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WO2018198834A1 - Tôle d'acier inoxydable ferritique et son procédé de fabrication - Google Patents

Tôle d'acier inoxydable ferritique et son procédé de fabrication Download PDF

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Publication number
WO2018198834A1
WO2018198834A1 PCT/JP2018/015578 JP2018015578W WO2018198834A1 WO 2018198834 A1 WO2018198834 A1 WO 2018198834A1 JP 2018015578 W JP2018015578 W JP 2018015578W WO 2018198834 A1 WO2018198834 A1 WO 2018198834A1
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content
hot
stainless steel
steel sheet
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PCT/JP2018/015578
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English (en)
Japanese (ja)
Inventor
修司 西田
知洋 石井
正崇 吉野
光幸 藤澤
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Ｊｆｅスチール株式会社
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Priority claimed from JP2018039384A external-priority patent/JP6432701B2/ja
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to US16/607,420 priority Critical patent/US11401573B2/en
Priority to KR1020197031020A priority patent/KR102286876B1/ko
Priority to CN201880026797.9A priority patent/CN110546293B/zh
Publication of WO2018198834A1 publication Critical patent/WO2018198834A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a ferritic stainless steel sheet having excellent corrosion resistance and excellent formability and ridging resistance.
  • Ferritic stainless steel sheet does not contain much Ni, so it is cheaper and more price stable than austenitic stainless steel sheet, and it is also a material with excellent rust resistance. It is used for various applications such as transportation equipment and home appliances. In particular, since it has magnetism unlike an austenitic stainless steel sheet, it is increasingly applied to cooking utensils that are compatible with the IH (induction heating) system. Most cooking utensils represented by pans and the like are formed by overhanging. Therefore, sufficient elongation is required for molding into a predetermined shape.
  • the ferritic stainless steel sheet has a problem that surface irregularities (riding) that often impairs the appearance of the surface occur during forming.
  • a polishing step is necessary to remove irregularities after molding. That is, when large ridging occurs, there is a problem that the manufacturing cost increases.
  • ferritic stainless steel sheets tend to have larger ridging as they are subjected to greater strain, i.e., more severely processed.
  • ferritic stainless steel sheets that can be processed more severely than before have been demanded. That is, a ferritic stainless steel sheet having a higher elongation is desired.
  • household cooking utensils are also required to reduce manufacturing costs. That is, a ferritic stainless steel sheet with reduced ridging that causes an increase in manufacturing cost is also required. From these facts, a ferritic stainless steel sheet having a higher elongation and having a sufficiently small ridging even when a larger strain than before is applied.
  • Patent Document 1 in Patent Document 1, C: 0.02 to 0.06%, Si: 1.0% or less, Mn: 1.0% or less, P: 0.05 %: S: 0.01% or less, Al: 0.005% or less, Ti: 0.005% or less, Cr: 11 to 30%, Ni: 0.7% or less, and 0.06 ⁇ ( C + N) ⁇ 0.12, 1 ⁇ N / C and 1.5 ⁇ 10 ⁇ 3 ⁇ (V ⁇ N) ⁇ 1.5 ⁇ 10 ⁇ 2 (C, N, and V represent mass% of each element, respectively)
  • a ferritic stainless steel sheet excellent in formability characterized by satisfying the above requirements is disclosed.
  • Patent Document 2 discloses a ferritic stainless steel sheet containing 0.15% or less C by weight and 13 to 25% Cr, and the hot-rolled sheet of this steel coexists with austenite and ferrite phase 930. By annealing within a range of 10 minutes within a range of ⁇ 990 ° C., the structure becomes a two-phase structure of a martensite phase and a ferrite phase, followed by cold rolling, and annealing a cold-rolled sheet within a range of 750-860 ° C. A method for producing a ferritic stainless steel sheet excellent in ridging resistance and workability is disclosed.
  • Patent Document 3 by mass, C: 0.005 to 0.035%, Si: 0.25 to less than 0.40%, Mn: 0.05 to 0.35%, P: 0.040 %: S: 0.01% or less, Cr: 15.5 to 18.0%, Al: 0.001 to 0.10%, N: 0.01 to 0.06%, Si and Mn Has disclosed 29.5 ⁇ Si-50 ⁇ Mn + 6 ⁇ 0, and the remainder is made of Fe and inevitable impurities.
  • the predistortion added for evaluating ridging is not described.
  • the present inventors produced a plurality of steel plates by the method described in Patent Document 2, and evaluated the ridging height when 23% pre-strain was applied by a ridging evaluation method described later. As a result, no excellent ridging resistance was obtained in any of the steel sheets.
  • the shape of the test piece used for evaluation of elongation is not described. It is a known fact that the elongation value obtained varies depending on the shape of the test piece used for evaluation.
  • the inventors prepared a plurality of steel plates by the method described in Patent Document 2, and evaluated the elongation at break of the steel plates by a tensile test method described later. As a result, excellent formability was not obtained in any steel sheet.
