WO2020084987A1 - Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé de production d'une telle tôle d'acier - Google Patents

Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé de production d'une telle tôle d'acier Download PDF

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WO2020084987A1
WO2020084987A1 PCT/JP2019/037430 JP2019037430W WO2020084987A1 WO 2020084987 A1 WO2020084987 A1 WO 2020084987A1 JP 2019037430 W JP2019037430 W JP 2019037430W WO 2020084987 A1 WO2020084987 A1 WO 2020084987A1
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hot
content
steel sheet
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PCT/JP2019/037430
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English (en)
Japanese (ja)
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正崇 吉野
佳士 井上
法剛 高
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Ｊｆｅスチール株式会社
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Priority to US17/286,657 priority Critical patent/US20210363604A1/en
Priority to KR1020237031897A priority patent/KR20230142630A/ko
Priority to MX2021004713A priority patent/MX2021004713A/es
Priority to CA3114743A priority patent/CA3114743C/fr
Priority to JP2020506852A priority patent/JP7038799B2/ja
Priority to CN201980069792.9A priority patent/CN112888802A/zh
Priority to KR1020217011576A priority patent/KR20210064281A/ko
Publication of WO2020084987A1 publication Critical patent/WO2020084987A1/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
    • C22C38/002—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
    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • 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
    • 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
    • C21D8/0247—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
    • C21D9/46—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
    • C22C38/001—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
    • C22C38/005—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a hot rolled annealed ferritic stainless steel sheet having excellent workability suitable for application to flanges and the like, and a method for manufacturing the same.
  • Exhaust gas generated by the engine is released to the atmosphere via exhaust gas recirculation (Exhaust Gas Recirculation, EGR) system and exhaust system parts such as muffler.
  • EGR exhaust Gas Recirculation
  • Each component of such an automobile exhaust system is fastened via a flange in order to prevent gas leakage.
  • the flange applied to the exhaust system component needs to have sufficient dimensional accuracy as a fastening component.
  • stainless steel is superior to ordinary steel in high-temperature strength and corrosion resistance, especially high-strength ferritic stainless steel sheet with a relatively small coefficient of thermal expansion and in which thermal stress is unlikely to occur (for example, ASTM A240 / 240M-S40975 ( 11 mass% Cr-Ti-Ni steel having a large plate thickness (for example, a plate thickness of 5 mm or more) is being applied.
  • the flange used for the exhaust system has a large plate thickness (often 5 mm or more), there is a problem that the flange part may not be manufactured properly due to cracking during punching during manufacturing the flange.
  • Patent Document 1 in mass%, C: 0.015% or less, Si: 0.01 to 0.4%, Mn: 0.01 to 0.8%, P: 0.04% or less, S: 0.01% or less, Cr: 14.0 to less than 18.0%, Ni: 0.05 to 1%, Nb: 0.3 to 0.6%, Ti: 0.05% or less, N: 0.020% or less, Al: 0.10% or less, B: 0.0002 to 0.0020%, the balance being Fe and unavoidable impurities, and Nb, C and Disclosed is a ferritic stainless hot rolled steel sheet having a N content satisfying Nb / (C + N) ⁇ 16, a Charpy impact value at 0 ° C. of 10 J / cm 2 or more, and a sheet thickness of 5.0 to 9.0 mm. Has been done.
  • the inventors of the present invention prototyped a ferritic stainless steel plate having a plate thickness of 10 mm having a steel component conforming to ASTM A240 / 240M-S40975 by using the method disclosed in Patent Document 1, and provided a flange having a 20 mm ⁇ hole with a flange. It was manufactured by punching with a clearance of 10%. As a result, none of the cracks due to punching occurred, but the outer peripheral dimension and / or the central hole dimension of the flange may exceed the allowable tolerance of the part, and it may not be sufficient to apply to thick flanges. It became clear.
  • the present invention solves the above problems, has sufficient corrosion resistance, and can obtain a predetermined dimensional accuracy without cracking during punching into a thick flange, and a ferritic stainless steel with excellent punching workability.
  • An object of the present invention is to provide annealed steel sheet and a manufacturing method thereof.
  • the present inventors conducted a detailed study to solve the above problems.
