EP2283167B1 - Eisen-chrom-aluminium-legierung mit hoher lebensdauer und geringen änderungen im warmwiderstand - Google Patents

Eisen-chrom-aluminium-legierung mit hoher lebensdauer und geringen änderungen im warmwiderstand Download PDF

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EP2283167B1
EP2283167B1 EP09730026.3A EP09730026A EP2283167B1 EP 2283167 B1 EP2283167 B1 EP 2283167B1 EP 09730026 A EP09730026 A EP 09730026A EP 2283167 B1 EP2283167 B1 EP 2283167B1
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alloy according
max
alloy
chromium
foil
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EP2283167A1 (de
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Heike Hattendorf
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VDM Metals International GmbH
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VDM Metals International GmbH
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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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/22—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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium

Definitions

  • the invention relates to a melt-metallurgically produced iron-chromium-aluminum alloy with a long service life and small changes in the heat resistance.
  • Iron-chromium-aluminum-tungsten alloy alloys are used to make electrical heating elements and catalyst supports. These materials form a dense, adherent alumina layer that protects them from destruction at high temperatures (eg up to 1400 ° C). This protection is improved by additions in the range of 0.01 to 0.3% of so-called reactive elements, such as Ca, Ce, La, Y, Zr, Hf, Ti, Nb, W, which inter alia improve the adhesion of the oxide layer and / or reduce the layer growth, as for example in “ Ralf Bürgel, Handbuch der Hochtemperatur-Werkstofftechnik, Vieweg Verlag, Braunschweig 1998 "from page 274 is described.
  • reactive elements such as Ca, Ce, La, Y, Zr, Hf, Ti, Nb, W
  • the aluminum oxide layer protects the metallic material against rapid oxidation. At the same time she is growing herself, albeit very slowly. This growth takes place using consumption of the aluminum content of the material. If no aluminum is present, other oxides (chromium and iron oxides) grow, the metal content of the material is consumed very quickly and the material fails due to destructive corrosion. The time to failure is defined as the lifetime. An increase in the aluminum content prolongs the service life.
  • WO 02/20197 A1 is a ferritic stainless steel alloy, especially for use as Bankleiterelement known.
  • the Alloy is formed by a powder metallurgically produced Fe-Cr-Al alloy containing less than 0.02% C, ⁇ 0.5% Si, ⁇ 0.2% Mn, 10.0 to 40.0% Cr, ⁇ 0 , 6% Ni, ⁇ 0.01% Cu, 2.0 to 10.0% Al, one or more element (s) from the group of reactive elements, such as Sc, Y, La, Ce, Ti, Zr, Hf , V, Nb, Ta, contained between 0.1 and 1.0%, balance iron and unavoidable impurities.
  • reactive elements such as Sc, Y, La, Ce, Ti, Zr, Hf , V, Nb, Ta
  • DE 199 28 842 A1 is an alloy with 16 to 22% Cr, 6 to 10% Al, 0.02 to 1.0% Si, max. 0.5% Mn, 0.02 to 0.1% Hf, 0.02 to 0.1% Y, 0.001 to 0.01% Mg, max. 0.02% Ti, max. 0.03% Zr, max. 0.02% SE, max. 0.1% Sr, max. 0.1% Ca, max. 0.5% Cu, max. 0.1% V, max. 0.1% Ta, max. 0.1% Nb, max. 0.03% C, max. 0.01% N, max. 0.01% B, remainder iron and impurities due to melting for use as a carrier film for catalytic converters, as a heating conductor and as a component in industrial furnace construction and in gas burners.
  • EP 0 290 719 B1 is an alloy with (in mass%) 12 to 30% Cr, 3.5 to 8% Al, 0.008 to 0.10% carbon, max. 0.8% silicon, 0.10 to 0.4% manganese, max. 0.035% phosphorus, max. 0.020% sulfur, 0.1 to 1.0% molybdenum, max.
