EP3666918B1 - Acier inoxydable ferritique présentant une excellente résistance à la corrosion et aux chocs - Google Patents

Acier inoxydable ferritique présentant une excellente résistance à la corrosion et aux chocs Download PDF

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EP3666918B1
EP3666918B1 EP19191488.6A EP19191488A EP3666918B1 EP 3666918 B1 EP3666918 B1 EP 3666918B1 EP 19191488 A EP19191488 A EP 19191488A EP 3666918 B1 EP3666918 B1 EP 3666918B1
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stainless steel
ferritic stainless
less
content
amount
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EP3666918A1 (fr
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Min Woo Kang
Chung An Lee
Seung Hyun Hong
Soon Woo Kwon
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Hyundai Motor Co
Kia Corp
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Hyundai Motor Co
Kia Corp
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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
    • 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
    • C22C38/02—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
    • 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
    • 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
    • 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

Definitions

  • the present invention relates to a ferritic stainless steel having improved impact resistance and corrosion resistance at high temperatures by suppressing formation of a sigma phase.
  • Exhaust system components such as exhaust pipes, mufflers, and the like, of automobiles have been required to have thermal fatigue properties, high temperature fatigue properties and oxidation resistance.
  • ferritic stainless steel having high corrosion resistance by including chromium (Cr) as an alloy component has been mainly used for exhaust system components.
  • ferritic stainless steel for an exhaust system component contains 15 to 20% of chromium (Cr) to maintain corrosion resistance at high temperatures.
  • Cr chromium
  • Mo molybdenum
  • cost is increased due to an increase in the content of the high-priced alloy elements.
  • a sigma phase may be formed, and as a fraction thereof may be increased, durability (impact resistance) may be deteriorated against expectations and corrosion resistance may also be deteriorated.
  • formation of the sigma phase include Fe, Si, Mn, Mo and Cr can be suppressed.
  • a conventional ferritic stainless steel may contain the sigma phase at a volume fraction of 5 to 20%.
  • a technique for reducing the volume fraction of the sigma phase in ferritic stainless steels has continuously been researched.
  • EP 2 723 910 A1 describes a heat-resistant Fe-Cr-Al alloy with low chromium vaporization rate comprising among others 1 to 4% tungsten and 0,25 to 2% niobium, wherein tungsten provides the high-temperature strength and creep strength.
  • EP 2 995 697 A1 discloses a stainless steel substrate for solar battery including among others 0,005 to 4% silicon, 0,05% phosphor or less and 0,01% sulfur or less, wherein the phosphor and the sulfur help in limiting an increase in the refining cost.
  • EP 3 339 460 A1 discloses a vibration-damping ferritic stainless steel material comprising among others from 0,01 to 0,6% nickel and from 0,1 to 1% silicon.
  • a ferritic stainless steel having improved impact resistance and corrosion resistance at high temperatures so that the ferritic stainless steel may be used as an exhaust system component exposed to a high temperature environment.
  • the ferritic stainless steel is obtained by suppressing formation of a sigma phase s.
  • the present invention provides a ferritic stainless steel with the features according to claim 1. Further preferred embodiments of the steel are described in the dependent claims.
  • a volume fraction of a sigma phase formed in a temperature range of 300 to 900 °C may be less than 5 %.
  • the term "sigma phase” as used herein refers to a non-magnetic stage or phase mainly including iron and calcium in stainless steels, e.g., ferritic and austenitic stainless steels.
  • the sigma phase may form at ferrite/austenite interfaces or boundaries and such intermolecular stage or phase may cause metal alloy or stainless steel to lose ductility, toughness, stability and corrosion resistance.
  • precipitation of the sigma phase can be often observed in various series of stainless steels and can be precipitated under an elevated temperature environment, for example, casting, rolling, welding, forging, and aging.
  • the sigma phase occurs during metallic exposure to a temperature range from 300 °C to 1000 °C, 300 to 900 °C, 400 to 900 °C or 500 to 900 °C.
