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WO2018199062A1 - Tôle d'acier inoxydable ferritique laminée à chaud et recuite et son procédé de production - Google Patents

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

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Publication number
WO2018199062A1
WO2018199062A1 PCT/JP2018/016545 JP2018016545W WO2018199062A1 WO 2018199062 A1 WO2018199062 A1 WO 2018199062A1 JP 2018016545 W JP2018016545 W JP 2018016545W WO 2018199062 A1 WO2018199062 A1 WO 2018199062A1
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Prior art keywords
hot
rolling
rolled
steel sheet
less
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Ceased
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PCT/JP2018/016545
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English (en)
Japanese (ja)
Inventor
正崇 吉野
佳士 井上
光幸 藤澤
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JFE Steel Corp
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JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
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Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to MX2019012549A priority Critical patent/MX2019012549A/es
Priority to US16/607,174 priority patent/US20200385835A1/en
Priority to CN201880027591.8A priority patent/CN110546294B/zh
Priority to EP18790531.0A priority patent/EP3587610B1/fr
Priority to ES18790531T priority patent/ES2924685T3/es
Priority to KR1020197030951A priority patent/KR20190131528A/ko
Priority to JP2018540074A priority patent/JP6432720B1/ja
Publication of WO2018199062A1 publication Critical patent/WO2018199062A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • 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
    • C22C38/002—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
    • C22C38/50—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 ferritic stainless hot-rolled annealed steel sheet excellent in workability suitable for application to a flange or the like and a method for producing the same.
  • an exhaust gas recirculation (EGR) system in which exhaust gas generated from an automobile engine is used again as intake air for the engine is being applied. Exhaust gas generated from the engine is supplied to the engine again after passing through an EGR cooler for lowering the gas temperature.
  • EGR exhaust gas recirculation
  • each exhaust system component is fastened via a flange in order to prevent gas leakage.
  • the flange applied to such an exhaust system part needs to have sufficient rigidity. For this reason, a thick flange (for example, a plate thickness of 5 mm or more) is applied to such an exhaust system component.
  • 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 inevitable impurities, Nb, C and 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 plate thickness of 5.0 to 9.0 mm is disclosed. Has been.
  • the present invention provides a ferritic stainless steel hot-rolled annealed steel sheet that can solve such problems, has sufficient corrosion resistance, and can suppress cracking when punching into a thick flange, and a method for producing the same. Objective.
  • the critical stress intensity factor K of the steel sheet is required for processing into a thick flange having a burring portion without causing cracks. I found that it would be better to increase the IC . Specifically, by setting the critical stress intensity factor K IC to 35 MPa ⁇ m 1/2 or more, it is possible to effectively suppress the occurrence of cracks in the burring part when processing into a thick flange having a burring part. It has been found that it can be sufficiently put into practical use for a thick flange having a burring portion.
  • the critical stress intensity factor K IC is improved by performing hot-rolled sheet annealing at an appropriate temperature on a hot-rolled steel sheet obtained by appropriately controlling the previous sheet thickness) ⁇ 100 [%]). I found out.
  • This invention is made
  • 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 0.001 to 0.100%
  • Cr 10.0 to 19.0%
  • Ni 0.65 to 1.50%
  • Ti 0.10 to 0.40%
  • N Ferritic stainless steel hot-rolled containing 0.001 to 0.020%, the balance having a composition composed of Fe and inevitable impurities, and a critical stress intensity factor K IC of 35 MPa ⁇ m 1/2 or more Annealed steel sheet.
  • the component composition is in mass%, and Cu: 0.01 to 1.00%, Mo: 0.01 to 2.00%, W: 0.01 to 0.20%, Co: 0
  • the component composition is in mass%, and V: 0.01 to 0.20%, Nb: 0.01 to 0.10%, Zr: 0.01 to 0.20%, REM: 0
  • V 0.01 to 0.20%
  • Nb 0.01 to 0.10%
  • Zr 0.01 to 0.20%
  • REM 0
  • B 0.0002 to 0.0025%
  • Mg 0.0005 to 0.0030%
  • Ca 0.0003 to 0.0030%
  • the final three passes of finish rolling are performed at a temperature of 800 to 1100 ° C.
  • the manufacturing method of the ferritic stainless steel hot-rolled annealing steel sheet which makes the cumulative rolling reduction
  • the critical stress intensity factor K IC was obtained by taking a CT test piece compliant with ASTM E399 from the center of the plate width so that the fatigue precrack is in the direction perpendicular to the rolling direction and the stress axis is in the rolling parallel direction, and ASTM E399. It refers to the stress intensity factor obtained by testing according to the above.
