WO2014147655A1 - Tôle d'acier inoxydable ferritique - Google Patents

Tôle d'acier inoxydable ferritique Download PDF

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WO2014147655A1
WO2014147655A1 PCT/JP2013/001824 JP2013001824W WO2014147655A1 WO 2014147655 A1 WO2014147655 A1 WO 2014147655A1 JP 2013001824 W JP2013001824 W JP 2013001824W WO 2014147655 A1 WO2014147655 A1 WO 2014147655A1
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steel sheet
stainless steel
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PCT/JP2013/001824
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Japanese (ja)
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孝 寒川
石川　伸
太田　裕樹
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Ｊｆｅスチール株式会社
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Priority to KR1020157006848A priority Critical patent/KR101683039B1/ko
Priority to JP2013553688A priority patent/JP5505575B1/ja
Priority to CN201380051384.3A priority patent/CN104685086B/zh
Priority to PCT/JP2013/001824 priority patent/WO2014147655A1/fr
Publication of WO2014147655A1 publication Critical patent/WO2014147655A1/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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • 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
    • 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
    • C22C38/44—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
    • C22C38/52—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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • the present invention relates to a ferritic stainless steel sheet that can be preferably applied to various uses such as automobile parts, household products, kitchen appliances, electrical appliances, etc., and has excellent formability and corrosion resistance.
  • Ferritic stainless steel is widely used as a material with excellent corrosion resistance in various fields including automobile parts and household goods. In general, this ferritic stainless steel is cheaper than austenitic stainless steel containing a large amount of Ni, but is inferior in formability. For example, ferritic stainless steel has a problem that irregularities called earrings occur at the edge of a molded member when deep drawing is performed. For this reason, ferritic stainless steel that has both corrosion resistance and formability such as deep drawing is required.
  • Patent Document 1 As a technique for improving the formability of ferritic stainless steel, for example, in Patent Document 1, C: 0.03 mass% or less, Si: 2.0 mass% or less, Mn: 0.8 mass% or less, S : 0.03 mass% or less, Cr: 6 to 25 mass%, N: 0.03 mass% or less, Al: 0.3 mass% or less, Ti: 0.4 mass% or less, V: 0.02 to 0 4 mass%, B: 0.0002 to 0.0050 mass% in a range satisfying the formulas: Ti / 48> N / 14 + C / 12, V / B> 10, with the balance being Fe and inevitable impurities
  • a ferritic stainless hot-rolled steel sheet characterized by comprising: This ferritic stainless steel hot-rolled steel sheet is said to have excellent skin resistance after forming and high temperature fatigue properties.
  • Patent Document 2 C: 0.03 to 0.08 mass%, Si: 1.0 mass% or less, Mn: 1.0 mass% or less, P: 0.05 mass% or less, S: 0 .015 mass% or less, Al: 0.10 mass% or less, N: 0.02 mass% or less, Cr: 5 to 60 mass%, Ti: 4 ⁇ (C content + N content) to 0.5 % By mass, Nb: 0.003-0.020% by mass, B: 0.0002-0.005% by mass, the balance being Fe and inevitable impurities, and ⁇ r being 0.3 or less
  • a featured chromium steel sheet is disclosed. This chromium steel sheet is said to be excellent in deep drawability and secondary work brittleness resistance.
  • the techniques described in the above patent documents have the following problems.
  • the in-plane anisotropy (hereinafter simply referred to as ⁇ r) of the plastic strain ratio (hereinafter simply referred to as r value) is not sufficiently improved.
  • the technique described in Patent Document 1 has a problem that earrings are generated at the edge of the molded member when deep drawing is performed.
  • the influence on the corrosion resistance due to the addition of B has not been studied, and the corrosion resistance of the ferritic stainless steel hot rolled steel sheet may be lowered.
  • the technique disclosed in Patent Document 2 although the r value and ⁇ r are improved, the influence on the corrosion resistance by adding B has not been studied, and the corrosion resistance of the chromium steel sheet may be lowered. is there.
  • An object of the present invention is to provide a ferritic stainless steel sheet that solves the above-described problems of the prior art and has excellent formability and corrosion resistance.
  • the present inventors have made various studies in order to achieve the above-described problems. As a result, a ferritic stainless steel sheet having both formability such as deep drawing and corrosion resistance can be obtained by adjusting the V content and B content to appropriate ranges and adjusting V / B to 15.0 or more. As a result, the present invention has been completed.