  • nickel 1% nickel, and the additives 0.010 to 1.0% zirconium, 0.003 to 0.3% titanium and 0.003 to 0.3% nitrogen, calcium plus magnesium 0.005 to 0.05%, and rare earth metals 0.003 to 0.80 %, Niobium of 0.5%, remainder iron described with common accompanying elements, for example as wire for Heating elements for electrically heated furnaces and as a construction material for thermally stressed parts and as a film for the preparation of catalyst supports is used.
  • US-A 4,414,023 is a steel with (in wt.%) 8.0 to 25.0% Cr, 3.0 to 8.0% Al, 0.002 to 0.06% rare earth metals, max. 4.0% Si, 0.06 to 1.0% Mn, 0.035 to 0.07% Ti, 0.035 to 0.07% Zr, including unavoidable impurities.
  • the DE 10 2005 016 722 A1 discloses a high-durability iron-chromium-aluminum alloy with (in mass%) 4 to 8% Al and 16 to 24% Cr and additions of 0.05 to 1% Si, 0.001 to 0.5% Mn, 0 , 02 to 0.2% Y, 0.1 to 0.3% Zr and / or 0.02 to 0.2% Hf, 0.003 to 0.05% C, 0.0002 to 0.05% Mg, 0 , 0002 to 0.05% Ca, max. 0.04% N, max. 0.04% P, max. 0.01% S, max. 0.5% Cu and the usual melting impurities, balance iron.
  • EP 0 516 267 A1 is a ferritic stainless steel, with ⁇ 0.03% C, ⁇ 1% Si, ⁇ 1% Mn, ⁇ 0.04% P, ⁇ 0.03% S, 15 to 25% Cr, ⁇ 0.03 % N, 3 to 6% Al, 0.01 to 4% Mo, 0.01 to 0.15% Y and / or SE, remainder iron.
  • at levels of 0.05 to 1% at least one of the elements Nb, V, Ti may be added.
  • the steel can be used for catalytic converters, exhaust systems and heating elements.
  • the US 5,411,610 discloses a high strength ferritic stainless steel foil containing 10 to 20% Cr, 1 to 10% Al, balance iron.
  • JP 08-269730 is a plate made of an iron-chromium-aluminum alloy containing 9 to 30% chromium and 3 to 8% aluminum, which is coated with a coating based on SE metals.
  • the plate further includes ⁇ 0.05% C, ⁇ 1% Si, ⁇ 1% Mn, ⁇ 0.04% P, ⁇ 0.01% S, and ⁇ 0.05% N.
  • the following elements may be given : 0.01 to 1% Nb, 0.01 to 0.5% Ti, 0.01 to 1% Zr, 0.1 to 1% V, 0.01 to 0.03% Hf and 0.5% SE ,
  • up to 3% Mo, up to 3% Ta and up to 3% Co can be added.
  • an iron-chromium-aluminum foil of the following composition is to be taken: ⁇ 0.02% C, ⁇ 1% Si, ⁇ 1 Mn, 11 to 26 Cr, 6 to 8% Al, ⁇ 0.02% N.
  • ⁇ 0.02% C ⁇ 0.02% C
  • ⁇ 1% Si ⁇ 1 Mn
  • 11 to 26 Cr 6 to 8%
  • ⁇ 0.02% N ⁇ 0.02%
  • SE and / or Y may be provided.
  • the alloy may further contain Ti, Nb, Zr, V and Hf in contents of 0.01 to 0.4%, and Mo, Ta and W in contents of 0.1 to 2%, remainder iron.
  • a heat-resistant stainless steel foil has become known for catalyst carriers or exhaust systems including> 0.06 to 0.15% Ln (La, Ce, Pr and Nd), 4.5 to 6.5% Al, 13 to 25% Cr, ⁇ 0.025% C, ⁇ 0.02% N, 2 to 4% Mo and / or W, balance iron.