  • a ferritic stainless hot rolled annealed steel sheet having sufficient corrosion resistance and excellent toughness capable of suppressing cracking when punching into a thick flange is obtained.
  • the critical stress intensity factor K IC obtained by taking the stress axis to be parallel to the rolling direction and testing in accordance with ASTM E399 is 35 MPa ⁇ m 1/2 or more.
  • the ferritic stainless steel hot-rolled annealed steel sheet of the present invention is, in 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: 0.001 to 0.100%, Cr: 10.0 to 19.0%, Ni: 0.65 to 1.50%, Ti: 0.10 to 0.40%, N: 0.001 to 0.020%, the balance is composed of Fe and inevitable impurities, and the critical stress intensity factor K IC is 35 MPa ⁇ m 1 / 2 or more.
  • the critical stress intensity factor K IC was obtained by collecting CT specimens in accordance with ASTM E399 from the center of the plate width so that the fatigue precrack is in the direction perpendicular to the rolling and the stress axis is in the direction parallel to the rolling, and in accordance with ASTM E399. Refers to the stress intensity factor obtained by testing.
  • the present inventors used various ferritic stainless steel plates with a thickness of 5.0 mm to cause cracks when forming 30 mm ⁇ flange hole portions into flanges having a burring portion that lifts 10 mm from the blank steel plate surface.
  • the cause was examined in detail. As a result, it was found that in the above-described steel plate in which cracking occurred, the micro crack generated in the vicinity of the central portion of the punched end face significantly progressed in the burring process, so that cracking occurred.
  • the present inventors examined in detail the relationship between the remarkable progress of the microcracks and the material properties. As a result, it was found that the development of microcracks tends to occur as the critical stress intensity factor of the steel sheet decreases. Therefore, as a result of attempts to form the flange using various ferritic stainless steel hot-rolled annealed steel plates (thickness 5.0 mm), cracks due to the development of microcracks are limited stress intensity factors obtained by a predetermined measurement method. Has been found to be particularly likely to occur in a steel sheet having a thickness of less than 35 MPa ⁇ m 1/2 .
  • the present inventors have investigated in detail the cracked portion of the steel sheet in order to clarify the cause of the small critical stress intensity factor of the steel sheet that has cracked during forming on the flange. As a result, it was found that in the steel plate in which cracks occurred, the cracks generated in the vicinity of the center portion of the punched end face significantly progressed at the grain boundary in the vicinity of the center portion of the plate thickness.
  • a crystal grain has a crystal orientation different from that of an adjacent crystal grain, and when a crack propagates on the grain boundary, a grain boundary having a different orientation functions as an obstacle to crack propagation.
  • the crystal orientations of adjacent crystal grains are almost equal in the colony, the effect of suppressing crack propagation due to the grain boundary between the crystal grains in the colony becomes small. Thereby, in the steel plate in which the colony was formed, the critical stress intensity
  • the present inventors diligently studied a method for improving the critical stress intensity factor in a ferritic stainless steel hot-rolled annealed steel sheet.
  • Hot rolling is performed at a temperature of 600% to 1100 ° C. on the hot-rolled steel sheet obtained by hot rolling under a condition that the sheet thickness before starting rolling of the pass) ⁇ 100 [%]) is 25% or more.
  • K IC critical stress intensity factor
  • the thickness of the ferritic stainless steel hot-rolled annealed steel sheet of the present invention is not particularly limited, but it is desirable that the thickness be applicable to a thick flange.
  • the plate thickness is preferably 5.0 mm or more. More preferably, it is 9.0 mm or more. About an upper limit, 15.0 mm or less is preferable. More preferably, it is 10.0 mm or less.
  • Coarse and expanded colonies are distributed along the casting direction in the central portion of the thickness of the slab before hot rolling of the ferritic stainless steel.
  • the steel plate deforms from the surface layer portion and extends. For this reason, when the rolling reduction is small, the amount of deformation in the central portion of the plate thickness is small, and almost no rolling strain is introduced into the central portion of the plate thickness.
  • ferritic stainless steel hardly undergoes dynamic recrystallization in hot rolling, and tends to cause recovery of processing strain due to rolling. Therefore, in the hot rolling according to the conventional technique, excessive recovery of the working strain introduced by rolling occurs, and the working strain cannot be effectively maintained until after hot rolling. As a result, the recrystallization sites become insufficient, the colonies are not effectively destroyed in the subsequent hot-rolled sheet annealing, and the predetermined critical stress intensity factor K IC cannot be obtained.
  • the present inventors diligently studied an effective method for reducing colonies remaining after hot-rolled sheet annealing from both the steel component and hot rolling methods.
