Patent Application
20050013993
The present invention generally relates to an environmental and thermal barrier coating, and to a component coated with such a coating. The present invention also relates to methods for preparing an environmental and thermal barrier coating, and for preparing a component coated with such a coating.
Advanced turbomachines use silicon-based (Si-based) non-metallic materials such as silicon nitride, silicon carbide, molybdenum silicides, niobium silicides, and their composites for hot-section components. Due to the high temperature capability of Si-based ceramics, those ceramic turbomachines operate at higher temperatures with minimum cooling and higher engine performance. However, at operating temperatures above about 1200° C., Si-based ceramics can be adversely affected by oxidation and water vapor present in the flow stream. Such hostile engine environments result in rapid recession of Si-based ceramics parts. Recession refers to the wear of a substrate or component due to the effects of ablation and/or erosion due to particulate impact.
In U.S. Pat. No. 6,159,553 to Li et al., discloses the use of tantalum oxide (Ta2O5) as coating material on silicon nitride parts. A tantalum oxide coating of 2 to 500 microns in thickness can effectively protect the surface of silicon nitride parts from oxidation and reaction with water vapor at high temperatures. However, pure tantalum oxide coatings on Si-based parts have some limitations, including the following.
Ta2O5 undergoes a phase transformation from a low temperature phase (β-phase) to a high temperature phase (α-phase) at about 1350° C., which may cause cracking in the coating due to the change in volume which occurs during the phase transformation.
Ta2O5 is susceptible to grain growth at temperatures above 1200° C. Pronounced grain growth results in a large grain microstructure of up to about 10μ, which reduces the mechanical strength of the coating, induces high local residual stresses in the coating, and causes the coating to spall.
Ta2O5 has a coefficient of thermal expansion (CTE) of about 3×10−6° C.−1, whereas silicon nitride has a CTE in the range of about 3-4×10−6° C.−1 and silicon carbide (SiC) has a CTE in the range of 4-5×10−6° C.−1. Since there is about 10 to 30% CTE mismatch between Ta2O5 and silicon nitride, and an even higher CTE mismatch between Ta2O5 and SiC, residual stresses will develop in the Ta2O5 coating on Si-based ceramics. These residual stresses can limit the service life of the coating.
Pure Ta2O5 coatings have a relatively low fracture toughness (probably from <1 to <3 MPa.m0.5), which may adversely affect the mechanical integrity and the lifetime of the coating during service where there are foreign object impact and particulate erosion events.
Due to the above limitations, Ta2O5 coatings on Si-based ceramics may not provide adequate protection for turbine engine applications at temperatures of about 1300° C. or above, thousands of thermal cycles occur, and a coating lifetime greater than five thousand (5000) hours is required. Furthermore, the cost of Ta2O5 raw powder material is relatively high compared with that of most other high temperature ceramic oxide powders. Still further, the density of Ta2O5 is relatively high, so the weight of the coating may negatively affect the performance of the turbine machinery. It would be highly desirable to significantly improve the Ta2O5 coating to meet the stringent demands of advanced ceramic turbine engine applications, and to reduce the cost and weight of the coating.
As can be seen, there is a need for an environmental and thermal barrier coating for coating Si-based substrates, e.g., comprising Si3N4, wherein the coating protects the substrate from recession and thermal cycling at temperatures in the range of from about 1300 to 1550° C. There is a further need for an effective, low weight, and low cost environmental and thermal barrier coating for coating Si-based gas turbine engine components. There is also a need for a process for coating a silicon-based gas turbine engine component with an environmental and thermal barrier to provide an environmentally and thermally protected component. The present invention provides such coatings, components, and processes, as will be described in enabling detail hereinbelow.
In one aspect of the present invention, there is provided an environmental and thermal barrier coating comprising a layer of a composition which comprises at least about 50 mole % AlTaO4, and the balance comprising at least one metal oxide selected from the group consisting of Ta, Al, Cr, Hf, Ti, Zr, Mo, Nb, Ni, Sr, Mg, Si, and the rare earth elements including Sc, Y, and the lanthanide series of elements. The composition may have a coefficient of thermal expansion (CTE) in the range of from about 3.5×10−6° C.−1 to 5×10−6° C.−1, and a thickness in the range of from about 0.1 to 50 mils.
