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WO2014045542A1 - Tôle d'acier inoxydable ferritique qui est facilement usinée - Google Patents

Tôle d'acier inoxydable ferritique qui est facilement usinée Download PDF

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WO2014045542A1
WO2014045542A1 PCT/JP2013/005305 JP2013005305W WO2014045542A1 WO 2014045542 A1 WO2014045542 A1 WO 2014045542A1 JP 2013005305 W JP2013005305 W JP 2013005305W WO 2014045542 A1 WO2014045542 A1 WO 2014045542A1
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less
rolled
cold
stainless steel
steel sheet
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孝 寒川
太田　裕樹
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JFE Steel Corp
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JFE Steel Corp
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Priority to KR1020157005725A priority Critical patent/KR101718757B1/ko
Priority to JP2014526300A priority patent/JP5614516B2/ja
Priority to CN201380046801.5A priority patent/CN104619874B/zh
Publication of WO2014045542A1 publication Critical patent/WO2014045542A1/fr
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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
    • C22C38/54—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
    • 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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties 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 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 by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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

Definitions

  • the present invention relates to a ferritic stainless steel sheet suitable for use in building kitchen appliances, household products, electrical appliances, automobile parts, and the like, and particularly, molding that satisfies deep drawability and ridging resistance (ridging resistance).
  • the present invention relates to a ferritic stainless steel sheet having excellent workability.
  • the steel plate in this invention shall include a steel strip, a steel plate, and foil material.
  • Ferritic stainless steel is widely used as a material with excellent corrosion resistance in various industrial fields including household goods and automobile parts. This ferritic stainless steel is less expensive than austenitic stainless steel containing a large amount of Ni. However, it is generally inferior in workability. For example, when a molding process is performed, surface defects called ridging are likely to occur, and it is not suitable for applications in which a strong process such as deep drawing is performed. In addition, ferritic stainless steel has a large in-plane anisotropy ( ⁇ r) of the plastic strain ratio (r value), and there is also a problem that non-uniform deformation is likely to occur during deep drawing.
  • ⁇ r plastic strain ratio
  • the r value which is an index of deep drawability, is improved, the in-plane anisotropy ( ⁇ r) of the plastic strain ratio is reduced, and the ridging resistance is also improved. Is required.
  • Patent Document 1 In response to such a request, for example, in Patent Document 1, C: 0.03 to 0.08%, Si: 0.4% or less, Mn: 0.5% or less, P: 0.03% or less , S: 0.008 or less, Ni: 0.3% or less, Cr: 15 to 20%, Al: N ⁇ 2 to 0.2% or less, N: 0.01% or less, balance Fe and unavoidable A ferritic stainless steel having excellent processability composed of impurities is disclosed.
  • Patent Document 3 mass%, C: 0.02 to 0.06%, Si: 1.0% or less, Mn: 1.0% or less, P: 0.05% or less, S: 0 0.01% or less, Al: 0.005% or less, Ti: 0.005% or less, Cr: 11 to 30% or less, Ni: 0.7% or less, and N in relation to the C content , 0.06 ⁇ (C + N) ⁇ 0.12 and 1 ⁇ N / C are satisfied, and further, V is 1.5 ⁇ 10 ⁇ 3 ⁇ (V ⁇ N) in relation to the N content.
  • a ferritic stainless steel sheet excellent in formability which is contained so as to satisfy ⁇ 1.5 ⁇ 10 ⁇ 2 and consists of the balance Fe and inevitable impurities.
  • Patent Document 4 C: 0.02% or less, Si: 1.0% or less, Mn: 2.0% or less, Cr: 11 to 35%, Ni: 0.5% by weight%, A ferritic stainless steel having excellent corrosion resistance, which is composed of N: 0.03% or less, V: 0.5-5.0%, the balance, iron and accompanying impurities is disclosed.
  • JP-A-52-24913 Japanese Patent Laid-Open No. 54-112319 Japanese Patent No. 3584881 JP 59-193250 A
  • Patent Literature 1 since the technique described in Patent Literature 1 is premised on low N, there is a problem in that an increase in cost in the steelmaking process cannot be avoided. Moreover, in the technique described in Patent Document 2, since a large amount of Zr is added, the amount of inclusions in the steel increases, and there is a problem that surface defects due to this increase cannot be avoided.
