WO2022080374A1 - オーステナイト系ステンレス鋼箔 - Google Patents

オーステナイト系ステンレス鋼箔 Download PDF

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WO2022080374A1
WO2022080374A1 PCT/JP2021/037756 JP2021037756W WO2022080374A1 WO 2022080374 A1 WO2022080374 A1 WO 2022080374A1 JP 2021037756 W JP2021037756 W JP 2021037756W WO 2022080374 A1 WO2022080374 A1 WO 2022080374A1
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stainless steel
austenitic stainless
steel foil
cold rolling
content
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French (fr)
Japanese (ja)
Inventor
光治 米村
圭一 木村
拓也 平賀
裕二 隈
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Nippon Steel Chemical and Materials Co Ltd
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Nippon Steel Chemical and Materials Co Ltd
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Priority to KR1020237011944A priority Critical patent/KR102854963B1/ko
Priority to CN202180069593.5A priority patent/CN116324008B/zh
Priority to US18/031,193 priority patent/US12428699B2/en
Priority to JP2022557009A priority patent/JP7518182B2/ja
Publication of WO2022080374A1 publication Critical patent/WO2022080374A1/ja
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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
    • 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
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    • 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 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
    • C—CHEMISTRY; METALLURGY
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    • 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 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
    • 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
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
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    • 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 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
    • C21D8/0263—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 following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • 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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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—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
    • 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
    • C21D2211/008—Martensite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries

Definitions

  • This disclosure relates to stainless steel foils, and more particularly to austenitic stainless steel foils.
  • JP-A-1-309919 Patent Document 1
  • JP-A-2005-307295 Patent Document 2 propose techniques for increasing the fatigue strength of austenitic stainless steel foils.
  • the stainless steel foil disclosed in Patent Document 1 is, in weight%, C: 0.02 to 0.2%, Si: 0.1 to 2%, Mn: 0.1 to 2%, S: 0.006. % Or less, Ni: 6.0 to 10.5%, Cr: 16 to 20%, Al: 0.01% or less, O: 0.01% or less, Mg: 0.001% or less, Ca: 0.0001 Stainless steel consisting of ⁇ 0.005%, N: 0.01 ⁇ 0.2%, and the balance Fe is repeatedly cold-rolled and annealed to a total rolling ratio of 98% or more and a final plate thickness of 100 ⁇ m or less. , The size of inclusions shall be 7 ⁇ m or less. It is described in Patent Document 1 that the stainless steel foil has excellent fatigue characteristics.
  • the austenitic stainless steel foil for springs disclosed in Patent Document 2 is a stainless steel strip for springs of JIS Z 4313 SUS301-CSP, and the average peak spacing Sm of the surface cross-sectional curve in the direction perpendicular to the rolling direction is 40 ⁇ m. Is. Patent Document 2 describes that the austenitic stainless steel foil for springs has excellent durability (fatigue characteristics).
  • an austenitic stainless steel foil having excellent fatigue strength can be obtained.
  • austenitic stainless steel foil having excellent fatigue strength may be obtained by a technique other than the techniques proposed in Patent Documents 1 and 2.
  • An object of the present disclosure is to provide an austenitic stainless steel foil having excellent fatigue strength.
  • the austenitic stainless steel foil according to the present disclosure is by mass%, C: 0.150% or less, Si: 1.00% or less, Mn: 2.00% or less, P: 0.045% or less, S: 0.0300% or less, Cr: 16.00 to 20.00%, Ni: 6.00 to 10.50%, N: 0.100% or less, Mo: 0-2.50%, Nb: 0 to 0.12%, V: 0 to 1.00%, Ta: 0 to 0.50%, Hf: 0 to 0.10%, Co: 0 to 0.50%, B: 0 to 0.0100%, Ca: 0-0.0200%, Mg: 0-0.0200%, Rare earth elements: 0-0.0100%, Al: 0 to 0.010%, Ti: 0 to 0.500%, Zr: 0 to 0.100%, Cu: 0 to 3.00% and The rest consists of Fe and impurities In the X-ray diffraction profile by CuK ⁇ ray, the half width Fw of the peak of the ⁇ 111 ⁇
  • the austenitic stainless steel foil according to the present disclosure has excellent fatigue strength.
  • FIG. 1 is a diagram showing the relationship between the half width Fw of the peak of the ⁇ 111 ⁇ plane and the number of fatigues in the X-ray diffraction profile of the CuK ⁇ ray of this embodiment.
  • FIG. 3 is a schematic diagram for explaining a method of measuring the bending habit angle shown in FIG. 2.
  • the present inventors investigated and examined a method for increasing the fatigue strength of austenitic stainless steel foil. As a result, the following findings were obtained.
  • the present inventors focused on the chemical composition and examined a method for obtaining an austenitic stainless steel foil having excellent fatigue strength.
  • C 0.150% or less
  • Si 1.00% or less
  • Mn 2.00% or less
  • P 0.045% or less
  • S 0.0300% or less
  • Cr 16 .00 to 20.00%
  • Ni 6.00 to 10.50%
  • N 0.100% or less
  • Mo 0 to 2.50%
  • Nb 0 to 0.12%
  • V 0-1 .00%
  • Ta 0 to 0.50%
  • B 0 to 0.0100%
  • Ca 0 to 0.0200%
  • Mg 0 to 0.0200%
  • rare earth elements 0 to 0.0100%
  • Al 0 to 0.010%
  • Ti 0 to 0.500%
  • Zr 0 to 0.100%
  • Cu 0 to 3
  • the present inventors manufactured various austenitic stainless steel foils having the above-mentioned chemical composition and investigated their fatigue strengths. As a result, it was clarified that even the austenitic stainless steel foil having the above-mentioned chemical composition may not have excellent fatigue strength. Therefore, the present inventors have investigated the cause of the decrease in fatigue strength and the method of increasing the fatigue strength in the austenitic stainless steel foil having the above-mentioned chemical composition. As a result, the following findings were obtained.
  • Non-uniform strain means that the lattice strain in the crystal is randomly distributed, and the factor thereof is typified by dislocation. That is, in the microstructure of austenitic stainless steel foil, the larger the non-uniform strain, the higher the dislocation density may be.
  • dislocation density in the steel material is increased, the strength of the steel material is increased by the dislocation strengthening. If the strength of the steel material is increased, the fatigue limit of the steel material is increased, and when stress is repeatedly applied, the number of repetitions until fracture may increase. That is, if the dislocation density of the steel material is increased, the strength of the steel material may be increased by the dislocation strengthening, and the fatigue strength of the steel material may be increased.
  • the present inventors have investigated and investigated in detail the relationship between the non-uniform strain and the fatigue strength in the austenitic stainless steel foil having the above-mentioned chemical composition.
  • the larger the random lattice strain (non-uniform strain) the broader the peak shape of the ⁇ 111 ⁇ plane in the X-ray diffraction profile. Therefore, the present inventors considered that the half width of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile can be used as an index of non-uniform strain. This point will be described in detail with reference to the drawings.
  • FIG. 1 is a diagram showing the relationship between the half width Fw of the peak of the ⁇ 111 ⁇ plane and the number of fatigues in the X-ray diffraction profile of the CuK ⁇ ray of this embodiment.
  • FIG. 1 shows the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray, which is an index of non-uniform strain, and the index of fatigue strength in the austenitic stainless steel foil having the above-mentioned chemical composition. It was created using the number of fatigues.
  • the half-value width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ rays and the number of fatigues were determined by the method described later.
  • the half width Fw in the relationship between the half width Fw of the peak of the ⁇ 111 ⁇ plane and the number of fatigues in the X-ray diffraction profile by CuK ⁇ ray. There is an inflection in the vicinity of 0.366 °. Then, it can be confirmed that if the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray exceeds 0.366 °, the number of fatigues of the steel material is remarkably increased.
  • the austenitic stainless steel foil according to the present embodiment has the above-mentioned chemical composition, and further increases the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray to be larger than 0.366 °. As a result, the austenitic stainless steel foil according to the present embodiment has excellent fatigue strength.
  • the gist of the austenitic stainless steel foil according to this embodiment completed based on the above findings is as follows.
  • the austenitic stainless steel foil of [1] has excellent fatigue strength.
  • the austenitic stainless steel foil of [3] or [4] has even better fatigue strength.
  • the austenitic stainless steel foil of [5] also has excellent durability against bending stress.
  • excellent durability against bending stress means that permanent deformation is unlikely to occur even when repeated bending stress is applied.
  • the chemical composition of the austenitic stainless steel foil according to this embodiment contains the following elements.
  • C 0.150% or less Carbon (C) is inevitably contained. That is, the lower limit of the C content is more than 0%. C forms carbides to increase the strength of the steel material. However, if the C content is too high, even if the content of other elements is within the range of the present embodiment, carbides are deposited at the grain boundaries, and the precipitation amount of the intermetallic compound at the grain boundaries is reduced. , The stability of the grain boundaries is reduced. If the C content is too high, carbides are further precipitated, and the toughness of the steel material is lowered. Therefore, the C content is 0.150% or less. The preferred upper limit of the C content is 0.140%, more preferably 0.130%, still more preferably 0.120%. Here, the extreme reduction of the C content greatly increases the manufacturing cost. Therefore, when industrial production is taken into consideration, the preferable lower limit of the C content is 0.001%, and more preferably 0.005%.
