EP2143815B1 - Austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance, and method for producing austenitic stainless steel - Google Patents

Austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance, and method for producing austenitic stainless steel Download PDF

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EP2143815B1
EP2143815B1 EP08752039.1A EP08752039A EP2143815B1 EP 2143815 B1 EP2143815 B1 EP 2143815B1 EP 08752039 A EP08752039 A EP 08752039A EP 2143815 B1 EP2143815 B1 EP 2143815B1
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stainless steel
less
austenitic stainless
steel material
temperature
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German (de)
English (en)
French (fr)
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EP2143815A1 (en
EP2143815A4 (en
Inventor
Kiyoshi Kiuchi
Ikuo Ioka
Chiaki Kato
Nobutoshi Maruyama
Ichiro Tsukatani
Makoto Tanabe
Jumpei Nakayama
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Kobe Steel Ltd
Kobelco Research Institute Inc
Japan Atomic Energy Agency
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Kobe Steel Ltd
Kobelco Research Institute Inc
Japan Atomic Energy Agency
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    • 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
    • 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.
  • Methods of improving the corrosion resistance of austenitic stainless steels include, for example, those described in Patent Documents 1 to 7.
  • Kain, V., et al., 'Case Review on the Effect of Microstructure on the Corrosion Behaviour of Austenitic Alloys For Processing and Storage of Nuclear Waste', Met. and Mat. Trans. A, Vol. 36A, May 2005 discloses a 310L NAG steel subject to oxidising nitric acid environments used to treat nuclear waste.
  • 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 2 discloses an austenitic stainless steel containing C at 0.015 wt% or less, Si at 0.5 wt% or less, Mn at 2 wt% or less, P at 0.015 wt% or less, Ni at 10 to 22 wt%, Cr at 15 to 30 wt%, Al at 0.01 wt% or less, Ca at 0.002 to 0.010 wt% or less and the balance of essentially Fe.
  • Favorable process-flow corrosion resistance is obtained while the contents of Si, P and Al in the austenitic stainless steel are restricted and Ca is added in suitable amount.
  • the austenitic stainless steel also shows favorable hot-processing efficiency and favorable corrosion resistance in high-temperature nitric acid.
  • 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.
  • the austenitic stainless steel which satisfies the formula: [Ni]+60[N]-4[Mo] ⁇ 7 and contains one or both of Ca and Ce in an individual or total amount of 2 ⁇ [S] to 0.03 (wt%), shows favorable corrosion resistance to tunnel-like corrosion.
  • the symbol [X] represents the content of element X in steel (wt%).
  • 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 6 discloses an austenitic stainless steel containing C at 0.02 wt% or less, Si at 0.8 wt% or less, Mn at 2.0 wt% or less, P at 0.04 wt% or less, S at 0.03 wt% or less, Ni at 6 to 22 wt%, Cr at 13 to 27 wt%, Al at 0.1 wt% or less, Cu at 0.3 wt% or less, N at 0.1 wt% or less and the balance of essentially Fe.
  • the austenitic stainless steel which satisfies the following formula: 1.5[Ni]+[Mn]+65([C]+[N])-5[Si]-2.5 ⁇ 52-2.3 ([Ni]+[Mn])-200 ([C]+[N]) and contains B in an amount of 5 wt ppm or less, shows favorable resistance to nitric acid corrosion after cold processing or deformation, when it has a total content of one or more elements selected from Ti, Nb, V, Hf and Ta at 1.0 wt% or less.
  • 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.
  • the high-Ni-content austenitic steel shows favorable stress corrosion cracking resistance in high-temperature high-pressure water or high-temperature high-pressure oxygen-saturated water at 270 to 350°C and at 70 to 160 atmospheric pressures even after neutron irradiation at a fluence of at least 1 ⁇ 10 22 n/cm 2 .
  • the average expansion coefficient of the high-Ni-content austenitic steel in the temperature range of room temperature to 400°C is in the range of 15 to 19 ⁇ 10 -6 /K.
  • 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.
  • Patent Document 13 discloses a method of preparing single crystal by removing random grain boundaries in austenitic stainless steel by unidirectional solidification method.