  • Example 1 (0.009 to 0.012)% C [C content in Table 1 means in the range of 0.009 to 0.012 mass%. The same applies hereinafter. ], (0.08 to 0.12)% Si, (0.19 to 0.23)% Mn, (0.033 to 0.037)% P, (0.001 to 0.002)% S, (17.2 to 17.5)% Cr, (0.02 to 0.03)% Al, (0.009 to 0.012)% N, (0.08 to 0.12)% Ni, (0 .25 to 0.27)% Ti, (0.010 to 0.016)% V, and (0.0002 to 0.0010)% B, changing the V / B ratio, the balance being Fe and inevitable impurities Stainless steel made of was melted in a 50 kg small vacuum melting furnace.
  • the combined cycle corrosion test is based on JASO M 609-91, salt spray (5% NaCl, 35 ° C., 2 h) ⁇ dry (60 ° C., relative humidity 20-30%) ⁇ wet (50 ° C., 2 h, relative humidity) 30 cycles of corrosion test with 1 cycle of ⁇ 95%) were performed.
  • an area ratio of 20% or more was determined to be unacceptable and less than 20% was determined to be acceptable.
  • Table 1 From Table 1, it can be seen that the corrosion resistance is improved by setting the V / B ratio to 15.0 or more.
  • the hot-rolled sheet was annealed at 1020 ° C. ⁇ 60 sec, then shot blasted, pickled with a mixed acid of hydrofluoric acid and nitric acid, and cold rolled into a cold-rolled sheet having a thickness of 0.7 mm. .
  • the obtained cold-rolled sheet was subjected to finish annealing at 980 ° C. ⁇ 40 sec to obtain a cold-rolled annealed sheet.
  • a test piece of 60 mm ⁇ 80 mm was cut out from the obtained cold-rolled annealed plate, the surface was polished with # 600 count, and corrosion resistance was evaluated by a combined cycle corrosion test. In the combined cycle corrosion test, the above corrosion test cycle was performed 30 times.
  • a hot-rolled sheet having a thickness of 0.0 mm was used. These hot-rolled sheets were subjected to hot-rolled sheet annealing at 930 ° C. ⁇ 60 sec, then pickled, and then cold-rolled to obtain cold-rolled sheets having a thickness of 0.7 mm. Further, these cold-rolled plates were subjected to finish annealing at 880 ° C. ⁇ 40 sec, and then pickled to obtain cold-rolled annealed pickled plates. About the obtained cold-rolled annealing pickling board, the tension test (JIS Z 2201) was done and elongation, r value, and (DELTA) r were calculated
  • an elongation of 30.0% or more, an r value of 1.50 or more, and ⁇ r of 0.30 or less were determined to be acceptable.
  • the surface of the test piece cut out from the cold rolled annealed pickling plate was polished with # 600 count, and the corrosion resistance was evaluated by a combined cycle corrosion test.
  • the above corrosion test cycle was performed 30 times.
  • an area ratio of 20% or more was determined to be unacceptable and less than 20% was determined to be acceptable.
  • FIG. 1 shows the relationship between the V / B and cold-rolled annealed pickling plate forming processability (elongation, r value, ⁇ r) and the corrosion resistance evaluation results. From FIG. 1, it was found that by satisfying V / B ⁇ 15.0, all of El, r value, ⁇ r, and corrosion resistance evaluation satisfy the determination criteria. In particular, it was found that r value and ⁇ r were excellent when V / B ⁇ 30.0.
  • the present invention provides the following.
  • V 0.010-0.040%
  • B 0.0001-0.0010%
  • ratio of V content to B content (V / B) ⁇ 15.0 When it is contained within a range satisfying Ti: 0.20% or more and 0.40% or less and Ti% + Nb% ⁇ 0.70, Ti is contained or Ti and Nb are contained, and Nb : 0.40% or more and 0.60% or less, Nb contained within a range satisfying Ti% + Nb% ⁇ 0.70, or a small amount when Nb and Ti are contained Satisfy one Kutomo, ferritic stainless steel sheet balance being Fe and unavoidable impurities.
