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EP1740733A2 - Alliage fer-chrome-aluminium - Google Patents

Alliage fer-chrome-aluminium

Info

Publication number
EP1740733A2
EP1740733A2 EP05746889A EP05746889A EP1740733A2 EP 1740733 A2 EP1740733 A2 EP 1740733A2 EP 05746889 A EP05746889 A EP 05746889A EP 05746889 A EP05746889 A EP 05746889A EP 1740733 A2 EP1740733 A2 EP 1740733A2
Authority
EP
European Patent Office
Prior art keywords
max
iron
chromium
aluminum alloy
alloy according
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP05746889A
Other languages
German (de)
English (en)
Other versions
EP1740733B1 (fr
Inventor
Heike Hattendorf
Angelika Kolb-Telieps
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
VDM Metals GmbH
Original Assignee
ThyssenKrupp VDM GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by ThyssenKrupp VDM GmbH filed Critical ThyssenKrupp VDM GmbH
Publication of EP1740733A2 publication Critical patent/EP1740733A2/fr
Application granted granted Critical
Publication of EP1740733B1 publication Critical patent/EP1740733B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • 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
    • C22C38/002—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
    • C22C38/005—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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
    • F01N2370/00—Selection of materials for exhaust purification
    • F01N2370/02—Selection of materials for exhaust purification used in catalytic reactors
    • 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
    • F01N3/00—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust
    • F01N3/08—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous
    • F01N3/10—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous by thermal or catalytic conversion of noxious components of exhaust
    • F01N3/24—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous by thermal or catalytic conversion of noxious components of exhaust characterised by constructional aspects of converting apparatus
    • F01N3/28—Construction of catalytic reactors
    • F01N3/2803—Construction of catalytic reactors characterised by structure, by material or by manufacturing of catalyst support
    • F01N3/2807—Metal other than sintered metal

