EP1589122B1 - Coating containing NiAl beta Phases - Google Patents

Coating containing NiAl beta Phases Download PDF

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Publication number
EP1589122B1
EP1589122B1 EP05105696A EP05105696A EP1589122B1 EP 1589122 B1 EP1589122 B1 EP 1589122B1 EP 05105696 A EP05105696 A EP 05105696A EP 05105696 A EP05105696 A EP 05105696A EP 1589122 B1 EP1589122 B1 EP 1589122B1
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Prior art keywords
phase
coating
weight
nial
alloy
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German (de)
French (fr)
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EP1589122A1 (en
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Mohamed Dr. Nazmy
Hans Joachim Dr. Schmutzler
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General Electric Technology GmbH
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Alstom Technology AG
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process

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  • the invention relates to the field of materials technology. It relates to a coating which contains large volume fractions, in the range from 20 to 90% by volume, of NiAl- ⁇ -phase in a ⁇ -matrix.
  • the coating material In order to fully exploit the advantage of a high temperature to increase the efficiency of the turbine and the excellent mechanical properties of the base material (for example, single crystals or directionally solidified microstructures), it is necessary that the coating material not only protects the base material against oxidation and corrosion, but also the mechanical properties of the base material are not affected.
  • a low ductile-brittle transition temperature Ductile Brittle Transition Temperature - DBTT
  • the ⁇ -phase of the NiAl alloys has an ordered cubic B2 crystal structure (CsCl prototype) and consists of two simple interpenetrating cubic cells, where the Al atoms are the cube corners of one sublattice and the Ni atoms are the cube corners of the other Subgitter occupy.
  • the ⁇ phase is coarse and therefore brittle.
  • the object of the invention is to improve the ductility of NiAl coatings which have a high proportion of ⁇ phase in a ⁇ matrix.
  • the ⁇ -phase can have a different composition, for example NiAlCr, NiAlMo.
  • the coating comprising a Ni-base alloy with an Al content which contains a NiAl- ⁇ phase with a proportion of NiAl- ⁇ in the range from 20 to 90% by volume in a ⁇ matrix, has the following chemical composition (in wt .-%) of the coating: 13 Cr, 30 Co, 11.5 Al, 0.5 Ta, 1.2 Si, 0.3 Y, 0.1-8 Fe, and optionally 0.0005-0.9 B and / or 0.0005-1 Zr, and / or 0.1-8 Mo and / or 0.1-8 Ga, wherein the Total content of Fe, Mo and Ga maximum 10%, balance Ni and unavoidable impurities.
  • the advantages of the invention are that the ductility of the coating is substantially improved.
  • micro-alloying with Fe and optionally with Ga and Mo it is achieved that the ⁇ -phase is refined and thus the ductility is increased, without the oxidation resistance being reduced.
  • Exceeding the specified ranges will adversely affect ductility and resistance to oxidation and corrosion.
  • the coating max. 4 wt .-% Fe, Ga, Mo contains.
  • B 0.001-0.5 wt .-%)
  • Zr 0.001-0.5 wt .-%)
  • C 0.5 wt .-%
  • the comparative alloy VL 2 was microalloyed with Zr and Fe.
  • the following alloy data in% by weight was prepared, at which the plastic deformation was also determined in a three-point bending test at 200 ° C.: Table 2: Inventive alloy (modified comparative alloy) According to Tab. 1 Zr Fe L 21 VL 2 0.2 3
  • Fig. 1 In the case of the three-point bending specimen of the comparative alloy VL2 known from the prior art, a fracture occurred with a force of approximately 0.9 kN and a deflection of approximately 1.65 mm.
  • the ductility of the coatings containing NiAl- ⁇ phase can thus be increased.
  • the micro-alloying elements refine the coarse ⁇ -phase.
  • B, Zr and C consolidate the grain boundaries and the ⁇ / ⁇ phase boundaries.
  • the plastic deformation and thus the ductility of the coating alloy could thus be significantly increased by the addition of these additional elements.
  • By ductilizing the NiAl phase crack propagation is slowed down, ie. H. the fracture toughness is increased, which has a positive effect on the stress behavior of the coatings.
  • alloy C and / or B as a ⁇ / ⁇ phase boundary agent. It is the addition of 0.0005 to 0.9, preferably 0.001 to 0.5 wt .-% B, 0.0005 to 1.0, preferably 0.001 to 0.5 wt .-% Zr and 0.0005 to 0.8 wt .-% C provided.
  • phase boundary strengtheners B, C and Zr may be added singly or in combination.