  • Patent Document 14 discloses an austenitic stainless steel containing C at 0.02 wt% or less, N at 0.6 wt% or less, Si at 1.0 wt% or less, P at 0.040 wt% or less, S at 0.030 wt% or less, Mn at 2.0 wt% or less, Mo at 3.0 wt% or less, Ni at 12 to 26 wt% and Cr at 16 to 26 wt%, in which austenite or ferrite phases are contained in the austenitic matrix in an amount of 10 vol.% or less at room temperature, the matrix contains sub-crystalline grains, and single-crystalline grain boundaries smaller in deviation from the coincidence orientation relationship and higher in crystal orientation are formed.
  • the austenitic stainless steel shows favorable corrosion resistance and stress corrosion cracking resistance and has superior mechanical properties.
  • 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.
  • B content it is only described that the B content is desirably lower, similarly to other normal impurity elements, and because the B contents in the austenitic stainless steels were at the same level between Examples and Comparative Examples, and there is no description that the B content should be adjusted.
  • 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 Documents 8 to 10 do not reduce the content of impurities, a cause of intergranular corrosion together with Cr-depletion layer, for prevention of the intergranular stress corrosion cracking by component adjustment. It is thus impossible in principle to solve the problem of stress corrosion cracking generated under the irradiation environment.
  • 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.
  • an method of producing an austenitic stainless steel material excellent in intergranular corrosion resistance and stress corrosion cracking resistance comprises: a step of hot working an ingot having a chemical composition of the stainless steel; and a step of solution treating a stainless steel material obtained by the hot working; wherein the solution treatment step comprises: a substep of heating the stainless steel material at a heat treatment temperature in a first temperature range of 1000 to 1150°C for 1 minute or more; and then, a substep of cooling the stainless steel material from the heat treatment temperature in the first temperature range to ordinary temperature by rapid or natural cooling.
  • an method of producing an austenitic stainless steel material excellent in intergranular corrosion resistance and stress corrosion cracking resistance comprises: a step of hot working an ingot having a chemical composition of the stainless steel; and a step of solution treating a stainless steel material obtained by the hot working; wherein the solution treatment step comprises: a substep of heating the stainless steel material at a heat treatment temperature in a first temperature range of 1000 to 1150°C for 1 minute or more; a substep of cooling the stainless steel material from the heat treatment temperature in the first temperature range by rapid or natural cooling; a substep of heating the stainless steel material at a heat treatment temperature in a second temperature range of 650°C or higher for 10 minutes or more after the cooling, and then, a substep of cooling the stainless steel material from the heat treatment temperature in the second temperature range to ordinary temperature by rapid or natural cooling.
  • the inventors After intensive studies to solve the problems above, the inventors have found that it is possible to improve the corrosion resistance to intergranular corrosion and stress corrosion cracking, 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 exposed to neutron irradiation, for example, in a light-water reactor core, by reducing the amount of impurities, in particular of B, present in grain boundaries of the austenitic stainless steel, which becomes the initial point of corrosion, as much as possible, and completed the present invention.
  • 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.
  • impurity elements such as C, P, S, N, O segregating in grain boundaries. It was also found that, when the B content is 3 wt ppm or less, it was possible to prevent the intergranular corrosion and the stress corrosion cracking by adjusting the total content of the impurity elements such as C, P, S, N and O to 0.02 wt% or less. The reason for the drastic increase in grain boundary damage when the total content of the impurity elements is 0.02 wt% or less is yet to be understood.
  • the impurity elements segregating in grain boundaries such as C, P, S, N and O are desirable lower in amount, but it is difficult and also uneconomical to eliminate these impurities completely by current refining technology. It is effective to add a stabilizing element (element immobilizing impurity elements) for elimination of such impurity elements as much as possible, but Ti is most desirable for elimination of these impurity elements. Addition of Ti allows conversion of impurities such as C, P, S, N and O that could not be removed, for example by the electrobeam-melting method described below, to Ti based compounds such as TiC, FeTiP, TiS, TiN and TiO 2 and control of segregation of the impurities in grain boundaries as solid-solution elements.
  • Nb is used as the stabilizing element in traditional technology, but it is difficult to form the compounds other than NbC by addition of Nb when the austenitic stainless steel contains impurities in the range of the present invention, and thus, the advantageous effects obtained by addition of Nb is limited.
  • the amount of Ti added should be stoichiometrically equivalent to or more than the total amount of C, P, S, N and O.
  • the material is heated in the temperature range of 1000 to 1150°C for 1 minute or more; and then, cooled rapidly or cooled by natural air from the heat treatment temperature to ordinary temperature, to make the Ti-addition effect more definite and also to make the relationship between the distribution state of the Ti based compounds generated and the position of grain boundaries present different. It is also effective to cold work the material, after solution treatment, to a working ratio of 40% or more and less than 75%; and then, to heat and hold the cold worked material at a temperature in the temperature range of 750°C or higher for 10 minutes or more for recrystallization.
