Patent Application
20100247953
Priority is claimed to European Application No. EP 09156515, filed Mar. 27, 2009, the entire disclosure of which is incorporated by reference herein.
The present invention relates to the field of thermal barrier coatings (TBC) as used in particular for the protection of components exposed to the hot gas path of machines such as gas turbines.
Gas turbines (GT) are increasingly requested to have higher efficiencies and this is normally achieved primarily through increase of the firing temperature up to 1750° C. at least for very short periods of time and reduced cooling effort to the GT components. These components in addition to handling the high temperatures should also be able to cope with harsh GT environments for extended periods of time (operating hours>24000 h).
There are the following main approaches to produce thermal barrier coating systems that are capable of handling high temperatures and harsh environments:
a) Oxide CMC+High Temperature Insulation
b) Non-Oxide CMC+EBC
The temperature capability Tmax of materials is defined specifically for industrial gas turbine application as the maximum possible surface temperature for 24000 h in gas turbine combustion gas environment without significant loss of functionality (e.g. reduced thermal barrier effect due to spallation, strain tolerance due sintering, degradation due to environmental attack of combustion gas constituents, thermal phase stability).
Tmax of state of the art TBC systems with about 7 wt % Yttria Stabilized Zirconia (7YSZ) have been determined to be <1150° C. because of sintering behaviour which results in higher stiffness and lower strain tolerance for thermal cycling (start-stop-cycle of the turbine). Also the thermal phase stability of YSZ is limited to about 1100° C. for long-term operation. Tmax for the environmental attack due to Ca-compound form the combustion gas was determined to be around 1200° C.
As all these degradation processes are thermally activated (exponential growth of reaction rates) Tmax is defined as that temperature where significant material degradation compared to virgin material occurs.
The quantification of degradation can be done by state of the art test and evaluation tools, e.g. X-ray diffraction, Knoop hardness, SEM, dilatometer, etc.
The limitations of this prior art coating systems can essentially be summarised as follows:
Document EP 1 806 435 discloses, on a metallic substrate, a bond coat, and on this a so-called inner layer based on a ceramic material, followed by an outer layer also based on a ceramic material. Optionally on this outermost layer additionally an alumina layer may be provided. There is no disclosure of applying prefabricated monolithic ceramic elements in the context of making such a layer structure.
US 2006/280954 relates to layer structures on silicon containing substrates, and not on metal based substrates. There is an outermost sealing layer which may comprise calcium aluminate, and on this sealing layer there can be provided a further TBC layer. Again the document does not disclose the application of prefabricated monolithic ceramic elements in the context of making such a layer structure.
An aspect of the present invention is thus to provide a thermal protection system that is capable of handling high temperatures and harsh environments as will be required of future gas turbines.
This is achieved by typically a four-layer metal/ceramic hybrid system on a metallic substrate (component, e.g. nickel-based superalloy). The system among other aspects relies on e.g. utilizing the current state of the art metal/BC/TBC systems and to augment their temperature capability by bonding a high temperature capable ceramic material able to withstand harsh GT environments to the metal/BC/TBC system.
Specifically, the present invention relates to a multilayer thermal protection system, in which a first ceramic layer (TBC layer) is attached via a bond coat layer on a metallic substrate. On the first ceramic layer there is provided at least one second ceramic layer attached to the first ceramic layer via a ceramic adhesive layer. The first ceramic layer is normally applied by plasma spraying (or another thermal spraying method) and the second ceramic layer comprises monolithic ceramic elements adhesively attached by the ceramic adhesive layer to the first ceramic layer.
Monolithic ceramic elements are to be understood as pre-fabricated elements which can be in the form of tiles, columnar structures, block structures or the like, what is important is that they are pre-manufactured and already sintered prior to the application to the substrate. These monolithic ceramic elements are typically sintered at temperatures of around 1600° C. and therefore do not undergo a further sintering process anymore when mounted in the machine.
Typically, the first plasma sprayed ceramic layer has a thickness in the range of 0.1 to 2 mm.
Typically the second ceramic layer, i.e. the monolithic ceramic elements have a thickness (measured perpendicular to the surface plane of the substrate) in the range of 2 to 35 mm, preferably in the range of 5-10 mm.
According to one preferred embodiment, the first ceramic layer is a low-temperature ceramic layer and the second ceramic layer is a high temperature ceramic layer.
