WO2017002147A1 - Feuille d'acier inoxydable ferritique et son procédé de fabrication - Google Patents

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

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WO2017002147A1
WO2017002147A1 PCT/JP2015/003339 JP2015003339W WO2017002147A1 WO 2017002147 A1 WO2017002147 A1 WO 2017002147A1 JP 2015003339 W JP2015003339 W JP 2015003339W WO 2017002147 A1 WO2017002147 A1 WO 2017002147A1
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phase
stainless steel
ferritic stainless
annealing
hot
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PCT/JP2015/003339
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English (en)
Japanese (ja)
Inventor
正崇 吉野
映斗 水谷
光幸 藤澤
力 上
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Ｊｆｅスチール株式会社
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Priority to CN201580081418.2A priority Critical patent/CN107709592B/zh
Priority to KR1020177036666A priority patent/KR102027769B1/ko
Priority to PCT/JP2015/003339 priority patent/WO2017002147A1/fr
Priority to US15/737,932 priority patent/US20180171430A1/en
Priority to JP2015552676A priority patent/JP5884211B1/ja
Priority to TW104122004A priority patent/TW201702406A/zh
Publication of WO2017002147A1 publication Critical patent/WO2017002147A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • 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
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    • 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
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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    • 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
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    • 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
    • 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
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    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • 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 steel sheet having sufficient corrosion resistance and excellent formability and ridging resistance, and a method for producing the same.
  • Ferritic stainless steel sheet is more economical than austenitic stainless steel containing a large amount of expensive Ni.
  • SUS430 stainless steel plate (16 to 18% by mass Cr) is particularly economical and is used in various applications such as building materials, transportation equipment, home appliances, kitchen appliances, and automobile parts. The range of application has been further expanded in recent years. In order to apply to these applications, not only corrosion resistance but also sufficient formability that can be processed into a predetermined shape is required.
  • SUS430 stainless steel sheet is often applied to applications that require a good appearance, and is required to have excellent ridging resistance.
  • Ridging is a surface irregularity generated due to distortion in molding.
  • a crystal grain group (colony) having a similar crystal orientation may be generated during casting and / or hot rolling.
  • colony crystal grain group
  • a large difference occurs in the strain amount between the colony part and other parts at the time of forming, and thus surface irregularities (ridging) occur after forming.
  • a polishing step is required to remove surface irregularities, and the manufacturing cost of the molded product increases.
  • Patent Document 1 by mass, C: 0.02 to 0.06%, Si: 1.0% or less, Mn: 1.0% or less, P: 0.05% or less, S: 0.01%
  • Al 0.005% or less
  • Ti 0.005% or less
  • Cr 11 to 30%
  • Ni 0.7% or less
  • An excellent ferritic stainless steel is disclosed. However, when the present inventors manufactured ferritic stainless steel by the method described in Patent Document 1, excellent elongation at break was obtained in the rolling direction of the steel sheet.
  • box annealing for example, annealing for 8 hours at 860 degreeC
  • box annealing has a problem of low productivity because it takes about one week when heating and cooling processes are included.
  • the manufacturing cost increases because a technique for reducing solid solution N by adding V, which is an expensive transition metal element, is used.
  • box annealing is performed in the single-phase temperature range of ferrite for hot-rolled sheet annealing, ferrite colonies remain with almost no destruction, and there is also a problem that ridging resistance is significantly lowered.
  • Patent Document 2 by mass, C: 0.01 to 0.10%, Si: 0.05 to 0.50%, Mn: 0.05 to 1.00%, Ni: 0.01 to 0.00. 50%, Cr: 10 to 20%, Mo: 0.005 to 0.50%, Cu: 0.01 to 0.50%, V: 0.001 to 0.50%, Ti: 0.001 to 0 .50%, Al: 0.01-0.20%, Nb: 0.001-0.50%, N: 0.005-0.050% and B: 0.00010-0.00500%
  • hot-rolled sheet annealing is performed in the ferrite single-phase temperature range using a box furnace or a continuous furnace of AP line (Annealing and Pickling line), followed by cold rolling and finish annealing.