Definitions

  • the invention relates to an iron-chromium-aluminum alloy produced by melt metallurgy and having a long service life.
  • Alloys of this type are used for the production of electrical heating elements and catalyst supports. These materials form a dense, firmly adhering aluminum oxide layer, which protects them from destruction at high temperatures (e.g. up to 1400 ° C). This protection is improved by adding so-called reactive elements such as Ca, Ce, La, Y, Zr, Hf, Ti, Nb, W, which, among other things. Improve the adhesion of the oxide layer and / or reduce the layer growth, as described, for example, in “Ralf Bürgel, Handbook of High Temperature Material Technology, Vieweg Verlag, Braunschweig 1998” from page 274.
  • the aluminum oxide layer protects the metallic material from rapid oxidation. It grows itself, albeit very slowly. This growth takes place while consuming the aluminum content of the material. If there is no more aluminum, 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 lifespan. Increasing the aluminum content extends the service life.
  • WO 02/20197 has disclosed a ferritic stainless steel alloy, in particular for use as a heating conductor element.
  • the alloy is formed by a FeCrAI alloy produced by powder metallurgy, containing (in mass%) 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, in contents between 0.1 and 1.0%, the rest iron and unavoidable impurities.
  • reactive elements such as Sc, Y, La, Ce, Ti, Zr, Hf, V, Nb, Ta
  • EP-B 0 387 670 an alloy with (in mass%) 20 to 25% Cr, 5 to 8% Al and additions of 0.03 to 0.08% yttrium, 0.004 to 0.008% nitrogen, 0.020 to 0.040 % Carbon, and approximately equal parts 0.035 to 0.07% Ti and 0.035 to 0.07% zirconium, and max. 0.01% phosphorus, max. 0.01% magnesium, max. 0.5% manganese, max. 0.005% sulfur, the rest iron is described, the sum of the contents of Ti and Zr being 1.75 to 3.5% as large as the percentage of the contents of C and N and impurities due to melting. All or part of Ti and Zr can be replaced by hafnium and / or tantalum or vanadium.
  • EP-B 0 290 719 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 from 0.003 to 0.80 %, Niobium of 0.5%, rest of iron described with usual accompanying elements, which are used, 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 production of catalyst supports.
  • tß service life, defined as the time until the occurrence of oxides other than
  • ⁇ m * is the critical weight change at which spalling begins.
  • the temperature cycle defines the combination of heating time, holding time at temperature, cooling time and waiting time before heating up again.
  • Temperature cycles with a short heating up time, a short cooling down time and one Only short holding times at high temperatures are called short and fast temperature cycles in the following. These include e.g. B. temperature cycles with a total duration in the range of several seconds to several minutes, wherein the total duration means the sum of heating time, holding time at temperature, cooling time and waiting time until the beginning of the next heating.
  • Heat conductors which consist of thin foils (e.g. approx. 30 to 100 ⁇ m thick with a width in the range of one or more millimeters), are characterized by a large surface area to volume ratio. This is advantageous if you want to achieve fast heating and cooling times, such as. B. in the heat conductors used in ceramic hobs, to make the heating quickly visible and to achieve rapid heating similar to a gas cooker. At the same time, the large surface to volume ratio is disadvantageous for the life of the heating conductor (see above). In addition, the temperature under the glass must be limited in this application to protect it from damage. This can be achieved by repeatedly switching off the current for a short time. Both result in a load on the heating conductor due to short heating-up times and rapid cooling and only short holding times, which, as described above, further reduces the service life.
  • an increased oxidation rate due to the excessive addition of a reactive element in the mentioned article are an iron-chromium-aluminum alloy with 18.8% Cr, 7% Al and an addition of 0.11% Y or an iron Chromium-aluminum alloy with 20% Cr, 7% Al and additions of 0.04% yttrium, 0.05% Zr and 0.05% Ti.
  • J. Klöwer Materials and Corrosion 51 (2000), pages 373 to 385, 0.04% Zr in an iron-chromium-aluminum alloy with 20% Cr, 7% Al and 0.05% Y already causes an increased oxidation rate.
  • the invention is based on the object of providing an iron-chromium-aluminum alloy which has a longer service life than the iron-chromium-aluminum alloys used hitherto, in particular for components with a large surface area to volume ratio or a small strip thickness.
