WO2019039774A1 - Acier inoxydable ferritique ayant une ténacité à l'impact à basse température améliorée et son procédé de production - Google Patents

Acier inoxydable ferritique ayant une ténacité à l'impact à basse température améliorée et son procédé de production Download PDF

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WO2019039774A1
WO2019039774A1 PCT/KR2018/008969 KR2018008969W WO2019039774A1 WO 2019039774 A1 WO2019039774 A1 WO 2019039774A1 KR 2018008969 W KR2018008969 W KR 2018008969W WO 2019039774 A1 WO2019039774 A1 WO 2019039774A1
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ferritic stainless
stainless steel
rolling
less
temperature
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PCT/KR2018/008969
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English (en)
Korean (ko)
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공정현
이문수
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주식회사 포스코
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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 and a method of manufacturing the ferritic stainless steel, and more particularly, to a ferritic stainless steel having improved low temperature impact toughness and a method of manufacturing the ferritic stainless steel.
  • ferritic stainless steels are widely used in building materials, kitchen containers, and household appliances.
  • Ferritic stainless steels are lower in workability, toughness and high temperature strength than austenitic stainless steels, but are less expensive because they do not contain a large amount of Ni, and have recently been used in automotive exhaust system components because of their small thermal expansion.
  • ferritic stainless steels containing high Cr and containing Nb and Ti have poor workability and impact toughness as their thickness becomes thicker than those of austenitic stainless steels. Therefore, brittle brittle brittle cracks may occur during cold rolling at a target thickness after hot rolling, cracks may be generated when the plate is broken due to crack propagation, or when the final cold rolled product is formed into a predetermined shape And it is difficult to develop an aggregate structure related to workability, so that it is difficult to manufacture cold-rolled products themselves.
  • ferritic stainless steels containing Nb and Ti are firstly reacted with carbon (C) and nitrogen (N), which are interstitial elements, during precipitation of Ti in molten steel at a high temperature,
  • C carbon
  • N nitrogen
  • Embodiments of the present invention are to provide a ferritic stainless steel improved in low temperature impact toughness through grain refinement and aggregate structure control through control of an alloy component and a manufacturing process of a ferritic stainless steel and a method for manufacturing the ferritic stainless steel.
  • the ferritic stainless steel improved in low temperature impact toughness includes 17.0 to 20% of Cr, 0.05 to 1.0% of Nb, 0.05 to 0.45% of Ti, 0.03% or less of C (Excluding 0), N: not more than 0.03% (excluding 0), the balance of Fe and other unavoidable impurities, satisfies the following formulas (1) to (3) and has a thickness of 1.8 mm or more.
  • the? -Fibre (111) refers to a group of aggregates of orientations generated in a direction orthogonal to the (111) plane of the texture.
  • the ferritic stainless steel can satisfy the following formula (4).
  • a method for manufacturing a semiconductor device comprising the steps of: providing an alloy containing at most 0.6% of Si (excluding 0), 0.5% or less of Mn (excluding 0) 0.01% or less (excluding 0).
  • the ferritic stainless steel may be a cold rolled annealed steel sheet having a thickness of 1.8 to 2.2 mm.
  • the Charpy impact test value at -40 ⁇ may be 140 J / cm 2 or more.
  • the Ductile to Brittle Transition Temperature (DBTT) value may be less than -45 ° C.
  • a method of manufacturing a ferritic stainless steel having improved low temperature impact toughness includes: 17 to 20% of Cr, 0.05 to 1.0% of Nb, 0.05 to 0.45% of Ti, 0.03 to 0.03 of C, % Or less (excluding 0), N: 0.03% or less (excluding 0), the balance of Fe and other unavoidable impurities, and satisfying the following formula (1): Reheating the slab at a temperature of 1,220 ⁇ ⁇ or less and subjecting the slab to hot rolling; And cold rolling the hot rolled hot rolled sheet. In the cold rolling step, the cold rolled annealed steel sheet is cold rolled at a temperature of not higher than 1,050 ⁇ to produce a cold rolled annealed steel sheet having a final thickness of at least 2.0 mm.
  • the reduction rate in the last rolling of the rough rolling is 35% or more
  • the temperature at the rear stage of rough rolling is 950 to 1,050 ⁇ ⁇ , Lt; 0 > C or less to produce a hot-rolled steel sheet having a final sheet thickness of 5.0 to 8.0 mm.
  • hot rolling may be performed at a temperature of 1,050 ° C or lower after hot rolling.
  • the cold-rolled and annealed steel sheet may satisfy the following formulas (2) and (3).
  • the cold-rolled and annealed steel sheet may have a Charpy impact test value of 140 J / cm 2 or more at -40 ° C and a DBTT of -45 ° C or less.
  • Embodiments of the present invention provide a ferritic stainless steel improved in low temperature impact toughness which can be used in cold regions and winter months through grain refinement and aggregate structure control by controlling alloy components and manufacturing processes of ferritic stainless steels and a method for manufacturing the ferritic stainless steels can do.
  • 1 is a graph for explaining impact toughness of a ferrite stainless steel of 2 mm thickness according to an embodiment of the present invention.
  • the ferritic stainless steel improved in low temperature impact toughness includes 17.0 to 20% of Cr, 0.05 to 1.0% of Nb, 0.05 to 0.45% of Ti, 0.03% or less of C (Excluding 0), N: not more than 0.03% (excluding 0), the balance of Fe and other unavoidable impurities, satisfies the following formulas (1) to (3) and has a thickness of 1.8 mm or more.
