EP1029101B1 - Product, especially a gas turbine component, with a ceramic heat insulating layer, and process for making the same - Google Patents
Product, especially a gas turbine component, with a ceramic heat insulating layer, and process for making the same Download PDFInfo
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- EP1029101B1 EP1029101B1 EP98961067A EP98961067A EP1029101B1 EP 1029101 B1 EP1029101 B1 EP 1029101B1 EP 98961067 A EP98961067 A EP 98961067A EP 98961067 A EP98961067 A EP 98961067A EP 1029101 B1 EP1029101 B1 EP 1029101B1
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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
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
- C23C28/042—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material including a refractory ceramic layer, e.g. refractory metal oxides, ZrO2, rare earth oxides
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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
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
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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
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/10—Oxides, borides, carbides, nitrides or silicides; Mixtures thereof
- C23C4/11—Oxides
Definitions
- the invention relates to a product which a hot, can be exposed to aggressive gas, with a metallic base body, which is a bonding agent layer forming a bonding oxide carries and has a ceramic thermal barrier coating.
- the invention further relates to hot gas components in thermal machines, especially in a gas turbine, to protect against a hot aggressive gas with a Thermal insulation layer are provided.
- US-PS 4,585,481 is a protective layer to protect a metallic substrate made of a superalloy High temperature oxidation and corrosion specified.
- This Protective layer has 5 to 40% chromium, 8 to 35% aluminum, 0.1 up to 2% of an oxygen-active element from group IIIb of the periodic table including the lanthanides and actinides and mixtures thereof, 0.1 to 7% silicon, 0.1 to 3% Hafnium and a radical comprising nickel and / or cobalt (The percentages relate to percent by weight).
- the corresponding protective layers made of MCrAlY alloys are according to US-PS 4,585,481 using a Plasma spraying applied.
- a gas turbine component is described in US Pat. No. 4,321,310, which is a body made of a nickel-based superalloy MAR-M-200 has.
- On the base material is a layer of an MCrAlY alloy, in particular one NiCoCrAlY alloy with 18% chromium, 23% cobalt, 12.5% aluminum, 0.3% yttrium and a remainder made of nickel.
- This layer of the MCrAlY alloy has a polished Surface on which an aluminum oxide layer is applied is.
- a ceramic thermal barrier coating is on this aluminum oxide layer applied, which has a stem-shaped structure having. Due to this columnar microstructure of the thermal insulation layer the crystallite columns are perpendicular to the surface of the basic body. Stabilized as a ceramic material Zirconia specified.
- GB 2 286 977 A1 describes a composition for an inorganic Coating described, the coating is applied to a low alloy steel and one Possesses high temperature resistance.
- the main characteristic of Coating is its corrosion resistance, which is due to integration of iron in the coating is reached.
- the coating exhibits metal oxides before a chemical reaction on, which at temperatures above 1000 ° C in spinels convert.
- a high-temperature protective layer comprising a metallic mixed oxide system
- A is a metal from group IIIb of the periodic table
- B is a metal from main group II (alkaline earth metals) from the periodic table
- M is a metal from one of groups VIb, VIIb and VIIIb from the periodic table.
- the stoichiometric factor X is between 0 and 0.8.
- the coating is used on a temperature-resistant steel or an alloy for use at temperatures above 600 ° C, especially for a component of a gas turbine.
- An austenitic material based on nickel, cobalt or iron is preferably used as the base material for the component of the gas turbine.
- the object of the invention is to provide a product with a metallic Base body and a thermal insulation layer attached to it, especially with a metallic mixed oxide system, specify.
- the invention is based on the knowledge that previously used ceramic thermal insulation layers despite the use of, for example partially stabilized zirconia a Thermal Have expansion coefficients that only about a maximum of 70% the coefficient of thermal expansion of the used Basic body, in particular made of a super alloy. Due to the smaller compared to the metallic base body thermal expansion coefficient result when applied with a hot gas thermal stresses. To at changing thermal load such resulting stresses counteracting this is a stretch-tolerant microstructure the thermal insulation layer is required, e.g. by Setting an appropriate porosity or a stem-shaped Structure of the thermal insulation layer.
- thermal barrier coating known from the prior art made of partially stabilized zirconium oxide with stabilizers how yttrium oxide, cerium oxide and lanthanum oxide tensions occur, that from a thermally induced phase transition (tetragonal in monoclinic and cubic) result. Also at an associated change in volume is a maximum permissible Surface temperature for thermal insulation layers made of zirconium oxide given.
- the object is directed to a product solved in that the ceramic thermal barrier coating is a metallic Mixed oxide system comprising lanthanum aluminate and / or Has calcium zirconate.
- the thermal barrier coating is immediate or indirectly through an adhesive layer to the Basic body connected.
- the connection is preferably made over an oxide layer, which e.g. by oxidation of the base body or the adhesion promoter layer is formed.
- the connection can also or additionally via mechanical clamping, e.g. due to a roughness of the base body or the adhesion promoter layer.
- thermal insulation layers serve to extend the life of hot gas products, in particular components in gas turbines, such as blades and heat shields.
- the thermal barrier coating has a low thermal conductivity, a high melting point and chemical inertness.
- a lanthanum aluminate is also understood to mean a mixed oxide, in particular with a perovskite structure, in which the lanthanum is partially replaced by a substitute element. If necessary, it is possible that the aluminum is at least partially replaced by a further substitute element.
- a chemical structural formula of the type La 1-x M x Al 1-y N y O 3 can be specified for the lanthanum aluminate in question.
- M stands for a substitute element, which preferably comes from the group of lanthanides (rare earths).
- N stands for chrome, for example.
- the substitute element is more preferably gadolinium (Gd).
- the substitute factor X can be up to 0.8 and is preferably in the range of about 0.5. In the range of 0.5, the thermal conductivity of such a lanthanum aluminate has a minimum, so that the thermal insulation layer thus has a particularly low thermal conductivity.
- the substitution factor y is preferably in the range of 0.
- the metallic mixed oxide system has calcium zirconate, preferably in a perovskite structure, the calcium being partially replaced by at least one subtitle element, in particular strontium (Sr) or barium (Ba).
- a chemical structural formula of the type Ca 1-x Sr x Zr 1-y MyO 3 can be specified for such a calcium zirconate.
- the substitute factor X is greater than zero to 1, in particular greater than 0.2, and less than 0.8, and is preferably in the range of 0.5.
- such a calcium zirconate also has a minimum of thermal conductivity, so that the thermal conductivity of the thermal barrier coating is also particularly low. It is also possible to use a mixed oxide system with barium zirconate or strontium zirconate.
- Ba 1-x X x Zr 1-y M y O 3 , Sr 1-x X x Zr 1-y MyO 3 can stand for Ti or Hf.
- the lanthanum aluminates and the calcium, Strontium or barium zirconate mixed crystals as ternary Oxide or pseudo-ternary oxide.
- a ternary oxide here means an oxide in which oxygen (Anions) are connected to two other elements (cations) is.
- a pseudoternary oxide is a substance understood that atoms of more than two different atoms has chemical elements (cations). Here but these atoms (cations) only belong to two different ones Element groups, the atoms of each element in each of the three different element groups in crystallographically equivalent.
- the ternary oxide is preferably based on elements which form materials of the perovskite material group, with appropriate mixed crystal formation and microstructure modification being made possible.
- the two different forms of perovskites due to valence namely perovskite A (A 2+ B 4+ O 3 ) and perovskite B (A 3+ B 3+ O 3 ), can occur.
- Coating materials with a perovskite structure have the general chemical structural formula ABO 3 .
- the ions, which are identified by the placeholder A are smaller than the ions, which are designated by the placeholder B.
- the perovskite structure has four atoms in a unit cell.
- the perovskite structure can be characterized by the fact that the larger B ions and the O ions together form a densest cubic sphere packing in which 1/4 of the octahedral gaps are occupied by A ions.
- the B ions are coordinated by 12 O ions in the form of a cubic octahedron, the O ions are each adjacent to four B ions and two A ions.