  • the volume fraction of the sigma phase formed in the temperature range of 300 to 900 °C may suitably be 0.5 % or less or may not be precipitated.
  • the volume fraction of the sigma phase formed in the temperature range of 300 to 900 °C may not be precipitated.
  • a volume fraction of Cr 3 Si formed in the temperature range of 300 to 900 °C may suitably be 0.5% or less.
  • a volume fraction of each of AlN and Al 2 O 3 formed in the temperature range of 300 to 900 °C may suitably be 0.0001 % or less.
  • a volume fraction of M 23 C 6 formed in the temperature range of 300 to 900 °C may suitably be less than 0. 2%.
  • a volume fraction of a laves phase formed in the temperature range of 300 to 900 °C may suitably be 0.2% or less.
  • a pitting potential (Ept) of the stainless steel in 3.5 % of sodium chloride (NaCl) at a temperature of 25 °C may suitably be 300 mV SCE or greater.
  • pitting potential refers to an electrochemical potential that corresponds to the least positive current and voltage at which pits develop or grow on a metallic surface and a corrosion pit initiates on a metallic surface.
  • pitting for a stainless steel as used herein may be characterized electrochemically by the critical pitting potential (Ept).
  • Ept critical pitting potential
  • a time required for forming rust in a condition of 5 % of sodium chloride (NaCl) after 3 % of salt water is sprayed may be 250 days or greater.
  • Impact resistance strength of the ferritic stainless steel measured by a Charpy keyhole-notch impact test may suitably be 55 J or greater.
  • an exhaust system component of a vehicle that includes the ferritic stainless steel as described herein.
  • vehicle or “vehicular” or other similar term as used herein is inclusive of motor vehicles in general such as passenger automobiles including sports utility vehicles (SUV), buses, trucks, various commercial vehicles, watercraft including a variety of boats and ships, aircraft, and the like, and includes hybrid vehicles, electric vehicles, plug-in hybrid electric vehicles, hydrogen-powered vehicles and other alternative fuel vehicles (e.g. fuels derived from resources other than petroleum).
  • a hybrid vehicle is a vehicle that has two or more sources of power, for example both gasoline-powered and electric-powered vehicles.
  • FIG. 1 shows various exemplary steel compositions in Inventive Examples and Comparative Examples
  • FIG. 2 shows phases generated in Inventive Examples and Comparative Examples.
  • a ferritic stainless steel that is optimized in the content of major alloy components to suppress formation of a structure or intermetallic phase (e.g., a sigma phase) that negatively affects physical properties of stainless steel.
  • the ferritic stainless steel is disclosed in the appended claims.
  • Carbon (C) is contained in an amount of 0.015 wt% or less based on the total weight of the ferric stainless steel.
  • Carbon (C) as used herein is an element effective for enhancing strength of stainless steel. For instance, Ti(C,N) may be formed to expect a precipitation strengthening effect and suppress high temperature structure growth (grain growth) such that an increased in creep strength and enhancement of tempering physical properties may be expected.
  • M 23 C 6 carbide may be formed to deteriorate thermal impact characteristics.
  • Silicon (Si) is contained in an amount of 0.17 wt% or less based on the total weight of the ferric stainless steel. Silicon (Si) as used herein is an element that acts as a deoxidizer and increases oxidation resistance and castability. However, when the content of silicon (Si) is greater than 0.17%, a sigma phase may be formed to deteriorate impact resistance and corrosion resistance.
  • Manganese (Mn) is contained in an amount of 1.35 wt% or less based on the total weight of the ferric stainless steel. Manganese (Mn) as used herein improves hardenability and yield strength of steel. However, when the content of manganese (Mn) is greater than 1.35 wt%, a sigma phase may be formed to deteriorate impact resistance and corrosion resistance.
