses an austenitic stainless steel containing C at 0.02 wt% or less, Si at 0.5 wt% or less, Mn at 0.5 wt% or less, P at 0.03 wt% or less, S at 0.002 wt% or less, Ni at 10 to 16 wt%, Cr at 16 to 20 wt%, Mo at 2.0 to 3.0 wt%, N at 0.06 to 0.15 wt% and the balance of essentially Fe.
  • Patent Document 4 discloses a method of producing an austenitic stainless steel resistant to corrosion by high-temperature nitric acid containing oxidizing metal ions. Specifically, the stainless steel is heat-treated at a temperature in the range of 650 to 950°C for 1 minute or more. Then, if the heat-treatment temperature is lower than the range of 650 to 850°C, the stainless steel is cooled to ordinary temperature by rapid or natural cooling. Alternatively if the heat-treatment temperature is higher than the range of 850 to 950°C, the stainless steel is cooled to ordinary temperature by rapid cooling. The austenitic stainless steel prepared in this way shows favorable resistance to corrosion by high-temperature nitric acid.
  • Patent Document 5 disclosed a method of producing an austenitic stainless steel containing B at 30 wt ppm or less and satisfying, when the diameter of the austenitic grains is designated by d, the following formula: B (wt ppm) ⁇ d ( ⁇ m) ⁇ 700.
  • the austenitic stainless steel when subjected to solution treatment, as heated at a particular temperature, which is a function of B (wt ppm) ⁇ d ( ⁇ m), or higher, shows excellent intergranular corrosion resistance and intergranular stress corrosion cracking resistance.
  • Patent Document 7 discloses a method of producing an austenitic stainless steel by forming clean grain boundaries. Specifically, the austenitic stainless steel is cold worked to a working ratio of 40% or more. Then, the stainless steel obtained after cold working is kept at a temperature that is lower than the recrystallization temperature and allows carbide precipitation, for recrystallization in a temperature range prohibiting segregation of P and other elements in grain boundaries. After the treatment, the austenitic stainless steel shows favorable corrosion resistance even corrosive environment of nitric acid solution containing oxidants.
  • the austenitic stainless steel material when used in a light water reactor core under an environment in high-temperature high-pressure water exposed to neutron irradiation, it becomes more susceptible to intergranular stress corrosion cracking (IGSCC) by long-term irradiation.
  • IGSCC intergranular stress corrosion cracking
  • a solution-treated austenitic stainless steel in solid-solution state shows resistance to intergranular stress corrosion cracking outside the reactor core where no neutron is irradiated, but such resistance is lost when it is exposed to high level of irradiation, in particular to fluence equivalent to or more than about 1.0 ⁇ 10 21 n/cm 2 or more in the reactor core.
  • Such cracking which is also called irradiation-assisted stress corrosion cracking (IASCC) is a concern recently in old light water reactors.
  • Patent Documents 8 and 9 disclose methods of adjusting the elements constituting the austenitic stainless steel.
  • Patent Document 10 discloses a steel that is lower in Cr deficiency in grain boundaries and has dispersed Cr-depletion regions, which is prepared by reducing the amount of carbide precipitation per unit grain boundary by means of heating a Ni-Cr austenitic stainless steel that have a C content restricted to 0.03 wt% or less and a content of N, which is higher in solid solution-forming efficiency, adjusted to 0.15 wt% or less in its chemical composition for prevention of precipitation of carbides, a cause of intergranular stress corrosion cracking, in grain boundaries in a temperature range of 1100 to 1300°C, and a preparative method thereof.
  • Patent Document 11 discloses a high-Ni-content austenitic steel excellent in neutron deterioration resistance prepared by subjecting an austenitic stainless steel in the chemical composition containing C at 0.005 to 0.08 wt% or less, Mn at 0.3 wt% or less, Si+P+S at 0.2 wt% or less, Ni at 25 to 40 wt%, Cr at 25 to 40 wt%, Mo+W at 5.0 wt% or less, Nb+Ta at 0.3 wt% or less, Ti at 0.3 wt% or less, B at 0.001 wt% or less and others, to solution treatment in a temperature range of 1000 to 1150°C, cold working to its ratio of 30%, and heat treatment in a temperature range of 600 to 750°C for 100 hours.