- the ternary oxide is preferably lanthanum aluminate (LaAlO 3 ) or calcium zirconate (CaZrO 3 ). These ternary oxides have a low tendency to sinter, a high thermal conductivity and a high coefficient of thermal expansion. In addition, they have high phase stability and a high melting point.
- the thermal expansion coefficient of the ternary oxide is preferably between 7 x 10 -6 / K and 17 x 10 -6 / K.
- the thermal conductivity is preferably between 1.0 and 4.0 W / mK.
- the specified value ranges for expansion coefficient and thermal conductivity apply to bodies made of a ternary non-porous material.
- the thermal conductivity can be further reduced by specifically introducing porosities.
- the melting temperature is significantly more than 1750 ° C.
- Calcium zirconate (CaZrO 3 ) has an expansion coefficient at a temperature between 500 and 1500 ° C of 15 x 10 -6 / K and a thermal conductivity of approx. 1.7 W / mK.
- Lanthanum aluminate (LaAlO 3 ) has a thermal expansion coefficient of approximately 10 x 10 -6 / K at a temperature in the range of approximately 500 to 1500 ° C. The thermal conductivity is around 4.0 W / mK.
- Lanthanum aluminate and calcium zirconate can be synthesized as perovskite by conventional methods such as the so-called mixed oxide method.
- the ternary oxide is essentially phase-pure.
- a full implementation of the lanthanum oxide (La 2 O 3 ) used in the production certainly avoids a two-phase process.
- Calcium zirconate is particularly suitable due to its ease of manufacture, its favorable phases or a variable crystal chemistry, ie in particular an exchange of zirconium by titanium and hafnium. It is also sprayable.
- Lanthanum aluminate has a low tendency to sinter and favorable adhesive conditions, which are caused in particular by the aluminum.
- the mixed oxide system can have a further oxide, the ceramic thermal barrier coating permitting a higher surface temperature and a longer service life than a thermal barrier coating made of zirconium oxide.
- the further oxide can be calcium oxide (CaO) or zirconium oxide (ZrO 2 ) or a mixture thereof, in particular if the ternary oxide is calcium zirconate.
- the ternary oxide can have magnesium oxide (MgO) or strontium oxide (SrO) as additional oxide. It is also possible for the ternary oxide to have yttrium oxide (Y 2 O 3 ), scandium oxide (Sc 2 O 3 ) or a rare earth oxide as well as a mixture of these oxides.
- the lanthanum aluminate can have aluminum oxide together with zirconium oxide and optionally also with yttrium oxide.
- the mixed oxide system with the ternary oxide can additionally have hafnium oxide (HfO 2 ) and / or magnesium oxide (MgO).
- the adhesion promoter layer is preferably an alloy one of the elements of the metallic mixed oxide system, in particular ternary oxides, for example lanthanum, zircon, Aluminum or other. Suitable as an adhesive layer particularly when using a base body from a Nickel-based cobalt-based, or chrome-based superalloy Alloy type MrCrAlY.
- M stands for one of the elements or several elements of the group comprising iron, cobalt or nickel, Cr for chrome and Al for aluminum.
- Y stands for yttrium, cerium, scandium or a group IIIb element the periodic table and the actinides or lanthanides.
- the MCrAlY alloy can contain other elements, e.g. Rhenium.
- the product is preferably a component of a thermal Machine, especially a gas turbine. It can be a turbine blade, a turbine vane or heat shield a combustion chamber.
- a thermal Machine especially a gas turbine. It can be a turbine blade, a turbine vane or heat shield a combustion chamber.
- an inventive Thermal insulation layer is particularly in the case of gas turbine blades with full load operation of the gas turbine even at an operating temperature of 1250 ° C on the surface of the thermal barrier coating a service life greater than that of conventional thermal insulation layers available from zirconium oxide.
- a ternary oxide, in particular as a perovskite undergoes no phase change the operating temperature of the gas temperature, which is above 1250 ° C, in particular can be up to about 1400 ° C.
- the thermal insulation layer is preferably applied by atmospheric plasma spraying, especially with a predeterminable porosity. It is also possible to use the metallic one Mixed oxide system using a suitable vapor deposition process, a suitable PVD process (Physical Vapor Deposition), in particular a reactive PVD method.
- a suitable vapor deposition process Physical Vapor Deposition
- a reactive PVD method When applying the thermal barrier coating using a Vapor deposition process, e.g. an electron beam PVD process, if necessary, a stem structure is also achieved.
- a reactive PVD process there is a reaction in particular a transformation of the individual components a ternary oxide or a pseudoternary oxide, only during the coating process, especially immediately when hitting the product.
- non-reactive Evaporation processes are the ones that have already been pre-reacted Products, especially the ternary oxides with perovskite structure, evaporates and separate again from the steam on the Product from.
- pre-reacted products is special especially when using a plasma spraying process advantageous.
- the gas turbine blade 3 shown in FIG. 1 has a metallic base body 1 made of a nickel-based cobalt base, or chrome-based superalloy.
- a coated airfoil 9 extends between a blade root 10 and a sealing strip 8.
- an adhesion promoter layer 2 is applied to the base body 1.
- the adhesion promoter layer 2 can be an alloy of the MCrAlY type comprising chromium, aluminum, yttrium, lanthanum and / or zircon and a remainder of one or more elements from the group comprising iron, cobalt and nickel.
- a thermal insulation layer 4 with a metallic mixed oxide system is applied to the adhesive layer 2.
- the mixed oxide system here preferably has lanthanum aluminate (LaAlO 3 ), it being possible for the lanthanum to be partially replaced by, for example, gadolinum.
- the mixed oxide system can alternatively have calcium zirconate with partial substitution of calcium by strontium (Ca 1-X Sr X Zr 2 O 3 ).
- Another oxide, such as aluminum oxide or zirconium oxide, is preferably added to the ternary oxide (LaAlO 3 , Ca 1 -X Sr X ZrO 3 ).
- the oxide layer 5 with the bonding oxide is formed between the adhesive layer 2 and the thermal barrier layer 4.
- the bonding oxide is preferably formed by oxidation of the adhesion-promoting layer 2, which leads to a proportion of lanthanum oxide in the presence of lanthanum, to a proportion of zirconium oxide etc. in the case of zirconium.
- the oxide layer 5 provides a good connection of the thermal insulation layer 4 to the metallic base body 1 via the adhesive layer 2.
- a hot aggressive gas 7 flows past an outer surface 6 of the thermal insulation layer 4, which gas is effectively kept away from the metallic base body 1 by the ceramic thermal insulation layer 4 and the adhesive layer 2.
- a hot aggressive gas 7 flows past an outer surface 6 of the thermal insulation layer 4, which gas is effectively kept away from the metallic base body 1 by the ceramic thermal insulation layer 4 and the adhesive layer 2.
- FIG. 3 shows a layer system analogous to FIG. 2, in which an adhesion promoter layer 2 is applied to the base body 1 and the thermal insulation layer 4 is applied thereon.
- the adhesion promoter layer 2 has a surface that is so rough that the thermal insulation layer 4 is bonded to the adhesion promoter layer 2 and thus to the base body 1 essentially without chemical bonding by mechanical clipping.
- Such roughness of a surface 11 of the adhesion promoter layer 2 can already be achieved by applying the adhesion promoter layer 2, for example by vacuum spraying (plasma spraying).
- plasma spraying in particular, products which have already been prereacted (for example La 1-x Gd x AlO 3 or Ca 1-x Sr x ZrO 3 ) are applied to the product.
- the thermal insulation layer 4 can also be attached directly to the metallic base body 1 by a corresponding roughness of the metallic base body 1. It is also possible to apply an additional bonding layer, for example with an aluminum nitride or a chromium nitride, between the adhesion promoter layer 2 and the heat insulation layer 4.
- phase diagram of lanthanum aluminate shown in FIG. 4 and the phase diagram of FIG Calcium zirconate can be seen that with a suitable choice of Additions of oxides have a melting temperature of well above 1750 ° C and a high phase stability without phase transition given at operating temperatures above 1250 ° C is.