  • the JP 04-128343 discloses a stainless steel foil of the following composition:> 0.06 to 0.15% Ln (La, Ce, Pr and Nd), 4.5 to 6.5% Al, 13 to 25% Cr, ⁇ 0.025% C, ⁇ 0 , 02% N, 1 to 2.5% Si and / or 0.01 to 0.1% Mg, balance iron.
  • an iron-chromium-aluminum alloy of the following composition: ⁇ 0.03% C, ⁇ 0.5% Si, ⁇ 1.0% Mn, 10 to 28% Cr, 2 to 6.5% Al, ⁇ 0 , 02% N, 0.01 to 0.05% Zr, 0.01 to 0.2% La and 1 to 5% in total of Mo and / or W, balance iron.
  • WO 01/49441 is a high temperature material, based on a FeCrAl powder metal has become known, in addition to Fe as the remainder, Cr 15 to 25%, Al 3 to 7%, Mo 0 to 5%, Y 0.05 to 0.6%, Zr 0, 01 to 0.3%, Hf 0.05 to 0.5%, Ta 0.05 to 0.5%, Ti 0 to 0.1%, C 0.01 to 0.05%, N 0.01 to 0.06%, O 0.02 to 0.1%, Si 0.1 to 0.7%, Mn 0.05 to 0.5%, P 0 to 0.08%, and S 0 to 0.005%.
  • t B 4.4 ⁇ 10 - 3 ⁇ C 0 - C B ⁇ ⁇ ⁇ d ⁇ k - 1 n ⁇ ⁇ m * 1 n - 1 where ⁇ m * is the critical weight change at which the flakes begin.
  • Heating conductors which consist of thin foils (for example, approximately 20 to 300 ⁇ m thick with a width in the range of one or several millimeters), are characterized by a large surface area to volume ratio. This is advantageous if you want to achieve fast heating and cooling times, as z. B. in the in Be required glass ceramic panels used to make the heating quickly visible and to achieve a rapid heating similar to a gas cooker. At the same time, however, the large surface area to volume ratio is disadvantageous for the service life of the heating conductor.
  • the behavior of the hot resistor must be considered. As a rule, a constant voltage is applied to the heating conductor. If the resistance remains constant over the life of the heating element, the current and the power of this heating element will not change.
  • the temperature of the heating element decreases.
  • the life of the heating conductor and thus also of the heating element is extended.
  • the warm resistance R w decreases over time
  • the power P increases while the voltage at the heating element remains constant.
  • the temperature also increases and thus the service life of the heating conductor or heating element is shortened.
  • the deviations of the heat resistance as a function of time should therefore be kept within a narrow range around zero.
  • the lifetime and the behavior of the heat resistance can be measured, for example, in an accelerated life test.
  • Such a test is z. In Harald Pfeifer, Hans Thomas, Zinderfest alloys, Springer Verlag, Berlin / Göttingen / Heidelberg / 1963 on page 113 described. It is carried out with a switching cycle of 120 s at a constant temperature on helically shaped wire with a diameter of 0.4 mm. As a test temperature temperatures of 1200 ° C and 1050 ° C are proposed. However, since this case is specifically about the behavior of thin films, the test was modified as follows: Film strips of 50 ⁇ m thickness and 6 mm width were clamped between 2 current feedthroughs and heated up to 1050 ° C. by applying a voltage.
  • the heating at 1050 ° C was carried out for 15 s, then the power supply was interrupted for 5 s.
  • the temperature is automatically measured during the life test with a pyrometer and corrected by a program control if necessary to the setpoint temperature.
  • the burning time or burning time is the addition of the times in which the sample is heated.
  • the burning time is the time to failure of the samples, the burning time the current time during an experiment.
  • the burning time or the burning time is given as a relative value in%, based on the burning time of a reference sample, and referred to as relative burning time or relative burning time.