  • Chromium (Cr) is contained in an amount of 17 to 20 wt% based on the total weight of the ferric stainless steel. Chromium (Cr) as used herein is an important element to ensure corrosion resistance of stainless steel and to obtain solid solution strengthening effect and stabilize an austenite phase. However, when the content of chromium (Cr) is less than 17 wt%, oxidation resistance may be deteriorated, and when the content of chromium (Cr) is greater than 20 wt%, the austenite phase may be stabilized and a matrix structure may be changed to an austenitic system or duplex system.
  • Aluminum (Al) is contained in an amount of 3 to 5 wt% based on the total weight of the ferric stainless steel.
  • Aluminum (Al) which is an element acting as a solubility enhancer, increases oxidation resistance and makes the structure finer and uniform. If the content of aluminum (Al) is less than 3%, a sigma phase may be formed to lower structure uniformity, and if the content of aluminum (Al) exceeds 5%, a negative phase such as Cr 3 Si may be formed.
  • Titanium (Ti) is contained in an amount of 0.5 wt% or less based on the total weight of the ferric stainless steel. Titanium (Ti) as used herein forms carbides to improve precipitation strengthening and high temperature strength. When the content of titanium (Ti) is greater than 0.5%, a laves phase may be formed and impact resistance and corrosion resistance may be decreased. The content of titanium (Ti) is limited to a minimum value of 0.1 wt%. When the content of titanium (Ti) is less than 0.1 wt%, formation of AlN, which deteriorates strength and weldability at high temperatures, may be increased.
  • the content of nitrogen (N) is less than 0.02 wt% based on the total weight of the ferric stainless steel.
  • Nitrogen (N) as used herein induces formation of carbonitride, for example, Ti(C,N) may be formed to obtain a precipitation strengthening effect and suppress high temperature structure growth (grain growth). As such, creep strength may be increased and tempering physical properties may be improved.
  • the content of nitrogen is greater than 0.02 wt%, formation of AlN is increased.
  • Oxygen (O) is contained in an amount of less than 0.001 wt% based on the total weight of the ferric stainless steel. Oxygen (O) forms inclusions to decrease impact resistance, and is controlled to be as low as possible. An upper limit value of oxygen (O) is 0.001 wt% in consideration of a removing process.
  • zirconium (Zr), calcium (Ca), and magnesium (Mg) The sum of the contents of zirconium (Zr), calcium (Ca), and magnesium (Mg) is adjusted to 0.001 wt% to 0.01 wt% based on the total weight of the ferric stainless steel.
  • Zirconium (Zr), calcium (Ca), and magnesium (Mg) as used herein serves as a deoxidizer.
  • the total content of zirconium (Zr), calcium (Ca), and magnesium (Mg) is less than 0.001 wt%, Al 2 O 3 may be generated, and when the total content of Al 2 O 3 is greater than 0.01 wt%, castability may be deteriorated.
  • the remainder other than the above-mentioned components includes Fe and inevitably contained impurities.
  • molten steel having the composition described above may be continuously cast through a general method to produce a slab, the slab is re-heated, a post-treatment such as hot rolling, hot annealing, cold rolling, and cold annealing is subsequently performed thereon.
  • a phase which negatively affects physical properties
  • a sigma phase is suppressed at a temperature of 300 to 900 °C, where an exhaust system component is typically used, by controlling the amount of Si, Mn, and Al which affects formation of a negative phase.
  • the amount of Si, Mn, and Al satisfies [Equation 1] below. 20 Si + Mn / Al ⁇ 0.7
  • Si, Mn, and Al refer to the content (wt%) of each component.
  • the content of Zr, Ca, and Mg is further limited to suppress formation of AlN and Al 2 O 3 .
  • the content of Zr, Ca, and Mg satifies [Equation 2] below. 0.001 ⁇ Zr + Ca + Mg ⁇ 0.01
  • Equation 2 Zr, Ca and Mg refer to the content (wt%) of each component.
  • each slab continuously cast using molten steel adjusted in composition may be re-heated and hot-rolled in a temperature range of 1050 to 1100 °C and subsequently annealed at a continuous annealing line (CAL) for 90 seconds in a temperature range of 900 to 950°C.
