WO2023075282A1 - Acier inoxydable ferritique ayant des propriétés magnétiques améliorées et son procédé de fabrication - Google Patents

Acier inoxydable ferritique ayant des propriétés magnétiques améliorées et son procédé de fabrication Download PDF

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WO2023075282A1
WO2023075282A1 PCT/KR2022/015945 KR2022015945W WO2023075282A1 WO 2023075282 A1 WO2023075282 A1 WO 2023075282A1 KR 2022015945 W KR2022015945 W KR 2022015945W WO 2023075282 A1 WO2023075282 A1 WO 2023075282A1
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less
stainless steel
ferritic stainless
magnetic properties
equation
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PCT/KR2022/015945
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English (en)
Korean (ko)
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김경훈
이문수
김학
박지언
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주식회사 포스코
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Priority to CN202280071684.7A priority Critical patent/CN118176314A/zh
Priority to EP22887478.0A priority patent/EP4394075A1/fr
Publication of WO2023075282A1 publication Critical patent/WO2023075282A1/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
    • 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
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic

Definitions

  • the present invention relates to a ferritic stainless steel having improved magnetic properties by controlling alloy components and a manufacturing process in order to increase responsiveness to an externally applied magnetic field and a manufacturing method thereof.
  • a material having high magnetic permeability has excellent shielding ability, and in particular, a demand for a material exhibiting high magnetic permeability against a low externally applied magnetic field is increasing.
  • An object of the present invention to solve the above problems is to provide a ferritic stainless steel with improved magnetic properties and a method for manufacturing the same, which has increased reactivity to electromagnetic wave shielding by exhibiting a large magnetic permeability to a low externally applied magnetic field. .
  • Ferritic stainless steel with improved magnetic properties according to an embodiment of the present invention, in weight%, C: greater than 0% and 0.02% or less, N: greater than 0% and 0.02% or less, Si: 0.5% or more and 2.0% or less, Mn: 0.1% or more and 0.3% or less, Cr: 16.0% or more and 20.1% or less, Mo: 1.0% or more and 2.0% or less, Ti: 0.1% or more and 0.4% or less, the remainder including Fe (iron) and other unavoidable impurities, including the following The value of Equation (1) may be 130 or less.
  • Equation (1) 30 + 2500 * ([C] + [N]) - 15 * [Si] + 2.5 * [Cr] + 22 * [Mo]
  • [C], [N], [Si], [Cr], and [Mo] mean the content (wt%) of each element.
  • ferritic stainless steel having improved magnetic properties may have a value of 50 or less in Equation (2) below.
  • Equation (2) 18 + 800 * ([C] + [N]) - 6 * [Si] + [Cr] + 6 * [Mo]
  • ferritic stainless steel with improved magnetic properties may further include Nb: more than 0% and less than 0.1% and Sn: more than 0% and less than 0.1%, in weight%.
  • ferritic stainless steel having improved magnetic properties may have a maximum magnetic permeability of 1,000 or more in a 50Hz frequency band.
  • ferritic stainless steel having improved magnetic properties according to an embodiment of the present invention may have an externally applied magnetic field of 130 A/m or less to exhibit maximum magnetic permeability.
  • ferritic stainless steel having improved magnetic properties may have a coercive force of less than 50 A/m under conditions of maximum magnetic permeability in a 50 Hz frequency band.
  • ferritic stainless steel having improved magnetic properties may have a pitting potential value of 300 mV or more.
  • ferritic stainless steel having improved magnetic properties may have a hardness of Hv 140 or more.
  • Equation (1) 30 + 2500 * ([C] + [N]) - 15 * [Si] + 2.5 * [Cr] + 22 * [Mo]
  • [C], [N], [Si], [Cr], and [Mo] mean the content (wt%) of each element.
  • Equation (2) 18 + 800 * ([C] + [N]) - 6 * [Si] + [Cr] + 6 * [Mo]
  • the cold rolling may be performed at a reduction ratio of 70% or more.