  • the steel components, particularly Cr and Ni contents are controlled within an appropriate range to generate a predetermined amount of austenite phase in the hot rolling process, and the final three passes of finish hot rolling in the hot rolling process. It was found that it was effective to perform rolling at a large cumulative reduction ratio while controlling in an appropriate temperature range.
  • the Cr content is in the range of 10.0 to 19.0% and the Ni content is in the range of 0.65 to 1.50% so that an austenite phase is generated during heating before hot rolling.
  • the temperature of the final three passes of finishing hot rolling consisting of 3 passes or more is 800 to 1100 ° C.
  • Hot-rolled sheet annealing is a process of recrystallizing a processed structure formed by hot rolling. Therefore, it is necessary to perform annealing at a temperature at which sufficient recrystallization occurs.
  • hot-rolled sheet annealing is performed at an excessively high temperature, recrystallization occurs but recrystallized grains become extremely coarse.
  • this remarkably coarse recrystallized grain is an independent single crystal grain, the grain boundary length becomes remarkably long. For this reason, as in the case where the colonies existed, it was found that the effect of suppressing crack propagation due to grain boundaries having different orientations was reduced, and a predetermined limit stress intensity factor could not be obtained.
  • the present inventors investigated in detail the relationship between the recrystallized grain size and the annealing temperature. As a result, it has been found that by suppressing the hot-rolled sheet annealing temperature to 1100 ° C. or less, the formation of coarse recrystallized grains is suppressed, thereby obtaining a good limit stress intensity factor.
  • the C content is in the range of 0.001 to 0.020%.
  • the lower limit is preferably 0.003% or more, more preferably 0.004% or more.
  • About an upper limit Preferably it is 0.015% or less, More preferably, it is 0.012% or less.
  • Si 0.05 to 1.00%
  • Si has an effect of concentrating on an oxide film formed at the time of welding to improve the corrosion resistance of the welded portion, and is also an element useful as a deoxidizing element in the steel making process. These effects are obtained by containing 0.05% or more of Si, and the effect increases as the content increases. However, if Si is contained in excess of 1.00%, the rolling load increases in the hot rolling process and a significant scale is generated. In the annealing process, the pickling property decreases due to the formation of the Si concentrated layer on the steel sheet surface layer. Respectively, which causes an increase in surface defects and an increase in manufacturing cost. Therefore, the Si content is set to 0.05 to 1.00%.
  • the lower limit is preferably 0.15% or more, more preferably 0.20% or more.
  • the upper limit is preferably 0.60% or less, and more preferably 0.40% or less.
  • Mn 0.05 to 1.00% Mn has the effect of increasing the strength of the steel and 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%, precipitation of MnS, which is a starting point of corrosion, is promoted, and the corrosion resistance is lowered. Therefore, the Mn content is set to 0.05 to 1.00%.
  • the lower limit is preferably 0.10% or more, more preferably 0.20% or more.
  • the upper limit is preferably 0.60% or less, and more preferably 0.40% or less.
  • P 0.04% or less
  • P is an element inevitably contained in steel. However, it is preferably reduced as much as possible because it is an element harmful to corrosion resistance and workability. In particular, when the P content exceeds 0.04%, workability is remarkably lowered due to solid solution strengthening. Therefore, the P content is 0.04% or less. Preferably, the P content is 0.03% or less. In order to reduce the P content excessively, an excessive production cost is required. Therefore, considering the production cost, the P content is preferably 0.01% or more.
  • S 0.01% or less S is an element inevitably contained in steel like P. However, it is preferably reduced as much as possible because it is an element harmful to corrosion resistance and workability. In particular, when the S content exceeds 0.01%, the corrosion resistance significantly decreases. Therefore, the S content is 0.01% or less. Preferably, the S content is 0.008% or less. More preferably, the S content is 0.003% or less. In addition, since excessive manufacturing cost is required to reduce the S content excessively, the S content is preferably 0.001% or more in consideration of the manufacturing cost.
  • Al 0.001 to 0.100%
  • Al is an effective deoxidizer. Furthermore, since Al has a stronger affinity for nitrogen than Cr, when nitrogen penetrates into the weld zone, it has the effect of precipitating nitrogen by precipitating nitrogen as Al nitride instead of Cr nitride. These effects can be obtained by containing 0.001% or more of Al. However, it is not preferable to contain Al exceeding 0.100% because the penetration property during welding is lowered and the welding workability is lowered. Therefore, the Al content is in the range of 0.001 to 0.100%.
  • the lower limit is preferably 0.010% or more, more preferably 0.020% or more.