  • Si Silicon
  • the lower limit of the Si content is more than 0%. Si deoxidizes steel. However, if the Si content is too high, coarse oxides remain in the steel material and the hot workability of the steel material deteriorates even if the content of other elements is within the range of the present embodiment. Therefore, the Si content is 1.00% or less.
  • the upper limit of the Si content is preferably 0.95%, more preferably 0.90%, still more preferably 0.80%.
  • the extreme reduction of the Si content greatly increases the manufacturing cost. Therefore, when industrial production is taken into consideration, the preferable lower limit of the Si content is 0.01%, and more preferably 0.05%.
  • Mn 2.00% or less Manganese (Mn) is inevitably contained. That is, the lower limit of the Mn content is more than 0%. Mn deoxidizes steel. Mn further stabilizes the austenite phase. Mn further fixes S in the steel material as a sulfide to improve the hot workability of the steel material. However, if the Mn content is too high, even if the content of other elements is within the range of the present embodiment, the formation of a spinel-type oxide film is promoted, and the oxidation resistance of the steel material at high temperatures is lowered. If the Mn content is too high, further, the work-induced martensitic transformation caused by cold working may not be sufficiently obtained.
  • the Mn content is 2.00% or less.
  • the preferred upper limit of the Mn content is 1.90%, more preferably 1.80%, still more preferably 1.70%.
  • the preferable lower limit of the Mn content for effectively obtaining the above effect is 0.30%, and more preferably 0.50%.
  • P 0.045% or less Phosphorus (P) is an impurity. That is, the lower limit of the P content is more than 0%. If the P content is too high, even if the content of other elements is within the range of this embodiment, the grain boundaries are embrittled and the stress relaxation crack sensitivity of the steel material is increased. Therefore, the P content is 0.045% or less.
  • the preferred upper limit of the P content is 0.040%, more preferably 0.035%. It is preferable that the P content is as low as possible. However, an extreme reduction in P content significantly increases manufacturing costs. Therefore, when industrial production is taken into consideration, the preferable lower limit of the P content is 0.001%, and more preferably 0.003%.
  • S 0.0300% or less Sulfur (S) is an impurity. That is, the lower limit of the S content is more than 0%. If the S content is too high, even if the content of other elements is within the range of the present embodiment, S segregates at the grain boundaries and the stress relaxation crack sensitivity of the steel material increases. Therefore, the S content is 0.0300% or less.
  • the preferred upper limit of the S content is 0.0200%, more preferably 0.0150%, still more preferably 0.0100%. It is preferable that the S content is as low as possible. However, an extreme reduction in S content significantly increases manufacturing costs. Therefore, when industrial production is taken into consideration, the preferable lower limit of the S content is 0.0001%, and more preferably 0.0003%.
  • Chromium (Cr) enhances corrosion resistance such as oxidation resistance, steam oxidation resistance, and high temperature corrosion resistance of steel materials. Cr further forms carbides to increase the strength of the steel material and increase the interplanar spacing of the austenite phase. If the Cr content is too low, the above effect cannot be sufficiently obtained even if the content of other elements is within the range of the present embodiment. If the Cr content is too low, further, processing-induced martensitic transformation may be excessively generated by cold working, and an austenite phase may not be sufficiently obtained.
  • the Cr content is 16.00 to 20.00%.
  • the lower limit of the Cr content is preferably 16.05%, more preferably 16.10%, still more preferably 16.20%.
  • the preferred upper limit of the Cr content is 19.95%, more preferably 19.90%, still more preferably 19.80%.
  • Ni 6.00 to 10.50%
  • Nickel (Ni) stabilizes austenite. Ni further enhances the ductility of steel materials. If the Ni content is too low, 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 is too high, even if the content of other elements is within the range of the present embodiment, the deformation resistance in the grains increases and the ductility of the steel material decreases. If the Ni content is too high, further, the work-induced martensitic transformation caused by cold working may not be sufficiently obtained. Therefore, the Ni content is 6.00 to 10.50%.
  • the lower limit of the Ni content is preferably 6.10%, more preferably 6.20%, still more preferably 6.30%.
  • the preferred upper limit of the Ni content is 10.40%, more preferably 10.20%, still more preferably 10.00%.
  • N 0.100% or less Nitrogen (N) is inevitably contained. That is, the N content is more than 0%. N dissolves in the steel material to increase the strength of the steel material. N further stabilizes the austenite phase. On the other hand, if the N content is too high, the strength of the steel material becomes too high and the ductility of the steel material decreases even if the content of other elements is within the range of the present embodiment. If the N content is too high, further, the work-induced martensitic transformation caused by cold working may not be sufficiently obtained. Therefore, the N content is 0.100% or less.
  • the preferable lower limit of the N content for effectively obtaining the above effect is 0.001%, more preferably 0.005%, still more preferably 0.010%.
  • the preferred upper limit of the N content is 0.090%, more preferably 0.080%, still more preferably 0.060%.
  • the balance of the chemical composition of the austenitic stainless steel foil 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 austenitic stainless steel foil is industrially manufactured, and the austenitic stainless steel foil of the present embodiment is mixed. It means something that is acceptable as long as it does not adversely affect.
  • the austenitic stainless steel foil according to the present embodiment may further contain one or more elements selected from the group consisting of Mo, Nb, V, Ta, Hf, and Co, instead of a part of Fe. All of these elements are optional elements and increase the strength of steel materials.
  • Mo Molybdenum
  • Mo is an optional element and may not be contained. That is, the Mo content may be 0%. When contained, Mo dissolves in the steel material to increase the strength of the steel material. In this case, Mo further forms carbides in the steel to increase the strength of the steel. If Mo is contained even in a small amount, the above effect can be obtained to some extent. However, if the Mo content is too high, the strength of the steel material becomes too high and the hot workability of the steel material deteriorates even if the content of other elements is within the range of the present embodiment. Therefore, the Mo content is 0 to 2.50%.
  • the lower limit of the Mo content is more than 0%, more preferably 0.01%, still more preferably 0.05%, still more preferably 0.10%.
  • the preferred upper limit of the Mo content is 2.20%, more preferably 2.00%, still more preferably 1.70%.
  • Niobium (Nb) is an optional element and may not be contained. That is, the Nb content may be 0%. When contained, Nb refines the crystal grains of the steel material and enhances the corrosion resistance of the steel material. If even a small amount of Nb is contained, the above effect can be obtained to some extent. However, if the Nb content is too high, coarse carbides are formed even if the content of other elements is within the range of the present embodiment, and the strength, ductility, and hot workability of the steel material are lowered. Therefore, the Nb content is 0 to 0.12%.
  • the preferred lower limit of the Nb content is more than 0%, more preferably 0.01%, still more preferably 0.02%.
  • the preferred upper limit of the Nb content is 0.10%, more preferably 0.09%.
  • 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 forms carbonitrides and / or intermetallic compounds, increasing the strength of the steel. In this case, the crystal grains of the steel material are further refined. If V is contained even in a small amount, the above effect can be obtained to some extent. However, if the V content is too high, the ductility and toughness of the steel material will decrease due to the occurrence of high-temperature corrosion and the precipitation of the embrittled phase, even if the content of other elements is within the range of this embodiment. Therefore, the V content is 0 to 1.00%.
  • the lower limit of the V content is preferably more than 0%, more preferably 0.01%, still more preferably 0.03%.
  • the preferred upper limit of the V content is 0.90%, more preferably 0.80%.
  • Tantalum (Ta) is an optional element and may not be contained. That is, the Ta content may be 0%. When contained, Ta enhances grain boundaries and increases the strength of the steel. If even a small amount of Ta is contained, the above effect can be obtained to some extent. However, if the Ta content is too high, the hot workability is lowered even if the content of other elements is within the range of the present embodiment. Therefore, the Ta content is 0 to 0.50%.
  • the preferred lower limit of the Ta content is more than 0%, more preferably 0.01%, still more preferably 0.03%.
  • the preferred upper limit of the Ta content is 0.45%, more preferably 0.40%.
  • 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 enhances grain boundaries and increases the strength of the steel. If even a small amount of Hf is contained, the above effect can be obtained to some extent. However, if the Hf content is too high, the hot workability is lowered even if the content of other elements is within the range of the present embodiment. Therefore, the Hf content is 0 to 0.10%.
  • the lower limit of the Hf content is more than 0%, more preferably 0.01%, still more preferably 0.03%.
  • the preferred upper limit of the Hf content is 0.09%, more preferably 0.08%.
  • Co is an optional element and may not be contained. That is, the Co content may be 0%. When contained, Co dissolves in the steel material to increase the strength of the steel material. If even a small amount of Co is contained, the above effect can be obtained to some extent. However, if the Co content is too high, the strength of the steel material becomes too high and the hot workability of the steel material deteriorates even if the content of other elements is within the range of the present embodiment. Therefore, the Co content is 0 to 0.50%.