  • the present invention has been developed in view of the above-described present situation, and an object of the present invention is to provide a ferritic stainless steel sheet having excellent corrosion resistance, excellent formability and ridging resistance, and a method for producing the same.
  • excellent corrosion resistance means that the ridge area ratio measured by the method described below is 30% or less. More preferably, it is 20% or less.
  • the corrosion test for evaluating the corrosion resistance is performed according to JASO M609-91. First, as a test method, the test piece is polished up to No. 600 with emery polishing paper, washed with water, and then ultrasonically degreased in ethanol for 5 minutes. Thereafter, one cycle is salt spray (5% by weight NaCl aqueous solution, 35 ° C.) 2 h ⁇ dry (60 ° C., relative humidity 40%) 4 h ⁇ wet (50 ° C., relative humidity 95% or more) 2 h. To implement. After the test, appearance of the corroded surface is photographed, and the wrinkle area ratio is calculated by image analysis from the obtained photograph for a 30 mm ⁇ 30 mm region at the center of the test piece.
  • excellent formability means that the elongation at break of the steel sheet measured by the method described below is 28% or more. More preferably, it is 32% or more.
  • a JIS No. 13 B tensile test piece is collected.
  • a tensile test based on JIS Z 2241 is performed to measure the elongation at break (El).
  • the three-way average of the obtained elongation at break ((L + 2D + C) / 4, where L, D, and C are the elongation at break (%) in each direction) is calculated as the elongation at break of the steel sheet.
  • excellent ridging resistance means that the ridging height of the steel sheet surface measured by the method described below is 3.0 ⁇ m or less. More preferably, it is 2.5 ⁇ m or less. More preferably, it is 2.0 ⁇ m or less.
  • a JIS No. 5 tensile test piece is taken in parallel with the rolling direction.
  • the surface of the collected test piece is polished with # 600 emery paper, and then 23% tensile strain is applied.
  • the surface shape is measured with a laser displacement meter in the direction perpendicular to the rolling direction on the polished surface of the parallel part of the test piece. The measurement length is 16 mm per line, and the height is measured in increments of 0.05 mm.
  • a total of 50 lines are measured with an interval of each line being 0.1 mm.
  • the obtained shape data of each line is subjected to smoothing and undulation removal processing using a Hanning window function type FIR (Finite Impulse Response) bandpass filter having a high cut filter wavelength of 0.8 mm and a low cut filter wavelength of 8 mm. .
  • FIR Finite Impulse Response
  • the data of 2 mm for each end of each line is excluded, and the arithmetic average waviness Wa defined in JIS B 0601 (2001) is determined for each line. taking measurement.
  • the average value of 50 lines of this arithmetic average waviness Wa is defined as the ridging height of the steel sheet surface.
  • the present inventors have studied a ferritic stainless steel having excellent corrosion resistance, excellent formability and ridging resistance, and a method for producing the same, with respect to the above problems. As a result, the following knowledge was obtained.
  • annealing is performed in a suitable temperature range that is a two-phase region of ferrite phase and austenite phase, and further cold rolling
  • a subsequent ferritic stainless steel sheet having excellent formability and ridging resistance can be obtained by annealing the subsequent steel sheet in an appropriate temperature range for an appropriate time.
  • the C content is set to 0.030% or less
  • the Cr content is set to 14.4% or less
  • the N content is set to 0.060% or less.
  • the steel ingot having the above components is hot-rolled, followed by hot-rolled sheet annealing at 900 to 1100 ° C., which becomes a ferrite-austenite two-phase region.
  • the amount of Cr contained in the steel is sufficiently low, a sufficient amount of austenite phase is generated in the steel sheet during the hot-rolled sheet annealing. This austenite phase becomes a martensite phase during the cooling process after hot-rolled sheet annealing.
  • the hot-rolled annealed sheet containing the martensite phase By rolling the hot-rolled annealed sheet containing the martensite phase in the subsequent cold rolling, colonies (crystal grains having similar crystal orientations) that cause ridging are destroyed, and ferrite / Rolling strain is efficiently imparted to the martensite grain boundary.
  • subsequent cold-rolled sheet annealing in the present invention, as described above, because the rolling distortion is efficiently imparted, further, the amount of Cr, C amount and N amount contained in the steel is sufficiently low, Recrystallization is promoted. Due to the effect of promoting recrystallization, the cold-rolled sheet is sufficiently recrystallized in a temperature range of 780 to 830 ° C. in the ferrite single phase region, and a cold-rolled annealed sheet having excellent formability is obtained. Moreover, the cold-rolled annealing board has the outstanding ridging resistance by the effect of the colony destruction mentioned above.
  • the present invention is based on the above findings, and the gist of the present invention is as follows.
  • the balance has a component composition consisting of Fe and inevitable impurities, A ferritic stainless steel sheet having a breaking elongation of 28% or more and a ridging height of a steel sheet surface imparted with a tensile strain of 23% in the rolling direction is 3.0 ⁇ m or less.