  • 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.
  • intergranular corrosion i.e., selectively corrosion in the region, occurs.
  • it leads to deterioration in nitric acid corrosion resistance and stress corrosion cracking resistance of the austenitic stainless steel.
  • the impurities are removed by addition of Ti and thermomechanical treatment in the present embodiment, because, if the C content in the austenitic stainless steel is larger, it may possibly leads to microscopic precipitation of Cr based carbides, the content of C is preferably 0.005 wt% or less, more preferably 0.003 wt% or less.
  • the Si content is 0.5 wt% or less. However, for prevention of intergranular corrosion, the content is desirably smaller, and it is more preferably 0.3 wt% or less.
  • Manganese is effective in improving the stability of the austenite phase and in preventing generation of ⁇ -ferrite and processing-induced phase transformation which are hazardous to corrosion resistance, but does not exhibit desired effects even at a content of more than 0.5 wt% and rather accelerates corrosion, as Mn in the solid-solution state, and thus, the Mn content is 0.5 wt% or less. It is more preferably 0.3 wt% or less.
  • the P content is desirably lower and preferably 0.005 wt% or less, more preferably 0.003 wt% or less.
  • the S content is desirably lower, and preferably 0.005 wt% or less, more preferably 0.003 wt% or less.
  • Nickel is an element needed for stabilization of austenite structure and also for control of intergranular corrosion and stress corrosion cracking.
  • the Ni content of less than 15 wt% cannot assure generation of the austenite structure sufficiently and acquisition of swelling resistance under neutron irradiation environment.
  • the Ni content of more than 40 wt% leads to increase in price and the Ni content is thus desirably 15.0 to 40.0 wt%. It is more preferably 18.0 wt% or more, from the point of stability of the austenite structure. It is more preferably 38.0 wt% or less for control of swelling.
  • Chromium is an element needed for formation of a passive film and thus for assuring corrosion resistance of the stainless steel.
  • the Cr content is preferably about 16%, as in typical stainless steels specified in JIS standard such as SUS304 and SUS316.
  • the Cr content should be at least 20 wt% for assuring sufficient corrosion resistance under an overpassivation corrosion environment under a corrosion environment for a boiling heat transfer surface in a high-concentration nitric acid solution containing highly oxidizing metal ions such as in reprocessing plants, and under an environment in high-temperature high-pressure water exposed to neutron irradiation such as in light water reactor cores.
  • the Cr content of more than 30 wt% leads to precipitation of Cr-rich brittle phases, and, for generation of complete austenite structure while avoiding the precipitation, the Ni content should be raised, inevitably leading to increase in cost, and thus, the Cr content is desirably 20.0 to 30.0 wt%. It is more preferably 22.0 wt% or more from the viewpoint of corrosion resistance. It is further more preferably 28.0 wt% or less.
  • 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.
  • Nitrogen and Oxygen are both elements that leads to deterioration in intergranular corrosion resistance and stress corrosion cracking resistance, and thus, the content thereof is preferably lower, and the content of each element is 0.01 wt% at most.
  • the N content is more preferably 0.005 wt% or less.
  • the O content is more preferably 0.005 wt% or less.
  • the contents of impurity elements of C, P, S, O and N are adjusted respectively under the regulation conditions above, it is not possible to have favorable intergranular corrosion resistance and stress corrosion cracking resistance if the total content of these elements exceeds 0.02 wt%, and thus, the upper limit of the total content is 0.02 wt%.
  • the upper limit is more preferably 0.015 wt%.
  • the method of forming the ingot of a high-purity austenitic stainless steel having a total impurity element content of 0.02 wt% or less is not particularly limited, but one of effective means is to use an electrobeam-melting method in the combination of ingot-forming step. It is possible by employing the electrobeam-melting method in the production process of austenitic stainless steel ingot, to obtain ultrahigh-cleanness steel ingot reduced in the contents of the impurity elements segregating in austenite grain boundaries, such as C, P, S, N and O, and also of highly volatile alkali group metals.
  • the method of forming the raw electrode for electrobeam melting is not particularly limited, and a most suitable electrode forming method is selected according to the purity of the raw materials for primary melting.
  • 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.