  • the steel sheet should have a ferrite single-phase structure and its average crystal grain size should be controlled within the range of 5 to 20 ⁇ m. I found out that.
  • hot rolling is performed on a ferritic stainless steel having an appropriate component, and the obtained hot rolled steel sheet is subjected to appropriate conditions to be a ferrite single phase region, specifically, 600 ° C or higher and lower than 750 ° C. It has been found that by performing hot-rolled sheet annealing for 1 minute to 24 hours, the metal structure can be controlled to a ferrite single phase and the average crystal grain size can be controlled to the range of 5 to 20 ⁇ m.
  • the present invention has been made based on the above findings, and has the following gist. [1]% by mass, C: 0.001 to 0.020%, Si: 0.05 to 1.00%, Mn: 0.05 to 1.00%, P: 0.04% or less, S: 0.01% or less, Al: 0.01 to 0.10%, Cr: 10.0 to 20.0%, Ni: 0.50 to 2.00%, Ti: 0.10 to 0.40%, N: 0.001 to 0.020%, a balance of Fe and unavoidable impurities in the balance, and a ferritic stainless steel with a metallic structure of a ferrite single-phase structure with an average crystal grain size of 5 to 20 ⁇ m. Annealed steel sheet.
  • Sufficient corrosion resistance in the present invention means a salt water spray cycle test (salt water spray (5 mass% NaCl, 35% by mass, 35% by mass NaCl, 35% by weight) on a steel plate whose end surface is sealed after polishing the surface with # 600 emery paper.
  • salt water spray 5 mass% NaCl, 35% by mass, 35% by mass NaCl, 35% by weight
  • C., spray 2 hr ⁇ dry (60 ° C., 4 hr, relative humidity 40%) ⁇ wet (50 ° C., 2 hr, relative humidity ⁇ 95%)
  • a 100 mm ⁇ 100 mm test piece was sampled from a hot-rolled annealed steel sheet, and a hole of ⁇ 20 mm (tolerance ⁇ 0.1 mm) was formed in the center of the test piece.
  • a crank press equipped with an upper die (punch) having a 20 mm diameter columnar cutting blade and a lower die (die) having holes with a diameter of 20 mm or more, five test pieces are prepared by punching. .
  • the punching process is performed by selecting the hole diameter on the lower mold side in accordance with the thickness of the test piece plate so that the clearance between the upper mold and the lower mold is 10%.
  • the clearance (C) [%], the diameter of the hole of the die (the inner diameter of the die) (Dd) [mm] and the diameter of the punch (Dp) [mm] are also the plate thickness (t) [mm]. Including, it is expressed by the following equation (1).
  • C (Dd ⁇ Dp) ⁇ (2 ⁇ t) ⁇ 100 ... Equation (1)
  • the ferritic stainless steel hot rolled annealed steel sheet of the present invention in mass%, is C: 0.001 to 0.020%, Si: 0.05 to 1.00%, Mn: 0.05 to 1.00%, P : 0.04% or less, S: 0.01% or less, Al: 0.01 to 0.10%, Cr: 10.0 to 20.0%, Ni: 0.50 to 2.00%, Ti: 0.10 to 0.40%, N: 0.001 to 0.020%, with the balance being Fe and inevitable impurities, and having a metal structure of 5 to 20 ⁇ m in average crystal grain size. It is a ferritic stainless steel hot-rolled and annealed steel sheet having a ferrite single-phase structure.
  • ASTM A240 / 240M-S40975 (the composition of components is% by mass, C ⁇ 0.03%, Si ⁇ 1.00%, Mn ⁇ 1.00%, P ⁇ 0.040%, S ⁇ 0.030%, Cr: 10.5 to 11.7%, Ni: 0.50 to 1.00%, N ⁇ 0.03%, Ti: 6 ⁇ (C + N) to 0.74% , The balance Fe and unavoidable impurities.)
  • Using various ferritic stainless steel plates with a plate thickness of 10 mm a flange having a hole of 20 mm ⁇ was punched with a clearance of 10%. As a result, it was found that the cracks due to punching did not occur in either case, but the outer peripheral dimension of the flange and / or the central hole dimension may exceed the allowable tolerance of the component.
