WO2020004710A1 - Acier inoxydable ferritique à faible teneur en cr présentant une excellente capacité d'amortissement et son procédé de fabrication - Google Patents

Acier inoxydable ferritique à faible teneur en cr présentant une excellente capacité d'amortissement et son procédé de fabrication Download PDF

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WO2020004710A1
WO2020004710A1 PCT/KR2018/010699 KR2018010699W WO2020004710A1 WO 2020004710 A1 WO2020004710 A1 WO 2020004710A1 KR 2018010699 W KR2018010699 W KR 2018010699W WO 2020004710 A1 WO2020004710 A1 WO 2020004710A1
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stainless steel
vibration damping
ferritic stainless
low
precipitates
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PCT/KR2018/010699
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English (en)
Korean (ko)
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정일찬
류승희
이계만
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주식회사 포스코
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Priority to ES18924969T priority Critical patent/ES2978502T3/es
Priority to EP18924969.1A priority patent/EP3795711B1/fr
Publication of WO2020004710A1 publication Critical patent/WO2020004710A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C22C38/02—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
    • C22C38/48—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

Definitions

  • the present invention relates to a low Cr ferritic stainless steel having excellent vibration damping ability to absorb external vibration energy and a method of manufacturing the same.
  • Ferritic stainless steels are excellent in corrosion resistance even though less expensive alloying elements are added, and have a higher price competitiveness than austenitic stainless steels.
  • the low Cr ferritic stainless steel of 9-14% is more cost-competitive, and is used in exhaust system parts (Muffler, Ex-manifold, Collector cone, etc.) corresponding to the exhaust gas temperature range from room temperature to 800 ° C.
  • Steel sheets for automobile exhaust systems must be able to absorb the noises and vibrations generated during engine or other driving, and to withstand external environmental factors such as exhaust gases, rain or fog generated inside the vehicle. It must be secured.
  • Embodiments of the present invention are to provide a low Cr ferritic stainless steel and a method of manufacturing the same by maximizing the vibration damping ability by using Nb, Cu fine precipitated phase.
  • Low Cr ferritic stainless steel having excellent vibration damping ability according to an embodiment of the present invention, in weight%, C: 0.005 to 0.01%, N: 0.005 to 0.01%, Si: 0.1 to 0.9%, Mn: 0.1 to 0.9 %, Cr: 9-14%, Ni: 0.3% or less, P: 0.04% or less, S: 0.002% or less, Ti: 0.15 to 0.3%, Nb: 0.15 to 0.3%, Cu: 0.15 to 0.3%, Al: 0.01 to 0.05%, remaining Fe and unavoidable impurities, and containing at least 5 ⁇ 10 2 / mm 2 of Nb laves phase precipitates and Cu precipitates.
  • the stainless steel may satisfy the following formula (1).
  • Nb, Cu, Ti means content (wt%) of each element.
  • the stainless steel may satisfy the following formula (2).
  • Nb and Cu mean content (weight%) of each element.
  • the Nb Laves phase precipitate is Fe 2 Nb
  • the size of the Nb Laves phase precipitate and Cu precipitates may be 1 to 200nm.
  • the vibration damping index (Q-1) of the stainless steel may be 2.0 ⁇ 10 -4 or more at 25 ° C, 2.5 ⁇ 10 -4 or more at 300 ° C.
  • Low Cr ferritic stainless steel manufacturing method excellent in vibration damping ability in weight%, C: 0.005 to 0.01%, N: 0.005 to 0.01%, Si: 0.1 to 0.9%, Mn: 0.1 To 0.9%, Cr: 9 to 14%, Ni: 0.3% or less, P: 0.04% or less, S: 0.002% or less, Ti: 0.15 to 0.3%, Nb: 0.15 to 0.3%, Cu: 0.15 to 0.3%, Al: cold rolling annealing the ferritic stainless steel cold rolled steel sheet containing 0.01 to 0.05%, the remaining Fe and unavoidable impurities at a temperature of (Ac 1-10) °C or less; And quenching at 400 to 600 ° C. for 5 minutes or more.
