WO2021205876A1 - 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 - Google Patents

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 Download PDF

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WO2021205876A1
WO2021205876A1 PCT/JP2021/012196 JP2021012196W WO2021205876A1 WO 2021205876 A1 WO2021205876 A1 WO 2021205876A1 JP 2021012196 W JP2021012196 W JP 2021012196W WO 2021205876 A1 WO2021205876 A1 WO 2021205876A1
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stainless steel
ferritic stainless
annealing
cold
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French (fr)
Japanese (ja)
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祐太 吉村
直樹 平川
石丸　詠一朗
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Nippon Steel Stainless Steel Corp
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Nippon Steel Stainless Steel Corp
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Priority to JP2022514387A priority Critical patent/JP7422218B2/ja
Priority to CN202180020073.5A priority patent/CN115244207B/zh
Priority to KR1020227031042A priority patent/KR20220134780A/ko
Priority to EP21783137.9A priority patent/EP4134461A4/en
Publication of WO2021205876A1 publication Critical patent/WO2021205876A1/ja
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • 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
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys 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
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • 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
    • C22C38/54—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
    • 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
    • C21D2211/008—Martensite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present invention relates to ferritic stainless steel and a method for producing ferritic stainless steel.
  • Patent Document 1 discloses a stainless steel sheet that has been temper-rolled to reduce stretcher strain.
  • One aspect of the present invention is to realize a ferritic stainless steel or the like which can reduce stretcher strain without performing temper rolling and has high press formability.
  • the ferrite stainless steel according to one aspect of the present invention has a mass% of C: 0.12% or less, Si: 1.0% or less, Mn: 1.0% or less, Ni: 1.0% or less, Cr: 12.0 to 18.0%, N: 0.10% or less, Al: 0.50% or less, the balance is Fe and unavoidable impurities, parallel to the rolling direction.
  • the area ratio of the martensite phase in the cross section cut in the plane perpendicular to the rolling width direction is 1.0% or more and less than 15.0%, and the balance excluding the martensite phase from the ferritic stainless steel is mainly It is composed of a ferrite phase, has a yield elongation of 2.0% or less, and a breaking elongation of 22.0% or more.
  • the area ratio of the martensite phase in the cross section of stainless steel cut in a plane parallel to the rolling direction and perpendicular to the rolling width direction is referred to as "martensite area ratio”.
  • the martensite area ratio means the area ratio of the martensite phase to the area of the cross section of the stainless steel cut in a plane parallel to the rolling direction and perpendicular to the rolling width direction.
  • the present inventors have found through diligent studies that the dispersion of the martensite phase is effective for reducing the yield elongation and the stretcher strain.
  • the martensite phase has high strength, it has a property that the yield stress is low, and it has an effect of storing solid solution carbon and nitrogen that cause the yield elongation in the phase, so that it is effective in reducing the yield elongation.
  • excessive dispersion of the martensite phase causes deterioration of characteristics such as a decrease in ductility or a decrease in corrosion resistance due to an increase in strength. From the above, the present inventors can reduce the stretcher strain without performing temper rolling by dispersing an appropriate amount of martensite phase, and obtain a ferritic stainless steel having high press formability. I found that it could be achieved.
  • index value represented by the following formula (1) (hereinafter referred to as an index value) is an index representing the maximum amount of the austenite phase produced by annealing.
  • each element symbol represents the mass% concentration of the element.
  • the austenite phase formed during annealing can be transformed into a martensite phase during the cooling process.
  • the index value By setting the index value to 15 or more and 50 or less, it becomes easy to control the maximum amount of austenite phase produced by annealing and appropriately control the amount of martensite phase produced in the cooling process. Therefore, by setting the index value to 15 or more and 50 or less, it becomes easy to manage the martensite area ratio, which will be described later, to 1.0% or more and less than 15.0%.
  • the present invention is applied to, for example, stainless steel containing the following components, but the present invention is not limited thereto.