  • the present inventors examined in detail the cause that the dimensional accuracy in punching greatly differs depending on the steel sheet.
  • the average grain size of the steel sheet subjected to punching was less than 5 ⁇ m
  • the dimension of the part after punching was smaller than the allowable tolerance
  • the average grain size of the steel sheet was more than 20 ⁇ m. It was found that in the case of punching, the part size after punching tends to be larger than the allowable tolerance. From this, the present inventors can not stably obtain sufficient dimensional accuracy in the punching process, when the average crystal grain size is too small, the steel plate is too hard during the punching process. It was found that this is due to the fact that the shear surface ratio of No. 2 was small, and that when the average crystal grain size was excessively large, large sagging or burrs occurred during punching.
  • the inventors of the present invention have a method of obtaining a ferritic stainless steel sheet having a ferrite single-phase structure having an average crystal grain size of 5 to 20 ⁇ m in terms of steel composition, hot rolling method and hot rolled sheet annealing method. Diligently studied. As a result, the steel components, especially Cr and Ni contents were controlled in an appropriate range to generate an austenite phase and a ferrite phase in the hot rolling step, and then hot rolling was performed, followed by the ferrite single phase temperature range. It was found that it is effective to carry out hot-rolled sheet annealing in the appropriate temperature range.
  • the hot-rolled sheet annealing process is performed by holding the ferrite single-phase temperature range in an appropriate temperature range, specifically, 600 ° C or higher and lower than 750 ° C for 1 minute to 24 hours.
  • an appropriate temperature range specifically, 600 ° C or higher and lower than 750 ° C for 1 minute to 24 hours.
  • recrystallization of the ferrite phase existing in the metal structure after hot rolling and transformation of the martensite phase into the ferrite phase are caused to obtain a ferrite single phase structure.
  • the hot-rolled sheet annealing temperature is less than 600 ° C., recrystallization of the ferrite phase and transformation of the martensite phase into the ferrite phase become insufficient, and punching cracks due to excessive hardening of the steel sheet occur. It tends to occur.
  • the annealing temperature is 750 ° C. or higher
  • the crystal grains become excessively coarse and the average crystal grain size exceeds 20 ⁇ m, and large sagging or burrs are likely to occur during the punching process, and the predetermined dimensional accuracy during the punching process is not achieved. I can't get it. If the holding time is less than 1 minute, recrystallization of the ferrite phase and transformation of the martensite phase to the ferrite phase become insufficient, and punching cracks due to excessive hardening of the steel sheet are likely to occur.
  • the holding time exceeds 24 hours, the crystal grains become excessively coarse and the average crystal grain size exceeds 20 ⁇ m, and large sagging or burrs are likely to occur during punching, so that the prescribed dimensional accuracy can be obtained during punching. I can't. Therefore, in the present invention, it is necessary to perform hot rolled sheet annealing in the temperature range of 600 ° C. or higher and lower than 750 ° C. for 1 minute to 24 hours.
  • the metal structure is a ferrite single-phase structure
  • the average crystal grain size of the ferrite single-phase structure is 5 to 20 ⁇ m.
  • the average crystal grain size is 7 ⁇ m or more, and more preferably 10 ⁇ m or more.
  • the average crystal grain size is preferably 18 ⁇ m or less, more preferably 15 ⁇ m or less.
  • a test piece for observing a structure is taken from the center of the plate width, the cross section in the rolling direction is mirror-polished, and then measured and analyzed in the visual field including the total thickness by using the SEM / EBSD method, A boundary having an orientation difference of 15 ° or more can be defined as a grain boundary and can be obtained based on the Area method.
  • the plate thickness of the ferritic stainless steel hot-rolled annealed steel sheet of the present invention is not particularly limited, but is preferably a plate thickness applicable to a thick flange, and is preferably 5.0 mm or more, more preferably , 8.0 mm or more.
  • the plate thickness is preferably 15.0 mm or less, more preferably 13.0 mm or less.