In another aspect of the present invention, an environmental and thermal barrier coating comprises a layer of a composition which comprises at least about 99 mole % AlTaO4. The composition may be prepared by reacting a starting powder mixture comprising about 50 mole % Ta2O5 and about 50 mole % Al2O3. Such an environmental and thermal barrier coating may have a coefficient of thermal expansion (CTE) in the range of from about 4×10−6° C.−1 to 5×10−6° C.−1.
In still another aspect of the present invention, there is provided a thermally protected component comprising a substrate having a surface, and an environmental and thermal barrier coating disposed on the substrate surface. The environmental and thermal barrier coating may comprise at least about 50 mole % AlTaO4, and the balance may consist essentially of Ta2O5 or Al2O3. Such an environmental and thermal barrier coating may be characterized by a coefficient of thermal expansion (CTE) in the range of from about 4×10−6° C.−1 to 5×106° C.−1.
In yet another aspect of the present invention, a thermally protected component comprises a substrate having a surface, and an environmental and thermal barrier coating disposed on the substrate surface. The environmental and thermal barrier coating may comprise at least about 50 mole % AlTaO4, and the balance may comprise at least one metal oxide including Ta, Al, Cr, Hf, Ti, Zr, Mo, Nb, Ni, Sr, Mg, Si, and the rare earth elements including Sc, Y, and the lanthanide series of elements.
In an additional aspect of the present invention, a method for preparing an environmentally and thermally protected component may include: providing a mixture of Ta2O5 (or a precursor thereof), and Al2O3 (or a precursor thereof); reacting the mixture to provide a reaction product comprising at least about 50 mole % AlTaO4; and depositing a layer of the reaction product on a component surface to form an environmental and thermal barrier coating on the component surface.
In a further aspect of the present invention, a method for making an environmentally and thermally protected component includes: providing a composition comprising at least about 90 mole % AlTaO4, and the balance consisting predominantly of a metal oxide such as Al2O3 or Ta2O5; providing a substrate having a surface to be coated; and depositing a layer of the composition on the substrate surface to form an environmental and thermal barrier coating on the substrate. Such a coating may have a coefficient of thermal expansion (CTE) in the range of from about 4×10−6° C.−1 to 5×10−6° C.−1, and a thickness in the range of from about 0.1 to 50 mils.
In another aspect of the present invention, there is provided a method for making an environmentally and thermally protected component including: providing a substrate to be coated with an environmental and thermal barrier coating. The substrate provided may comprise silicon carbide. Thereafter, the method further includes providing a composition comprising at least about 90 mole % AlTaO4, and the balance comprising an oxide of an element selected from the group consisting of Ta, Al, Cr, Hf, Ti, Zr, Mo, Nb, Ni, Sr, Mg, Si, and the rare earth elements including Sc, Y, and the lanthanide series of elements. Thereafter, the method still further includes depositing a layer of the composition on the substrate surface to form the environmental and thermal barrier coating. Each of the substrate and the environmental and thermal barrier coating may have a coefficient of thermal expansion (CTE) in the range of from about 4×10−6° C.−1 to 5×10−6° C.−1.
These and other features, aspects and advantages of the present invention will become better understood with reference to the following drawings, description and claims.
The following detailed description is of the best currently contemplated modes of carrying out the invention. The description is not to be taken in a limiting sense, but is made merely for the purpose of illustrating the general principles of the invention, since the scope of the invention is best defined by the appended claims.
The present invention provides AlTaO4-based coatings which can effectively protect substrates or components exposed to thermal cycling during service. Coatings of the invention are adapted to protect Si-based ceramic components from thermal damage during repeated thermal cycling to temperatures in the range of from about 1300 to 1550° C., and to protect such components from recession during service.
As an example, the present invention may be used to protect gas turbine engine components during exposure to service conditions. The environmental and thermal barrier coating compositions of the invention have a coefficient of thermal expansion (CTE) match with Si-based ceramic substrates, such as SiC- and Si3N4-based ceramics or composites. Coatings of the invention are therefore well adapted for coating Si-based substrates, e.g., gas turbine engine components comprising Si3N4, wherein the coating protects the substrate from recession and thermal cycling at temperatures in the range of from about 1300 to 1550° C.