This means that the first ceramic layer normally has a temperature capability Tmax up to and including a temperature of 1150° C., preferably up to and including a temperature of 1100° C., as for example the case for conventional TBC layer as outlined above.
The second ceramic layer, i.e. the monolithic ceramic elements, Preferentially has a higher temperature capability Tmax than the first ceramic layer. This means that preferably the temperature capability Tmax of the second ceramic layer is at least 100° C., preferably at least 200° C. or even 300° C., larger than the temperature capability Tmax of the first ceramic layer.
Normally the second ceramic layer has a temperature capability Tmax of at least 1200° C., more preferably of at least 1500° C., even more preferably in the range of 1200-1750° C. Tmax of the second layer is defined by the sintering, phase stability and environmental stability.
As outlined above, the temperature capability Tmax of materials is defined specifically for industrial gas turbine applications as the maximum possible surface temperature for 24000 h in gas turbine combustion gas environment without significant loss of functionality such as reduced thermal barrier effect due to spallation, strain tolerance due sintering, degradation due to environmental attack of combustion gas constituents, thermal phase stability.
The quantification of degradation for the determination of the temperature capability can be done by state of the art test and evaluation tools, e.g. X-ray diffraction, Knoop hardness, SEM, dilatometer, etc. as concerns the measurement of these quantities, reference is made to the following literature: ASTM C 1326-08e1 Standard Test Method for Knoop Indentation Hardness of Advanced Ceramics; ASTM E831 Standard Test Method for Linear Thermal Expansion of Solid Materials by Thermomechanical Analysis; G. Witz, V. Shklover, W. Steurer, S. Bachegowda, H.-P. Bossmann: MONITORING THE PHASE EVOLUTION OF YTTRIA STABILIZED ZIRCONIA IN THERMAL BARRIER COATINGS USING THE RIETVELD METHOD, Journal of the American Ceramic Society, Volume 90 Issue 9, Pages 2935-2940 (2007).
Using these quantities the temperature capability can be determined as described in the above mentioned publication from Witz. A time-temperature-relation was established for the temperature range 1100-1400° C. for exposure times 1-1400 h. The measured kinetics of phase evolution (or phase stability) was combined with the temperature dependence using the Arrhenius equation for thermally activated processes. Tmax for a certain time of exposure can be extrapolated from these data. This approach is applicable also for sintering and environmental stability. For this purpose the individual layers can be tested and investigated as stand-alone layers.
The nature of the system ensures that the thermal mismatch between the adjacent layers is minimized to reduce internal stresses at the interfaces of the various layers. Metal/BC/TBC systems have a limited temperature capability, by bonding an independent ceramic part that is capable handling higher temperature and having higher environmental resistance to hot gas exposed surface of the Metal/BC/TBC system, the system can be made to operate at temperatures above 1400° C.
The top ceramic part can be a single, multilayer or graded system prepared by any state of the art processes. This independent part is bonded to the metal/BC/TBC system. The preferred bonding method being adhesive, achieved by means of ceramic cement pastes. The cements paste used in this context preferably have a solid to liquid ratio of in the range of 60-90 wt % (equalling roughly 35-70 vol %).
The present invention also relates to a method for making a multilayer thermal protection system as defined above and further below.
The wet cements can be applied to the surfaces of the parts for example using a sponge. The cement thickness is preferably less than 0.5 mm, even more preferably the cement thickness is less than 0.1 mm, or in the range of 0.05 mm.
The cements are preferably dried at room temperature for 4 to 12 hr. Preferably the drying takes place under a compressive load in the range of 70 to 850 g/cm2 preferentially applied perpendicularly to the joint face (“wet loading”). The load can for example be produced by using gravity and steel plates as weights. The wet loading can have significant influences on the joint adhesion.
The cements can be cured in atmospheric box furnaces, preferably at a temperature in the range of 500 to 600° C. and more preferably within a timespan of 5 to 15 h. Preferably curing takes place with a curing load of up to 250 g/cm2 applied perpendicularly to the joint face. Also a staged during protocol as possible. It is for example possible to cure cements according to yet another preferred embodiment in steps of in the range of 90-100° C. for 0.5-3 h followed by curing at a temperature of 200-300° C. for 0.5-3 h followed by curing at a temperature in the range of 300-400° C. for 0.5-3 h with a curing load of up to 250 g/cm2 applied perpendicular to the joint face. For specific applications/materials a final curing step of a 500-700° C. for 3-6 h can be used.