  • Patent Document 2 As in Patent Document 1, when an attempt was made to produce a press member mainly composed of stretch forming, it could not be formed into a predetermined shape, and as expected from elongation at break. No stretch formability was obtained. Furthermore, in general, ferritic stainless steel as in Patent Document 2 generates a group of crystal grains (colony) having a similar crystal orientation during casting or hot rolling, and hot-rolled sheet annealing is performed in a ferrite single-phase temperature range. The ferrite phase colonies cannot be sufficiently destroyed. Therefore, there is a problem that the colony expands and remains in the rolling direction by cold rolling after hot-rolled sheet annealing, and significant ridging occurs after forming.
  • colony crystal grains
  • Patent Document 3 a ferritic stainless steel containing 0.15% or less of C and 13 to 25% of Cr, and a range of 930 to 990 ° C. in which austenite and a ferrite phase coexist on the hot-rolled sheet of this steel.
  • the structure becomes a two-phase structure of martensite phase and ferrite phase, and then cold rolling and cold-rolled sheet annealing are performed, which is excellent in ridging resistance and workability
  • a method for producing a ferritic stainless steel sheet is disclosed.
  • Patent Document 3 only elongation is mentioned as workability.
  • Japanese Patent No. 3584881 (Republished WO 00/60134) Japanese Patent No. 3581801 (Japanese Patent Laid-Open No. 2001-3134) Japanese Patent Publication No.47-1878
  • An object of the present invention is to solve such problems and to provide a ferritic stainless steel sheet having sufficient corrosion resistance, excellent formability and ridging resistance, and a method for producing the same.
  • sufficient corrosion resistance refers to a salt spray cycle test (salt spray (35 ° C., 5 ° C., JIS H 8502) applied to a steel plate whose surface is polished with # 600 emery paper and the end face is sealed. (Mass% NaCl, spraying 2 hr) ⁇ drying (60 ° C., relative humidity 40%, 4 hr) ⁇ wetting (50 ° C., relative humidity ⁇ 95%, 2
  • excellent moldability means having excellent stretch formability, elongation at break, and average r value.
  • Excellent stretch formability means that the minimum value of the maximum logarithmic strain of the forming limit determined based on the forming limit diagram (FLD) of steel is 0.15 or more.
  • the excellent elongation at break means that the elongation at break (El) in a tensile test according to JIS Z 2241 is 28% or more in a test piece perpendicular to the rolling direction.
  • An excellent average r value is an average rankford value (hereinafter referred to as an average r value) calculated by the following equation (1) when a strain of 15% is applied in a tensile test based on JIS Z 2241: It means that it is more than .75.
  • r L is an r value when a tensile test is performed in a direction parallel to the rolling direction
  • r D is an r value when a tensile test is performed in a direction of 45 ° with respect to the rolling direction
  • r C is a direction perpendicular to the rolling direction. The r value when a tensile test is performed.
  • excellent ridging resistance means that the ridging height measured by the following method is 2.5 ⁇ m or less.
  • a JIS No. 5 tensile test piece is taken in parallel with the rolling direction.
  • 20% tensile strain is applied.
  • the arithmetic average waviness (Wa) defined by JIS B 0601 (2001) is measured with a surface roughness meter in the direction perpendicular to the rolling direction on the polishing surface at the center of the parallel part of the test piece.
  • the measurement conditions are a measurement length of 16 mm, a high cut filter wavelength of 0.8 mm, and a low cut filter wavelength of 8 mm. This arithmetic mean swell is defined as the ridging height.
  • An appropriate component ferritic stainless steel sheet is annealed at a suitable temperature range of a ferrite phase and an austenite phase after hot rolling and before cold rolling (hereinafter referred to as hot rolled sheet annealing). Further, by annealing the cold-rolled steel sheet at a temperature that becomes a ferrite single-phase region (hereinafter referred to as cold-rolled sheet annealing), it is a ferrite single-phase structure, but an intragranular carbonitride. A mixed grain structure of ferrite grains having a large amount of ferrite and ferrite grains having a small amount of carbonitride in the grains. As a result, it has been found that a ferritic stainless steel sheet having sufficient corrosion resistance and excellent formability and ridging resistance can be obtained.
  • all% which shows the component of steel is the mass%.
  • a ferritic stainless steel sheet having sufficient corrosion resistance and excellent formability and ridging resistance can be obtained.
