WO2021141107A1 - オーステナイト系ステンレス鋼材 - Google Patents

オーステナイト系ステンレス鋼材 Download PDF

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Publication number
WO2021141107A1
WO2021141107A1 PCT/JP2021/000448 JP2021000448W WO2021141107A1 WO 2021141107 A1 WO2021141107 A1 WO 2021141107A1 JP 2021000448 W JP2021000448 W JP 2021000448W WO 2021141107 A1 WO2021141107 A1 WO 2021141107A1
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Prior art keywords
steel material
content
stainless steel
austenite
still
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PCT/JP2021/000448
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English (en)
French (fr)
Japanese (ja)
Inventor
孝裕 小薄
伸之佑 栗原
佳奈 浄▲徳▼
悠平 鈴木
翔伍 青田
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Nippon Steel Corp
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Nippon Steel Corp
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Priority to KR1020227027311A priority Critical patent/KR102810752B1/ko
Priority to US17/757,126 priority patent/US12188111B2/en
Priority to CN202180008515.4A priority patent/CN114929917B/zh
Priority to EP21739014.5A priority patent/EP4089195A4/en
Priority to JP2021570104A priority patent/JP7307372B2/ja
Publication of WO2021141107A1 publication Critical patent/WO2021141107A1/ja
Anticipated expiration legal-status Critical
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
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    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • 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
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    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • This disclosure relates to steel materials, and more particularly to austenite-based stainless steel materials.
  • Chemical plant equipment includes multiple equipment.
  • Each device of the chemical plant equipment is, for example, a vacuum distillation device, a desulfurization device, a catalytic reformer, and the like. These devices include heating furnace tubes, reaction towers, tanks, heat exchangers, piping and the like.
  • the average operating temperature of each device is different.
  • the average temperature during operation is referred to as "average operating temperature”.
  • the operating temperature varies greatly depending on the raw materials and products processed in the chemical plant equipment.
  • High creep strength is required for equipment that operates at an average operating temperature of over 600 to 750 ° C.
  • Patent Document 1 discloses an improvement in creep strength of an austenite-based stainless steel material used in a high temperature region.
  • the austenite-based stainless steel disclosed in this document is C: 0.030% or less, Si: 0.10 to 1.00%, Mn: 0.20 to 2.00%, P: 0 in mass%. .040% or less, S: 0.010% or less, Cr: 16.0 to 25.0%, Ni: 10.0 to 30.0%, Mo: 0.1 to 5.0%, Nb: 0. 20 to 1.00%, N: 0.050 to 0.300%, sol.
  • a steel material used for a long period of time at an average operating temperature of more than 600 to 750 ° C. not only has high creep strength but also can suppress stress relaxation cracking, that is, has high stress relaxation relaxation cracking resistance.
  • Patent Document 1 The austenitic stainless steel proposed in Patent Document 1 exhibits excellent creep strength. However, Patent Document 1 does not study stress relaxation cracking resistance.
  • An object of the present disclosure is to have high creep strength even when used at an average operating temperature of more than 600 to 750 ° C. after high heat input welding, and an average operating temperature of more than 600 to 750 ° C. after high heat input welding. It is an object of the present invention to provide an austenite-based stainless steel material having excellent stress-relaxing cracking resistance even after being used for a long time.
  • Austenite stainless steel material The chemical composition is mass%, C: 0.030% or less, Si: 1.50% or less, Mn: 2.00% or less, P: 0.045% or less, S: 0.0300% or less, Cr: 15.00 to 25.00%, Ni: 8.00 to 20.00%, N: 0.050 to 0.250%, Nb: 0.10 to 1.00%, Mo: 0.05-5.00%, B: 0.0005 to 0.0100%, Ti: 0 to 0.50%, Ta: 0 to 0.50%, V: 0 to 1.00%, Zr: 0 to 0.10%, Hf: 0 to 0.10%, Cu: 0-4.00%, W: 0 to 5.00%, Co: 0 to 1.00%, sol.
  • the rest consists of Fe and impurities
  • the ratio of the solid solution N content (mass%) in the austenite stainless steel material to the N content (mass%) in the austenite stainless steel material is 0.40 to 0.90.
  • the austenite-based stainless steel material of the present disclosure has high creep strength even when used at an average operating temperature of more than 600 to 750 ° C. after high heat input welding, and has a temperature of more than 600 to 750 ° C. after high heat input welding. It has excellent stress-relaxing crack resistance even after long-term use at average operating temperature.
  • the present inventors have high creep strength even when used at an average operating temperature of more than 600 to 750 ° C. after high heat input welding, and have an average operating temperature of more than 600 to 750 ° C. after high heat input welding.
  • An austenite-based stainless steel material having excellent stress-relaxing cracking resistance even after being used for a long time was examined.
  • an environment having an average operating temperature of more than 600 to 750 ° C. is also referred to as a “high temperature environment”.
  • the present inventors first examined the stress relaxation cracking resistance. Stress relaxation cracking is considered to occur by the following mechanism. In a high temperature environment, Cr carbides are formed at the grain boundaries in the steel material. As a result, a Cr-deficient region (decarburized region) is formed along the grain boundaries. The Cr-deficient region is soft. Therefore, the strength difference between the inside of the crystal grains that have undergone secondary induction precipitation hardening and the Cr-deficient region along the grain boundaries becomes large. As a result, stress relaxation cracks occur.
  • the present inventors examined the chemical composition of the steel material.
  • the chemical composition is C: 0.030% or less, Si: 1.50% or less, Mn: 2.00% or less, P: 0.045% or less, S: 0.0300% or less in mass%.
  • Cr 15.00 to 25.00%
  • Ni 8.00 to 20.00%
  • N 0.050 to 0.250%
  • Nb 0.10 to 1.00%
  • Mo 0.05 ⁇ 5.00%
  • B 0.0005 to 0.0100%
  • Zr 0 to 0.
  • the formation of Cr-deficient regions can be suppressed.
  • C and Cr are contained, a Cr-deficient region is inevitably formed. Therefore, the present inventors have studied the suppression of stress relaxation cracking by means different from the conventional ones.
  • the present inventors have described a method for suppressing the generation of Cr-deficient regions as much as possible by suppressing the C content to 0.030% or less, and in addition, strengthening the Cr-deficient regions even if Cr-deficient regions are generated. Study was carried out.
  • the Cr-deficient region is a decarburized region, carbide precipitation strengthening cannot be used in the Cr-deficient region. Therefore, the present inventors have considered precipitating nitrides in the steel material when used in a high temperature environment. Since C is not used in the formation of the nitride, the Cr-deficient region (decarburization region) does not increase. If nitrides precipitate in the Cr-deficient region generated near the grain boundaries during use in a high-temperature environment, softening near the grain boundaries can be suppressed by precipitation strengthening.
  • the strength difference between the inside of the crystal grains that have undergone secondary induction precipitation hardening and the Cr-deficient region formed along the crystal grain boundaries can be reduced, and the stress relaxation resistance cracking property can be enhanced. Further, by strengthening the Cr-deficient region, the creep strength is also increased.
  • a solid solution N for forming a nitride that precipitates and strengthens the Cr-deficient region and the inside of the grain when used in a high temperature environment It is important to deposit the nitride in advance in the steel material before use after securing the amount. By forming the nitride in the steel material before use, the pinning effect of the nitride is generated and the crystal grains can be refined. If the crystal grains can be made finer, the grain boundary precipitation amount (coating rate) of Cr carbide will be reduced, and the grain boundary segregation amount of phosphorus (P) and sulfur (S) will be further reduced.
