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WO2018074164A1 - Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé pour la fabriquer - Google Patents

Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé pour la fabriquer Download PDF

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Publication number
WO2018074164A1
WO2018074164A1 PCT/JP2017/034949 JP2017034949W WO2018074164A1 WO 2018074164 A1 WO2018074164 A1 WO 2018074164A1 JP 2017034949 W JP2017034949 W JP 2017034949W WO 2018074164 A1 WO2018074164 A1 WO 2018074164A1
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Prior art keywords
hot
rolling
rolled
content
steel sheet
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Ceased
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English (en)
Japanese (ja)
Inventor
正崇 吉野
光幸 藤澤
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JFE Steel Corp
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JFE Steel Corp
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Filing date
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Priority to EP17862905.1A priority Critical patent/EP3486347B1/fr
Priority to CN201780051736.3A priority patent/CN109642286B/zh
Priority to US16/327,988 priority patent/US20190226045A1/en
Priority to KR1020197005080A priority patent/KR102201004B1/ko
Priority to ES17862905T priority patent/ES2831841T3/es
Priority to JP2017567271A priority patent/JP6304469B1/ja
Publication of WO2018074164A1 publication Critical patent/WO2018074164A1/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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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

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 to prevent the exhaust gas from leaking.
  • 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 inventors of the present invention have made a detailed study in order to solve the problem.
  • the workability is the Charpy impact value that has been used conventionally.
  • a Threshold Stress Intensity Factor K IC which is a toughness evaluation index in the field of thick plates. This is because with thin steel plates with a thickness of less than 5.0 mm, the plastic deformation region near the punched end surface during processing is larger than the plate thickness, so the fracture phenomenon associated with forming is uniquely handled by fracture mechanics.
  • the plastic deformation region near the punched end surface during processing sufficiently satisfies the small-scale yield state where the thickness is sufficiently small relative to the plate thickness. Therefore, it can be considered that the fracture phenomenon associated with the predetermined processing can be handled by the stress intensity factor, which is a quantitative index of fracture mechanics, and particularly the critical value, that is, the critical stress intensity factor K IC can be accurately evaluated. .
  • the present inventors have investigated in detail the relationship between the presence or absence of cracking and the limit stress intensity factor K IC when processing into a flange of a predetermined shape.
  • the critical stress intensity factor K IC 20 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. I found out.
  • component composition in mass%, Cu: 0.01 to 1.00%, Mo: 0.01 to 2.00%, W: 0.01 to 0.20%, Co: 0.01 The ferritic stainless steel hot-rolled annealed steel sheet according to the above [1], containing one or more selected from ⁇ 0.20%.
  • component composition in mass%, V: 0.01 to 0.20%, Nb: 0.01 to 0.10%, Zr: 0.01 to 0.20%, REM: 0.00.
  • a hot-rolled steel sheet is obtained by setting the pass to a temperature range of 800 to 1100 ° C. and the cumulative rolling reduction ratio of the final three passes to 25% or more, and the hot-rolled steel plate is further annealed at 800 to 1100 ° C.
  • the critical stress intensity factor K IC is taken from the center of the plate width from a CT (Compact Tension) test piece according to ASTM E399 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. It refers to the stress intensity factor obtained by testing in accordance with ASTM E399.
  • a ferritic stainless steel hot-rolled annealed steel sheet having sufficient corrosion resistance and excellent workability capable of suppressing cracking when punching into a thick flange is obtained.
  • sufficient corrosion resistance in the present invention refers to a salt spray cycle test (salt spray (5 mass% NaCl) specified in JIS H8502 on a steel plate whose end face is sealed after polishing the surface to be evaluated with # 600 emery paper. , 35 ° C., spraying 2 hr) ⁇ drying (60 ° C., 4 hr, relative humidity 40%) ⁇ wet (50 ° C., 2 hr, relative humidity
  • 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 24.0%, Ni: 0.01 to 0.60%, 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 20 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 examined in detail the relationship between the remarkable progress of the microcracks and the material properties. As a result, progress of microcracks have found that there is a tendency to occur as the critical stress intensity factor K IC of the steel sheet is small. 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. It has been found that K IC is particularly likely to occur in a steel sheet having a value of less than 20 MPa ⁇ m 1/2 .