The CTE of a 10 mole % Al2O3/90 mole % Ta2O5 alloy is about 3.5×10−6° C.−1. As the alloy composition increases to 25 mole % Al2O3/75 mole % Ta2O5, the microstructure includes a mixture of Ta2O5—Al2O3 solid solution and AlTaO4, and the CTE is about 4×10−6° C.−1. Coatings comprising from about 10 mole % Al2O3/90 mole % Ta2O5 up to about 25 mole % Al2O3/75 mole % Ta2O5, having CTE values in the range of 3.5-4×10−6° C.−1, may provide a suitable CTE match for coating Si3N4-based substrates. A starting mixture for forming a coating of the invention for coating SiC-based substrates (which may have a CTE in the range of 4-5×10−6° C.−1), may comprise from about 25 to 50 mole % Al2O3. For a starting mixture having about 50 mole % Al2O3/50 mole % Ta2O5 the majority of the phase in the coating is AlTaO4, and the CTE is about 5×10−6° C.−1, thereby providing a good CTE match between the coating and the SiC-based substrate. In contrast, prior art coatings have CTE values too low to provide a good CTE match with SiC-based substrates.
According to one aspect of the present invention, there is provided an environmental and thermal barrier coating (e.g.,
The AlTaO4-based coatings of the present invention prevent the loss of silica oxidation product formed on the surface of the Si-based substrate. The close CTE match between AlTaO4 (ca. 5×10−6° C.−1) and SiC-based substrates (ca. 4-5×10−6° C.−1) makes the AlTaO4-based materials of the present invention suitable coatings for SiC-based materials and composites. Besides the benefit of CTE match, AlTaO4 further enjoys the benefits of having a stable crystalline structure at temperatures in the range of from about 1300 to 1550° C. (e.g., does not undergo β- to α-phase transformation at a temperature of 1550° C. (see Example 5)), a relatively low weight (e.g., a weight which is about 30% less than that of prior art Ta2O5 coatings), and a low production cost due to the low cost of Al2O3 powder employed as starting material. Since, coating compositions of the invention do not undergo β- to α-phase transformation at temperatures as high as 1550° C., such coatings may protect components exposed to at least 1550° C.
Generally, the AlTaO4 in the coating of this invention may be prepared via the chemical reaction between Al2O3 and Ta2O5 powders, or their precursors, provided in a starting mixture, or may be formed from a commercially available AlTaO4 powder. Various dopants or additives may be included in the starting mixture using either wet or dry mixing techniques in order to alter the CTE of the final product. Such dopants or additives may include one or more oxides, other compounds, or their precursors, of an element such as Hf, Ti, Zr, Mo, Nb, Ni, Sr, Mg, Si, Al, Cr, Ta, or the rare earth elements including Sc, Y, and the lanthanide series of elements. A coating composition prepared by firing such a mixture may be applied to a substrate to be coated using various deposition techniques well known in the art, such as plasma spray coating, dip coating, spray coating, sol-gel coating, chemical vapor deposition, physical vapor deposition, or electron beam physical vapor deposition.
The sintering property of Ta2O5 is improved by the inclusion of Al2O3 (alumina), as disclosed in commonly assigned co-pending U.S. Patent Application Publication No. 2002/0136835 A1, the disclosure of which is incorporated by reference herein in its entirety. Pressed pellets comprising alumina, e.g., containing from about 1.0 to 10 mole % of Al2O3, show higher density (e.g., as shown by less internal cracking of the Al2O3 containing pellets) as compared with pure Ta2O5 pellets sintered under the same conditions. For example, pure Ta2O5 pellets tend to fracture and disintegrate at room temperature, whereas the Al2O3 containing pellets remain intact. This improved sinterability is believed to be due to a reduction in the rate of Ta2O5 grain coarsening by the addition of Al2O3, and/or the enhancement of Ta ion lattice diffusion as the number of cation vacancies is increased by the diffusion kinetics due to the presence of Al ions.
The solid solubility of Al2O3 in Ta2O5 may be about 10 mole % at about 1500° C. Since α-Al2O3 has a CTE of about 8×10−6° C.−1, the CTE of a 10 mole % Al2O3/90 mole % Ta2O5 alloy would be about 3.5×10−6° C.−1, which is 10% higher than the CTE of pure Ta2O5 and closer to the CTE of silicon nitride. When the amount of Al2O3 in Ta2O5 exceeds about 10 mole %, a second phase having the formula of AlTaO4 forms that has a CTE of about 5×10−4° C.−1. As the alloy composition increases to 25 mole % Al2O3/75 mole % Ta2O5, the microstructure includes a mixture of Ta2O5—Al2O3 solid solution and AlTaO4, and the CTE is about 4×10−6° C.−1, which provides a good CTE match with SiC. If the Al2O3 concentration exceeds 25 mole %, the CTE of the coating may become too high for application on Si3N4 substrates. For SiC and its composites having a CTE in the range of 4-5×10−6 C−1, the starting mixture for forming the coating composition may comprise up to about 50 mole % Al2O3, so that the majority of the phase in the coating is AlTaO4, and there is a good CTE match between the coating and the substrate.