Abstract
Description
Die Erfindung betrifft ein Erzeugnis, welches einem heißen, aggressiven Gas aussetzbar ist, mit einem metallischen Grundkörper, der eine ein Anbindungsoxid bildende Haftvermittlerschicht trägt und eine keramische Wärmedämmschicht aufweist. Die Erfindung betrifft weiterhin heißgasbeaufschlagte Bauteile in thermischen Maschinen, insbesondere in einer Gasturbine, die zum Schutz vor einem heißen aggressiven Gas mit einer Wärmedämmschicht versehen sind.The invention relates to a product which a hot, can be exposed to aggressive gas, with a metallic base body, which is a bonding agent layer forming a bonding oxide carries and has a ceramic thermal barrier coating. The invention further relates to hot gas components in thermal machines, especially in a gas turbine, to protect against a hot aggressive gas with a Thermal insulation layer are provided.
In der US-PS 4,585,481 ist eine Schutzschicht zum Schutz eines metallischen Substrats aus einer Superlegierung gegen Hochtemperatur-Oxidation und -Korrosion angegeben. Für die Schutzschichten findet eine MCrAlY-Legierung Anwendung. Diese Schutzschicht weist 5 bis 40% Chrom, 8 bis 35% Aluminium, 0,1 bis 2% eines sauerstoffaktiven Elements aus der Gruppe IIIb des Periodensystems einschließlich der Lanthanide und Actinide sowie Mischungen davon, 0,1 bis 7% Silizium, 0,1 bis 3% Hafnium sowie einen Rest umfassend Nickel und/oder Kobalt angegeben (Die prozentualen Angaben beziehen sich auf Gewichtsprozent). Die entsprechenden Schutzschichten aus MCrAlY-Legierungen werden gemäß der US-PS 4,585,481 mittels eines Plasmaspritzverfahrens aufgebracht.In US-PS 4,585,481 is a protective layer to protect a metallic substrate made of a superalloy High temperature oxidation and corrosion specified. For the Protective layers are used with an MCrAlY alloy. This Protective layer has 5 to 40% chromium, 8 to 35% aluminum, 0.1 up to 2% of an oxygen-active element from group IIIb of the periodic table including the lanthanides and actinides and mixtures thereof, 0.1 to 7% silicon, 0.1 to 3% Hafnium and a radical comprising nickel and / or cobalt (The percentages relate to percent by weight). The corresponding protective layers made of MCrAlY alloys are according to US-PS 4,585,481 using a Plasma spraying applied.
In der US-PS 4,321,310 ist eine Gasturbinenkomponente beschrieben, die einen Grundkörper aus einer Nickel-Basis-Superlegierung MAR-M-200 aufweist. Auf den Grundwerkstoff ist eine Schicht aus einer MCrAlY-Legierung, insbesondere einer NiCoCrAlY-Legierung mit 18% Chrom, 23% Kobalt, 12,5% Aluminium, 0,3% Yttrium und einem Rest aus Nickel aufgebracht. Diese Schicht aus der MCrAlY-Legierung weist eine polierte Oberfläche auf, auf die eine Aluminiumoxidschicht aufgebracht ist. Auf diese Aluminiumoxidschicht ist eine keramische Wärmedämmschicht aufgebracht, welche eine stengelförmige Struktur aufweist. Durch diese kolumnare Mikrostruktur der Wärmedämmschicht stehen die Kristallitsäulen senkrecht zur Oberfläche des Grundkörpers. Als keramischer Werkstoff wird stabilisiertes Zirkonoxid angegeben.A gas turbine component is described in US Pat. No. 4,321,310, which is a body made of a nickel-based superalloy MAR-M-200 has. On the base material is a layer of an MCrAlY alloy, in particular one NiCoCrAlY alloy with 18% chromium, 23% cobalt, 12.5% aluminum, 0.3% yttrium and a remainder made of nickel. This layer of the MCrAlY alloy has a polished Surface on which an aluminum oxide layer is applied is. A ceramic thermal barrier coating is on this aluminum oxide layer applied, which has a stem-shaped structure having. Due to this columnar microstructure of the thermal insulation layer the crystallite columns are perpendicular to the surface of the basic body. Stabilized as a ceramic material Zirconia specified.
In der US-PS 5,236,787 ist angegeben, zwischen dem Grundkörper und einer keramischen Wärmedämmschicht eine Zwischenschicht einzubringen, die aus einer Metall-Keramik-Mischung besteht. Dadurch soll der metallische Anteil dieser Zwischenschicht zum Grundkörper hin zunehmen und zur Wärmedämmschicht abnehmen. Umgekehrt soll entsprechend der keramische Anteil in Nähe des Grundkörpers niedrig, in Nähe der Wärmedämmschicht hoch sein. Als Wärmedämmschicht wird ein durch Yttriumoxid stabilisiertes Zirkonoxid mit Anteilen von Ceroxid angegeben. Durch die Zwischenschicht soll eine Anpassung der unterschiedlichen thermischen Ausdehnungskoeffizienten zwischen metallischem Grundkörper und keramischer Wärmedämmschicht erreicht werden.In US Pat. No. 5,236,787 it is stated between the base body and a ceramic thermal barrier layer an intermediate layer bring in a metal-ceramic mixture consists. As a result, the metallic part of this intermediate layer should Increase towards the base body and towards the thermal insulation layer lose weight. Conversely, the ceramic portion should accordingly low near the main body, near the thermal insulation layer be high. Yttrium oxide is used as the thermal insulation layer Stabilized zirconium oxide with proportions of cerium oxide. The intermediate layer is intended to adapt the different coefficients of thermal expansion between metallic base and ceramic thermal barrier coating can be achieved.
In der US-PS 4,764,341 ist das Anbinden einer dünnen Metallschicht auf einer Keramik für die Herstellung von elektrischen Schaltkreisen, sogenannten gedruckten Schaltungen, beschrieben. Für die Metallschicht werden Nickel, Kobalt, Kupfer sowie Legierungen dieser Metalle verwendet. Zur Anbindung der Metallschicht an ein keramisches Substrat wird auf das keramische Substrat ein Zwischenoxid, wie Aluminiumoxid, Chromoxid, Titanoxid oder Zirkonoxid, aufgebracht, welches bei einer hinreichend hohen Temperatur durch Oxidation ein ternäres Oxid unter Einbeziehung eines Elementes der metallischen Beschichtung bildet.In US-PS 4,764,341 is the binding of a thin metal layer on a ceramic for the manufacture of electrical Circuits, so-called printed circuits, described. Nickel, cobalt, copper are used for the metal layer as well as alloys of these metals. For connection the metal layer on a ceramic substrate is on the ceramic substrate an intermediate oxide, such as aluminum oxide, Chromium oxide, titanium oxide or zirconium oxide, which applied at a sufficiently high temperature by oxidation ternary oxide incorporating an element of the metallic Coating forms.
In der GB 2 286 977 A1 ist eine Zusammensetzung für eine anorganische
Beschichtung beschrieben, wobei die Beschichtung
auf einen niedrig legierten Stahl aufgebracht wird und eine
Hochtemperaturbeständigkeit besitzt. Die Haupteigenschaft der
Beschichtung ist ihre Korrosionsfestigkeit, die durch Einbindung
von Eisen in die Beschichtung erreicht wird. Die Beschichtung
weist vor einer chemischen Reaktion Metalloxide
auf, die sich bei Temperaturen oberhalb von 1000 °C in Spinelle
umwandeln.