  • the present inventors investigated in detail the crack part of said steel plate in order to clarify the cause of the small critical stress intensity factor K IC of the steel plate in which cracking occurred 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.
  • the crystal grains of the portion where the cracks remarkably progressed are independent crystal grains, It was ascertained that so-called colonies (groups of crystal grains having similar crystal orientations) having substantially the same crystal orientation as adjacent crystal grains were formed.
  • 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 present inventors have intensively studied a method for improving the critical stress intensity factor K IC in a ferritic stainless hot-rolled annealed steel sheet.
  • the final three passes in the hot rolling process in which finish rolling consisting of multiple passes is performed in the temperature range of 800 to 1100 ° C., and the cumulative reduction ratio of the final three passes.
  • the thickness of the ferritic stainless steel hot-rolled annealed steel sheet according to the present invention is not particularly limited. However, since it is desirable that the thickness be applicable to a thick flange, 5.0 mm or more is preferable, and 7.0 mm or more is preferable. More preferred. Moreover, the said plate
  • ferritic stainless steel hardly undergoes dynamic recrystallization (referred to as recrystallization during deformation) during 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.
  • recrystallization during deformation dynamic recrystallization
  • the present inventors diligently studied a method for effectively and sufficiently introducing rolling distortions over the entire thickness of the steel sheet in the hot rolling process.
  • the final three passes of finish hot rolling are controlled within an appropriate temperature range, and rolling is performed at a large cumulative reduction rate, thereby suppressing the recovery of rolling distortion and reducing the rolling distortion to the center of the plate thickness.
  • 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, but the grain boundary length is remarkably long, so that the effect of suppressing crack growth by grain boundaries with different orientations is the same as when colonies existed. It was found that the predetermined critical stress intensity factor K IC could not be obtained.
  • the present inventors investigated in detail the relationship between the grain size of recrystallized grains and the annealing temperature. As a result, it has been found that by suppressing the hot-rolled sheet annealing temperature to 1100 ° C. or lower, it is possible to suppress the generation of coarse recrystallized grains so that the critical stress intensity factor K IC is significantly reduced.
  • component composition of the ferritic stainless steel hot-rolled annealed steel sheet of the present invention will be described.
  • % indicating the component composition means mass%.
  • the C content is in the range of 0.001 to 0.020%.
  • the C content is preferably 0.003% or more, and 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 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.
  • Si is contained in excess of 1.00%, the rolling load increases in the hot rolling process and a significant scale is generated.
  • the pickling property decreases due to the formation of the Si concentrated layer on the steel sheet surface layer.
  • the Si content is set to 0.05 to 1.00%.
  • the Si content is preferably 0.10% or more.
  • Si content becomes like this. Preferably it is 0.60% or less, More preferably, it is 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%, the generation of MnS that is the 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 Mn content is preferably 0.10% or more. Further, the Mn content is preferably 0.60% or less, more preferably 0.30% 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.
  • 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.
  • 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 Al content is preferably 0.005% or more, and more preferably 0.010% or more. Moreover, Al content becomes like this. Preferably it is 0.060% or less, More preferably, it is 0.040% or less.
  • Cr 10.0-24.0% 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 the Cr content exceeds 24.0%, the toughness is remarkably reduced due to the formation of the ⁇ (sigma) phase, and in the present invention, the predetermined critical stress intensity factor K IC cannot be obtained. Therefore, the Cr content is in the range of 10.0 to 24.0%.
  • the Cr content is preferably 14.0% or more, more preferably 16.0% or more, and further preferably 17.0% or more. Moreover, Cr content becomes like this. Preferably it is 21.5% or less, More preferably, it is 19.5% or less, More preferably, it is 18.5% or less.