  • the invention has for its object to provide an iron-chromium-aluminum alloy for a specific application, which has a longer life than the iron-chromium-aluminum alloys previously used, with little change in the heat resistance over time at a given application temperature Has.
  • the alloy is to be provided for specific applications in which short and fast cycles are given and at the same time a particularly long life is required.
  • the element Y can be replaced wholly or partially by at least one of the elements Sc and / or La and / or Cerium, with ranges between 0.02 and 0.1% being conceivable in the case of partial substitution.
  • the element Hf can also be replaced as required by at least one of the elements Sc and / or Ti and / or cerium wholly or partially, with partial substitution ranges between 0.01 and 0.1% are conceivable.
  • the alloy with max. 0.005% S are melted.
  • Preferred Fe-Cr-Al alloys are characterized by the following composition: al 4.9 - 5.8% Cr 19 - 22% W 1.5 - 2.5% Si 0.05 - 0.5% Mn 0.005 - 0.5% Y 0.03 - 0.09% Zr 0.02-0.08% Hf 0.02-0.08% C 0.003 - 0.020% mg 0.0001 - 0.05% Ca 0.0001 - 0.03% P 0.002 to 0.030 S Max. 0.01% N Max. 0.03% O max 0.01% Cu Max. 0.5% Ni Max. 0.5% Not a word Max. 0.1% Fe rest
  • the alloy according to the invention is preferably usable for use as a foil for heating elements, in particular for electrically heatable heating elements.
  • the alloy according to the invention is used for films in the thickness range from 0.02 to 0.03 mm, in particular from 20 to 200 ⁇ m, or from 20 to 100 ⁇ m.
  • Another advantage is the use of the alloy as a film heat conductor for use in hobs, especially in glass ceramic cooktops.
  • alloy for use as a carrier film in heatable metallic catalytic converters is also conceivable, as is the use of the alloy as a film in fuel cells.
  • Table 1 shows own industrially molten iron-chromium-aluminum alloys T1 to T6, own laboratory melts L1 to L7, A1 to A5, V1 to V17 and the alloy E1 according to the invention.
  • illustration 1 shows an exemplary graph of the course of the heat resistance according to wire conductor test of wire according to the prior art.
  • Figure 2 shows by way of example for the batch T6 the heat resistance curve according to the heating conductor test for films on an iron-chromium-aluminum alloy (Aluchrom Y) with a composition of Cr 20.7% al 5.2% Si 0.15% Mn 0.22% Y 0.04% Zr 0.04% Ti 0.04%.
  • Aluchrom Y iron-chromium-aluminum alloy
  • Figure 3 shows the internal oxidation (I) of A4 according to Table 1 after 25% relative firing time.
  • the resistance is shown relative to its initial value at the beginning of the measurement. It shows a decrease in the heat resistance. Towards the end of the further course just before burning through the sample, the heat resistance increases sharply (in illustration 1 from approx. 100% relative burning time).
  • a w the maximum deviation of the heat resistance ratio from the initial value 1.0 at the beginning of the experiment (or shortly after the start after formation of the contact resistance) to the beginning of the steep increase.
  • This material (Aluchrom Y) typically has a relative burning time of about 100% and an Aw of about -1 to -3%, as examples T4 to T6 in Table 3 show.
  • T4 to T6 are 3 batches of the iron-chromium-aluminum alloy Aluchrom Y with a composition of about 20% chromium, about 5.2% aluminum, about 0.03% carbon and additions of Y, Zr and Ti of each about 0.05%. They achieve a relative burning time of 91% (T4) to 124% (T6) and an excellent Aw value of -1 to -3%.
  • the batches T1 to T3 of the material Aluchrom YHf with 19 to 22% Cr, 5.5 to 6.5% aluminum, max. 0.5% Mn, max. 0.5% Si, max. 0.05% carbon and additions of max. 0.10% Y, max. 0.07% Zr and max. 0.1% Hf registered.