  • the? -Fibre (111) refers to a group of aggregates of orientations generated in a direction orthogonal to the (111) plane of the texture.
  • the ferritic stainless steel improved in low temperature impact toughness includes 17.0 to 20% of Cr, 0.05 to 1.0% of Nb, 0.05 to 0.45% of Ti, 0.03% or less of C (Excluding 0), N: 0.03% or less (excluding 0), the balance Fe and other unavoidable impurities.
  • Chromium (Cr) is the most important element added for securing the corrosion resistance and oxidation resistance of stainless steel. In the present invention, it is added in an amount of 17.0% or more. However, if the content is excessive, not only the production cost increases but also the intergranular corrosion occurs, so that the content is limited to 20% or less.
  • NbN is preferentially bonded with intercalation elements carbon (C) and nitrogen (N) to form a precipitate that inhibits deterioration of corrosion resistance. NbN attaches to TiN and precipitates. When NbN precipitates, TiN A small amount of a Cr-depleted region is formed so as not to affect the corrosion resistance.
  • the content of Nb is less than 0.05%, there is a problem that the high temperature strength of the material is lowered and the grain size becomes coarse because the amount of Nb contained in the material is small.
  • the content of Nb exceeds 1%, not only the raw material cost rises, Thereby impeding the propagation of the electric potential, increasing the resistance to the propagation of stress and electric potential, and degrading the plastic deformation, thereby deteriorating toughness.
  • Titanium (Ti) is an element effective in reducing the amount of solid carbon and solid nitrogen in steel by fixing carbon (C) and nitrogen (N) and improving the high temperature strength and corrosion resistance of steel. But also surface defects are formed due to the formation of Ti inclusions, and the elongation and the low-temperature impact toughness are weakened by increasing the amount of solute Ti, which is limited to 0.45% or less.
  • the carbon (C) is an interstitial element that improves the strength of the material.
  • the impurities increase and the elongation and the work hardening index (n value) DBTT) increases and the impact characteristic is weakened, so that the upper limit is limited to 0.03%.
  • the lower limit can be limited to 0.002%.
  • Nitrogen (N) is an element that accelerates recrystallization by precipitation of austenite during hot rolling.
  • n value elongation and work hardening index
  • DBTT brittle transition temperature
  • the lower limit can be limited to 0.002%.
  • the ferritic stainless steel may contain not more than 0.6% of Si (excluding 0), 0.5% or less of Mn (excluding 0), 0.5% or less of Ni (excluding 0), 0.05 to 0.4% of Cu, Al: 0.01% or less (excluding 0).
  • Silicon (Si) is an element added for deoxidation of molten steel and stabilization of ferrite during steelmaking. However, if the content is excessive, the material is hardened and ductility of the steel is deteriorated, and it is limited to 0.6% or less. Preferably, the content of Si may be 0.01 to 0.5%.
  • Manganese (Mn) may be added in an amount of 0.01% or more as an element to be added in terms of corrosion resistance. However, when 0.5% or more is exceeded, there is a problem that the impurities of the material increase and the elongation and the corrosion resistance are deteriorated.
  • the content of Mn may be 0.01 to 0.5%.
  • Ni 0.5% or less (excluding 0)
  • Nickel (Ni) is an element added to improve corrosion resistance. However, if the content is excessive, stress cracking may occur, so it is limited to 0.5% or less. Preferably, the content of Ni may be 0.1 to 0.5%.
  • Copper (Cu) may be added in an amount of 0.05% or more as an element added for improving corrosion resistance. However, if the content is excessive, the workability may deteriorate, and therefore, it is preferable to limit the content to 0.4% or less.
  • Aluminum (Al) is a powerful deoxidizer, which serves to lower the oxygen content in molten steel. However, if the content is excessive, a sleeve defect of the cold-rolled strip occurs due to the increase of non-metallic inclusions, and at the same time, the weldability is deteriorated.
  • the content of Al may be 0.001 to 0.1%.
  • P is an impurity inevitably contained in the steel, and is an element that causes grain boundary corrosion during pickling or hinders hot workability. Therefore, it is preferable to control the content as low as possible. In the present invention, the upper limit of the content of P is controlled to 0.05%.
  • S is an impurity inevitably contained in steel, and is an element that segregates in grain boundaries and is a main cause of inhibiting hot workability. Therefore, it is preferable to control the content to be as low as possible. In the present invention, the upper limit of the content of S is controlled to 0.005%.
  • ferritic stainless steels containing a large amount of Nb and Ti are firstly reacted with carbon (C) and nitrogen (N), which are interstitial elements during the cooling of Ti at a high temperature, ,
  • C carbon
  • N nitrogen
  • the propagation of the potential generated during processing interferes with resistance to the propagation of stress and the propagation of dislocations, resulting in a drastic decrease in plastic deformation.
  • Nb is contained in a larger amount than Ti
  • the surplus Nb remaining after reaction with C and N is converted into Fe (Nb), which is an intermetallic compound having a dense packed structure of Fe 2 Nb type, phase is formed and the impact toughness is weakened.
  • the reheating temperature of the material before hot rolling is lowered, the rough rolling load distribution at the time of hot rolling is moved to the rear end, and strong rolling is performed at a lower temperature, (homogeneous and fine crystals were obtained by accelerating the recrystallization and homogenization of the inner crystals during annealing after cold rolling.