  • the ferritic stainless steel sheet of the present invention has excellent formability (formability) and excellent corrosion resistance. Specifically, the ferritic stainless steel sheet of the present invention has a formability satisfying an elongation of 30.0% or more, an r value of 1.50 or more, and ⁇ r of 0.30 or less, and was polished by # 600. Corrosion resistance satisfying a cracking area ratio of less than 20% in a combined cycle corrosion test (30 cycles) in accordance with JASO M 609-91 on the surface of a steel plate.
  • C 0.003-0.013%
  • the lower the C content the better from the viewpoint of corrosion resistance and moldability.
  • the lower limit of the C content is 0.003%.
  • the C content is in the range of 0.003 to 0.013%. More preferably, it is 0.004 to 0.011%.
  • Si 0.01 to 0.95%
  • Si is an element useful as a deoxidizer for steel.
  • the Si content is 0.01% or more.
  • the Si content exceeds 0.95%, the rolling load increases in the hot rolling process, and a scale is very easily generated.
  • the pickling property is lowered due to the formation of a scale in which Si is concentrated on the surface layer of the steel sheet.
  • the Si content is in the range of 0.01 to 0.95%. More preferably, it is 0.05 to 0.50%.
  • the Ti content to be described later is 0.25% or more, the pickling property is significantly reduced by Si.
  • the preferable range of the Si content is 0.05 to 0.20%. It is.
  • Mn 0.01 to 0.40% Mn combines with S present in the steel to form MnS and lowers the corrosion resistance. Therefore, the Mn content is set to 0.40% or less. On the other hand, if the content of Mn is decreased more than necessary, the refining cost increases. For this reason, the Mn content is preferably 0.01% or more. In order to achieve particularly high corrosion resistance while suppressing refining costs, the preferable range of the Mn content is 0.05 to 0.35%.
  • P 0.020 to 0.040%
  • P is an element inevitably contained in steel. Since P is an element harmful to corrosion resistance and moldability, the P content is preferably low. In particular, if the P content exceeds 0.040%, the formability of the steel sheet decreases due to solid solution strengthening. For this reason, content of P is 0.040% or less. On the other hand, in order to make the P content less than 0.020%, it is necessary to perform refining over time, and making the P content less than 0.020% is not preferable in production. Therefore, the P content is in the range of 0.020 to 0.040%. Preferably, it is in the range of 0.025 to 0.035%.
  • S 0.010% or less S 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) reduce the elongation of the steel sheet, and sometimes cause cracks in the steel sheet during bending of the steel sheet. For this reason, it is desirable to reduce the S content as much as possible, and the allowable S content is up to 0.010%.
  • a preferable S content is 0.005% or less.
  • Al 0.01 to 0.45%
  • Al is an element useful as a deoxidizer for steel.
  • the Al content needs to be 0.01% or more.
  • the range of Al content is set to 0.01 to 0.45%.
  • a preferable range of the Al content is 0.01 to 0.10%.
  • a more preferred range is 0.02 to 0.04%.
  • Cr 14.5-21.5%
  • Cr is an element that contributes to improving corrosion resistance, and is an element included as an essential element in a stainless steel plate.
  • the Cr content is less than 14.5%, a steel sheet having sufficient corrosion resistance cannot be obtained.
  • the Cr content exceeds 21.5%, in addition to the toughness of the steel sheet being lowered, the steel is too hard and the elongation of the steel sheet is also significantly reduced. Therefore, the Cr content range is 14.5 to 21.5%. Further, from the viewpoint of corrosion resistance and manufacturability, the preferable range of the Cr content is 16.0 to 21.5%.
  • Ni 0.01 to 0.60% Ni has an effect of reducing crevice corrosion. In order to obtain this effect, the Ni content must be 0.01% or more. However, in addition to Ni being an expensive element, even if Ni exceeds 0.60%, the above effect is saturated and the hot workability is reduced. Therefore, the range of Ni content is set to 0.01 to 0.60%. A preferable range of the Ni content is 0.10 to 0.40%.
  • N 0.005 to 0.012% N combines with V to form nitrides or carbonitrides, refines the crystal grains of the final product plate, and contributes to the improvement of the r-value characteristics.
  • the N content is less than 0.005%, the effect of refining crystal grains due to fine precipitation of V (C, N) carbonitride cannot be obtained.
  • the N content exceeds 0.012%, the Cr nitride amount or the Cr carbonitride amount increases, the steel plate becomes hard and the elongation decreases. Therefore, the range of N content is set to 0.005 to 0.012%.
  • the preferable range of the N content is 0.006 to 0.010%.
