EP3705595A1 - Acier inoxydable austénitique non magnétique ayant une résistance et une conductivité de surface améliorées - Google Patents

Acier inoxydable austénitique non magnétique ayant une résistance et une conductivité de surface améliorées Download PDF

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EP3705595A1
EP3705595A1 EP18890862.8A EP18890862A EP3705595A1 EP 3705595 A1 EP3705595 A1 EP 3705595A1 EP 18890862 A EP18890862 A EP 18890862A EP 3705595 A1 EP3705595 A1 EP 3705595A1
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Prior art keywords
stainless steel
austenitic stainless
content
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present disclosure
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EP18890862.8A
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German (de)
English (en)
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EP3705595A4 (fr
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Jong-Hee Kim
Kwang Min Kim
Bo-Sung Seo
Hak Kim
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Posco Holdings Inc
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Posco Co Ltd
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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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/34—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
    • C21D2211/001—Austenite
    • 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 disclosure relates to a non-magnetic austenitic stainless steel, and more particularly, to a non-magnetic austenitic stainless steel with improved strength and surface conductivity applicable to environments requiring strength and surface conductivity along with non-magnetic properties.
  • materials for electronic parts require austenitic stainless steel having excellent surface conductivity in addition to high strength and non-magnetic characteristics or high strength and non-magnetic characteristics.
  • a material for electronic parts contains a large amount of expensive Ni, which has a problem of increasing the raw material cost.
  • Austenitic stainless steel represented by STS304
  • STS304 has good corrosion resistance, and exhibits a non-magnetic austenite structure in annealing heat treatment, and is used as a non-magnetic steel in various devices.
  • working is performed depending on the application, and when deep drawing and press working are applied to STS304 steel, due to the phase transformation to strain induced martensite structure, it is difficult to maintain non-magnetic properties, and there is a problem that delayed cracks occur.
  • the embodiments of the present disclosure solve the above problems and provide non-magnetic austenitic stainless steel with improved strength and surface conductivity by controlling the content element without adding Ni to suppress strain induced martensite, and controlling ⁇ -ferrite content during solidification.
  • an austenitic stainless steel includes, in percent (%) by weight of the entire composition, C: 0.07 to 0.2%, N: 0.15 to 0.4%, Si: 0.8 to 2%, Mn: 16 to 22%, S: 0.01% or less (excluding 0), Cr: 12.5 to 20%, Cu: 1 to 3%, the remainder of iron (Fe) and other inevitable impurities, and satisfies the following equation (1).
  • Ni, Cr, Mn, Si, C, N are % by weight of each element.
  • the yield strength represented by the following equation (2) may be 450 MPa or more.
  • yield strength MPa 185 + 1977 C + 605 N + 3.65 Cu ⁇ 3.63 Mn C, N, Cu, Mn are % by weight of each element.
  • the ferrite content measured after 70% cold working may be less than 0.1%.
  • the permeability may be 1.005 or less even at 70% cold working
  • the stacking fault energy (SFE) represented by the following equation (3) may be 41 mJ/m 2 or more.
  • SFE mJ / m 2 25.7 + 1.59 Ni + Cu ⁇ 0.85 Cr + 0.001 Cr 2 + 38.2 N 0.5 ⁇ 2.8 Si ⁇ 1.34 Mn + 0.06 Mn 2 Ni, Cu, Cr, N, Si, Mn are % by weight of each element.
  • the cold rolled material hardness (Hv) value may be 215 or more.
  • the Cu + Mn content in the region within 2nm of the passivation film may be 0.2% or more.
  • the surface resistance may be less than 10m ⁇ cm 2 .
  • non-magnetic austenitic stainless steel with improved strength and surface conductivity can be used in various applications for non-magnetic components used in various devices.
  • an additional process of heat-treating the material for a long time in order to remove magnetism by ⁇ -ferrite is unnecessary, and thus it is possible to provide a non-magnetic austenitic stainless steel with a simple manufacturing process.
  • a non-magnetic austenitic stainless steel with improved strength and surface conductivity includes, in percent (%) by weight of the entire composition, C: 0.07 to 0.2%, N: 0.15 to 0.4%, Si: 0.8 to 2%, Mn: 16 to 22%, S: 0.01 % or less (excluding 0), Cr: 12.5 to 20%, Cu: 1 to 3%, the remainder of iron (Fe) and other inevitable impurities, and satisfies the following equation (1).