  • C 0.001 to 0.020% If the content of C exceeds 0.020%, the workability and the corrosion resistance of the welded part are significantly reduced. The smaller the C content is, the more preferable it is from the viewpoint of corrosion resistance and workability. However, if the C content is less than 0.001%, refining takes time, which is not preferable in terms of production. Therefore, the C content is set to the range of 0.001 to 0.020%. Preferably, the C content is 0.003% or more, more preferably 0.004% or more. Further, the C content is preferably 0.015% or less, and more preferably 0.012% or less.
  • Si 0.05-1.00%
  • Si has the effect of concentrating in the oxide film formed during welding to improve the corrosion resistance of the welded portion, and is also a useful element as a deoxidizing element in the steelmaking process. These effects are obtained by containing 0.05% or more of Si, and the larger the content, the greater the effects.
  • the Si content is set to 0.05 to 1.00%.
  • the Si content is preferably 0.10% or more, more preferably 0.15% or more. Further, the Si content is preferably 0.60% or less, and more preferably 0.40% or less.
  • Mn 0.05-1.00%
  • Mn is an austenite forming element, and has an effect of increasing the amount of austenite generated during heating before rolling in the hot rolling step. It also acts as a deoxidizer. In order to obtain the effect, it is necessary to contain 0.05% or more of Mn. However, if the Mn content exceeds 1.00%, the precipitation of MnS, which is the starting point of corrosion, is promoted, and the corrosion resistance decreases. Therefore, the Mn content is set to 0.05 to 1.00%.
  • the Mn content is 0.10% or more, more preferably 0.15% or more. Further, the Mn content is preferably 0.60% or less, and more preferably 0.30% or less.
  • P 0.04% or less
  • P is an element that is inevitably contained in steel, but it is an element harmful to corrosion resistance and workability, so it is preferable to reduce it as much as possible.
  • the P content exceeds 0.04%, solid-solution strengthening significantly reduces the workability. Therefore, the P content is 0.04% or less.
  • the P content is 0.03% or less.
  • S 0.01% or less
  • S is an element that is inevitably contained in steel similarly to P, but it is an element harmful to corrosion resistance and workability, so it is preferable to reduce it as much as possible.
  • the S content exceeds 0.01%, the corrosion resistance is significantly reduced. Therefore, the S content is 0.01% or less.
  • the S content is 0.008% or less. More preferably, the S content is 0.003% or less.
  • Al 0.01 to 0.10%
  • Al is an effective deoxidizer. Furthermore, since Al has a stronger affinity for nitrogen than Cr, when nitrogen penetrates into the welded portion, it has the effect of precipitating nitrogen as Al nitride instead of Cr nitride and suppressing sensitization. These effects are obtained by containing Al by 0.01% or more. However, if Al is contained in excess of 0.10%, the meltability during welding is deteriorated and the welding workability is deteriorated, which is not preferable. Therefore, the Al content is set to the range of 0.01 to 0.10%. The Al content is preferably 0.02% or more, more preferably 0.03% or more. Further, the Al content is preferably 0.06% or less, and more preferably 0.04% or less.
  • Cr 10.0-20.0% Cr is the most important element for ensuring the corrosion resistance of stainless steel. If the content is less than 10.0%, sufficient corrosion resistance cannot be obtained in an automobile exhaust gas atmosphere. On the other hand, if Cr is contained in excess of 20.0%, even if a predetermined amount of Ni is contained, the amount of austenite phase generated in the hot rolling process is insufficient, and the metal structure is refined in the hot rolling process. The effect becomes insufficient, and the average crystal grain size after hot-rolled sheet annealing exceeds 20 ⁇ m, and a predetermined dimensional accuracy cannot be obtained during punching. Therefore, the Cr content is set in the range of 10.0 to 20.0%. Preferably, the Cr content is in the range of 10.0 to 17.0%. More preferably, the Cr content is 10.5% or more, and further preferably 11.2% or more. Further, the Cr content is more preferably 12.0% or less, and further preferably 11.7% or less.
  • Ni is an austenite-forming element and has an effect of increasing the amount of austenite generated during heating before rolling in the hot rolling step.
  • the austenite phase is generated at the time of heating in the hot rolling step by controlling the contents of Cr and Ni to predetermined amounts. Due to the formation of the austenite phase, the coarse metal structure formed during casting is refined, and the austenite phase undergoes dynamic and / or static recrystallization during hot rolling. The structure is further refined, and as a result, it contributes to the refinement of the metal structure after hot-rolled sheet annealing. These effects can be obtained by containing 0.50% or more of Ni.
