EP1818422B2 - Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist - Google Patents

Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist Download PDF

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EP1818422B2
EP1818422B2 EP07290039A EP07290039A EP1818422B2 EP 1818422 B2 EP1818422 B2 EP 1818422B2 EP 07290039 A EP07290039 A EP 07290039A EP 07290039 A EP07290039 A EP 07290039A EP 1818422 B2 EP1818422 B2 EP 1818422B2
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Prior art keywords
sheet
ferritic
steel sheet
stainless steel
niobium
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French (fr)
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EP1818422A1 (de
EP1818422B1 (de
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Francis Chassagne
Pierre-Olivier Santacreu
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Aperam Stainless France SA
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ArcelorMittal Stainless France SA
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Priority to SI200730015T priority patent/SI1818422T2/sl
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • 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
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/18—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
    • C22C38/22—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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/08—Other arrangements or adaptations of exhaust conduits
    • F01N13/10—Other arrangements or adaptations of exhaust conduits of exhaust manifolds
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/16—Selection of particular materials
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N2530/00—Selection of materials for tubes, chambers or housings
    • F01N2530/02—Corrosion resistive metals
    • F01N2530/04—Steel alloys, e.g. stainless steel

Definitions

  • the invention relates to a ferritic stainless steel, said to be 19% Niobium stabilized Cr, and its use for parts subjected to high temperatures, in particular above 950-1000.degree.
  • a good resistance to oxidation and a good mechanical resistance at high temperature are simultaneously sought: high mechanical characteristics, good resistance to creep and to thermal fatigue.
  • the high-temperature mechanical behavior must also be adapted to the thermal cycles associated with the accelerator-deceleration phases of the engines.
  • some parts such as exhaust manifolds require good cold formability to be shaped by bending or hydroforming.
  • the present invention aims to solve the problems mentioned above. It aims in particular at providing a ferritic stainless steel that has good heat resistance, that is to say a high resistance to creep, thermal fatigue and oxidation at higher periodic temperatures of use at 950 ° C and cold forming ability close to existing grades.
  • the subject of the invention is a ferritic stainless steel sheet according to claim 1.
  • the steel piece resulting from this sheet contains an intergranular precipitation comprising at least 80% of cubic Fe 2 Nb 3 compounds.
  • the linear fraction f of ferritic grain boundaries exhibiting a precipitation of cubic Fe 2 Nb 3 compounds is greater than or equal to 5%.
  • the invention also relates to a method of manufacturing a ferritic stainless steel sheet according to claim 4.
  • Another subject of the invention is a method for manufacturing a part according to which a sheet of ferritic stainless steel manufactured according to the above process is supplied, forming the sheet to obtain a part, and then subjecting the part to a or several thermal cycles in a temperature range between 650 and 1050 ° C for a cumulative duration of more than 30 minutes.
  • the invention also relates to the use of a steel sheet according to the characteristics described above, or manufactured by the method described above, for the manufacture of parts subjected to a periodic temperature of use higher than 950 ° C, including automobile exhaust gas exhaust manifolds, burners, heat exchangers, turbocharger housings, or boilers.
  • carbon increases mechanical characteristics at high temperatures, in particular creep resistance.
  • the carbon tends to precipitate in the form of carbides M 23 C 6 or M 7 C 3 at a temperature below about 900 ° C.
  • This precipitation generally located at grain boundaries, can lead to a depletion of chromium in the vicinity of these joints and thus to an awareness of intergranular corrosion.
  • This sensitization can occur especially in the Heat Affected Zones in welding that have been heated to very high temperatures.
  • the carbon content must therefore be limited to 0.03% to obtain a satisfactory resistance to intergranular corrosion and not to reduce the formability.
  • the carbon content must satisfy a relationship with molybdenum, niobium and nitrogen, as will be explained later.