  • the ferritic stainless steel sheet of the present invention is intended to be used in various applications such as building material parts, home appliance parts, kitchen appliances, or automobile parts by press working. In order to apply to these uses, sufficient moldability is required.
  • the present inventors conducted an overhang forming test assuming a ventilation hood using various ferritic stainless steel sheets (including those corresponding to Patent Documents 1 to 3) having different components and production methods.
  • various ferritic stainless steel sheets including those corresponding to Patent Documents 1 to 3 having different components and production methods.
  • the superiority or inferiority of the stretch formability is not necessarily determined by the magnitude of the elongation at break. Therefore, when the steel sheet used in the bulge forming test was prepared and the bulge formability was evaluated in detail by creating an FLD (formation limit diagram), good formability was obtained by the bulge hood assumed above. It has become clear that a stretchable formability of 0.15 or more, preferably 0.18 or more is required as the minimum value of the maximum logarithmic strain at the forming limit based on FLD.
  • the present inventors investigated the cause of the case where the superiority or inferiority of the stretch formability of the ferritic stainless steel plate obtained by the conventional technique does not correspond to the magnitude of the elongation at break.
  • the structure after cold rolling annealing is a ferrite single-phase structure in which carbonitrides are dispersed in a large amount and uniformly, and this is the cause. It was.
  • voids are generated in the structure as the amount of strain increases, and when these voids are connected, they become cracks and eventually break.
  • the ferritic stainless steel sheet obtained by the conventional technique is a ferrite single-phase structure in which carbonitride is dispersed in a large amount and uniformly. A very large amount of voids are generated from the entire surface. That is, in the prior art, cracks due to the connection of voids are likely to occur. As a result, even in the case of uniaxial deformation such as a tensile test, rupture occurs because void connection occurs in all directions in stretch forming in which multiaxial stress and strain are applied, even though it shows high elongation at break. It was easy to find out that sufficient stretchability could not be obtained.
  • the present inventors performed hot rolling sheet annealing on a steel sheet having an appropriate component in a two-phase region of a ferrite phase and an austenite phase, and then cold-rolled the steel sheet in a conventional manner, and further performed cold rolling sheet annealing on a single ferrite sheet.
  • an austenite phase with an area ratio of 3 to 20% is generated by hot-rolled sheet annealing. Almost all of the austenite phase is transformed into a martensite phase in the cooling process after hot-rolled sheet annealing.
  • the martensite phase is decomposed into a ferrite phase and a carbonitride during cold-rolled sheet annealing.
  • the structure after the cold-rolled sheet annealing becomes ferrite grains formed by the decomposition of ferrite grains that were ferrite phases and martensite phases from the beginning. That is, there are a large amount of carbonitrides in the grain boundaries and in the grains of the ferrite phase formed by the decomposition of the martensite phase, and in the entire metal structure, ferrite with an extremely large amount of carbonitrides in and on the grain boundaries. It becomes a mixed grain structure composed of ferrite grains with few grains and carbonitrides.
  • the ferrite grains having a high carbonitride are relatively hard, and a hardness difference of a grain unit occurs in the metal structure. It was found that when such a steel sheet is stretched, voids are mainly generated from carbonitrides on the interface between ferrite grains with a large amount of carbonitride and few ferrite grains, and the amount of voids generated in other parts is small. .
  • the steel according to the present invention there is little void formation in a portion where ferrite grains having a large amount of carbonitride are continuously located, a portion where ferrite grains having a small amount of carbonitride are continuous, and a ferrite grain. Therefore, the distance between the voids is longer than that of the ferritic stainless steel plate obtained by the prior art, cracks due to void connection during overhang forming are less likely to occur, and the minimum value of the maximum logarithmic strain at the forming limit based on FLD is small. High stretch formability of 0.15 or more is manifested.
  • the ferrite grains with many carbonitrides generated by subsequent cold-rolled sheet annealing increase, and the interface area between the ferrite grains with many carbonitrides and the few ferrite grains that become the starting point of voids during processing increases.
  • the overhang moldability cannot be expressed. Therefore, the upper limit of each of the C content and the N content needs to be 0.025%.
  • a predetermined amount of austenite phase can be stably secured by annealing in the two-phase region of the ferrite phase and the austenite phase, particularly in the range of 900 to 1100 ° C. Good surface quality can be obtained without excessively coarsening the particle size.