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  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)

Description

Technisches GebietTechnical area

Die Erfindung bezieht sich auf das Gebiet der Werkstofftechnik. Sie betrifft eine Beschichtung, welche grosse Volumenanteile, im Bereich von 20 bis 90 Vol%, an NiAl-β-Phase in einer γ-Matrix enthält.The invention relates to the field of materials technology. It relates to a coating which contains large volume fractions, in the range from 20 to 90% by volume, of NiAl-β-phase in a γ-matrix.

Stand der TechnikState of the art

Es sind eine Vielzahl von Legierungen bekannt, welche zur Beschichtung von z. B. Gasturbinenkomponenten eingesetzt werden. Die Gasturbinenkomponenten, beispielsweise Turbinenschaufeln, sind hohen Temperaturen ausgesetzt und sollen mittels der Beschichtungen vor Oxidation und Korrosion geschützt werden.There are a variety of alloys known which for coating z. B. gas turbine components are used. The gas turbine components, such as turbine blades, are exposed to high temperatures and are to be protected by the coatings from oxidation and corrosion.

Um den Vorteil einer hohen Temperatur zur Steigerung des Wirkungsgrades der Turbine und der hervorragenden mechanischen Eigenschaften des Grundmaterials (beispielsweise Einkristalle oder gerichtet erstarrte Gefüge) voll auszuschöpfen, ist es notwendig, dass das Beschichtungsmaterial das Grundmaterial nicht nur vor Oxidation und Korrosion schützt, sondern auch die mechanischen Eigenschaften des Grundmaterials nicht beeinträchtigt werden. Insbesondere soll eine niedrige Duktil-Spröd-Übergangstemperatur (Duktile Brittle Transition Temperature - DBTT) und damit eine gewisse Duktilität bei niedrigen Temperaturen für das Beschichtungsmaterial erreicht werden.In order to fully exploit the advantage of a high temperature to increase the efficiency of the turbine and the excellent mechanical properties of the base material (for example, single crystals or directionally solidified microstructures), it is necessary that the coating material not only protects the base material against oxidation and corrosion, but also the mechanical properties of the base material are not affected. In particular, a low ductile-brittle transition temperature (Ductile Brittle Transition Temperature - DBTT) should and to achieve some ductility at low temperatures for the coating material.

Dies ist bei den bisher bekannten Beschichtungen leider nicht der Fall.Unfortunately, this is not the case with the previously known coatings.

In US 5,943,138 wird beispielsweise eine Beschichtung beschrieben, welche eine typische Ni-Basis-Superlegierung (Einkristall-Legierung) ist mit Zusatz von Yttrium und Silizium. Diese Elemente verbessern zwar die Kriechfestigkeit und führen ausserdem zu einer niedrigen Duktil-Spröd-Übergangstemperatur, aber die ausserdem enthaltenen Elemente W, Mo und die geringen Anteile an Cr und Co bewirken einen schädlichen Effekt auf den Oxidationswiderstand.In US 5,943,138 For example, a coating is described which is a typical Ni base superalloy (single crystal alloy) with the addition of yttrium and silicon. Although these elements improve creep resistance and also result in a low ductile-brittle transition temperature, the addition of elements W, Mo and the low levels of Cr and Co cause a deleterious effect on the oxidation resistance.