  • the stainless steel according to the embodiment of the present invention may contain various components in addition to the following components.
  • C is an important element that forms a carbide with Cr to form an interface that is a source of dislocations when the stainless steel is deformed.
  • the C content is set to 0.12% or less. Further, in order to generate the martensite phase, the C content is preferably 0.030% or more.
  • Si has an effect as an antacid at the melting stage. However, if Si is added in excess, the stainless steel becomes hard and the ductility decreases. Therefore, the Si content is set to 1.0% or less.
  • Mn has an effect as an antacid. However, if Mn is excessively added, the amount of MnS produced increases and the corrosion resistance of the stainless steel decreases. Therefore, the Mn content is set to 1.0% or less.
  • Ni is an austenite-forming element and is an effective element for controlling the martensite area ratio and strength after annealing.
  • the austenite phase is stabilized more than necessary, the ductility of stainless steel is lowered, and the raw material cost of stainless steel is increased. Therefore, the Ni content is set to 1.0% or less.
  • Cr 12.0 to 18.0%> Cr is required to form a passivation film on the surface of the cold-rolled steel sheet to enhance corrosion resistance. However, if Cr is added in excess, the ductility of stainless steel is reduced. Therefore, the Cr content is set to 12.0 to 18.0%.
  • N is an important element that forms a nitride with Cr to form an interface that is a source of dislocations when the stainless steel is deformed. However, if N is added in excess, an excess martensite phase is likely to occur and ductility is reduced. Therefore, the content of N is set to 0.10% or less.
  • Al 0.50% or less> Al, together with an element effective for deoxidation, it is possible to reduce the adverse effects A 2 inclusions in press formability. However, when Al is added in excess, surface defects increase. Therefore, the Al content is set to 0.50% or less.
  • Mo is an element effective for improving corrosion resistance. However, if Mo is added in excess, the raw material cost of stainless steel increases. Therefore, the Mo content is preferably set to 0.50% or less.
  • Cu is an element effective for improving corrosion resistance.
  • the Cu content is preferably set to 1.0% or less.
  • O produces non-metallic inclusions, reducing impact value and fatigue life. Therefore, the O content is preferably set to 0.01% or less.
  • V is an element effective for improving hardness and strength. However, if V is added in excess, the raw material cost of stainless steel increases. Therefore, the V content is preferably set to 0.15% or less.
  • B is an element effective for improving toughness. However, this effect saturates above 0.10%. Therefore, the content of B is preferably set to 0.10% or less.
  • Ti can immobilize C and N and reduce the stretcher strain by forming a carbide or nitride with the solid solution C or N that causes the stretcher strain.
  • Ti is an expensive element, if Ti is added in excess, the raw material cost of stainless steel increases. Therefore, the Ti content is preferably set to 0.50% or less.
  • Co is an element effective for improving corrosion resistance and heat resistance. However, if Co is added in excess, the raw material cost of stainless steel increases. Therefore, the Co content is preferably set to 0.01 to 0.50%.
  • Zr is an element effective for denitrification, deoxidation and desulfurization. However, if Zr is added in excess, the raw material cost of stainless steel increases. Therefore, the Zr content is preferably set to 0.01 to 0.10%.
  • Nb can immobilize C and N and reduce the stretcher strain by forming a carbide or a nitride with the solid solution C or the solid solution N that causes the stretcher strain. ..
  • Nb is an expensive element, if Nb is excessively added, the raw material cost of stainless steel increases. Therefore, the Nb content is preferably set to 0.01 to 0.10%.
  • Mg forms Mg oxide together with Al in molten steel and acts as an antacid.
  • Mg content is preferably set to 0.0005 to 0.0030%, more preferably 0.0020% or less.
  • Ca is an element effective for degassing.
  • the Ca content is preferably set to 0.0003 to 0.0030%.
  • Y is an element effective for improving hot workability and oxidation resistance. However, these effects saturate above 0.20%. Therefore, the Y content is preferably set to 0.01 to 0.20%.