  • CAL continuous annealing line
  • structures cold-rolled and cold-annealed samples were observed at a temperature of 300 to 900 °C, which is a temperature range at which an exhaust system component is generally used. Results thereof are illustrated in FIGS. 2 and 3 .
  • sample No. 18, which is Inventive Example satisfying the kind and content of the alloy components given in the present invention included Ti(C,N) and laves phase formed on the basis of ferrite as a matrix structure but a sigma phase was not formed.
  • the laves phase which negatively affects physical properties, was formed, a maximum volume fraction thereof was generated, for example, 0.13% of the laves phase was formed.
  • Ti(C,N), sigma phase, laves phase, and G phase were formed on the basis of ferrite as a matrix structure.
  • the sigma phase which negatively affects the physical properties, was formed by 5% or greater based on a volume fraction and that the laves phase was formed by 0.2% or greater based on the volume fraction.
  • samples No. 5 and No. 6, which are Comparative Examples, did not satisfy the condition of [Equation 1] and the sigma phase was formed by 17% and 18%, respectively.
  • M 23 C 6 a negative phase, was formed in by 0.2%.
  • M denotes metallic elements which are Fe, Cr, Mn, and Ti in the present invention.
  • Sample No. 8 is Comparative Example including the content of Si greater than the predetermined amount discussed above and the condition of [Equation 1] given in the present invention was not met
  • Sample No. 9 is Comparative Example including the content of Mn greater than the predetermined amount discussed above in the present invention.
  • the sigma phase was formed by 10% and 8%, respectively.
  • Sample No. 10 satisfied most of the contents of the alloy elements given in the present invention, and the sigma phase and the laves phase, which are negative phases, were not formed.
  • the content of Ti in Sampel No. 10 was less than the predetermined content of Ti as discussed above in the present invention. Since the content of Ti is less than a limit range, AlN, which deteriorates strength and weldability at high temperatures, was formed by 0.0002%.
  • Sample No. 11 is Comparative Example including the content of Ti greater than the predetermined amount as discussed above in the present invention such that laves phase was formed by 2.1%.
  • Samples No. 12 and No 13 are Comparative Examples that did not satisfy the content of Al given in the present invention.
  • Sample No 12 contained the sigma phase formed by 7% when the content of Al was less than the predetermined range discussed above and sample No. 13 contained Cr 3 Si formed by 0.8% as the content of Al is greater than the predetermined range discussed above.
  • Sample No. 14 is Comparative Example that did not satisfy the content of N given in the present invention. When the content of N is greater than the predetermined range discussed above, AlN was formed by 0.001%.
  • Sample No. 15 is Comparative Example that did not satisfy the content of O given in the present invention, and when the content of O was greater than the predetermined range discussed above, Al 2 O 3 was formed by 0.0002%.
  • Sample No. 16 is Comparative Example that did not satisfy the condition of [Equation 1] and the sigma phase was formed by 8%.
  • Sample No. 17 is Comparative Example that did not satisfy the condition of [Equation 2] and the content of Zr, Ca and Mg was less than the condition of [Equation 2] so Al 2 O 3 was formed by 0.0002%.
  • formation of Cr 3 Si AlN, Al 2 O 3 , and M 23 C 6 , including the sigma phase and the laves phase, which are negative phases, are suppressed by controlling the kind and content of the alloy components to satisfy the conditions discussed above
  • pitting potential a pitting potential of 3.5% of sodium chloride (NaCl) at a temperature of 25 °C was measured.
  • the pitting potential was measured by a type of measurement instrument using saturated calomel electrode (SCE) as a reference point.
  • SCE saturated calomel electrode
  • Impact resistance was measured by a Charpy keyhole-notch impact test, and a corrosion amount was measured when exposed to the atmosphere at a temperature section of 600 to 900°C in which the exhaust system component is generally used.
  • the pitting potential (Ept) at 3.5% sodium chloride (NaCl) was measured as 300 mV SCE at a temperature of 25°C.
  • all of samples No. 1 to No. 4 were measured to be less than 300 mV SCE .