  • Patent Document 12 discloses a high-alloy austenitic stainless steel containing C at 0.05 wt% or less, Si at 1.0 to 4.0 wt%, Mn at 0.3 wt% or less, Ni at 6 to 22 wt%, Cr at 18 to 23 wt%, Cu at 1 to 3 wt%, Mo at 0.3 to 2.0 wt%, N at 0.05 wt% or less, S at 0.004 wt% or less, a small amount of B added at 0.0005 to 0.005 wt%, one or both of Ca and Mg added in an amount of: [S] ⁇ [Mg]+1/2 and [Ca] ⁇ 0.007, and the balance of essentially Fe. It is disclosed that the austenitic stainless steel is improved significantly in processing efficiency without deterioration in its favorable corrosion resistance.
  • an austenitic stainless steel is used in an acid recovery evaporator by thermosiphon process, in which nitric acid is recovered by distillation of a nitric acid solution in heat-transfer pipes by application of heat from outside, generation of highly oxidizing ions associated with distillation of nitric acid and thermal decomposition and solubilization by reductive reaction occur at the same time.
  • the corrosion environment to the austenitic stainless steel is in a boiling-inducing heat transfer surface corrosion. It is a severe environment in which the corrosion rate is higher than that by immersion corrosion at the same metal surface temperature and the corrosion rate increases gradually over time. For that reason, even if the austenitic stainless steel materials described in Patent Documents 1 to 7 or the preparation methods thereof are used, there still remains a possibility of severe intergranular corrosion.
  • Patent Document 1 discloses that it is possible to suppress formation of MnS and thus generation of the tunnel-like corrosion caused by MnS that is extending in the rolling direction by restricting the P content, and Patent Documents 2 and 3, by adding Ca and Ce that have strong binding force to S.
  • Patent Documents 4 and 5 only consider economy, and the stainless steels cannot be considered to be resistance to nitric acid corrosion consistently.
  • Patent Document 6 discloses an austenitic stainless steel containing B at 5 wt ppm or less and one or more elements selected from Ti, Nb, V, Hf and Ta in a total amount of 1.0 wt% or less.
  • the test in Patent Document 6 was carried out under a mild corrosive condition of immersion only in boiling 65% nitric acid for 48 hours.
  • the test is an evaluation test simulating the corrosion environment containing highly oxidizing metal ions that is used in reprocessing plants for spent nuclear fuels, and is not suited for evaluation of advantages and disadvantages in corrosion resistance of stainless steels.
  • Patent Document 7 discloses a thermomechanical treatment of cold working a steel material to a working ratio of 40% or more, recrystallizing it by keeping it at a temperature in the temperature range lower than the recrystallization temperature but allowing precipitation of carbides and prohibiting segregation for example of P in grain boundaries, but the C content in the steel was not specified sufficient.
  • Cr based carbides a possible cause of intergranular corrosion, are dispersed uniformly, but the Cr-depletion layers formed around the Cr based carbides precipitating in great amounts lead to acceleration of corrosion.
  • the heat treatment is not effective at all for removal of the impurity elements, such as P, S, N and O, segregating in grain boundaries.
  • the amounts of the impurity elements, such as P, segregating in grain boundaries are not described sufficiently, and no measure is taken for their removal. Accordingly, the method unlikely gives desired corrosion resistance.
  • Patent Document 11 specifies that the contents of elements P, S, Si, Nb, Ta, Ti and B are preferably lower, and the contents of Nb, Ta and Ti are specifications when used as a deoxidizing agent, and thus, the contents are not adjusted intentionally for improvement in stress corrosion cracking resistance.
  • Mn and B contents the B content is specified as 0.001 wt% or less, the lowest value practically possible by the steel making technologies at the time of invention, but the lowest value of the B content found in Examples is 0.0003 wt%.
  • the influence exerted by a B content of less than 0.0003 wt% on stress corrosion cracking resistance is unknown. Because the C content, which is the most important constituent component leading to deterioration in stress corrosion cracking resistance, is not reduced sufficient, it is not always possible to obtain favorable stress corrosion cracking resistance.