  • the cold rolled steel sheet may satisfy the following formula (1).
  • Nb, Cu, Ti means content (wt%) of each element.
  • the cold rolled steel sheet may satisfy the following formula (2).
  • Nb and Cu mean content (weight%) of each element.
  • Low Cr ferritic stainless steel according to an embodiment of the present invention can increase the vibration damping ability by more than 100% through the sound absorption mechanism by the movement of the solid solution C, N and the vibration damping mechanism through the suppression of precipitation of carbonitride.
  • low-Cr ferritic stainless steel according to an embodiment of the present invention is excellent in corrosion resistance to ensure quietness and durability when used in automobile exhaust system parts and the like.
  • 1 is a graph showing the correlation between the vibration damping index according to the number of Nb Laves phase precipitate and Cu precipitates.
  • Fig. 2 is a photograph showing distribution of Nb Laves phase precipitates and Cu precipitates at a known interface.
  • Low Cr ferritic stainless steel having excellent vibration damping ability according to an embodiment of the present invention, in weight%, C: 0.005 to 0.01%, N: 0.005 to 0.01%, Si: 0.1 to 0.9%, Mn: 0.1 to 0.9 %, Cr: 9-14%, Ni: 0.3% or less, P: 0.04% or less, S: 0.002% or less, Ti: 0.15 to 0.3%, Nb: 0.15 to 0.3%, Cu: 0.15 to 0.3%, Al: 0.01 to 0.05%, remaining Fe and unavoidable impurities, and containing at least 5 ⁇ 10 2 / mm 2 of Nb laves phase precipitates and Cu precipitates.
  • the stainless steel may satisfy the following formula (1).
  • the sound absorbing mechanism causes energy loss as C and N, which are employed during vibration, change position in the lattice, resulting in sound absorption.
  • the sound absorbing effect by solid solution C and N has a characteristic proportional to the amount of solid solution C and N, and the vibration damping effect by magnetic domain wall hinders the movement of magnetic domain walls such as precipitates, dislocations and internal stresses. The more elements there are, the better.
  • Nb is added to the ferritic stainless steel applied at a high temperature of exhaust gas of 400 ° C. or higher, and Cu is further added as a solid solution strengthening element.
  • Nb Laves phases (Fe 2 Nb) and Cu precipitated phases having a fine size of 1 to 200 nm may be generated under specific heat treatment conditions.
  • the vibration will vibrate together, by absorbing the external vibration energy can increase the vibration damping ability.
  • the effect is further increased when precipitated in complex than when precipitated in Nb Laves phase or Cu alone.
  • the vibration damping ability can be maximized by depositing fine Nb Laves phase precipitates and Cu precipitates at known interfaces.
  • Low Cr ferritic stainless steel having excellent vibration damping ability according to an embodiment of the present invention, in weight%, C: 0.005 to 0.01%, N: 0.005 to 0.01%, Si: 0.1 to 0.9%, Mn: 0.1 to 0.9 %, Cr: 9-14%, Ni: 0.3% or less, P: 0.04% or less, S: 0.002% or less, Ti: 0.15 to 0.3%, Nb: 0.15 to 0.3%, Cu: 0.15 to 0.3%, Al: 0.01 to 0.05%, remaining Fe and unavoidable impurities, and containing at least 5 ⁇ 10 2 / mm 2 of Nb laves phase precipitates and Cu precipitates.
  • the content of C is 0.005 to 0.01%.
  • the content of N is 0.005 to 0.01%.
  • N in steel is a key element that causes sound absorption and vibration attenuation through the same mechanism as C.
  • the vibration damping ability increases.
  • the concentration of solid solution N reaches its limit, and it binds with Cr and forms Cr 2 N precipitates, which hinders the movement of the magnetic domain walls, and due to local Cr depletion in the base, Golden dust Occurs and corrosion resistance falls.
  • the solid solution C and N in the matrix may be increased to suppress the precipitation of carbonitride and to improve the vibration damping ability due to the smooth movement of the magnetic domain walls.