  • This material can z. B. as a film for catalyst support, but also as a heating conductor, use. If the batches T1 to T3 are subjected to the foil conductor test described above, then the significantly increased service life (burning time) of T1 at 188% and T2 at 152% and T3 at 189% can be seen. T1 has a longer life than T2, which can be explained by the increased aluminum content from 5.6 to 5.9%.
  • T1 shows an A w of -5% and T2 of -8%.
  • an A w of -8% is too high and, experience has shown, leads to a significant increase in the temperature of the component, which compensates for the longer service life of this material, that is, a total of none Advantage brings.
  • Tables 1 and 2 show the charge T3 which, like T1 and T2, is an iron-chromium-aluminum alloy containing 20.1% Cr 6.0% aluminum, 0.12% Mn, 0.33% Si, 0.008% carbon and additions of 0.05% Y, 0.04% Zr and 0.03% Hf.
  • L1 and L2 it contains a very low carbon content of only 0.008%.
  • the goal was to increase the lifetime beyond the T9 level of 189% while achieving an Aw of approximately 1% to -3%.
  • a longer service life than T3 had laboratory batches A1 with 262%, A3 with 212%, A4 with 268% and A5 with 237%, V9 with 224%, V10 with 271% and the subject invention E1 with the highest achieved value of 323%.
  • the alloys T1 to T6, V8, V11 to V13 and the subject invention E1 all have an I less than zero and show no internal oxidation.
  • the alloys A1 to A5, V9, V10 have an I greater than zero and show enhanced internal oxidation.
  • E1 shows an alloy which can be used according to the invention for films in application ranges from 20 ⁇ m to 0.300 mm thickness.
  • the inventive alloy E1 shows in addition to the required significantly higher lifetime of 323%, a very favorable behavior of the heat resistance with a mean Aw of -1.3% and satisfies the condition I ⁇ 0.
  • Tungsten solidifies the alloy. This contributes to the dimensional stability during cyclic deformation and thus to the fact that the Aw is in the range of -3 to 1%. It should therefore not fall below a lower limit of 1%.
  • a minimum content of 0.02% Y is necessary to obtain the oxidation resistance-enhancing effect of Y.
  • the upper limit is set at 0.1% for economic reasons.
  • a minimum content of 0.02% Zr is necessary in order to obtain a good service life and a low A w .
  • the upper limit is set at 0.1% Zr for cost reasons.
  • a minimum content of 0.02% Hf is necessary to obtain the oxidation resistance enhancing effect of Hf.
  • the upper limit is set at 0.1% Hf for economic reasons.
  • the carbon content should be less than 0.030% to obtain a low value of A w . It should be greater than 0.003% to ensure good processability.
  • the nitrogen content should not exceed 0.03% in order to avoid the formation of nitrides, which negatively affect processability. It should be greater than 0.003% to ensure good processability of the alloy.
  • the content of phosphorus should be less than 0.030% since this surfactant affects the oxidation resistance.
  • the P content is preferably ⁇ 0.002%.
  • the content of sulfur should be kept as low as possible, since this surfactant affects the oxidation resistance. It will therefore max. 0.01% S set.
  • the content of oxygen should be kept as low as possible, since otherwise the oxygen-affinity elements such as Y, Zr, Hf, Ti, etc. are mainly bound in oxidic form.
  • the positive effect of the oxygen affinity elements on the oxidation resistance is u. a. impaired by the fact that the oxygen-affinity elements bound in oxidic form are distributed very unevenly in the material and are not available to the required extent throughout the material. It is therefore max. 0.01% O set.
  • Chromium contents between 16 and 24% by mass have no decisive influence on the service life, as in J. Klöwer, Materials and Corrosion 51 (2000), pages 373-385 can be read.
  • a certain chromium content is necessary, because chromium is the formation of the particularly stable and protective ⁇ - Al 2 O 3 layer promotes. Therefore, the lower limit is 16%.