  • the steel having the C content and the N content is subjected to hot-rolled sheet annealing at a two-phase region temperature of a ferrite phase and an austenite phase, which is one of the technical features of the present invention, to thereby obtain an elongation at break and an average r It has been found that beneficial effects are also obtained with respect to value and ridging resistance.
  • hot-rolled sheet annealing was performed at a ferrite single-phase temperature, but in the present invention, hot-rolled sheet annealing is performed at a high temperature that is a two-phase region of a ferrite phase and an austenite phase. Grain growth is further promoted and the crystal grain size is increased appropriately.
  • stimulation of the development of an annealing texture are acquired.
  • the elongation at break is also improved for the following reasons.
  • the amount of carbonitride produced after cold-rolled sheet annealing is reduced, and the generation of voids and the connection of voids during tensile deformation are suppressed. . This also improves the elongation at break.
  • the reason why a beneficial effect can be obtained with respect to ridging resistance is as follows.
  • the austenite phase is generated with a crystal orientation different from that of the ferrite phase before annealing.
  • the metal structure after hot-rolled sheet annealing becomes a two-phase structure of a martensite phase and a ferrite phase.
  • rolling strain is locally concentrated in the ferrite phase sandwiched between the martensite phases, and an orientation difference is formed in the ferrite phase.
  • recrystallization occurs preferentially at a site where the orientation difference is introduced in the subsequent cold-rolled sheet annealing.
  • the ferrite phase colonies are effectively destroyed, and excellent ridging resistance with a ridging height of 2.5 ⁇ m or less is obtained.
  • the steel components have a C content and an N content generated by the austenite phase.
  • the C content and the N content are reduced within a range in which a predetermined amount of austenite phase can be generated.
  • About steel which has such a component after performing hot-rolled sheet annealing at the two-phase region temperature of a ferrite phase and austenite, cold rolling and cold-rolled sheet annealing are performed. As a result, it is necessary to obtain a ferrite single-phase structure composed of ferrite grains containing a large amount of carbonitride and few ferrite grains.
  • C 0.005 to 0.025%
  • C promotes the formation of the austenite phase and has the effect of expanding the two-phase temperature range where the ferrite phase and the austenite phase appear during hot-rolled sheet annealing.
  • a content of 0.005% or more is necessary.
  • the amount of C exceeds 0.025%, the amount of austenite phase produced in the hot-rolled sheet annealing becomes excessive, and the amount of ferrite grains containing many carbonitrides becomes excessive after cold-rolled sheet annealing.
  • the distance between voids in the metal structure is reduced, and breakage due to void connection is likely to occur at the time of molding, and sufficient stretch formability cannot be obtained. Therefore, the C content is in the range of 0.005 to 0.025%. Preferably it is 0.010 to 0.020% of range.
  • Si 0.02 to 0.50% Si is an element that acts as a deoxidizer during steel melting. In order to acquire this effect, 0.02% or more needs to be contained. However, if the amount of Si exceeds 0.50%, the steel sheet becomes hard, the rolling load during hot rolling increases, and the ductility after finish annealing decreases. For this reason, the Si content is in the range of 0.02 to 0.50%. Preferably it is 0.10 to 0.35% of range. More preferably, it is in the range of 0.10 to 0.20%.
  • Mn 0.55 to 1.00% Mn, like C, promotes the formation of an austenite phase and has the effect of expanding the two-phase temperature range in which a ferrite phase and an austenite phase appear during hot-rolled sheet annealing. In order to acquire this effect, 0.55% or more needs to be contained. However, if the amount of Mn exceeds 1.00%, the amount of MnS produced increases and the corrosion resistance decreases. Therefore, the Mn content is set in the range of 0.55 to 1.00%. Preferably it is 0.60 to 0.90% of range. More preferably, it is in the range of 0.75 to 0.85%.
  • P 0.04% or less Since P is an element that promotes grain boundary fracture due to grain boundary segregation, the lower one is desirable, and the upper limit is made 0.04%. Preferably it is 0.03% or less. More preferably, it is 0.01% or less.
  • S 0.01% or less
  • S is an element that exists as sulfide inclusions such as MnS and lowers ductility, corrosion resistance, etc., and particularly when the content exceeds 0.01%, their adverse effects Is noticeable. For this reason, the S amount is desirably as low as possible.