  • the lower limit of the Co content is preferably more than 0%, more preferably 0.01%, still more preferably 0.05%.
  • the preferred upper limit of the Co content is 0.45%, more preferably 0.40%.
  • the austenitic stainless steel foil according to the present embodiment may further contain one or more elements selected from the group consisting of B, Ca, Mg, and rare earth elements instead of a part of Fe. All of these elements are optional elements and enhance the hot workability of steel materials.
  • B 0 to 0.0100%
  • Boron (B) is an optional element and may not be contained. That is, the B content may be 0%. When contained, B suppresses the precipitation of carbides and enhances the high temperature toughness of the steel material by the effect of refining the precipitates. If B is contained even in a small amount, the above effect can be obtained to some extent. However, if the B content is too high, boron nitride (BN) will be formed and the toughness of the steel material will be reduced even if the content of other elements is within the range of this embodiment. Therefore, the B content is 0 to 0.0100%.
  • the lower limit of the B content is more than 0%, more preferably 0.0001%, still more preferably 0.0005%, still more preferably 0.0010%.
  • the preferred upper limit of the B content is 0.0080%, more preferably 0.0070%, still more preferably 0.0050%.
  • 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 S in the steel material as a sulfide to enhance the hot workability of the steel material. If even a small amount of Ca is contained, the above effect can be obtained to some extent. However, if the Ca content is too high, coarse oxides are formed even if the content of other elements is within the range of the present embodiment, and the hot workability and ductility of the steel material are lowered. Therefore, the Ca content is 0 to 0.0200%.
  • the lower limit of the Ca content is more than 0%, more preferably 0.0001%, still more preferably 0.0003%.
  • the preferred upper limit of the Ca content is 0.0180%, more preferably 0.0150%.
  • Mg 0-0.0200%
  • Mg Magnesium (Mg) is an optional element and may not be contained. That is, the Mg content may be 0%. When contained, Mg fixes S in the steel material as a sulfide to improve the hot workability of the steel material. If even a small amount of Mg is contained, the above effect can be obtained to some extent. However, if the Mg content is too high, coarse oxides are formed even if the content of other elements is within the range of the present embodiment, and the hot workability and ductility of the steel material are deteriorated. Therefore, the Mg content is 0 to 0.0200%.
  • the lower limit of the Mg content is more than 0%, more preferably 0.0001%, still more preferably 0.0003%.
  • the preferred upper limit of the Mg content is 0.0180%, more preferably 0.0150%.
  • Rare earth elements are optional elements and may not be contained. That is, the REM content may be 0%.
  • REM fixes S in the steel material as a sulfide to enhance the hot workability of the steel material.
  • REM further enhances the adhesion of the Cr 2 O 3 protective film on the surface of the steel material and enhances the oxidation resistance of the steel material.
  • REM further strengthens the grain boundaries to increase the strength and breaking strain of the steel. If even a small amount of REM is contained, the above effect can be obtained to some extent. However, if the REM content is too high, even if the content of other elements is within the range of the present embodiment, a coarse oxide is formed and the hot workability of the steel material is lowered.
  • the REM content is 0 to 0.0100%.
  • the preferred lower limit of the REM content is more than 0%, more preferably 0.0001%, still more preferably 0.0003%.
  • the preferred upper limit of the REM content is 0.0090%, more preferably 0.0080%.
  • the REM in the present specification refers to scandium (Sc) having an atomic number of 21, yttrium (Y) having an atomic number of 39, and lanthanum (La) having an atomic number of 57 to 71, which is a lanthanoid.
  • Sc scandium
  • Y yttrium
  • La lanthanum
  • the REM content in the present specification is the total content of these elements.
  • the austenitic stainless steel foil according to the present embodiment may further contain one or more elements selected from the group consisting of Al, Ti, and Zr instead of a part of Fe. All of these elements are optional elements and deoxidize steel materials.
  • Al 0 to 0.010%
  • 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. If Al is contained even in a small amount, the above effect can be obtained to some extent. However, if the Al content is too high, coarse inclusions are formed and the fatigue strength of the steel material is lowered even if the content of other elements is within the range of the present embodiment. Therefore, the Al content is 0 to 0.010%.
  • the lower limit of the Al content is more than 0%, more preferably 0.001%, still more preferably 0.002%.
  • the preferred upper limit of the Al content is 0.009%, more preferably 0.008%.
  • Titanium (Ti) is an optional element and may not be contained. That is, the Ti content may be 0%. When contained, Ti deoxidizes the steel. If even a small amount of Ti is contained, the above effect can be obtained to some extent. However, if the Ti content is too high, coarse inclusions are formed and the hot workability of the steel material is lowered even if the content of other elements is within the range of the present embodiment. Therefore, the Ti content is 0 to 0.500%.
  • the lower limit of the Ti content is more than 0%, more preferably 0.001%, still more preferably 0.002%.
  • the preferred upper limit of the Ti content is 0.450%, more preferably 0.400%.
  • Zr Zirconium
  • Zr Zirconium
  • the Zr content may be 0%. If contained, Zr deoxidizes the steel. If even a small amount of Zr is contained, the above effect can be obtained to some extent. However, if the Zr content is too high, the toughness and hot workability of the steel material will decrease even if the content of other elements is within the range of this embodiment. Therefore, the Zr content is 0 to 0.100%.
  • the preferable lower limit of the Zr content is more than 0%, more preferably 0.001%, still more preferably 0.002%.
  • the preferred upper limit of the Zr content is 0.090%, more preferably 0.080%.
  • the austenitic stainless steel foil according to the present embodiment may further contain Cu instead of a part of Fe.
  • Cu 0 to 3.00% Copper (Cu) is an optional element and may not be contained. That is, the Cu content may be 0%. When contained, Cu enhances the corrosion resistance and oxidation resistance of the steel material. If even a small amount of Cu is contained, the above effect can be obtained to some extent. However, if the Cu content is too high, even if the content of other elements is within the range of the present embodiment, grain boundary embrittlement at high temperature is promoted and the hot workability of the steel material is lowered. Therefore, the Cu content is 0 to 3.00%.
  • 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%.
  • the preferred upper limit of the Cu content is 2.20%, more preferably 2.00%, still more preferably 1.70%.
  • the chemical composition of the austenitic stainless steel foil according to this embodiment can be measured by a well-known component analysis method. Specifically, chips are collected from austenitic stainless steel foil. The collected chips are dissolved in acid to obtain a solution. ICP-AES (Inductively Coupled Plasma Atomic Emission Spectroscopy) is performed on the solution to perform elemental analysis of the chemical composition. The 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 Inert Gas Melting-Thermal Conductivity Method.
  • ICP-AES Inductively Coupled Plasma Atomic Emission Spectroscopy
  • each element content is a numerical value obtained by rounding off the fraction of the element content specified in this embodiment (the number one digit below the minimum digit).
  • the C content is a numerical value up to the third decimal place obtained by rounding off the fourth decimal place of the value obtained by the above method.
  • the elemental content other than the C content is also the value obtained by rounding off the fraction of the elemental content specified in the present embodiment with respect to the value obtained by the above method.
  • the element content means rounding down if the fraction is 4 or less, and rounding up if the fraction is 5 or more.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is larger than 0.366 °.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile corresponds to a random lattice strain typified by dislocation.
  • the larger the half-value width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray the larger the non-uniform strain.
  • the cause of the non-uniform strain which is a random lattice strain, is typified by dislocations. That is, the higher the dislocation density, the higher the strength of the steel material due to the dislocation strengthening, and the higher the fatigue strength may be.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray exceeds 0.366 °, the number of fatigues of the steel material is remarkably increased.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is made larger than 0.366 °.
  • the austenitic stainless steel foil according to the present embodiment has excellent fatigue strength.
  • the preferable lower limit of the half width Fw of the peak of the ⁇ 111 ⁇ plane of the austenitic stainless steel foil is 0.368 °, more preferably 0.370 °, still more preferably 0.380 °. It is more preferably 0.390 °, still more preferably 0.400 °, still more preferably 0.410 °, still more preferably 0.420 °, still more preferably 0.430 °. Yes, more preferably 0.440 °.
  • the upper limit of the half width Fw of the peak of the ⁇ 111 ⁇ plane of the austenitic stainless steel foil is not particularly limited, but is, for example, 0.600 °.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane can be obtained by the following method.
  • a test piece is prepared from the austenitic stainless steel foil according to the present embodiment.
  • the size of the test piece is not particularly limited, and the thickness of the test piece is the same as the thickness of the steel foil.
  • the observation surface (surface of the steel foil) of the test piece is measured by X-ray diffraction method (XRD) to obtain a diffraction profile.
  • XRD X-ray diffraction method
  • the radiation source is CuK ⁇ ray
  • the tube voltage is 45 kV
  • the tube current is 200 mA.