  • Chromium contents> 24% complicate the processability of the alloy.
  • An aluminum content of 4.5% is at least necessary to obtain an alloy with sufficient life.
  • Al-Gehatte> 6.5% no longer increase the lifespan of film heating conductors.
  • a minimum content of 0.001% Mn is required to improve processability.
  • Manganese is limited to 0.5% because this element reduces oxidation resistance.
  • Copper is heated to max. 0.5% limited as this element reduces the oxidation resistance. The same goes for nickel.
  • the contents of magnesium and calcium are set in the spread range of 0.0001 to 0.05 wt .-%, respectively 0.0001 to 0.03 wt .-%.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Resistance Heating (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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EP09730026.3A 2008-04-10 2009-04-02 Eisen-chrom-aluminium-legierung mit hoher lebensdauer und geringen änderungen im warmwiderstand Active EP2283167B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL09730026T PL2283167T3 (pl) 2008-04-10 2009-04-02 Stop żelazowo-chromowo-glinowy o wysokiej trwałości i niewielkich zmianach w rezystancji termicznej
SI200931884T SI2283167T1 (sl) 2008-04-10 2009-04-02 Zlitina železo-krom-aluminj z visoko življenjsko dobo in majhnimi spremembami v toplotni odpornosti

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DE102008018135A DE102008018135B4 (de) 2008-04-10 2008-04-10 Eisen-Chrom-Aluminium-Legierung mit hoher Lebensdauer und geringen Änderungen im Warmwiderstand
PCT/DE2009/000450 WO2009124530A1 (de) 2008-04-10 2009-04-02 Eisen-chrom-aluminium-legierung mit hoher lebensdauer und geringen änderungen im warmwiderstand

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EP2283167A1 EP2283167A1 (de) 2011-02-16
EP2283167B1 true EP2283167B1 (de) 2018-08-29

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US (1) US8580190B2 (es)
EP (1) EP2283167B1 (es)
JP (1) JP5490094B2 (es)
KR (1) KR101282804B1 (es)
CN (1) CN101981218A (es)
BR (1) BRPI0911429B1 (es)
CA (1) CA2719363C (es)
DE (1) DE102008018135B4 (es)
DK (1) DK2283167T3 (es)
ES (1) ES2692866T3 (es)
MX (1) MX2010011129A (es)
PL (1) PL2283167T3 (es)
SI (1) SI2283167T1 (es)
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WO (1) WO2009124530A1 (es)

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DE102007005154B4 (de) * 2007-01-29 2009-04-09 Thyssenkrupp Vdm Gmbh Verwendung einer Eisen-Chrom-Aluminium-Legierung mit hoher Lebensdauer und geringen Änderungen im Warmwiderstand
CN101892434A (zh) * 2010-06-12 2010-11-24 北京首钢吉泰安新材料有限公司 一种超高温电热合金及其制备方法
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PL2283167T3 (pl) 2019-03-29
DE102008018135A1 (de) 2009-10-29
MX2010011129A (es) 2010-12-14
JP2011516731A (ja) 2011-05-26
WO2009124530A1 (de) 2009-10-15
JP5490094B2 (ja) 2014-05-14
CA2719363C (en) 2013-08-06
BRPI0911429A2 (pt) 2015-09-29
KR20100133411A (ko) 2010-12-21
CA2719363A1 (en) 2009-10-15
CN101981218A (zh) 2011-02-23
EP2283167A1 (de) 2011-02-16
ES2692866T3 (es) 2018-12-05
DE102008018135B4 (de) 2011-05-19
TR201815862T4 (tr) 2018-11-21
KR101282804B1 (ko) 2013-07-05
BRPI0911429B1 (pt) 2022-12-13
US20110031235A1 (en) 2011-02-10
DK2283167T3 (en) 2018-11-26
SI2283167T1 (sl) 2018-12-31

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