  • ⁇ Rare earth metals excluding Y preferably 0.01 to 0.10% in total>
  • Rare earth metals other than Y Rare Earth Metal: REM
  • REM Rare earth Metal
  • Sc and La are also effective in improving hot workability and oxidation resistance, similarly to Y.
  • these effects saturate above 0.10%. Therefore, the total content of REM excluding Y is preferably set to 0.01 to 0.10%.
  • Sn is an element effective for improving corrosion resistance. However, if Sn is added in excess, hot workability and tenacity are reduced. Therefore, the Sn content is preferably set to 0.001 to 0.500%.
  • Sb is effective in improving workability by promoting the formation of a deformation band during rolling.
  • the Sb content is preferably set to 0.001 to 0.500%, more preferably 0.200% or less.
  • Pb is an element effective for improving free-cutting property.
  • the Pb content is preferably set to 0.01 to 0.10%.
  • W is an element effective for improving high temperature strength. However, if W is added in excess, the raw material cost of stainless steel increases. Therefore, the W content is preferably set to 0.01 to 0.50%.
  • ⁇ Others> The rest other than the components mentioned above are Fe and unavoidable impurities.
  • Inevitable impurities as used herein, mean impurities that are unavoidably mixed in during production.
  • the content of unavoidable impurities is preferably as low as possible.
  • FIG. 1 is a flowchart showing an example of a method for manufacturing stainless steel according to an embodiment of the present invention.
  • the stainless steel containing the above components is melted to produce a steel slab.
  • general melting equipment and melting conditions for stainless steel can be used.
  • the steel slab is hot rolled to produce a hot-rolled steel sheet.
  • a general hot rolling apparatus and hot rolling conditions for stainless steel can be used.
  • the hot-rolled steel sheet is heat-treated at 500 to 1100 ° C. to soften it.
  • the softening step S3 may be omitted depending on, for example, the composition of stainless steel or the conditions of hot rolling or cold rolling.
  • the hot-rolled steel sheet after the softening step S3 or, if the softening step S3 can be omitted the hot-rolled steel sheet after the hot-rolling step S2 is cold-rolled to obtain the cold-rolled steel sheet.
  • a general cold rolling apparatus and cold rolling conditions for stainless steel can be used.
  • the cold-rolled steel sheet is annealed.
  • the maximum annealing temperature (° C.), which is the maximum temperature in the annealing step S5, is set as follows.
  • the TA represented by the following formula (2) is calculated.
  • the TA may be calculated in advance.
  • TA 35 ⁇ (Cr + 1.72Mo + 2.09Si + 4.86Nb + 8.29V + 1.77Ti + 21.4Al + 40B-7.14C-8.0N-3.24Ni-1.89Mn-0.51Cu) +310 ...
  • each element symbol represents the mass% concentration of the element.
  • the maximum annealing temperature (° C.) is set to 0.65 ⁇ TA + 291 or more and 1.10 ⁇ TA-48 or less.
  • the maximum annealing temperature (° C.) is 0.65 ⁇ TA + 291 or more and 1050 ° C. or less.
  • TA is a guideline for the start temperature of austenite phase formation.
  • the temperature in the annealing step S5 exceeds TA, the amount of austenite increases, and when the temperature further rises, the amount of austenite reaches a peak amount and then starts to decrease.
  • the maximum annealing temperature is TA or more and the austenite amount is high in order to make the martensite area ratio described later 1.0% or more and less than 15.0%. It should be set below a temperature that does not increase too much.
  • TA is a guideline for the regression equation, and there is a discrepancy from the temperature at which the austenite phase actually begins to form. Therefore, as a result of diligent studies by the present inventors, when TA is less than 921, the maximum annealing temperature (° C.) is set to 0.65 ⁇ TA + 291 or more and 1.10 ⁇ TA-48 or less to obtain martensite. It was found that the area ratio could be 1.0% or more and less than 15.0%.