  • Ni, Cr, Mn, Si, C, N are % by weight of each element.
  • part when a part "includes” or “comprises” an element, unless there is a particular description contrary thereto, the part may further include other elements, not excluding the other elements.
  • non-magnetic austenitic stainless steel which can secure non-magnetic properties even if it is manufactured in a normal process without requiring an additional process for decomposing ⁇ -ferrite by controlling the content of ⁇ -ferrite present in the microstructure of the steel and has improved strength and surface conductivity compared to commonly used STS304 stainless steel.
  • the present disclosure provides austenitic stainless steel that exhibits excellent non-magnetic properties only by controlling the alloying element, without the addition of expensive Ni, even without an additional heat treatment process.
  • An austenitic stainless steel includes, in percent (%) by weight of the entire composition, C: 0.07 to 0.2%, N: 0.15 to 0.4%, Si: 0.8 to 2%, Mn: 16 to 22%, S: 0.01% or less (excluding 0), Cr: 12.5 to 20%, Cu: 1 to 3%, the remainder of iron (Fe) and other inevitable impurities, and satisfies the following equation (1).
  • the content of C is 0.07 to 0.2%.
  • Carbon (C) is a strong austenite phase stabilizing element, and it is desirable to add 0.07% or more to increase the material strength by solid solution strengthening.
  • a carbide-forming element such as Cr effective for corrosion resistance to lower the Cr content around the grain boundaries to lower the corrosion resistance, and the upper limit can be limited to 0.2%.
  • the content of N is 0.15 to 0.4%.
  • Nitrogen (N) is a strong austenite phase stabilizing element and is an essential element in steels that do not contain Ni. It is desirable to add 0.15% or more in the present disclosure. However, if the content is excessive, surface defects due to nitride precipitation and nitrogen pores may be generated, and the upper limit may be limited to 0.4%.
  • the content of Si is 0.8 to 2%.
  • Silicon (Si) is an element useful for deoxidation, and when Ni is not added, it has an effect of improving corrosion resistance, so it is preferable to add 0.8% or more. However, if the content is excessive, the mechanical properties related to impact toughness are reduced, and the upper limit can be limited to 2%.
  • the content of Mn is 16 to 22%.
  • Manganese (Mn) is a core element that is essential for stabilization of the austenite phase when Ni is not added, and it is preferable to add 16% or more. However, if the content is excessive, surface defects may occur, and the upper limit may be limited to 22%.
  • the content of S is 0.01% or less.
  • S Sulfur
  • MnS becomes a starting point of corrosion and reduces corrosion resistance, so it is preferable to limit it to 0.01% or less.
  • the content of Cr is 12.5 to 20%.
  • Chromium (Cr) is the most contained element of the corrosion resistance improving element of stainless steel, and it is preferable to add 12.5% or more to express corrosion resistance.
  • Cr is a ferrite stabilizing element. As the Cr content increases, the ferrite fraction increases to inhibit austenite stabilization.
  • the upper limit can be limited to 20%.
  • the content of Cu is 1 to 3%.
  • Copper (Cu) is an essential element in the present disclosure, such as Mn, which increases the austenite phase stability and improves corrosion resistance.
  • copper (Cu) is added together with Mn to be dissolved in the passivation film to increase the surface conductivity, so it is preferable to add 1% or more.
  • the content is excessive, the moldability is rather deteriorated, and the upper limit can be limited to 3%.
  • Nickel (Ni) is treated as an impurity in the present disclosure because its elution and formability are deteriorated when added in small amounts.
  • the remaining component of the present disclosure is iron (Fe).
  • Fe iron
  • impurities that are not intended from the raw material or the surrounding environment can be inevitably mixed, and therefore cannot be excluded. Since these impurities are known to anyone skilled in the ordinary manufacturing process, they are not specifically mentioned in this specification.
  • austenitic stainless steel which is used for electronic parts, requires processes such as plate forming and deep drawing.
  • a deformed structure having a deformation amount of about 50% or more is formed, and non-magnetic properties must be maintained even in these deformed portions.
  • the permeability ⁇ of the steel applied to the parts should be 1.005 or less for normal operation. To satisfy this, it is necessary to control the content of ⁇ -ferrite formed during solidification of the steel.