  • a ferritic stainless steel with improved magnetic properties which has increased reactivity to electromagnetic wave shielding by deriving a component system exhibiting high permeability and exhibiting a large permeability to a low externally applied magnetic field, and manufacturing thereof method can be provided.
  • Ferritic stainless steel with improved magnetic properties according to an embodiment of the present invention, in weight%, C: greater than 0% and 0.02% or less, N: greater than 0% and 0.02% or less, Si: 0.5% or more and 2.0% or less, Mn: 0.1% or more and 0.3% or less, Cr: 16.0% or more and 20.1% or less, Mo: 1.0% or more and 2.0% or less, Ti: 0.1% or more and 0.4% or less, the remainder including Fe (iron) and other unavoidable impurities, including the following The value of Equation (1) may be 130 or less.
  • Equation (1) 30 + 2500 * ([C] + [N]) - 15 * [Si] + 2.5 * [Cr] + 22 * [Mo]
  • [C], [N], [Si], [Cr], and [Mo] mean the content (wt%) of each element.
  • Ferritic stainless steel with improved magnetic properties according to an embodiment of the present invention, in weight%, C: greater than 0% and 0.02% or less, N: greater than 0% and 0.02% or less, Si: 0.5% or more and 2.0% or less, Mn: 0.1% or more and 0.3% or less, Cr: 16.0% or more and 20.1% or less, Mo: 1.0% or more and 2.0% or less, Ti: 0.1% or more and 0.4% or less, the balance may include Fe (iron) and other unavoidable impurities .
  • the content of C (carbon) may be greater than 0% and 0.02% or less.
  • C is an impurity element inevitably contained in steel, it is desirable to lower its content as much as possible.
  • the content of C is excessive, since magnetic properties deteriorate due to formation of carbides, magnetic permeability may deteriorate.
  • the elongation rate decreases due to the increase in impurities, the strain hardening index n value decreases, and the ductile to brittle transition temperature (DBTT) increases, resulting in a decrease in impact properties.
  • the upper limit of the C content may be limited to 0.02%.
  • the upper limit of the C content may preferably be limited to 0.01% by weight.
  • the content of N may be more than 0% and 0.02% or less.
  • the upper limit of the N content may be limited to 0.02%.
  • the upper limit of the N content may preferably be limited to 0.015% by weight.
  • the content of Si may be 0.5% or more and 2.0% or less.
  • Si is an element effective in realizing an increase in magnetic permeability with respect to a low externally applied magnetic field. Considering this, Si may be added in an amount of 0.5% or more. However, when the content of Si is excessive, the elongation is lowered, the strain hardening index n value is lowered, and the Si-based inclusions are increased, resulting in lower workability. Considering this, the upper limit of the Si content may be limited to 2.0%. Considering workability, the upper limit of the Si content may preferably be limited to 1.0% by weight.
  • the content of Mn (manganese) may be 0.1% or more and 0.3% or less.
  • Mn When the content of Mn is low, fine MnS precipitates are formed to cause crystal grain refinement, thereby weakening the magnetism. Therefore, Mn may be added in an amount of 0.1% or more so that MnS precipitates can be coarsely formed. However, when the Mn content is excessive, magnetic properties may be deteriorated due to an increase in the MnS precipitate fraction. Considering this, the upper limit of the Mn content may be limited to 0.3%.
  • the content of Cr (chromium) may be 16.0% or more and 20.1% or less.
  • Cr is an element that improves corrosion resistance by forming a passivation film in an oxidizing environment. In consideration of this, 16.0% or more of Cr may be added. However, when the Cr content is excessive, it promotes the formation of delta ( ⁇ ) ferrite in the slab, resulting in lower elongation and impact toughness, and lower permeability. Considering this, the upper limit of the Cr content may be limited to 20.1%.
  • the content of Mo (molybdenum) may be greater than 1.0% and less than or equal to 2.0%.
  • Mo is an element effective in increasing the corrosion resistance of stainless steel. In consideration of this, 1.0% or more may be added. However, when the content of Mo is excessive, it is segregated at the grain boundary and plays a role of suppressing grain growth, thereby causing crystal grain refinement, so that magnetism may be inferior. Considering this, the upper limit of the Mo content may be limited to 2.0%.