Aus der US-PS 4,971,839 ist eine Hochtemperaturschutzschicht umfassend ein metallisches Mischoxidsystem bekannt, welches eine Perowskitstruktur mit der chemischen Strukturformel A1-xBxMO3 aufweist. Hierin ist A ein Metall der Gruppe IIIb des Periodensystems, B ein Metall der Hauptgruppe II (Erdalkalimetalle) des Periodensystems und M ein Metall aus einem der Gruppen VIb, VIIb und VIIIb des Periodensystems. Der Stöchiometriefaktor X liegt hierbei zwischen 0 und 0,8. Die Beschichtung wird hierbei auf einen temperaturbeständigen Stahl oder eine Legierung für den Einsatz bei Temperaturen oberhalb von 600 °C verwendet, insbesondere für ein Bauteil einer Gasturbine. Vorzugsweise wird ein austenitisches Material basierend auf Nickel, Kobalt oder Eisen als Grundwerkstoff für das Bauteil der Gasturbine verwendet.From US Pat. No. 4,971,839, a high-temperature protective layer comprising a metallic mixed oxide system is known, which has a perovskite structure with the chemical structural formula A 1-x B x MO 3 . Here, A is a metal from group IIIb of the periodic table, B is a metal from main group II (alkaline earth metals) from the periodic table and M is a metal from one of groups VIb, VIIb and VIIIb from the periodic table. The stoichiometric factor X is between 0 and 0.8. The coating is used on a temperature-resistant steel or an alloy for use at temperatures above 600 ° C, especially for a component of a gas turbine. An austenitic material based on nickel, cobalt or iron is preferably used as the base material for the component of the gas turbine.
In dem Artikel "On the development of plasma-sprayed thermal barrier coatings" von R. Sivakumar und M.P.Srivastava in: Oxidation of metals, Vol. 20, Nos. 3/4, 1983, sind verschiedene Beschichtungen, die ein Zirkonat aufweisen, angebeben. Diese Beschichtungen sind auf Bauteilen aus Nimonik-75 und alternativ einer Haftschicht der Art CoCrAlY mittels Plasmaspritzens aufgebracht. Es sind Ergebnisse betreffend Calciumzirkonate und Magnesiumzirkonate bei einer zyklischen Temperaturbelastung angegeben.In the article "On the development of plasma-sprayed thermal barrier coatings "by R. Sivakumar and M.P.Srivastava in: Oxidation of metals, vol. 20, Nos. 3/4, 1983, are different Specify coatings that have a zirconate. These coatings are on components made of Nimonik-75 and alternatively an adhesive layer of the type CoCrAlY by means of plasma spraying upset. There are results regarding calcium zirconates and magnesium zirconates with a cyclical temperature load specified.
Aufgabe der Erfindung ist es, ein Erzeugnis mit einem metallischen Grundkörper und einer darauf angebundenen Wärmedämmschicht, insbesondere mit einem metallischen Mischoxidsystem, anzugeben.The object of the invention is to provide a product with a metallic Base body and a thermal insulation layer attached to it, especially with a metallic mixed oxide system, specify.
Die Erfindung geht von der Erkenntnis aus, daß bisher eingesetzte keramische Wärmedämmschichten trotz Einsatz von beispielsweise teilstabilisiertem Zirkonoxid einen thermischen Ausdehnungskoeffizienten aufweisen, der nur etwa maximal 70% der thermischen Ausdehnungskoeffizienten der eingesetzten Grundkörper, insbesondere aus einer Superlegierung, besitzt. Durch den gegenüber dem metallischen Grundkörper geringeren thermischen Ausdehnungskoeffizient resultieren bei Beaufschlagung mit einem heißen Gas thermische Spannungen. Um bei wechselnder thermischer Belastung solche resultierenden Spannungen entgegenzuwirken, ist eine dehnungstolerante Mikrostruktur der Wärmedämmschicht erforderlich, z.B. durch Einstellung einer entsprechenden Porosität oder einer stengelförmigen Struktur der Wärmedämmschicht. Zusätzlich können bei einer aus dem Stand der Technik bekannten Wärmedämmschicht aus teilstabilisiertem Zirkonoxid mit Stabilisatoren wie Yttriumoxid, Ceroxid und Lanthanoxid Spannungen auftreten, die aus einer thermisch bedingten Phasenumwandlung (tetragonal in monoklin und kubisch) resultieren. Auch bei einer damit verbundenen Volumenänderung ist eine maximale zulässige Oberflächentemperatur für Wärmedämmschichten aus Zirkonoxid gegeben.The invention is based on the knowledge that previously used ceramic thermal insulation layers despite the use of, for example partially stabilized zirconia a thermal Have expansion coefficients that only about a maximum of 70% the coefficient of thermal expansion of the used Basic body, in particular made of a super alloy. Due to the smaller compared to the metallic base body thermal expansion coefficient result when applied with a hot gas thermal stresses. To at changing thermal load such resulting stresses counteracting this is a stretch-tolerant microstructure the thermal insulation layer is required, e.g. by Setting an appropriate porosity or a stem-shaped Structure of the thermal insulation layer. In addition, you can in a thermal barrier coating known from the prior art made of partially stabilized zirconium oxide with stabilizers how yttrium oxide, cerium oxide and lanthanum oxide tensions occur, that from a thermally induced phase transition (tetragonal in monoclinic and cubic) result. Also at an associated change in volume is a maximum permissible Surface temperature for thermal insulation layers made of zirconium oxide given.
Erfindungsgemäß wird die auf ein Erzeugnis gerichtete Aufgabe dadurch gelöst, daß die keramische Wärmedämmschicht ein metallisches Mischoxidsystem umfassend Lanthanaluminat und/oder Kalziumzirkonat aufweist. Die Wärmedämmschicht ist unmittelbar oder mittelbar durch eine Haftvermittlerschicht an den Grundkörper angebunden. Die Anbindung erfolgt vorzugsweise über eine Oxidschicht, welche z.B. durch Oxidation des Grundkörpers oder der Haftvermittlerschicht gebildet ist. Die Anbindung kann auch oder zusätzlich über eine mechanische Verklammerung, z.B. durch eine Rauhigkeit des Grundkörpers oder der Haftvermittlerschicht, erfolgen.According to the invention, the object is directed to a product solved in that the ceramic thermal barrier coating is a metallic Mixed oxide system comprising lanthanum aluminate and / or Has calcium zirconate. The thermal barrier coating is immediate or indirectly through an adhesive layer to the Basic body connected. The connection is preferably made over an oxide layer, which e.g. by oxidation of the base body or the adhesion promoter layer is formed. The connection can also or additionally via mechanical clamping, e.g. due to a roughness of the base body or the adhesion promoter layer.
Diese Wärmedämmschichten dienen der Verlängerung der Lebensdauer von heißgasbeaufschlagten Erzeugnissen, insbesondere Bauteilen in Gasturbinen, wie Schaufeln und Hitzeschilde. Die Wärmedämmschicht besitzt eine geringe Wärmeleitfähigkeit, einen hohen Schmelzpunkt sowie eine chemische Inertheit. Unter einem Lanthanaluminat wird hierbei auch ein Mischoxid, insbesondere mit Perowskitstruktur, verstanden, bei dem das Lanthan teilweise durch ein Substitutelement ersetzt ist. Gegebenenfalls ist es hierbei möglich, daß das Aluminium durch ein weiteres Substitutelement zumindest teilweise ersetzt ist. Für das betreffende Lanthanaluminat läßt sich eine chemische Strukturformel der Art La1-xMxAl1-yNyO3 angeben. M steht hierbei für ein Substituts-Element, welches vorzugsweise aus der Gruppe der Lanthaniden (seltene Erden) stammt. N steht z.B. für Chrom. Weiter bevorzugt ist das Substitutelement hierbei Gadolinium (Gd). Der Substitutsfaktor X kann hierbei bis zu 0,8 betragen und liegt vorzugsweise im Bereich von etwa 0,5. Im Bereich von 0,5 weist die Wärmeleitfähigkeit eines solchen Lanthanaluminats ein Minimum auf, so daß die Wärmedämmschicht hiermit eine besonders geringe Wärmeleitfähigkeit besitzt. Der Substitutsfaktor y liegt vorzugsweise im Bereich von 0.These thermal insulation layers serve to extend the life of hot gas products, in particular components in gas turbines, such as blades and heat shields. The thermal barrier coating has a low thermal conductivity, a high melting point and chemical inertness. A lanthanum aluminate is also understood to mean a mixed oxide, in particular with a perovskite structure, in which the lanthanum is partially replaced by a substitute element. If necessary, it is possible that the aluminum is at least partially replaced by a further substitute element. A chemical structural formula of the type La 1-x M x Al 1-y N y O 3 can be specified for the lanthanum aluminate in question. M stands for a substitute element, which preferably comes from the group of lanthanides (rare earths). N stands for chrome, for example. The substitute element is more preferably gadolinium (Gd). The substitute factor X can be up to 0.8 and is preferably in the range of about 0.5. In the range of 0.5, the thermal conductivity of such a lanthanum aluminate has a minimum, so that the thermal insulation layer thus has a particularly low thermal conductivity. The substitution factor y is preferably in the range of 0.