  • V 0.010 to 0.040%
  • B 0.0001 to 0.0010%
  • V / B 15.0 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 has an effect of assisting the grain growth suppression by concentrating on the ferrite grain boundary and delaying the grain boundary movement. Due to the combined effect of V and B, the crystal grains of the hot-rolled annealing plate are refined.
  • the area of the grain boundary which is the preferential nucleation site of ⁇ 111 ⁇ recrystallized orientation grains after cold rolling annealing, increases the ⁇ 111 ⁇ orientation, thereby improving the r value. It is considered that the ⁇ r value decreases.
  • V content is less than 0.010%, the effect of refining crystal grains due to fine precipitation of VN or V (C, N) cannot be obtained.
  • B content is less than 0.0001%, there is no effect of suppressing grain growth.
  • V content exceeds 0.040% or the B content exceeds 0.0010% the effect of refinement of crystal grains during growth and suppression of growth and improvement of moldability are only saturated. On the contrary, the material is hardened, the ductility is lowered, and the formability of the steel sheet is deteriorated. Therefore, the content range of V is 0.010 to 0.040%, and the content range of B is 0.0001 to 0.0010%.
  • V / B The content ratio of V and B affects the balance between the ferrite crystal grain size and the ferrite grain interfacial area and the precipitation behavior of Cr 2 B at the grain boundaries, and affects the moldability and corrosion resistance. It is conceivable that. As described in Tables 1 and 2 and FIG. 1, when the V / B ratio is less than 15.0, B combines with Cr and precipitates as Cr 2 B at the grain boundary. As a result, the effect of suppressing grain growth is reduced, and the r value is insufficiently improved. Furthermore, the Cr concentration in the vicinity of the grain boundary decreases, and the corrosion resistance of the steel sheet deteriorates. Therefore, (V / B) is set to 15.0 or more. In addition, from a viewpoint of ensuring high moldability, the preferable range of V / B is 30.0 or more.
  • Ti 0.20% or more and 0.40% or less, Ti in a range satisfying Ti% + Nb% ⁇ 0.70, or Ti and Nb, and Nb: 0.40% or more and 0.60 % Or less, when Nb is contained in a range satisfying Ti% + Nb% ⁇ 0.70, or Nb and Ti are contained Ti and Nb are both solid solution C and N are fixed as a compound to fix the corrosion resistance of the steel sheet. And has the effect of improving moldability. For this reason, it is necessary to use either Ti or Nb alone or to use both Ti and Nb. Specifically, in order to acquire the said effect, it is necessary to contain Ti: 0.20% or more or Nb: 0.40% or more.
  • the Ti amount is 0.40% or less, the Nb amount is 0.60% or less, and Ti% + Nb% ⁇ 0.70 (in the present invention, all of Ti amount, Nb amount, Ti% + Nb% Must be less than or equal to the upper limit).
  • the Ti content is 0.35% or less, the Nb content is 0.55% or less, and Ti% + Nb% ⁇ 0.65.
  • the ferritic stainless steel sheet of the present invention contains the essential components described above, with the balance being Fe and inevitable impurities.
  • the ferritic stainless steel sheet of the present invention further includes one or more selected from one or two of Cu and Mo, Zr, REM, W, Co, Mg, and Ca, if necessary. You may contain in the following range.
  • Cu 0.01 to 1.40%
  • Cu is an element that improves the corrosion resistance.
  • Cu is an element that is particularly effective for improving the corrosion resistance when the steel sheet is in an aqueous solution or when weakly acidic water droplets adhere to the steel sheet. This effect is obtained by containing 0.01% or more of Cu, and increases as the Cu content increases.
  • the Cu content exceeds 1.40%, the hot workability deteriorates and Cu-derived oxide called red scale is generated on the hot-rolled slab during hot rolling, resulting in surface defects. Therefore, it is not preferable.
  • the Cu content exceeds 1.40%, descaling after annealing becomes difficult, which is not preferable for production. Therefore, when Cu is contained, the content range is preferably 0.01 to 1.40%. Further, the more preferable range of the Cu content is 0.10 to 1.00%, and the most preferable range is 0.30 to 0.50%.