  • the lower limit value of the B content is restricted to 0.0005 wt% for improvement in hot processing efficiency and the higher limit value to 0.005 wt% for prevention of deterioration in intergranular corrosion resistance, but it is obvious that the limitation above is not sufficiently effective in improving the corrosion resistance.
  • Patent Document 13 The method of preparing a single crystal described in Patent Document 13 imposes restriction on casting condition, in particular on withdrawing velocity, which makes industrial application thereof, in particular application to large-sized materials, difficult.
  • Patent Document 14 discloses that stainless steel production methods include deformation annealing method, Tammann method, Bridgemann method, floating zone melting method, unidirectional solidification method, and continuous casting method and use of a unidirectional solidification method or a continuous casting method is preferable for production of relatively large-sized steel.
  • the patent document does not specify typical manufacturing conditions, and it is doubtful that a single-crystalline metal structure having subcrystal grains can be obtained.
  • the content of the steel components, in particular Ni is not sufficient for prevention of swelling under the neutron irradiation environment, and it is unlikely that desired irradiation resistance is obtained.
  • the present invention was made to solve the problems above. It is an object of the invention to provide an austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance even under two environments: one environment is a corrosion environment for a boiling heat transfer surface in a high-concentration nitric acid solution containing highly oxidizing metal ions; and another environment is an environment in high-temperature high-pressure water exposed to neutron irradiation. It is another object of the invention to provide a method for producing an austenitic stainless steel material excellent in intergranular corrosion resistance and stress corrosion cracking resistance even under the abovementioned two environments.
  • an austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance comprises: C: 0.005 wt% or less; Si: 0.5 wt% or less; Mn: 0.5 wt% or less; P: 0.005 wt% or less; S: 0.005 wt% or less; Ni: 15.0 to 40.0 wt%, Cr: 20.0 to 30.0 wt%, N: 0.01 wt% or less; O: 0.01 wt% or less; and the balance of Fe and inevitable impurities, wherein the content of B included in the inevitable impurities is 3 wt ppm or less.
  • the Cr content in steel is 20 wt% or more, the Cr content remains at about 12 wt%, which is needed for generation of a passive film, even after generation of the depletion layer by carbide precipitation.
  • Patent Document 7 teaches that, in steels at conventional impurity level, a B content of more than 5 wt ppm shows at least an adverse effect leading to deterioration in intergranular corrosion resistance, and a B content of more than 10 wt ppm, to particularly drastic deterioration.
  • the detection limit in conventional chemical analysis was about 2 wt ppm, but it is now possible to analyze B content in the order of wt ppm or less and to elucidate the relationship between a trace content of B and intergranular corrosion or stress corrosion cracking, by GD-MS analysis.
  • Contamination at about 2 to 5 wt ppm from raw materials such as alloy irons and scraps was inevitable in ingots of normal austenitic stainless steels, but it became possible to select a raw material lower in B content by progress of analysis technology and additionally to produce an ingot of low austenitic stainless steel lower in B content by progress of the steel-making technology such as oxidizing refining.
  • the precipitation reaction above may possibly proceed insufficiently from the point of reaction rate in a material having a chemical composition lower in the amount of reactive impurity elements such as C, P, S, N and O, as in the present invention, it is also effective to cold work the material to a working ratio of 40% or more and less than 75%, apply deposit precipitation treatment under strain aging on it by heating and holding it in a temperature range of 500 to 650°C for 30 minutes or more, and then, heat and hold it in a temperature range of 750°C or higher for 10 minutes or more.