  • each element symbol in the above formula (1) represents the content (% by mass) of each element, and the element not contained is 0. [4] Furthermore, in mass%, B: 0.0003 to 0.0030%, Mg: 0.0005 to 0.0100%, Ca: 0.0003 to 0.0030%, Y: 0.01 to 0.20%, and REM (rare earth metal): 0.001 to 0.100%
  • B 0.0003 to 0.0030%
  • Mg 0.0005 to 0.0100%
  • Ca 0.0003 to 0.0030%
  • Y 0.01 to 0.20%
  • REM rare earth metal
  • the ferritic stainless steel sheet of the present invention is, in mass%, C: 0.005 to 0.030%, Si: 0.05 to 1.00%, Mn: 0.05 to 1.00%, P: 0.00. 040% or less, S: 0.030% or less, Al: 0.001 to 0.150%, Cr: 10.8 to 14.4%, Ni: 0.01 to 2.50%, and N: 0.00. 005 to 0.060%, the balance is Fe and inevitable impurities, the elongation at break is 28% or more, and the steel sheet surface has a ridging height of 23% in the rolling direction. Is 3.0 ⁇ m or less, and is excellent in corrosion resistance, moldability and ridging resistance.
  • % which is a unit of content of a component means the mass% unless there is particular notice.
  • C 0.005 to 0.030%
  • C is an element effective for increasing the strength of steel. Furthermore, C is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. This effect can be obtained by setting the C content to 0.005% or more. However, if the C content exceeds 0.030%, the steel becomes hard and the formability decreases. Therefore, the C content is set to 0.005 to 0.030%.
  • the C content is preferably 0.007% or more, and more preferably 0.010% or more. Further, the C content is preferably 0.020% or less, more preferably 0.015% or less.
  • Si 0.05 to 1.00%
  • Si is an element useful as a deoxidizer. This effect can be obtained by setting the Si content to 0.05% or more. However, if the Si content exceeds 1.00%, the steel becomes hard and the formability decreases. Furthermore, the austenite phase produced
  • Mn 0.05 to 1.00% Mn has a deoxidizing action. Furthermore, Mn is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. These effects can be obtained by making the Mn content 0.05% or more. However, if the Mn content exceeds 1.00%, precipitation and coarsening of MnS are promoted, and this MnS becomes a starting point of rusting and the corrosion resistance is lowered. Therefore, the Mn content is 0.05 to 1.00%. The Mn content is preferably 0.10% or more, more preferably 0.15% or more. Further, the Mn content is preferably 0.80% or less, and more preferably 0.60% or less.
  • P 0.040% or less
  • P is an element that lowers corrosion resistance. Moreover, P reduces hot workability by segregating at the grain boundaries. Therefore, the P content is desirably as low as possible, and is set to 0.040% or less. Preferably, the P content is 0.030% or less.
  • S 0.030% or less S forms Mn and precipitate MnS. This MnS becomes a starting point of pits and causes a decrease in corrosion resistance. Therefore, the lower S content is desirable, and it is 0.030% or less. Preferably, the S content is 0.020% or less.
  • Al 0.001 to 0.150%
  • Al is an effective element for deoxidation. This effect is obtained when the Al content is 0.001% or more. However, if the Al content exceeds 0.150%, the steel becomes hard and the formability decreases. Therefore, the Al content is set to 0.001 to 0.150%.
  • the Al content is preferably 0.005% or more, and more preferably 0.010% or more. Moreover, Al content becomes like this. Preferably it is 0.100% or less, More preferably, it is 0.050% or less.
  • Cr 10.8 to 14.4% Cr is an element that improves the corrosion resistance by forming a passive film on the surface. If the Cr content is less than 10.8%, sufficient corrosion resistance cannot be obtained. On the other hand, if the Cr content exceeds 14.4%, the austenite phase is not sufficiently formed in the steel in the hot-rolled sheet annealing process, the ridging resistance is lowered, the steel is further hardened, and the formability is lowered. . Therefore, the Cr content is 10.8 to 14.4%.
  • the Cr content is preferably 11.0% or more, more preferably 11.5% or more, and further preferably 12.0% or more. Moreover, Cr content becomes like this. Preferably it is 14.0% or less, More preferably, it is 13.5% or less, More preferably, it is 13.0% or less.
  • Ni 0.01-2.50%
  • Ni is an element that suppresses active dissolution in a low pH environment.
  • a so-called gap structure portion in which steel plates are overlapped a low pH environment that easily causes corrosion may be formed.
  • an aqueous solution containing chloride ions that causes the steel plate to become concentrated is concentrated on the steel plate, salt is precipitated from the aqueous solution, A gap structure is formed between the steel sheets, and a low pH environment that easily causes corrosion may be formed.
  • Ni suppresses the progress of corrosion in such an environment and improves the corrosion resistance of steel.