According to a preferred embodiment, the second ceramic layer has a thickness in the range of 2-20 mm, preferably in the range of 5-10 mm. The second ceramic layer (but also the first ceramic layer) can be a single layer, multilayer or graded layer system.
According to a further preferred embodiment, the second ceramic layer so the monolithic ceramic elements are alpha-alumina based and/or magnesia based, wherein preferably elements of the second ceramic layer essentially consist of alpha alumina and/or magnesia. They can be produced using methods according to the state-of-the-art, where starting from this material a green compact is produced which is subsequently sintered, normally at temperatures around 1600° C.
The ceramic plates can be cut with a low speed diamond saw or by water jet to avoid crack initiation at the cutting edges. Before joining both surfaces can be abraded with SiC paper and subsequently cleaned ultrasonically in ethanol to improve adhesion of the cement. These prefabricated elements are subsequently joined to the first (TBC) layer using the adhesive, braze etc. on a TBC coated metallic substrate.
Multilayer thermal protection system can be characterised in that the porosity of the first layer is in the range of 5-25%.
Preferentially, second ceramic layer is a multilayer structure with at least one dense surface exposed layer with a porosity of below 30%, preferably in the range of 0-25% or 5-10%, and with at least one porous interface layer (can be of the same constitution or of a different constitution) with a porosity of above 30%, preferably in the range of 50-90%, at the interface with the first ceramic layer.
Yet another preferred embodiment is characterised in that the second ceramic layer comprises at least one surface exposed layer and at least one underlying additional layer, and the surface exposed layer is structured as a two-dimensional array of tiles separated by gaps.
The gaps between the tiles can be slots with parallel sidewalls perpendicular to or inclined with respect to the surface plane of the substrate. In this case the sidewalls of the tiles are planes perpendicular to the surface plane or inclined with respect to the surface plane, respectively.
In the alternative is also possible to have sidewalls of the tiles which have an interlocking shape, such as key and slot joints or tongue and groove joints.
The tiles structure of the most surface exposed layer allows to reduce thermal expansion problems and allows to keep local damage due to foreign object impact (FOD) to a minimum. The tiles can be of rectangular, quadratic, rhombic or hexagonal shape. Preferably, in particular in case of a regular hexagonal shape (honeycomb) the lateral extension of a tile in both dimensions is in the range of 2-35 mm, preferably in the range of 10-20 mm.
The ceramic adhesive layer can be a refractory cement paste layer. It can be calcium aluminate based, or can even essentially consist of calcium aluminate.
According to a preferred embodiment, the bond coat is composed of MCrAlY, where M═Co, Ni or Co/Ni, and/or of PtAl.
Preferably the composition of the bond coat is given as 25Cr 5.5Al 2.5Si 1Ta 0.6Y with the remainder Ni, or as 12Co 20Cr 11Al 2.7Si 1Ta 0.6Y with the remainder Ni.
As mentioned above, typically the first ceramic layer is a conventional TBC layer, and can for example be based on or consist of 7YSZ. (ZrO2, stabilised with 7 wt.-% Y2O3).
In order to ensure mechanical bonding, grooves, ribs, anchors and roughening can be utilized this means, that, according to a preferred embodiment, at least one of the interfaces to the ceramic adhesive layer mechanical bonding aids are provided, preferably in the form of grooves, ribs, anchors, and/or surface texture (roughening) provided in the first ceramic layer and/or the second ceramic layer.
Furthermore the present invention relates to the use of a thermal barrier coating layer system as outlined above for coating at least a part of a component exposed to temperatures above 1400° C.
More specifically, it relates to the use of a thermal barrier coating layer system as outlined above for coating at least partially components exposed to the hot gas path in thermal engines, in particular in gas turbines, preferably exposed to hot gases with temperatures above 1400° C.
Such a thermal barrier coating layer system can for example be used for selectively coating only the most temperature exposed parts of gas turbine components exposed to the hot gas path, while surrounding parts are coated with a thermal barrier coating system consisting of a thermal barrier coating layer attached to the metallic substrate by a bond coat layer.