  • Boron is the factor most important in the configuration of the present invention. It is fundamentally an impurity element that segregates in grain boundaries and causes deterioration in intergranular corrosion resistance and stress corrosion cracking resistance, and thus, the content thereof is preferably lower as much as possible. It was not possible to determine a B content of 0.0003 wt% or less by conventional analytical methods. However, the inventors have identified the relationship between the trace concentration of B and the corrosion resistance by using recent analytical methods and, as a result, found that it was possible to prevent the intergranular corrosion and the stress corrosion cracking completely by reducing the concentration thereof to 0.0003 wt% or less. Thus, the B content is 3 wt ppm (0.0003 wt%) or less from the viewpoint above. It is more preferably 1.5 wt ppm or less.
  • Titanium An amount stoichiometrically equivalent to or more than the total content of C, P, S, N and O. Titanium is a factor important in the configuration of the present invention and is added for complete removal of the impurity elements such as C, P, S, N and O, causes of intergranular corrosion, by conversion to Ti based carbides, nitrides and other compounds such as TiC, TiN, FeTiP, TiS and TiO 2 .
  • the contents of these impurity elements are already at en extremely lowered level in the steel ingot-forming phase.
  • studies by the inventors showed that trace amounts of impurity elements not removed by electrobeam melting could exert adverse effects on intergranular corrosion.
  • An electrobeam-melting method is employed in the steel ingot production process in the present embodiment.
  • the electrobeam-melting methods are basically grouped into drip melting method and cold-hearth melting method.
  • the drip melting method is a method of irradiating the edge of a raw material electrode with electron beam and spraying the generated droplets directly onto a water-cooled cylindrical mold in layer.
  • the cold-hearth melting method is a method of collecting the droplets generated on the edge of a raw material once in a water-cooled shallow copper container called cold hearth and depositing the molten metal on a base plate called starting block in layer, by pouring the molten metal overflowing therefrom onto a water-cooled cylindrical mold. Any one of the melting methods may be used in the present embodiment.
  • the precipitation treatment may be carried out for efficient and uniform dispersion of the carbides after cold working and before recrystallization treatment. Theoretically, it is desired then to heat the material at a constant temperature in the range of 500°C or higher for 30 minutes or more. On the other hand, high temperature shortens the period needed for carbide precipitation, but excessively high temperature leads to recovery and recrystallization before carbide precipitation. It prohibits precipitation at the dislocation sites once introduced and uniform dispersion of the carbides, because of preferential precipitation in grain boundaries, and thus leads to further growth of the grains. It consequently prohibits superior intergranular corrosion resistance and stress corrosion cracking resistance. From the viewpoints above, the carbide precipitation treatment is preferably carried out, as the stainless steel is heated consistently at a temperature in the range of 500 to 650°C for 30 minutes or more.
  • the sample of steel numbers R and S represent samples of Comparative Example, and contain Si at more than 0.5 wt% or Mn at more than 0.5 wt%.
  • Table 2 shows that the samples of steel numbers A to D and steel numbers K to L have intergranular corrosion resistance and stress corrosion cracking resistance more favorable than those of the samples of steel numbers E to J and steel numbers M to S.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
EP08752039.1A 2007-04-27 2008-04-24 Austenitischer edelstahl mit hervorragender beständigkeit gegenüber korngrenzkorrosion und spannungsrisskorrosion sowie verfahren zur herstellung des austenitischen edelstahls Active EP2143815B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2007117981 2007-04-27
JP2008015094 2008-01-25
PCT/JP2008/057940 WO2008136354A1 (ja) 2007-04-27 2008-04-24 耐粒界腐食性および耐応力腐食割れ性に優れたオーステナイト系ステンレス鋼およびオーステナイト系ステンレス鋼材の製造方法