Coating compositions of the present invention exhibit low grain growth rate (e.g., having smaller grains, as shown by scanning electron microscopy, when Al2O3 is present with Ta2O5, as compared to Ta2O5 without Al2O3), good CTE match with Si-based substrates (as described hereinbelow), and high fracture toughness (e.g., as shown by difficulty in machining samples formed from the coating composition). The composition for forming the coating may comprise tantalum oxide (Ta2O5), or a mixture of Ta2O5 and Al2O3. Other oxides, compounds, or their precursors, of elements such as Cr, Hf, Si, Ln (rare earth elements including the entire lanthanum series and Y), Mg, Mo, Ni, Nb, Sr, Ti, and Zr may be added as dopants or additives. Such dopants may have some effect on the CTE of the resultant coating composition, mostly shifting it higher.
Additional additives (e.g., nitrides, carbides, borides, suicides) can be introduced to further inhibit grain growth, to modify the CTE, and reinforce tantalum oxide. By selecting particular dopants or combinations of dopants and additives, the above characteristics of grain growth rate, CTE/substrate match, and fracture toughness may be achieved.
A variety of ceramic processing methods can be used to introduce and incorporate various dopants and additives into coatings of the present invention. As shown by the method 100 in
After mixing (and drying, if wet mixing in a liquid medium is used) the mixture 104 may be coated on a substrate during a coating operation or step 108. Alternatively, the mixture may be subjected to a calcination step 112 in which the mixture is heat-treated, e.g., at a temperature up to about 1600° C., before performing the coating step 108. Optionally, a milling or grinding step 110 may be preformed after the calcination step 112 and before the coating step 108.
Referring to
The coating step 108 (
The coating 204 typically comprises at least about 50 mole % AlTaO4. The coating 204 may be formed from a starting mixture comprising at least about 25 mole % Ta2O5 and at least about 25 mole % Al2O3. One or more dopants or additives may be included in the starting mixture, as described hereinabove. In some embodiments, coating 204 may comprise at least about 90 mole % AlTaO4, and the balance may consist predominantly of Ta2O5 or Al2O3. In other embodiments, coating 204 may comprise more than 99 mole % AlTaO4.
Lesser amounts of dopants or additives may be added to the starting powder mix, according to the desired properties of the environmental and thermal barrier coating to be formed from the starting mix. Such dopants or additives may comprise oxides, or other compounds, or their precursors, of elements including Al, Ta, Cr, Hf, Ti, Zr, Mo, Nb, Ni, Sr, Mg, Si, and the rare earth elements including Sc, Y, and the lanthanide series of elements. In one embodiment, the starting mixture may comprise about 50 mole % Al2O3 and about 50 mole % Ta2O5.
The composition of the starting mixture provided in step 300 may be selected in order to achieve a particular CTE for the environmental and thermal barrier coating product, to provide a CTE “match” with a particular substrate to be coated. That is to say, the composition of the starting mixture, and hence that of the environmental and thermal barrier coating, may be chosen according to the application, or the component to be coated to achieve a suitable CTE match between the component/substrate and the coating deposited thereon. For example, the substrate to be coated may have a CTE in the range of from about 4×10−6° C.−1 to 5×10−6° C.−1, and the environmental and thermal barrier coating to be applied thereon may have a CTE in the same range.
The starting mixture may be mixed with a suitable solvent, e.g., an alcohol such as isopropanol. After mixing, the starting mixture may be dried to remove solvent (step 302) prior to firing.
Step 304 involves firing the starting mixture at an elevated temperature to form a reaction product. The firing step 304 may be performed in a furnace in the presence of air. Typically, the firing temperature is in excess of 1000° C., usually in the range of from about 1200 to 1600° C., and often in the range of about 1500° C. The firing step may be continued until reaction between Al2O3 and Ta2O5 in the starting mixture is complete.
Step 306 involves forming a particulate reaction product. For example, the reaction product may be broken up mechanically, e.g., by grinding and the like, to form particles of the reaction product. In one embodiment, a particular size range of the particulate reaction product is selected preparatory to depositing a layer of environmental and thermal barrier coating on the surface of a substrate/component. For example, a particulate reaction product formed in step 306 may be sieved to provide particles having a size range of from about 2 to 200μ, and more typically in the range of from about 5 to 100μ.