  • the Ti content is preferably an amount stoichiometrically equivalent to or more than the amount needed for conversion of all impurity elements of C, P, S, N and O to Ti based carbides, nitrides and other compounds such as TiC, TiN, FeTiP, ,TiS and TiO 2 .
  • Ti (wt%) ⁇ (48/12)C (wt%) + (48/31)P (wt%)+ (48/32)S (wt%) + (48/14)N (wt%) + (48/16) ⁇ (1/2)O (wt%).
  • it is preferably 0.05 wt% or more, considering the dynamic precipitation reaction of dilute elements.
  • addition of Ti in great amount leads to cost increase and thus, the Ti content is preferably 0.3 wt% or less.
  • 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 vacuum in the chamber should be kept at 1 ⁇ 10 -2 Pa or more.
  • the degree of vacuum is desirably 1 ⁇ 10 -4 Pa or less.
  • the raw material for the raw material electrode may be prepared, for example, by the AOD method (argon oxygen decarburization method) or the VOD method (vacuum oxygen decarburization method), both of which are widely known as the methods of forming a stainless steel ingot, or a special melting method such as vacuum induction melting method or cold crucible induction melting method.
  • AOD method argon oxygen decarburization method
  • VOD method vacuum oxygen decarburization method
  • a plate or pipe material of austenitic stainless steel is heat-treated in the production process (for example, in the hot working step) at a heat-treatment temperature in the range of 1000 to 1150°C for 1 minute or more. It is then cooled from the heat-treatment temperature in the range of 1000 to 1150°C to ordinary temperature by rapid or natural cooling in solution treatment.
  • the plate or pipe material may be cooled to or reheated after cooling to a heat-treatment temperature in the range of 650°C or higher; and then, heated additionally for 10 minutes or more at a heat-treatment temperature in the range of 650°C or higher. It is possible in this way to make the austenite phase more homogeneous and to raise the efficiency in improving the intergranular corrosion resistance and the stress corrosion cracking resistance by restriction of the chemical composition of the austenitic stainless steel.
  • the material may be subjected to cold working (cold rolling) and recrystallization treatment, after the solution treatment.
  • the cold working if carried out, can introduce dislocations, i.e., sites for carbide precipitation, in great amount.
  • the recrystallization treatment by heat treatment after the cold working allows uniformly disperses precipitation and co-recrystallization of the deposits.
  • the working ratio in the cold working is 40% or more. Excessive increase in working ratio only leads to saturation of the density of the dislocation sites introduced and distortion-induced phase transformation from the austenite phase to the martensite phase. The phase transformation makes industrial processing more difficult and prohibits generation of homogeneous austenite structure in the following recrystallization treatment, consequently leading to deterioration in intergranular corrosion resistance and stress corrosion cracking resistance.
  • the working ratio of the cold working is less than 75%.
  • the temperature for recrystallization of the processing structure depends on the working ratio of the steel, specifically on the density of introduced dislocation sites and the dispersion state of the carbides inhibiting movement of dislocations in the recovery-recrystallization process. For that reason, the temperature should be kept at 700°C or higher for 10 minutes or more for the steel having the chemical compositions and structures according to the present invention.
  • excessively high temperature leads to deterioration in strength, by growth of the recrystallized austenite grains obtained. Further, the deposits aggregate and form coarse particles, which are distributed in the recrystallized austenite grain boundaries. It thus leads to deterioration in intergranular corrosion resistance and stress corrosion cracking resistance. Accordingly, the recrystallization temperature is desirably 900°C or lower.
  • 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.
  • an austenitic stainless steel in the chemical compositions shown in Table 1 was melted by vacuum induction melting (VIM) and cast into a mold, to give an ingot.
  • the units for elements in the chemical compositions shown in Table 1 are respectively weight percentage (wt%), except the unit for B of wt ppm.
  • an electrode was prepared by grinding the vacuum-melted ingot and subjecting the ingot to electron-beam (EB) re-melting, to give a cylindrical ingot. It is then processed by forging and hot rolling into a plate material having a thickness of 6 mm, which is then solution-treated under a condition of 1050°C for 1/2 hour, to give a plate material having a thickness of 6 mm.
  • Coriou corrosion test a test simulating intergranular corrosion in nitric acid solution containing higher-concentration metal ions
  • SSRT slow strain rate test
  • CBB test tests simulating stress corrosion cracking in high-temperature high-pressure water.
  • the samples were sensitized at 620°C for 100 hours before the tests.