  • the upper limit is preferably 0.080% or less, more preferably 0.060% or less.
  • Cr 10.0-19.0% 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, when Cr is contained exceeding 19.0%, even if a predetermined amount of Ni is contained, a predetermined amount of austenite phase is not generated during heating in the hot rolling process, so that a sufficient colony destruction effect is obtained. Therefore, a predetermined critical stress intensity factor cannot be obtained. Therefore, the Cr content is in the range of 10.0 to 19.0%.
  • the lower limit is preferably 10.5% or more, more preferably 11.0% or more.
  • the upper limit is preferably 16.5% or less, more preferably 12.5% or less, and further preferably 11.5% or less.
  • Ni 0.65 to 1.50%
  • Ni is an austenite generating element and has an effect of increasing the amount of austenite generated during heating before rolling in the hot rolling process.
  • an austenite phase is generated during heating in the hot rolling process.
  • the formation of the austenite phase destroys the ferrite phase colonies formed during casting.
  • the metal structure becomes a two-phase structure of ferrite phase + austenite phase at the heating temperature before hot rolling.
  • the hot phase rolling process is performed because the heterogeneous interface between the ferrite phase present before heating and the austenite phase generated during heating functions as an obstacle to grain growth.
  • the previous metal structure becomes finer.
  • the metal structure after hot rolling and after the hot-rolled sheet annealing in the next process is refined, and a further excellent toughness improving effect can be expressed.
  • the metal structure may become an austenite single phase at the heating temperature before hot rolling, but the austenite phase may also be changed in the same manner as described above when the metal structure at the heating temperature becomes an austenite single phase structure.
  • the austenite phase is less susceptible to grain coarsening in the slab heating temperature range before hot rolling, and the microstructure before hot rolling is higher than that of ferritic stainless steel based on the prior art.
  • the toughness improving effect can be obtained by making the crystal grains finer. These effects can be obtained by containing Ni in an amount of 0.65% or more.
  • the Ni content When the Ni content is 0.65% or more, a critical stress intensity factor of 35 MPa ⁇ m 1/2 or more can be obtained by these effects. On the other hand, if the Ni content exceeds 1.50%, the improvement effect of the limit stress intensity factor is saturated and the workability is lowered. Furthermore, stress corrosion cracking is likely to occur. Therefore, the Ni content is set to 0.65 to 1.50%.
  • the lower limit is preferably 0.70% or more, more preferably 0.75% or more.
  • the upper limit is preferably 1.00% or less, and more preferably the Ni content is 0.90% or less.
  • Ti 0.10 to 0.40%
  • Ti is an extremely important element. Ti preferentially binds to C and N, suppresses the precipitation of Cr carbonitride, lowers the recrystallization temperature, and suppresses the decrease in corrosion resistance due to sensitization due to the precipitation of Cr carbonitride. is there. In order to obtain these effects, it is necessary to contain 0.10% or more of Ti. However, if the Ti content exceeds 0.40%, the solid solution Ti amount increases excessively, so the recrystallization temperature rises conversely, and the technique of the present invention cannot be applied. In addition, if Ti content exceeds 0.40%, coarse Ti carbonitrides are produced in the casting process and cause surface defects, which is not preferable in production.
  • the Ti content is set to 0.10 to 0.40%.
  • the lower limit is preferably 0.15% or more, more preferably 0.20% or more. Even more preferably, it is 0.25% or more.
  • the upper limit is preferably 0.35% or less, more preferably 0.30% or less. In view of corrosion resistance of the welded portion, it is preferable that the Ti content satisfy the formula: Ti / (C + N) ⁇ 8 (Ti, C, and N in the formula are the contents (mass%) of each element). .
  • N 0.001 to 0.020%
  • the workability and the corrosion resistance of the welded portion are significantly reduced. From the viewpoint of corrosion resistance, the lower the N content, the better.
  • reducing the N content to less than 0.001% requires refining for a long time, which is not preferable because it causes an increase in manufacturing cost and a decrease in productivity. . Therefore, the N content is in the range of 0.001 to 0.020%.
  • the lower limit is preferably 0.005% or more, more preferably 0.007% or more.
  • the upper limit is preferably 0.015% or less, more preferably 0.012% or less.
  • the present invention is a ferritic stainless steel characterized in that it contains the above-mentioned essential components and the balance consists of Fe and inevitable impurities. Furthermore, as required, one or more selected from Cu, Mo, W and Co, or / or one selected from V, Nb, Zr, REM, B, Mg and Ca. Or 2 or more types can be contained in the following range. In addition, when there is a lower limit in the following range, the effect of the present invention is not harmed even if it contains the following element below the lower limit. Inevitable impurities.