Publications (3)

Publication Number Publication Date
EP2143815A1 true EP2143815A1 (de) 2010-01-13
EP2143815A4 EP2143815A4 (de) 2011-12-21
EP2143815B1 EP2143815B1 (de) 2014-01-08

Family

ID=39943465

Family Applications (1)

Application Number Title Priority Date Filing Date
EP08752039.1A Active EP2143815B1 (de) 2007-04-27 2008-04-24 Austenitischer edelstahl mit hervorragender beständigkeit gegenüber korngrenzkorrosion und spannungsrisskorrosion sowie verfahren zur herstellung des austenitischen edelstahls

Country Status (7)

Country Link
US (1) US20100116382A1 (de)
EP (1) EP2143815B1 (de)
JP (1) JP5756935B2 (de)
KR (1) KR20090130331A (de)
CN (1) CN101668873B (de)
RU (1) RU2420598C1 (de)
WO (1) WO2008136354A1 (de)

Families Citing this family (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5493060B2 (ja) * 2008-11-06 2014-05-14 スーパーピュアメタル合同会社 オーステナイト系高純度鉄合金
JP5493061B2 (ja) * 2008-11-06 2014-05-14 スーパーピュアメタル合同会社 耐照射損傷性に優れるオーステナイト系高純度鉄合金
JP5463527B2 (ja) * 2008-12-18 2014-04-09 独立行政法人日本原子力研究開発機構 オーステナイト系ステンレス鋼からなる溶接材料およびそれを用いた応力腐食割れ予防保全方法ならびに粒界腐食予防保全方法
CN101798659B (zh) * 2010-04-07 2012-01-04 朝阳鸿翔冶炼有限公司 用于不锈耐酸钢的低碳低磷镍铬铁合金的制备方法
BR112012026595A2 (pt) * 2010-04-19 2016-07-12 Jfe Steel Corp tubo de aço contendo cr para tubo para condução excelente em resistência a rachaduras por corrosão sob tensão intergranular em zona termicamente afetada soldada
EP2527156A1 (de) * 2011-05-25 2012-11-28 RLS Merilna Tehnika D.O.O. Vorrichtung und Verfahren zum Schreiben eines Musters in ein Substrat
CA2837281C (en) * 2011-06-28 2015-12-29 Nippon Steel & Sumitomo Metal Corporation Austenitic stainless steel tube
EP2737961B1 (de) * 2011-07-29 2016-12-14 Nippon Steel & Sumitomo Metal Corporation Verfahren zur herstellung eines austenitischen edelstahls
FR2980804B1 (fr) * 2011-09-30 2014-06-27 Areva Np Procede de realisation a partir d'une ebauche en acier inoxydable austenitique a faible teneur en carbone d'une gaine resistant a l'usure et a la corrosion pour reacteur nucleaire, gaine et grappe de commande correspondantes
JP6139224B2 (ja) * 2013-04-04 2017-05-31 株式会社東芝 高強度薄肉伝熱管ならびにその製造方法および伝熱管製造装置
CN105803356A (zh) * 2016-05-30 2016-07-27 苏州双金实业有限公司 一种具有韧性高性能的钢
US9541485B1 (en) * 2016-08-15 2017-01-10 Kuwait Institute For Scientific Research System for testing stress corrosion cracking
CN107916374A (zh) * 2017-11-15 2018-04-17 钢铁研究总院 一种耐应力腐蚀性能优异的控氮奥氏体不锈钢
CN110174460B (zh) * 2019-03-20 2022-10-28 苏州热工研究院有限公司 一种奥氏体不锈钢辐照加速应力腐蚀开裂敏感性的磁性评估方法
TWI751454B (zh) * 2019-11-29 2022-01-01 財團法人金屬工業研究發展中心 高強度耐腐蝕沃斯田鐵不銹鋼合金及其製造方法
CN112067402A (zh) * 2020-09-23 2020-12-11 广东省科学院半导体研究所 一种位错缺陷分析方法
CN112763396B (zh) * 2020-12-07 2022-09-20 中国核电工程有限公司 模拟核燃料后处理腐蚀性高放废液的料液及进行腐蚀试验的方法
CN112986113B (zh) * 2020-12-07 2022-11-11 中国核电工程有限公司 模拟核燃料后处理腐蚀性溶解液的料液及其使用方法
CN113252539B (zh) * 2020-12-07 2023-09-05 中国核电工程有限公司 模拟核燃料后处理放射性真实料液腐蚀性的方法及模拟料液
CN113881830B (zh) * 2021-09-29 2022-11-18 太原理工大学 一种提升超级奥氏体不锈钢耐晶间腐蚀性能的方法
CN114351043A (zh) * 2021-11-29 2022-04-15 中国科学院金属研究所 一种用于第四代钠冷快堆的316kd奥氏体不锈钢及其制备与应用
CN114657465B (zh) * 2022-03-04 2023-10-13 中国科学院金属研究所 一种提高铅基堆用高性能紧固件抗应力松弛性能的合金化方法
CN114657475B (zh) * 2022-03-04 2023-10-10 中国科学院金属研究所 高温紧固件用耐液态铅铋腐蚀奥氏体不锈钢及其制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH481223A (de) * 1965-05-14 1969-11-15 Westinghouse Electric Corp Austenitischer rostfreier Stahl
US3486885A (en) * 1967-04-03 1969-12-30 Atomic Energy Commission Stainless steel alloy with low phosphorus content
EP0691412A1 (de) * 1994-01-26 1996-01-10 Kawasaki Steel Corporation Verfahren zur herstellung eines stahlbleches mit hoher korrosionsbeständigkeit