  • the diffraction angle (2 ⁇ ) was measured in the range of 40 to 50 degrees, the pitch was 0.01 degrees, and the pitch was 1 ° / min by the concentration method.
  • the peak of the ⁇ 111 ⁇ plane can be specified from the obtained diffraction profile, and the half width Fw can be obtained.
  • the uniform strain is not particularly limited. However, in the austenitic stainless steel foil according to the present embodiment, the uniform strain e may be less than -2.89 ⁇ 10 -4 .
  • the "uniform strain” means a lattice strain accompanied by a change in the surface spacing. More specifically, as used herein, the term “uniform strain” means the uniform strain of the (111) plane. The smaller the uniform strain e, the more the unit cell is distorted toward microscopic compression. On the other hand, the larger the uniform strain e, the more the unit cell is distorted toward the microscopic pull.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane has a correlation with the non-uniform strain typified by the dislocation density. That is, the austenitic stainless steel foil according to the present embodiment in which the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is made larger than 0.366 ° may have an increased dislocation density. On the other hand, in the microstructure in steel materials to which repeated stress is applied, dislocations may move and accumulate, which may be the starting point of cracks.
  • the austenitic stainless steel foil according to the present embodiment tends to have a high dislocation density, there is a possibility that a decrease in fatigue strength due to the accumulation of dislocations becomes apparent. Therefore, in the present embodiment, it is preferable to reduce the uniform strain e to less than -2.89 ⁇ 10 -4 . If the uniform strain is reduced, the growth of cracks can be suppressed even if cracks are generated due to the accumulation of dislocations.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is made larger than 0.366 °, and the uniform strain e is further set to -2. It is preferably less than .89 ⁇ 10 -4 .
  • the austenitic stainless steel foil according to the present embodiment has further excellent fatigue strength.
  • the more preferable upper limit of the uniform strain e of the austenitic stainless steel foil is -2.90 ⁇ 10 -4 , more preferably -3.50 ⁇ 10 -4 , and further preferably -3.
  • the lower limit of the uniform strain e of the austenitic stainless steel foil is not particularly limited, but is, for example, ⁇ 37.20 ⁇ 10 -4 .
  • the uniform strain e can be obtained by the following method.
  • a diffraction profile is obtained by X-ray diffraction (XRD), similar to the method for measuring non-uniform strain described above.
  • XRD X-ray diffraction
  • a test piece is produced from the austenitic stainless steel foil according to the present embodiment.
  • the size of the test piece is not particularly limited, and the thickness of the test piece is the same as the thickness of the steel foil.
  • the observation surface (surface of the steel foil) of the test piece is measured by XRD to obtain a diffraction profile.
  • the radiation source is CuK ⁇ ray
  • the tube voltage is 45 kV
  • the tube current is 200 mA.
  • the diffraction angle (2 ⁇ ) is set in the range of 40 to 50 degrees
  • the pitch is 0.01 degrees
  • the measurement is performed by the concentration method.
  • the peak of the (111) plane is specified, and the lattice plane spacing d ( ⁇ ) is obtained.
  • the lattice plane spacing d ( ⁇ ) can be obtained by using the peak position (2 ⁇ ) of the (111) plane and Bragg's equation (formula (A)).
  • d ⁇ / 2sin ⁇ (A)
  • the wavelength of the X-ray is substituted by ⁇ for ⁇ in the equation (A)
  • the value obtained by dividing the peak position of the (111) plane by 2 is substituted for ⁇ .
  • the uniform strain e can be obtained by using the lattice plane spacing d ( ⁇ ) of the obtained (111) plane and the following equation (B).
  • e (d ⁇ d 0 ) / d 0 (B)
  • the lattice spacing is assigned by ⁇ to d in the equation (B)
  • the lattice spacing of the (111) plane in the case of tempering is substituted by ⁇ in d 0 .
  • a measured value of 2.0782 ⁇ is used as d 0 .
  • the austenitic stainless steel foil to which the bending stress is repeatedly applied has not only excellent fatigue strength but also excellent durability against bending stress.
  • excellent durability against bending stress means that permanent deformation is unlikely to occur even when repeated bending stress is applied. If the durability against bending stress is high, the shape can be maintained even if the bending stress is repeatedly applied.
  • the austenitic stainless steel foil has a foil strip shape with a thickness of 100 ⁇ m or less and is very thin.
  • cold working is carried out with a high degree of processing as described by a preferable manufacturing method described later.
  • work-induced martensitic transformation occurs in the manufactured steel foil.
  • the microstructure of the austenitic stainless steel foil having the above-mentioned chemical composition includes not only the austenitic phase but also the martensite phase.
  • the strain at the interface between the austenite phase and the martensite phase is related to the durability against repeated bending stress.
  • the ratio of the surface spacing ⁇ 111 ⁇ ⁇ of the ⁇ 111 ⁇ planes of the austenite phase to the plane spacing ⁇ 110 ⁇ ⁇ 'of the ⁇ 110 ⁇ planes of the martensite phase is the bending stress. It was revealed that it is involved in durability against. This point will be described in detail with reference to the drawings.
  • the bending habit means permanent deformation remaining in the bending direction of the steel foil when repeated bending stress is applied. That is, the smaller the bending habit angle, the higher the durability against repeated bending stress.
  • FIG. 2 is an example of an austenitic stainless steel foil according to the present embodiment, obtained by using Fn1 obtained by the method described later and a bending habit angle (°) obtained by the method described later.
  • Fn1 obtained by the method described later
  • a bending habit angle (°) obtained by the method described later.
  • the austenitic stainless steel foil according to the present embodiment has the above-mentioned chemical composition, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is larger than 0.366 °, and further, Fn1 Is preferably 1.0220 or more.
  • the austenitic stainless steel foil according to the present embodiment has excellent fatigue strength and also has excellent durability against repeated bending stress.
  • the present inventors speculate on this reason as follows. Repeated bending stresses introduce dislocations into the austenitic stainless steel foil. The movement of dislocations in a crystal may cause plastic deformation represented by shear deformation. On the other hand, when the ratio of the surface spacing of the ⁇ 111 ⁇ planes of the austenite phase to the face spacing of the ⁇ 110 ⁇ planes of the martensite phase is increased, the strain at the interface between the austenite phase and the martensite phase becomes large, and the strain at the interface becomes large. The movement of dislocations is suppressed. In this way, the movement of dislocations is hindered, so that plastic deformation is less likely to occur. As a result, the present inventors speculate that the durability of the austenitic stainless steel foil is increased.
  • the lower limit of Fn1 is 1.0221, more preferably 1.0222, still more preferably 1.0223, still more preferably 1.0224, and even more preferably 1.0225. It is more preferably 1.0226.
  • the preferable upper limit of Fn1 is not particularly limited, and is, for example, 1.0230.
  • Fn1 can be obtained by the following method.
  • a test piece is produced from the austenitic stainless steel foil according to the present embodiment.
  • the size of the test piece is not particularly limited, and the thickness of the test piece is the same as the thickness of the steel foil.
  • the observation surface (surface of the steel foil) of the test piece is measured by X-ray diffraction method (XRD) to obtain a diffraction profile.
  • XRD X-ray diffraction method
  • the radiation source is CuK ⁇ ray
  • the tube voltage is 40 kV
  • the tube current is 40 mA.
  • the diffraction angle (2 ⁇ ) is set to a range of 40 to 50 degrees
  • the pitch is 0.01 degrees and 1 ° / min.
  • the concentration method is used as the measurement method.
  • the peaks of the ⁇ 111 ⁇ plane of the austenite phase and the ⁇ 110 ⁇ plane of the martensite phase are specified.
  • the lattice spacing between the ⁇ 111 ⁇ plane of the austenite phase and the ⁇ 110 ⁇ plane of the martensite phase Each d ( ⁇ ) can be obtained.
  • d ⁇ / 2sin ⁇ (A)
  • the wavelength of the X-ray is substituted by ⁇ for ⁇ in the equation (A), and the value obtained by dividing the position of each peak by 2 is substituted for ⁇ .
  • Fn1 can be obtained from the surface spacing of the ⁇ 111 ⁇ plane of the obtained austenite phase and the ⁇ 110 ⁇ plane of the martensite phase and the formula (1). In this embodiment, it is sufficient if Fn1 is 1.0220 or more, and the austenite phase ⁇ 111 ⁇ plane spacing ⁇ 111 ⁇ ⁇ and the martensite phase ⁇ 110 ⁇ plane spacing ⁇ 110 ⁇ ⁇ ′. Is not particularly limited.
  • the interplanar spacing ⁇ 111 ⁇ ⁇ of the ⁇ 111 ⁇ planes of the austenite phase is, for example, 2.0730 to 2.0760 ⁇ .
  • the interplanar spacing ⁇ 110 ⁇ ⁇ 'of the ⁇ 110 ⁇ planes of the martensite phase is, for example, 2.0250 to 2.0350 ⁇ .