  • the Ni content is 0.50 to 2.00%.
  • the Ni content is preferably 0.60% or more, more preferably 0.70% or more. More preferably, it is 0.75% or more. Further, the Ni content is more preferably 1.50% or less, and further preferably 1.00% or less.
  • Ti 0.10 to 0.40% Ti binds preferentially to C and N, suppresses the precipitation of Cr carbonitrides, lowers the recrystallization temperature, and suppresses the deterioration of corrosion resistance due to sensitization due to the precipitation of Cr carbonitrides. There is. To obtain these effects, it is necessary to contain 0.10% or more of Ti. However, if the Ti content exceeds 0.40%, coarse Ti carbonitrides are generated in the casting process, the toughness of the steel sheet is significantly reduced, and surface defects are caused, which is not preferable in manufacturing. Therefore, the Ti content is set to 0.10 to 0.40%. Preferably, the Ti content is 0.15% or more, more preferably 0.20% or more.
  • the Ti content is preferably 0.35% or less, and more preferably the Ti content is 0.30% or less. From the viewpoint of weld corrosion resistance, it is preferable to set the Ti content to satisfy the formula: Ti / (C + N) ⁇ 8 (Ti, C and N in the formula are the contents (mass%) of each element). .
  • the N content is set in the range of 0.001 to 0.020%.
  • the N content is 0.005% or more, more preferably 0.007% or more.
  • the N content is preferably 0.015% or less, and more preferably the N content is 0.012% or less.
  • the present invention is a ferritic stainless steel containing the above essential components and the balance being Fe and inevitable impurities. Furthermore, if necessary, one or more selected from Cu, Mo, W and Co, or / and further one selected from V, Nb, Zr, REM, B, Mg and Ca. Alternatively, two or more kinds may be contained within the following range. In addition, since the effects of the present invention are not impaired even if the following elements are contained below the lower limit in the range below, the effect of the present invention is not impaired when the following elements are contained below the lower limit.
  • Cu 0.01-1.00%
  • Cu is an element that is particularly effective in improving the corrosion resistance of the base material and the welded portion when an aqueous solution or weakly acidic water drops adhere. This effect is obtained when the content is 0.01% or more, and the higher the Cu content, the higher the effect.
  • the Cu content is preferably in the range of 0.01 to 1.00%. More preferably, the Cu content is 0.10% or more, and further preferably 0.30% or more. Further, the Cu content is more preferably 0.60% or less, and further preferably 0.45% or less.
  • Mo 0.01-2.00% Mo is an element that significantly improves the corrosion resistance of stainless steel. This effect is obtained when the content is 0.01% or more, and the effect is improved as the content is increased. However, if the Mo content exceeds 2.00%, the rolling load at the time of hot rolling increases, the productivity may decrease, and the steel sheet strength may excessively increase. Moreover, since Mo is an expensive element, the inclusion of a large amount increases the manufacturing cost. Therefore, when Mo is contained, the Mo content is preferably 0.01 to 2.00%. More preferably, the Mo content is 0.10% or more, and further preferably 0.30% or more. Further, the Mo content is more preferably 1.40% or less, and further preferably 0.90% or less.
  • W 0.01 to 0.20% W has an effect of improving the corrosion resistance similarly to Mo. This effect is obtained by containing 0.01% or more of W. However, if W is contained in excess of 0.20%, the strength is increased and the productivity may be decreased due to an increase in rolling load. Therefore, when W is contained, the W content is preferably in the range of 0.01 to 0.20%. More preferably, the W content is 0.05% or more. Further, more preferably, the W content is 0.15% or less.
  • Co 0.01 to 0.20%
  • Co is an element that improves toughness. This effect is obtained by containing 0.01% or more of Co. On the other hand, if the Co content exceeds 0.20%, the workability may decrease. Therefore, when Co is contained, the Co content is preferably in the range of 0.01 to 0.20%.