Die in den letzten Jahren entwickelten hochfesten NiAl-Legierungen können zwar in gewisser Weise mit den Ni-Basis-Superlegierungen konkurrieren, jedoch ist ein Nachteil ihre im Vergleich zu den duktilen hochzähen Ni-Basis-Superlegierungen niedrige Zähigkeit und ihre hohe DBT-Temperatur ( R. Dariola: NiAl for Turbine Airfoil Application, Structural Intermetallics, The Minerals, Metals & Materials Society, 1993, S. 495-504 ), was sich in einer niedrigen Duktilität dieser Legierungen bei niedrigen Temperaturen widerspiegelt. Die β-Phase der NiAl-Legierungen weist eine geordnete kubische B2-Kristallstrukur (CsCl Prototyp) auf und besteht aus zwei einfachen sich durchdringenden kubischen Zellen, bei denen die Al-Atome die Würfelecken des einen Subgitters und die Ni-Atome die Würfelecken des anderen Subgitters besetzen. Die β-Phase ist grob und daher spröd.Although the high-strength NiAl alloys developed in recent years can somewhat compete with the Ni-base superalloys, a disadvantage is their low toughness and high DBT temperature (compared to the ductile high-strength Ni-base superalloys). R. Dariola: NiAl for Turbine Airfoil Application, Structural Intermetallics, The Minerals, Metals and Materials Society, 1993, pp. 495-504 ), which is reflected in low ductility of these alloys at low temperatures. The β-phase of the NiAl alloys has an ordered cubic B2 crystal structure (CsCl prototype) and consists of two simple interpenetrating cubic cells, where the Al atoms are the cube corners of one sublattice and the Ni atoms are the cube corners of the other Subgitter occupy. The β phase is coarse and therefore brittle.

Aus US 5,116,438 sind β-Phasen Ni-Aluminide bekannt, die mit Gallium mikrolegiert sind. Diese weisen bei etwa 0,25 Atom% Ga eine signifikante Verbesserung der Duktilität bei Raumtemperatur auf. Ein höherer Ga-Anteil wirkt sich negativ aus.Out US 5,116,438 For example, β-phase Ni aluminides are known which are microalloyed with gallium. At about 0.25 at.% Ga, these exhibit a significant improvement in room temperature ductility. A higher proportion of Ga has a negative effect.

Die Zugabe von geringen Anteilen an Bor, sowie Hf, Zr, Fe und Kombinationen dieser Elemente zu Ni3Al-Legierungen zum Zwecke der Duktilitätsverbesserung ist beispielsweise aus US 4,478,791 und US 4,612,165 bekannt.The addition of small amounts of boron, as well as Hf, Zr, Fe and combinations of these elements to Ni 3 Al alloys for the purpose of ductility improvement is for example US 4,478,791 and US 4,612,165 known.

Aus US 4,045,255 ist eine eutektische gerichtet erstarrte Ni-Basis-Superlegierung bekannt, welche eine γ-Phase und einen erheblichen Anteil an β-Phase aufweist und als Grundmaterial für lastaufnehmende Bauteile eingesetzt wird, weil diese Legierung eine erhöhte Temperaturfestigkeit aufweist. Für Beschichtungen ist sie aber nicht geeignet. In der Druckschrift EP 0 207 874 werden verschiedene Beschichtungsmaterialien mit geringem Anteil (<10%) an der NiAl-β-Phase offenbart. Die US 4,451,431 beschreibt eine korrosionsbeständige und duktile Beschichtung für Turbinenbauteile aus einer Superlegierung, wobei die Beschichtung aus einer Ni-Basis-Legierung besteht mit z. B. folgender Zusammensetzung: 18 % Cr, 12 % Co, 12 % Al, 0.6 % Y, 1.2 % Mo oder 2.8 % Mo, Rest Nickel.Out US 4,045,255 For example, a eutectic directionally-solidified Ni-base superalloy is known which has a γ-phase and a substantial amount of β-phase and is used as a base material for load-bearing components because this alloy has an increased temperature resistance. But it is not suitable for coatings. In the publication EP 0 207 874 various coating materials with low levels (<10%) of the NiAl-β phase are disclosed. The US 4,451,431 describes a corrosion resistant and ductile coating for turbine components of a superalloy, wherein the coating consists of a Ni-base alloy with z. Example, the following composition: 18% Cr, 12% Co, 12% Al, 0.6% Y, 1.2% Mo or 2.8% Mo, balance nickel.

Darstellung der ErfindungPresentation of the invention

Der Erfindung liegt die Aufgabe zugrunde, die Duktilität von NiAl-Beschichtungen, welche einen hohen Anteil an β-Phase in einer γ-Matrix aufweisen, zu verbessern. Die β-Phase kann dabei eine unterschiedliche Zusammensetzung haben, beispielsweise NiAlCr, NiAlMo.The object of the invention is to improve the ductility of NiAl coatings which have a high proportion of β phase in a γ matrix. The β-phase can have a different composition, for example NiAlCr, NiAlMo.