  • the decrease in hardness at the crystal grain boundary and the vicinity of the crystal grain boundary can be suppressed, and the strength difference between the inside of the crystal grain and the crystal grain boundary and the Cr-deficient region can be reduced. Therefore, the stress relaxation cracking property of the steel material is enhanced.
  • the present inventors generate nitrides in the steel material before use in the high temperature environment to refine the crystal grains by the pinning effect, and generate nitrides in the steel material in use in the high temperature environment. It was considered that the stress relaxation cracking resistance could be enhanced by strengthening the Cr-deficient region. As a result of considering both creep strength and stress relaxation cracking resistance, the ratio of the solid-dissolved N amount in the steel material to the N content in the steel material having the above-mentioned chemical composition is 0.40 to 0. The present inventors have found that if it is .90, it is possible to achieve both creep strength and stress relaxation cracking resistance.
  • the austenite-based stainless steel material of the present embodiment completed based on the above knowledge has the following constitution.
  • Austenite stainless steel material The chemical composition is mass%, C: 0.030% or less, Si: 1.50% or less, Mn: 2.00% or less, P: 0.045% or less, S: 0.0300% or less, Cr: 15.00 to 25.00%, Ni: 8.00 to 20.00%, N: 0.050 to 0.250%, Nb: 0.10 to 1.00%, Mo: 0.05-5.00%, B: 0.0005 to 0.0100%, Ti: 0 to 0.50%, Ta: 0 to 0.50%, V: 0 to 1.00%, Zr: 0 to 0.10%, Hf: 0 to 0.10%, Cu: 0-4.00%, W: 0 to 5.00%, Co: 0 to 1.00%, sol.
  • the austenite-based stainless steel material contains at least one element belonging to any of the first to fourth groups.
  • Austenite stainless steel material Group 1: Ti: 0.01-0.50%, Ta: 0.01-0.50%, V: 0.01-1.00%, Zr: 0.01 to 0.10%, and Hf: 0.01 to 0.10%, Group 2: Cu: 0.01-4.00%, W: 0.01 to 5.00% and Co: 0.01-1.00%, Group 3: sol. Al: 0.001 to 0.100%, Group 4: Ca: 0.0001-0.0200%, Mg: 0.0001 to 0.0200% and Rare earth element: 0.001 to 0.100%.
  • austenite-based stainless steel material of the present embodiment will be described in detail.
  • "%" for an element means mass%.
  • the chemical composition of the austenite-based stainless steel material of the present embodiment contains the following elements.
  • C 0.030% or less Carbon (C) is inevitably contained. That is, the C content is more than 0%. C produces M 23 C 6 type Cr carbides at the grain boundaries. In this case, a Cr-deficient region is generated at the grain boundary, and the stress relaxation resistance of the steel material is reduced. When the C content exceeds 0.030%, the stress relaxation resistance cracking property of the steel material is remarkably lowered even if the content of other elements is within the range of the present embodiment. Therefore, the C content is 0.030% or less.
  • the preferred upper limit of the C content is 0.026%, more preferably 0.024%, further preferably 0.022%, still more preferably 0.020%, still more preferably 0.018%. %.
  • the C content is preferably as low as possible. However, excessive reduction of C content increases manufacturing costs. Therefore, in terms of industrial production, the preferable lower limit of the C content is 0.001%, and more preferably 0.002%.
  • Si 1.50% or less Silicon (Si) is inevitably contained. That is, the Si content is more than 0%. Si deoxidizes steel in the steelmaking process. Si further enhances the oxidation resistance and steam oxidation resistance of the steel material when the steel material is used in a high temperature environment (average operating temperature of more than 600 to 750 ° C.). If even a small amount of Si is contained, the above effect can be obtained to some extent. However, if the Si content exceeds 1.50%, the weld crack sensitivity is significantly increased even if the other element content is within the range of the present embodiment. Further, long-term use in a high temperature environment produces a sigma phase ( ⁇ phase) in the steel material. The ⁇ phase reduces the toughness of the steel material.
  • ⁇ phase sigma phase
  • the Si content is 1.50% or less.
  • the lower limit of the Si content is preferably 0.01%, more preferably 0.05%, still more preferably 0.10%, still more preferably 0.15%, still more preferably 0.18. %.
  • the preferred upper limit of the Si content is 1.40%, more preferably 1.20%, still more preferably 1.00%, still more preferably 0.80%, still more preferably 0.70. %, More preferably 0.60%, still more preferably 0.50%.
  • Mn 2.00% or less Manganese (Mn) is inevitably contained. That is, the Mn content is more than 0%. Mn combines with S in the steel material to form MnS, which enhances the hot workability of the steel material. Mn further deoxidizes the welded portion of the steel material during welding. If even a small amount of Mn is contained, the above effect can be obtained to some extent. However, if the Mn content exceeds 2.00%, even if the content of other elements is within the range of this embodiment, a sigma phase ( ⁇ phase) is likely to be generated when used in a high temperature environment. .. The ⁇ phase reduces the toughness of the steel material when used in a high temperature environment. Therefore, the Mn content is 2.00% or less.
  • the preferable lower limit of the Mn content is 0.01%, more preferably 0.10%, still more preferably 0.40%, still more preferably 0.50%, still more preferably 0.60. %.
  • the preferred upper limit of the Mn content is 1.80%, more preferably 1.60%, still more preferably 1.50%, still more preferably 1.30%, still more preferably 1.10. %, More preferably 0.95%.
  • P 0.045% or less Phosphorus (P) is inevitably contained. That is, the P content is more than 0%. P segregates at the grain boundaries of the steel material during large heat input welding. As a result, stress relaxation cracking resistance is reduced. If the P content exceeds 0.045%, the stress relaxation cracking resistance is lowered even if the content of other elements is within the range of the present embodiment. Therefore, the P content is 0.045% or less.
  • the preferred upper limit of the P content is 0.035%, more preferably 0.030%.
  • the P content is preferably as low as possible. However, excessive reduction of P content raises the manufacturing cost of steel materials. Therefore, considering normal industrial production, the preferable lower limit of the P content is 0.001%, more preferably 0.002%.
  • S 0.0300% or less Sulfur (S) is inevitably contained. That is, the S content is more than 0%. S segregates at the grain boundaries of the steel material during large heat input welding. As a result, stress relaxation cracking resistance is reduced. If the S content exceeds 0.0300%, the stress relaxation cracking resistance is lowered even if the content of other elements is within the range of the present embodiment. Therefore, the S content is 0.0300% or less.
  • the preferred upper limit of the S content is 0.0150%, more preferably 0.0100%, still more preferably 0.0050%, still more preferably 0.0030%.
  • the S content is preferably as low as possible. However, excessive reduction of S content raises the manufacturing cost of steel materials. Therefore, considering normal industrial production, the preferred lower limit of the S content is 0.0001%, more preferably 0.0002%.
  • Chromium (Cr) enhances the oxidation resistance and corrosion resistance of the steel material when used in a high temperature environment. If the Cr content is less than 15.00%, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment. On the other hand, if the Cr content exceeds 25.00%, the stability of austenite in the steel material in a high temperature environment is lowered even if the content of other elements is within the range of the present embodiment. In this case, the creep strength of the steel material decreases. Therefore, the Cr content is 15.00 to 25.00%.
  • the lower limit of the Cr content is preferably 16.00%, more preferably 16.20%, still more preferably 16.40%.