  • the peak amount of the austenite phase itself is small, so that even if the total amount of the peak amount is transformed from the austenite phase to the martensite phase, the martensite area ratio is 1.0% or more. It could be less than 15.0%. Therefore, when TA is 921 or more, it is not necessary to limit the upper limit of the maximum annealing temperature (° C.) to 1.10 ⁇ TA-48. In this case, annealing at an excessively high temperature causes coarsening of crystal grains and causes deterioration of characteristics such as rough skin during processing. Therefore, the upper limit of the maximum annealing temperature is set to 1050 ° C.
  • the heating rate in the annealing step S5 is preferably set to 10 ° C./s or higher.
  • the heating time in the annealing step S5 can be shortened, so that the time required for producing the ferritic stainless steel can be shortened. Therefore, the productivity of ferritic stainless steel can be improved.
  • the soaking time at the maximum annealing temperature in the annealing step S5 is preferably set to 5 seconds or more.
  • the austenite phase can be reliably generated during the soaking.
  • the austenite phase transforms into a martensite phase during cooling. Therefore, by setting the soaking time to 5 seconds or more, it becomes easier to control the martensite area ratio, which will be described later, to 1.0% or more and less than 15.0%.
  • the cooling rate in the annealing step S5 is set to 5.0 ° C./s or higher. As will be described later, if the cooling rate is less than 5.0 ° C./s, the austenite phase is transformed into a stable ferrite phase due to the time required for cooling from the maximum annealing temperature, so that the martensite area The ratio decreases and the yield growth increases. Therefore, in order to reduce the yield elongation, the cooling rate in the annealing step S5 is set to 5.0 ° C./s or higher.
  • the balance of stainless steel excluding the martensite phase is mainly composed of a ferrite phase.
  • the martensite area ratio of stainless steel in this embodiment is 1.0% or more and less than 15.0%.
  • the martensite area ratio can be measured using, for example, EBSD (electron back scattering diffraction) crystal orientation analysis. Specifically, first, an EBSD detector mounted on a scanning electron microscope (SEM) is used to acquire an EBSD pattern of a cross section of stainless steel.
  • SEM scanning electron microscope
  • the EBSD pattern acquisition conditions are as follows, for example.
  • the acquired EBSD pattern is made into an IQ (Image Quality) image by OIM analysis software.
  • the IQ image is an image analysis representing sharpness.
  • the martensite phase has a more complicated internal structure than the ferrite phase and has low sharpness, so that it appears dark in the IQ image.
  • the ferrite phase has a simpler internal structure and higher sharpness than the martensite phase, so that it appears bright in the IQ image.
  • the martensite area ratio can be calculated by binarizing the IQ image and dividing the area of the martensite phase by the area of the entire stainless steel.
  • Yield elongation and breaking elongation Yield elongation and elongation at break of stainless steel can be measured, for example, by a tensile test specified in JIS Z 2241. At this time, as the tensile test piece, for example, one having a shape defined as JIS13B in JISZ2201 can be used.
  • the yield elongation of the stainless steel in the present embodiment is 2.0% or less, and the breaking elongation is 22.0% or more.
  • the ferrite-based stainless steel according to one aspect of the present invention has a mass% of C: 0.12% or less, Si: 1.0% or less, Mn: 1.0% or less, Ni: 1.0% or less, Cr. 12.0 to 18.0%, N: 0.10% or less, Al: 0.50% or less, the balance is composed of Fe and unavoidable impurities, and cut in a plane parallel to the rolling direction and perpendicular to the rolling width direction.
  • the area ratio of the martensite phase in the cross section is 1.0% or more and less than 15.0%, and the remainder of the ferritic stainless steel excluding the martensite phase is mainly composed of the ferrite phase and has a yield elongation. It is 2.0% or less and the elongation at break is 22.0% or more.
  • the yield elongation can be reduced while maintaining the large fracture elongation of the ferritic stainless steel.