  • Ni has a high effect on crevice corrosion resistance, and remarkably suppresses the progress of corrosion in the active dissolution state, thereby improving the corrosion resistance. Furthermore, Ni is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. This effect is obtained when the Ni content is 0.01% or more. On the other hand, if it exceeds 2.50%, the steel becomes hard and its formability decreases. Therefore, the Ni content is 0.01 to 2.50%.
  • the Ni content is preferably 0.03% or more, more preferably 0.05% or more, and further preferably 0.10% or more. Moreover, Ni content becomes like this. Preferably it is 1.20% or less, More preferably, it is 0.80% or less, More preferably, it is 0.25% or less.
  • N 0.005 to 0.060%
  • N is an element effective for increasing the strength of steel.
  • N is an element that promotes the formation of an austenite phase during hot-rolled sheet annealing and improves ridging resistance. This effect can be obtained by making the N content 0.005% or more.
  • the N content is set to 0.005 to 0.060%.
  • the N content is preferably 0.007% or more, and more preferably 0.010% or more.
  • N content becomes like this. Preferably it is 0.020% or less, More preferably, it is 0.015% or less.
  • the balance other than the above components is Fe and inevitable impurities.
  • Typical examples of the inevitable impurities mentioned here include O (oxygen), Zn, Ga, Ge, As, Ag, In, Hf, Ta, Re, Os, Ir, Pt, Au, and Pb.
  • O (oxygen) can be contained in a range of 0.02% or less. About another element, it can contain in 0.1% or less of total.
  • Co 0.01 to 0.50%
  • Co is an element that improves the crevice corrosion resistance of stainless steel. On the other hand, when it contains excessively, the effect will be saturated and workability will fall. Therefore, when Co is contained, the Co content is preferably 0.01 to 0.50%.
  • the Co content is more preferably 0.30% or less, and still more preferably 0.10% or less.
  • Cu 0.01 to 0.80%
  • Cu is an element that reinforces the passive film and improves the corrosion resistance.
  • the content is excessive, the effect is saturated, workability is further lowered, and ⁇ -Cu is liable to precipitate, resulting in a decrease in corrosion resistance. Therefore, when Cu is contained, the Cu content is preferably set to 0.01 to 0.80%.
  • the Cu content is more preferably 0.15% or more, and further preferably 0.40% or more. Further, the Cu content is more preferably 0.60% or less, and further preferably 0.45% or less.
  • Mo 0.01-0.30% Mo has the effect of improving the crevice corrosion resistance of stainless steel. On the other hand, when it contains excessively, the effect will be saturated and workability will fall. Therefore, when Mo is contained, the Mo content is preferably 0.01 to 0.30%. The Mo content is more preferably 0.20% or less, and still more preferably 0.10% or less.
  • W 0.01 to 0.50%
  • W is an element that improves the crevice corrosion resistance of stainless steel.
  • the W content is preferably set to 0.01 to 0.50%.
  • the W content is more preferably 0.03% or more, and even more preferably 0.05% or more.
  • W content becomes like this. More preferably, it is 0.30% or less, More preferably, it is 0.10% or less.
  • Ti 0.01 to 0.30%
  • Ti is an element having a high affinity with C and N, and precipitates as a carbide or nitride during hot rolling to reduce solute C and solute N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • the Ti content is preferably 0.01 to 0.30%.
  • the Ti content is more preferably 0.02% or more. Further, the Ti content is more preferably 0.10% or less, and further preferably 0.08% or less.
  • V 0.01 to 0.10%
  • V is an element having a high affinity with C and N, and precipitates as a carbide or nitride during hot rolling to reduce solid solution C and solid solution N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • generation of the austenite phase in a hot-rolled sheet annealing process will be inhibited, and ridging resistance will fall. Therefore, when V is contained, the V content is preferably 0.01 to 0.10%.
  • the V content is more preferably 0.02% or more, and further preferably 0.03% or more. Further, the V content is more preferably 0.08% or less, and still more preferably 0.05% or less.
  • Zr 0.01 to 0.10%
  • Zr is an element having a high affinity with C and N, and precipitates as carbide or nitride during hot rolling to reduce solid solution C and solid solution N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • the Zr content is preferably 0.01 to 0.10%.
  • the Zr content is more preferably 0.02% or more, and further preferably 0.03% or more. Further, the Zr content is more preferably 0.08% or less, still more preferably 0.05% or less.
  • Nb 0.01-0.30%
  • Nb is an element having a high affinity with C and N, and precipitates as a carbide or nitride during hot rolling to reduce solute C and solute N in the matrix, and workability after cold-rolled sheet annealing. There is an effect of improving.
  • the Nb content is preferably 0.01 to 0.30%.
  • the Nb content is more preferably 0.02% or more. Further, the Nb content is more preferably 0.10% or less, and further preferably 0.08% or less.
  • each element symbol in the above formula (1) represents the content (% by mass) of each element, and the element not contained is 0.
  • the content of each element is as described above in order to obtain excellent ridging resistance.