  • the preferred upper limit of the Cr content is 24.00%, more preferably 23.00%, still more preferably 22.00%, still more preferably 21.00%, still more preferably 20.00. %, More preferably 19.00%.
  • Ni 8.00 to 20.00%
  • Nickel (Ni) stabilizes austenite and increases the creep strength of steel materials in high temperature environments. If the Ni content is less than 8.00%, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment. On the other hand, if the Ni content exceeds 20.00%, the above effect is saturated and the production cost is further increased. Therefore, the Ni content is 8.00 to 20.00%.
  • the preferable lower limit of the Ni content is 8.50%, more preferably 9.00%, still more preferably 9.20%, still more preferably 9.40%.
  • the preferable upper limit of the Ni content is 18.00%, more preferably 16.00%, still more preferably 15.00%, still more preferably 14.00%.
  • N 0.050 to 0.250% Nitrogen (N) dissolves in the matrix (matrix) to stabilize austenite.
  • the solid solution N further forms fine nitrides in the steel during use in a high temperature environment. Since the fine nitride strengthens the Cr-deficient region, it enhances the stress relaxation crackability of the steel material. Fine nitrides produced during use in high temperature environments further increase creep strength by precipitation strengthening. If the N content is less than 0.050%, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment. On the other hand, if the N content exceeds 0.250%, Cr nitride (Cr 2 N) is generated at the grain boundaries even if the content of other elements is within the range of the present embodiment.
  • the N content is 0.050 to 0.250%.
  • the lower limit of the N content is preferably 0.052%, more preferably 0.055%, still more preferably 0.060%.
  • the preferred upper limit of the N content is 0.200%, more preferably 0.150%, still more preferably 0.120%.
  • Nb 0.10 to 1.00% Niobium (Nb), together with N, forms fine nitrides in steel during use in high temperature environments. Since the fine nitride strengthens the Cr-deficient region, it enhances the stress relaxation crackability of the steel material. Fine nitrides produced during use in high temperature environments further increase creep strength by precipitation strengthening. Nb further combines with C to form MX-type Nb carbides. By generating Nb carbide and fixing C, the amount of solid solution C in the steel material is reduced. As a result, during the use of the steel material in a high temperature environment, precipitation of Cr carbides at the grain boundaries is suppressed, and the stress relaxation resistance cracking property of the steel material is enhanced.
  • the Nb content is less than 0.10%, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment.
  • the Nb content exceeds 1.00%, nitrides and carbides are excessively produced even if the content of other elements is within the range of the present embodiment. In this case, the strength in the crystal grains becomes excessively high, and the difference in strength between the inside of the crystal grains and the grain boundaries becomes large. Therefore, stress concentration occurs at the grain interface, and the stress relaxation resistance cracking property is lowered. Therefore, the Nb content is 0.10 to 1.00%.
  • the preferable lower limit of the Nb content is 0.20%, more preferably 0.23%, still more preferably 0.25%, still more preferably 0.30%, still more preferably 0.35. %.
  • the preferred upper limit of the Nb content is 0.80%, more preferably 0.60%, still more preferably 0.50%.
  • Mo 0.05-5.00% Molybdenum (Mo) suppresses the formation and growth of M 23 C 6 type Cr carbides at grain boundaries during the use of steel materials in high temperature environments. As a result, the stress relaxation crackability of the steel material is enhanced. Mo, as a solid solution strengthening element, further enhances the creep strength of steel materials in a high temperature environment. If the Mo content is less than 0.05%, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment. On the other hand, if the Mo content exceeds 5.00%, the formation of intermetallic compounds such as the LAVES phase is remarkably promoted in the crystal grains even if the content of other elements is within the range of the present embodiment.
  • the Mo content is 0.05 to 5.00%.
  • the preferable lower limit of the Mo content is 0.06%, more preferably 0.10%, still more preferably 0.15%, still more preferably 0.20%, still more preferably 0.24. %, More preferably 0.28%, still more preferably 0.32%.
  • the preferred upper limit of the Mo content is 4.00%, more preferably 3.00%, still more preferably 2.00%, still more preferably 1.50%, still more preferably 1.00. %.
  • B 0.0005 to 0.0100% Boron (B) segregates at the grain boundaries during use of the steel material in a high temperature environment to increase the grain boundary strength. Therefore, the stress relaxation cracking resistance of the steel material is enhanced. If the B content is less than 0.0005%, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment. On the other hand, if the B content exceeds 0.0100%, B promotes the formation of Cr carbides at the grain boundaries even if the content of other elements is within the range of the present embodiment. In this case, the stress relaxation crackability of the steel material is reduced. Therefore, the B content is 0.0005 to 0.0100%.
  • the preferred lower limit of the B content is 0.0012%, more preferably 0.0014%, even more preferably 0.0016%, even more preferably 0.0018%, still more preferably 0.0020. %.
  • the preferred upper limit of the B content is 0.0080%, more preferably 0.0060%, still more preferably 0.0050%, still more preferably 0.0040%, still more preferably 0.0035. %, More preferably 0.0030%.
  • the balance of the chemical composition of the austenite-based stainless steel material according to this embodiment is composed of Fe and impurities.
  • the impurities are those mixed from ore, scrap, or the manufacturing environment as a raw material when the austenite-based stainless steel material is industrially manufactured, and adversely affect the austenite-based stainless steel material of the present embodiment. Means what is allowed within the range that does not give.
  • the contents of Sn, As, Zn, Pb and Sb are as follows. Sn: 0 to 0.010%, As: 0-0.010%, Zn: 0 to 0.010%, Pb: 0 to 0.010%, Sb: 0 to 0.010%, Tin (Sn), arsenic (As), zinc (Zn), lead (Pb) and antimony (Sb) are all impurities.
  • the Sn content may be 0%.
  • the As content may be 0%.
  • the Zn content may be 0%.
  • the Pb content may be 0%.
  • the Sb content may be 0%. When contained, all of these elements segregate at the grain boundaries to lower the melting point of the grain boundaries or reduce the binding force of the grain boundaries.
  • the hot workability and weldability of the steel material are lowered even if the content of other elements is within the range of the present embodiment.
  • the As content exceeds 0.010%
  • the hot workability and weldability of the steel material are lowered even if the content of other elements is within the range of the present embodiment.
  • the Zn content exceeds 0.010%
  • the hot workability and weldability of the steel material are lowered even if the other element content is within the range of the present embodiment.
  • the Pb content exceeds 0.010%, the hot workability and weldability of the steel material are lowered even if the content of other elements is within the range of the present embodiment.
  • the Sn content is 0 to 0.010%.
  • the As content is 0 to 0.010%.
  • the Zn content is 0 to 0.010%.
  • the Pb content is 0 to 0.010%.
  • the Sb content is 0 to 0.010%.
  • the chemical composition of the austenite-based stainless steel material according to the present embodiment may further contain one element or two or more elements selected from the group consisting of Ti, Ta, V, Zr and Hf instead of a part of Fe. .. All of these elements combine with C to form carbides and reduce the amount of solid solution C, thereby further enhancing the stress relaxation resistance and cracking property of the steel material.
  • Titanium (Ti) is an optional element and may not be contained. That is, the Ti content may be 0%. When contained, Ti combines with C in the steel to form carbides. As a result, the formation of Cr carbides is suppressed, and the stress relaxation resistance cracking property of the steel material is further enhanced. If even a small amount of Ti is contained, the above effect can be obtained to some extent. However, if the Ti content exceeds 0.50%, carbides will be excessively precipitated in the crystal grains even if the content of other elements is within the range of the present embodiment. In this case, the strength in the crystal grains becomes excessively high, and the difference in strength between the inside of the crystal grains and the grain boundaries becomes large.