  • Ni 0.01 to 0.60%
  • Ni is an element that improves the corrosion resistance of stainless steel, and is an element that suppresses the progress of corrosion in a corrosive environment where a passive film is not formed and active dissolution occurs.
  • Ni is a strong austenite generating element, and has the effect of suppressing ferrite formation at the weld and suppressing sensitization due to precipitation of Cr carbonitride. This effect is obtained by containing 0.01% or more of Ni, and increases as the Ni content increases. However, when the Ni content exceeds 0.60%, workability is lowered and stress corrosion cracking is likely to occur. Furthermore, since Ni is an expensive element, an increase in the content of Ni causes an increase in manufacturing cost, which is not preferable. Therefore, the Ni content is set to 0.01 to 0.60%.
  • the Ni content is preferably 0.10% or more. Moreover, Ni content becomes like this. Preferably it is 0.50% or less, More preferably, it is 0.40% 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 There is. 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 Ti content is preferably 0.15% or more, and more preferably 0.20% or more. Moreover, Ti content becomes like this. Preferably it is 0.35% or less, More preferably, it is 0.30% or less. From the viewpoint of corrosion resistance of the weld zone, the Ti content satisfies the formula: Ti / (C + N) ⁇ 8 (in the formula, Ti, C, and N are the contents (mass%) of each element). It is preferable.
  • 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 N content is preferably 0.005% or more, and more preferably 0.007% or more.
  • N content becomes like this. Preferably it is 0.015% or less, More preferably, it is 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.
  • 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 Cu content is more preferably 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 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 Mo content is more preferably 0.10% or more, and further preferably 0.30% or more. Moreover, Mo content becomes like this. More preferably, it is 1.40% or less, More preferably, it is 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%. The W content is more preferably 0.05% or more. Further, the W content is more preferably 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.
  • 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%.
  • the Co content is more preferably 0.10% or less.
  • V 0.01-0.20%
  • V forms carbonitride with C and N, suppresses sensitization during welding 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%.
  • the V content is more preferably 0.03% or more. Further, the V content is more preferably 0.10% or less, and even more preferably 0.05% 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. When the Nb content exceeds 0.10%, the annealing temperature necessary for causing sufficient recrystallization by hot-rolled sheet annealing becomes excessively high. As a result, recrystallized grains become extremely coarse as the crystal grain size reaches 300 ⁇ m or more during annealing, and a predetermined critical stress intensity factor K IC may not be obtained. Therefore, when Nb is contained, the Nb content is preferably in the range of 0.01 to 0.10%. The Nb content is more preferably 0.02% or more. Further, the Nb content is more preferably 0.05% or less.
  • Zr 0.01-0.20%
  • 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 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%.
  • the Zr content is more preferably 0.02% or more. Further, the Zr content is more preferably 0.10% or less, and even more preferably 0.05% or less.
  • REM 0.001 to 0.100% REM (Rare Earth Metals) has an effect of improving the oxidation resistance, and suppresses formation of a Cr-deficient region immediately below the oxide film by suppressing formation of an oxide film (weld temper color) in the welded portion. This effect is acquired by containing REM 0.001% or more.
  • 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%.
  • the REM content is more preferably 0.010% or more.
  • the REM content is more preferably 0.050% or less.
  • B 0.0002 to 0.0025%
  • B is an element effective for improving the secondary work brittleness resistance after molding. This effect is obtained by making the B content 0.0002% or more. On the other hand, if the B content exceeds 0.0025%, workability and toughness may be reduced. Therefore, when B is contained, the B content is preferably in the range of 0.0002 to 0.0025%. The B content is more preferably 0.0003% or more. Further, the B content is more preferably 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%. The Mg content is more preferably 0.0010% or more. The Mg content is more preferably 0.0020% or less.
  • 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 Ca content is more preferably 0.0005% or more. Moreover, Ca content becomes like this. More preferably, it is 0.0015% or less, More preferably, it is 0.0010% or less.
  • Limit stress intensity factor K IC 20 MPa ⁇ m 1/2 or more
  • the ferritic stainless steel hot rolled annealed steel sheet of the present invention has a limit stress intensity factor K IC of 20 MPa ⁇ m 1/2 or more, so that it becomes a thick flange. It is possible to suppress cracks during the punching process.