Step 308 involves depositing the reaction product on the substrate/component to form an environmentally and thermally protected component having an environmental and thermal barrier coating disposed on the surface of the substrate/component. Techniques for depositing solid coatings on a surface are well known in the art. For example, the environmental and thermal barrier coating may be applied to the surface of the substrate/component by a process such as plasma spray coating, dip coating, spray coating, sol-gel coating, chemical vapor deposition, physical vapor deposition, or electron beam physical vapor deposition.
The environmental and thermal barrier coating deposited in step 308 typically comprises at least 50 mole % AlTaO4, and may have a CTE in the range of 3.5×10−6° C.−1 to 5×10−6° C.−1. In some embodiments, the environmental and thermal barrier coating may comprise at least about 50 mole % AlTaO4 and the balance may consist essentially of Al2O3 or Ta2O5.
In some embodiments, an environmental and thermal barrier coating of the invention may comprise at least about 90 mole % AlTaO4. Such an environmental and thermal barrier coating may consist essentially of AlTaO4 and a metal oxide, such as Al2O3 or Ta2O5. For example, an environmental and thermal barrier coating of the invention may comprise at least about 90 mole % AlTaO4 and the balance may consist predominantly of Al2O3 or Ta2O5. In some embodiments, the Al2O3 or Ta2O5 component of the coating may be present in only trace amounts. An environmental and thermal barrier coating of the invention comprising about 90 mole % AlTaO4 may have a CTE in the range of from about 4×10−6° C.−1 to 5×10−6° C.−1. Such coatings typically provide a good CTE match between the coating and SiC-based substrates. In certain embodiments, an environmental and thermal barrier coating of the invention may comprise more than 99 mole % AlTaO4.
The CTE of the environmental and thermal barrier coating varies according to the mole % AlTaO4 present therein. Thus, the mole % AlTaO4 present in the environmental and thermal barrier coating may be varied according to the intended application, e.g., to obtain a suitable match between the CTE of the environmental and thermal barrier coating and the CTE of a substrate to be coated with the environmental and thermal barrier coating.
In an alternative approach to the method described with reference to
Three compositions were prepared from starting mixtures having 1, 10, and 25 mole % Al2O3, respectively, as the additive to Ta2O5. For each composition, about 1 Kg of a commercial β-Ta2O5 powder was mixed with commercial Al2O3 powder in isopropanol in a milling jar for about 2 hours. After drying the mixture, the resultant powder was sieved to classify the particle size in the range of about 5 to 100 microns in preparation for plasma spray coating. If the particle size was too fine, a calcining process was included to coarsen the particles.
A coating of each of the above compositions was then applied to coupons of silicon nitride and SiC—SiC composite substrates by an air-plasma spraying process, as follows. The silicon nitride coupons had an as-sintered surface on which the plasma coating was applied. (Alternatively, a grit-blasted machine surface could have been utilized.) The coupons were degreased, and preheated to about 1000° C. by either a torch or furnace. The powder was then fed into a high velocity, high temperature plasma air flow. The ceramic powder became molten and subsequently was quenched and solidified onto the coupons. The coating thickness varied from about 2 to 10 mils. (i.e., from about 50 to 250 microns).
The coated samples were then subjected to a thermal cycling regime wherein each sample was held in a furnace at about 2400° F. (1315° C.) for about 30 minutes, and then quickly removed from the furnace and quenched to about 200° C. in a stream of blowing air. The silicon nitride coupons coated with all three compositions survived about 100 hours and 200 cycles without spalling. X-ray diffraction showed the Ta2O5 remained in the β-phase.
Four compositions were prepared from starting mixtures having 3, 4, 6, and 10 mole % La2O3, respectively, as the additive to Ta2O5. In each batch, about 1 Kg of a commercial β-Ta2O5 powder was mixed with commercial La2O3 powder in isopropanol in a milling jar for about 2 hours. After drying the mixture, the resultant powder was sieved to classify the particle size in the range of from about 5 to 100 microns preparatory to plasma spray coating.
Each composition was applied to coupons of silicon nitride and SiC—SiC composite substrates which were prepared and coated essentially as described in Example 1. The coating thickness varied from about 2 to 10 mils. The coated samples were then subjected to cyclic furnace testing essentially as described in Example 1.