  • Cu 0.01 to 1.00%
  • Cu is an element particularly effective for improving the corrosion resistance of the base material and the welded part when an aqueous solution or weakly acidic water droplets adhere. This effect is obtained when the content is 0.01% or more, and the effect increases as the Cu content increases. However, when Cu is contained exceeding 1.00%, hot workability may be reduced and surface defects may be induced. In addition, descaling after annealing may be difficult. Therefore, when Cu is contained, the Cu content is preferably in the range of 0.01 to 1.00%.
  • the lower limit is more preferably 0.10% or more, and further preferably 0.30% or more.
  • the upper limit is more preferably 0.60% or less, and still more preferably 0.45% or less.
  • Mo 0.01-2.00% Mo is an element that remarkably improves the corrosion resistance of stainless steel. This effect is obtained when the content is 0.01% or more, and the effect improves as the content increases. However, if the Mo content exceeds 2.00%, the rolling load at the time of hot rolling increases, and the manufacturability may decrease, or the steel sheet strength may increase excessively. Moreover, since Mo is an expensive element, a large content increases the manufacturing cost. Therefore, when Mo is contained, the Mo content is preferably 0.01 to 2.00%.
  • the lower limit is more preferably 0.10% or more, and further preferably 0.30% or more.
  • the upper limit is more preferably 1.40% or less, and still more preferably 0.90% or less.
  • W 0.01-0.20% W, like Mo, has the effect of improving corrosion resistance. This effect is obtained by containing 0.01% or more of W. However, if it exceeds 0.20% and W is contained, the strength increases, and the productivity may decrease 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 lower limit is 0.05% or more. More preferably, the upper limit is 0.15% or less.
  • Co 0.01-0.20%
  • 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%, workability may be reduced. Therefore, when Co is contained, the Co content is preferably in the range of 0.01 to 0.20%.
  • V 0.01-0.20%
  • V forms carbonitride with C and N, suppresses the precipitation of Cr carbonitride, and improves the corrosion resistance of the weld. 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 lower limit is 0.02% or more. More preferably, the upper limit is 0.10% or less.
  • Nb 0.01 to 0.10%
  • Nb has the effect of improving the toughness of the steel sheet by refining crystal grains and dissolving in the matrix. These effects are obtained when the Nb content is 0.01% or more.
  • Nb also has an effect of increasing the recrystallization temperature.
  • the annealing temperature necessary for causing sufficient recrystallization by hot-rolled sheet annealing becomes excessively high.
  • recrystallization grains become significantly coarser as the crystal grain size reaches 300 ⁇ m or more during annealing, making it impossible to obtain a predetermined critical stress intensity factor. Therefore, when Nb is contained, the Nb content is preferably in the range of 0.01 to 0.10%. More preferably, the lower limit is 0.02% or more. More preferably, the upper limit is 0.08% or less.
  • Zr 0.01-0.20% V forms carbonitride with C and N, suppresses the precipitation of Cr carbonitride, and improves the corrosion resistance of the weld. This effect is obtained by containing 0.01% or more of Zr. On the other hand, if the Zr content exceeds 0.20%, the workability may be significantly reduced. Therefore, when Zr is contained, the Zr content is preferably in the range of 0.01 to 0.20%. More preferably, the lower limit is 0.03% or more. More preferably, the upper limit is 0.10% or less.
  • REM 0.001 to 0.100% REM (Rare Earth Metals) has the effect of improving the oxidation resistance, suppresses the formation of an oxide film (weld temper collar) in the welded part, and suppresses the formation of a Cr-deficient region immediately below the oxide film, thereby providing a welded part. Improve the corrosion resistance. This effect is acquired by containing REM 0.001% or more. On the other hand, when it contains REM exceeding 0.100%, productivity, such as pickling at the time of cold rolling annealing, may be reduced. Therefore, when REM is contained, the REM content is preferably in the range of 0.001 to 0.100%. More preferably, the lower limit is 0.005% or more. More preferably, the upper limit is 0.050% or less.
  • B 0.0002 to 0.0025%
  • B is an element effective for improving secondary work embrittlement resistance after deep drawing. This effect is obtained by making the B content 0.0002% or more.
  • the B content is preferably in the range of 0.0002 to 0.0025%. More preferably, the lower limit is 0.0003% or more. More preferably, the upper limit is 0.0006% or less.