Erfindungsgemäss wird dies dadurch erreicht, dass die Beschichtung aus einer Ni-Basislegierung mit einem Al-Gehalt, welche eine NiAl-β-Phase mit einem Anteil an NiAl-β im Bereich von 20 bis 90 Vol.% in einer γ-Matrix enthält, folgende chemische Zusammensetzung (Angaben in Gew.-%) der Beschichtung aufweist: 13 Cr, 30 Co, 11.5 Al, 0.5 Ta, 1.2 Si, 0.3 Y, 0.1-8 Fe, sowie wahlweise 0.0005-0.9 B und/oder 0.0005-1 Zr, und/oder 0.1-8 Mo und/oder 0.1-8 Ga, wobei der Gesamtanteil Fe, Mo und Ga maximal 10 % beträgt, Rest Ni und unvermeidbare Verunreinigungen.According to the invention, this is achieved by the coating comprising a Ni-base alloy with an Al content which contains a NiAl-β phase with a proportion of NiAl-β in the range from 20 to 90% by volume in a γ matrix, has the following chemical composition (in wt .-%) of the coating: 13 Cr, 30 Co, 11.5 Al, 0.5 Ta, 1.2 Si, 0.3 Y, 0.1-8 Fe, and optionally 0.0005-0.9 B and / or 0.0005-1 Zr, and / or 0.1-8 Mo and / or 0.1-8 Ga, wherein the Total content of Fe, Mo and Ga maximum 10%, balance Ni and unavoidable impurities.

Die Erfindung wird in den Ansprüchen angegeben.The invention is specified in the claims.

Die Vorteile der Erfindung bestehen darin, dass die Duktilität der Beschichtung wesentlich verbessert wird. Durch das Mikrolegieren mit Fe und wahlweise mit Ga und Mo wird erreicht, dass die β-Phase verfeinert und damit die Duktilität erhöht wird, ohne dass der Oxidationswiderstand verringert wird. Werden die angegebenen Bereiche überschritten, so hat das ungünstige Auswirkungen auf die Duktilität und den Widerstand gegen Oxidation und Korrosion.The advantages of the invention are that the ductility of the coating is substantially improved. By micro-alloying with Fe and optionally with Ga and Mo, it is achieved that the β-phase is refined and thus the ductility is increased, without the oxidation resistance being reduced. Exceeding the specified ranges will adversely affect ductility and resistance to oxidation and corrosion.

Es ist besonders zweckmässig, wenn die Beschichtung max. 4 Gew.-% Fe, Ga, Mo enthält.It is particularly useful if the coating max. 4 wt .-% Fe, Ga, Mo contains.

Ferner ist es vorteilhaft, wenn zusätzlich geringe Mengen an B (0.001-0.5 Gew.-%), Zr (0.001-0.5 Gew.-%) und/oder C (0.5 Gew.-%) zugegeben werden. B, Zr und C festigen die Korngrenzen und die β/γ-Phasengrenzen.Furthermore, it is advantageous if in addition small amounts of B (0.001-0.5 wt .-%), Zr (0.001-0.5 wt .-%) and / or C (0.5 wt .-%) are added. B, Zr and C consolidate the grain boundaries and the β / γ phase boundaries.

Kurze Beschreibung der ZeichnungShort description of the drawing

In der Zeichnung ist ein Ausführungsbeispiel der Erfindung dargestellt.In the drawing, an embodiment of the invention is shown.

Es zeigen:

Fig. 1
ein Kraft-Durchbiegungs-Diagramm für die Legierung VL 2 (Stand der Technik) und
Fig. 2
ein Kraft-Durchbiegungs-Diagramm für die Legierung L 21 in einer Ausführungsvariante der Erfindung.
Show it:
Fig. 1
a force-deflection diagram for the alloy VL 2 (prior art) and
Fig. 2
a force-deflection diagram for the alloy L 21 in an embodiment of the invention.

Weg zur Ausführung der ErfindungWay to carry out the invention

Nachfolgend wird die Erfindung anhand eines Ausführungsbeispieles und der Fig. 1 bis 2 näher erläutert.Hereinafter, the invention with reference to an embodiment and the Fig. 1 to 2 explained in more detail.