  • the value of the above formula (1) must be 0.0 or less.
  • Ti, V, Zr, and Nb have an effect of inhibiting the austenite phase generation in the hot-rolled sheet annealing process.
  • B 0.0003 to 0.0030%
  • B is an element effective for preventing embrittlement at low temperature secondary work.
  • the B content is preferably 0.0003 to 0.0030%.
  • the B content is more preferably 0.0005% or more. Further, the B content is more preferably 0.0020% or less.
  • Mg 0.0005 to 0.0100% Mg forms Mg oxide together with Al in molten steel and acts as a deoxidizer. On the other hand, when it contains excessively, the toughness of steel will fall and productivity will fall. Therefore, when Mg is contained, the Mg content is preferably 0.0005 to 0.0100%.
  • the Mg content is more preferably 0.0010% or more. Moreover, Mg content becomes like this. More preferably, it is 0.0050% or less, More preferably, it is 0.0030% or less.
  • Ca 0.0003 to 0.0030%
  • Ca is an element that improves hot workability.
  • the toughness of steel will fall and productivity will fall, and also corrosion resistance will fall by precipitation of CaS. Therefore, when Ca is contained, the Ca content is preferably 0.0003 to 0.0030%.
  • the Ca content is more preferably 0.0010% or more. Further, the Ca content is more preferably 0.0020% or less.
  • Y 0.01-0.20%
  • Y is an element that decreases the viscosity of molten steel and improves cleanliness. On the other hand, when it contains excessively, the effect will be saturated and workability will fall. Therefore, when Y is contained, the Y content is preferably 0.01 to 0.20%. The Y content is more preferably 0.10% or less.
  • REM rare earth metal
  • REM rare earth metal: elements having atomic numbers 57 to 71 such as La, Ce, and Nd
  • the REM content is preferably 0.001 to 0.100%.
  • the REM content is more preferably 0.005% or more.
  • the REM content is more preferably 0.05% or less.
  • Sn 0.001 to 0.500%
  • Sn is effective in improving ridging by promoting deformation band generation during rolling.
  • the Sn content is preferably 0.001 to 0.500%.
  • the Sn content is more preferably 0.003% or more. Further, the Sn content is more preferably 0.200% or less.
  • Sb 0.001 to 0.500%
  • Sb is effective in improving ridging by promoting deformation band generation during rolling.
  • the Sb content is preferably 0.001 to 0.500%.
  • the Sb content is more preferably 0.003% or more.
  • the Sb content is more preferably 0.200% or less.
  • the steel having the above component composition is melted by a known method such as a converter, electric furnace, vacuum melting furnace or the like, and is made into a steel material (steel slab) by a continuous casting method or an ingot-bundling method.
  • This steel material is heated to 1000 ° C. or more and 1200 ° C. or less, and then hot-rolled to a sheet thickness of 2.0 to 6.0 mm under a finishing temperature of 700 ° C. to 1000 ° C.
  • the hot-rolled sheet thus prepared is annealed by hot-rolled sheet holding for 5 seconds to 15 minutes at a temperature range of 900 ° C. or higher and 1100 ° C.
  • Cold-rolled sheet annealing is performed in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes.
  • pickling is performed in a pickling line to remove scale.
  • Skin pass rolling may be performed on the cold-rolled annealed pickled plate from which the scale has been removed.
  • a process in which hot-rolled sheet annealing is performed by holding a hot-rolled sheet in a temperature range of 900 ° C. to 1100 ° C. for 5 seconds to 15 minutes to form a hot-rolled annealed sheet. Annealing is performed in the phase region or a temperature region close thereto, and a sufficient amount of austenite phase is not formed in the hot-rolled sheet. On the other hand, even when the hot-rolled sheet annealing temperature exceeds 1100 ° C., annealing is performed in a ferrite single phase region or a temperature region close thereto, and a sufficient amount of austenite phase is not generated in the hot-rolled plate.
  • hot-rolled sheet annealing is performed by holding at a temperature range of 900 ° C. to 1100 ° C.
  • the hot-rolled sheet annealing is preferably performed in a temperature range of 950 ° C. or higher. Moreover, it is preferable to perform hot-rolled sheet annealing in the temperature range of 1050 degrees C or less.
  • the hot-rolled sheet annealing is preferably held for 20 seconds or more in the above temperature range. Moreover, it is preferable that hot-rolled sheet annealing is hold
  • the hot-rolled annealed sheet is cold-rolled to obtain a cold-rolled sheet.
  • the conditions for cold rolling need not be specified, and can be performed according to a conventional method. As an example, in cold rolling, cold rolling with a total rolling reduction of 40 to 90% can be performed.
  • Cold-rolled sheet annealing process in which the cold-rolled sheet is held at a temperature range of 780 ° C. to 830 ° C. for 5 seconds to 5 minutes. If the cold-rolled sheet annealing temperature is less than 780 ° C., an unrecrystallized structure remains in the steel sheet. As a result, sufficient moldability cannot be obtained. On the other hand, when the cold-rolled sheet annealing temperature exceeds 830 ° C., an austenite phase is generated in the steel at the time of annealing, and a martensite phase is present in the structure after annealing, so that sufficient formability cannot be obtained.