  • ⁇ -ferrite present in the microstructure of austenitic stainless steel becomes magnetic due to the characteristics of the structure having a body-centered cubic structure, and austenite does not become magnetic due to the face-centered cubic structure. Therefore, it is possible to obtain a magnetic property of a desired size by controlling the fraction of ⁇ -ferrite, and in the case of non-magnetic steel, it is necessary to make the fraction of ⁇ -ferrite as low as possible or eliminate the fraction of ⁇ -ferrite.
  • the fraction of ⁇ -ferrite can be reduced by adding an austenite stabilizing element.
  • formation of ⁇ -ferrite can be suppressed by controlling Ni content useful for stabilizing austenite without deteriorating other physical properties.
  • Ni is a very expensive element, its range of use may be limited. Therefore, present disclosure attempted to secure the non-magnetic properties of austenitic stainless steel by controlling the content of Mn, Si, C, N without adding Ni.
  • the non-magnetic property can be expressed as a Ni equivalent (Nieq) value indicating austenite stability.
  • Ni equivalent refers to the minimum Ni content that does not form ⁇ -ferrite in a given compositional component, and can be expressed as follows.
  • Nieq Ni + 0.65 Cr + 1.05 Mn + 0.35 Si + 12.6 C + 33.6 N
  • Ni, Cr, Mn, Si, C, and N are weight% of each element.
  • the inventors of the present disclosure discovered that when the Ni equivalent value is 40 or more, the ferrite content measured after 70% cold working by simulating the actual severe molding part should satisfy 0.1% or less, so that the permeability is 1.005 or less, so that non-magnetic properties can be satisfied..
  • FIG.1 is a graph showing the correlation of permeability according to Nieq. Referring to FIG. 1 , it can be seen that permeability satisfies 1.005 or less after 70% cold deformation of austenite stainless steel when the Ni equivalent is 40 or more.
  • the cold-rolled annealing plate of austenitic stainless steel may satisfy a yield strength of 450 Mpa or more and a hardness (Hv) value of 215 or more, expressed by the following equation (2).
  • yield strength MPa prediction equation 185 + 1977 C + 605 N + 3.65 Cu ⁇ 3.63 Mn
  • C, N, Cu, Mn are weight% of each element.
  • the yield strength prediction equation including C, N and Cu content represented by equation (2), reflects the strength of the steel well, and have found that when the range of equation (2) is 450 or more, the desired strength can be secured.
  • FIG. 2 is a graph showing the correlation of yield strength (MPa) according to Nieq.
  • the yield strength of the cold rolled annealing plate of austenite stainless steel satisfies 450 Mpa or more.
  • austenitic stainless steel may satisfy a stacking fault energy represented by the following equation (3) of 41 mJ/m 2 or more.
  • SFE mJ / m 2 25.7 + 1.59 Ni + Cu ⁇ 0.85 Cr + 0.001 Cr 2 + 38.2 N 0.5 ⁇ 2.8 Si ⁇ 1.34 Mn + 0.06 Mn 2
  • Stacking fault energy (SFE, mJ / m 2 ) of the austenite phase is known to control the deformation mechanism of the austenite phase.
  • the stacking fault energy of the austenite phase indicates the degree to which the plastic deformation energy added from the outside contributes to the deformation of the austenite phase in the case of austenitic stainless steel in a single phase.
  • the lower the stacking fault energy the more the strain induced martensite phase that contributes to the work hardening of the steel increases after the formation of the epsilon martensite phase in the austenite phase.
  • a strain induced martensite phase is formed after the epsilon martensite phase is formed in the austenite phase, or a strain induced martensite phase is formed after mechanical twinning is formed in the austenite phase.
  • austenitic stainless steel may have a Cu + Mn content of 0.2% or more in a region within 2 nm from the surface layer.
  • stainless steel was produced through 50 kg ingot casting while changing the content of each component of the steel. After heating the ingot at 1250°C for 3 hours, hot rolling was performed to produce a 4 mm thick hot rolled material. The hot rolled material was cold rolled, processed to a final thickness of 2.5 mm, annealed at 1100°C for 30 seconds in the air, and pickled.