  • the phase fraction of the ⁇ -fiber 111 which is known to improve the toughness of the material, is increased to have a thickness of 1.8 mm or more, and a ferritic stainless steel final cooled To improve the impact resistance at low temperatures.
  • the? -Fibre (111) refers to a group of aggregates of orientations generated in a direction orthogonal to the (111) plane of the texture.
  • the ferritic stainless steel according to one embodiment of the present invention is a cold-rolled annealed steel sheet having a thickness of 1.8 mm or more, for example, a cold-rolled annealed steel sheet having a thickness of 1.8 to 2.2 mm.
  • the ferritic stainless steel satisfies the following formula (1).
  • the ferritic stainless steel satisfies the following formula (2).
  • the ⁇ -fiber (111) is a texture known to improve the toughness of the material and can increase the phase fraction of the ⁇ -fiber (111) texture by accumulating strain energy through the control of hot rolling conditions.
  • B is less than 24.0%, sufficient low temperature impact toughness desired in the present invention can not be obtained.
  • the fraction of the ⁇ -fiber (111) phase can be achieved by controlling the hot rolling condition of the present invention, and the ferritic stainless steel produced according to the conventional process has a ⁇ -fiber (111) phase fraction of less than about 20.0% And a Charpy impact test value of -40 DEG C of less than 20 J / cm < 2 > (See Table 1)
  • the ferritic stainless steel satisfies the following formula (3).
  • the ferritic stainless steel satisfies the following formula (4).
  • the ferritic stainless steel according to one embodiment of the present invention has a Charpy impact test value of 140 J / cm 2 or more at a temperature of -40 ° C, thereby improving the low-temperature impact resistance of the stainless steel.
  • the ferritic stainless steel satisfies the following formula (5).
  • DBTT Ductile to Brittle Transition Temperature
  • DBTT is a ductile brittle transition temperature, and the fracture behavior is changed from soft fracture to brittle fracture based on the DBTT temperature. Accordingly, the ferritic stainless steel according to one embodiment of the present invention has DBTT It has a value of minus 45 ° C or less and can be improved in workability even at a low temperature.
  • the slab reheating temperature, rough rolling reduction ratio, and finish rolling out temperature (FDT) should be controlled during the hot rolling process.
  • a ferritic stainless steel for producing the ferritic stainless steel according to the present invention comprises 17.0 to 20% of Cr, 0.05 to 1% of Nb, 0.05 to 0.45% of Ti, %, C: not more than 0.03% (excluding 0), N: not more than 0.03% (excluding 0), the balance Fe and other unavoidable impurities are produced in a usual manner to produce a slab.
  • the rough rolling load distribution can be shifted to the lower end temperature, which is lower than the shearing temperature.
  • the hot rolling when the hot rolling is performed at the final rolling, it is strongly pressed down to 35% or more, thereby allowing the nucleation sites to be maximally induced, thereby increasing the fine and uniform crystal grains.
  • the temperature at the downstream end of the hot rough rolling can be controlled to 950 to 1,050 ° C.
  • finishing mill delivery temperature designed to be higher than the recrystallization temperature is maintained at 920 ° C or lower so that sufficient deformation energy is given to the inside of the slab so that recrystallization may actively occur during hot rolling and annealing.
  • the finish rolling-out temperature may be 850 DEG C or less.
  • Such a low temperature hot rolling step affects the texture of the hot rolled annealed structure and the final cold rolled steel, thereby improving the workability during cold rolling and the formability of the final cold rolled annealed material.
  • the hot-rolled and annealed heat treatment is performed at a temperature of 1,050 ⁇ ⁇ or lower, whereby a hot-rolled annealed steel sheet having a final thickness of 5.0 mm or more can be produced.
  • the hot rolled annealed steel sheet is cold-rolled to a thickness of 2.0 mm
  • a cold-rolled and annealed steel sheet having a final grain thickness of 2.0 mm or more having fine and uniform crystal grains both in the width direction and the longitudinal direction of the cross-section of the work can be produced by accelerating the recrystallization and homogenization of the grain inside the work.
  • 19Cr-0.4Nb STS 430J1L Steel slabs were reheated to 1,200 ° C in a heating zone and were subjected to a rolling reduction of 35% at each of the final rolling (R4) and pre-rolling (R3) of the rough rolling,
  • the hot rolled coil was controlled to 1,020 ⁇ ⁇ and the finish rolling out temperature (FDT) was 850 ⁇ ⁇ to produce a hot rolled coil having a thickness of 5 mm.
  • Annealing heat treatment at 900 ⁇ ⁇ , cold rolling and cold annealing at 900 ⁇ ⁇ are performed to produce a cold-rolled annealed coil having a final thickness of 2.0 mm.
  • the Charpy impact values of the above Examples and Comparative Examples were measured and are shown in Table 1 below.
  • the Charpy impact value was measured by Charpy impact test according to ASTM E 23 standard.
  • FIG. 1 is a graph showing a Charpy impact test value according to temperature for explaining impact toughness of a 2 mm thick ferritic stainless steel cold-rolled annealed steel sheet according to an embodiment of the present invention.
  • FIG. 1 is a graph showing the Charpy impact energy of the embodiment and the comparative example.
  • Fig. 2 is a graph showing measured phase fractions of the texture of the hot-rolled steel sheets of the examples and comparative examples.
  • the ferritic stainless steel according to the embodiment of the present invention is improved in low temperature impact toughness and can be applied to a variety of uses such as a product material of an exhaust system.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