  • cold-rolled sheet annealing is performed in a temperature range of 780 ° C. or higher and 830 ° C. or lower for 5 seconds to 5 minutes.
  • Cold-rolled sheet annealing is preferably performed in a temperature range of 790 ° C or higher. Moreover, it is preferable to perform cold-rolled sheet annealing in a temperature range of 810 ° C. or lower. Cold-rolled sheet annealing is preferably maintained for 20 seconds or more in the above temperature range. Moreover, it is preferable that cold-rolled sheet annealing is hold
  • Each of the hot-rolled sheets described above is divided into five sheets, and four of them are annealed in the atmosphere at temperatures of 830 to 1200 ° C. shown in Table 1 for 20 seconds to form hot-rolled annealed sheets. Then, the scale was removed to obtain a material for cold rolling. In addition, the remaining one sheet obtained by dividing each hot-rolled sheet is annealed at 800 ° C. for 8 hours in an air atmosphere to form a hot-rolled annealed sheet, and both the front and back surfaces are ground to remove the scales. The material.
  • Each obtained cold rolling material was then cold rolled into a cold rolled sheet having a thickness of 1.0 mm.
  • the obtained cold-rolled plate was annealed at 800 ° C. for 20 seconds in an air atmosphere to obtain a cold-rolled annealed plate.
  • the obtained cold-rolled annealed plate was pickled by a normal method to obtain a ferritic stainless steel cold-rolled annealed pickled plate.
  • a steel plate having a length of 80 mm and a width of 60 mm is cut out from the cold-rolled annealed pickling plate produced above by grinding, then the surface is polished to No. 600 with emery polishing paper, washed with water, and in ethanol for over 5 minutes. Sonic degreasing was performed to obtain a test piece. A corrosion test was performed on the obtained test piece in accordance with JASO M609-91 to evaluate the corrosion resistance. The test piece was placed in the test apparatus at an inclination of 60 ° with the length direction being vertical after covering the end and the back with vinyl tape.
  • One cycle was salt spray (5 mass% NaCl aqueous solution, 35 ° C.) 2 h ⁇ drying (60 ° C., relative humidity 40%) 4 h ⁇ wet (50 ° C., relative humidity 95% or more) 2 h, and 3 cycles were performed. After the test, appearance of the corroded surface was photographed, and the wrinkle area ratio was calculated from the obtained photograph by image analysis for a 30 mm ⁇ 30 mm region at the center of the test piece. ⁇ The area ratio was 20% or less “ ⁇ ” (pass: excellent), 20% to 30% or less “ ⁇ ” (pass), more than 30% Evaluated as “ ⁇ ” (failed).
  • ⁇ Moldability> Furthermore, from the manufactured cold-rolled annealed pickled plate, a No. 13B test piece defined in JIS Z 2241 is rolled in the rolling direction (L direction), 45 ° direction (D direction) with respect to the rolling direction, and rolling direction. Each sample was sampled so that the direction perpendicular to (C direction) was the length of the test piece, and a tensile test was performed at room temperature in accordance with the same standard to evaluate the moldability.
  • smoothing and swell removal processing were performed using a Hanning window function type FIR (Finite Impulse Response) bandpass filter having a high cut filter wavelength of 0.8 mm and a low cut filter wavelength of 8 mm.
  • FIR Finite Impulse Response
  • the data of 2 mm for each end of each line is excluded, and the arithmetic average waviness Wa defined in JIS B 0601 (2001) is determined for each line. It was measured. The interval between each line was 0.1 mm, and a total of 50 lines were measured. And the average value of 50 lines of this arithmetic mean wave
  • the results obtained are shown in Table 1.
  • the evaluation of corrosion resistance is “O” or “ ⁇ ”
  • the evaluation of moldability is “O” or “ ⁇ ”
  • the evaluation of ridging resistance is “ ⁇ ” or “O”.
  • Test No. The Comparative Example 2-35 was inferior in corrosion resistance because the Cr content was lower than the component range of the present invention.
  • Test No. The comparative example 2-36 was inferior in ridging resistance because the Cr content was higher than the component range of the present invention.
  • Test No. The Comparative Example 2-37 was inferior in corrosion resistance because the Ni content was lower than the component range of the present invention.
  • Test No. The comparative example of 2-38 was inferior in moldability because the Ni content was higher than the component range of the present invention.
  • the comparative examples 2-40 and 2-42 were inferior in moldability because the contents of C and N were higher than the component range of the present invention.
  • Test No. The comparative example 2-43 was inferior in moldability and ridging resistance because the Si content was higher than the component range of the present invention.
  • Test No. The comparative example 2-44 was inferior in ridging resistance because the Cr content was higher than the component range of the present invention.