  • the Ti content is 0 to 0.50%.
  • the lower limit of the Ti content is more than 0%, more preferably 0.01%, still more preferably 0.02%, still more preferably 0.03%.
  • the preferred upper limit of the Ti content is 0.45%, more preferably 0.40%, still more preferably 0.35%, still more preferably 0.30%.
  • Tantalum (Ta) is an optional element and may not be contained. That is, the Ta content may be 0%. When contained, Ta combines with C to form carbides. As a result, the formation of Cr carbides is suppressed, and the stress relaxation resistance cracking property of the steel material is further enhanced. If even a small amount of Ta is contained, the above effect can be obtained to some extent. However, if the Ta content exceeds 0.50%, carbides will be excessively precipitated in the crystal grains even if the content of other elements is within the range of the present embodiment. In this case, the strength in the crystal grains becomes excessively high, and the difference in strength between the inside of the crystal grains and the grain boundaries becomes large.
  • the Ta content is 0 to 0.50%.
  • the preferable lower limit of the Ta content is more than 0%, more preferably 0.01%, further preferably 0.02%, still more preferably 0.03%, still more preferably 0.05%.
  • the preferred upper limit of the Ta content is 0.45%, more preferably 0.40%, still more preferably 0.35%, still more preferably 0.30%.
  • V 0 to 1.00%
  • Vanadium (V) is an optional element and may not be contained. That is, the V content may be 0%. When contained, V combines with C to form carbides. As a result, the formation of Cr carbides is suppressed, and the stress relaxation resistance cracking property of the steel material is further enhanced. If even a small amount of V is contained, the above effect can be obtained to some extent. However, if the V content exceeds 1.00%, carbides will be excessively precipitated in the crystal grains even if the content of other elements is within the range of the present embodiment. In this case, the strength in the crystal grains becomes excessively high, and the difference in strength between the inside of the crystal grains and the grain boundaries becomes large.
  • the V content is 0 to 1.00%.
  • the preferable lower limit of the V content is more than 0%, more preferably 0.01%, further preferably 0.02%, still more preferably 0.04%, still more preferably 0.06. %.
  • the preferred upper limit of the V content is 0.50%, more preferably 0.40%, still more preferably 0.35%, still more preferably 0.30%.
  • Zr Zirconium
  • Zr Zirconium
  • the Zr content may be 0%.
  • Zr combines with C to form carbides.
  • the formation of Cr carbides is suppressed, and the stress relaxation resistance cracking property of the steel material is further enhanced. If even a small amount of Zr is contained, the above effect can be obtained to some extent.
  • the Zr content exceeds 0.10%, carbides will be excessively precipitated in the crystal grains even if the content of other elements is within the range of the present embodiment. In this case, the strength in the crystal grains becomes excessively high, and the difference in strength between the inside of the crystal grains and the grain boundaries becomes large.
  • the Zr content is 0 to 0.10%.
  • the preferable lower limit of the Zr content is more than 0%, more preferably 0.01%, still more preferably 0.02%.
  • the preferred upper limit of the Zr content is 0.09%, more preferably 0.08%, still more preferably 0.07%, still more preferably 0.06.
  • Hf 0 to 0.10%
  • Hafnium (Hf) is an optional element and may not be contained. That is, the Hf content may be 0%. When contained, Hf combines with C to form carbides. As a result, the formation of Cr carbides is suppressed, and the stress relaxation resistance cracking property of the steel material is further enhanced. If even a small amount of Hf is contained, the above effect can be obtained to some extent. However, if the Hf content exceeds 0.10%, carbides will be excessively precipitated in the crystal grains even if the content of other elements is within the range of the present embodiment. In this case, the strength in the crystal grains becomes excessively high, and the difference in strength between the inside of the crystal grains and the grain boundaries becomes large.
  • the Hf content is 0 to 0.10%.
  • the preferred lower limit of the Hf content is more than 0%, more preferably 0.01%, still more preferably 0.02%.
  • the preferred upper limit of the Hf content is 0.09%, more preferably 0.08%, still more preferably 0.07%, still more preferably 0.06%.
  • the chemical composition of the austenite-based stainless steel material according to the present embodiment may further contain one element or two or more elements selected from the group consisting of Cu, W and Co, instead of a part of Fe. All of these elements further enhance the creep strength of steel at average operating temperatures above 600-750 ° C.
  • Cu 0-4.00% Copper (Cu) is an optional element and may not be contained. That is, the Cu content may be 0%. When contained, Cu precipitates as a Cu phase in the grains during use of the steel material in a high temperature environment, and the creep strength of the steel material is further increased by precipitation strengthening. If the Cu content is contained even in a small amount, the above effect can be obtained to some extent. However, if the Cu content exceeds 4.00%, the precipitation amount of the Cu phase may increase and the creep ductility may decrease during use in a high temperature environment. Therefore, the Cu content is 0 to 4.00%.
  • the lower limit of the Cu content is more than 0%, more preferably 0.01%, still more preferably 0.05%, still more preferably 0.10%, still more preferably 0.20%. It is more preferably 0.30%.
  • the preferred upper limit of the Cu content is 3.50%, more preferably 3.00%, still more preferably 2.50%, still more preferably 2.00%.
  • W 0 to 5.00%
  • Tungsten (W) is an optional element and may not be contained. That is, the W content may be 0%. When contained, W further enhances the creep strength of the steel material by solid solution strengthening during use of the steel material in a high temperature environment. If W is contained even in a small amount, the above effect can be obtained to some extent. However, if the W content exceeds 5.00%, the stability of austenite will decrease and the toughness will decrease even if the content of other elements is within the range of this embodiment. Therefore, the W content is 0 to 5.00%.
  • the preferable lower limit of the W content is more than 0%, more preferably 0.01%, further preferably 0.10%, still more preferably 0.20%, still more preferably 0.25%. It is more preferably 0.30%.
  • the preferred upper limit of the W content is 4.00%, more preferably 3.00%, still more preferably 2.50%, still more preferably 2.00%, still more preferably 1.50. %.
  • Co is an optional element and may not be contained. That is, the Co content may be 0%. When contained, Co stabilizes austenite and further enhances the creep strength of the steel at average operating temperatures above 600-750 ° C. If even a small amount of Co is contained, the above effect can be obtained to some extent. However, if the Co content exceeds 1.00%, the raw material cost increases even if the content of other elements is within the range of the present embodiment. Therefore, the Co content is 0 to 1.00%.
  • the lower limit of the Co content is preferably more than 0%, more preferably 0.01%, still more preferably 0.04%, still more preferably 0.10%.
  • the preferred upper limit of the Co content is 0.90%, more preferably 0.80%, still more preferably 0.70%, still more preferably 0.60%.
  • the chemical composition of the austenite-based stainless steel material according to the present embodiment may further contain Al instead of a part of Fe. Al deoxidizes the steel in the steelmaking process.
  • sol. Al 0 to 0.100%
  • Aluminum (Al) is an optional element and may not be contained. That is, the Al content may be 0%. When contained, Al deoxidizes the steel in the steelmaking process. If Al is contained even in a small amount, the above effect can be obtained to some extent. However, sol. If the Al content exceeds 0.100%, the workability and ductility of the steel material will decrease even if the other element content is within the range of this embodiment. Therefore, sol.