  • fitting resistance is excellent.
  • the pitting potential was improved when the type and content of the alloy components of the present invention were satisfied.
  • a time required for forming rust due to 5% of sodium chloride (NaCl) after 3% of salt water was sprayed was measured to be 294 days, greater than 250 days compared to Comparative Examples No. 1 to No. 4 where rust was formed earlier than 250 days.
  • a precipitation temperature range of the sigma phase narrowed and the volume fraction decreased as the content of Al increased until the Al content reached 3%.
  • stability of the sigma phase was significantly reduced so as not to be formed.
  • the content of Al is greater than 5 wt%, Cr 3 Si was produced.
  • the sigma phase may be formed when the content of Si and Mn is large.
  • the formation of the sigma phase may affect Si, Mn and Cr in this order in the alloy components, and the content of Si may have sensitivity of 20 times as compared with the content of Mn.
  • the formation of the sigma phase was suppressed when the relational expression described in [Equation 1] was satisfied. This phenomenon is also confirmed with the results of samples No. 12 and 17.
  • AlN was formed when the content of N was 0.03 wt% or greater.
  • the content of N is limited to be less than 0.02 wt%.
  • Al 2 O 3 was formed when the total amount of Zr, Ca, and Mg was less than 0.001 wt% and that Al 2 O 3 was not formed when the total amount of Zr, Ca, and Mg was greater than 0.01 wt%.
  • the ferritic stainless steel has obtained excellent corrosion resistance and impact resistance at high temperatures at which the exhaust system component is generally used by suppressing formation of the sigma phase and by controlling the content of the alloy elements that affect formation of the sigma phase and the laves phase.
  • the excellent corrosion resistance and impact resistance at high temperatures is maintained without adding high-priced alloy elements, and thus, cost are reduced as compared to other steel products that realize similar performance.
  • the ferritic stainless steel may have obtained excellent corrosion resistance and impact resistance at high temperatures at which the exhaust system component is generally used by suppressing formation of the sigma phase and by controlling the content of the alloy elements that affect formation of the sigma phase and the laves phase.
  • the excellent corrosion resistance and impact resistance at high temperatures may be maintained without adding high-priced alloy elements, and thus, cost may be reduced as compared to other steel products that realize similar performance.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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Claims (11)

  1. Acier inoxydable ferritique composé de :
    une quantité de 0,015 % en poids ou moins, à l'exclusion de 0 % en poids, de carbone (C),
    une quantité de 0,17 % en poids ou moins, à l'exclusion de 0 % en poids, de silicium (Si),
    une quantité de 1,35 % en poids ou moins, à l'exclusion de 0 % en poids, de manganèse (Mn),
    une quantité de 17 à 20 % en poids de chrome (Cr),
    une quantité de 0,1 à 0,5 % en poids de titane (Ti),
    une quantité de 3 à 5 % en poids d'aluminium (Al),
    une quantité inférieure à 0,001 % en poids d'oxygène (O),
    une quantité inférieure à 0,02 % en poids d'azote (N),
    le fer (Fe) constituant le reste de l'acier inoxydable ferritique,
    tous les pourcentages en poids sont basés sur le poids total de l'acier inoxydable ferritique,
    dans lequel les teneurs en Si, Mn et Al satisfont à l'[Équation 1],
    (20Si+Mn)/Al < 0,7 [Équation 1]
    où Si, Mn et Al dans l'Équation 1 représentent la teneur en % en poids de chaque composant,
    comprenant en outre :
    du zirconium (Zr), du calcium (Ca) et du magnésium (Mg),
    dans lequel les teneurs en Zr, Ca et Mg satisfont à [l'Équation 2] 0,001 ≤ Zr+Ca+Mg ≤ 0,01 [Équation 2]
    dans lequel Zr, Ca et Mg dans l'Équation 2 représentent la teneur en % en poids de chaque composant.
  2. Acier inoxydable ferritique selon la revendication 1, dans lequel une fraction volumique d'une phase sigma formée dans une plage de température de 300 à 900 °C est inférieure à 5 %.