  • Mg 0.0005 to 0.0030%
  • Mg is an element that improves the equiaxed crystal ratio of the slab and is effective in improving workability and toughness. Further, in the steel containing Ti as in the present invention, when Ti carbonitride becomes coarser, the toughness decreases, but Mg also has an effect of suppressing the coarsening of Ti carbonitride. These effects can be obtained by containing 0.0005% or more of Mg. On the other hand, if the Mg content exceeds 0.0030%, the surface properties of the 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 lower limit is 0.0010% or more. More preferably, the upper limit is 0.0020% or more.
  • Ca 0.0003 to 0.0030%
  • Ca is an effective component for preventing nozzle clogging due to crystallization of Ti-based inclusions that are likely to occur during continuous casting. The effect is acquired by containing 0.0003% or more of Ca. However, if the Ca content exceeds 0.0030%, the corrosion resistance may decrease due to the formation of CaS. Therefore, when Ca is contained, the Ca content is preferably in the range of 0.0003 to 0.0030%.
  • the lower limit is more preferably 0.0005% or more, and further preferably 0.0006% or more.
  • the upper limit is more preferably 0.0015% or less, and still more 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 composition, and in hot rolling consisting of rough rolling and finishing rolling of three or more passes, the final three passes of finishing rolling are performed at a temperature of By carrying out the conditions at 800 to 1100 ° C. and a cumulative rolling reduction of the final three passes of 25% or more to obtain a hot-rolled steel sheet, and further subjecting the hot-rolled steel sheet to hot-rolled sheet annealing at 600 to 1100 ° C. can get.
  • the molten steel having the above component composition is melted by a known method such as a converter, an electric furnace, a vacuum melting furnace or the like, and a steel material (slab) is obtained by a continuous casting method or an ingot-bundling method.
  • the slab is heated at 1050 to 1250 ° C. for 1 to 24 hours, or directly subjected to hot rolling as it is cast without heating.
  • hot rolling there is no particular limitation for rough rolling.
  • the cast structure is effectively destroyed before finish hot rolling, it is superior to refinement of crystal grains in subsequent finish hot rolling.
  • the sheet is rolled to a predetermined plate thickness by finish hot rolling, but the final three passes of finish rolling are performed in a temperature range of 800 to 1100 ° C., and the cumulative reduction ratio is 25% or more.
  • Rolling temperature range for the final 3 passes 800-1100 ° C Cumulative rolling reduction of the final three passes: 25% or more Although the coarse cast structure is destroyed in the rough rolling before the finish rolling, the crystal grains of the structure are extremely coarse. In order to obtain a predetermined critical stress intensity factor after hot-rolled sheet annealing, it is possible to control the final three-pass rolling temperature and the cumulative reduction ratio, while suppressing the recovery of strain during rolling, particularly the sheet thickness. It is necessary to effectively apply rolling strain to the central portion.
  • the rolling process is a process for reducing the thickness of the steel sheet by shearing the steel sheet.
  • the amount of shear strain in rolling decreases from the surface layer toward the center of the plate thickness. Therefore, when the rolling reduction is small, a large rolling strain is applied in the vicinity of the steel sheet surface layer, while the amount of rolling strain applied to the central portion of the plate thickness is small.
  • the rolling strain becomes a recrystallization site in the next process, hot-rolled sheet annealing.
  • the rolling temperature of the final three passes is set in the range of 800 to 1100 ° C., and the cumulative of the final three passes.
  • the cumulative reduction ratio of the final three passes is set to 25% or more.
  • the cumulative rolling reduction is 30% or more. More preferably, the cumulative rolling reduction is 35% or more.
  • the upper limit of the cumulative rolling reduction is not particularly limited, but if the cumulative rolling reduction is excessively increased, the rolling load increases and the productivity decreases, and surface roughness may occur after rolling. It is preferable to do.
  • the rolling temperature of the final three passes is less than 800 ° C.
  • the rolling load increases remarkably as the steel plate temperature decreases, which is not preferable for production. Further, rolling at a low temperature may cause the surface roughness of the steel sheet to deteriorate the surface quality.
  • the rolling temperature of the final three passes exceeds 1100 ° C., recovery of strain imparted by rolling occurs, and the recrystallization sites after the hot-rolled sheet annealing in the next step are insufficient. It remains, and a predetermined critical stress intensity factor cannot be obtained. Therefore, the rolling temperature for the final three passes is in the range of 800 to 1100 ° C. About a minimum, Preferably it is 850 ° C or more. The upper limit is preferably 1050 ° C. or lower, more preferably 1000 ° C. or lower.
  • the rolling temperature in the final three passes means the rolling end temperature, and the rest means the rolling start temperature.
  • the rolling temperature range of the first pass of the final three passes is 950 to 1100 ° C., which is performed next to the first pass.