  • the content of Si is 0.1 to 0.9%.
  • Si is an element that acts as a deoxidizer during steelmaking and contains 0.1% or more.
  • the inclusions are generated due to the Si oxide, and the inclusions interfere with the movement of the magnetic domain walls, thereby inhibiting the vibration damping ability, thereby limiting the content to 0.9% or less.
  • the content of Mn is 0.1 to 0.9%.
  • Mn plays a role in stabilizing austenite.
  • the austenite-ferrite transformation point (Ac1) is lowered, and since the high temperature annealing which can solidify C and N after cold rolling becomes impossible, the content is limited to 0.9% or less.
  • the content of Cr is 9-14%.
  • Cr increases the magnetostriction constant of the steel to further promote the movement of the magnetic domain walls compared to the carbon steel when vibration occurs, and increases the vibration damping ability by the magnetic domain walls. In addition, it plays a positive role in the vibration damping effect by C, N. However, if the content of Cr exceeds 14%, it easily bonds with C and N, making it easier to produce carbonitrides, thereby lowering the amount of solid solution C and N, and because the precipitate interferes with the movement of the magnetic domain walls, the content falls within the above range. Restrict.
  • the content of Ni is 0.3% or less.
  • Ni may be contained in an amount of about 0.1%, which is inevitably included in steel by melting the scrap, and the upper limit thereof is limited to 0.3%.
  • the content of P is 0.04% or less.
  • P is an unavoidable impurity contained in steel, and is limited to 0.04% or less because it causes grain boundary corrosion during pickling or inhibits hot workability. Preferable content of P is 0.01 to 0.04%.
  • the content of S is 0.002% or less.
  • S is an unavoidable impurity contained in steel, and segregates at grain boundaries and inhibits hot workability, so the content is limited to 20 ppm or less.
  • the content of Ti is 0.15 to 0.3%.
  • Ti must be added in order to increase the corrosion resistance of the weld is added 0.15% or more. However, Ti combines with C and N to form Ti (C, N) precipitates, lowering the amount of solid solution C and N, and inferior to the vibration damping ability because Ti (C, N) precipitates interfere with the movement of the magnetic domain walls. Make it. Therefore, the content is limited to 0.3% or less.
  • the content of Nb is 0.15 to 0.3%.
  • Nb is also an essential element to increase the corrosion resistance of welded parts, and if it satisfies the proper composition conditions and heat treatment conditions, fine Laves phase precipitates are formed, which helps to improve vibration damping ability. .
  • Nb combines with C and N to form Nb (C, N) precipitates, thereby lowering the amount of solid solution C and N. Since Nb (C, N) precipitates interfere with the movement of the magnetic domain walls, Nb is inferior to vibration damping ability. Therefore, the content is limited to 0.3% or less.
  • the content of Cu is 0.15 to 0.3%.
  • Cu generates fine precipitates by appropriate heat treatment and is added in an amount of 0.15% or more to help improve vibration damping ability.
  • the hot hot workability may be inhibited, so the content is limited to 0.3% or less.
  • the content of Al is 0.01 to 0.05%.
  • Al combines with N to form AlN precipitates, lowering the amount of solid solution N, and inferior to the vibration damping ability because AlN precipitates interfere with the movement of the magnetic domain walls.
  • Al is an alloy component added as a deoxidizer during steelmaking, but the content is limited to 0.01 to 0.05% because it exists as a non-metallic inclusion when a large amount is added, causing a sleeve defect of the cold rolled strip.
  • the remainder of the ferritic stainless steel except for the alloying elements described above is composed of Fe and other unavoidable impurities.
  • Low Cr ferritic stainless steel according to an embodiment of the present invention may satisfy the following formula (1).
  • the vibration damping effect by the fine Nb Laves phase precipitate and Cu precipitate should be increased by increasing the Nb + Cu content.
  • the low Cr ferritic stainless steel according to an embodiment of the present invention may satisfy the following formula (2).