The silicon nitride samples coated with La2O3 in the range of 3, 4, and 6 mole % survived more than 1000 hours and 2000 cycles at 1315° C. The SiC—SiC samples coated with compositions having La2O3 at 4, 6, and 10 mole % survived more than 2,000 hours and 4,000 cycles. SEM examination showed needle-shaped La2O3— Ta2O5 precipitates on the surface of the coating. X-ray diffraction showed the existence of a second phase containing La, possibly the La2Ta12O33 phase according to the phase diagram. These needle-shaped second phases, which were distributed uniformly throughout the coating, increased the fracture toughness and mechanical strength of the coating. The second phase also increased the CTE of the coating, such that the CTE mismatch between the coating and the substrate was significantly reduced, resulting in improved coating life performance as shown by thermal cyclic testing.
A SiC—SiC coupon was coated with a composition prepared, from a starting mixture comprising about 50 mole % Al2O3 and 50 mole % Ta2O5, by a process essentially as described for Example 1. The coating prepared in this manner survived the thermal cycling regime of Example 1 (i.e., 1315° C. for about 30 minutes, and then quenched to about 200° C. in a stream of blowing air) for over 3000 hours without spalling. After the thermal cyclic testing, the coating was found to have been transformed to the AlTaO4 phase, with some residual Ta2O5.
Coated silicon nitride coupons having coating compositions of 10 mole % Al2O3/90 mole % Ta2O5 survived thermal cycling at 1315° C. for 500 hours and 1000 cycles without spalling. X-ray diffraction of the thermally tested coating showed that the predominant phase in the coating was β-Ta2O5 with some AlTaO4 phase.
Two coating compositions, 1 mole % Al2O3/99 mole % Ta2O5 and 5 mole % Al2O3/95 mole % Ta2O5, were heat-treated at 1450° C. for 2 hours. X-ray diffraction showed that the samples remained predominantly as β-Ta2O5 after the heat treatment. In contrast, pure β-Ta2O5 completely transformed to α-Ta2O5 after a heat treatment of 1 hour at 1450° C. Scanning electron microscopic (SEM) examination showed that the grain size for the 5 mole % Al2O3 coating composition fired at 1450° C. was significantly smaller than that of the pure Ta2O5 sample fired at the same temperature. The coating composition of 5 mole % Al2O3/95 mole % Ta2O5 was further heated at 1550° C. for 15 hours, and the Ta2O5 remained as the β-phase after the heat treatment.
Powders of two compositions, 7.5 mole % Al2O3/92.5 mole % Ta2O5 and 4 mole % La2O3/96 mole % Ta2O5, respectively, were pressed into cylindrically-shaped green parts and sintered at 1350° C. for 10 hours to form ingots for EB-PVD coating. Substrates of silicon nitride and SiC—SiC composites were loaded in a vacuum chamber and an electron beam was focused on an ingot of the material to be deposited. The substrate was preheated to 800-1200° C. to improve bonding with the deposited material. The electron bombardment resulted in high local heating on the coating material, which evaporated atomistically and condensed onto the substrate. Oxygen gas was then fed into the system to compensate for the loss of oxygen from Ta2O5 during the evaporation. The coating was chemically bonded to the substrate. The coated silicon nitride and SiC—SiC parts having a 50 micron thick coating survived the above described thermal cycling regime at 1315° C. for over 500 hours and 1000 cycles.
An AlTaO4 powder compound was prepared by mixing 500 g of powder containing 50 mole % Al2O3 and 50 mole % Ta2O5 in isopropanol in a milling jar for about 2 hours, drying the mixture, and firing the resultant powder in a furnace in air at 1500° C. for 1 hour. X-ray diffraction confirmed the complete reaction between Al2O3 and Ta2O5 powders to form AlTaO4. The reacted powder was broken down mechanically and sieved to classify the particle size to about 5 to 100 micron range in preparation for plasma spray coating (Example 8).
The resultant AlTaO4 powder prepared according to Example 7 was plasma-sprayed on a SiC—SiC composite substrate of about 2 cm×2 cm×1 mm to form a coating about 5 mils in thickness. The coated substrate was tested by thermal cycling at 1315° C. under the conditions described in Example 1. The coating survived 100 hours and 200 cycles without spallation and effectively protected the SiC—SiC substrate.
An AlTaO4 coating prepared according to the invention was examined by scanning electron microscopy to reveal a fined-grained microstructure (
It should be understood, of course, that the foregoing relates to preferred embodiments of the invention and that modifications may be made without departing from the spirit and scope of the invention as set forth in the following claims.