  • the technique described in Patent Document 3 aims at improving elongation and r value and improving ridging resistance as an index of moldability. However, no consideration is given to the reduction of the in-plane anisotropy ( ⁇ r), and there remains a problem in the moldability. In the technique described in Patent Document 4, it is said that the addition of V significantly improves the corrosion resistance, particularly the stress corrosion cracking resistance.
  • an object of the present invention is to provide a ferritic stainless steel sheet excellent in formability that satisfies deep drawability and ridging resistance.
  • V / B 10 or more, and the contents of V and B are optimal ranges, such as carbides and nitrides in steel.
  • the precipitate By controlling the precipitate, the crystal grain size can be refined to improve deep drawability, ridging can be suppressed, and a ferritic stainless steel sheet excellent in forming processability can be obtained.
  • the gist of the present invention is as follows.
  • the ferritic stainless steel sheet excellent in moldability means a ferritic stainless steel sheet satisfying an elongation (El) of 30% or more, an r value of 1.3 or more, and ⁇ r0.3 or less.
  • FIG. 1 is a graph showing the relationship between mechanical properties and V / B of a cold-rolled annealed plate
  • (a) is a graph showing the relationship between elongation (El) and V / B
  • (b) is an r value and V / B.
  • (c) is the graph which shows the relationship between (DELTA) r and V / B
  • (d) is the graph which shows the relationship between ridging height and V / B.
  • FIG. 2 is a graph showing the relationship between the contents of V and B for ensuring the sensitization characteristics of the cold-rolled annealed sheet.
  • % showing the quantity of a component means the mass%.
  • C 0.010 to 0.070% C forms a solid solution in the steel and contributes to stabilization of the austenite phase during hot rolling, and is combined with Cr and precipitated as Cr carbide or Cr carbonitride in the crystal grains and the grain boundaries.
  • C is less than 0.010%, the effect of refining crystal grains due to fine precipitation of carbonitrides and carbides such as V (C, N), VC, and V 4 C 3 cannot be obtained.
  • the austenite phase fraction during hot rolling is reduced, so that ridging is noticeably generated in the cold-rolled steel sheet, which is a product sheet, and the formability is deteriorated.
  • C is set to 0.010% to 0.070%. More preferably, it is 0.020 to 0.040%.
  • Si 1.00% or less Si is an element useful as a deoxidizer for steel. In order to obtain this effect, 0.05% or more is preferable. However, if it exceeds 1.00%, the ductility is lowered and the moldability is lowered. Therefore, Si is made 1.00% or less. More preferably, it is 0.05 to 0.50% or less. If Si is 0.28% or less, the pickling property is improved. If pickling is required, the content is set to 0.05% to 0.28%.
  • Mn 1.00% or less Mn combines with S present in the steel to form MnS and lowers the corrosion resistance. Therefore, Mn is made 1.00% or less. More preferably, it is 0.80% or less. On the other hand, 0.05% or more is preferable because refining costs increase to reduce Mn more than necessary. From the viewpoint of particularly high corrosion resistance and refining cost, 0.05 to 0.60% is more preferable. If Mn is 0.92% or less, the pickling property becomes good. If pickling property is required, the content is made 0.05% to 0.92%.
  • P 0.040% or less Since P is an element harmful to corrosion resistance, it is preferably reduced as much as possible. Moreover, when it exceeds 0.040%, workability will fall by solid solution strengthening. Therefore, P is set to 0.040% or less. More preferably, it is 0.030% or less.
  • S 0.010% or less S forms sulfides in steel.
  • Mn When Mn is contained, it combines with Mn to form MnS.
  • MnS expands by hot rolling or the like and exists as precipitates (inclusions) at ferrite grain boundaries and the like.
  • Such sulfide-based precipitates (inclusions) lower the elongation, and particularly have a great influence on the occurrence of cracks during bending. Therefore, it is desirable to reduce S as much as possible, and it is acceptable up to 0.010%. In addition, Preferably it is 0.005% or less.
  • Cr 14.00-20.00%
  • Cr is an element that contributes to improving the corrosion resistance while solid-strengthening steel, and is an essential element for a stainless steel plate.
  • Cr is less than 14.00%, the corrosion resistance as stainless steel is insufficient.