  • the Al content is 0 to 0.100%. sol.
  • the lower limit of the Al content is more than 0%, more preferably 0.001%, still more preferably 0.005%, still more preferably 0.010%.
  • the preferred upper limit of the Al content is 0.080%, more preferably 0.060%, still more preferably 0.040%. In this embodiment, sol.
  • the Al content means the content of acid-soluble Al (sol.Al).
  • the chemical composition of the austenite-based stainless steel material according to the present embodiment may further contain one element or two or more elements selected from the group consisting of Ca, Mg and rare earth elements (REM) instead of a part of Fe. .. All of these elements enhance the hot workability of steel materials.
  • REM rare earth elements
  • Ca 0-0.0200% Calcium (Ca) is an optional element and may not be contained. That is, the Ca content may be 0%. When contained, Ca fixes O (oxygen) and S (sulfur) as inclusions and enhances the hot workability of the steel material. Ca further fixes S and suppresses grain boundary segregation of S. This reduces embrittlement cracking of HAZ during welding. If even a small amount of Ca is contained, the above effect can be obtained to some extent. However, if the Ca content exceeds 0.0200%, the cleanliness of the steel material is lowered and the hot workability of the steel material is rather lowered even if the content of other elements is within the range of the present embodiment. Therefore, the Ca content is 0 to 0.0200%.
  • the preferable lower limit of the Ca content is more than 0%, more preferably 0.0001%, still more preferably 0.0002%, still more preferably 0.0005%.
  • the preferred upper limit of the Ca content is 0.0150%, more preferably 0.0100%, even more preferably 0.0080%, even more preferably 0.0050%, still more preferably 0.0040. %.
  • Mg 0 to 0.0200%
  • Magnesium (Mg) is an optional element and may not be contained. That is, the Mg content may be 0%. When contained, Mg fixes O (oxygen) and S (sulfur) as inclusions and enhances the hot workability of the steel material. Mg further fixes S and suppresses grain boundary segregation of S. This reduces embrittlement cracking of HAZ during welding. If even a small amount of Mg is contained, the above effect can be obtained to some extent. However, if the Mg content exceeds 0.0200%, the cleanliness of the steel material is lowered and the hot workability of the steel material is rather lowered even if the content of other elements is within the range of the present embodiment.
  • the Mg content is 0 to 0.0200%.
  • the preferable lower limit of the Mg content is more than 0%, more preferably 0.0001%, still more preferably 0.0002%, still more preferably 0.0005%.
  • the preferred upper limit of the Mg content is 0.0150%, more preferably 0.0100%, even more preferably 0.0080%, even more preferably 0.0050%, still more preferably 0.0040. %.
  • Rare earth element 0 to 0.100%
  • Rare earth elements are optional elements and may not be contained. That is, the REM content may be 0%. When contained, REM fixes O (oxygen) and S (sulfur) as inclusions and enhances the hot workability of the steel material. However, if the REM content is too high, the hot workability of the steel material will decrease even if the content of other elements is within the range of this embodiment. Therefore, the REM content is 0 to 0.100%.
  • the preferred lower limit of the REM content is more than 0%, more preferably 0.001%, still more preferably 0.002%.
  • the preferred upper limit of the REM content is 0.080%, more preferably 0.060%.
  • the REM in the present specification contains at least one element or two or more elements of Sc, Y, and a lanthanoid (Atomic number 57 La to 71 Lu), and the REM content is the total content of these elements. Means quantity.
  • the chemical composition of the austenite-based stainless steel material of the present embodiment can be determined by a well-known component analysis method. Specifically, when the austenite-based stainless steel material is a steel pipe, a drill having a diameter of 5 mm is used to drill at the center position of the wall thickness to generate chips, and the chips are collected. When the austenite-based stainless steel material is a steel plate, a drill having a diameter of 5 mm is used to drill at the center of the plate width and the center of the plate thickness to generate chips, and the chips are collected.
  • the austenite-based stainless steel material is steel bar
  • a drill having a diameter of 5 mm is used to drill at the R / 2 position to generate chips, and the chips are collected.
  • the R / 2 position means the central position of the radius R in the cross section perpendicular to the longitudinal direction of the steel bar.
  • ICP-AES Inductively Coupled Plasma Atomic Emission Spectroscopy
  • C content and S content are determined by a well-known high-frequency combustion method (combustion-infrared absorption method).
  • the N content is determined using the well-known Inactive Gas Melt-Thermal Conductivity Method.
  • Solid solution N ratio Solid solution N amount in steel material (mass%) / N content in steel material (mass%)
  • the solid solution N ratio is 0.40 to 0.90.
  • the solid solution N ratio is less than 0.40, there is too much nitride in the austenite-based stainless steel material. In this case, since the amount of N solid solution in the steel material is insufficient, fine nitrides are not sufficiently precipitated in the Cr-deficient region during use in a high-temperature environment. Therefore, the stress relaxation cracking property and creep strength of the steel material in a high temperature environment are lowered. On the other hand, if the solid solution N ratio exceeds 0.90, the amount of nitride in the austenite-based stainless steel material is too small. In this case, the grain refinement by the nitride becomes insufficient. As a result, the strength of the grain boundaries is lowered, and the stress relaxation resistance cracking property is lowered.
  • the solid solution N ratio is 0.40 to 0.90, a sufficient amount of solid solution N is present in the austenite-based stainless steel material to form a nitride during use in a high temperature environment, and crystals are formed. There are enough nitrides to refine the grains. Therefore, sufficient stress relaxation cracking resistance and creep strength can be obtained in the austenite-based stainless steel material in a high temperature environment.
  • the preferable lower limit of the solid solution N ratio is 0.45, more preferably 0.48, still more preferably 0.50, still more preferably 0.55, still more preferably 0.58. , More preferably 0.60, still more preferably 0.63.
  • the preferable upper limit of the solid solution N ratio is 0.88, more preferably 0.86, still more preferably 0.85, still more preferably 0.83, still more preferably 0.80. It is more preferably 0.78, still more preferably 0.75.
  • the cross section perpendicular to the longitudinal direction of the test piece may be circular or rectangular.
  • the austenite-based stainless steel material is a steel pipe
  • the test piece is collected so that the center of the cross section perpendicular to the longitudinal direction of the test piece is the wall thickness center position and the longitudinal direction of the test piece is the longitudinal direction of the steel pipe.
  • the austenite-based stainless steel material is a steel plate
  • the test piece is collected so that the center of the cross section perpendicular to the longitudinal direction of the test piece is the center of the plate thickness and the longitudinal direction of the test piece is the longitudinal direction of the steel plate.
  • the test piece is sampled so that the center of the cross section perpendicular to the longitudinal direction of the test piece is the R / 2 position of the steel bar and the longitudinal direction of the test piece is the longitudinal direction of the steel bar. ..
  • the surface of the collected test piece is polished by about 50 ⁇ m by preliminary electrolytic polishing to obtain a new surface.
  • the electropolished test piece is electrolyzed with an electrolytic solution (10% acetylacetone + 1% tetraammonium + methanol).
  • the electrolytic solution after electrolysis is passed through a 0.2 ⁇ m filter to capture the residue.
  • the obtained residue is acid-decomposed and the mass of N in the residue is determined by ICP (inductively coupled plasma) emission spectrometry. Further, the mass of the test piece before the main electrolysis and the mass of the test piece after the main electrolysis are measured.