  • the Nb + Cu content becomes higher than necessary, coarsening of precipitates easily occurs. In this case, the interface coherence between the precipitate and the matrix is reduced, and the number and total interface area of the precipitate are reduced, so that vibration damping effects due to Nb Laves phase precipitate and Cu precipitate are hardly expressed. Therefore, the Nb + Cu content is limited to 0.5% or less.
  • Nb Laves phase precipitate is Fe 2 Nb
  • the size of the Nb Laves phase precipitate and Cu precipitates may be 1 to 200nm.
  • the size of the precipitate is preferably controlled to 200 nm or less.
  • the Nb Laves phase precipitate, and the precipitate of Cu 200nm than 5 ⁇ 10 2 pieces / low-Cr ferritic stainless steel according to the present invention comprises at least mm2 is, the vibration attenuation factor (Q-1) is 2.0 ⁇ 10 eseo 25 °C - 4 or more, it is possible to exhibit excellent vibration damping capacity of 2.5 ⁇ 10 ⁇ 4 or more at 300 ° C.
  • the method for producing a low Cr ferritic stainless steel having excellent vibration damping ability of the present invention can be made of a cold rolled steel sheet through a conventional manufacturing process, and the ferritic stainless steel cold rolled steel sheet containing the alloying composition described above (Ac1-10) ° C. Cold rolling annealing at the following temperature; And quenching at 400 to 600 ° C. for 5 minutes or more.
  • the slab including the alloy component composition described above may be hot rolled, the hot rolled hot rolled steel sheet is annealed and heat-treated, and cold rolled to produce a cold rolled steel sheet.
  • Cold-rolled steel sheet is cold-rolled and annealed in the temperature range below 10 degreeC lower than austenite-ferrite transformation temperature (Ac1).
  • austenite phase is partially present, so that the annealing temperature is limited to (Ac 1-10) ° C. or less to prevent reverse transformation.
  • Annealing is carried out so that C and N can be sufficiently dissolved in the matrix within the above temperature range.
  • quenching is required in the temperature range of 400 to 600 °C after cold rolling annealing in order to suppress the production of Cr carbonitride, and the number of fine Nb Laves phase precipitate and Cu precipitates by heat treatment maintained for 5 minutes or more in the temperature range By increasing the vibration damping capacity can be maximized.
  • the Nb + Cu content according to Equation (2) exceeds 0.5%, the precipitated precipitates are coarsened compared to the Nb Laves phase precipitates and Cu precipitates additionally generated by the heat treatment, thereby reducing the total number of precipitates. Can be. Therefore, when the Nb + Cu content is more than 0.5%, it is preferable not to perform additional heat treatment after cold rolling annealing.
  • Vibration damping was measured using IMCE's "RFDA LTVP800" instrument.
  • the above instrument generates a vibration damping index (Q-1) by measuring the attenuation of sound after generating a vibration of natural frequency by giving a shock of a constant force to a sample of 80mm (length) * 20mm (width).
  • the higher the vibration attenuation index the faster the damping of the vibration. That is, the vibration damping ability is excellent.
  • vibration damping index can be obtained for the temperature range of 25 ⁇ 800 °C.
  • vibration damping indices of room temperature (25 °C) and 300 °C were obtained.
  • the natural frequency was 1 kHz.
  • the number of Nb Laves phase precipitates and Cu precipitates was measured only for precipitates having a size of 200 nm or less.
  • the total amount of Nb Laves phase precipitates and Cu precipitates is not required even after heat treatment at 500 ° C. for at least 5 minutes.
  • the vibration damping index (Q-1) was measured to be 2.3 ⁇ 10 ⁇ 4 or more at room temperature of 500 or more. Particularly, when the heat treatment was performed, the total amount of precipitates increased by 100 to 150 and increased by 15 to 30%.
  • the vibration attenuation index (Q-1) also increased by 20 to 35% and increased by 3.1 ⁇ 10 ⁇ 4 or more. Was measured.