  • the term "steel foil” as used herein means a steel sheet having a thickness of 100 ⁇ m or less. Therefore, the austenitic stainless steel foil according to the present embodiment has a foil strip shape having a thickness of 100 ⁇ m or less and is very thin. In short, the thickness of the austenitic stainless steel foil according to the present embodiment is 100 ⁇ m or less. Preferably, the thickness of the austenitic stainless steel foil according to the present embodiment is about 10 to 100 ⁇ m. In this case, it is suitable as an electronic device material that requires high fatigue strength.
  • the austenitic stainless steel foil according to the present embodiment has the above-mentioned chemical composition, and the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is larger than 0.366 °.
  • the austenitic stainless steel foil according to the present embodiment has excellent fatigue strength.
  • the excellent fatigue strength is defined as follows.
  • a test piece is produced from the austenitic stainless steel foil according to the present embodiment.
  • the size of the test piece is, for example, 110 mm in the rolling direction of the steel foil, 100 mm in the width direction of the steel foil, and the same thickness as the thickness of the steel foil.
  • the prepared test piece is repeatedly subjected to bending stress by a general-purpose repetitive bending tester until the test piece breaks.
  • the direction in which the bending stress is applied is the direction perpendicular to the rolling direction of the steel foil.
  • the bending period is 1.25 Hz
  • the bending radius is 2 mm
  • the bending angle is 0 to 125 °.
  • the number of repeated bends until fracture is defined as the number of fatigues. When the number of fatigues according to the above definition is 4.5 ⁇ 10 4 times or more, it is judged to have excellent fatigue strength.
  • the austenitic stainless steel foil according to the present embodiment has the above-mentioned chemical composition, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is larger than 0.366 °, and the uniform strain e. Is preferably less than -2.89 ⁇ 10 -4 .
  • the austenitic stainless steel foil according to the present embodiment has further excellent fatigue strength.
  • the excellent fatigue strength is defined as follows.
  • excellent durability is defined as follows.
  • a test piece is produced from the austenitic stainless steel foil according to the present embodiment.
  • the size of the test piece is, for example, 110 mm in the rolling direction of the steel foil, 100 mm in the width direction of the steel foil, and the same thickness as the thickness of the steel foil.
  • Repeated bending stress is applied to the produced test piece by a general-purpose repeated bending tester.
  • the direction in which the bending stress is applied is the direction perpendicular to the rolling direction of the steel foil.
  • the bending period is 1.25 Hz
  • the bending radius is 2.5 mm
  • the bending angle is 0 to 125 °.
  • the number of times of repeated bending stress is 20000 times (20,000 times).
  • the bending habit angle of the test piece to which the repeated bending stress of 20,000 times is applied is defined as follows.
  • the test piece before the repeated bending stress application test is a straight line when viewed from the side.
  • FIG. 3 is a schematic diagram for explaining a method of measuring the bending habit angle shown in FIG. 2. As shown in FIG. 3, in the side view of the test piece 10, the angle 100 formed by the bent portion of the test piece 10 after the test and the straight line L is defined as a bending habit angle.
  • the bending habit angle is measured by the following method.
  • the test piece 10 after the test is placed upright on a horizontal plate and allowed to stand still. After standing still, measure the bending habit angle.
  • both ends of the test piece 10 may be sandwiched between plate members to make it easier to stand still so that the test piece does not deform. It is judged that the austenitic stainless steel foil according to the present embodiment has excellent durability against bending stress when the bending habit angle defined as described above is 6.0 ° or less.
  • An example of the method for producing an austenitic stainless steel foil according to the present embodiment includes an intermediate steel material preparation step, a first cold rolling step, a bright annealing step, a second cold rolling step, and a tension annealing step.
  • the first cold rolling step and the bright annealing step may be repeated a plurality of times.
  • an intermediate steel material having the above-mentioned chemical composition is prepared.
  • the intermediate steel material is an intermediate product for producing an austenitic stainless steel foil according to the present embodiment, and means a steel sheet having a thickness of several hundred ⁇ m to several mm.
  • the intermediate steel material is, for example, a cold-rolled coil obtained by cold-rolling a hot-rolled coil.
  • the intermediate steel material may be manufactured and prepared, or may be prepared by purchasing from a third party. That is, the process of preparing the intermediate steel material is not particularly limited.
  • a molten steel having the above-mentioned chemical composition is produced.
  • a slab (slab, bloom, or billet) is produced by a continuous casting method using molten steel.
  • a steel ingot may be produced by an ingot method using molten steel. If necessary, slabs, blooms or ingots may be lump-rolled to produce billets.
  • the manufactured slabs or ingots are hot-worked to produce steel sheets with a thickness of several hundred ⁇ m to several mm.
  • the method of hot working is not particularly limited, and a well-known method may be used. Hot working is, for example, hot rolling.
  • Hot rolling is, for example, hot rolling.
  • the intermediate steel material is manufactured by hot rolling, for example, it can be manufactured by the following method.
  • the conditions for hot rolling are not particularly limited, and well-known conditions may be appropriately set. If necessary, cold rolling and annealing may be repeated on the hot-rolled intermediate steel material. If necessary, skin pass rolling may be further performed on the hot-rolled intermediate steel material. If necessary, the hot-rolled intermediate steel material may be further annealed. By the above steps, the intermediate steel material according to the present embodiment is prepared.
  • first cold rolling process cold rolling is carried out on the intermediate steel material prepared in the intermediate steel material preparation step.
  • the cold rolling in the first cold rolling can be carried out by using a well-known device.
  • a continuous rolling mill equipped with a plurality of cold rolling stands may be used.
  • the preferable cold rolling ratio CR1 is 45% or more.
  • the cold rolling ratio CR1 (%) means the reduction rate (%) of the thickness of the intermediate steel material from before the start of the first cold rolling process to after the end of the first cold rolling process. .. That is, the cold rolling ratio CR1 in the first cold rolling step is defined by the following formula (C).
  • CR1 (%) 100- (thickness of intermediate steel material after first cold rolling process) / (thickness of intermediate steel material before first cold rolling process) x 100 (C)
  • the cold rolling ratio CR1 in the first cold rolling process is too low, the dislocations introduced in the microstructure of the intermediate steel material will decrease. As a result, in the manufactured austenitic stainless steel foil, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray may not be sufficiently increased. If the cold rolling ratio CR1 is too low, the compressive strain applied in the crystal lattice of the intermediate steel material becomes smaller. As a result, the uniform strain e of the produced austenitic stainless steel foil may not be sufficiently reduced. If the cold rolling ratio CR1 is too low, the strain applied to the austenite phase becomes smaller. As a result, in the produced austenitic stainless steel foil, Fn1 may not be sufficiently increased.
  • the cold rolling ratio CR1 is preferably 45% or more.
  • a further preferable lower limit of the cold rolling ratio CR1 in the first cold rolling step is 47%, still more preferably 50%.
  • the upper limit of the cold rolling ratio CR1 in the first cold rolling step is not particularly limited, but is, for example, 75%.
  • the bright annealing treatment is carried out on the intermediate steel material cold-rolled in the first cold rolling step.
  • the bright annealing treatment means an annealing treatment in an extremely low oxygen atmosphere. Since the atmosphere is extremely low oxygen, the surface of the intermediate steel material that has been subjected to the bright annealing treatment is hardly oxidized, and the surface gloss can be maintained.
  • the preferable annealing temperature in the bright annealing step is 900 to 1200 ° C. If the annealing temperature is too low, the constituent elements are unevenly distributed and recrystallization does not occur, resulting in an inhomogeneous structure. As a result, in the manufactured austenitic stainless steel foil, the half width Fw of the ⁇ 111 ⁇ plane may decrease, and the fatigue strength may decrease. If the annealing temperature is too low, the constituent elements are unevenly distributed and recrystallization does not occur, resulting in an inhomogeneous structure. As a result, the uniform strain e of the produced austenitic stainless steel foil may not be sufficiently reduced.
  • the annealing temperature is preferably 900 to 1200 ° C.
  • the lower limit of the more preferable annealing temperature in the bright annealing step is 920 ° C.
  • the upper limit of the more preferable annealing temperature in the bright annealing step is 1180 ° C.
  • the preferable annealing time in the bright annealing step is 5 to 10 seconds. If the annealing time is too short, the inherent stress cannot be sufficiently relieved and the structure becomes inhomogeneous. As a result, in the manufactured austenitic stainless steel foil, the half width Fw of the ⁇ 111 ⁇ plane may decrease, and the fatigue strength may decrease. As a result, the uniform strain e of the produced austenitic stainless steel foil may not be sufficiently reduced.
  • the annealing time is preferably 5 to 10 seconds.
  • the "annealing temperature" of the bright annealing means the temperature (° C.) of the heat treatment furnace for carrying out the annealing treatment.
  • the "annealing time” of the bright annealing means the time (seconds) required for the intermediate steel material to pass through the heat treatment furnace for performing the annealing treatment.