  • chromium is a very effective element for increasing the resistance to oxidation during thermal cycling. To fulfill this role, a minimum content of 0.3% by weight is necessary. The inventors have also demonstrated that the weight contents of chromium and silicon must obey the relationship: Cr + 5 Si ⁇ 20%, so as to obtain good resistance to cyclic oxidation at 1000 ° C.
  • the silicon content must be limited to 1% by weight.
  • Sulfur and phosphorus are impurities that decrease hot ductility and formability. Phosphorus easily segregates at grain boundaries and decreases cohesion. As such, the sulfur and phosphorus contents must be respectively less than or equal to 0.01 and 0.04% by weight.
  • Chromium is an essential element for stabilizing the ferritic phase and increasing the resistance to oxidation.
  • its minimum content must be greater than or equal to 18% in order to obtain a ferritic structure at any temperature and to obtain good resistance to cyclic oxidation. Its maximum content must not, however, exceed 22%, otherwise the mechanical resistance to the ambient temperature will be excessively increased and the fitness ability will be reduced consecutively.
  • Nickel is a gamma element that increases the ductility of steel. In order to maintain a ferritic single-phase structure, its content must be less than or equal to 0.5% by weight.
  • Molybdenum not only increases the high temperature resistance but also the resistance to oxidation. However, above 2.5% by weight of Mo, the yield strength and room temperature resistance are excessively increased, ductility and workability decrease. As will be discussed below, molybdenum must also satisfy a relationship with niobium, carbon and nitrogen, to obtain satisfactory mechanical strength and creep resistance at 1000 ° C and fatigue resistance. between 100 ° C and 1000 ° C.
  • Copper has a heat-curing effect. In excessive quantities, however, it reduces the ductility during hot rolling. As such, the copper content must be less than or equal to 0.5% by weight.
  • the inventors have demonstrated that the contents of titanium, aluminum and zirconium must be jointly limited in order to obtain a more intense precipitation of cubic Fe 2 Nb 3 : this precipitation of compounds intermetallic acting at high temperature, provides good resistance to cyclic oxidation and creep at 1000 ° C.
  • the weight contents of Ti, Zr, Al must be limited to 0.02% each, and the sum of their contents must be such that: Ti + Al + Zr 0,0 0.030%.
  • niobium precipitates, not in the form of Fe 2 Nb 3 , but from 650 ° C in the form of Fe 2 Nb compounds, less effective to resist creep.
  • Niobium is an important element of the invention. Usually, this element can be used as a stabilizing element in ferritic stainless steels: in fact, the sensitization phenomenon mentioned above can be avoided by the addition of elements forming carbides or carbonitrides which are very thermally stable. In this way, carbon and nitrogen are minimized in solution, and subsequent precipitation of carbides and nitrides of chromium is avoided. Niobium (as well as titanium and, to a lesser extent, zirconium and vanadium) thus stably fixes carbon and nitrogen.
  • niobium content is greater than 1% by weight, the hardening obtained is too important, the steel is less easily deformable and recrystallization after cold rolling is more difficult .
  • Vanadium is an element that increases resistance to high temperature. In order to ensure satisfactory adhesion of the oxide layer formed during use at high temperature and to ensure good resistance to oxidation, the inventors have shown that the titanium and vanadium contents must satisfy the relationship: V +10 Ti ⁇ 0.06%. However, the vanadium content should be limited to 0.2% in order not to reduce the formability.
  • nitrogen increases the mechanical characteristics. However, nitrogen tends to precipitate at grain boundaries as nitrides, thus reducing corrosion resistance. In order to limit sensitization problems, the nitrogen content must be less than or equal to 0.03%.
  • the average grain size of the steel in the delivery state is between 10 and 60 micrometers, the subsequent precipitation of intermetallic compounds also making it possible to stabilize the grain size during use.
  • a grain size of less than 10 microns has a detrimental effect on intergranular creep.
  • a grain size greater than 60 microns will lead to the appearance of unsightly surface irregularities, or "orange peel", when shaping at room temperature.
  • the steels according to the invention comprise an intergranular precipitation of Fe 2 Nb 3 compounds of cubic structure, after a heat treatment of between 650 ° C. and 1050 ° C. for a time greater than 30 minutes.