  • V 0.01 to 0.20%
  • V forms carbonitrides with C and N, suppresses sensitization during welding, and improves the corrosion resistance of the welded portion. This effect is obtained when the V content is 0.01% or more.
  • the V content is preferably 0.01 to 0.20%. More preferably, the V content is 0.02% or more. Further, more preferably, the V content is 0.050% or less.
  • Nb 0.01 to 0.10%
  • Nb has the effect of increasing the 0.2% proof stress by refining the crystal grains and precipitating as fine carbonitrides. These effects are obtained when the Nb content is 0.01% or more.
  • Nb also has the effect of raising the recrystallization temperature, and if the Nb content exceeds 0.10%, the annealing temperature necessary for causing sufficient recrystallization in hot-rolled sheet annealing becomes excessively high. Therefore, it may not be possible to obtain a ferrite single-phase structure having an average crystal grain size of 5 to 20 ⁇ m, which is required by the present invention, after annealing a hot rolled sheet. Therefore, when Nb is contained, the Nb content is preferably in the range of 0.01 to 0.10%. More preferably, the Nb content is 0.01 to 0.05%.
  • Zr 0.01 to 0.20%
  • Zr has the effect of binding to C and N to suppress sensitization. This effect is obtained by containing 0.01% or more of Zr.
  • the Zr content is preferably in the range of 0.01 to 0.20%. More preferably, the Zr content is in the range of 0.01 to 0.10%.
  • REM 0.001 to 0.100% REM (Rare Earth Metals) has the effect of improving the oxidation resistance, and suppresses the formation of an oxide film (welding temper color) at the welded part to suppress the formation of a Cr-deficient region immediately below the oxide film. This effect is obtained by containing REM in an amount of 0.001% or more. On the other hand, if REM is contained in excess of 0.100%, the hot workability may be deteriorated. Therefore, when REM is contained, the REM content is preferably in the range of 0.001 to 0.100%. More preferably, the REM content is in the range of 0.001 to 0.050%.
  • B 0.0002 to 0.0025%
  • B is an element effective for improving the secondary working brittleness resistance after deep drawing. This effect is obtained when the B content is 0.0002% or more. On the other hand, if B is contained in excess of 0.0025%, the workability and toughness may decrease. Therefore, when B is contained, the B content is preferably in the range of 0.0002 to 0.0025%. More preferably, the B content is 0.0003% or more. Further, more preferably, the B content is 0.0006% or less.
  • Mg 0.0005 to 0.0030%
  • Mg is an element effective for improving the equiaxed crystal ratio of the slab and improving the workability and toughness. Further, in the steel containing Ti as in the present invention, when the Ti carbonitride coarsens, the toughness decreases, but Mg also has the effect of suppressing the coarsening of the Ti carbonitride. These effects are obtained by containing 0.0005% or more of Mg. On the other hand, if the Mg content exceeds 0.0030%, the surface properties of steel may be deteriorated. Therefore, when Mg is contained, the Mg content is preferably in the range of 0.0005 to 0.0030%. More preferably, the Mg content is 0.0010% or more. Further, more preferably, the Mg content is 0.0020% or less.
  • Ca 0.0003 to 0.0030%
  • Ca is an effective component for preventing clogging of the nozzle due to crystallization of Ti-based inclusions that are likely to occur during continuous casting. The effect is obtained by containing 0.0003% or more of Ca.
  • the Ca content is preferably in the range of 0.0003 to 0.0030%. More preferably, the Ca content is 0.0005% or more. Further, the Ca content is more preferably 0.0015% or less, and further preferably 0.0010% or less.
  • the ferritic stainless steel hot-rolled annealed steel sheet of the present invention uses a steel slab having the above-mentioned composition, and obtains a hot-rolled steel sheet by an ordinary hot rolling, and further 600 ° C or more and less than 750 ° C to the hot-rolled steel sheet. It is obtained by performing hot-rolled sheet annealing for 1 minute to 24 hours.
  • molten steel composed of the above-mentioned composition is melted by a known method such as a converter, an electric furnace, a vacuum melting furnace, etc., and made into a steel material (slab) by the continuous casting method or the ingot-casting method.