  • the upper limit of the S amount is set to 0.01%. Preferably it is 0.007% or less. More preferably, it is 0.005% or less.
  • Al 0.001 to 0.10%
  • Al is an element that acts as a deoxidizing agent like Si. In order to acquire this effect, 0.001% or more needs to be contained. However, when the Al content exceeds 0.10%, Al-based inclusions such as Al 2 O 3 increase, and the surface properties tend to decrease. Therefore, the Al content is set in the range of 0.001 to 0.10%. Preferably it is 0.001 to 0.07% of range. More preferably, it is in the range of 0.001 to 0.05%.
  • Cr 15.5 to 18.0% Cr is an element having an effect of improving the corrosion resistance by forming a passive film on the surface of the steel sheet. In order to obtain this effect, the Cr amount needs to be 15.5% or more. However, if the Cr content exceeds 18.0%, the austenite phase is not sufficiently generated during hot-rolled sheet annealing, and desired material characteristics cannot be obtained. Therefore, the Cr content is in the range of 15.5 to 18.0%. Preferably it is 16.0 to 17.0% of range. More preferably, it is in the range of 16.0 to 16.5%.
  • Ni 0.1 to 1.0%
  • Ni is an element that improves corrosion resistance, and it is effective to contain it particularly when high corrosion resistance is required.
  • Ni also has the effect of promoting the formation of the austenite phase and expanding the two-phase temperature range in which the ferrite phase and austenite phase appear during hot-rolled sheet annealing. These effects become significant when the content is 0.1% or more. However, if the Ni content exceeds 1.0%, the formability deteriorates, which is not preferable. Therefore, when Ni is contained, the content is made 0.1 to 1.0%. Preferably it is 0.1 to 0.3% of range.
  • N 0.005 to 0.025%
  • N like C and Mn, promotes the formation of the austenite phase and has the effect of expanding the two-phase temperature range in which the ferrite phase and austenite phase appear during hot-rolled sheet annealing.
  • the N amount needs to be 0.005% or more.
  • the N content exceeds 0.025%, the ductility is remarkably lowered, and the amount of austenite phase generated in hot-rolled sheet annealing becomes excessive, and the amount of ferrite grains that are rich in carbonitride after cold-rolled sheet annealing is increased. Becomes excessive.
  • the N content is set in the range of 0.005 to 0.025%. Preferably it is 0.010 to 0.020% of range.
  • the balance is Fe and inevitable impurities.
  • Cu 0.1 to 1.0%
  • V 0.01 to 0.10%
  • Ti 0.001 to 0.05%
  • Nb 0.001 to 0.05%
  • Mo 0.1 to One or more selected from 0.5%
  • Co 0.01 to 0.2%
  • Cu 0.1 to 1.0%
  • Cu is an element that improves corrosion resistance, and it is effective to contain it particularly when high corrosion resistance is required.
  • Cu has an effect of promoting the generation of an austenite phase and expanding a two-phase temperature range in which a ferrite phase and an austenite phase appear during hot-rolled sheet annealing. These effects become significant when the content is 0.1% or more. However, if the Cu content exceeds 1.0%, formability may be deteriorated, which is not preferable. Therefore, when Cu is contained, the content is made 0.1 to 1.0%. Preferably it is 0.2 to 0.3% of range.
  • V 0.01-0.10% V combines with C and N in the steel to reduce solute C and solute N. This improves the average r value. In order to acquire this effect, it is necessary to contain V amount 0.01% or more. However, if the amount of V exceeds 0.10%, the workability is lowered and the manufacturing cost is increased. Therefore, when V is contained, the content is made 0.01 to 0.10%. Preferably it is 0.02 to 0.08% of range.
  • Ti and Nb are elements having a high affinity with C and N, like V, and precipitate as carbide or nitride during hot rolling, reducing the solid solution C and solid solution N in the matrix, and cold rolling. There is an effect of improving workability after sheet annealing. In order to obtain this effect, it is necessary to contain 0.001% or more of Ti and 0.001% or more of Nb. However, when the Ti content exceeds 0.05% or the Nb content exceeds 0.05%, good surface properties cannot be obtained due to excessive precipitation of TiN and NbC.