  • an iron-chromium-aluminum alloy with a long service life produced by melt metallurgy, with (in mass%) 4 to 8% Al, 16 to 24% Cr and additions of 0.05 to 1% Si, 0.001 to 0 , 5% Mn, 0.02 to 0.2% Y and 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-related impurities, the rest iron.
  • the element Hf can furthermore be completely or partially replaced by at least one of the elements Sc and / or Ti and / or V and / or Nb and / or Ta and / or La and / or Cer, ranges being between 0 and 0 in the case of partial substitution , 02 and 0.15 mass% are conceivable.
  • the alloy according to the invention with (in mass%) max. 0.02% N, max. 0.02% P and max. 0.005% S can be melted.
  • the alloy according to the invention can preferably be used for electrical heating elements, in particular with short heating up and cooling down times, short holding times at temperature and short waiting times until a new heating starts.
  • the alloy according to the invention can also be used in heating elements which require high dimensional stability or low sagging.
  • the alloy according to the invention can also be used in heating conductors made of foils with a thickness of 20 to 100 ⁇ m.
  • Table 1 shows laboratory-melted iron-chromium-aluminum alloys L1 to L8 and E1 to E6 and the industrially melted alloys G1 to G3.
  • alloys melted in the laboratory both wire and 50 ⁇ m thick foil were produced from the material cast in blocks using hot and cold forming and suitable intermediate annealing. The film was cut into strips 6 mm wide.
  • a sample with a strip thickness of 50 ⁇ m was taken from the industrial production and, if necessary, cut to the appropriate width of approx. 6 mm.
  • the heating conductor life test is carried out on wires with a diameter of 0.40 mm, from which wire coils with 12 turns, a coil diameter of 4 mm and a coil length of 50 mm.
  • the wire coils are clamped between two power supplies and heated up to 1200 ° C by applying a voltage.
  • the heating to 1200 ° C takes place for 2 minutes, then the power supply is interrupted for 15 seconds.
  • the wire fails because the remaining cross-section melts.
  • An analog life test can be carried out on film strips.
  • film strips with a thickness of 50 ⁇ m and a width of 6 mm are clamped between two current feedthroughs and heated up to 1050 ° C by applying a voltage.
  • the heating to 1050 ° C was carried out for 15 s, then the power supply is interrupted for 5 s.
  • the film fails because the remaining cross section melts.
  • the life time is the total time that the wire or film is at the specified temperature without interruption times.
  • the temperature is measured with an optical pyrometer during the life test and corrected to the target temperature if necessary.
  • the results of the life tests are entered in Table 1.
  • the mean values given in the table are the mean values of at least 3 samples.
  • the filaments are initially clamped horizontally. They sag in the course of the life test. The lower the sagging, the greater the dimensional stability of the material. A high level of dimensional stability is an advantageous technological property, since this means that the parts made from the material show a slight change in shape during use at higher temperatures.
  • the industrially melted alloys G1 and G2 and the laboratory melted alloy L2 show an iron-chromium-aluminum alloy with (in mass%) approx. 20% Cr, approx.
  • the lifespan of 50 ⁇ m thick film at 1050 ° C and a cycle of 15 s "on” and 5 s “off” is between 102 and 124% of the lifespan of the laboratory batch L1.
  • the industrially melted alloy G3 also shows an iron-chromium-aluminum alloy with approx. 20% Cr, approx. 5% Al and additions of 0.06% Y, 0.04% Zr, 0.02% Hf, a carbon content of 0.029%, an Si content of 0.28%, a Mn content of 0.20% and minor contents of P, Mg, Ca, as indicated in Table 1 according to the prior art.
  • the lifespan of 50 ⁇ m thick film at 1050 ° C and a cycle of 15 s “on” and 5 s “off” is 148% of the lifespan of the laboratory batch L1.
  • the alloys according to the prior art thus have values of approximately 100% to approximately 150% of L1 in the service life test on 50 ⁇ m thick film at 1050 ° C. and a cycle of 15 s “on” and 5 s “off”.
  • the variants L3 and L7 with only one Y Addition of 0.06% or 0.05% and a carbon content of 0.002 or 0.031% and an Si content of 0.34 or 0.35% has a service life of only 41% or 51%.
  • the variants L4 and L5 with an addition of 0.04 or 0.05% Y and 0.05 or 0.014% Zr and carbon contents of 0.002 or 0.003% and the Si contents of 0.33 or 0.35 % have a lifespan of 79% and 86%, respectively, which is better than that of L3 and L7, but has not yet reached the lifespan of L2 or L1.
  • the variant L6 with an addition of 0.05% Y and 0.05% Hf and carbon contents of 0.010% and an Si content of 0.36% has a service life of 85%, which is also better than that of L3 and L7