  • the ferritic stainless steel according to one aspect of the present invention is represented by the following formula (1), and the following index values representing the maximum amount of austenite phase produced by annealing are 15 or more and 50 or less.
  • index value 420C-11.5Si + 7Mn + 23Ni-11.5Cr-12Mo + 9Cu-49Ti-52Al + 470N + 189 ...
  • each element symbol represents the mass% concentration of the element.
  • the index value is 15 or more and 50 or less.
  • the austenite phase formed during annealing can be transformed into a martensite phase during the cooling process.
  • the index value is 15 or more and 50 or less.
  • ferritic stainless steel according to one aspect of the present invention has Mo: 0.5% or less, Cu: 1.0% or less, O: 0.01% or less, V: 0.15% or less in mass%. , B: 0.10% or less, Ti: 0.50% or less, and one or more selected from these may be further contained.
  • the corrosion resistance of the ferritic stainless steel when Mo is contained in an amount of 0.5% or less, the corrosion resistance of the ferritic stainless steel can be improved and the increase in raw material cost can be suppressed. Further, when Cu is contained in an amount of 1.0% or less, the corrosion resistance of the ferritic stainless steel can be improved. Further, when the O content is 0.01% or less, the impact value and the tired life can be improved. Further, when V is contained in an amount of 0.15% or less, the hardness and strength of the ferritic stainless steel can be effectively improved. Further, when B is contained in an amount of 0.10% or less, the toughness of the ferritic stainless steel can be effectively improved. Further, when Ti is contained in an amount of 0.50% or less, the stretcher strain can be reduced and the increase in raw material cost can be suppressed.
  • the ferrite-based stainless steel according to one aspect of the present invention has Co: 0.01 to 0.50%, Zr: 0.01 to 0.10%, Nb: 0.01 to 0.10 in mass%. %, Mg: 0.0005 to 0.0030%, Ca: 0.0003 to 0.0030%, Y: 0.01 to 0.20%, rare earth metals excluding Y: 0.01 to 0.10 in total %, Sn: 0.001 to 0.500%, Sb: 0.001 to 0.500%, Pb: 0.01 to 0.10%, W: 0.01 to 0.50%. It may further contain one kind or two or more kinds.
  • the rare earth metal excluding Y is contained in the range of 0.01 to 0.10% in total, the hot workability and the oxidation resistance can be effectively improved. Further, when Sn is contained in an amount of 0.001 to 0.500%, corrosion resistance can be improved. Further, when Pb is contained in an amount of 0.01 to 0.10%, the free-cutting property can be improved. Further, when W is contained in an amount of 0.01 to 0.50%, the high temperature strength can be improved.
  • the method for producing a ferritic stainless steel according to one aspect of the present invention is, in terms of mass%, C: 0.12% or less, Si: 1.0% or less, Mn: 1.0% or less, Ni: 1.
  • (Index value) 420C-11.5Si + 7Mn + 23Ni-11.5Cr-12Mo + 9Cu-49Ti-52Al + 470N + 189 ...
  • each element symbol represents the mass% concentration of the element, after the hot rolling step of hot rolling a steel slab to produce a hot-rolled steel sheet and the hot rolling step.
  • the cold-rolling step of cold-rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet and the ablation step of annealing the cold-rolled steel sheet after the cold-rolling step are included in the baking step.
  • About TA expressed by the following formula (3) of steel slab TA 35 ⁇ (Cr + 1.72Mo + 2.09Si + 4.86Nb + 8.29V + 1.77Ti + 21.4Al + 40B-7.14C-8.0N-3.24Ni-1.89Mn-0.51Cu) +310 ...
  • each element symbol represents the mass% concentration of the element
  • the maximum annealing temperature (° C.) is 0.65 ⁇ TA + 291 or more.
  • the maximum annealing temperature (° C.) is 0.65 ⁇ TA + 291 or more and 1050 ° C. or less, and the cooling rate is 5. Anneal at 0 ° C./s or higher.