  • the range when Ti is contained, the range is 0.001 to 0.05%, and when Nb is contained, the range is 0.001 to 0.05%.
  • the amount of Ti is preferably in the range of 0.003 to 0.03%. More preferably, it is in the range of 0.005 to 0.015%.
  • the amount of Nb is preferably in the range of 0.003 to 0.03%. More preferably, it is in the range of 0.005 to 0.015%.
  • Mo 0.1 to 0.5%
  • Mo is an element that improves corrosion resistance, and it is effective to contain it particularly when high corrosion resistance is required. This effect becomes remarkable when the content is 0.1% or more. However, if the Mo content exceeds 0.5%, the austenite phase is not sufficiently generated during hot-rolled sheet annealing, and desired material characteristics cannot be obtained. Therefore, when it contains Mo, it is 0.1 to 0.5%. Preferably it is 0.2 to 0.3% of range.
  • Co 0.01 to 0.2% Co is an element that improves toughness. This effect is obtained when the content is 0.01% or more. On the other hand, if the content exceeds 0.2%, the moldability is lowered. Therefore, if Co is contained, the content is made 0.01 to 0.2%.
  • Mg 0.0002 to 0.0050%
  • Ca 0.0002 to 0.0020%
  • B 0.0002 to 0.0050%
  • REM 0.01 to 0.10%
  • Mg is an element that has an effect of improving hot workability. In order to acquire this effect, 0.0002% or more needs to be contained. However, when the amount of Mg exceeds 0.0050%, the surface quality deteriorates. Therefore, when Mg is contained, the content is made 0.0002 to 0.0050%. Preferably it is 0.0005 to 0.0035% of range. More preferably, it is in the range of 0.0005 to 0.0020%.
  • Ca 0.0002 to 0.0020%
  • Ca is an effective component for preventing nozzle clogging due to crystallization of inclusions that are likely to occur during continuous casting. In order to acquire the effect, 0.0002% or more needs to be contained. However, if the Ca content exceeds 0.0020%, CaS is generated and the corrosion resistance is lowered. Therefore, when Ca is contained, the content is made 0.0002 to 0.0020%. Preferably it is 0.0005 to 0.0015% of range. More preferably, it is in the range of 0.0005 to 0.0010%.
  • B 0.0002 to 0.0050%
  • B is an element effective for preventing embrittlement at low temperature secondary work. In order to acquire this effect, 0.0002% or more needs to be contained. However, when the amount of B exceeds 0.0050%, hot workability deteriorates. Therefore, when B is contained, the content is made 0.0002 to 0.0050%. Preferably it is 0.0005 to 0.0035% of range. More preferably, it is in the range of 0.0005 to 0.0020%.
  • REM 0.01-0.10% REM (Rare Earth Metals) is an element that improves oxidation resistance, and is particularly effective in suppressing the formation of an oxide film on the welded portion and improving the corrosion resistance of the welded portion.
  • a content of 0.01% or more is necessary. However, if the content exceeds 0.10%, productivity such as pickling at the time of cold rolling annealing is lowered.
  • REM is an expensive element, excessive inclusion is not preferable because it causes an increase in manufacturing cost. Therefore, when REM is contained, the content is made 0.01 to 0.10%. Preferably it is 0.01 to 0.05% of range.
  • the ferritic stainless steel sheet of the present invention is subjected to hot rolling on a steel slab having the above component composition, followed by hot rolling sheet annealing at a temperature range of 900 to 1100 ° C. for 5 seconds to 15 minutes, After cold rolling, it is obtained by annealing a cold-rolled sheet that is held at a temperature range of 800 to 900 ° C. for 5 seconds to 5 minutes.
  • 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 directly hot-rolled as cast without heating to form a hot-rolled sheet.
  • the winding temperature is preferably 500 ° C. or higher and 850 ° C. or lower. If it is less than 500 degreeC, a martensite phase will produce
  • Hot-rolled sheet annealing held for 5 seconds to 15 minutes in the temperature range of 900 to 1100 ° C. Thereafter, hot rolling for 5 seconds to 15 minutes in the temperature range of 900 to 1100 ° C. which is a two-phase temperature range of the ferrite phase and austenite phase Sheet annealing is performed.