  • Test No. The comparative example 2-52 was inferior in ridging resistance because the Ti content was higher than the component range of the present invention.
  • the comparative examples of 2-53, 2-54, and 2-56 were inferior in ridging resistance because the value of the formula (1) exceeded 0.0. Test No.
  • Comparative Example 2-55 the Cr content was lower than the component range of the present invention, and the value of formula (1) exceeded 0.0, so the corrosion resistance and ridging resistance were inferior. Test No. In Comparative Example 2-57, the ridging resistance was inferior because the Nb content was higher than the component range of the present invention.
  • the ferritic stainless steel sheet of the present invention is excellent in corrosion resistance, and further excellent in formability and ridging resistance. It can be suitably used for applications such as piping and building materials.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne : une tôle d'acier inoxydable ferritique présentant une excellente résistance à la corrosion, une excellente aptitude au moulage et une excellente résistance au striage ; et son procédé de production. La présente tôle d'acier inoxydable ferritique est pourvue d'une composition de composant qui comprend, en % en masse, 0,005-0,030 % de C, 0,05-1,00 % de Si, 0,05-1,00 % de Mn, 0 040 % ou moins de P, 0 030 % ou moins de S, 0,001-0,150 % d'Al, 10,8-14,4 % de Cr, 0,01-2,50 % de Ni, et 0,005-0,060 % de N, le reste comprenant du Fe et des impuretés inévitables. La tôle d'acier inoxydable ferritique a un allongement à la rupture de 28 % ou plus. La hauteur de couverture de la surface de la tôle d'acier à laquelle la contrainte de traction à 23 % a été appliquée dans la direction de laminage est de 3,0 µm ou moins.
PCT/JP2018/015578 2017-04-25 2018-04-13 Tôle d'acier inoxydable ferritique et son procédé de fabrication WO2018198834A1 (fr)

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US16/607,420 US11401573B2 (en) 2017-04-25 2018-04-13 Ferritic stainless steel sheet and method for manufacturing the same
KR1020197031020A KR102286876B1 (ko) 2017-04-25 2018-04-13 페라이트계 스테인리스 강판 및 그의 제조 방법
CN201880026797.9A CN110546293B (zh) 2017-04-25 2018-04-13 铁素体系不锈钢板及其制造方法

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2021056602A1 (fr) * 2019-09-24 2021-04-01 王平 Acier inoxydable ferritique contenant du nickel fondu à partir de minerai de nickel latérite, et son procédé de préparation
CN113767181A (zh) * 2019-05-29 2021-12-07 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法
WO2022085708A1 (fr) * 2020-10-23 2022-04-28 日鉄ステンレス株式会社 Acier inoxydable ferritique et procédé de fabrication d'acier inoxydable ferritique
CN116145030A (zh) * 2022-12-23 2023-05-23 鞍钢股份有限公司 三代核电站关键设备支撑用铁素体不锈钢钢板及制造方法
CN116240456A (zh) * 2022-12-23 2023-06-09 鞍钢股份有限公司 核电站关键设备支撑用马氏体不锈钢板及其制造方法

Citations (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10121205A (ja) * 1995-09-26 1998-05-12 Kawasaki Steel Corp 面内異方性が小さく耐リジング性に優れるフェライト系ステンレス鋼板およびその製造方法
JP2001271143A (ja) * 2000-03-28 2001-10-02 Nisshin Steel Co Ltd 耐リジング性に優れたフェライト系ステンレス鋼及びその製造方法
JP2004002974A (ja) * 2002-03-27 2004-01-08 Nippon Steel Corp フェライト系ステンレス鋼の鋳片及び鋼板ならびにそれらの製造方法
JP2006104498A (ja) * 2004-10-01 2006-04-20 Nisshin Steel Co Ltd 加工性および低温靭性に優れた高純度フェライト系鋼板
JP2006328524A (ja) * 2005-01-24 2006-12-07 Nippon Steel & Sumikin Stainless Steel Corp 成形時の面内異方性が小さく耐リジング性及び耐肌荒れ性に優れたフェライト系ステンレス鋼薄板及びその製造方法
JP2008138270A (ja) * 2006-12-05 2008-06-19 Nippon Steel & Sumikin Stainless Steel Corp 加工性に優れた高強度ステンレス鋼板およびその製造方法
JP2009235555A (ja) * 2008-03-28 2009-10-15 Nippon Steel & Sumikin Stainless Steel Corp 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板