  • the preferred N2 fraction in the atmospheric gas is 35-65% by volume. If the N2 fraction in the atmospheric gas is too low, the manufacturing cost will increase significantly. On the other hand, if the N2 fraction in the atmospheric gas is too high, Cr nitride precipitation may be promoted on the surface layer of the steel material. In this case, Cr nitride remains even in the produced austenitic stainless steel foil. Therefore, in the matrix phase of the austenitic stainless steel foil, the effect of fixing dislocations due to the solid solution Cr decreases as the Cr concentration decreases.
  • the atmospheric gas is a mixed gas of 35 to 65% by volume of N 2 gas and the balance is H 2 gas.
  • the dew point of the atmospheric gas is not particularly limited. However, when an austenitic stainless steel foil having even better fatigue strength is to be obtained, it is preferable that the dew point of the atmospheric gas is less than ⁇ 73 ° C. When the dew point of the atmospheric gas is high, Cr nitrides are likely to precipitate in the intermediate steel material being blunted. As a result, Cr nitride may remain even in the produced austenitic stainless steel foil. In this case, as the Cr concentration of the matrix of the austenitic stainless steel foil decreases, the lattice spacing d 0 may decrease and the uniform strain e may increase.
  • a thick oxide film may be formed on the surface layer of the intermediate steel material. In this case, the appearance quality of the manufactured austenitic stainless steel foil is deteriorated. In this case, further, in the second cold rolling step described later, a surface defect may be formed, which may be a fracture starting point in repeated bending.
  • the dew point of the atmospheric gas is set to less than ⁇ 73 ° C.
  • the precipitation of Cr nitrides can be stably suppressed, and the uniform strain e of the austenitic stainless steel foil can be reduced.
  • the dew point of the atmospheric gas is preferably less than ⁇ 73 ° C.
  • the furnace pressure is not particularly limited in the bright annealing process.
  • the furnace pressure is preferably 100 to 800 Pa.
  • the term "fire pressure” means the difference between the pressure inside the furnace and the atmospheric pressure. That is, "the furnace pressure in the bright annealing step is 100 to 800 Pa” means that the pressure in the furnace in the bright annealing step is 100 to 800 Pa higher than the atmospheric pressure. If the furnace pressure is too low, when the intermediate steel material is introduced into the furnace, the atmosphere is likely to be introduced into the furnace. As a result, the atmosphere in the furnace may change, and the fatigue strength of the produced austenitic stainless steel foil may decrease.
  • the furnace pressure is preferably 100 to 800 Pa in the bright annealing step of the present embodiment.
  • the first cold rolling step and the bright annealing step may be repeated a plurality of times. For example, when the first cold rolling and the bright annealing are repeated twice, the first cold rolling and the first bright annealing are carried out, and then the second first cold rolling is performed. Inter-rolling and a second bright annealing are performed. Even in this case, it is preferable that both the first cold rolling and the bright annealing are carried out under the above-mentioned conditions.
  • the second cold rolling is carried out on the intermediate steel material which has been subjected to the bright annealing treatment in the bright annealing step.
  • the cold rolling in the second cold rolling step can also be carried out using a well-known device in the same manner as the cold rolling in the first cold rolling step.
  • a continuous rolling mill equipped with a plurality of cold rolling stands may be used.
  • the preferable cold rolling ratio CR2 is 45% or more.
  • the cold rolling ratio CR2 (%) means the reduction rate (%) of the thickness of the intermediate steel material from before the start of the second cold rolling process to after the end of the second cold rolling process. .. That is, the cold rolling ratio CR2 in the second cold rolling step is defined by the following formula (D).
  • CR2 (%) 100- (thickness of intermediate steel material after the second cold rolling process) / (thickness of intermediate steel material before the second cold rolling process) x 100 (D)
  • the cold rolling ratio CR2 in the second cold rolling process is too low, the dislocations introduced in the microstructure of the intermediate steel material will decrease. As a result, in the manufactured austenitic stainless steel foil, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray may not be sufficiently increased. If the cold rolling ratio CR2 is too low, the compressive strain applied in the crystal lattice of the intermediate steel material becomes smaller. As a result, the uniform strain e of the produced austenitic stainless steel foil may not be sufficiently reduced. If the cold rolling ratio CR2 is too low, the strain applied to the austenite phase becomes smaller. As a result, in the produced austenitic stainless steel foil, Fn1 may not be sufficiently increased.
  • the cold rolling ratio CR2 is preferably 45% or more.
  • a further preferable lower limit of the cold rolling ratio CR2 in the second cold rolling step is 47%, still more preferably 50%.
  • the upper limit of the cold rolling ratio CR2 in the second cold rolling step is not particularly limited, but is, for example, 75%.
  • tension annealing process tension annealing is performed on the intermediate steel material that has been cold-rolled in the second cold rolling step.
  • Tension annealing means that the annealing treatment is performed while applying tension.
  • the intermediate steel material subjected to tension annealing can maintain the flatness of the intermediate steel material by the tension.
  • the preferred annealing temperature in the tension annealing step is 350 to 850 ° C. If the annealing temperature is too low, sufficient strain aging may not be obtained. On the other hand, if the annealing temperature is too high, the dislocation density introduced is too low in the microstructure of the intermediate steel material. As a result, in the manufactured austenitic stainless steel foil, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray may not be sufficiently increased.
  • the annealing temperature is preferably 350 to 850 ° C.
  • the lower limit of the more preferable annealing temperature in the tension annealing step is 360 ° C.
  • the upper limit of the more preferable annealing temperature in the tension annealing step is 800 ° C.
  • the annealing time is not particularly limited.
  • the annealing time is, for example, 5 to 10 seconds.
  • the "annealing temperature" of the tension annealing means the temperature (° C.) of the heat treatment furnace for performing the annealing treatment.
  • the "annealing time” of the tension annealing means the time (seconds) required for the intermediate steel material to pass through the heat treatment furnace for performing the annealing treatment.
  • the preferred tension in the tension annealing step is 2.0 to 6.0 N / mm 2 . If the tension applied to the intermediate steel material is too low, the flatness of the austenitic stainless steel foil may decrease. On the other hand, if the tension is too high, the dislocation density introduced will be too low. As a result, in the manufactured austenitic stainless steel foil, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray may not be sufficiently increased. Therefore, in the tension annealing step of the present embodiment, the tension applied is preferably 2.0 to 6.0 N / mm 2 . The lower limit of the more preferable tension in the tension annealing step is 3.0 N / mm 2 . The upper limit of the more preferable tension in the tension annealing step is 5.0 N / mm 2 .
  • the intermediate steel material preparation process, the first cold rolling process, the bright annealing process, the second cold rolling process, and the tension annealing process are carried out.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray is strongly influenced by the first cold rolling step, the bright annealing step, and the second cold rolling step.
  • the value changes. That is, the value of the half width Fw of the ⁇ 111 ⁇ plane changes depending on the balance between the first cold rolling step, the bright annealing step, and the second cold rolling step.
  • the conditions of the first cold rolling step, the bright annealing step, and the second cold rolling step satisfy the following formula (2), so that the above-mentioned chemical composition can be obtained.
  • Austenitic stainless steel foil having a half-price width Fw of ⁇ 111 ⁇ plane larger than 0.366 ° can be stably manufactured.
  • Eq1, Eq2, Eq3, Eq4, Eq5, and Eq6 in the formula (2) are defined by the following formulas (3) to (8).
  • the cold rolling ratio in the first cold rolling step is substituted in% for CR1 in the formula (3).
  • the cold rolling ratio in the second cold rolling step is substituted in% for CR2 in the formula (4).
  • the LM in the formulas (5) and (6) is defined by the following formula (9).
  • the annealing temperature in the tension annealing step is substituted at ° C. for T T in the equation (7).
  • the tension in the tension annealing step is substituted into FT in the equation (8) by N / mm 2 .
  • the annealing temperature in the bright annealing step is substituted in ° C. for T in the equation (9), and the annealing time in the bright annealing step is substituted in time for t.
  • FnA is an index of the condition that the half width Fw of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray can be increased in the manufacturing method according to the present embodiment.
  • FnA is 0.80 or less, the ⁇ 111 ⁇ plane larger than 0.366 ° in the above chemical composition and the X-ray diffraction profile by CuK ⁇ ray. It is possible to stably produce an austenitic stainless steel foil having a half-value width of Fw. Therefore, in the production method according to this embodiment, it is preferable that FnA is 0.80 or less.
  • the uniform strain e is strongly influenced by the first cold rolling step, the bright annealing step, and the second cold rolling step, and its value changes. That is, the value of the uniform strain e changes depending on the balance between the first cold rolling step, the bright annealing step, and the second cold rolling step. Therefore, in order to obtain an austenitic stainless steel foil having even better fatigue strength, in addition to the above-mentioned conditions, the conditions of the first cold rolling step, the bright annealing step, and the second cold rolling step. However, it is preferable that the following equation (10) is satisfied.
  • FnB is an index of conditions under which uniform strain is stably reduced in the production method according to the present embodiment.
  • FnB is an index of conditions under which uniform strain is stably reduced in the production method according to the present embodiment.