  • the Fe 2 Nb 3 precipitates are very much in the majority of the intergranular precipitates, that is to say they represent more than 80% of the intergranular population.
  • the nature and distribution of these precipitates are very favorable to resist creep, in comparison with Fe 2 Nb precipitates, or Laves phases.
  • the Fe 2 Nb compounds which precipitate in intra- or intergranular form are stable only up to 950 ° C., unlike stable Fe 2 Nb 3 precipitates up to 1050 ° C.
  • the structure of the steel in the delivery state is completely recrystallized: in this way, the Subsequent precipitation of Fe 2 Nb 3 compounds occurs in a very homogeneous manner.
  • the expression f thus translates the degree of recovery of ferritic grain boundaries by a precipitation of cubic Fe 2 Nb 3 .
  • the inventors have highlighted, as the present figure 2 , that the creep resistance in a so-called sag-test, was very much improved when the linear fraction of cubic Fe 2 Nb 3 precipitates was greater than or equal to 5%: under these conditions, these precipitates play a role. very effective anchoring of joints and slow creep.
  • the sheet is then scoured and the sheet is then rolled under the usual conditions, for example by applying a reduction ratio of 30 to 90%.
  • the cold-rolled sheet is then annealed at a temperature T R and for a time t R.
  • T R and t R are chosen such that a complete recrystallization with an average ferritic grain size of between 10 and 60 microns is obtained.
  • An increase in T R and t R increases the recrystallization rate as well as the average grain size.
  • a temperature T R of between 1030 and 1130 ° C. and a time t R of between 10 seconds and 3 minutes make it possible simultaneously to obtain a complete recrystallization and a mean ferritic grain size of between 10 and 60 microns.
  • the steel sheet is in the delivery condition.
  • a part can then be manufactured from this sheet steel by implementing common modes of deformation, such as stamping, hydroforming or folding.
  • common modes of deformation such as stamping, hydroforming or folding.
  • one or more thermal cycles in a temperature range between 650 and 1050 ° C for a cumulative time greater than 30 minutes lead to a precipitation of Fe 2 Nb 3 and an increase of creep resistance.
  • This resistance is particularly high when the linear fraction f of ferritic grain boundaries comprising a precipitation of Fe 2 Nb 3 compounds is greater than or equal to 5%.
  • the recrystallization is complete and the average ferritic grain size is between 10 and 60 micrometers.
  • the figure 3 annexed illustrates the precipitates observed after creep tests at 1000 ° C in the flows I1, I2, I3 and I4 according to the invention.
  • the presence of intra- and especially intergranular precipitates covering a large part of the ferritic grain boundaries is noted.
  • Analyzes by energy dispersive spectrometry (EDS) and wavelength (WDS) reveal that more than 80% of these precipitates consist of niobium and iron, of Fe 2 Nb 3 stoichiometry, and that they do not contain neither carbon nor nitrogen.
  • figure 6 shows precipitates observed in the reference steels R3, R4 and R5.
  • the degree of recovery of the ferritic grain boundaries by these precipitates is very low after creep tests at 1000 ° C.
  • Experimental electron diffraction patterns and theoretical views along the zone axis of these precipitates are plotted respectively at Figures 7 and 8 .
  • the EDS analysis and the diffraction examinations reveal that they are precipitated Fe 2 Nb, or Laves phase, of hexagonal network.
  • the steels I1 to I4 according to the invention combine good mechanical properties when hot: mechanical resistance, resistance to creep, thermal fatigue and cyclic oxidation.
  • the R1 and R2 steels have a combination of insufficient titanium and vanadium: the resistances to cyclic oxidation and thermal fatigue are unsatisfactory due to the lack of adhesion of the oxide layers to the substrate steel.
  • R5 steel also has an excessive titanium content and a combination (Ti + Al + Zr) unsatisfactory. Moreover, its combination: Mo + 3 ⁇ Nb, is insufficient. As a result, the steel does not exhibit satisfactory mechanical properties at high temperature, in particular creep.
  • R6 steel has an insufficient chromium content as well as combinations: Mo + 3 ⁇ Nb, Cr + 5% Si insufficient. Despite the presence of Fe 2 Nb 3 compounds, the properties of oxidation resistance and high temperature mechanical properties are insufficient.
  • the steels according to the invention will be used with advantage for the manufacture of parts subjected to a temperature periodic use greater than 950 ° C, and in particular exhaust gas collectors in the automotive field, burners, heat exchangers or envelopes turbochargers, boilers.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Catalysts (AREA)