  • Hot-rolled sheet annealing is an extremely important process for the present invention to obtain excellent formability and ridging resistance.
  • the hot-rolled sheet annealing temperature is less than 900 ° C., sufficient recrystallization does not occur and the ferrite single-phase region is obtained, so that the effects of the present invention that are manifested by annealing in the two-phase temperature region may not be obtained.
  • the annealing temperature exceeds 1100 ° C.
  • the amount of austenite phase produced is significantly reduced, and the predetermined ridging resistance may not be obtained.
  • the annealing time is less than 5 seconds, even if annealing is performed at a predetermined temperature, generation of austenite phase and recrystallization of the ferrite phase do not occur sufficiently, so that desired formability may not be obtained.
  • the annealing time exceeds 15 minutes, C concentration in the austenite phase is promoted and the martensite phase becomes excessively hard.
  • the hot-rolled sheet annealing is held in the temperature range of 900 to 1100 ° C. for 5 seconds to 15 minutes.
  • the temperature is maintained at 920 to 1080 ° C. for 15 seconds to 5 minutes. More preferably, the temperature is kept at 940 to 1040 ° C. for 30 seconds to 3 minutes.
  • cold rolling is preferably performed at a rolling reduction of 50% or more from the viewpoints of extensibility, bendability, press formability, and shape correction.
  • cold rolling and annealing may be repeated twice or more. Further, in order to improve the surface properties, grinding or polishing may be performed.
  • Cold-rolled sheet annealing is carried out for 5 seconds to 5 minutes in a temperature range of 800 to 900 ° C. Next, cold-rolled sheet annealing is performed.
  • Cold-rolled sheet annealing is an important process for making a two-phase structure of a ferrite phase and a martensite phase formed by hot-rolled sheet annealing into a ferrite single-phase structure. If the cold-rolled sheet annealing temperature is less than 800 ° C., sufficient recrystallization does not occur and a predetermined formability cannot be obtained. On the other hand, when the cold-rolled sheet annealing temperature exceeds 900 ° C., the steel component in which the temperature exceeding 900 ° C.
  • the ferrite phase becomes the two-phase temperature range of the ferrite phase and the austenite phase generates a martensite phase after the cold-rolled sheet annealing. Becomes hard, and the predetermined elongation at break and stretchability cannot be obtained. Moreover, even if it is a steel component in which the temperature exceeding 900 ° C. is the ferrite single phase temperature range, the glossiness of the steel sheet is lowered due to the remarkable coarsening of crystal grains, which is not preferable from the viewpoint of surface quality.
  • the annealing time is less than 5 seconds, even if annealing is performed at a predetermined temperature, the ferrite phase is not sufficiently recrystallized, and therefore, a predetermined formability cannot be obtained.
  • cold-rolled sheet annealing is held for 5 seconds to 5 minutes in a temperature range of 800 to 900 ° C.
  • the temperature is maintained at 850 ° C. to 900 ° C. for 15 seconds to 3 minutes.
  • BA annealing (bright annealing) may be performed.
  • Stainless steel having the chemical composition shown in Table 1 was melted in a 50 kg small vacuum melting furnace. These steel ingots were heated at 1150 ° C. for 1 hour and then hot rolled to form hot rolled sheets having a thickness of 3.5 mm. Subsequently, these hot-rolled sheets were subjected to hot-rolled sheet annealing under the conditions shown in Table 2, and then the surfaces were descaled by shot blasting and pickling. Further, after cold rolling to a plate thickness of 0.8 mm, cold rolled sheet annealing was performed under the conditions shown in Table 2. Furthermore, descaling treatment by pickling was performed to obtain a cold-rolled pickling annealed plate (ferritic stainless steel plate).
  • the cold roll pickling annealed plate (ferritic stainless steel plate) thus obtained was evaluated as follows.
  • Photograph the surface of the specimen after 8 cycles of salt spray cycle test measure the rusting area on the specimen surface by image analysis, and calculate the rusting rate (( Rust area / total area of test piece) ⁇ 100 [%]) was calculated.
  • a rusting rate of 10% or less was determined to pass with excellent corrosion resistance ()), more than 10% to 25% or less passed ( ⁇ ), and more than 25% to reject (x).