Der Duktilisierungseffekt der erfindungsgemässen Mikrolegierung von Schichtmaterialien, welche grosse Anteile an NiAl-β-Phase in einer γ-Matrix enthalten, wurde an Proben nachgewiesen, die durch Schmelzen des Materials und anschliessendes Schmieden zu einem Streifen der Grösse 7 x 2 x35 mm3 hergestellt wurden und die etwa 40-70 Vol.% NiAl-β enthalten.The ductilization effect of the inventive microalloying of layered materials containing large amounts of NiAl-β-phase in a γ matrix was demonstrated on samples prepared by melting the material and then forging into a strip of size 7 × 2 × 35 mm 3 and containing about 40-70 vol.% NiAl-β.

An diesen Proben wurden Drei-Punkt-Biegeversuche bei 200 °C durchgeführt. Es wurde der Betrag der plastische Deformation ermittelt, welcher ein Mass für die Duktilität der Beschichtungen darstellt.Three-point bending tests at 200 ° C were performed on these samples. The amount of plastic deformation was determined which represents a measure of the ductility of the coatings.

Als Vergleichsmaterial diente folgende Legierung (Angabe in Gew.-%): Tabelle 1: Vergleichslegierungen Ni Cr Co Al Y Si Ta VL 2 Rest 13 30 11.5 0.3 1.2 0.5 The following alloy was used as reference material (in% by weight): Table 1: Comparative alloys Ni Cr Co al Y Si Ta VL 2 rest 13 30 11.5 0.3 1.2 0.5

Erfindungsgemäss wurde die Vergleichslegierung VL 2 mikrolegiert mit Zr und Fe. Im einzelnen wurde folgende Legierung (Angaben in Gew.-%) hergestellt, an der ebenfalls im Drei-Punkt-Biegeversuch bei 200 °C die plastische Deformation ermittelt wurde: Tabelle 2: Erfindungsgemässe Legierung (modifizierte Vergleichslegierung) Gemäss Tab. 1 Zr Fe L 21 VL 2 0.2 3 According to the invention, the comparative alloy VL 2 was microalloyed with Zr and Fe. In detail, the following alloy (data in% by weight) was prepared, at which the plastic deformation was also determined in a three-point bending test at 200 ° C.: Table 2: Inventive alloy (modified comparative alloy) According to Tab. 1 Zr Fe L 21 VL 2 0.2 3

Gemäss Fig. 1 kam es bei der Drei-Punkt-Biege-Probe der aus dem Stand der Technik bekannten Vergleichslegierung VL2 bei einer Krafteinwirkung von etwa 0.9 kN und einer Durchbiegung von etwa 1.65 mm zum Bruch.According to Fig. 1 In the case of the three-point bending specimen of the comparative alloy VL2 known from the prior art, a fracture occurred with a force of approximately 0.9 kN and a deflection of approximately 1.65 mm.

Wird dagegen die erfindungsgemässe Legierung L 21 (= VL 2 + 0.2 Gew.-% Zr + 3 Gew.-% Fe) im Drei-Punkt-Biegeversuch untersucht (Fig. 2), so kann die plastische Durchbiegung wesentlich erhöht werden. Der Bruch trat erst bei einer Kraft von ca. 1.4 kN ein, wobei die Durchbiegung der Probe ca. 2,5 mm betrug.If, on the other hand, the alloy L 21 (= VL 2 + 0.2% by weight Zr + 3% by weight Fe) according to the invention is investigated in a three-point bending test ( Fig. 2 ), so the plastic deflection can be significantly increased. The break occurred only at a force of about 1.4 kN, the deflection of the sample was about 2.5 mm.

Durch Mikrolegieren mit Fe und Zr kann somit die Duktilität der NiAl-β-Phase enthaltenen Beschichtungen erhöht werden. Die Mikrolegierungselemente verfeinern die grobe β-Phase. B, Zr und C festigen die Korngrenzen und die β/γ-Phasengrenzen.By microalloying with Fe and Zr, the ductility of the coatings containing NiAl-β phase can thus be increased. The micro-alloying elements refine the coarse β-phase. B, Zr and C consolidate the grain boundaries and the β / γ phase boundaries.