  • the rolling temperature range of the second pass is preferably 925 to 1075 ° C.
  • the rolling temperature range of the third pass performed after the second pass is preferably 875 to 1050 ° C.
  • the method for producing a ferritic stainless steel hot-rolled annealed steel sheet according to the present invention is characterized in that a large reduction is applied after controlling the temperature range in the final three passes of finishing hot rolling consisting of three or more passes. If rolling with a large reduction is performed over the final four passes or more, even if the cumulative reduction rate is the same, the reduction rate will be distributed to each pass, so the strain applied to the center of the plate thickness will be insufficient, and each pass Since the accumulated conveyance time increases, recovery during conveyance between each pass is promoted, and the effect of imparting strain is reduced.
  • the rolling temperature and the cumulative reduction ratio of the finish rolling are controlled to the final two passes or less, the rolling load is significantly increased and the productivity is lowered because the large reduction with the cumulative reduction ratio of 25% or more is performed in two passes. This is not preferable. Therefore, in the method for producing a ferritic stainless steel hot-rolled steel sheet according to the present invention, the rolling temperature and cumulative rolling reduction of the final three passes of finish rolling are controlled.
  • the rolling temperature and the cumulative reduction ratio of the final three passes may be performed.
  • the maximum number of passes is greater than 15 passes, the steel plate temperature is likely to decrease due to an increase in the number of contacts with the rolling roll, and heating from the outside is required to maintain the steel plate temperature within a predetermined temperature range.
  • the maximum number of passes is preferably set to 15 or less because there may be a decrease in manufacturability or an increase in manufacturing cost. More preferably, the maximum number of paths is 10 paths or less.
  • the steel sheet After finishing hot rolling, the steel sheet is cooled, and then the steel sheet is wound to form a hot-rolled steel strip.
  • the coiling temperature is not particularly limited, but when the coiling temperature is more than 450 to less than 500 ° C., embrittlement due to 475 ° C. embrittlement may occur. Therefore, the winding temperature is preferably 450 ° C. or lower or 500 ° C. or higher.
  • Hot-rolled sheet annealing temperature 600-1100 ° C
  • hot-rolled sheet annealing is performed after the hot rolling step.
  • the rolled structure formed in the hot rolling process is recrystallized.
  • the rolling strain is effectively applied in the hot rolling process, and the recrystallization sites are increased, thereby promoting the destruction of colonies in the hot-rolled sheet annealing.
  • the hot-rolled sheet annealing temperature is in the range of 600 to 1100 ° C.
  • a lower limit Preferably it is 650 degreeC or more. More preferably, it is 700 ° C. or higher.
  • About an upper limit Preferably it is 1050 degrees C or less, More preferably, it is 900 degrees C or less.
  • maintenance time and method of hot-rolled sheet annealing You may implement by any of box annealing (batch annealing) and continuous annealing.
  • the obtained hot-rolled annealed steel sheet may be descaled by shot blasting or pickling as necessary. Furthermore, in order to improve the surface properties, grinding or polishing may be performed. In addition, the hot-rolled annealed steel sheet provided by the present invention may be subsequently subjected to cold rolling and cold-rolled sheet annealing.
  • a molten stainless steel having the chemical composition shown in Table 1 is melted by refining a converter with a capacity of 150 ton and strong stirring and vacuum oxygen decarburization (SS-VOD), and a steel slab having a width of 1000 mm and a thickness of 200 mm by continuous casting. did. No. Except for 36, the slab was heated at 1150 ° C. for 1 hr, and then hot-rolled by reverse rough rolling using a three-stage stand to obtain a steel plate having a thickness of about 40 mm, and then the final 3 of the final rolling consisting of 7 passes. Passes (5th pass, 6th pass, 7th pass) were performed under the conditions shown in Table 2 to obtain hot-rolled steel sheets. No. No.
  • the obtained hot-rolled steel sheet was subjected to hot-rolled sheet annealing by box annealing under the conditions shown in Table 2 to obtain a hot-rolled annealed sheet. Note that the thickness at the end of the seventh pass is the thickness of the hot-rolled steel plate. The following evaluation was performed about the obtained hot-rolled annealing steel plate.
  • Photograph the surface of the specimen to be evaluated after 5 cycles of the salt spray cycle test measure the rusting area of the specimen surface by image analysis, and determine the rusting rate (( The rusting area in the test piece / the total area of the test piece) ⁇ 100 [%]) was calculated.
  • a rusting rate of 10% or less was evaluated as being particularly excellent with respect to corrosion resistance ()), more than 10% being 25% or less, passing (O), and more than 25% being rejecting (X).