Zusätzlich oder alternativ weist das metallische Mischoxidsystem Kalziumzirkonat, vorzugsweise in einer Perowskitstruktur, auf, wobei das Kalzium teilweise durch zumindest ein Subtitutelement, insbesondere Strontium (Sr) oder Barium (Ba) ersetzt ist. Für ein solches Kalziumzirkonat läßt sich ein chemische Strukturformel der Art Ca1-xSrxZr1-yMyO3 angeben. Der Substitutsfaktor X ist hierbei größer als Null bis 1, insbesondere größer als 0,2, und kleiner als 0,8, und liegt vorzugsweise im Bereich von 0,5. In diesem Bereich hat ein solches Kalziumzirkonat ebenfalls ein Minimum der Wärmeleitfahigkeit, so daß hierdurch auch die Wärmeleitfähigkeit der Wärmedämmschicht besonders gering ist. Es ist ebenfalls möglich, ein Mischoxidsystem mit Bariumzirkonat oder Strontiumzirkonat zu verwenden. (Ba1-xXxZr1-yMyO3, Sr1-xXxZr1-yMyO3), mit X; Ca, Sr bzw. Ba. M kann hierbei für Ti oder Hf stehen. Additionally or alternatively, the metallic mixed oxide system has calcium zirconate, preferably in a perovskite structure, the calcium being partially replaced by at least one subtitle element, in particular strontium (Sr) or barium (Ba). A chemical structural formula of the type Ca 1-x Sr x Zr 1-y MyO 3 can be specified for such a calcium zirconate. The substitute factor X is greater than zero to 1, in particular greater than 0.2, and less than 0.8, and is preferably in the range of 0.5. In this area, such a calcium zirconate also has a minimum of thermal conductivity, so that the thermal conductivity of the thermal barrier coating is also particularly low. It is also possible to use a mixed oxide system with barium zirconate or strontium zirconate. (Ba 1-x X x Zr 1-y M y O 3 , Sr 1-x X x Zr 1-y MyO 3 ), with X; Ca, Sr and Ba, respectively. M can stand for Ti or Hf.
Im folgenden werden die Lanthanaluminate sowie die Kalzium-, Strontium oder Bariumzirkonat-Mischkristalle als ternäres Oxid bzw. pseudoternäres Oxid bezeichnet.In the following, the lanthanum aluminates and the calcium, Strontium or barium zirconate mixed crystals as ternary Oxide or pseudo-ternary oxide.
Ein ternäres Oxid bezeichnet hierbei ein Oxid, bei dem Sauerstoff (Anionen) mit zwei weiteren Elementen (Kationen) verbunden ist. Unter einem pseudoternären Oxid wird eine Substanz verstanden, die an sich Atome von mehr als zwei verschiedenen chemischen Elementen (Kationen) aufweist. Hierbei gehören diese Atome (Kationen) aber nur zu zwei unterschiedlichen Elementgruppen, wobei die Atome der einzelnen Elemente in jeweils einer der drei unterschiedlichen Elementgruppen in kristallographischer Hinsicht gleich wirkend sind.A ternary oxide here means an oxide in which oxygen (Anions) are connected to two other elements (cations) is. Under a pseudoternary oxide is a substance understood that atoms of more than two different atoms has chemical elements (cations). Here but these atoms (cations) only belong to two different ones Element groups, the atoms of each element in each of the three different element groups in crystallographically equivalent.
Vorzugsweise basiert das ternäre Oxid auf Elementen, die Materialien der Stoffgruppe Perowskite bilden, wobei eine entsprechende Mischkristallbildung und Mikrostrukturmodifikation ermöglicht ist. Hierbei können die beiden unterschiedlichen valenzbedingten Formen der Perowskite, nämlich Perowskit A (A2+B4+O3) und Perowskit B (A3+B3+O3), auftreten. Beschichtungswerkstoffe mit einer Perowskitstruktur haben die allgemeine chemische Strukturformel ABO3. Hierbei sind die Ionen, welche durch den Platzhalter A gekennzeichnet sind, gegenüber den Ionen, die durch den Platzhalter B bezeichnet sind, kleiner. Die Perowskitstruktur weist vier Atome in einer Elementarzelle auf. Die Perowskitstruktur läßt sich dadurch charakterisieren, daß die größeren B-Ionen und die O-Ionen zusammen eine kubisch dichteste Kugelpackung bilden, in der 1/4 der oktaedrischen Lücken mit A-Ionen besetzt sind. Die B-Ionen werden von jeweils 12 O-Ionen in Form eines Kubo-Oktaeders koordiniert, den O-Ionen sind jeweils vier B-Ionen und zwei A-Ionen benachbart.The ternary oxide is preferably based on elements which form materials of the perovskite material group, with appropriate mixed crystal formation and microstructure modification being made possible. Here, the two different forms of perovskites due to valence, namely perovskite A (A 2+ B 4+ O 3 ) and perovskite B (A 3+ B 3+ O 3 ), can occur. Coating materials with a perovskite structure have the general chemical structural formula ABO 3 . Here, the ions, which are identified by the placeholder A, are smaller than the ions, which are designated by the placeholder B. The perovskite structure has four atoms in a unit cell. The perovskite structure can be characterized by the fact that the larger B ions and the O ions together form a densest cubic sphere packing in which 1/4 of the octahedral gaps are occupied by A ions. The B ions are coordinated by 12 O ions in the form of a cubic octahedron, the O ions are each adjacent to four B ions and two A ions.
Das ternäre Oxid ist vorzugsweise Lanthanaluminat (LaAlO3) oder Kalziumzirkonat (CaZrO3). Diese ternären Oxide haben eine geringe Sinterneigung, eine hohe Wärmeleitfähigkeit und einen hohen thermischen Ausdehnungskoeffizienten. Darüber hinaus verfügen sie über eine hohe Phasenstabilität und einen hohen Schmelzpunkt.The ternary oxide is preferably lanthanum aluminate (LaAlO 3 ) or calcium zirconate (CaZrO 3 ). These ternary oxides have a low tendency to sinter, a high thermal conductivity and a high coefficient of thermal expansion. In addition, they have high phase stability and a high melting point.
Der thermische Ausdehnungskoeffizient des ternären Oxides liegt vorzugsweise zwischen 7 x 10-6/K und 17 x 10-6/K. Die Wärmeleitfähigkeit liegt vorzugsweise zwischen 1,0 und 4,0 W/mK. Die angegebenen Wertebereiche für Ausdehnungskoeffizient und Wärmeleitfähigkeit gelten für Körper 2us einem ternaren porenfreien Werkstoff. Durch gezielt eingebrachte Porositäten kann die Wärmeleitfähigkeit weiter verringert werden. Die Schmelztemperatur beträgt hierbei deutlich mehr als 1750 °C.The thermal expansion coefficient of the ternary oxide is preferably between 7 x 10 -6 / K and 17 x 10 -6 / K. The thermal conductivity is preferably between 1.0 and 4.0 W / mK. The specified value ranges for expansion coefficient and thermal conductivity apply to bodies made of a ternary non-porous material. The thermal conductivity can be further reduced by specifically introducing porosities. The melting temperature is significantly more than 1750 ° C.