La présente invention concerne un acier inoxydable ferritique ayant une ténacité à l'impact à basse température améliorée et son procédé de production. Un acier inoxydable ferritique selon un mode de réalisation de la présente invention comprend de 18,0 à 20,0 % en poids de Cr, de 0,4 à 2,0 % en poids de Nb, une proportion inférieure ou égale à 0,1 % en poids (mais non nulle) de Ti, une proportion inférieure ou égale à 0,03 % en poids de C, et une proportion inférieure ou égale à 0,03 % en poids de N, le complément étant constitué de Fe et d'autres impuretés inévitables, la fraction de la phase (111) de la fibre γ de l'acier inoxydable ferritique étant supérieure ou égale à 24,0 %, la proportion des grains cristallins d'au moins 55 μm étant inférieure ou égale à 10,0 %, et l'épaisseur étant supérieure ou égale à 1,8 mm. Par conséquent, la valeur d'essai de résilience Charpy à -40 °C est supérieure ou égale à 140 J/cm2 et la DBTT est inférieure ou égale à -45 °C, la ténacité à l'impact à basse température pouvant ainsi être améliorée.
PCT/KR2018/008969 2017-08-25 2018-08-07 Acier inoxydable ferritique ayant une ténacité à l'impact à basse température améliorée et son procédé de production WO2019039774A1 (fr)