  • the content of Ti may be 0.1% or more and 0.4% or less.
  • Ti is an effective element for improving strength by causing precipitation. Considering this, Ti may be added in an amount of 0.1% or more. However, when the content of Ti is excessive, the Ti-based precipitate is excessively increased and the crystal grain size does not become sufficiently large, resulting in a decrease in magnetic permeability. Considering this, the upper limit of the Ti content may be limited to 0.4%.
  • the remaining component of the present invention is iron (Fe).
  • Fe iron
  • ferritic stainless steel with improved magnetic properties may further include Nb: more than 0% and less than 0.1% and Sn: more than 0% and less than 0.1%, in weight%.
  • the content of Nb (niobium) may be greater than 0% and less than or equal to 0.1%.
  • Nb is an element that forms a fine precipitated phase like Ti.
  • Ti forms a relatively high-temperature phase
  • fine precipitation can be prevented by heat treatment, but since Nb forms a stable phase at a relatively low temperature, it is re-dissolved during hot rolling and may cause fine precipitation during annealing. Therefore, when the content of Nb is excessive, magnetic deterioration due to fine precipitation may occur, so it is preferable to manage it as an impurity.
  • the upper limit of the Nb content may be limited to 0.1%.
  • the content of Sn (tin) may be greater than 0% and 0.1% or less.
  • Sn like Ti
  • Ti forms a relatively high temperature phase
  • fine precipitation can be prevented by heat treatment, but Sn forms a stable phase at a relatively low temperature, so it is re-dissolved during hot rolling and may cause fine precipitation during annealing. Therefore, when the content of Sn is excessive, magnetic deterioration due to fine precipitation may occur, so it is preferable to manage it as an impurity. Considering this, the upper limit of the Sn content may be limited to 0.1%.
  • Equation (1) below may be 130 or less.
  • Equation (1) 30 + 2500 * ([C] + [N]) - 15 * [Si] + 2.5 * [Cr] + 22 * [Mo]
  • [C], [N], [Si], [Cr], and [Mo] mean the content (wt%) of each element.
  • An object of the present invention is to provide a ferritic stainless steel with improved magnetic properties and a method for manufacturing the same, which has increased reactivity to electromagnetic shielding by exhibiting a large magnetic permeability to a low externally applied magnetic field.
  • the value of Equation (1) exceeds 130, since it shows a large permeability value with respect to a relatively high externally applied magnetic field, the reactivity to electromagnetic wave shielding is poor. Therefore, the value of Equation (1) may be 130 or less.
  • the ferritic stainless steel with improved magnetic properties may have a maximum magnetic permeability of 1,000 or more in a 50Hz frequency band.
  • the externally applied magnetic field for showing the maximum magnetic permeability may be 130 A/m or less.
  • Equation (2) below may be 50 or less.
  • Equation (2) 18 + 800 * ([C] + [N]) - 6 * [Si] + [Cr] + 6 * [Mo]
  • the coercive force refers to the magnitude of an external magnetic field in a reverse direction required to return a magnetized magnetic material to a non-magnetized state.
  • the value of Equation (2) may be 50 or less.
  • the ferritic stainless steel with improved magnetic properties may have a coercive force of less than 50 A / m under the condition of showing the maximum magnetic permeability in the 50 Hz frequency band. .
  • ferritic stainless steel with improved magnetic properties may have a pitting potential value of 300 mV or more by improving corrosion resistance by controlling the alloy composition and manufacturing process.
  • ferritic stainless steel with improved magnetic properties may have a hardness of Hv 140 or more by improving strength by controlling the alloy composition and manufacturing process.
  • Equation (1) 30 + 2500 * ([C] + [N]) - 15 * [Si] + 2.5 * [Cr] + 22 * [Mo]
  • [C], [N], [Si], [Cr], and [Mo] mean the content (wt%) of each element.
  • Equation (2) 18 + 800 * ([C] + [N]) - 6 * [Si] + [Cr] + 6 * [Mo]
  • a series of hot rolling, cold rolling, and final annealing may be performed.