Kalziumzirkonat (CaZrO3) hat einen Ausdehnungskoeffizienten bei einer Temperatur zwischen 500 und 1500 °C von 15 x 10-6/K und eine Wärmeleitfähigkeit von ca. 1,7 W/mK. Lanthanaluminat (LaAlO3) hat einen thermischen Ausdehnungskoeffizienten von etwa 10 x 10-6/K bei einer Temperatur im Bereich von ca. 500 bis 1500 °C. Die Wärmeleitfähigkeit liegt bei etwa 4,0 W/mK. Lanthanaluminat sowie Kalziumzirkonat lassen sich als Perowskit durch konventionelle Methoden, wie beispielsweise die sogenannte Mixed-Oxide-Methode synthetisieren. Bereits nach etwa 3 Stunden Reaktionsglühen (1400 °C bei CaZrO3; 1700 °C bei LaAlO3) an Luft liegt das ternäre Oxid im wesentlichen phasenrein vor. Durch eine vollständige Umsetzung des bei der Herstellung eingesetzten Lanthanoxides (La2O3) wird sicher eine Zweiphasigkeit vermieden. Kalziumzirkonat eignet sich insbesondere durch seine leichte Herstellbarkeit, seine gunstigen Phasen bzw. eine variable Kristallchemie, d.h. insbesondere einen Austausch von Zirkon durch Titan und Hafnium aus. Darüber hinaus ist es spritzfähig. Lanthanaluminat hat eine geringe Sinterneigung sowie gunstige Haftbedingungen, die insbesondere durch das Aluminium hervorgerufen werden.Calcium zirconate (CaZrO 3 ) has an expansion coefficient at a temperature between 500 and 1500 ° C of 15 x 10 -6 / K and a thermal conductivity of approx. 1.7 W / mK. Lanthanum aluminate (LaAlO 3 ) has a thermal expansion coefficient of approximately 10 x 10 -6 / K at a temperature in the range of approximately 500 to 1500 ° C. The thermal conductivity is around 4.0 W / mK. Lanthanum aluminate and calcium zirconate can be synthesized as perovskite by conventional methods such as the so-called mixed oxide method. After about 3 hours of reaction annealing (1400 ° C with CaZrO 3 ; 1700 ° C with LaAlO 3 ) in air, the ternary oxide is essentially phase-pure. A full implementation of the lanthanum oxide (La 2 O 3 ) used in the production certainly avoids a two-phase process. Calcium zirconate is particularly suitable due to its ease of manufacture, its favorable phases or a variable crystal chemistry, ie in particular an exchange of zirconium by titanium and hafnium. It is also sprayable. Lanthanum aluminate has a low tendency to sinter and favorable adhesive conditions, which are caused in particular by the aluminum.
Das Mischoxidsystem kann ein weiteres Oxid aufweisen, wobei die keramische Wärmedämmschicht, die eine höhere Oberflächentemperatur und eine höhere Einsatzdauer als eine Wärmedämmschicht aus Zirkonoxid zuläßt. Das weitere Oxid kann Calciumoxid (CaO) oder Zirkonoxid (ZrO2) oder eine Mischung daraus sein, insbesondere dann, wenn das ternäre Oxid Kalziumzirkonat ist.The mixed oxide system can have a further oxide, the ceramic thermal barrier coating permitting a higher surface temperature and a longer service life than a thermal barrier coating made of zirconium oxide. The further oxide can be calcium oxide (CaO) or zirconium oxide (ZrO 2 ) or a mixture thereof, in particular if the ternary oxide is calcium zirconate.
Weiterhin kann das ternäre Oxid als zusätzliches Oxid Magnesiumoxid (MgO) oder Strontiumoxid (SrO) aufweisen. Es ist ebenfalls möglich, daß das ternäre Oxid als Oxid Yttriumoxid (Y2O3), Scandiumoxid (Sc2O3) oder ein Oxid der Seltenen Erden sowie eine Mischung aus diesen Oxiden aufweist.Furthermore, the ternary oxide can have magnesium oxide (MgO) or strontium oxide (SrO) as additional oxide. It is also possible for the ternary oxide to have yttrium oxide (Y 2 O 3 ), scandium oxide (Sc 2 O 3 ) or a rare earth oxide as well as a mixture of these oxides.
Das Lanthanaluminat kann als weiteres Oxid Aluminiumoxid zusammen mit Zirkonoxid und gegebenenfalls weiterhin mit Yttriumoxid aufweisen. Alternativ kann das Mischoxidsystem mit dem ternären Oxid zusätzlich Hafniumoxid (HfO2) und/oder Magnesiumoxid (MgO) aufweisen.As a further oxide, the lanthanum aluminate can have aluminum oxide together with zirconium oxide and optionally also with yttrium oxide. Alternatively, the mixed oxide system with the ternary oxide can additionally have hafnium oxide (HfO 2 ) and / or magnesium oxide (MgO).
Die Haftvermittlerschicht ist vorzugsweise eine Legierung umfassend eines der Elemente des metallischen Mischoxidsystems, insbesondere ternären Oxids, beispielsweise Lanthan, Zirkon, Aluminium oder andere. Als Haftvermittlungsschicht eignet sich insbesondere bei Verwendung eines Grundkörpers aus einer Nickelbasis-Kobaltbasis, oder Chrombasis-Superlegierung eine Legierung der Art MrCrAlY. Hierbei steht M für eines der Elemente oder mehrere Elemente der Gruppe umfassend Eisen, Kobalt oder Nickel, Cr für Chrom und Al für Aluminium. Y steht für Yttrium, Cer, Scandium oder ein Element der Gruppe IIIb des Periodensystems sowie der Aktiniden oder Lanthaniden. Die MCrAlY-Legierung kann weitere Elemente, z.B. Rhenium, aufweisen.The adhesion promoter layer is preferably an alloy one of the elements of the metallic mixed oxide system, in particular ternary oxides, for example lanthanum, zircon, Aluminum or other. Suitable as an adhesive layer particularly when using a base body from a Nickel-based cobalt-based, or chrome-based superalloy Alloy type MrCrAlY. M stands for one of the elements or several elements of the group comprising iron, cobalt or nickel, Cr for chrome and Al for aluminum. Y stands for yttrium, cerium, scandium or a group IIIb element the periodic table and the actinides or lanthanides. The MCrAlY alloy can contain other elements, e.g. Rhenium.
Das Erzeugnis ist vorzugsweise ein Bauteil einer thermischen Maschine, insbesondere einer Gasturbine. Es kann eine Turbinenlaufschaufel, eine Turbinenleitschaufel oder ein Hitzeschild einer Brennkammer sein. Mit einer erfindungsgemäßen Wärmedämmschicht ist insbesondere bei Gasturbinenschaufeln bei Vollastbetrieb der Gasturbine auch bei einer Betriebstemperatur von 1250 °C an der Oberfläche der Wärmedämmschicht eine Standzeit größer als die konventioneller Wärmedämmschichten aus Zirkonoxid erreichbar. Ein ternäres Oxid, insbesondere als Perowskit, erfährt keine Phasenumwandlung bei der Betriebstemperatur der Gastemperatur, die über 1250 °C, insbesondere bis etwa 1400 °C betragen kann.The product is preferably a component of a thermal Machine, especially a gas turbine. It can be a turbine blade, a turbine vane or heat shield a combustion chamber. With an inventive Thermal insulation layer is particularly in the case of gas turbine blades with full load operation of the gas turbine even at an operating temperature of 1250 ° C on the surface of the thermal barrier coating a service life greater than that of conventional thermal insulation layers available from zirconium oxide. A ternary oxide, in particular as a perovskite, undergoes no phase change the operating temperature of the gas temperature, which is above 1250 ° C, in particular can be up to about 1400 ° C.