  • test results are shown in Table 2 together with hot rolling and hot rolled sheet annealing conditions.
  • the steel components, hot rolling conditions and hot rolled sheet annealing conditions satisfy the scope of the present invention as shown in No. 2 in Table 2.
  • a predetermined critical stress intensity factor was obtained as a result of the colony being effectively destroyed by predetermined hot rolling and hot-rolled sheet annealing.
  • corrosion resistance of the obtained hot-rolled annealed plates it was confirmed that all had a rusting rate of 25% and sufficient corrosion resistance.
  • No. No. 36 is an example in which the slab is heated at 1300 ° C. for 1 h and then subjected to hot rolling, and the rolling temperature range of the final three passes of finish hot rolling is all over 1100 ° C. No. 36, since the recovery of processing strain occurred during the final three-pass rolling and the introduction of recrystallization sites became insufficient, the colony destruction effect due to hot-rolled sheet annealing was insufficient, The critical stress intensity factor was not obtained.
  • No. of the rolling temperature range for the final 3 passes is less than the range of the present invention for all 3 passes.
  • the rolling load increased remarkably, and the rolling exceeded the allowable range when the final third pass was rolled, so the rolling could not be completed and the predetermined evaluation could not be performed.
  • No. No. of hot-rolled sheet annealing temperature is below the range of the present invention. In 50, since recrystallization was insufficient, a sufficient colony destruction effect could not be obtained, and a predetermined critical stress intensity factor could not be obtained.
  • the ferritic stainless steel hot-rolled annealed steel sheet obtained by the present invention is particularly suitable for applications requiring high workability and corrosion resistance, such as a flange having a burring portion.

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Abstract

L'invention concerne : une tôle d'acier inoxydable ferritique laminée à chaud et recuite présentant une résistance à la corrosion suffisante, et permettant de supprimer la fissuration lors de la mise en œuvre d'un processus de poinçonnage sur une bride épaisse ; et son procédé de production. La tôle d'acier inoxydable ferritique laminée à chaud et recuite contient de 0,00 à 0,020 % en masse de C, de 0,05 à 1,00 % en masse de Si, de 0,05 à 1,00 % en masse de Mn, au plus 0,04 % en masse de P, au plus 0,01 % en masse de S, de 0,001 à 0,100 % en masse d'Al, de 10,0 à 19,0 % en masse de Cr, de 0,65 à 1,50 % en masse de Ni, de 0,10 à 0,40 % en masse de Ti, et de 0,001 à 0,020 % en masse de N, et le complément étant constitué de Fe et d'impuretés inévitables, le facteur d'intensité de contrainte KIC de seuil étant d'au moins 35 MPa∙m1/2.
PCT/JP2018/016545 2017-04-27 2018-04-24 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et son procédé de production Ceased WO2018199062A1 (fr)

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MX2019012549A MX2019012549A (es) 2017-04-27 2018-04-24 Lamina de acero inoxidable ferritico laminado en caliente y recocido y metodo para fabricar la misma.
US16/607,174 US20200385835A1 (en) 2017-04-27 2018-04-24 Hot-rolled and annealed ferritic stainless steel sheet and method for manufacturing the same
CN201880027591.8A CN110546294B (zh) 2017-04-27 2018-04-24 铁素体系不锈钢热轧退火钢板及其制造方法
EP18790531.0A EP3587610B1 (fr) 2017-04-27 2018-04-24 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et son procédé de production
ES18790531T ES2924685T3 (es) 2017-04-27 2018-04-24 Lámina de acero inoxidable ferrítico laminada en caliente y recocida, y método para fabricar la misma
KR1020197030951A KR20190131528A (ko) 2017-04-27 2018-04-24 페라이트계 스테인리스 열연 어닐링 강판 및 그 제조 방법
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WO2020084987A1 (fr) * 2018-10-25 2020-04-30 Ｊｆｅスチール株式会社 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé de production d'une telle tôle d'acier
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CN113166831A (zh) * 2018-12-11 2021-07-23 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法

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ES2924685T3 (es) 2022-10-10
CN110546294A (zh) 2019-12-06
TW201843316A (zh) 2018-12-16
KR20190131528A (ko) 2019-11-26
JP6432720B1 (ja) 2018-12-05
JPWO2018199062A1 (ja) 2019-06-27
CN110546294B (zh) 2022-03-22
EP3587610A4 (fr) 2020-03-04
US20200385835A1 (en) 2020-12-10
MX2019012549A (es) 2019-12-02
TWI685574B (zh) 2020-02-21
EP3587610B1 (fr) 2022-07-06

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