  • the slab may be hot rolled at a reheating temperature of 1050 to 1150 ° C.
  • the reheating temperature of the slab may be 1050 ° C or higher. However, if the reheating temperature is too high, the grain diameter of the slab may be excessively coarsened, resulting in inferior strength. Considering this, the upper limit of the reheating temperature of the slab may be limited to 1150 ° C.
  • the cold rolling may be performed at a reduction ratio of 70% or more. If the reduction ratio is less than 70%, it may be difficult to achieve the desired strength.
  • the cold-rolled material may be final annealed at 1050 to 1150 ° C.
  • the final annealing temperature is low, it takes a long time, and manufacturing cost may increase. Considering this, the final annealing temperature may be 1050 °C or more. However, if the final annealing temperature is high, the microstructure may be excessively coarse, and mechanical properties may be deteriorated. Considering this, the final annealing temperature may be 1150 °C or less.
  • equation (1) The values of equation (1) and equation (2), maximum magnetic permeability, applied magnetic field, coercive force, pit potential and hardness are shown in Table 2 below.
  • the value of equation (1) is 30 + 2500 * ([C] + [N]) - This is the calculated value of 15 * [Si] + 2.5 * [Cr] + 22 * [Mo].
  • [C], [N], [Si], [Cr], [Mo] means the content (wt%) of each element.
  • Equation (2) is a calculated value of 18 + 800 * ([C] + [N]) - 6 * [Si] + [Cr] + 6 * [Mo].
  • the magnetic properties were evaluated by measuring the magnetic field due to the magnetization of the material while gradually increasing the externally applied magnetic field in a 50 Hz frequency band.
  • the maximum magnetic permeability was measured using a non-magnetic magnetic permeability meter having a model name of Ferropro FP-5 by contacting a probe to a cross section of a steel sample having a diameter of 20 mm or more and a thickness of 5 mm or more.
  • the pitting potential represents a value measured by immersing in a NaCl solution and applying a potential to generate pitting potential.
  • the temperature of the NaCl solution was set to 30 °C and the concentration was set to 3.5%.
  • Hardness was measured using a Vickers hardness tester from Zwick Roell.
  • Examples 1 to 7 all satisfied the value of Equation (1) of 130 or less and the value of Equation (2) of 50 or less. Therefore, the maximum magnetic permeability in the 50Hz frequency band was 1,000 or more, the externally applied magnetic field to indicate the maximum permeability was 130 A/m or less, and the coercive force was less than 50 A/m under the conditions of maximum permeability. . That is, it can be seen that Examples 1 to 7 exhibit high magnetic permeability to a low externally applied magnetic field, thereby increasing reactivity to electromagnetic wave shielding and improving magnetic properties. In addition, Examples 1 to 7 had a pitting potential value of 300 mV or more and a hardness of Hv 140 or more. That is, Examples 1 to 7 were excellent in corrosion resistance and strength.
  • Comparative Examples 1 to 5 the value of Formula (1) did not satisfy 130 or less. Accordingly, Comparative Examples 1 to 5 did not satisfy the externally applied magnetic field of 130 A/m or less to indicate the maximum magnetic permeability. In Comparative Examples 1 to 5, the value of Formula (2) did not satisfy 50 or less. Therefore, Comparative Examples 1 to 5 did not satisfy the coercive force of less than 50 A/m. That is, since Comparative Examples 1 to 5 had a relatively high externally applied magnetic field, it could be seen that their reactivity to electromagnetic wave shielding was inferior.
  • Comparative Example 4 Mo component was not added, and the pitting potential value did not satisfy 300 mV or more due to the relatively low level of Cr content. That is, Comparative Example 4 was inferior in corrosion resistance.
  • a ferritic stainless steel with improved magnetic properties which has increased reactivity to electromagnetic wave shielding by deriving a component system exhibiting high permeability and exhibiting a large permeability to a low externally applied magnetic field, and manufacturing thereof As a method can be provided, industrial applicability is recognized.