  • Mo 0.01 to 1.62%
  • Mo is an element that significantly improves the corrosion resistance of the stainless steel plate. This effect is obtained by adding 0.01% or more of Mo to the steel sheet, and the effect improves as the Mo content increases. However, if the Mo content exceeds 1.62%, the hot workability deteriorates and surface defects frequently occur during hot rolling. Moreover, since Mo is an expensive element, an increase in the Mo content increases the manufacturing cost. Therefore, when Mo is contained, the content range is preferably 0.01 to 1.62%. A more preferable content range is 0.30 to 1.62%, and most preferably 0.40 to 1.20%.
  • the Mo content is preferably 0.30 to 1.40%. More preferably, it is in the range of 0.40 to 1.00%.
  • the said component in the case of containing the 1 type (s) or 2 or more types chosen from Zr, REM, W, Co, Mg, Ca is demonstrated.
  • Zr 0.01-0.20%
  • Zr binds to C and N and has the effect of suppressing sensitization. This effect is obtained when the Zr content is 0.01% or more.
  • the content of Zr exceeds 0.20%, the workability of the steel sheet decreases. Further, since Zr is an expensive element, an increase in the Zr content increases the manufacturing cost. Therefore, when Zr is contained, the content range is preferably 0.01 to 0.20%.
  • REM 0.001 to 0.100% REM has the effect of improving oxidation resistance. This effect is obtained by containing REM 0.001% or more. On the other hand, if REM is contained in an amount exceeding 0.100%, hot rollability is lowered and surface defects frequently occur, which is not preferable. Therefore, when it is contained, the content range of REM is preferably 0.001 to 0.100%, and more preferably 0.001 to 0.050%.
  • W 0.01-0.20% W has the effect of improving the corrosion resistance like Mo. This effect is obtained when the W content is 0.01% or more. On the other hand, when the amount of W exceeds 0.20%, the strength increases, and the productivity decreases due to an increase in rolling load or the like. Therefore, the range of W content is preferably 0.01 to 0.20%, and more preferably 0.01 to 0.10%.
  • Co 0.01-0.20%
  • Co has the effect of improving the corrosion resistance. This effect is obtained when the Co content is 0.01% or more.
  • the range of Co content is preferably 0.01 to 0.20%, and more preferably 0.01 to 0.10%.
  • Mg 0.0001 to 0.0010%
  • Mg is an element that improves the equiaxed crystal ratio of the slab and is effective in improving formability and toughness. This effect is obtained when the Mg content is 0.0001% or more. On the other hand, if the Mg content exceeds 0.0010%, Mg-based inclusions increase and the surface properties are deteriorated. Therefore, the content range of Mg is preferably 0.0001 to 0.0010%, more preferably 0.0002 to 0.0004%.
  • Ca 0.0003 to 0.0030%
  • Ca is an effective component for preventing nozzle clogging due to precipitation of Ti-based inclusions that are likely to occur during continuous casting. The effect is obtained when the Ca content is 0.0003% or more. However, when the Ca content exceeds 0.0030%, the corrosion resistance decreases due to the generation of CaS. Therefore, the preferable content range of Ca is 0.0003 to 0.0030%, more preferably 0.0005 to 0.0020%, and most preferably 0.0005 to 0.0015%. .
  • the manufacturing method of the ferritic stainless steel of this invention is not limited to the following embodiment.
  • 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, AOD, etc., and then preferably cast by a continuous casting method to obtain 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 750 to 900 ° C.
  • a hot-rolled sheet can perform hot-rolled sheet annealing as needed. When hot-rolled sheet annealing is performed, it is preferable to perform short-term continuous annealing in the temperature range of 850 to 1150 ° C.
  • 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%.
  • recrystallization annealing finish annealing at 800 to 1100 ° C.
  • the finish of the cold-rolled sheet can be 2D, 2B, BA and various types of polishing defined by Japan industrial Standard (JIS) G4305.
  • the steel plate as used in this invention shall contain a steel strip and foil material.
  • Example 1 Molten steel having the composition shown in Table 3 (the balance being Fe) was melted by a converter and secondary refining (VOD), and a slab was formed by a continuous casting method. After these slabs were heated to 1120 ° C., hot rolling was performed at a finishing temperature of 800 ° C. to obtain hot rolled sheets having a thickness of 4.0 mm. These hot-rolled sheets were subjected to hot-rolled sheet annealing at 940 ° C. ⁇ 60 sec, and then pickled and cold-rolled to obtain cold-rolled sheets. Next, these cold-rolled plates were subjected to finish annealing at 900 ° C.