  • Cr exceeds 20.00%, in addition to the toughness being lowered, the steel is too hardened and the elongation is also significantly lowered. Therefore, the Cr content is 14.00 to 20.00%. Further, from the viewpoint of corrosion resistance and manufacturability, it is preferably 16.00 to 18.00%.
  • Al 0.150% or less
  • Al is an element useful as a deoxidizer for steel. In order to acquire this effect, 0.001% or more is preferable. However, excessive addition causes a surface flaw due to an increase in Al-based inclusions, so the content is made 0.150% or less. More preferably, it is 0.100% or less. More preferably, it is 0.010% or less.
  • Ni 1.00% or less Ni has an effect of reducing crevice corrosion. In order to obtain this effect, 0.05% or more is preferable. However, in addition to being an expensive element, even if the content exceeds 1.00%, those effects are saturated, and on the contrary, the hot workability is lowered. Therefore, Ni is made 1.00% or less. More preferably, it is 0.05 to 0.40%.
  • N 0.010 to 0.060%
  • N contributes to the stabilization of the austenite phase during hot rolling by solid solution in steel, and combines with Cr to form Cr nitrides or Cr carbonitrides in crystal grains or crystals. Precipitates at grain boundaries and the like. Furthermore, it combines with V, which is important in the present invention, to form nitrides and carbonitrides, and refines the crystal grains of the final product to contribute to the improvement of the r value. If N is less than 0.010%, the austenite phase fraction during hot rolling decreases, and therefore, ridging occurs significantly in the cold-rolled steel sheet, which is the final product, and the formability deteriorates.
  • N is set to 0.010 to 0.060%. More preferably, it is 0.020 to 0.050%.
  • V 0.005 to 0.100%
  • B 0.0001 to 0.0050%
  • V / B ⁇ 10 or more V and B are extremely important elements in the present invention.
  • V is combined with N to form nitrides and carbonitrides such as VN and V (C, N), and has an effect of suppressing coarsening of crystal grains of the hot-rolled annealing plate.
  • B also has an effect of assisting the suppression of grain growth by concentrating on ferrite grain boundaries and delaying grain boundary migration. Due to the combined effect of V and B, the crystal grains of the hot-rolled annealing plate are refined.
  • C 0.04%, Si: 0.40%, Mn: 0.80%, P: 0.030%, S: 0.004%, Al: 0.002%, Cr: 16. 20%, Ni: 0.10%, N: 0.060% contained, the steel added by changing the amount of V and B, and the steel slab was heated to 1170 ° C, the finishing temperature was Hot rolling at 830 ° C. was performed to obtain a hot rolled sheet.
  • These hot-rolled sheets were subjected to hot-rolled sheet annealing at 860 ° C. ⁇ 8 hours, then pickled, and then cold-rolled with a total rolling reduction of 86% to obtain cold-rolled sheets. Then, these cold-rolled plates were subjected to finish annealing at 820 ° C.
  • FIG. 1 shows the relationship between V / B and the mechanical properties (elongation, r value, ⁇ r, ridging height) of the cold-rolled annealed sheet. From FIG. 1, when the V amount is 0.005% or more, the B amount is 0.0001% or more, and V / B ⁇ 10, all of El, r value, ⁇ r, and ridging height are satisfied. all right.
  • V is 0.005 to 0.1%
  • B is 0.0001 to 0.0050%
  • V / B ⁇ 10. If V and B are added excessively exceeding 0.1% and 0.0050%, respectively, not only the effect of refinement of crystal grains and suppression of growth and improvement of forming processability during annealing will be saturated, but conversely The material is cured and the ductility is lowered, and the molding processability is deteriorated.
  • V is 0.005 to 0.03% or less and B is 0.0001 to 0.0020%.
  • the V / B ratio is less than 10, since B is combined with N and precipitates as a nitride, the effect of suppressing the grain growth by reducing the concentration of B at the grain boundary is reduced. Is considered to be insufficient.
  • the finish annealing temperature is not always constant, and fluctuations in heating time and ultimate temperature cannot be avoided.
  • ferritic stainless steel sheets that do not contain stabilizing elements such as Ti and Nb that fix C and N, when annealing is performed at high temperatures, sensitization occurs during cooling, and grain boundaries are eroded during subsequent pickling. The surface quality may deteriorate. For this reason, it is extremely important to prevent sensitization from occurring in a wide temperature range in order to obtain stable quality in actual operation.