  • Comparative Example 1 satisfies Equations (1) and (2), but the content of Ti, Nb, and Cu was less than 0.15%, and the total amount of precipitates was less than 360 pieces / mm 2 even after annealing at 500 ° C. for further heat treatment. This was found to be due to the lack of Nb and Cu content to form Nb Laves phase precipitate and Cu precipitates.
  • Comparative Example 3 satisfies all the component ranges of the present invention including Ti, Nb, and Cu, but the content of Ti is higher than that of Nb + Cu, and thus dissatisfied with Equation (1), whereby a large amount of Ti (C, N) carbonitride Precipitated.
  • 2 is a photograph showing distribution of Nb Laves phase precipitates and Cu precipitates at a known interface of Comparative Example 3.
  • FIG. It can be seen that the Ti content is high due to the high Ti content.
  • the TiN precipitate not only lowers the solid solution C and N, but also the precipitate itself interferes with the movement of the magnetic domain walls, and the vibration damping index is also 1.7 ⁇ 10 ⁇ 4 or less after further heat treatment. Was measured.
  • Comparative Example 4 satisfies the component range and formula (1) of the present invention including Ti, Nb, and Cu, but has a high Nb + Cu content, which dissatisfies formula (2).
  • the content of Nb + Cu was 0.55%, so that the Nb Laves phase precipitate and the Cu precipitate were coarsened.
  • the total amount of precipitates having a size of 200 nm or less was rather reduced, and it was confirmed that this was due to coarsening of precipitates.
  • the vibration damping index after the additional heat treatment of Comparative Example 4 was the lowest despite satisfying the component range of the present invention.
  • Ferritic stainless steel according to the present invention can ensure the quietness and durability of automobile exhaust system components by maximizing vibration damping ability by utilizing Nb, Cu fine precipitated phase.

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Abstract

L'invention concerne un acier inoxydable ferritique à faible teneur en Cr présentant une excellente capacité d'amortissement, pour absorber l'énergie de vibration externe par une régulation des précipités et son procédé de fabrication. Un acier inoxydable ferritique à faible teneur en Cr présentant une excellente capacité d'amortissement selon un mode de réalisation de la présente invention comprend, en pourcentage en poids : C : 0,005 à 0,01 % ; N : 0,005 à 0,01 % ; Si : 0,1 à 0,9 % ; Mn : 0,1 à 0,9 % ; Cr : 9 à 14 % ; Ni : 0,3 % au maximum ; P : 0,04 % au maximum ; S : 0,002 % au maximum ; Ti : 0,15 à 0,3 % ; Nb : 0,15 à 0,3 % ; Cu : 0,15 à 0,3 % ; Al : 0,01 à 0,05 % ; et le reste étant constitué de Fe et d'impuretés inévitables, l'acier inoxydable ferritique à faible teneur en Cr présentant une excellente capacité d'amortissement comprenant 5×102/㎟ ou plus de précipités de phase de Nb-Laves et de précipités de Cu.
PCT/KR2018/010699 2018-06-26 2018-09-12 Acier inoxydable ferritique à faible teneur en cr présentant une excellente capacité d'amortissement et son procédé de fabrication WO2020004710A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
ES18924969T ES2978502T3 (es) 2018-06-26 2018-09-12 Acero inoxidable ferrítico de bajo contenido en Cr con excelente capacidad de amortiguación y método de fabricación del mismo
EP18924969.1A EP3795711B1 (fr) 2018-06-26 2018-09-12 Acier inoxydable ferritique à faible teneur en cr présentant une excellente capacité d'amortissement et son procédé de fabrication

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KR10-2018-0073250 2018-06-26
KR1020180073250A KR102109898B1 (ko) 2018-06-26 2018-06-26 진동 감쇄능이 우수한 저Cr 페라이트계 스테인리스강 및 그 제조방법

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KR (1) KR102109898B1 (fr)
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009299182A (ja) * 2008-05-12 2009-12-24 Nisshin Steel Co Ltd フェライト系ステンレス鋼
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KR102109898B1 (ko) 2020-05-12
EP3795711A1 (fr) 2021-03-24
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