  • ElL, ElD, and ElC represent elongations in the L direction, the D direction, and the C direction, respectively.
  • rL, rD, and rC represent r values in the L direction, the D direction, and the C direction, respectively.
  • Corrosion resistance A test piece of 60 mm x 80 mm was cut out from the obtained cold-rolled annealed plate, the surface was polished with # 600 count, a test piece for corrosion resistance evaluation was produced, and corrosion resistance evaluation was performed by a combined cycle corrosion test. In the combined cycle corrosion test, the above-described corrosion test cycle was performed 30 times, and an area ratio of 20% or more was rejected, and less than 20% was determined to be acceptable.
  • Example 2 Molten steel having the composition shown in Table 4 was melted by a converter and secondary refining (VOD) to obtain a slab by a continuous casting method. After these slabs were heated to 1120 ° C., hot rolling was performed at a finishing temperature of 800 ° C. to obtain hot rolled sheets having a thickness of 4.0 mm. These hot-rolled sheets were subjected to hot-rolled sheet annealing at 1020 ° C. ⁇ 60 sec, followed by pickling and cold rolling to obtain cold-rolled sheets. Next, these cold-rolled plates were subjected to finish annealing at 1000 ° C. ⁇ 40 sec, and then pickled to obtain cold-rolled annealed pickled plates having a thickness of 0.7 mm. About the obtained cold-rolled annealing pickling board, forming processability and corrosion resistance evaluation were performed. The evaluation method is as follows.
  • Table 5 shows the results obtained in Example 1, and Table 6 shows the results obtained in Example 2.
  • the present invention by optimizing the component composition, in particular, the V and B contents, a ferritic stainless steel sheet having excellent forming processability and corrosion resistance can be produced, and an industrially remarkable effect is achieved.

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Abstract

La présente invention se rapporte à une tôle d'acier inoxydable ferritique qui présente une excellente aptitude au façonnage et une excellente résistance à la corrosion. La tôle d'acier inoxydable ferritique est caractérisée en ce qu'elle contient, en % en masse, entre 0,003 et 0,013 % de carbone, entre 0,01 et 0,95 % de silicium, entre 0,01 et 0,40 % de manganèse, entre 0,020 et 0,040 % de phosphore, une quantité de soufre inférieure ou égale à 0,010 %, entre 0,01 et 0,45 % d'aluminium, entre 14,5 et 21,5 % de chrome, entre 0,01 et 0,60 % de nickel, et entre 0,005 et 0,012 % d'azote. La tôle d'acier inoxydable ferritique est en outre caractérisée : en ce qu'elle contient entre 0,010 et 0,040 % de vanadium et entre 0,0001 et 0,0010 % de bore dans une plage qui satisfait la relation V/B ≥ 15,0; en ce qu'elle contient soit une quantité de titane comprise entre 0,20 et 0,40 %, soit une quantité de niobium comprise entre 0,40 et 0,60 %, ou en ce qu'elle contient à la fois du titane et du niobium dans une plage dans laquelle la quantité totale de titane et de niobium se situe entre 0,40 et 0,70 %; et en ce que le reste comprend du fer et des impuretés inévitables.
PCT/JP2013/001824 2013-03-18 2013-03-18 Tôle d'acier inoxydable ferritique WO2014147655A1 (fr)

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JP2013553688A JP5505575B1 (ja) 2013-03-18 2013-03-18 フェライト系ステンレス鋼板
CN201380051384.3A CN104685086B (zh) 2013-03-18 2013-03-18 铁素体系不锈钢板
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WO2016092713A1 (fr) * 2014-12-11 2016-06-16 Ｊｆｅスチール株式会社 Acier inoxydable, et procédé de fabrication de celui-ci
US20170073800A1 (en) * 2014-05-14 2017-03-16 Jfe Steel Corporation Ferritic stainless steel
CN107002200A (zh) * 2014-12-11 2017-08-01 杰富意钢铁株式会社 铁素体系不锈钢及其制造方法
JP2020015945A (ja) * 2018-07-25 2020-01-30 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼板およびその製造方法

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US10400318B2 (en) * 2014-05-14 2019-09-03 Jfe Steel Corporation Ferritic stainless steel
JP5900717B1 (ja) * 2014-12-11 2016-04-06 Ｊｆｅスチール株式会社 ステンレス鋼板およびその製造方法
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