  • the slab is heated at 1050 to 1250 ° C for 1 to 24 hours, or directly subjected to hot rolling as cast before the slab after casting falls below the above temperature range.
  • the winding treatment is preferably performed at 550 ° C. or higher.
  • Hot-rolled sheet annealing Hold at 600 ° C. or higher and lower than 750 ° C. for 1 minute to 24 hours
  • hot-rolled sheet annealing is performed after the hot rolling process is completed.
  • the rolling structure formed in the hot rolling process is recrystallized and the martensite phase generated in the hot rolling process is transformed into a ferrite phase without excessively coarsening the metal structure. Let In order to obtain this effect, it is necessary to perform hot-rolled sheet annealing at 600 ° C. or higher and lower than 750 ° C.
  • the annealing temperature is less than 600 ° C., recrystallization becomes insufficient, the hot rolled structure becomes fine recovery grains and the metal structure becomes excessively fine, and a predetermined dimensional accuracy cannot be obtained during punching. Further, in the metal structure after hot-rolled sheet annealing, the work structure and martensite phase remain, even if the average crystal grain size is within a predetermined range, punching cracks due to excessive hardening of the steel sheet May occur. On the other hand, when the annealing temperature is 750 ° C. or higher, the crystal grains become excessively coarse and exceed the average crystal grain size of 20 ⁇ m, and a predetermined dimensional accuracy cannot be obtained during punching.
  • hot-rolled sheet annealing is performed by holding in the temperature range of 600 ° C or higher and lower than 750 ° C for 1 minute to 24 hours.
  • the hot-rolled sheet annealing temperature is 600 ° C or higher, more preferably 640 ° C or higher.
  • the hot rolled sheet annealing temperature is 700 ° C. or lower.
  • the holding time is preferably 1 hour or longer, more preferably 6 hours or longer. Further, the preferable holding time is 20 hours or less, and more preferably 12 hours or less.
  • the method of hot-rolled sheet annealing is not particularly limited, and may be box annealing (batch annealing) or continuous annealing.
  • the obtained hot-rolled annealed steel sheet may be subjected to descaling treatment by shot blasting or pickling if necessary. Furthermore, in order to improve the surface texture, grinding or polishing may be performed. Further, the hot rolled annealed steel sheet provided by the present invention may be subjected to cold rolling and cold rolled sheet annealing thereafter.
  • Molten stainless steel having the chemical composition shown in Table 1 was melted by a 100 kg vacuum melting furnace. These steel ingots are heated at 1100 ° C. for 1 hour, hot-rolled to the plate thickness shown in Table 2 (see the plate thickness after hot rolling in Table 2), and then held at 650 ° C. for 1 h and then cooled in a furnace. A hot-rolled steel sheet was obtained by performing a winding simulation process. Then, after holding for 8 hours at the temperature shown in Table 2 (refer to the hot-rolled sheet annealing temperature in Table 2), the hot-rolled sheet was annealed to obtain a hot-rolled annealed steel sheet. The plate thickness of each of the obtained hot-rolled annealed steel plates was the same as the hot-rolled finished plate thickness. The hot rolled annealed steel sheet thus obtained was evaluated as follows.
  • a test piece for microstructure observation was sampled from the center of the plate width, the cross section in the rolling direction was mirror-polished, and then corroded for observation with an aqueous solution of picric acid-hydrochloric acid to reveal a metal structure, and the magnification was 500 times. It was determined whether the metal structure of each steel sheet was a ferrite single phase structure by distinguishing the ferrite phase and the martensite phase from the morphology of the metal structure by observing with an optical microscope of No. 2. Specifically, a region in which crystal grains are uniform and flat and a relatively bright contrast is exhibited was determined to be a ferrite phase.
  • the surface morphology peculiar to the martensite phase such as sub-grain boundaries and block boundaries was observed in the crystal grains, and a region exhibiting a darker contrast than the ferrite phase was determined to be the martensite phase.
  • F represents that the metal structure was a ferrite single phase structure.
  • the surface of the test piece was photographed after 5 cycles of the salt spray cycle test, the rusted area on the surface of the test piece was measured by image analysis, and the rusted area ratio (( Rust area / total area of test piece) ⁇ 100 [%]) was calculated.