  • Laboratory lot L8 has additions of 0.05% Y, 0.21% Zr and 0.11% Ti and a carbon content of 0.018% and an Si content of only 0.02%. Due to the high content of Zr and Ti according to J. Klöwer, Materials and Corrosion 51 (2000), pages 373 to 385, this is already in the concentration range of the increased oxidation rate in the life test with long cycles of e.g. B. 100 h or 96 h in the oven. Nevertheless, it shows a service life of 105% in the heat conductor life test on wire, which is between L1 and L2.
  • the alloys E1 according to the invention with 0.05% Y, 0.18% Zr, 0.04% Hf, 0.006% C and 0.35% Si and E2 with 0.03% Y, 0.20% Zr, 0.11% Ti instead of hafnium, 0.020% C and 0.61% Si. Both alloys have good lifetimes of 96% for E2 and even 118% for E1 in the heating conductor life test on wire. This results in the following ranking for the laboratory melts for the service life (sorted with decreasing service life):
  • Top group E1, L1, L8, L2, E2, characterized by the addition of Y and Zr and also an addition of Ti or Hf.
  • Average life L5, L6, L4, characterized by the addition of Y and Zr or Y and Hf.
  • Bad service life L7, L3, characterized by the addition of only Y.
  • the alloy L2 corresponds e.g. B. the industrially melted alloys according to the prior art G1 and G2.
  • the alloys L3 and L7, which show a poor service life when tested on wire show a lifetime of 94% and 110% of L1, which is in the range of the lifetime of the prior art alloys.
  • the alloys L1 and L2 in the top group in the test on wire show a service life of 100% and 125% of L1, the alloy L8 shows a service life of a good 140% of L1, which is in the range of the service life of the alloys after State of the art.
  • Group with lifetimes in the range of approximately 100% to 150% of L1. which corresponds to the prior art: G3, L5, L8, L2, G2, L4, L6, G1, L1, L7, L3, characterized by less addition of Y and Zr and / or Hf and / or Ti outside the range of the increased Oxidation rate in the life test with long cycles of e.g. B. 100 h or 96 h in the oven or in the case of L8 due to an insufficient Si content with the addition of Y, Zr and Hf in the area of the increased oxidation rate.
  • the alloys E1, E2 and L8 according to the invention with values between 5 and 7 mm are in the top group compared to the other alloys L1 to L7 after State of the art with values between 17 and 19 mm.
  • the alloys according to the invention therefore still have the advantage of high dimensional stability.
  • a minimum content of 0.02% Y is necessary in order to maintain the oxidation-increasing effect of Y.
  • the upper limit is set at 0.2% by mass for cost reasons.
  • a minimum content of 0.1% Zr is necessary in order to achieve a long service life with short and fast temperature cycles.
  • the upper limit is set at 0.3 mass% Zr.
  • a minimum content of 0.02% Hf is necessary in order to maintain the oxidation-increasing effect of the Hf.
  • the upper limit is set at 0.2% by mass Hf for cost reasons.
  • a minimum content of 0.02% Ti is necessary in order to maintain the oxidation-increasing effect of the Ti.
  • the upper limit is set at 0.2 mass% Ti for cost reasons.
  • the carbon content should be 0.003% to 0.05% to ensure processability.
  • the nitrogen content should be a maximum of 0.04% in order to avoid the formation of nitrides which impair the processability.
  • Chromium contents between 16 and 24% by mass have no decisive influence on the service life as can be read in J. Klöwer, Materials and Corrosion 51 (2000), pages 373 to 385.
  • a certain chromium content is necessary, since chromium promotes the formation of the particularly stable and protective ⁇ - Al 2 0 3 layer. This is guaranteed from approx. 16%. Therefore the lower limit is 16%.
  • the aluminum content of the alloy according to the invention should be 4 to 8%. Approximately 4% aluminum are required according to the “Handbook of High Temperature Materials Technology, Ralf Bürgel, Vieweg Verlag, Braunschweig 1998” on page 272 in Figure 5.13 in order to form a closed ⁇ - AI 2 0 3 layer. Higher AI contents than 8 % affect the workability. According to J. Klöwer, Materials and Corrosion 51 (2000), pages 373 to 385, the addition of silicon increases the service life by improving the adhesion of the top layer. A silicon content of at least 0.05% by mass is therefore necessary. Excessively high Si contents make it difficult to process the alloy. Therefore the upper limit is 1%.
  • Manganese is limited to 0.5% by mass because this element reduces the resistance to oxidation. The same applies to copper.
  • the magnesium and calcium contents are set in the range of 0.0002 to 0.05 mass%.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
  • Resistance Heating (AREA)
  • Soft Magnetic Materials (AREA)
  • Materials For Medical Uses (AREA)
  • Cookers (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)
  • Laminated Bodies (AREA)