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Cited By (1)

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Publication number Priority date Publication date Assignee Title
CN113088654A (zh) * 2021-04-06 2021-07-09 山西太钢不锈钢股份有限公司 一种改善含铌铁素体不锈钢板宏观偏析的生产方法

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JPS63235450A (ja) * 1987-03-24 1988-09-30 Sumitomo Metal Ind Ltd 低温靭性にすぐれたフエライトステンレス鋼
JP2003138348A (ja) * 2001-10-31 2003-05-14 Kawasaki Steel Corp フェライト系ステンレス鋼板およびその製造方法
JP2014177659A (ja) * 2013-03-13 2014-09-25 Nippon Steel & Sumikin Stainless Steel Corp 低温靭性に優れた耐熱フェライト系ステンレス鋼板およびその製造方法
US20170107593A1 (en) * 2014-03-26 2017-04-20 Nippon Steel & Sumikin Stainless Steel Corporation Rolled ferritic stainless steel sheet, method for producing the same, and flange part
JP2017088977A (ja) * 2015-11-13 2017-05-25 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼

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KR101485639B1 (ko) 2012-12-20 2015-01-22 주식회사 포스코 내리징성이 우수한 페라이트계 스테인리스강 및 그 제조 방법

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Publication number Priority date Publication date Assignee Title
JPS63235450A (ja) * 1987-03-24 1988-09-30 Sumitomo Metal Ind Ltd 低温靭性にすぐれたフエライトステンレス鋼
JP2003138348A (ja) * 2001-10-31 2003-05-14 Kawasaki Steel Corp フェライト系ステンレス鋼板およびその製造方法
JP2014177659A (ja) * 2013-03-13 2014-09-25 Nippon Steel & Sumikin Stainless Steel Corp 低温靭性に優れた耐熱フェライト系ステンレス鋼板およびその製造方法
US20170107593A1 (en) * 2014-03-26 2017-04-20 Nippon Steel & Sumikin Stainless Steel Corporation Rolled ferritic stainless steel sheet, method for producing the same, and flange part
JP2017088977A (ja) * 2015-11-13 2017-05-25 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113088654A (zh) * 2021-04-06 2021-07-09 山西太钢不锈钢股份有限公司 一种改善含铌铁素体不锈钢板宏观偏析的生产方法
CN113088654B (zh) * 2021-04-06 2022-09-13 山西太钢不锈钢股份有限公司 一种改善含铌铁素体不锈钢板宏观偏析的生产方法

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