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Abstract

La présente divulgation concerne de l'acier inoxydable ferritique et un procédé de fabrication dans lequel l'acier inoxydable ferritique a des propriétés magnétiques améliorées en contrôlant les composants d'alliage et un processus de fabrication afin d'augmenter la réactivité à un champ magnétique appliqué de manière externe. L'acier inoxydable ferritique ayant des propriétés magnétiques améliorées selon un mode de réalisation de la présente invention peut comprendre, en % en poids, C : 0 % (exclus) à 0,02 % (inclus), N : 0 % (exclus) à 0,02 % (inclus), Si : 0,5 % à 2,0 % (respectivement inclus), Mn : 0,1 % à 0,3 % (respectivement inclus), Cr : 16,0 % à 20,1 % (respectivement inclus), Mo : 1,0 % (exclus) à 2,0 % (inclus), Ti : 0,1 % à 0,4 % (respectivement inclus), et le reste de fer (Fe) et d'impuretés inévitables.
PCT/KR2022/015945 2021-10-26 2022-10-19 Acier inoxydable ferritique ayant des propriétés magnétiques améliorées et son procédé de fabrication WO2023075282A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
CN202280071684.7A CN118176314A (zh) 2021-10-26 2022-10-19 具有提高的磁性能的铁素体系不锈钢及其制造方法
EP22887478.0A EP4394075A1 (fr) 2021-10-26 2022-10-19 Acier inoxydable ferritique ayant des propriétés magnétiques améliorées et son procédé de fabrication

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KR1020210143705A KR20230059480A (ko) 2021-10-26 2021-10-26 자기적 성질이 향상된 페라이트계 스테인리스강 및 그 제조방법
KR10-2021-0143705 2021-10-26

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09176802A (ja) * 1995-12-27 1997-07-08 Nippon Steel Corp 磁気特性に優れたフェライト系ステンレス鋼板およびその製造方法
KR20060049716A (ko) * 2004-07-01 2006-05-19 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 내식성, 냉간 가공성 및 인성이 우수한 자성을 가지는스텐레스강 선재 또는 강선
CN101492792A (zh) * 2008-01-24 2009-07-29 宝山钢铁股份有限公司 一种用于铁磁性部件的易切削铁素体不锈钢
JP2013185183A (ja) * 2012-03-07 2013-09-19 Nippon Steel & Sumikin Stainless Steel Corp 軟磁性ステンレス鋼細線およびその製造方法
JP2020063472A (ja) * 2018-10-16 2020-04-23 日鉄ステンレス株式会社 磁気特性に優れたフェライト系ステンレス鋼
JP2021161469A (ja) * 2020-03-31 2021-10-11 日鉄ステンレス株式会社 フェライト系ステンレス鋼

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09176802A (ja) * 1995-12-27 1997-07-08 Nippon Steel Corp 磁気特性に優れたフェライト系ステンレス鋼板およびその製造方法
KR20060049716A (ko) * 2004-07-01 2006-05-19 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 내식성, 냉간 가공성 및 인성이 우수한 자성을 가지는스텐레스강 선재 또는 강선
CN101492792A (zh) * 2008-01-24 2009-07-29 宝山钢铁股份有限公司 一种用于铁磁性部件的易切削铁素体不锈钢
JP2013185183A (ja) * 2012-03-07 2013-09-19 Nippon Steel & Sumikin Stainless Steel Corp 軟磁性ステンレス鋼細線およびその製造方法
JP2020063472A (ja) * 2018-10-16 2020-04-23 日鉄ステンレス株式会社 磁気特性に優れたフェライト系ステンレス鋼
JP2021161469A (ja) * 2020-03-31 2021-10-11 日鉄ステンレス株式会社 フェライト系ステンレス鋼

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