  • the sample was immersed in 500 ml of 8N boiling nitric acid solution containing 1.0 g/L of Cr 6+ ion for 24 hours repeatedly for four times, while the solution was exchanged, and the weight loss was determined and the corrosion rate and others calculated.
  • the slow strain rate test was carried out by using a test piece having a gauge section diameter of 3 mm and a distance between marked points of 20 mm under the condition of a deformation speed of 0.5 ⁇ m/min in high-temperature high-pressure water (saturated oxygen concentration: 8 wt ppm, 70 kgf/cm 2 , 290°C).
  • the CBB test was carried out by using a test piece having a thickness of 2 mm, a width of 10 mm and a length of 50 mm and also using the jig shown in Figure 2 in an autoclave and the jig, while the sample was immersed in high-temperature high-pressure water (saturated oxygen concentration: 8 wt ppm, 70 kgf/cm 2 , 290°C) for 500 hours.
  • the test piece 1 was held between holders 3, together with graphite fiber wool 2 for spacing; bolts were inserted into bolt holes 4; and the test piece was tightened between the curved-surface holders 3.
  • each holder has a region having a curvature of 100R. After immersion, the test piece was separated, and cracking of the test piece was evaluated by observation of the cross section.
  • the intergranular corrosion resistance in the higher-concentration metal ion-containing boiling nitric acid was evaluated in the Coriou corrosion test according to the following criteria:
  • the stress corrosion cracking resistance in the high-temperature high-pressure water was evaluated in the SSRT corrosion test and the CBB test, according to the following criteria:
  • Test results after evaluation are summarized in Table 2.
  • the samples of steel numbers A to D and steel numbers K to L each containing the following elements at the indicated contents: C, at 0.005 wt% or less; Si, at 0.5 wt% or less; Mn, at 0.5 wt% or less; P, at 0.005 wt% or less; S, at 0.005 wt% or less; Ni, at 15.0 to 40.0 wt%; Cr, at 20.0 to 30.0 wt%; N, at 0.01 wt% or less; O, at 0.01 wt% or less; and B, at 3 wt ppm or less, and thus represent the inventive examples.
  • the samples of steel numbers E to G and M represent samples of Comparative Examples and contain B in an amount of more than 3 wt ppm.
  • the samples of steel numbers H and I represent samples of Comparative Examples and contain Cr in an amount of less than 20.0 wt% and Ni in an amount of less than 15.0 wt%.
  • the sample of steel number J represents a sample of Comparative Example and contains Cr in an amount of more than 30.0 wt%.
  • the samples of steel numbers N to Q represent samples of Comparative Example and contain C, at more than 0.005 wt%; P, at more than 0.005 wt%; S, at more than 0.005 wt%; N, at more than 0.01 wt%: or O, at more than 0.01 wt%.
  • 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.
  • Figure 1B the relationship between the intergranular corrosion depth in Coriou corrosion test and the B content of the sample of steel numbers A to G, L and M corresponding to 25Cr-20Ni steel is shown in Figure 1B.
  • Figures 1A and 1B show that a B content of more than 3 wt ppm leads to drastic increase in corrosion rate and intergranular corrosion depth. It also shows that, when the B contents are the same, the corrosion rate and the intergranular corrosion depth are reduced further by addition of Ti.
  • Table 2 CORIOU TEST SSRT TEST CBB TEST STEEL NO.
  • Plate materials having a thickness of 6 mm were prepared by using the samples of steel numbers B, K and L shown in Table 1 under the various conditions shown in Table 3.
  • the sample of production lot number 1 was an ingot obtained by vacuum induction melting (VIM) and casting into a mold under vacuum, while the samples of other production lot numbers (2 to 8) were subjected additionally to electron-beam re-melting (EB).
  • Each plate material finished by forging and hot rolling was subjected to solution treatment and additionally to thermomechanical treatment (cold work-recrystallization or cold work-carbide precipitation-recrystallization) (the thickness of the plate having a different cold-working ratio was adjusted during solution treatment).
  • the samples were analyzed in the Coriou corrosion test simulating intergranular corrosion in higher-concentration boiling nitric acid solution containing highly oxidizing metal ion, and the slow strain rate test (SSRT) and the CBB test simulating stress corrosion cracking in high-temperature high-pressure water.
  • the samples were sensitized at 620°C ⁇ 100 hours, in the slow strain rate test and the CBB test simulating neutron irradiation-induced precipitation.