  • the above chemical composition and the X-ray diffraction profile by CuK ⁇ ray are 0.366 °. It is possible to stably produce an austenitic stainless steel foil having a larger half width Fw of ⁇ 111 ⁇ plane and further having a uniform strain e of less than -2.89 ⁇ 10 -4 . Therefore, in the production method according to the present embodiment, it is preferable that FnB is 0.15 to 1.00.
  • Fn1 is strongly influenced by the first cold rolling step, the bright annealing step, and the second cold rolling step, and its value changes. That is, the value of Fn1 changes depending on the balance between the first cold rolling step, the bright annealing step, and the second cold rolling step. Therefore, in order to obtain an austenitic stainless steel foil having excellent durability, in addition to the above-mentioned conditions, the conditions of the first cold rolling step, the bright annealing step, and the second cold rolling step are required. , It is preferable to satisfy the following formula (12).
  • an austenitic stainless steel having the above-mentioned chemical composition and a half-value width Fw of ⁇ 111 ⁇ plane larger than 0.366 ° in the X-ray diffraction profile by CuK ⁇ ray, and further having Fn1 of 1.0220 or more.
  • the foil can be stably manufactured.
  • Eq1, Eq2, Eq3, Eq4, and Eq5 in the formula (12) are defined by the above formulas (3) to (7).
  • Eq8 in the equation (12) is defined by the following equation (13).
  • the furnace pressure in the bright annealing step is substituted into P in the equation (13) by Pa.
  • FnC The left side of equation (13) is defined as "FnC".
  • FnC is 1.70 or less, half of the ⁇ 111 ⁇ plane larger than 0.366 ° in the above chemical composition and the X-ray diffraction profile by CuK ⁇ ray.
  • FnC is 1.70 or less.
  • the austenitic stainless steel foil according to the present embodiment can be manufactured.
  • the above-mentioned manufacturing method is an example of a method for manufacturing an austenitic stainless steel foil according to the present embodiment. That is, the method for producing an austenitic stainless steel foil according to the present embodiment is not limited to the above-mentioned production method, and may be another production method.
  • the austenitic stainless steel foil according to the present embodiment will be described more specifically by way of examples.
  • the examples described below are examples for confirming the effect of the austenitic stainless steel foil according to the present embodiment, and do not limit the present invention.
  • a slab was produced by continuous casting from molten steel having the chemical composition shown in Table 1.
  • "-" in Table 1 means that it was 0% when the fraction of the numerical value shown in Table 1 was rounded off.
  • Hot rolling and annealing were performed on the steel A to L slabs to manufacture a hot rolling coil with a thickness of 4 mm.
  • Cold rolling and annealing were repeatedly carried out on the produced hot-rolled coils of steels A to L to produce a foil strip-shaped intermediate steel material (cold-rolled coil) having a thickness of 300 ⁇ m.
  • the first cold rolling was carried out under the conditions shown in Table 2 using intermediate steel materials of steels A to L. Specifically, the first cold rolling and bright annealing were repeated for the intermediate steel materials of test numbers 1-1 to 1-21 the number of times shown in Table 2. More specifically, when “once” is described in Table 2, it means that the first cold rolling and the bright annealing were performed once. When “twice” is described in Table 2, it means that the combination of the first cold rolling and the bright annealing was repeated twice.
  • Table 2 shows the cold rolling ratio CR1 (%) of the first cold rolling carried out on the intermediate steel materials of test numbers 1-1 to 1-21.
  • the cold rolling ratio CR1 of the first cold rolling was the same both times. It was the rolling ratio.
  • Bright annealing was carried out on the intermediate steel materials of test numbers 1-1 to 1-21 in which the first cold rolling was carried out.
  • Table 2 shows the annealing temperature (° C.) and annealing time (seconds) of the bright annealing performed on the intermediate steel materials of test numbers 1-1 to 1-21. Further, Table 2 shows the N2 fraction (%) in the atmosphere gas of brilliant burning.
  • Second cold rolling was carried out on the intermediate steel materials of test numbers 1-1 to 1-21 to which bright annealing was carried out.
  • Table 2 shows the cold rolling ratio CR2 (%) of the second cold rolling carried out on the intermediate steel materials of test numbers 1-1 to 1-21.
  • Tension annealing was performed on the intermediate steel material that had undergone the second cold rolling.
  • Table 2 shows the annealing temperature (° C.) of tension annealing performed on the intermediate steel materials of test numbers 1-1 to 1-21.
  • Table 2 shows the tension (N / mm 2 ) of the tension annealing performed on the intermediate steel materials of test numbers 1-1 to 1-21.
  • test numbers 1-1 to 1-21 the conditions of first cold rolling, bright annealing, second cold rolling, and tension annealing, and the above equations (2) to (9) were used. Eq1, Eq2, Eq3, Eq4, Eq5, Eq6, LM, and FnA were determined. The obtained FnA is shown in Table 2. Table 3 shows the obtained Eq1, Eq2, Eq3, Eq4, Eq5, Eq6, LM, and FnA.
  • the austenite-based stainless steel foils of test numbers 1-1 to 1-13 satisfy the entire range of chemical composition of the present embodiment, and further, in the manufacturing method, first cold rolling.
  • Cold rolling rate CR1, annealing temperature, annealing time and N2 fraction of bright annealing, cold rolling rate CR2 of second cold rolling, annealing temperature and tension of tension annealing, and FnA are all.
  • the preferred range described in the specification was satisfied.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was larger than 0.366 °.
  • the number of fatigues exceeded 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was excellent.
  • the cold rolling ratio CR1 of the first cold rolling was too low and the FnA exceeded 0.80 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the annealing temperature of the bright annealing was too high and the FnA exceeded 0.80 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the annealing time of bright annealing was too short in the manufacturing process, and FnA exceeded 0.80.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the cold rolling ratio CR2 of the second cold rolling was too low and the FnA exceeded 0.80 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the tension of the tension annealing was too high in the manufacturing process, and the FnA exceeded 0.80.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the annealing temperature of the tension annealing was too high, the tension of the tension annealing was too high, and the FnA exceeded 0.80 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the tension of the tension annealing was too high in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • Example 2 Similar to Example 1, hot rolling and annealing were performed on the slabs of steels A to L shown in Table 1 to produce a hot rolling coil having a thickness of 4 mm. In the same manner as in Example 1, cold rolling and annealing were repeatedly performed on the hot-rolled coils of the manufactured steels A to L, and a foil strip-shaped intermediate steel material (cold-rolled coil) having a thickness of 300 ⁇ m was repeatedly carried out. ) Was manufactured.
  • the first cold rolling was carried out under the conditions shown in Table 4 using intermediate steel materials of steels A to L. Specifically, for the intermediate steel materials of test numbers 2-1 to 2-18, the first cold rolling and bright annealing were repeated the number of times shown in Table 4. More specifically, when “once” is described in Table 4, it means that the first cold rolling and the bright annealing were performed once. When “twice” is described in Table 4, it means that the combination of the first cold rolling and the bright annealing was repeated twice.
  • Table 4 shows the cold rolling ratio CR1 (%) of the first cold rolling performed on the intermediate steel materials of test numbers 2-1 to 2-18.
  • the cold rolling ratio CR1 of the first cold rolling was the same both times. It was the rolling ratio.
  • Bright annealing was carried out on the intermediate steel materials of test numbers 2-1 to 2-18 in which the first cold rolling was carried out.
  • Table 4 shows the annealing temperature (° C.) and annealing time (seconds) of the bright annealing performed on the intermediate steel materials of test numbers 2-1 to 2-18.
  • Second cold rolling was carried out on the intermediate steel materials of test numbers 2-1 to 2-18 in which bright annealing was carried out.
  • Table 4 shows the cold rolling ratio CR2 (%) of the second cold rolling carried out on the intermediate steel materials of test numbers 2-1 to 2-18.
  • Tension annealing was performed on the intermediate steel material that had undergone the second cold rolling.
  • Table 4 shows the annealing temperature (° C.) of tension annealing performed on the intermediate steel materials of test numbers 2-1 to 2-18.
  • Table 4 shows the tension (N / mm 2 ) of the tension annealing performed on the intermediate steel materials of test numbers 2-1 to 2-18.
  • Eq1, Eq2, Eq3, Eq4, Eq5, Eq6 , LM, Eq7, FnA, and FnB are shown in Table 4.
  • Table 5 shows the obtained Eq1, Eq2, Eq3, Eq4, Eq5, Eq6, LM, Eq7, FnA, and FnB.
  • the uniform strain e was determined under the above conditions. Specifically, test pieces were prepared from austenitic stainless steel foils of each test number, and diffraction profiles were obtained by XRD. In XRD, the radiation source was CuK ⁇ ray, the tube voltage was 45 kV, and the tube current was 200 mA. Further, the diffraction angle (2 ⁇ ) was measured in the range of 40 to 50 degrees, the pitch was 0.01 degrees, and the pitch was 1 ° / min by the concentration method.
  • the peak of the (111) plane was identified from the obtained diffraction profile, and the lattice plane spacing d ( ⁇ ) was determined by Bragg's formula represented by the above formula (A).