  • the value obtained by subtracting the mass of the test piece after the main electrolysis from the mass of the test piece before the main electrolysis is defined as the amount of the base material subjected to the main electrolysis.
  • the shape of the austenite-based stainless steel material of the present embodiment is not particularly limited.
  • the austenite-based stainless steel material of the present embodiment may be a steel pipe, a steel plate, or a steel bar. Further, the austenite-based stainless steel material of the present embodiment may be a forged product.
  • the austenite-based stainless steel material of the present embodiment is suitable for equipment applications used at an average operating temperature of more than 600 to 750 ° C. (that is, a high temperature environment).
  • the austenite-based stainless steel material of the present embodiment is further suitable for equipment applications that are used for a long period of time at an average operating temperature of more than 600 to 750 ° C. after high heat input welding is performed.
  • the average operating temperature is over 600 to 750 ° C, and even if the operating temperature temporarily exceeds 750 ° C, if the average operating temperature is over 600 to 750 ° C, the austenite-based stainless steel of the present embodiment Suitable for use of steel materials.
  • the maximum temperature reached of these devices may be higher than 750 ° C.
  • Such equipment is, for example, equipment for chemical plant equipment represented by petroleum refining and petrochemistry. These devices include, for example, a heating furnace pipe, a tank, a pipe, and the like.
  • the austenite-based stainless steel material of the present embodiment can naturally be used for equipment other than chemical plant equipment.
  • the equipment other than the chemical plant equipment is, for example, a thermal power generation boiler equipment (for example, a boiler tube), which is expected to be used at an average operating temperature of more than 600 to 750 ° C. like the chemical plant equipment.
  • austenite-based stainless steel material of the present embodiment a method for producing the austenite-based stainless steel material of the present embodiment.
  • the method for producing an austenite-based stainless steel material described below is an example of the method for producing an austenite-based stainless steel material according to the present embodiment. Therefore, the austenite-based stainless steel material having the above-mentioned structure may be manufactured by a manufacturing method other than the manufacturing methods described below. However, the manufacturing method described below is a preferable example of the manufacturing method of the austenite-based stainless steel material of the present embodiment.
  • the method for producing an austenite-based stainless steel material of the present embodiment requires a step of preparing a material (preparation step), a step of performing hot working on the material to manufacture an intermediate steel material (hot working step), and a necessary step.
  • the intermediate steel material after the hot working process is pickled and then cold-worked (cold working process), and the intermediate steel material after the cold working process is melted.
  • a material having the above-mentioned chemical composition is prepared.
  • the material may be supplied by a third party or may be manufactured.
  • the material may be ingot, slab, bloom, billet.
  • the material is manufactured by the following method.
  • a molten steel having the above-mentioned chemical composition is produced.
  • the ingot is manufactured by the ingot method using the manufactured molten steel.
  • Slabs, blooms, and billets may be produced by a continuous casting method using the produced molten steel.
  • the billets may be manufactured by performing hot working on the manufactured ingots, slabs, and blooms.
  • the ingot may be hot forged to produce a cylindrical billet, and this billet may be used as a material (cylindrical material).
  • the temperature of the material immediately before the start of hot forging is not particularly limited, but is, for example, 1000 to 1300 ° C.
  • the method of cooling the material after hot forging is not particularly limited.
  • the intermediate steel material may be, for example, a steel pipe, a steel plate, or a steel bar.
  • the intermediate steel material is a steel pipe
  • the following processing is performed in the hot processing process.
  • An intermediate steel material (steel pipe) is manufactured by performing hot extrusion represented by the Eugene Sejurne method on a cylindrical material having through holes.
  • the temperature of the material immediately before hot extrusion is not particularly limited.
  • the temperature of the material immediately before hot extrusion is, for example, 1000 to 1300 ° C.
  • a hot punching pipe manufacturing method may be carried out.
  • a steel pipe may be manufactured by performing perforation rolling by the Mannesmann method.
  • the round billet is drilled and rolled by a drilling machine.
  • the drilling ratio is not particularly limited, but is, for example, 1.0 to 4.0.
  • the perforated round billet is further hot-rolled with a mandrel mill, reducer, sizing mill or the like to form a raw pipe.
  • the cumulative surface reduction rate in the hot working process is not particularly limited, but is, for example, 20 to 80%.
  • the hot working process uses, for example, one or more rolling mills equipped with a pair of work rolls.
  • a steel plate is manufactured by hot rolling a material such as a slab using a rolling mill. The material is heated before hot rolling. Hot rolling is performed on the heated material. The temperature of the material immediately before hot rolling is, for example, 1000 to 1300 ° C.
  • the hot working process includes, for example, a rough rolling process and a finish rolling process.
  • the material is hot-processed to produce billets.
  • a bulk rolling mill is used for the rough rolling process. Billets are manufactured by performing slab rolling on the material with a slab rolling mill.
  • a continuous rolling mill is installed downstream of the ingot rolling mill, hot rolling is further performed on the billet after the ingot rolling using the continuous rolling mill to produce a smaller billet. You may.
  • a continuous rolling mill for example, horizontal stands having a pair of horizontal rolls and vertical stands having a pair of vertical rolls are alternately arranged in a row.
  • materials such as bloom are manufactured into billets.
  • the material temperature immediately before the rough rolling step is not particularly limited, but is, for example, 1000 to 1300 ° C.
  • the finish rolling process the billet is first heated.
  • the billets after heating are hot-rolled using a continuous rolling mill to produce steel bars.
  • the heating temperature in the heating furnace in the finish rolling step is not particularly limited, but is, for example, 1000 to 1300 ° C.
  • the intermediate steel material after hot working is allowed to cool for a certain period of time and then rapidly cooled.
  • the conditions for quenching are as follows. Time from completion of hot working to start of quenching t1: 0.50 to 5.00 minutes Intermediate steel temperature at start of quenching T1: 700 ° C or higher Cooling rate from completion of hot working to start of quenching CR1: 15 ° C / min that's all
  • the time t1 (minutes) from the completion of hot working to the start of quenching is referred to as "leaving time" t1.
  • a water cooling device is used.
  • the intermediate steel material is rapidly cooled (water cooled) by a water cooling device.
  • the intermediate steel material is intentionally left for a certain period of time. This promotes the formation of nitrides.
  • the standing time t1 is shorter than 0.50 minutes, quenching is started without sufficiently forming nitrides.
  • the solid solution N ratio becomes more than 0.90, and the nitride is insufficient. Therefore, the pinning effect is not sufficiently obtained, the crystal grains are coarsened, and the stress relaxation resistance cracking property of the steel material is lowered.
  • the standing time t1 is longer than 5.00 minutes, a large amount of nitride is generated in the intermediate steel material during the leaving time t1. In this case, even if the other conditions in the hot working step and the conditions in the solution treatment step described later are satisfied, the solid solution N ratio is less than 0.40%, and the solid solution N amount is insufficient.
  • the standing time t1 is 0.50 to 5.00 minutes, the solid-dissolved N ratio is 0.40 to 0.90 on the premise that other manufacturing conditions are satisfied, and excellent stress relaxation resistance and cracking resistance Creep strength is obtained.
  • the preferable upper limit of the leaving time t1 is 4.50 minutes, more preferably 4.00 minutes, and further preferably 3.50 minutes.