Die plastische Deformation und damit die Duktilität der Beschichtungslegierung konnte somit entscheidend durch die Zugabe dieser zusätzlichen Elemente erhöht werden. Durch die Duktilisierung der NiAl-Phase wird die Rissausbreitung verlangsamt, d. h. die Risszähigkeit wird erhöht, was sich positiv auf das Beanspruchungsverhalten der Beschichtungen auswirkt.The plastic deformation and thus the ductility of the coating alloy could thus be significantly increased by the addition of these additional elements. By ductilizing the NiAl phase, crack propagation is slowed down, ie. H. the fracture toughness is increased, which has a positive effect on the stress behavior of the coatings.

Selbstverständlich ist die Erfindung gemäss den Ansprüchen nicht auf das beschriebene Ausführungsbeispiel beschränkt. Die genannten Elemente verfeinern die β-Phase und erhöhen damit die Duktilität, ohne den Oxidationswiderstand zu verringern. Werden die angegebenen Bereiche überschritten, so hat das ungünstige Auswirkungen auf die Duktilität und den Widerstand gegen Oxidation und Korrosion.Of course, the invention is not limited to the described embodiment according to the claims. The elements mentioned refine the β-phase and thus increase the ductility without reducing the oxidation resistance. Exceeding the specified ranges will adversely affect ductility and resistance to oxidation and corrosion.

Ausser der im Ausführungsbeispiel beschriebenen Zugabe von Zr kann als ein β/γ-Phasengrenzenfestiger auch C und/oder B zulegiert werden. Es ist die Zugabe von 0.0005 bis 0.9, vorzugsweise 0.001 bis 0.5 Gew.-% B, 0.0005 bis 1.0, vorzugsweise 0.001 bis 0.5 Gew.-% Zr und 0.0005 bis 0.8 Gew.-% C vorgesehen.Apart from the addition of Zr described in the exemplary embodiment, it is also possible to alloy C and / or B as a β / γ phase boundary agent. It is the addition of 0.0005 to 0.9, preferably 0.001 to 0.5 wt .-% B, 0.0005 to 1.0, preferably 0.001 to 0.5 wt .-% Zr and 0.0005 to 0.8 wt .-% C provided.

Die Phasengrenzenverfestiger B, C und Zr können einzeln oder in Kombination zugegeben werden.The phase boundary strengtheners B, C and Zr may be added singly or in combination.

Claims (8)

  1. Coating comprising an Ni-base alloy with an Al content, which contains an NiAl-β phase with an NiAl-β content in the range from 20 to 90% by volume in a γ matrix, characterized by the following chemical composition (data in % by weight) of the coating: 13 Cr, 30 Co, 11.5 Al, 0.5 Ta, 1.2 Si, 0.3 Y, 0.1-8 Fe, and optionally 0.0005-0.9 B and/or 0.0005-1 Zr, and/or 0.1-8 Mo and/or 0.1-8 Ga, with the total content of Fe, Mo and Ga amounting to at most 10%, remainder Ni and inevitable impurities.
  2. Coating according to Claim 1, characterized by (data in % by weight) max. 4 Fe and/or max. 4 Mo and/or max. 4 Ga.
  3. Coating according to Claim 1, characterized by 0.001-0.5% by weight Zr.
  4. Coating according to Claim 3, characterized by 0.2% by weight Zr.
  5. Coating according to Claim 1, characterized by 0.001-0.5% by weight B.
  6. Coating according to Claim 5, characterized by 0.2% by weight B.
  7. Coating according to Claim 1, characterized by 0.5% by weight C.
  8. Coating according to Claim 1, characterized by (data in % by weight) 13 Cr, 30 Co, 11.5 Al, 0.3 Y, 1.2 Si, 0.5 Ta, 0.2 Zr, 3 Fe, remainder Ni.
EP05105696A 1999-06-08 2000-05-12 Coating containing NiAl beta Phases Expired - Lifetime EP1589122B1 (en)

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DE19926669 1999-06-08
DE19926669A DE19926669A1 (en) 1999-06-08 1999-06-08 Coating containing NiAl beta phase
EP00810410A EP1061150B1 (en) 1999-06-08 2000-05-12 Coating containing NiAl beta Phases

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EP1061150B1 (en) 2005-10-19
CN1280210A (en) 2001-01-17
EP1061150A2 (en) 2000-12-20
EP1589122A1 (en) 2005-10-26
EP1061150A3 (en) 2000-12-27
DE19926669A1 (en) 2000-12-14
DE50015301D1 (en) 2008-09-18
DE50011352D1 (en) 2006-03-02
CN1250771C (en) 2006-04-12

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