  • the uniform strain e was obtained by using the lattice plane spacing d ( ⁇ ) of the obtained (111) plane and the above formula (B). In this example, a measured value of 2.0782 ⁇ was used as d 0 .
  • Table 4 shows the uniform strain e ( ⁇ 10 -4 ) of the austenitic stainless steel foil of each test number obtained.
  • the austenite-based stainless steel foils of test numbers 2-1 to 2-13 and 2-18 satisfy the entire range of the chemical composition of the present embodiment, and further, in the production method, the first Cold rolling rate CR1 for one cold rolling, annealing temperature, annealing time and N2 fraction for bright annealing, cold rolling rate CR2 for second cold rolling, annealing temperature and tension for tension annealing, and FnA.
  • all of them satisfied the preferable range described in the specification.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was larger than 0.366 °.
  • the number of fatigues exceeded 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was excellent.
  • the dew point in the atmosphere gas of bright baking was less than ⁇ 73 ° C. in the manufacturing method.
  • the uniform strain e was less than -2.89 ⁇ 10 -4 .
  • the number of fatigues exceeded 5.0 ⁇ 104 times in the repeated bending test, and the fatigue strength was further excellent.
  • the cold rolling ratio CR1 of the first cold rolling is too low, the tension of the tension annealing is too high, and the FnB is less than 0.15 in the manufacturing process.
  • Met the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the uniform strain e was -2.89 ⁇ 10 -4 or more.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the annealing temperature of the bright annealing was too low, the FnA was more than 0.80, and the FnB was less than 0.15 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the uniform strain e was -2.89 ⁇ 10 -4 or more.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the cold rolling ratio CR2 of the second cold rolling was too low, the tension of the tension annealing was too high, the FnA exceeded 0.80, and further. FnB was less than 0.15.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the uniform strain e was -2.89 ⁇ 10 -4 or more.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the tension of the tension annealing was too low and the FnB was less than 0.15 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • the uniform strain e was -2.89 ⁇ 10 -4 or more.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • Example 2 hot rolling and annealing were performed on the slabs of steels A to L shown in Table 1 to produce a hot rolling coil having a thickness of 4 mm.
  • cold rolling and annealing were repeatedly carried out on the hot-rolled coils of the manufactured steels A to L, and a foil strip-shaped intermediate steel material (cold-rolled coil) having a thickness of 300 ⁇ m was repeatedly carried out. ) Was manufactured.
  • the first cold rolling was carried out under the conditions shown in Table 6 using intermediate steel materials of steels A to L. Specifically, the first cold rolling and bright annealing were repeated for the intermediate steel materials of test numbers 3-1 to 3-22 the number of times shown in Table 6. More specifically, when “once” is described in Table 6, it means that the first cold rolling and the bright annealing were performed once. When “twice” is described in Table 6, it means that the combination of the first cold rolling and the bright annealing was repeated twice.
  • Table 6 shows the cold rolling ratio CR1 (%) of the first cold rolling performed on the intermediate steel materials of test numbers 3-1 to 3-22.
  • the cold rolling ratio CR1 of the first cold rolling was the same both times. It was the rolling ratio.
  • Bright annealing was carried out on the intermediate steel materials of test numbers 3-1 to 3-22 in which the first cold rolling was carried out.
  • Table 6 shows the annealing temperature (° C.) and annealing time (seconds) of the bright annealing performed on the intermediate steel materials of test numbers 3-1 to 3-22. Further, Table 6 shows the N2 fraction (%) and the furnace pressure (Pa) in the brilliantly blunted atmosphere gas.
  • Second cold rolling was carried out on the intermediate steel materials of test numbers 3-1 to 3-22 that had been brightly annealed.
  • Table 6 shows the cold rolling ratio CR2 (%) of the second cold rolling carried out on the intermediate steel materials of test numbers 3-1 to 3-22.
  • Tension annealing was performed on the intermediate steel material that had undergone the second cold rolling.
  • Table 6 shows the annealing temperature (° C.) of the tension annealing performed on the intermediate steel materials of test numbers 3-1 to 3-22.
  • Table 6 shows the tension (N / mm 2 ) of the tension annealing performed on the intermediate steel materials of test numbers 3-1 to 3-22.
  • Eq1 and Eq2 , Eq3, Eq4, Eq5, Eq6, LM, Eq8, FnA, and FnC are shown in Table 6.
  • Table 7 shows the obtained Eq1, Eq2, Eq3, Eq4, Eq5, Eq6, LM, Eq8, FnA, and FnC.
  • the diffraction angle (2 ⁇ ) was measured in the range of 40 to 50 degrees, the pitch was 0.01 degrees, and the pitch was 1 ° / min by the concentration method. From the obtained diffraction profile, the peaks of the ⁇ 111 ⁇ plane of the austenite phase and the ⁇ 110 ⁇ plane of the martensite phase were identified, and the plane spacing ⁇ 111 ⁇ ⁇ of the ⁇ 111 ⁇ plane of the austenite phase and the martensite phase The surface spacing ⁇ 110 ⁇ ⁇ 'of the ⁇ 110 ⁇ surface was obtained. Fn1 was obtained from the obtained ⁇ 111 ⁇ ⁇ and ⁇ 110 ⁇ ⁇ '. The obtained Fn1 is shown in Table 6.
  • a bending habit angle measurement test was performed on the austenitic stainless steel foils of each test number under the above-mentioned conditions. Specifically, test pieces were prepared from austenitic stainless steel foils of each test number, and a bending habit angle measurement test was carried out. The size of the test piece was 110 mm in the rolling direction of the steel foil and 100 mm in the width direction, and the thickness was the same as the thickness of the steel foil. Bending stress was repeatedly applied to the test piece 20,000 times (20,000 times) in the direction perpendicular to the rolling direction. The bending period was 1.25 Hz, the bending radius was 2.5 mm, and the bending angle was 0 to 125 °. As shown in FIG.
  • the austenite-based stainless steel foils of test numbers 3-1 to 3-13, 3-21, and 3-22 satisfy the entire range of chemical composition of the present embodiment, and further.
  • Both the tension and FnA met the preferred ranges described herein.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was larger than 0.366 °.
  • the number of fatigues exceeded 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was excellent.
  • the furnace pressure for bright annealing was 100 to 800 Pa in the manufacturing method.
  • the ratio Fn1 of the surface spacing ⁇ 111 ⁇ ⁇ of the ⁇ 111 ⁇ plane of the austenite phase to the plane spacing ⁇ 110 ⁇ ⁇ 'of the ⁇ 110 ⁇ plane of the martensite phase is 1. It was over 0220.
  • the bending habit angle was 6.0 ° or less in the bending habit angle measurement test, and it had excellent durability against bending stress.
  • the cold rolling ratio CR1 of the first cold rolling is too low, FnA exceeds 0.80, and FnC is 1.70 in the manufacturing process. Beyond. As a result, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less. As a result, Fn1 was less than 1.0220. As a result, the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent. As a result, in the bending habit angle measurement test, the bending habit angle exceeded 6.0 ° and did not have excellent durability against bending stress.
  • the annealing temperature of the bright annealing is too high, the furnace pressure of the bright annealing is too low, the tension of the tension annealing is too high, and the FnA exceeds 0.80 in the manufacturing process. Furthermore, FnC exceeded 1.70. As a result, the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less. As a result, Fn1 was less than 1.0220. As a result, the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent. As a result, in the bending habit angle measurement test, the bending habit angle exceeded 6.0 ° and did not have excellent durability against bending stress.
  • the annealing time of bright annealing is too short, the furnace pressure of bright annealing is too low, the tension of tension annealing is too high, and FnA exceeds 0.80 in the manufacturing process. Furthermore, FnC exceeded 1.70.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • Fn1 was less than 1.0220.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the bending habit angle measurement test the bending habit angle exceeded 6.0 ° and did not have excellent durability against bending stress.
  • the furnace pressure for bright annealing is too high, the cold rolling ratio CR2 for the second cold rolling is too low, and the FnC exceeds 1.70 in the manufacturing process. rice field.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • Fn1 was less than 1.0220.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the bending habit angle measurement test the bending habit angle exceeded 6.0 ° and did not have excellent durability against bending stress.
  • the furnace pressure of bright annealing is too low, the tension of tension annealing is too high, FnA exceeds 0.80, and FnC is 1.70 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • Fn1 was less than 1.0220.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the bending habit angle measurement test the bending habit angle exceeded 6.0 ° and did not have excellent durability against bending stress.
  • the annealing temperature of the tension annealing was too high, the FnA exceeded 0.80, and the FnC exceeded 1.70 in the manufacturing process.
  • the half width Fw of the peak of the ⁇ 111 ⁇ plane in the X-ray diffraction profile by CuK ⁇ ray was 0.366 ° or less.
  • Fn1 was less than 1.0220.
  • the number of fatigues was less than 4.5 ⁇ 104 times in the repeated bending test, and the fatigue strength was not excellent.
  • the bending habit angle measurement test the bending habit angle exceeded 6.0 ° and did not have excellent durability against bending stress.

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