  • the temperature T1 (° C.) of the intermediate steel material at the start of quenching is referred to as "quenching start temperature" T1. If the quenching start temperature T1 is less than 700 ° C., coarse nitrides are formed in the intermediate steel material during the standing time t1. In addition, Cr carbides are generated at the grain boundaries. In this case, during the standing time t1, the nitride grows coarsely in the intermediate steel material, and the Cr carbides at the grain boundaries become coarse. In this case, the solid solution N ratio is less than 0.40, and the stress relaxation cracking resistance and creep strength are lowered. When the quenching start temperature T1 is 700 ° C.
  • the pinning effect of fine nitrides also acts on the intermediate steel material during the standing time t1, and the coarsening of crystal grains is suppressed. Therefore, the crystal grains of the intermediate steel material after quenching are maintained finely.
  • the solid solution N ratio is 0.40 to 0.90, and excellent stress relaxation resistance cracking resistance and creep strength can be obtained.
  • the preferred lower limit of the quenching start temperature T1 is 750 ° C., more preferably 780 ° C., still more preferably over 790 ° C., and even more preferably 800 ° C.
  • the preferred lower limit of the cooling rate CR1 is 18 ° C./min, more preferably 20 ° C./min.
  • the cooling rate CR1 is a value obtained by dividing the difference between the surface temperature of the intermediate steel material immediately after the completion of hot working and the surface temperature of the intermediate steel material immediately before the start of quenching by the standing time t1.
  • the cold working process is carried out as needed. That is, the cold working process does not have to be carried out.
  • the intermediate steel material is pickled and then cold-worked.
  • the cold working is, for example, cold drawing.
  • the intermediate steel material is a steel plate
  • the cold working is, for example, cold rolling.
  • strain is applied to the intermediate steel material before the solution treatment step. As a result, recrystallization and sizing can be performed during the solution treatment step.
  • the surface reduction rate in the cold working process is not particularly limited, but is, for example, 10 to 90%.
  • the solution treatment is carried out on the intermediate steel material after the hot working step or the cold working step.
  • the solution treatment is carried out by the following method.
  • An intermediate steel material is charged into a heat treatment furnace in which the atmosphere inside the furnace is an atmospheric atmosphere.
  • the atmospheric atmosphere referred to here means an atmosphere containing 78% or more by volume of nitrogen, which is a gas constituting the atmosphere, and 20% or more by volume of oxygen.
  • the temperature is maintained at the solution treatment temperature, and then the mixture is rapidly cooled at the cooling rate described later.
  • the solid solution N ratio can be set to 0.4 to 0.9 in the austenite-based stainless steel material having the above-mentioned chemical composition. can do.
  • Solution treatment temperature T2 1020 to 1350 ° C
  • Cooling rate CR2 5 ° C / sec or more
  • the solution treatment temperature T2 is 1020 to 1350 ° C.
  • the solid solution N ratio is 0.40 to 0.90 on the premise that other conditions are also satisfied.
  • the preferable lower limit of the solution treatment temperature T2 is 1030 ° C.
  • the upper limit of the solution treatment temperature T2 is preferably 1300 ° C, more preferably 1250 ° C.
  • the holding time at the solution treatment temperature T2 is not particularly limited.
  • the holding time at the solution treatment temperature T2 is, for example, 2 minutes or more.
  • the upper limit of the holding time is not particularly limited, but is, for example, 500 minutes.
  • the cooling rate CR2 After holding at the solution treatment temperature T2, the cooling rate CR2 in the temperature range of at least 1000 to 600 ° C. is cooled at 5 ° C./sec or more.
  • the cooling rate CR2 referred to here means an average cooling rate (° C./sec) in a temperature range in which the steel material temperature is 1000 to 600 ° C.
  • the cooling rate CR2 is less than 5 ° C./sec, an excessively large amount of coarse nitride precipitates is generated during cooling. As a result, the solid solution N ratio is less than 0.40.
  • the cooling rate CR2 is 5 ° C./sec or more, it is possible to suppress the formation of an excessively large amount of nitride in the steel material while cooling in the temperature range of 1000 to 600 ° C. As a result, the solid solution N ratio is 0.40 to 0.90 on the premise that other conditions are satisfied.
  • the preferable lower limit of the cooling rate CR2 is 6 ° C./sec, and more preferably 7 ° C./sec.
  • the quenching method may be water cooling or oil cooling.
  • the austenite-based stainless steel material of the present embodiment can be manufactured.
  • the above-mentioned manufacturing method is an example of the manufacturing method of the austenite-based stainless steel material of the present embodiment. Therefore, the method for producing the austenite-based stainless steel material of the present embodiment is not limited to the above-mentioned production method.
  • the austenite-based stainless steel material of the present embodiment is not limited to the above-mentioned production method as long as it has the above-mentioned chemical composition and the solid solution N ratio is 0.40 to 0.90.
  • each element in the chemical composition is within the above numerical range, and the solid solution N ratio is 0.40 to 0.90. Therefore, the austenite-based stainless steel material of the present embodiment has high creep strength and excellent resistance even when used for a long period of time at an average operating temperature of more than 600 to 750 ° C. after large heat injection welding. Has stress relaxation cracking property.
  • the welded joint is manufactured by the following method.
  • a groove is formed on the prepared base material. Specifically, a groove is formed at the end of the base metal by a well-known processing method.
  • the groove shape may be a V shape, a U shape, an X shape, or a shape other than the V shape, the U shape, and the X shape. ..
  • Welding is performed on the prepared base metal to manufacture a welded joint. Specifically, two base materials having a groove formed are prepared. Match the prepared base metal grooves with each other. Then, welding is performed on the pair of abutted groove portions using the above-mentioned welding material to form a weld metal having the above-mentioned chemical composition.
  • the welding method may be one layer of weld metal or multi-layer welding.
  • the welding methods are, for example, TIG welding (GTAW), shielded metal arc welding (SMAW), flux-welded wire arc welding (FCAW), gas metal arc welding (GMAW), and submerged arc welding (SAW).
  • GTAW TIG welding
  • SMAW shielded metal arc welding
  • FCAW flux-welded wire arc welding
  • GMAW gas metal arc welding
  • SAW submerged arc welding
  • Blanks in Table 1 indicate that the corresponding element content was below the detection limit. If it was below the detection limit, it was considered that the element was not contained.
  • An ingot with an outer diameter of 120 mm and a weight of 30 kg was manufactured using molten steel. Hot forging was performed on the ingot to obtain a material having a thickness of 30 mm. The temperature of the ingot before hot forging was 1250 ° C. Further, the material was hot-rolled, and the steel material after the hot-rolling was rapidly cooled (water-cooled) to produce an intermediate steel material (steel plate) having a thickness of 15 mm. At that time, the material temperature before hot working (hot rolling) was changed to 1050 to 1250 ° C.
  • the leaving time t1 (minutes) from the completion of hot working to the start of quenching (water cooling), the quenching start temperature T1 (° C.), and the cooling rate CR1 (° C./min) from the completion of hot working to the start of quenching. ) was changed.
  • the leaving time t1 of the test numbers A1 to A17, B1 to B5, B7 to B9 and B11 was 0.50 to 5.00 minutes.
  • the leaving time t1 of the test number B6 was 6.00 to 7.00 minutes.
  • the leaving time t1 of the test number B10 was 0.25 minutes.
  • the quenching start temperature T1 of the test numbers A1 to A17, B1 to B6 and B8 to B11 was 700 ° C.
  • the quenching start temperature T1 of the test number B7 was 600 to 650 ° C.
  • the cooling rates CR1 of the test numbers A1 to A17, B1 to B7 and B10 to B11 were 15 ° C./min or more.
  • the cooling rates CR1 of test numbers B8 and B9 were 10 ° C./min or less.