WO2014045542A1 (fr) * 2012-09-24 2014-03-27 Ｊｆｅスチール株式会社 Tôle d'acier inoxydable ferritique qui est facilement usinée
WO2014119796A1 (fr) * 2013-02-04 2014-08-07 新日鐵住金ステンレス株式会社 Feuille d'acier inoxydable ferritique ayant une excellente aptitude au façonnage
WO2016051437A1 (fr) * 2014-10-02 2016-04-07 Ｊｆｅスチール株式会社 Acier inoxydable ferritique et son procédé de production
WO2016068139A1 (fr) * 2014-10-31 2016-05-06 新日鐵住金ステンレス株式会社 Plaque d'acier inoxydable à base de ferrite, tube d'acier et son procédé de production
WO2016092714A1 (fr) * 2014-12-11 2016-06-16 Ｊｆｅスチール株式会社 Acier inoxydable ferritique, et procédé de fabrication de celui-ci
JP2016113670A (ja) * 2014-12-16 2016-06-23 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼およびその製造方法
WO2017002148A1 (fr) * 2015-07-02 2017-01-05 Ｊｆｅスチール株式会社 Matériau de type feuille d'acier inoxydable laminée à froid, son procédé de fabrication et feuille d'acier laminée à froid
JP2017508067A (ja) * 2013-12-24 2017-03-23 ポスコＰｏｓｃｏ 成形性及び耐リッジング性が向上したフェライト系ステンレス鋼及びその製造方法

Patent Citations (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10121205A (ja) * 1995-09-26 1998-05-12 Kawasaki Steel Corp 面内異方性が小さく耐リジング性に優れるフェライト系ステンレス鋼板およびその製造方法
JP2001271143A (ja) * 2000-03-28 2001-10-02 Nisshin Steel Co Ltd 耐リジング性に優れたフェライト系ステンレス鋼及びその製造方法
JP2004002974A (ja) * 2002-03-27 2004-01-08 Nippon Steel Corp フェライト系ステンレス鋼の鋳片及び鋼板ならびにそれらの製造方法
JP2006104498A (ja) * 2004-10-01 2006-04-20 Nisshin Steel Co Ltd 加工性および低温靭性に優れた高純度フェライト系鋼板
JP2006328524A (ja) * 2005-01-24 2006-12-07 Nippon Steel & Sumikin Stainless Steel Corp 成形時の面内異方性が小さく耐リジング性及び耐肌荒れ性に優れたフェライト系ステンレス鋼薄板及びその製造方法
JP2008138270A (ja) * 2006-12-05 2008-06-19 Nippon Steel & Sumikin Stainless Steel Corp 加工性に優れた高強度ステンレス鋼板およびその製造方法
JP2009235555A (ja) * 2008-03-28 2009-10-15 Nippon Steel & Sumikin Stainless Steel Corp 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板
WO2014045542A1 (fr) * 2012-09-24 2014-03-27 Ｊｆｅスチール株式会社 Tôle d'acier inoxydable ferritique qui est facilement usinée
WO2014119796A1 (fr) * 2013-02-04 2014-08-07 新日鐵住金ステンレス株式会社 Feuille d'acier inoxydable ferritique ayant une excellente aptitude au façonnage
JP2017508067A (ja) * 2013-12-24 2017-03-23 ポスコＰｏｓｃｏ 成形性及び耐リッジング性が向上したフェライト系ステンレス鋼及びその製造方法
WO2016051437A1 (fr) * 2014-10-02 2016-04-07 Ｊｆｅスチール株式会社 Acier inoxydable ferritique et son procédé de production
WO2016068139A1 (fr) * 2014-10-31 2016-05-06 新日鐵住金ステンレス株式会社 Plaque d'acier inoxydable à base de ferrite, tube d'acier et son procédé de production
WO2016092714A1 (fr) * 2014-12-11 2016-06-16 Ｊｆｅスチール株式会社 Acier inoxydable ferritique, et procédé de fabrication de celui-ci
JP2016113670A (ja) * 2014-12-16 2016-06-23 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼およびその製造方法
WO2017002148A1 (fr) * 2015-07-02 2017-01-05 Ｊｆｅスチール株式会社 Matériau de type feuille d'acier inoxydable laminée à froid, son procédé de fabrication et feuille d'acier laminée à froid

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113767181A (zh) * 2019-05-29 2021-12-07 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法
WO2021056602A1 (fr) * 2019-09-24 2021-04-01 王平 Acier inoxydable ferritique contenant du nickel fondu à partir de minerai de nickel latérite, et son procédé de préparation
WO2022085708A1 (fr) * 2020-10-23 2022-04-28 日鉄ステンレス株式会社 Acier inoxydable ferritique et procédé de fabrication d'acier inoxydable ferritique
JPWO2022085708A1 (fr) * 2020-10-23 2022-04-28
JP7374338B2 (ja) 2020-10-23 2023-11-06 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびフェライト系ステンレス鋼の製造方法
CN116145030A (zh) * 2022-12-23 2023-05-23 鞍钢股份有限公司 三代核电站关键设备支撑用铁素体不锈钢钢板及制造方法
CN116240456A (zh) * 2022-12-23 2023-06-09 鞍钢股份有限公司 核电站关键设备支撑用马氏体不锈钢板及其制造方法
CN116145030B (zh) * 2022-12-23 2023-12-15 鞍钢股份有限公司 三代核电站关键设备支撑用铁素体不锈钢钢板及制造方法

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