EP1818422A1 - 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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Publication number
EP1818422A1
EP1818422A1 EP07290039A EP07290039A EP1818422A1 EP 1818422 A1 EP1818422 A1 EP 1818422A1 EP 07290039 A EP07290039 A EP 07290039A EP 07290039 A EP07290039 A EP 07290039A EP 1818422 A1 EP1818422 A1 EP 1818422A1
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Prior art keywords
steel sheet
sheet
ferritic
niobium
stainless steel
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EP07290039A
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English (en)
French (fr)
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EP1818422B1 (de
EP1818422B2 (de
Inventor
Francis Chassagne
Pierre-Olivier Santacreu
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Aperam Stainless France SA
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Ugine et Alz France SA
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Priority to SI200730015T priority Critical patent/SI1818422T2/sl
Priority to EP07290039A priority patent/EP1818422B2/de
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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 to provide a stainless steel ferritic which has good heat resistance, ie high creep, thermal fatigue and oxidation resistance at periodic temperatures above 950 ° C and Cold shaping close to existing shades.
  • the subject of the invention is a ferritic stainless steel sheet whose composition comprises, the contents being expressed by weight: 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%, the rest of the composition consisting of iron and unavoidable impurities resulting from the elaboration, the contents of titanium, aluminum and zirconium satisfying the relationship: Ti + Al + Zr ⁇ 0.030%, the contents in silicon and chromium satisfying the relationship: Cr + 5 Si ⁇ 20%, the contents of niobium, carbon, nitrogen and molybdenum satisfying the relation: Mo + 3 (Nb-7C-7N) ⁇ 1.5%, the contents
  • the steel 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 structure is entirely recrystallized and the average ferritic grain size of the steel is between 10 and 60 micrometers.
  • T R and t R are chosen so that a completely recrystallized structure with a grain size of between 10 and 60 microns is obtained.
  • 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 time greater 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 intermetallic compounds operating at high temperature makes it possible to obtain 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., contrary to 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 the Fe 2 Nb 3 compounds occurs in a very homogeneous manner.
  • the inventors have demonstrated that the efficiency of the cubic Fe 2 Nb 3 compounds was particularly increased when the linear fraction of ferritic grain boundaries which had a precipitation of these compounds was greater than or equal to 5%.
  • the definition of this linear fraction f is given in FIG. 1: If one considers a particular grain whose contour is limited by successive grain boundaries of length L 1 , L 2 , .. L i , observations in microscopy electronic show that this grain can comprise precipitates Fe 2 Nb 3 along the joints over a length d 1 , ..d i ...
  • 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 demonstrated, as shown in FIG. 2, that the creep resistance during a so-called "sag-test" test was very much improved when the linear fraction of cubic Fe 2 Nb 3 precipitates was greater than or equal to at 5%: under these conditions, these precipitates play a very effective role of anchoring 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 with 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.
  • FIG. 3 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.
  • EDS energy dispersive spectrometry
  • WDS wavelength
  • 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 given in Figures 7 and 8, respectively.
  • the EDS analysis and the diffraction studies reveal that they are Fe 2 Nb precipitates. , or phase of Laves, 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 periodic operating temperature greater than 950 ° C., and in particular of combustion gas exhaust manifolds in the automobile field, of burners, of Heat exchangers or envelopes of 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)
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
SI200730015T SI1818422T2 (sl) 2006-02-08 2007-01-11 Feritno nerjavno jeklo z kroma stabilizirano z niobijem
EP07290039A EP1818422B2 (de) 2006-02-08 2007-01-11 Ferritischer Edelstahl mit 19 % Chrom, der mit Niob stabilisiert ist

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)

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

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Family Applications (2)

Application Number Title Priority Date Filing Date
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

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP06290231A Withdrawn EP1818421A1 (de) 2006-02-08 2006-02-08 Ferritischer, Niobium-stabilisierter 19% Chrom-Edelstahl

Country Status (7)

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EP (2) EP1818421A1 (de)
AT (1) ATE417134T1 (de)
DE (1) DE602007000326D1 (de)
DK (1) DK1818422T4 (de)
ES (1) ES2317629T5 (de)
PT (1) PT1818422E (de)
SI (1) SI1818422T2 (de)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014033372A1 (fr) 2012-09-03 2014-03-06 Aperam Stainless France Tôle d'acier inoxydable ferritique, son procédé de fabrication, et son utilisation, notamment dans des lignes d'échappement
US20170275723A1 (en) * 2014-10-31 2017-09-28 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
EP3670692A1 (de) 2018-12-21 2020-06-24 Outokumpu Oyj Ferritischer edelstahl
CN114364820A (zh) * 2019-08-05 2022-04-15 株式会社Posco 具有改善的高温蠕变抗力的铁素体不锈钢及其制造方法
US11384405B2 (en) 2012-11-20 2022-07-12 Outokumpu Oyj Ferritic stainless steel