Vorzugsweise erfolgt die Aufbringung der Wärmedämmschicht durch atmosphärisches Plasmaspritzen, insbesondere mit einer vorgebbaren Porosität. Es ist ebenfalls möglich, das metallische Mischoxidsystem mittels eines geeigneten Aufdampfverfahrens, eines geeigneten PVD-Verfahrens (Physical Vapour Deposition), insbesondere eines reaktiven PVD-Verfahrens, aufzubringen. Bei Aufbringen der Wärmedämmschicht mittels eines Aufdampfverfahrens, z.B. eines Elektronenstrahl-PVD-Verfahrens, wird, falls erforderlich, auch eine Stengelstruktur erreicht. Bei einem reaktiven PVD-Verfahren erfolgt eine Reaktion, insbesondere eine Umwandlung, der einzelnen Bestandteile eines ternären Oxides oder eines pseudoternären Oxides, erst während des Beschichtungsprozesses, insbesondere unmittelbar beim Auftreffen auf das Erzeugnis. Bei einem nicht reaktiven Aufdampfverfahren werden die bereits vorreagierten Produkte, insbesondere die ternären Oxide mit Perowskitstruktur, verdampft und scheiden sich wieder aus dem Dampf auf dem Erzeugnis ab. Die Verwendung vorreagierter Produkte ist insbesondere bei Anwendung eines Plasmaspritz-Verfahrens besonders vorteilhaft.The thermal insulation layer is preferably applied by atmospheric plasma spraying, especially with a predeterminable porosity. It is also possible to use the metallic one Mixed oxide system using a suitable vapor deposition process, a suitable PVD process (Physical Vapor Deposition), in particular a reactive PVD method. When applying the thermal barrier coating using a Vapor deposition process, e.g. an electron beam PVD process, if necessary, a stem structure is also achieved. In a reactive PVD process, there is a reaction in particular a transformation of the individual components a ternary oxide or a pseudoternary oxide, only during the coating process, especially immediately when hitting the product. With a non-reactive Evaporation processes are the ones that have already been pre-reacted Products, especially the ternary oxides with perovskite structure, evaporates and separate again from the steam on the Product from. The use of pre-reacted products is special especially when using a plasma spraying process advantageous.
Anhand der in der Zeichnung dargestellten Ausführungsbeispiele wird das Erzeugnis mit der Wärmedämmschicht näher erläutert. Es zeigen:
- FIG 1
- Eine perspektivische Darstellung einer Gasturbinenlaufschaufel,
- FIG 2, 3
- jeweils einen Ausschnitt eines Querschnitts durch
die
Turbinenschaufel analog Figur 1, - FIG 4
- eine Darstellung des Phasendiagramms von Lanthanaluminat bei Zusatz von Lanthanoxid und Aluminiumoxid, und
- FIG 5
- das Phasendiagramm für Kalziumzirkonat bei Zusatz von Zirkonoxid und Kalziumoxid.
- FIG. 1
- A perspective view of a gas turbine blade,
- FIG 2, 3
- a section of a cross section through the turbine blade analogous to FIG. 1,
- FIG 4
- a representation of the phase diagram of lanthanum aluminate with the addition of lanthanum oxide and aluminum oxide, and
- FIG 5
- the phase diagram for calcium zirconate with the addition of zirconium oxide and calcium oxide.
Die in Figur 1 dargestellte Gasturbinenlaufschaufel 3 weist
einen metallischen Grundkörper 1 aus einer Nickelbasis-Kobaltbasis,
oder Chrombasis-Superlegierung auf. Zwischen einem
Schaufelfuß 10 und einem Dichtband 8 erstreckt sich ein beschichtetes
Schaufelblatt 9. Auf den Grundkörper 1 ist gemäß
Figur 2 eine Haftvermittlerschicht 2 aufgebracht. Die Haftvermittlerschicht
2 kann eine Legierung der Art MCrAlY sein
umfassend Chrom, Aluminium, Yttrium, Lanthan und/oder Zirkon
sowie einen Rest aus einem Element oder mehreren Elementen
aus der Gruppe umfassend Eisen, Kobalt und Nickel. Auf der
Haftvermittlungsschicht 2 ist eine Wärmedämmschicht 4 mit einem
metallischen Mischoxidsystem aufgebracht. Das Mischoxidsystem
weist hierbei vorzugsweise Lanthanaluminat (LaAlO3)
auf, wobei das Lanthan teilweise durch z.B. Gadolinum ersetzt
sein kann. Das Mischoxidsystem kann auch alternativ Kalziumzirkonat
mit einer Teilsubstituierung des Kalziums durch
Strontium (Ca1-XSrXZr2O3) aufweisen. Dem ternären Oxid (LaAlO3,
Ca1-XSrXZrO3) vorzugsweise ein weiteres Oxid, wie Aluminiumoxid
oder Zirkonoxid, beigemischt. Zwischen der Haftvermittlungsschicht
2 und der Wärmedämmschicht 4 ist die Oxidschicht
5 mit dem Anbindungsoxid gebildet. Das Anbindungsoxid
entsteht vorzugsweise durch eine Oxidation der Haftvermittlungsschicht
2, welches bei Vorhandensein von Lanthan zu einem
Anteil von Lanthanoxid, bei Zirkon zu einem Anteil von
Zirkonoxid etc. führt. Durch die Oxidschicht 5 erfolgt eine
gute Anbindung der Wärmedämmschicht 4 über die Haftvermittlungsschicht
2 an den metallischen Grundkörper 1. An einer
äußeren Oberfläche 6 der Wärmedämmschicht 4 strömt bei einem
Einsatz der Gasturbinenlaufschaufel 1 in einer nicht näher
dargestellten Gasturbine ein heißes aggressives Gas 7 vorbei,
welches durch die keramische Wärmedämmschicht 4 und die Haftvermittlungsschicht
2 wirksam von dem metallischen Grundkörper
1 ferngehalten wird. Hierdurch wird selbst bei wechselnden
thermischen Belastungen der Gasturbinenschaufeln eine
hohe Standzeit erreicht.The gas turbine blade 3 shown in FIG. 1 has a
In Figur 3 ist ein Schichtsystem analog zu Figur 2 dargestellt,
bei dem auf den Grundkörper 1 eine Haftvermittlerschicht
2 und darauf die Wärmedämmschicht 4 aufgebracht ist.
Die Haftvermittlerschicht 2 weist hierbei eine so rauhe Oberfläche
auf, daß die Wärmedämmschicht 4 im wesentlichen ohne
eine chemische Anbindung durch eine mechanische Verklammerung
an die Haftvermittlerschicht 2 und damit an den Grundkörper 1
angebunden ist. Eine solche Rauhigkeit einer Oberfläche 11
der Haftvermittlerschicht 2 kann bereits durch das Aufbringen
der Haftvermittlerschicht 2, beispielsweise durch Vakuumspritzen
(Plasma-Spritzen), erfolgen. Insbesondere beim Plasmaspritzen
werden auf das Erzeugnis bereits vorreagierte Produkte
(z.B. La1-xGdxAlO3 oder Ca1-xSrxZrO3) aufgebracht. Das
heißt, die Produkte werden in einem Arbeitsschritt vor der
eigentlichen Beschichtung hergestellt und dann im wesentlichen
ohne weitere chemische. Reaktionen und Umwandlungen auf
das Erzeugnis 3 aufgebracht. Eine unmittelbare Anbringung der
Wärmedämmschicht 4 an den metallischen Grundkörper 1 kann
hierbei auch durch eine entsprechende Rauhigkeit des metallischen
Grundkörpers 1 erfolgen. Es ist ebenfalls moglich, zwischen
der Haftvermittlerschicht 2 und der Wärmedämmschicht 4
eine zusätzliche Anbindungsschicht beispielsweise mit einem
Aluminiumnitrid oder einem Chromnitrid aufzubringen.FIG. 3 shows a layer system analogous to FIG. 2, in which an
Gemäß dem in Figur 4 dargestellten Phasendiagramm von Lanthanaluminat und dem in Figur 5 dargestellten Phasendiagramm von Calciumzirkonat ist erkennbar, daß bei geeigneter Wahl der Zusätze an Oxiden eine Schmelztemperatur von deutlich oberhalb 1750 °C sowie eine hohe Phasenstabilitat ohne Phasenübergang bei Betriebstemperaturen von über 1250 °C gegeben ist.According to the phase diagram of lanthanum aluminate shown in FIG. 4 and the phase diagram of FIG Calcium zirconate can be seen that with a suitable choice of Additions of oxides have a melting temperature of well above 1750 ° C and a high phase stability without phase transition given at operating temperatures above 1250 ° C is.
Claims (14)
- Product (3) which can be exposed to a hot aggressive gas, having a metallic base body (1), applied to which there is a ceramic thermal barrier layer (4) which contains a mixed metal oxide system comprising a lanthanum aluminate.
- Product (3) according to Claim 1, in which the lanthanum in the lanthanum aluminate is partially replaced by at least one substitute element.