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS52117224A (en) * 1976-03-30 1977-10-01 Nippon Steel Corp Austenite stainless steel with excellent stress corrosion cracking res istance in water of high temperature and pressure
JPS59222563A (ja) 1983-06-01 1984-12-14 Sumitomo Metal Ind Ltd 耐食性に優れたオ−ステナイトステンレス鋼
JPS59222559A (ja) * 1983-06-01 1984-12-14 Sumitomo Metal Ind Ltd 耐硝酸性オーステナイトステンレス鋼
JPS60100629A (ja) 1983-11-08 1985-06-04 Sumitomo Metal Ind Ltd オ−ステナイトステンレス鋼の製造方法
JP2639798B2 (ja) * 1986-03-12 1997-08-13 住友金属工業株式会社 オーステナイト系ステンレス鋼の製造方法
JPS6369947A (ja) 1986-09-11 1988-03-30 Kawasaki Steel Corp クリ−プ破断延性の優れたオ−ステナイト系ステンレス鋼
US4836976A (en) 1987-04-20 1989-06-06 General Electric Company Light water reactor cores with increased resistance to stress corrosion cracking
JPH07238315A (ja) 1987-07-27 1995-09-12 Nkk Corp 耐硝酸腐食性の優れたオーステナイト系ステンレス鋼材の製造方法
JP2574917B2 (ja) 1990-03-14 1997-01-22 株式会社日立製作所 耐応力腐食割れ性に優れたオーステナイト鋼及びその用途
JPH0559494A (ja) 1991-09-03 1993-03-09 Hitachi Ltd 耐照射誘起偏析に優れたオーステナイトステンレス鋼
JPH05179405A (ja) 1992-01-06 1993-07-20 Kawasaki Steel Corp 耐応力腐食割れと耐食性に優れ、なおかつ熱間加工性に優れたオーステナイト系ステンレス鋼
JPH06306548A (ja) 1993-04-26 1994-11-01 Nippon Steel Corp 熱間加工性に優れた耐硝酸オーステナイト系ステンレス鋼
JP3141646B2 (ja) 1993-09-22 2001-03-05 住友金属工業株式会社 硝酸含有環境用オーステナイト系ステンレス鋼
JPH07113146A (ja) 1993-10-15 1995-05-02 Nkk Corp 高耐食性オーステナイト系ステンレス鋼およびその製造方法
JPH0813095A (ja) 1994-06-30 1996-01-16 Nkk Corp 耐硝酸腐食性に優れたオーステナイトステンレス鋼
AU4165496A (en) * 1994-11-03 1996-05-31 Electric Power Research Institute, Inc. Cobalt-free hardfacing alloys with improved welding characteristics
JPH08269550A (ja) 1995-03-31 1996-10-15 Nippon Steel Corp 耐粒界応力腐食割れ性に優れたオーステナイト系ステンレス鋼の製造方法
JPH09125205A (ja) 1995-09-01 1997-05-13 Mitsubishi Heavy Ind Ltd 耐中性子照射劣化高Ｎｉオーステナイト系ステンレス鋼
JPH1180905A (ja) 1997-09-10 1999-03-26 Hitachi Ltd 耐食性に優れたオーステナイト系ステンレス鋼及びその用途