  • the maximum annealing temperature in the annealing process is appropriately set according to the composition of the ferritic stainless steel, and the cooling rate is appropriately controlled. Therefore, the area ratio of the martensite phase can be controlled more reliably in the range of 1.0% or more and less than 15.0%. Therefore, the stretcher strain can be reduced without performing temper rolling, and a ferritic stainless steel having high press formability can be manufactured more reliably.
  • a hot-rolled steel sheet after the hot rolling step and before the cold rolling step is heat-treated at 500 ° C. or higher and 1100 ° C. or lower to be soft.
  • a softening step of rolling may be further included. According to the above method, since the softening step is further included, wrinkles (stretcher strain) generated in parallel with the rolling direction can be reduced when the ferritic stainless steel is pressed or pulled.
  • the heating rate in the annealing step may be 10 ° C./s or more. According to the above method, since the temperature rising time in the annealing step can be shortened, the time required for producing the ferritic stainless steel can be shortened. Therefore, the productivity of ferritic stainless steel can be improved. Further, since the heating rate in the annealing step is appropriately controlled, the area ratio of the martensite phase can be more reliably controlled within the range of 1.0% or more and less than 15.0%. Therefore, the stretcher strain can be reduced without performing temper rolling, and the ferritic stainless steel having high press formability can be more reliably produced.
  • the soaking time at the maximum annealing temperature in the annealing step may be 5 seconds or more.
  • the soaking time in the annealing step is appropriately controlled, so that the area ratio of the martensite phase can be controlled in the range of 1.0% or more and less than 15.0% more reliably. can. Therefore, the stretcher strain can be reduced without performing temper rolling, and the ferritic stainless steel having high press formability can be more reliably produced.
  • Table 1 The underlined values in Table 1 indicate values that are outside the preferred range in one embodiment of the present invention.
  • Ex1 to Ex10 are all in mass%, C: 0.12% or less, Si: 1.0% or less, Mn: 1.0% or less, Ni: 1.0% or less, Cr: 12.0 to 18.0%, N: 0.10% or less, Al: 0.50% or less, the balance consisted of Fe and unavoidable impurities, and the index value was 15 or more and 50 or less.
  • the contents of Mo, Nb, V, B, Ti and Cu of Ex5, Ex6, Ex7, Ex8, Ex9 and Ex10 were higher than those of the other composition examples, respectively.
  • CE1 had a C content of over 0.12% and an index value of over 50.
  • CE2 had a Cr content of more than 18.0% and an index value of less than 15. The index value of CE3 exceeded 50.
  • a hot-rolled steel sheet having a plate thickness of 3 mm and a plate width of 150 mm was produced. Then, the hot-rolled steel sheet was heat-treated at 980 ° C. for 30 seconds to soften it, and then cold-rolled to produce a cold-rolled steel sheet having a plate thickness of 1 mm and a plate width of 150 mm.
  • the lower limit of the recommended annealing temperature (° C.) was set to 0.65 ⁇ TA + 291 and the upper limit was set to 1050 ° C.
  • the upper limit of the recommended annealing temperature was set to 1050 ° C.
  • the composition and the actual annealing condition number are connected by "-" to represent the stainless steel in which the cold-rolled steel sheet of each composition is annealed under each annealing condition.
  • "stainless steel Ex1-2” is a stainless steel obtained by annealing a cold-rolled steel sheet having a composition of Ex1 under annealing conditions 2 (maximum annealing temperature: 832 ° C., soaking time: 5 seconds, cooling rate: 30 ° C./s). Represents.
  • Table 2 also shows the measurement results of the physical properties of each stainless steel. Specifically, for each stainless steel, the martensite area ratio was measured by EBSD crystal orientation analysis. Further, a JIS 13B test piece specified in JIS Z2201 was cut out from each stainless steel in the rolling direction, and a tensile test specified in JIS Z 2241 was performed to measure the yield elongation and the elongation at break of each stainless steel. The smaller the yield elongation, the less stretcher strain during press forming. Further, the larger the breaking elongation, the higher the ductility of the stainless steel and the better the press formability.