Preferred embodiments of the invention are described in the following with reference to the drawings, which are for the purpose of illustrating the present preferred embodiments of the invention and not for the purpose of limiting the same. In the drawings,
a) shows a schematic representation of a top view onto a honeycomb tile structure of the barrier coating, b) shows a schematic representation of a cut perpendicular to the plane of the substrate with planar surfaces of the sidewalls of the tiles and c) shows a schematic representation of a cut perpendicular to the plane of the substrate with interlocking surfaces of the sidewalls of the tiles;
Referring to the drawings, which are for the purpose of illustrating the present preferred embodiments of the invention and not for the purpose of limiting the same,
The metallic substrate 5 is a Ni-based superalloy, the bondcoat layer 4 is composed either of a MCrAlY or PtAl system, the low temperature ceramic layer 3 or TBC layer is based on or consists of 7YSZ and the adhesive layer 2 is a refractory cement paste normally a calcium aluminate based. The high temperature resistant ceramic part 1 can be a single, multilayer or graded system prepared by processes known in the art such as vapour deposition, sol gel processes, powder deposition, direct a position, plasma spray processes and the like. The high temperature resistant ceramic layer 1 has a thickness of at least 2 mm and up to 20 mm, preferred thickness is between 5 and 10 mm.
The ceramic part 1 is preferably alpha alumina based and/or magnesia based. The ceramic part 1 can be gas tight (closed porosity in the range of 0-10%), or have open plus closed porosity ranging from 15%-90%.
The layered system can, as illustrated in
The dense outer layer 1a can be, as illustrated in
As can be seen from
Experimental Part:
A first series of experiments was performed using a high grade calcium aluminate cement to join 7YSZ coating to an open-cell alpha-alumina monolithic ceramic with the porosity of about 80 percent prepared by a sol-gel process.
The cements paste used had a solid to liquid ratio of ˜60-90 wt % (˜35-70 vol %). The wet cements were applied to the surfaces of the parts with a sponge. The cement thickness were less than 0.5 mm typically in the range of or less than 0.05 mm.
The cements were dried at room temperature for 4 to 12 hr in laboratory atmosphere with a compressive load from 70 to 850 g/cm2 applied perpendicular to the joint face (“wet loading”). The load was produced by using gravity and steel plates as weights. The wet loading had a significant influence on the joint adhesion.
The cements were cured in atmospheric box furnaces at temperature from 500 to 600° C. for 5 to 15 hr with a curing load of 0.0 to 250 g/cm2 applied perpendicular to the joint face. Some cements were cured in steps of 93° C. for 2 hr plus 260° C. for 2 hr plus 372° C. for 2 hr with a curing load of 0.0 to 250 g/cm2 applied perpendicular to the joint face. Sometimes a final curing step of 600° C. for 5 hrs was used.
The ceramic plates were cut with a low speed diamond saw or by water jet to avoid crack initiation at the cutting edges. Before joining both surfaces were abraded with SiC paper and subsequently cleaned ultrasonically in ethanol to improve adhesion of the cement.
The sample was produced as follows:
On a substrate of nickel superalloy a NiCoCrAlY bondcoat (about 0.3 mm thickness) and a 7YSZ coating layer (about 0.8 mm thickness) was produced by plasma spray processes. A thin layer (about 0.1 mm) of the refractory cement was applied manually to the surface of this TBC layer and on an open cell alpha alumina monolithic ceramic (about 20 mm thickness). Subsequently both pieces were joined putting the cement layers together. After curing 24 h in humid environment, assembly was heat treated with the following steps: 60° C./2 h, 120° C./2 h, 300° C./2 h, 1000° C./20 h. The heating and cooling rate for the last step was about 50 K/h.
The corresponding structure is shown in
Subsequently a second series of experiments was conducted using the same substrate/Bondcoat/TBC system and the same refractory cement but as second layer 1 an alpha-alumina monolithic part with 20% porosity and 12 mm thickness was used. Grooves 9 were made on the mating surfaces of the TBC 3 and the alpha-alumina 1 in order to improve the mechanical interlocking of the cement, as shown in
The sample was produced similarly as in case of the above first series of experiments.
| Number | Date | Country | Kind |
|---|---|---|---|
| 09156515 | Mar 2009 | EP | regional |