Claims (6)

  1. Blech aus ferritischem Edelstahl, dessen Zusammensetzung Folgendes umfasst, wobei die Gehalte nach Gewicht ausgedrückt sind:
    C ≤ 0,03 %
    Mn ≤ 1 %
    0,3 ≤ Si ≤ 1 %
    s ≤ 0,01 %
    P ≤ 0, 04 %
    18 % ≤ Cr ≤ 22 %
    Ni ≤ 0,5 %
    Mo ≤ 2,5 %
    Cu ≤ 0, 5 %
    Ti ≤ 0,02 %
    Zr ≤ 0,02 %
    Al ≤ 0, 02 %
    0,2 % ≤ Nb ≤ 1 %
    v ≤ 0,2 %
    N ≤ 0, 03 %
    0,005 % ≤ Co ≤ 0,05 %
    Sn ≤ 0,05 %,
    mit der Maßgabe, dass
    Ti + Al + Zr ≤ 0,030 %
    Cr + 5 Si ≥ 20 %
    V + 10 Ti ≥ 0,06 %,
    wobei Eisen und unvermeidbare herstellungsbedingte Verunreinigungen den Rest der Zusammensetzung ausmachen, dessen Gefüge vollständig umkristallisiert ist und die mittlere Größe der ferritischen Körner 10 bis 60 Mikrometer beträgt.
  2. Werkstück, das aus einem Stahlblech nach Anspruch 1 hergestellt ist, dadurch gekennzeichnet, dass es eine intergranulare Abscheidung enthält, die mindestens 80% an kubischen Fe2Nb3-Verbindungen umfasst.
  3. Werkstück nach Anspruch 2, dadurch gekennzeichnet, dass die lineare Fraktion f der Grenzen der ferritischen Körner, welche eine Abscheidung von kubischen Fe2Nb3-Verbindungen aufweist, mindestens 5 % ausmacht, wobei die Fraktion "f' als f = (∑(s)di/(∑(s)Li), definiert ist, wobei Z(s)di die Gesamtlänge der Korngrenzen, die Fe2Nb3-Abscheidungen aufweisen im Verhältnis zur betrachteten Fläche (S) bezeichnet und ∑(s)Li für die Gesamtlänge der Korngrenzen steht.
  4. Herstellungsverfahren für ein Blech aus ferritischem Edelstahl, welches die folgenden Schritte umfasst:
    - Bereitstellen eines Stahls, der eine Zusammensetzung nach Anspruch 1 aufweist,
    - Gießen eines Halbzeugs aus diesem Stahl,
    - Erhitzen des Halbzeugs auf eine Temperatur von mehr als 1000 °C,
    - Warmwalzen des Halbzeugs, sodass ein warmgewalztes Blech erhalten wird,
    - Kaltwalzen des Blech, und anschließend
    - Glühen des kaltgewalzten Blechs bei einer Temperatur TR im Bereich von 1030 bis 1130 °C für eine Zeitdauer tR im Bereich von 10 Sekunden bis 3 Minuten, um ein vollständig umkristallisiertes Gefüge zu erhalten, in welchem die Größe der ferritischen Körner 10 bis 60 Mikrometer beträgt.
  5. Herstellungsverfahren für ein Werkstück, welches darin besteht, ein Blech aus ferritischem Edelstahl, das gemäß Anspruch 4 hergestellt wurde, bereitzustellen, um dann
    - das Blech derart zu formen, dass ein Werkstück erhalten wird, und anschließend
    - das Werkstück einem oder mehreren Erhitzungszyklen auszusetzen, wobei die Temperaturen im Bereich von 650 bis 1050 °C liegen und zwar während eines Zeitraums von insgesamt mehr als 30 Minuten.
  6. Verwendung des Stahlblechs nach einem beliebigen der Ansprüche 1 oder 3, oder aber eines solchen, das mittels eines Verfahrens nach Anspruch 4 hergestellt wurde, um Werkstücke herzustellen, die bei ihrer Verwendung zeitweise Temperaturen von mehr als 950 °C ausgesetzt sind, wobei es sich insbesondere um Abgaskrümmer für Verbrennungsgase im Kraftfahrzeugwesen, um Brenner, um Wärmetauscher, um Turboladergehäuse und um Heizkessel handelt.
EP07290039A 2006-02-08 2007-01-11 Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist Active EP1818422B2 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP07290039A EP1818422B2 (de) 2006-02-08 2007-01-11 Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist
SI200730015T SI1818422T2 (sl) 2006-02-08 2007-01-11 Feritno nerjavno jeklo z kroma stabilizirano z niobijem