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH481223A (de) * 1965-05-14 1969-11-15 Westinghouse Electric Corp Austenitischer rostfreier Stahl
US3486885A (en) * 1967-04-03 1969-12-30 Atomic Energy Commission Stainless steel alloy with low phosphorus content
EP0691412A1 (de) * 1994-01-26 1996-01-10 Kawasaki Steel Corporation Verfahren zur herstellung eines stahlbleches mit hoher korrosionsbeständigkeit

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
KAIN V ET AL: "Case reviews on the effect of microstructure on the corrosion behavior of austenitic alloys for processing and storage of nuclear waste", METALLURGICAL AND MATERIALS TRANSACTIONS A, SPRINGER-VERLAG, NEW YORK, vol. 36, no. 5, 1 May 2005 (2005-05-01), pages 1075-1084, XP019695133, ISSN: 1543-1940 *
RAJ B ET AL: "Materials development and corrosion problems in nuclear fuel reprocessing plants", PROGRESS IN NUCLEAR ENERGY, PERGAMON PRESS, OXFORD, GB, vol. 48, no. 4, 1 May 2006 (2006-05-01), pages 283-313, XP025059721, ISSN: 0149-1970, DOI: 10.1016/J.PNUCENE.2005.07.001 [retrieved on 2006-05-01] *
See also references of WO2008136354A1 *

Also Published As

Publication number Publication date
RU2420598C1 (ru) 2011-06-10
JP2009197316A (ja) 2009-09-03
EP2143815B1 (de) 2014-01-08
KR20090130331A (ko) 2009-12-22
US20100116382A1 (en) 2010-05-13
CN101668873A (zh) 2010-03-10
EP2143815A4 (de) 2011-12-21
WO2008136354A1 (ja) 2008-11-13
CN101668873B (zh) 2012-11-28
JP5756935B2 (ja) 2015-07-29

Similar Documents

Publication Publication Date Title
EP2143815B1 (de) Austenitischer edelstahl mit hervorragender beständigkeit gegenüber korngrenzkorrosion und spannungsrisskorrosion sowie verfahren zur herstellung des austenitischen edelstahls
RU2321670C2 (ru) Мелкозернистая, мартенситная нержавеющая сталь и способ ее производства
KR100831578B1 (ko) 원자력용 우수한 내식성을 갖는 지르코늄 합금 조성물 및이의 제조방법
EP2725113B1 (de) Verfahren zur herstellung eines rostfreien austenitischen stahls und rostfreies austenitisches stahlmaterial
CN109136653B (zh) 用于核电设备的镍基合金及其热轧板的制造方法
EP4257717A1 (de) Hochentropischer austenitischer edelstahl und herstellungsverfahren dafür
CN109112423A (zh) 一种优良低温韧性特厚合金钢板及其制备方法
JP7151945B1 (ja) マルテンサイト系ステンレス鋼材
CN114717488A (zh) 一种1800MPa级高塑韧性高耐蚀马氏体时效不锈钢及其制备方法
CN114921732A (zh) 一种多相强化超高强马氏体时效不锈钢及其制备方法
CN114717487A (zh) 一种2700MPa级高塑韧性高耐蚀马氏体时效不锈钢及其制备方法
KR100580112B1 (ko) 고 크롬 페라이트/마르텐사이트 내열합금의 제조방법
KR101630403B1 (ko) 다단 열간압연을 적용한 핵연료용 지르코늄 부품의 제조방법
KR101833404B1 (ko) 고강도 Fe―Cr―Ni―Al 멀티플렉스 스테인리스강 및 이의 제조방법
EP3633060B1 (de) Stahlplatte und verfahren zur herstellung derselben
US6696016B1 (en) High-chromium containing ferrite based heat resistant steel
CN117460856A (zh) 奥氏体系不锈钢和钢管
JP3620099B2 (ja) 強度と靱性に優れるＣｒ−Ｍｏ鋼の製造方法
RU2703318C1 (ru) Радиационно-стойкая аустенитная сталь для внутрикорпусной выгородки ввэр
EP0241553B1 (de) Hochfester rostfreistahl und dessen herstellung
JPH07238315A (ja) 耐硝酸腐食性の優れたオーステナイト系ステンレス鋼材の製造方法
CN116219268A (zh) 一种含硼超级双相不锈钢及无缝管制备方法
CN118048581A (zh) 一种高氮奥氏体不锈钢及其制备方法
CN118064799A (zh) 一种变速抽水蓄能发电机组用护环锻件及其制备方法
CN117646148A (zh) 低活化钢及其制备方法和应用