  • the critical stress intensity factor K IC is preferably 25 MPa ⁇ m 1/2 or more, more preferably 30 MPa ⁇ m 1/2 or more.
  • the thick flange is not particularly limited, and examples thereof include a flange having a thickness of 5.0 mm or more. As the flange, for example, a flange having a plate thickness of 5.0 to 15.0 mm is preferable, and a flange having a plate thickness of 5.0 to 10.0 mm is more preferable.
  • the temperature is the surface temperature measured with a surface thermometer such as a steel slab or hot-rolled steel sheet.
  • the ferritic stainless steel hot-rolled annealed steel sheet of the present invention uses a steel slab having the above composition, and in the hot rolling consisting of rough rolling and finishing rolling of 3 or more passes, the final 3 passes of finishing rolling are performed in a temperature range of 800. It is obtained by obtaining a hot-rolled steel sheet at a temperature of ⁇ 1100 ° C. and a cumulative reduction ratio of 25% or more in the final three passes, and subjecting the hot-rolled steel sheet to further hot-rolled sheet annealing at 800 to 1100 ° C.
  • the molten steel having the above component composition is melted by a known method such as a converter, electric furnace, vacuum melting furnace or the like, and is made into a steel material (slab) by a continuous casting method or an ingot-bundling method.
  • the slab is heated at 1100 to 1250 ° C. for 1 to 24 hours, or subjected to hot rolling at a stage where the temperature reaches 1100 to 1250 ° C. after casting without heating.
  • there is no particular limitation for rough rolling if the cast structure is effectively destroyed before finish hot rolling, it is superior to refinement of crystal grains in subsequent finish hot rolling.
  • Rolling temperature range for the final three passes of finish hot rolling 800-1100 ° C
  • Cumulative rolling reduction in the final three passes of finish hot rolling 25% or more
  • K IC critical stress intensity factor
  • the cumulative reduction ratio of the final three passes of finish hot rolling 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 in the final three passes of finish hot rolling 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.
  • the predetermined limit stress intensity factor K IC cannot be obtained. Therefore, the rolling temperature for the final three passes is in the range of 800 to 1100 ° C.
  • the rolling temperature in the final three passes is in the range of 800 to 1050 ° C. More preferably, the rolling temperature in the final three passes is in the range of 850 to 1000 ° C.
  • the rolling temperature range of the first pass among the final three passes is 950 to 1100 ° C., and this first pass
  • the rolling temperature range for the second pass to be performed next is preferably 925 to 1075 ° C.
  • the rolling temperature range for the third pass to be performed next to 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 manufacturing method of the ferritic stainless steel hot-rolled steel sheet of the present invention it is important to control the final three-pass rolling temperature and cumulative rolling reduction of the finish hot rolling, and if it is a finish rolling of three or more passes Any number of finishing rolls may be performed, but if 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 the steel plate temperature is kept within a predetermined temperature range.
  • the maximum number of passes is preferably 15 passes or less because it may lead to a decrease in manufacturability or an increase in manufacturing costs, such as heating from the outside required for maintenance. 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 ° C. 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 800-1100 ° 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 annealing temperature is less than 800 ° C., recrystallization is insufficient, and a predetermined critical stress intensity factor K IC cannot be obtained.
  • the hot-rolled sheet annealing temperature is in the range of 800 to 1100 ° C.
  • the hot-rolled steel sheet subjected to such hot-rolled sheet annealing has the above-described component composition, and has a critical stress intensity factor K IC of 20 MPa ⁇ m 1/2 or more.
  • the hot-rolled sheet annealing temperature is in the range of 800 to 1050 ° C.
  • the hot-rolled sheet annealing temperature is in the range of 850 to 1000 ° C.
  • 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.