  3. Acier inoxydable ferritique selon la revendication 2, dans lequel la fraction volumique de la phase sigma formée dans la plage de température de 300 à 900 °C est de 0,5 % ou moins ou n'est pas précipitée.
  4. Acier inoxydable ferritique selon la revendication 3, dans lequel la fraction volumique de la phase sigma formée dans la plage de température de 300 à 900 °C n'est pas précipitée.
  5. Acier inoxydable ferritique selon l'une des revendications 1 à 4, dans lequel une fraction volumique de CrsSi formée dans la plage de température de 300 à 900 °C est de 0,5 % ou moins.
  6. Acier inoxydable ferritique selon l'une des revendications 1 à 5, dans lequel une fraction volumique de chacun de AIN et Al2O3 formée dans la plage de température de 300 à 900 °C est de 0,0001 % ou moins.
  7. Acier inoxydable ferritique selon l'une des revendications 1 à 6, dans lequel une fraction volumique de M23C6 formée dans la plage de température de 300 à 900 °C est inférieure à 0, 2 %.
  8. Acier inoxydable ferritique selon l'une des revendications 1 à 7, dans lequel une fraction volumique d'une phase de laves formée dans la plage de température de 300 à 900 °C est de 0,2 % ou moins.
  9. Acier inoxydable ferritique selon l'une des revendications 1 à 8, dans lequel un potentiel de piqûration (Ept) de l'acier inoxydable ferritique dans 3,5 % de chlorure de sodium (NaCl) à une température de 25 °C est de 300 mVSCE ou supérieur.
  10. Acier inoxydable ferritique selon l'une des revendications 1 à 9, dans lequel un temps nécessaire à la formation de rouille dans une condition de 5 % de chlorure de sodium (NaCl) après pulvérisation de 3 % d'eau salée est de 250 jours ou plus.
  11. Acier inoxydable ferritique selon l'une des revendication1 à 10, dans lequel
    la résistance aux chocs de l'acier inoxydable ferritique mesurée par un essai de choc de Charpy par entaille en trou de serrure est de 55 J ou plus.
EP19191488.6A 2018-12-12 2019-08-13 Acier inoxydable ferritique présentant une excellente résistance à la corrosion et aux chocs Active EP3666918B1 (fr)

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JP3865452B2 (ja) * 1997-03-13 2007-01-10 日新製鋼株式会社 耐高温酸化性および耐高温変形性に優れたＦｅ−Ｃｒ−Ａｌフエライト系ステンレス鋼
JP5544106B2 (ja) * 2009-03-24 2014-07-09 新日鐵住金ステンレス株式会社 燃料電池用Ａｌ含有耐熱フェライト系ステンレス鋼およびその製造方法
KR20120108785A (ko) 2011-03-25 2012-10-05 주식회사 포스코 고온강도가 우수한 페라이트계 스테인리스강
DE202011106778U1 (de) * 2011-06-21 2011-12-05 Thyssenkrupp Vdm Gmbh Hitzebeständige Eisen-Chrom-Aluminium-Legierung mit geringer Chromverdampfungsrate und erhöhter Warmfestigkeit
DE102012004488A1 (de) * 2011-06-21 2012-12-27 Thyssenkrupp Vdm Gmbh Hitzebeständige Eisen-Chrom-Aluminium-Legierung mit geringer Chromverdampfungsrate und erhöhter Warmfestigkeit
JP6392501B2 (ja) * 2013-05-10 2018-09-19 新日鐵住金ステンレス株式会社 絶縁性に優れた熱膨張係数の小さいステンレス製太陽電池用基板およびその製造方法
JP6370276B2 (ja) * 2015-08-17 2018-08-08 日新製鋼株式会社 高Ａｌ含有制振性フェライト系ステンレス鋼材および製造方法

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CN111304528B (zh) 2023-02-17
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KR20200071980A (ko) 2020-06-22
CN111304528A (zh) 2020-06-19

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