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: 20091030

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

RIN1 Information on inventor provided before grant (corrected)

Inventor name: TANABE, MAKOTO

Inventor name: TSUKATANI, ICHIRO

Inventor name: KATO, CHIAKI

Inventor name: IOKA, IKUO

Inventor name: MARUYAMA, NOBUTOSHI

Inventor name: KIUCHI, KIYOSHI

Inventor name: NAKAYAMA, JUMPEI

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20111118

RIC1 Information provided on ipc code assigned before grant

Ipc: B21B 3/02 20060101ALI20111114BHEP

Ipc: C22C 38/50 20060101ALI20111114BHEP

Ipc: C22C 38/54 20060101ALI20111114BHEP

Ipc: C21D 8/02 20060101ALI20111114BHEP

Ipc: C22C 38/00 20060101AFI20111114BHEP

17Q First examination report despatched

Effective date: 20120615

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20130910

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

RIN1 Information on inventor provided before grant (corrected)

Inventor name: KIUCHI, KIYOSHI

Inventor name: KATO, CHIAKI

Inventor name: TSUKATANI, ICHIRO

Inventor name: MARUYAMA, NOBUTOSHI

Inventor name: TANABE, MAKOTO

Inventor name: NAKAYAMA, JUMPEI

Inventor name: IOKA, IKUO

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK 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: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 648822

Country of ref document: AT

Kind code of ref document: T

Effective date: 20140215

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602008029782

Country of ref document: DE

Effective date: 20140220

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 648822

Country of ref document: AT

Kind code of ref document: T

Effective date: 20140108

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20140108

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: 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: 20140508

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: 20140408

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: 20140108

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

Effective date: 20140108

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: 20140108

Ref country code: NL

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

Effective date: 20140108

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: 20140508

Ref country code: ES

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

Effective date: 20140108

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: 20140108

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: 20140108

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

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: 20140108

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: 20140108

Ref country code: BE

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: 20140108

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602008029782

Country of ref document: DE

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

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: 20140108

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: 20140108

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: 20140108

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: 20140108

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602008029782

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

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

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: 20140108

Ref country code: LU

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: 20140424

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: 20140108

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: 20140108

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

26N No opposition filed

Effective date: 20141009

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602008029782

Country of ref document: DE

Effective date: 20141009

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602008029782

Country of ref document: DE

Effective date: 20141101

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

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

Ref country code: LI

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

Effective date: 20140430

Ref country code: CH

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

Effective date: 20140430

Ref country code: DE

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

Effective date: 20141101

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: 20140424

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

Ref country code: SI

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

Effective date: 20140108

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

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

Ref country code: MT

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

Effective date: 20140108

REG Reference to a national code

Ref country code: GB

Ref legal event code: 732E

Free format text: REGISTERED BETWEEN 20160317 AND 20160323

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

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: 20140108

REG Reference to a national code

Ref country code: FR

Ref legal event code: CA

Effective date: 20160504

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: 20140409

Ref country code: IT

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

Effective date: 20140108

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: 20140108

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: 20080424

REG Reference to a national code

Ref country code: FR

Ref legal event code: TQ

Owner name: KABUSHIKI KAISHA KOBE SEIKO SHO, JP

Effective date: 20160926

Ref country code: FR

Ref legal event code: TQ

Owner name: KOBELCO RESEARCH INSTITUTE, INC., JP

Effective date: 20160926

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 10

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

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

Effective date: 20230513

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

Ref country code: GB

Payment date: 20240229

Year of fee payment: 17

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

Ref country code: FR

Payment date: 20240308

Year of fee payment: 17