  • a rusting area ratio of 10% or less was evaluated as excellent corrosion resistance ( ⁇ ), a value of more than 10% and 25% or less was evaluated as pass ( ⁇ ), and a value of more than 25% was evaluated as unacceptable ( ⁇ ).
  • Table 2 shows the test results together with the hot rolled sheet annealing conditions.
  • No. 1 in which the steel composition and hot-rolled sheet annealing conditions satisfy the scope of the present invention.
  • Nos. 1 to 36 in addition to the formation of an austenite phase during heating in the hot rolling process, recrystallization occurred without causing excessive coarsening of crystal grains by the predetermined hot-rolled sheet annealing, and a predetermined average crystal grain size was obtained.
  • a predetermined punching workability was obtained.
  • the corrosion resistance of the obtained hot-rolled annealed sheet it was confirmed that the rusting area ratios were all 25% or less, and that they also had sufficient corrosion resistance.
  • No. No. 44 is an example in which steel A14 having a predetermined steel composition was annealed at 806 ° C., which exceeds the range of the present invention, and the average grain size was coarsened to 34 ⁇ m, which exceeds the range of the present invention. Although it had a predetermined steel composition, the crystal grains were excessively coarse, so that significant sagging and burrs occurred during the punching process, and the predetermined punching workability was not obtained.
  • the ferritic stainless steel hot-rolled and annealed steel sheet obtained in the present invention is particularly suitable for applications requiring high workability and corrosion resistance, for example, flanges having burring portions.

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Abstract

La présente invention concerne : une tôle d'acier inoxydable ferritique laminée à chaud et recuite qui convient parfaitement à la découpe, présente une importante résistance à la corrosion, et permet d'obtenir une précision dimensionnelle prescrite sans fissuration lorsqu'elle est découpée en une bride épaisse ; et un procédé de production de la tôle d'acier inoxydable ferritique laminée à chaud et recuite. Une tôle d'acier inoxydable ferritique laminée à chaud et recuite présente une structure de ferrite à phase unique qui a une composition constitutive qui contient, en % en masse, de 0,001 % à 0,020 % de C, de 0,05 % à 1,00 % de Si, de 0,05 % à 1,00 % de Mn, pas plus de 0,04 % de P, pas plus de 0,01 % de S, de 0,01 % à 0,10 % d'Al, de 10,0 % à 20,0 % de Cr, de 0,50 % à 2,00 % de Ni, de 0,10 % à 0,40 % de Ti, et de 0,001 % à 0,020 % de N, le reste étant du Fe et des impuretés inévitables, la taille moyenne des grains cristallins de la structure métallique de la structure de ferrite à phase unique étant de 5 à 20 µm.
PCT/JP2019/037430 2018-10-25 2019-09-25 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé de production d'une telle tôle d'acier WO2020084987A1 (fr)

Priority Applications (7)

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US17/286,657 US20210363604A1 (en) 2018-10-25 2019-09-25 Hot-rolled and annealed ferritic stainless steel sheet and method for producing the same
KR1020237031897A KR20230142630A (ko) 2018-10-25 2019-09-25 페라이트계 스테인리스 열연 어닐링 강판 및 그 제조 방법
MX2021004713A MX2021004713A (es) 2018-10-25 2019-09-25 Chapa de acero inoxidable ferritico laminada en caliente y recocida y metodo para producir la misma.
CA3114743A CA3114743C (fr) 2018-10-25 2019-09-25 Tole d'acier inoxydable ferritique laminee a chaud et recuite et procede de production d'une telle tole d'acier
JP2020506852A JP7038799B2 (ja) 2018-10-25 2019-09-25 フェライト系ステンレス熱延焼鈍鋼板およびその製造方法
CN201980069792.9A CN112888802A (zh) 2018-10-25 2019-09-25 铁素体系不锈钢热轧退火钢板及其制造方法
KR1020217011576A KR20210064281A (ko) 2018-10-25 2019-09-25 페라이트계 스테인리스 열연 어닐링 강판 및 그 제조 방법

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JP7038799B2 (ja) 2022-03-18
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MX2021004713A (es) 2021-06-04
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KR20210064281A (ko) 2021-06-02

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