  • the present inventors investigated the relationship between sensitization characteristics and V / B.
  • component composition C: 0.04%, Si: 0.40%, Mn: 0.80%, P: 0.030%, S: 0.004%, Al: 0.002%, Cr: 16. 20%, Ni: 0.10%, N: 0.060% contained, the steel added by changing the amount of V and B, and the steel slab was heated to 1170 ° C, the finishing temperature was Hot rolling at 830 ° C. was performed to obtain a hot rolled sheet.
  • These hot-rolled sheets were subjected to hot-rolled sheet annealing at 860 ° C. ⁇ 8 hours, then pickled, and then cold-rolled with a total rolling reduction of 86% to obtain cold-rolled sheets.
  • these cold-rolled plates were subjected to finish annealing at 900 ° C. for 30 seconds in the air, and then pickled to obtain cold-rolled annealed pickled plates having a thickness of 0.7 mm.
  • the surface of the obtained cold-rolled annealed pickling plate is observed using a scanning electron microscope to observe the grain boundary in the 500 ⁇ m ⁇ 500 ⁇ m region, and the presence or absence of intergranular corrosion is evaluated to evaluate the surface quality. did.
  • the obtained results are shown in FIG. When no erosion occurred, it was marked as ⁇ , and when erosion occurred, it was marked as x.
  • FIG. 2 shows that by adding V and B so that the addition amount satisfies V / B ⁇ 20, grain boundary sensitization can be suppressed even by annealing at 900 ° C. This is because Cr carbonitriding at the grain boundaries that occurs during cooling after finish annealing even when the finish annealing temperature is as high as 900 ° C by fixing C and N in steel. This is thought to be due to the suppression of the precipitation of materials.
  • V / B is less than 20
  • the precipitation amount of the carbonitride of V decreases because the precipitation amount of the carbonitride of V is decreased by binding B to N and precipitates as a nitride. It is thought that sensitization progressed.
  • V is 0.005 to 0.03% or less and B is 0.0001 to 0.0020%.
  • Fe and inevitable impurities include, for example, Nb: 0.05% or less, Ti: 0.05% or less, Co: 0.5% or less, W: 0.01% or less, Zr: 0.01% or less, Ta : 0.01% or less, Mg: 0.0050% or less, Ca: 0.0020% or less are acceptable.
  • the molten steel having the above composition is melted in a generally known converter or electric furnace, and further refined by vacuum degassing (RH), VOD (Vacuum Oxygen Decarburization), AOD (Argon Oxygen Decarburization), etc., preferably continuously It is cast by the casting method and used as a rolled material (slab, etc.).
  • the rolled material is heated and hot-rolled to obtain a hot-rolled sheet.
  • the slab heating temperature for hot rolling is preferably in the temperature range of 1050 ° C. to 1250 ° C., and the finishing temperature for hot rolling is preferably 800 to 900 ° C. from the viewpoint of manufacturability.
  • the hot-rolled sheet can be subjected to hot-rolled sheet annealing as necessary for the purpose of improving workability in a subsequent process.
  • box annealing box annealing, batch annealing
  • continuous annealing in the temperature range of 900 to 1100 ° C for a short time. Is preferred.
  • a hot-rolled sheet can be descaled and used as a product as it is, or can be used as a material for cold rolling.
  • the hot-rolled sheet of the material for cold rolling is subjected to cold rolling at a cold rolling reduction ratio of 30% or more to obtain a cold-rolled sheet.
  • the cold rolling reduction ratio is preferably 50 to 95%. Further, in order to impart further workability of the cold-rolled sheet, finish annealing at 600 ° C. or higher, preferably 700 to 900 ° C. can be performed. Further, cold rolling and annealing may be repeated twice or more. Further, when glossiness is required, a skin pass or the like may be applied.
  • the finish processing of the cold-rolled sheet can be 2D, 2B, BA, and various types of polishing defined by Japan industrial Standard (JIS) G4305.