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EP2857538B1 (de) * 2012-05-28 2018-04-18 JFE Steel Corporation Ferritischer edelstahl
WO2016068291A1 (ja) * 2014-10-31 2016-05-06 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
US11261512B2 (en) 2016-09-02 2022-03-01 Jfe Steel Corporation Ferritic stainless steel
US20190316236A1 (en) * 2016-12-21 2019-10-17 Jfe Steel Corporation Ferritic stainless steel
KR102508125B1 (ko) * 2018-01-31 2023-03-08 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강
CN113186472B (zh) * 2021-01-15 2022-07-22 江苏省沙钢钢铁研究院有限公司 耐蚀钢筋及其生产方法

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US4726853A (en) * 1985-11-05 1988-02-23 Ugine Gueugnon Sa Ferritic stainless steel strip or sheet, in particular for exhaust systems
EP0478790A1 (de) * 1990-03-24 1992-04-08 Nisshin Steel Co., Ltd. Hitzebeständiger ferritischer nichtrostender stahl mit hervorragenden eigenschaften für zähigkeit bei tiefen temperaturen, schweissbarkeit und hitzebeständigkeit
EP1083241A1 (de) * 1999-09-09 2001-03-14 Ugine S.A. Ferritisches Niobium-stabilisiertes 14% Chrom-stahl und dessen Verwendung in Kraftfahrzeugen
EP1170392A1 (de) * 2000-07-04 2002-01-09 Kawasaki Steel Corporation Ferritischer rostfreier Stahl

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JPH0735556B2 (ja) † 1990-12-26 1995-04-19 川崎製鉄株式会社 高温強度と溶接熱影響部の靱性に優れたフェライト系ステンレス鋼
JPH0717988B2 (ja) † 1991-03-08 1995-03-01 日本冶金工業株式会社 靱性および耐食性がともに優れるフェライト系ステンレス鋼

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US4010049A (en) * 1975-10-06 1977-03-01 Jones & Laughlin Steel Corporation Columbium-stabilized high chromium ferritic stainless steels containing zirconium
US4726853A (en) * 1985-11-05 1988-02-23 Ugine Gueugnon Sa Ferritic stainless steel strip or sheet, in particular for exhaust systems
EP0478790A1 (de) * 1990-03-24 1992-04-08 Nisshin Steel Co., Ltd. Hitzebeständiger ferritischer nichtrostender stahl mit hervorragenden eigenschaften für zähigkeit bei tiefen temperaturen, schweissbarkeit und hitzebeständigkeit
EP1083241A1 (de) * 1999-09-09 2001-03-14 Ugine S.A. Ferritisches Niobium-stabilisiertes 14% Chrom-stahl und dessen Verwendung in Kraftfahrzeugen
EP1170392A1 (de) * 2000-07-04 2002-01-09 Kawasaki Steel Corporation Ferritischer rostfreier Stahl

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014033372A1 (fr) 2012-09-03 2014-03-06 Aperam Stainless France Tôle d'acier inoxydable ferritique, son procédé de fabrication, et son utilisation, notamment dans des lignes d'échappement
US11384405B2 (en) 2012-11-20 2022-07-12 Outokumpu Oyj Ferritic stainless steel
US20170275723A1 (en) * 2014-10-31 2017-09-28 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
US10752973B2 (en) 2014-10-31 2020-08-25 Nippon Steel & Sumikin Stainless Steel Corporation Ferrite-based stainless steel with high resistance to corrosiveness caused by exhaust gas and condensation and high brazing properties and method for manufacturing same
EP3670692A1 (de) 2018-12-21 2020-06-24 Outokumpu Oyj Ferritischer edelstahl
WO2020127275A1 (en) 2018-12-21 2020-06-25 Outokumpu Oyj Ferritic stainless steel
CN114364820A (zh) * 2019-08-05 2022-04-15 株式会社Posco 具有改善的高温蠕变抗力的铁素体不锈钢及其制造方法

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DK1818422T4 (da) 2012-10-29
DE602007000326D1 (de) 2009-01-22
SI1818422T1 (sl) 2009-04-30
EP1818422B1 (de) 2008-12-10
DK1818422T3 (da) 2009-02-23
ATE417134T1 (de) 2008-12-15
ES2317629T5 (es) 2012-12-26
EP1818422B2 (de) 2012-07-18
SI1818422T2 (sl) 2012-11-30
PT1818422E (pt) 2009-01-30
EP1818421A1 (de) 2007-08-15
ES2317629T3 (es) 2009-04-16

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