  • the Cr content falls below the scope of the present invention. With 38 (steel No. S30), although predetermined formability and ridging characteristics were obtained, the predetermined corrosion resistance was not obtained because the Cr content was insufficient.
  • No. C content is below the scope of the present invention.
  • No. 33 (steel No. S25), a predetermined elongation at break and an average r value were obtained, but since austenite generation ability was insufficient, an austenite phase was not formed in hot-rolled sheet annealing, and predetermined ridging resistance and overhanging properties were obtained. Formability could not be obtained.
  • the C content exceeds the range of the present invention.
  • Predetermined ridging resistance and stretch formability were obtained, but the steel sheet was hardened, so that the elongation was lowered and the predetermined breaking elongation was not obtained.
  • No. 27 (steel No. S27) was hardened by excessive Si content, and could not obtain a predetermined elongation at break.
  • No. N content is below the range of the present invention.
  • 40 steel No. S32
  • a predetermined elongation at break and an average r value were obtained, but since austenite forming ability was insufficient, an austenite phase was not formed in hot-rolled sheet annealing, and a predetermined ridging resistance and overhanging property were obtained. Formability could not be obtained.
  • the N content exceeds the range of the present invention.
  • No. 41 (steel No. S33), predetermined ridging resistance characteristics and stretch formability were obtained, but the predetermined breaking elongation was not obtained because the steel plate was hardened. Furthermore, sensitization caused by the precipitation of a large amount of Cr nitride in the structure occurred, and the predetermined corrosion resistance could not be obtained.
  • the ferritic stainless steel sheet obtained by the present invention is particularly suitable for applications requiring press-formed products mainly composed of overhang forming, such as kitchen appliances and tableware.

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Abstract

L'invention concerne une feuille d'acier inoxydable ferritique présentant une résistance à la corrosion appropriée, d'excellentes propriétés de formation et une excellente résistance à la formation de rides, et son procédé de fabrication. Cette feuille d'acier inoxydable ferritique contient, en % en masse, de 0,005 à 0,025 % de C, de 0,02 à 0,50 % de Si, de 0,55 à 1,00 % de Mn, une proportion inférieure ou égale à 0,04 % de P, une proportion inférieure ou égale à 0,01 % de S, de 0,001 à 0,10 % d'Al, de 15,5 à 18,0 % de Cr, de 0,1 à 1,0 % de Ni, et de 0,005 à 0,025 % de N, le reste comprenant du Fe et des impuretés inévitables, l'allongement à la rupture de la feuille d'acier inoxydable ferritique étant supérieur ou égal à 28 %, la valeur r moyenne correspondante étant supérieure ou égale à 0,75, et la valeur minimale de la souche logarithmique maximale de la limite de formation sur la base d'un diagramme des déformations limites (FLD) étant supérieure ou égale à 0,15.
PCT/JP2015/003339 2015-07-02 2015-07-02 Feuille d'acier inoxydable ferritique et son procédé de fabrication WO2017002147A1 (fr)

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CN110546293A (zh) * 2017-04-25 2019-12-06 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法
CN110546293B (zh) * 2017-04-25 2022-07-29 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法
US11401573B2 (en) 2017-04-25 2022-08-02 Jfe Steel Corporation Ferritic stainless steel sheet and method for manufacturing the same
CN109722508A (zh) * 2017-10-27 2019-05-07 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法
CN109722508B (zh) * 2017-10-27 2020-10-02 杰富意钢铁株式会社 铁素体系不锈钢板及其制造方法
WO2022085708A1 (fr) * 2020-10-23 2022-04-28 日鉄ステンレス株式会社 Acier inoxydable ferritique et procédé de fabrication d'acier inoxydable ferritique
CN115917029A (zh) * 2020-10-23 2023-04-04 日铁不锈钢株式会社 铁素体系不锈钢及铁素体系不锈钢的制造方法
JP7374338B2 (ja) 2020-10-23 2023-11-06 日鉄ステンレス株式会社 フェライト系ステンレス鋼およびフェライト系ステンレス鋼の製造方法

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US20180171430A1 (en) 2018-06-21
KR20180008788A (ko) 2018-01-24
JP5884211B1 (ja) 2016-03-15
TWI560284B (fr) 2016-12-01
KR102027769B1 (ko) 2019-10-02
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