Abstract

La présente invention concerne un alliage fer-chrome-aluminium de longévité élevée, comprenant (en % en masse) de 4 à 8 % de Al, de 16 à 24 % de CR, et des additifs en des quantités correspondant à 0,05 à 1 % de Si, 0,001 à 0,5 % de Mn, 0,02 à 0,2 % de Y, 0,1 à 0,3 % de Zr et/ou 0,02 à 0,2 % de Hf, 0,003 à 0,05 % de C, 0,0002 à 0,05 % de Mg, 0,0002 à 0,05 % de Ca, max. 0,04 % de N, max. 0,04 % de P, max. 0,01 % de S, max. 0,5 % de Cu, ainsi que les impuretés liées à la fusion, le reste de l'alliage étant du fer.
EP05746889A 2004-04-28 2005-04-23 Alliage fer-chrome-aluminium Expired - Lifetime EP1740733B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102004020900 2004-04-28
DE102005016722A DE102005016722A1 (de) 2004-04-28 2005-04-11 Eisen-Chrom-Aluminium-Legierung
PCT/DE2005/000748 WO2005106061A2 (fr) 2004-04-28 2005-04-23 Alliage fer-chrome-aluminium

Publications (2)

Publication Number Publication Date
EP1740733A2 true EP1740733A2 (fr) 2007-01-10
EP1740733B1 EP1740733B1 (fr) 2009-02-25

Family

ID=34969368

Family Applications (1)

Application Number Title Priority Date Filing Date
EP05746889A Expired - Lifetime EP1740733B1 (fr) 2004-04-28 2005-04-23 Alliage fer-chrome-aluminium

Country Status (10)

Country Link
US (1) US20070041862A1 (fr)
EP (1) EP1740733B1 (fr)
JP (1) JP2007534845A (fr)
AT (1) ATE423858T1 (fr)
BR (1) BRPI0510484A (fr)
CA (1) CA2564651A1 (fr)
DE (3) DE102005016722A1 (fr)
MX (1) MXPA06010897A (fr)
RU (1) RU2344192C2 (fr)
WO (1) WO2005106061A2 (fr)

Cited By (1)

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US9777357B2 (en) 2012-12-17 2017-10-03 Jfe Steel Corporation Stainless steel foil

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US8043718B2 (en) * 2007-09-14 2011-10-25 Siemens Energy, Inc. Combustion turbine component having rare earth NiCrAl coating and associated methods
US8039117B2 (en) * 2007-09-14 2011-10-18 Siemens Energy, Inc. Combustion turbine component having rare earth NiCoCrAl coating and associated methods
US8043717B2 (en) * 2007-09-14 2011-10-25 Siemens Energy, Inc. Combustion turbine component having rare earth CoNiCrAl coating and associated methods
DE102008018135B4 (de) 2008-04-10 2011-05-19 Thyssenkrupp Vdm Gmbh Eisen-Chrom-Aluminium-Legierung mit hoher Lebensdauer und geringen Änderungen im Warmwiderstand
US20100068405A1 (en) * 2008-09-15 2010-03-18 Shinde Sachin R Method of forming metallic carbide based wear resistant coating on a combustion turbine component
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JP7018315B2 (ja) * 2014-12-11 2022-02-10 サンドビック インテレクチュアル プロパティー アクティエボラーグ フェライト合金
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CN106636963B (zh) * 2016-10-21 2019-02-12 广东电网有限责任公司电力科学研究院 一种合金材料
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US20070041862A1 (en) 2007-02-22
WO2005106061A8 (fr) 2007-05-31
RU2006141845A (ru) 2008-06-10
JP2007534845A (ja) 2007-11-29
DE112005001627A5 (de) 2007-05-24
DE502005006695D1 (de) 2009-04-09
KR20070000503A (ko) 2007-01-02
ATE423858T1 (de) 2009-03-15
EP1740733B1 (fr) 2009-02-25
DE102005016722A1 (de) 2006-02-09
CA2564651A1 (fr) 2005-11-10
BRPI0510484A (pt) 2007-11-06
WO2005106061A2 (fr) 2005-11-10
WO2005106061A3 (fr) 2006-12-07
MXPA06010897A (es) 2006-12-15
WO2005106061B1 (fr) 2007-07-26
RU2344192C2 (ru) 2009-01-20

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