  • the underlined values in Table 2 indicate values that are outside the preferred range in one embodiment of the present invention.
  • the maximum annealing temperature under actual annealing conditions is the recommended annealing temperature. It was lower than the lower limit of. In these stainless steels, the martensite area ratio was as low as less than 1.0%, and the yield elongation was more than 2.0%. Therefore, it is suggested that stretcher strains are likely to occur in these stainless steels. It is presumed that the reason why the martensite area ratio was low in these stainless steels was that it was difficult to form the austenite phase, which is the martensite phase, due to the phase transformation during cooling due to the low maximum annealing temperature.
  • the maximum annealing temperature under actual annealing conditions was higher than the upper limit of the recommended annealing temperature.
  • the martensite area ratio was as high as 15.0% or more, and the elongation at break was as small as less than 22.0%. Therefore, it is suggested that these stainless steels have low press formability. It is presumed that the reason why the martensite area ratio was high in these stainless steels was that the high maximum annealing temperature produced a large amount of austenite at the maximum annealing temperature, and the martensite phase was generated more than necessary during cooling. ..
  • the cooling rate under actual annealing conditions was less than 5.0 ° C./s.
  • the martensite area ratio was as low as less than 1.0%, and the yield elongation was more than 2.0%. Therefore, it is suggested that stretcher strains are likely to occur in these stainless steels. It is presumed that the reason why the martensite area ratio was low in these stainless steels was that the austenite phase was transformed into a stable ferrite phase due to the long cooling time from the maximum annealing temperature.
  • stainless steels Ex1-2 to 3, Ex2-2 to 8, 10, 11, Ex3-2, Ex4-2 to 6, 8, Ex5-2, Ex6-2, Ex7-2, Ex8-2, Ex9- In 2 and Ex10-2 (hereinafter collectively referred to as stainless steel ExG)
  • the maximum annealing temperature was within the recommended annealing temperature range.
  • the soaking time was 5 seconds or more, and the cooling rate was 5 ° C./s or more.
  • Ex1 to Ex10 are all in mass%, C: 0.12% or less, Si: 1.0% or less, Mn: 1.0% or less, Ni: 1.0% or less, Cr: It was 12.0 to 18.0%, N: 0.10% or less, Al: 0.50% or less, and the balance consisted of Fe and unavoidable impurities, and the index value was 15 or more and 50 or less.
  • the martensite area ratio of the stainless steel ExG was 1.0% or more and less than 15.0%.
  • the yield elongation of the stainless steel ExG was 2.0% or less and the breaking elongation was 22.0% or more.
  • the stretcher strain can be reduced with stainless steel ExG. Further, since the elongation at break is 22.0% or more, it is suggested that the stainless steel ExG has good press formability.
  • the lower limit (746 ° C) of the recommended annealing temperature exceeds the upper limit (723 ° C), and strictly speaking, the range of the recommended annealing temperature could not be specified. Therefore, the annealing was performed with 730 ° C., which is between the two values, as the maximum annealing temperature, but the martensite area ratio was as high as 80.2% and the elongation at break was as small as 9.7%. It is presumed that the reason for this is that the index value exceeds 50, so that the amount of austenite produced at the maximum annealing temperature is large and the martensite phase is generated more than necessary during cooling.
  • the present invention can be used for manufacturing ferritic stainless steel and ferritic stainless steel.

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PCT/JP2021/012196 2020-04-10 2021-03-24 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 Ceased WO2021205876A1 (ja)

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CN202180020073.5A CN115244207B (zh) 2020-04-10 2021-03-24 铁素体类不锈钢及铁素体类不锈钢的制造方法
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KR20240098331A (ko) * 2022-12-21 2024-06-28 주식회사 포스코 구조용 페라이트계 스테인리스강 및 그 제조방법

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