  • SS-VOD strong stirring and vacuum oxygen decarburization
  • the slab was heated at 1200 ° C. for 1 h, and then hot-rolled by reverse rough rolling using a three-stage stand to obtain a steel plate of about 40 mm, and then the final three passes of final rolling consisting of 7 passes ( The fifth pass, the sixth pass, and the seventh pass) were performed under the conditions shown in Table 2 to obtain hot-rolled steel sheets.
  • No. No. 31 was subjected to hot rolling after heating the slab at 1300 ° C. for 1 h.
  • 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 anne
  • the obtained hot-rolled annealed steel sheet was evaluated as follows.
  • Photograph the evaluation surface of the test piece after 5 cycles of the salt spray cycle test measure the rusting area of the evaluation surface of the test piece by image analysis, and determine the rusting rate ((test Rust area in the piece / 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.
  • No. No. 31 is an example in which the slab was heated at 1300 ° C. for 1 h and then subjected to hot rolling, and the rolling temperature range in the final three passes of finish hot rolling was all over 1100 ° C. No. In No. 31, the recovery of excessive working strain occurred during the rolling of the final three passes and the recrystallization sites became insufficient, so that colonies remained after hot-rolled sheet annealing, and the predetermined critical stress intensity factor K IC was It 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 during the rolling of the final third pass, so that the rolling could not be completed and the predetermined evaluation could not be performed.
  • the ferritic stainless steel hot-rolled annealed steel sheet obtained by the present invention is particularly suitable for applications that require 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 qui présente une résistance à la corrosion suffisante et qui ne donne pas lieu à fissuration lorsqu'elle est découpée pour former une bride à paroi épaisse ; et un procédé pour la fabriquer. Cette tôle d'acier inoxydable ferritique laminée à chaud et recuite est caractérisée en ce qu'elle présente une composition de constituants comprenant, 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, au plus 0,04 % de P, au plus 0,01 % de S, de 0,001 à 0,100 % d'Al, de 10,0 à 24,0 % de Cr, de 0,01 à 0,60 % de Ni, de 0,10 à 0,40 % de Ti et de 0,001 à 0,020 % de N, le reste comprenant du Fe et des impuretés inévitables ; et en ce qu'elle a un facteur d'intensité de contrainte de seuil KIC d'au moins 20 MPa·m1/2.
PCT/JP2017/034949 2016-10-17 2017-09-27 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé pour la fabriquer Ceased WO2018074164A1 (fr)

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EP17862905.1A EP3486347B1 (fr) 2016-10-17 2017-09-27 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et procédé pour la fabriquer
CN201780051736.3A CN109642286B (zh) 2016-10-17 2017-09-27 铁素体系不锈钢热轧退火钢板及其制造方法
US16/327,988 US20190226045A1 (en) 2016-10-17 2017-09-27 Hot-rolled and annealed ferritic stainless steel sheet and method for manufacturing the same
KR1020197005080A KR102201004B1 (ko) 2016-10-17 2017-09-27 페라이트계 스테인리스 열연 어닐링 강판 및 그 제조 방법
ES17862905T ES2831841T3 (es) 2016-10-17 2017-09-27 Chapa de acero inoxidable ferrítico laminada en caliente y recocida y método para producir la misma
JP2017567271A JP6304469B1 (ja) 2016-10-17 2017-09-27 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

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WO2018199062A1 (fr) * 2017-04-27 2018-11-01 Ｊｆｅスチール株式会社 Tôle d'acier inoxydable ferritique laminée à chaud et recuite et son procédé de production
JP2020015945A (ja) * 2018-07-25 2020-01-30 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼板およびその製造方法
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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CN115386807B (zh) * 2022-09-19 2023-12-22 山西太钢不锈钢股份有限公司 铁素体不锈钢热轧中板及其制备方法
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CN109642286B (zh) 2021-02-12
KR102201004B1 (ko) 2021-01-11
KR20190032477A (ko) 2019-03-27
CN109642286A (zh) 2019-04-16
EP3486347B1 (fr) 2020-10-21
ES2831841T3 (es) 2021-06-09
EP3486347A1 (fr) 2019-05-22
EP3486347A4 (fr) 2019-07-10

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