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP06290231A EP1818421A1 (de) 2006-02-08 2006-02-08 Ferritischer, Niobium-stabilisierter 19% Chrom-Edelstahl
EP07290039A EP1818422B2 (de) 2006-02-08 2007-01-11 Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist

Publications (3)

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EP1818422A1 EP1818422A1 (de) 2007-08-15
EP1818422B1 EP1818422B1 (de) 2008-12-10
EP1818422B2 true EP1818422B2 (de) 2012-07-18

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EP06290231A Withdrawn EP1818421A1 (de) 2006-02-08 2006-02-08 Ferritischer, Niobium-stabilisierter 19% Chrom-Edelstahl
EP07290039A Active EP1818422B2 (de) 2006-02-08 2007-01-11 Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist

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EP06290231A Withdrawn EP1818421A1 (de) 2006-02-08 2006-02-08 Ferritischer, Niobium-stabilisierter 19% Chrom-Edelstahl

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AT (1) ATE417134T1 (de)
DE (1) DE602007000326D1 (de)
DK (1) DK1818422T4 (de)
ES (1) ES2317629T5 (de)
PT (1) PT1818422E (de)
SI (1) SI1818422T2 (de)

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MY160980A (en) * 2012-05-28 2017-03-31 Jfe Steel Corp Ferritic stainless steel
SI2893049T1 (sl) 2012-09-03 2021-03-31 Aperam Stainless France, Feritna nerjavna jeklena pločevina, postopek za njeno izdelavo in njena uporaba, zlasti v izpušnih vodih
FI124995B (fi) 2012-11-20 2015-04-15 Outokumpu Oy Ferriittinen ruostumaton teräs
JP6159775B2 (ja) 2014-10-31 2017-07-05 新日鐵住金ステンレス株式会社 耐排ガス凝縮水腐食性とろう付け性に優れたフェライト系ステンレス鋼及びその製造方法
EP3214198B1 (de) * 2014-10-31 2022-06-01 NIPPON STEEL Stainless Steel Corporation Ferrit-basierter rostfreier stahl mit hoher beständigkeit gegen korrosivität durch abgas und kondensation und mit guten löteigenschaften sowie verfahren zur herstellung davon
US11261512B2 (en) 2016-09-02 2022-03-01 Jfe Steel Corporation Ferritic stainless steel
CN110088324A (zh) * 2016-12-21 2019-08-02 杰富意钢铁株式会社 铁素体系不锈钢
KR102508125B1 (ko) * 2018-01-31 2023-03-08 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강
ES2927078T3 (es) 2018-12-21 2022-11-02 Outokumpu Oy Acero inoxidable ferrítico
KR102259806B1 (ko) * 2019-08-05 2021-06-03 주식회사 포스코 고온 내크립 특성이 향상된 페라이트계 스테인리스강 및 그 제조 방법
CN112375995B (zh) * 2021-01-15 2021-05-07 江苏省沙钢钢铁研究院有限公司 400MPa级耐蚀钢筋及其生产方法
CN116479330A (zh) * 2023-04-27 2023-07-25 山西常达精密金属科技有限公司 一种汽车排气系统焊接用超纯铁素体不锈钢材料及其制备

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Also Published As

Publication number Publication date
EP1818422A1 (de) 2007-08-15
DK1818422T3 (da) 2009-02-23
SI1818422T2 (sl) 2012-11-30
DE602007000326D1 (de) 2009-01-22
ES2317629T3 (es) 2009-04-16
EP1818421A1 (de) 2007-08-15
EP1818422B1 (de) 2008-12-10
ES2317629T5 (es) 2012-12-26
DK1818422T4 (da) 2012-10-29
PT1818422E (pt) 2009-01-30
SI1818422T1 (sl) 2009-04-30
ATE417134T1 (de) 2008-12-15

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