- Product (3) according to Claim 2, in which the at least one substitute element comes from the lanthanide group, and is in particular gadolinium (Gd).
- Product (3) which can be exposed to a hot aggressive gas, having a metallic base body (1), applied to which there is a ceramic thermal barrier layer (4) which contains a mixed metal oxide system comprising a calcium zirconate, in which calcium is partially replaced by at least one element, in particular strontium (Sr).
- Product (3) according to one of the preceding claims, in which the substitute element replaces up to 0.8, preferably 0.5, of the lanthanum or calcium, respectively.
- Product (3) according to one of the preceding claims, in which the mixed metal oxide system contains a further oxide.
- Product (3) according to one of the preceding claims, in which an adhesion promoter layer (2) forming a bonding oxide is arranged between the base body (1) and the thermal barrier layer (4).
- Product (3) according to one of the preceding claims, in which the adhesion promoter layer (2) is an alloy comprising one of the elements of the mixed metal oxide system.
- Product (3) according to one of the preceding claims, in which the metal base body (4) contains a superalloy based on nickel, cobalt and/or chromium.
- Product (3) according to one of the preceding claims, characterized by configuration as a component of a heat engine, in particular a gas turbine.
- Product (3) according to Claim 10, characterized by configuration as a turbine rotor blade, turbine guide vane or heat shield of a combustion chamber.
- Product (3) according to one of the preceding Claims, characterized in that the coefficient of thermal expansion α of the ternary oxide is between 7*10-6/K and 17*10-6/K.
- Product (3) according to one of the preceding Claims, characterized in that the thermal conductivity of the ternary oxide is between 1.0 W/mK and 4.0 W/mK.
- Process for the production of a thermal barrier layer on a product having a metallic base body, a prereacted mixed metal oxide system comprising a lanthanum aluminate and/or calcium zirconate, in which calcium is partially replaced by at least one element, in particular strontium (Sr), is applied by means of plasma spraying or an evaporation coating process.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE19748508 | 1997-11-03 | ||
DE19748508 | 1997-11-03 | ||
PCT/DE1998/003205 WO1999023271A1 (en) | 1997-11-03 | 1998-11-03 | Product, especially a gas turbine component, with a ceramic heat insulating layer |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1029101A1 EP1029101A1 (en) | 2000-08-23 |
EP1029101B1 true EP1029101B1 (en) | 2001-09-12 |
Family
ID=7847454
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98961067A Expired - Lifetime EP1029101B1 (en) | 1997-11-03 | 1998-11-03 | Product, especially a gas turbine component, with a ceramic heat insulating layer, and process for making the same |
Country Status (6)
Country | Link |
---|---|
US (2) | US6440575B1 (en) |
EP (1) | EP1029101B1 (en) |
JP (1) | JP2001521988A (en) |
DE (1) | DE59801471D1 (en) |
RU (1) | RU2218447C2 (en) |
WO (1) | WO1999023271A1 (en) |
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Families Citing this family (52)
Publication number | Priority date | Publication date | Assignee | Title |
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Family Cites Families (22)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5393134A (en) | 1977-01-27 | 1978-08-15 | Mitsubishi Heavy Ind Ltd | Heattproof acidification resistance metal portion material |
US4339509A (en) | 1979-05-29 | 1982-07-13 | Howmet Turbine Components Corporation | Superalloy coating composition with oxidation and/or sulfidation resistance |
US4321310A (en) | 1980-01-07 | 1982-03-23 | United Technologies Corporation | Columnar grain ceramic thermal barrier coatings on polished substrates |
US4585481A (en) | 1981-08-05 | 1986-04-29 | United Technologies Corporation | Overlays coating for superalloys |
DE3539029A1 (en) * | 1985-11-02 | 1987-05-07 | Bbc Brown Boveri & Cie | HIGH TEMPERATURE PROTECTIVE LAYER AND METHOD FOR THEIR PRODUCTION |
DE3543802A1 (en) * | 1985-12-12 | 1987-06-19 | Bbc Brown Boveri & Cie | HIGH TEMPERATURE PROTECTIVE LAYER AND METHOD FOR THEIR PRODUCTION |
US4764341A (en) | 1987-04-27 | 1988-08-16 | International Business Machines Corporation | Bonding of pure metal films to ceramics |
EP0486489B1 (en) | 1989-08-10 | 1994-11-02 | Siemens Aktiengesellschaft | High-temperature-resistant, corrosion-resistant coating, in particular for components of gas turbines |
DE3926479A1 (en) | 1989-08-10 | 1991-02-14 | Siemens Ag | RHENIUM-PROTECTIVE COATING, WITH GREAT CORROSION AND / OR OXIDATION RESISTANCE |
JPH03226553A (en) * | 1990-01-31 | 1991-10-07 | Nippon Steel Corp | A.c. plasma torch having high durability |
US5077140A (en) | 1990-04-17 | 1991-12-31 | General Electric Company | Coating systems for titanium oxidation protection |
JP2747087B2 (en) * | 1990-05-31 | 1998-05-06 | 新日本製鐵株式会社 | Thermal spray coating material and thermal spray coating heat resistant member |
US5032557A (en) * | 1990-07-02 | 1991-07-16 | Tocalo Co., Ltd. | Thermal spray material and and thermal sprayed member using the same |
US5082741A (en) * | 1990-07-02 | 1992-01-21 | Tocalo Co., Ltd. | Thermal spray material and thermal sprayed member using the same |
US5401307A (en) | 1990-08-10 | 1995-03-28 | Siemens Aktiengesellschaft | High temperature-resistant corrosion protection coating on a component, in particular a gas turbine component |
JPH04231451A (en) * | 1990-12-28 | 1992-08-20 | Nippon Steel Corp | Thermal spray material and sprayed heat-resistant member |
JPH04231452A (en) * | 1990-12-28 | 1992-08-20 | Nippon Steel Corp | Thermal spray material and sprayed heat-resistant member |
US5236787A (en) | 1991-07-29 | 1993-08-17 | Caterpillar Inc. | Thermal barrier coating for metallic components |
JP2697469B2 (en) * | 1992-04-03 | 1998-01-14 | 株式会社日立製作所 | Gas turbine blades, vanes and combustor liners and manufacturing method |
GB2286977A (en) | 1994-02-24 | 1995-09-06 | Lee Chwen Chern | Inorganic coating composition |
US5512382A (en) | 1995-05-08 | 1996-04-30 | Alliedsignal Inc. | Porous thermal barrier coating |
US6258467B1 (en) * | 2000-08-17 | 2001-07-10 | Siemens Westinghouse Power Corporation | Thermal barrier coating having high phase stability |
-
1998
- 1998-11-03 JP JP2000519122A patent/JP2001521988A/en active Pending
- 1998-11-03 WO PCT/DE1998/003205 patent/WO1999023271A1/en active IP Right Grant
- 1998-11-03 RU RU2000114253/02A patent/RU2218447C2/en not_active IP Right Cessation
- 1998-11-03 DE DE59801471T patent/DE59801471D1/en not_active Expired - Lifetime
- 1998-11-03 EP EP98961067A patent/EP1029101B1/en not_active Expired - Lifetime
-
2000
- 2000-05-01 US US09/562,877 patent/US6440575B1/en not_active Expired - Lifetime
-
2002
- 2002-07-01 US US10/187,504 patent/US6602553B2/en not_active Expired - Lifetime
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102004025798A1 (en) * | 2004-05-26 | 2005-12-22 | Mtu Aero Engines Gmbh | Thermal barrier coating system |
DE102015205807A1 (en) * | 2015-03-31 | 2016-10-06 | Siemens Aktiengesellschaft | Coating system for gas turbines |
Also Published As
Publication number | Publication date |
---|---|
DE59801471D1 (en) | 2001-10-18 |
JP2001521988A (en) | 2001-11-13 |
US6602553B2 (en) | 2003-08-05 |
RU2218447C2 (en) | 2003-12-10 |
US6440575B1 (en) | 2002-08-27 |
US20020164430A1 (en) | 2002-11-07 |
WO1999023271A1 (en) | 1999-05-14 |
EP1029101A1 (en) | 2000-08-23 |
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