  • the intermediate steel material after hot rolling was subjected to solution treatment.
  • the solution treatment temperature T2 in the solution treatment was in the range of 1050 to 1250 ° C., and the holding time at the solution treatment temperature T2 was 10 minutes.
  • the cooling rate CR2 was 10 to 20 ° C./sec.
  • the intermediate steel material of test number B11 was not solution-treated. Through the above steps, austenite-based stainless steel materials having each test number were manufactured.
  • the chemical composition of the austenite-based stainless steel material of each test number was determined by the following method. Using a drill with a diameter of 5 mm, drilling was performed at the center of the plate width and the center of the plate thickness of the steel material (steel plate) to generate chips, and the chips were collected. The collected chips were dissolved in acid to obtain a solution. ICP-AES was carried out on the solution to perform elemental analysis of the chemical composition. The C content and S content were determined by a well-known high-frequency combustion method (combustion-infrared absorption method). The N content was determined using the well-known Inactive Gas Melt-Thermal Conductivity Method. As a result, the chemical composition of the steel material of each test number was as shown in Table 1.
  • the solid solution N ratio of the austenite-based stainless steel material of each test number was determined by the following method.
  • a test piece was collected from an austenite-based stainless steel material (steel plate). Specifically, the test piece was collected so that the center of the cross section perpendicular to the longitudinal direction of the test piece was the center position of the plate thickness and the longitudinal direction of the test piece was the longitudinal direction of the steel sheet.
  • the surface of the collected test piece was polished to about 50 ⁇ m by preliminary electrolytic polishing to obtain a new surface.
  • the electropolished test piece was electrolyzed with an electrolytic solution (10% acetylacetone + 1% tetraammonium + methanol).
  • the electrolytic solution after electrolysis was passed through a 0.2 ⁇ m filter to capture the residue.
  • the obtained residue was acid-decomposed and the mass of N in the residue was determined by ICP (inductively coupled plasma) emission spectrometry. Further, the mass of the test piece before the main electrolysis and the mass of the test piece after the main electrolysis were measured.
  • the value obtained by subtracting the mass of the test piece after the main electrolysis from the mass of the test piece before the main electrolysis was defined as the amount of the base material subjected to the main electrolysis.
  • Square test pieces including the center position of the plate width and the center position of the plate thickness of the austenite stainless steel material of each test number were collected.
  • the longitudinal direction of the angular test piece was parallel to the longitudinal direction of the austenite-based stainless steel material.
  • the length of the square test piece was 100 mm.
  • the cross section (cross section) perpendicular to the longitudinal direction of the square test piece was a rectangle of 10 mm ⁇ 10 mm.
  • the center position of the cross section of the square test piece almost coincided with the center position of the plate width and the center position of the plate thickness of the austenite stainless steel material.
  • the following thermal history was given to the angular test piece using a high-frequency thermal cycle device.
  • the angular test piece was heated from room temperature to 1400 ° C. at 70 ° C./sec in the air. Further, it was held at 1400 ° C. for 10 seconds. Then, the angular test piece was cooled to room temperature at a cooling rate of 20 ° C./sec.
  • Stress relaxation crackability evaluation test (SR crack evaluation test) A stress relaxation resistance cracking test conforming to ASTM E328-02 was carried out using a large heat input welding simulated test piece.
  • a test piece for SR crack evaluation test was prepared from a large heat input welding simulated test piece.
  • 10% of cold strain at room temperature was applied to the test piece in a heating furnace.
  • the test piece in the heating furnace was heated to 650 ° C., and the test piece at 650 ° C. was further imparted with 10% strain and held for 1000 hours.
  • the test piece after 1000 hours was allowed to cool to room temperature.
  • the stress relaxation resistance cracking property was low (indicated as "B" (Bad) in the "SR cracking test” column in Table 2).
  • SEM scanning electron microscope
  • a creep rupture test conforming to JIS Z2271 (2010) was carried out. Specifically, the creep rupture test piece was heated at 650 ° C., and then the creep rupture test was performed. The test stress was 118 MPa, and the creep rupture time (time) was determined.
  • Table 2 shows the test results. With reference to Tables 1 and 2, in test numbers A1 to A17, the content of each element in the chemical composition was appropriate, and the N solid solution ratio was in the range of 0.40 to 0.90. Therefore, high creep strength was obtained, and stress relaxation resistance cracking resistance was high.
  • test number B1 the C content was too high. Therefore, the stress relaxation resistance cracking property was low.
  • test number B2 the Nb content was low. Therefore, the stress relaxation cracking property and the creep strength were low.
  • test number B3 the N content was low. Therefore, the stress relaxation cracking property and the creep strength were low.
  • test number B4 the Mo content was low. Therefore, the stress relaxation resistance cracking property was low.
  • test number B5 the B content was low. Therefore, the stress relaxation resistance cracking property was low.
  • test number B6 the leaving time t1 in the hot working process was too long. Therefore, the solid solution N ratio was less than 0.40. As a result, stress relaxation cracking resistance and creep strength were low.
  • test number B7 the quenching start temperature T1 in the hot working process was low. Therefore, the solid solution N ratio was less than 0.40. As a result, stress relaxation cracking resistance and creep strength were low.
  • test numbers B8 and B9 the cooling rate CR1 from the completion of hot working to the start of quenching was too slow. Therefore, the solid solution N ratio was less than 0.40. As a result, the stress relaxation cracking property and the creep strength were too low.
  • test number B10 the leaving time t1 from the completion of hot working to the start of quenching was too short. Therefore, the solid solution N ratio exceeded 0.90. As a result, the stress relaxation resistance cracking property was low.
  • test number B11 the solution treatment was not carried out. Therefore, the solid solution N ratio was less than 0.40. As a result, stress relaxation cracking resistance and creep strength were low.

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WO2023228979A1 (ja) * 2022-05-24 2023-11-30 日本製鉄株式会社 オーステナイト系ステンレス合金溶接継手、及び、オーステナイト系ステンレス合金溶接材料
JP7828015B2 (ja) 2022-05-24 2026-03-11 日本製鉄株式会社 オーステナイト系ステンレス合金溶接継手、及び、オーステナイト系ステンレス合金溶接材料
WO2023238851A1 (ja) * 2022-06-07 2023-12-14 日本製鉄株式会社 オーステナイト系ステンレス合金材
JPWO2023238851A1 (https=) * 2022-06-07 2023-12-14
JP7820667B2 (ja) 2022-06-07 2026-02-26 日本製鉄株式会社 オーステナイト系ステンレス合金材
EP4538406A4 (en) * 2022-06-07 2026-04-15 Nippon Steel Corp AUSTENITICAL STAINLESS ALLOY MATERIAL
WO2024135557A1 (ja) * 2022-12-19 2024-06-27 日本製鉄株式会社 オーステナイト系ステンレス鋼管及びその製造方法
WO2025258673A1 (ja) * 2024-06-12 2025-12-18 日本製鉄株式会社 オーステナイト系ステンレス鋼管及びその製造方法
WO2025258672A1 (ja) * 2024-06-12 2025-12-18 日本製鉄株式会社 オーステナイト系ステンレス鋼管及びその製造方法

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US20220411908A1 (en) 2022-12-29
EP4089195A1 (en) 2022-11-16
CN114929917B (zh) 2023-11-03
CN114929917A (zh) 2022-08-19
EP4089195A4 (en) 2024-03-20
US12188111B2 (en) 2025-01-07

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