  • Molten steel having the composition shown in Table 1 was melted by secondary refining using a converter and VOD, and was made into a slab by a continuous casting method. After these slabs were heated to 1170 ° C., hot rolling was performed at a finishing temperature of 830 ° C. to obtain hot rolled sheets. These hot-rolled sheets were subjected to hot-rolled sheet annealing at 860 ° C. ⁇ 8 hours, then pickled, and then cold-rolled with a total rolling reduction of 86% to obtain cold-rolled sheets. Next, Steel No. 1 to 18 and steel no. Coke oven gas was burned on cold rolled plates of 24-32 at an air ratio of 1.3, and finish annealing was performed at 820 ° C. for 30 seconds in this combustion atmosphere.
  • the obtained cold-rolled annealed pickled plate was evaluated for elongation, r value, and ⁇ r, and evaluated for formability. Moreover, the ridging height was calculated
  • rL, rD, and rC represent r values in the L direction, the D direction, and the C direction, respectively.
  • the ridging resistance was evaluated in four stages from the height of the waviness: A: 5 ⁇ m or less, B: more than 5 ⁇ m to 10 ⁇ m or less, C: more than 10 ⁇ m to 20 ⁇ m or less, D: more than 20 ⁇ m.
  • a evaluation with a swell height of 5.0 ⁇ m or less was regarded as acceptable.
  • Each of the inventive examples has an A evaluation with an elongation of 30% or more, an r value of 1.3 or more, an ⁇ r of 0.3 or less, and a waviness height of 5.0 ⁇ m or less, and good moldability and ridging resistance. It has sex. In contrast, the comparative example did not satisfy any of elongation, r value, ⁇ r, and ridging height.
  • Example No. 1 of Example 1 having good moldability and ridging resistance. 5-11 and no. About 19-36, although the pickling power was weaker than the pickling method of Example 1, the pickling property in the highly productive mixed acid of nitric acid and hydrochloric acid electrolytic method was evaluated. . Steel No. 1 produced in Example 1 was used. 5-11 and 19-36 with a thickness of 0.7 mm cold rolled sheet, 820 ° C. ⁇ 30 sec in weak reducing atmosphere (H 2 : 5 vol%, N 2 : 95 vol%, dew point ⁇ 40 degrees) Annealing was performed to obtain a cold-rolled annealed plate.
  • weak reducing atmosphere H 2 : 5 vol%, N 2 : 95 vol%, dew point ⁇ 40 degrees
  • the cold-rolled annealed plate was electrolyzed in a solution composed of 50 ° C., 10% by mass nitric acid and 1.0% by mass hydrochloric acid, and the pickling property was evaluated by visually observing the presence or absence of the oxide film residue.
  • 10A / dm 2 ⁇ 2 seconds oxide film by electrolysis performed twice what was completely removed ⁇ (excellent) could not be completely removed oxide coating by electrolysis performed 10A / dm 2 ⁇ 2 seconds twice and although, 10A / dm 2 ⁇ 4 seconds electrolytic twice performed and the ⁇ (good) which oxide film is completely removed, and also completely oxidized film went 10A / dm 2 x4 seconds electrolytic twice Those that could not be removed were evaluated as x (defect). ⁇ (Excellent) and ⁇ (Good) are acceptable.
  • Nos. 5 to 10, 19 to 26 and 30 to 34 are particularly excellent in pickling properties in addition to good moldability and ridging resistance. It can be produced not only by a general pickling method but also by a highly productive nitric acid hydrochloric acid electrolysis method.
  • Example 1 In the sensitization evaluation method, a cold-rolled sheet having a thickness of 0.7 mm produced in Example 1 was annealed at 900 ° C. ⁇ 30 sec, and washed with nitric acid after Na 2 SO 4 electrolysis under the same conditions as in Example 1. . Using a scanning electron microscope, the surface of the cold-rolled annealed pickling plate was observed for grain boundaries in a 500 ⁇ m ⁇ 500 ⁇ m region to investigate the presence or absence of grain boundary erosion, and the surface quality was evaluated. It was evaluated that there was no sensitization when no erosion occurred at the grain boundaries, and there was sensitization when erosion occurred. The results are shown in Table 4.
  • a ferritic stainless steel sheet satisfying deep drawability and ridging resistance and excellent in formability can be produced by optimizing the component composition, particularly V and B contents.
  • the effect of. Furthermore, by adjusting the V and B contents to the optimum ranges, the sensitization resistance is improved, and it is possible to stably produce ferritic stainless steel sheets with excellent surface quality in addition to forming processability. Become.

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