  • Table 4 shows that, when the samples of steel number B, K or L are processed by the treatments of production lot number 3, 5 or 7, i.e., solution-treated at 1050°C for 30 minutes and then reheated at 700°C for 1 hour (production lot number 3), or additionally cold-worked at a cold rolling ratio of 60% in the thermomechanical treatment step (production lot number 5), or precipitation-treated 600°C for 10 hours in the thermomechanical treatment step after cold working and before recrystallization treatment (production lot number 7), intergranular corrosion was not observed in the CBB test, indicating the more favorable intergranular corrosion resistance can be obtained for the samples above than for those obtained by the treatments of other production lot numbers (1, 2, 4, 6 and 8).
  • an aspect of the present invention is an austenitic stainless steel excellent in intergranular corrosion resistance and stress corrosion cracking resistance, comprising: 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.
  • Ni content 15.0 wt% or more. It is also possible to reduce the cost by adjusting the Ni content to 40.0 wt% or less. It is also possible by adjusting the Cr content to 20.0 wt% or more to assure sufficient corrosion resistance, for example, under an overpassivation corrosion environment under a corrosion environment for a boiling heat transfer surface in a high-concentration nitric acid solution containing highly oxidizing metal ions such as in reprocessing plants and under an environment in high-temperature high-pressure water exposed to neutron irradiation such as in light water reactor cores.
  • the total content of C, P, S, N and O in the austenitic stainless steel is preferably 0.02 wt% or less for obtaining favorable intergranular corrosion resistance and stress corrosion cracking resistance.
  • the austenitic stainless steel preferably further comprises Ti, wherein the content of Ti is in an amount stoichiometrically equivalent to or more than the total amount of C, P, S, N and O, because the intergranular corrosion-causing impurity elements such as C, N, P, S and O can be removed completely by conversion to Ti based carbides, nitrides or other compounds such as TiC, TiN, FeTiP, TiS and TiO 2 .
  • Another aspect of the present invention is a method of producing an austenitic stainless steel material excellent in intergranular corrosion resistance and stress corrosion cracking resistance.
  • the method comprises: a step of hot working an ingot having a chemical composition of the abovementioned stainless steel; and a step of solution treating a stainless steel material obtained by the hot working; wherein the solution treatment step comprises: a substep of heating the stainless steel material at a heat treatment temperature in a first temperature range of 1000 to 1150°C for 1 minute or more; and then, a substep of cooling the stainless steel material from the heat treatment temperature in the first temperature range to ordinary temperature by rapid or natural cooling.
  • Yet another aspect of the present invention is a method of producing an austenitic stainless steel material excellent in intergranular corrosion resistance and stress corrosion cracking resistance.
  • the method comprises: a step of hot working an ingot having a chemical composition of the abovementioned stainless steel; and a step of solution treating a stainless steel material obtained by the hot working; wherein the solution treatment step comprises: a substep of heating the stainless steel material at a heat treatment temperature in a first temperature range of 1000 to 1150°C for 1 minute or more; a substep of cooling the stainless steel material from the heat treatment temperature in the first temperature range by rapid or natural cooling; a substep of heating the stainless steel material at a heat treatment temperature in a second temperature range of 650°C or higher for 10 minutes or more after the cooling, and then, a substep of cooling the stainless steel material from the heat treatment temperature in the second temperature range to ordinary temperature by rapid or natural cooling.
  • the method of producing an austenitic stainless steel material preferably, after the solution treatment step, further comprises: a step of cold working the stainless steel material at a working ratio of 40% or more and less than 75%; and then a step of recrystallization treatment by heating the stainless steel material at a heat treatment temperature in a temperature range of 700°C or higher for 10 minutes or more.
  • the method of producing an austenitic stainless steel preferably, between the cold working step and the recrystallization treatment step further comprises: a step of deposit precipitation in strain aging by heating the stainless steel material at a heat treatment temperature in a range of 500 to 650°C for 30 minutes or more.
  • the austenitic stainless steel according to the present invention it is possible by using the austenitic stainless steel according to the present invention to improve both intergranular corrosion resistance and stress corrosion cracking resistance reliably, both under a corrosion environment for a boiling heat transfer surface in a high-concentration nitric acid solution containing highly oxidizing metal ions and under the environment in high-temperature high-pressure water exposed to neutron irradiation.

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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
WO1995020683A1 (fr) * 1994-01-26 1995-08-03 Kawasaki Steel Corporation Procede de production de tole d'acier inoxydable a haute resistance a la corrosion
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
EP0789786B1 (en) * 1994-11-03 2001-06-13 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

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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

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

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