  • the 2.5 mm cold rolled specimen was cold rolled at a cold reduction ratio of 70% to simulate the non-magnetic and surface resistance properties of a molded article made of an actual electronic parts material, thereby producing a cold rolled sheet having a thickness of 0.75 mm.
  • the ferrite content (%) of the manufactured cold rolled sheet was measured using a ferrite scope device, and permeability was measured using a permeability measurement device (FERROMASTER).
  • Mn + Cu (% by weight) in the passivation film at 2 nm from the surface layer of the cold rolled sheet was analyzed by using a Glow Discharge Spectrometer (GDS) analysis equipment.
  • GDS Glow Discharge Spectrometer
  • the surface resistance was expressed as a surface resistance value by measuring the resistance with a DC 4 terminal method by placing a gold-plated Cu-plate (area 2cm 2 ) on the top / bottom of a cold rolled plate and applying a pressure of 10 N/cm 2 .
  • the surface resistance measurement criterion was evaluated as being good if the surface resistance was less than 10 m ⁇ cm 2 , and insufficient if it was 10m ⁇ cm 2 or more.
  • SFE stacking fault energy
  • FIG. 1 is a graph showing the correlation of permeability according to Nieq.
  • the Nieq value represented by equation (1) is greater than or equal to 40 and the permeability is 1.005 or less compared to comparative examples, and thus it can be confirmed that the non-magnetic property is satisfied.
  • FIG. 2 is a graph showing the correlation of yield strength (MPa) according to Nieq.
  • the Nieq value represented by equation (1) is 40 or more, and the yield strength is 450 MPa or more and the hardness is 215 Hv or more, as compared with comparative examples.
  • the difference between the prediction equation of yield strength and the measured value of yield strength is minimal, so that equation (2) reflects the strength of austenitic stainless steel well.
  • the stacking fault energy (SFE) value was 41 mJ/m 2 or more as compared with Comparative Examples, and it was possible to suppress the formation of the martensite phase after plastic deformation, thereby ensuring ductility, and in the region within 2 nm from the surface layer, the Cu + Mn content is 0.2% or more and concentration of Cu and Mn occurs, so that the surface resistance is measured to be 10m ⁇ cm 2 or less. That is, it can be confirmed that the surface conductivity is improved.
  • Comparative Example 1 Ni is contained 8.1%, but the Mn content was excessively low at 1.5%, and the Nieq value was less than 40.
  • the Nieq value was 23.745, which was outside the present disclosure range, and the permeability is 5.2, it shows magnetism, so that high strength of 450 MPa or more and desired surface conductivity could not be secured.
  • the Nieq value was 30.38, which is less than 40, and the permeability was 2.5, so that the desired non-magnetic property could not be secured, and high-strength properties of 450 MPa or more could not be secured.
  • the austenitic stainless steel according to an embodiment of the present disclosure controls the content element without adding Ni to suppress strain induced martensite, and controls the ⁇ -ferrite content during solidification, thereby increasing strength and surface conductivity, while ensuring non-magnetic properties.
  • the non-magnetic austenitic stainless steel with improved surface conductivity according to embodiments of the present disclosure is applicable to materials for electronic parts.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP18890862.8A 2017-12-20 2018-10-05 Acier inoxydable austénitique non magnétique ayant une résistance et une conductivité de surface améliorées Pending EP3705595A1 (fr)

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KR1020170176559A KR102020507B1 (ko) 2017-12-20 2017-12-20 강도, 표면전도성이 향상된 비자성 오스테나이트계 스테인리스강
PCT/KR2018/011762 WO2019124689A1 (fr) 2017-12-20 2018-10-05 Acier inoxydable austénitique non magnétique ayant une résistance et une conductivité de surface améliorées

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EP3705595A4 EP3705595A4 (fr) 2020-09-09
EP3705595A1 true EP3705595A1 (fr) 2020-09-09

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US (1) US20200370154A1 (fr)
EP (1) EP3705595A1 (fr)
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KR (1) KR102020507B1 (fr)
CN (1) CN111492081B (fr)
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JP6983321B2 (ja) 2021-12-17
CN111492081B (zh) 2021-11-19
JP2021507103A (ja) 2021-02-22
WO2019124689A1 (fr) 2019-06-27
US20200370154A1 (en) 2020-11-26
KR20190074873A (ko) 2019-06-28
CN111492081A (zh) 2020-08-04

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