Patent Application
20210404045
This disclosure relates to a method of applying a barrier spray coating.
Air plasma-sprayed (APS) thermal barrier coatings (TBC) or environmental barrier coating (EBC) made from yttria-stabilized zirconia (YSZ) and gadolinium zirconium oxide are typically used to reduce the temperature of cooled turbine and combustor components. Additionally, these materials may also be used as abradable seal materials on cooled turbine blade outer air seals (BOAS). In these applications, there are several degradation and failure modes.
Conventional APS coatings are formed by a buildup of molten ceramic particles that impact the substrate and form splats. The adhesion of the splats is dependent on the interface formed on impact. Typically, this splat interface bonding is weak and results in low fracture toughness of the coating. This leads to poor erosion and cyclic performance during service.
Due to the high temperature environment, surface sintering and shrinkage as well as thermal cycling and gradient related stresses cause cracking of the coating. These cracks generally begin at the free surface, propagate through the thickness, then branch and cause delamination just above a bond coat on the component substrate. Also, impingement by particles can erode the coating, particularly on blade and vane leading edges. Erosion may also be evident on regions with lower impact angles, such as blade outer air seals (BOAS). Finally, gross coating stresses and coating cracking can be induced by the stresses related to thermal cycling in the presence of molten contaminants such as calcium-magnesium alumino-silicate (CMAS).
In one exemplary embodiment, a method of manufacturing a fiber reinforced coating. The method includes providing a substrate and plasma spraying a ceramic matrix having fibers encapsulated in a precursor material onto the substrate.
In a further embodiment of the above, the substrate is a metallic substrate.
In a further embodiment of any of the above, the metallic substrate is a nickel superalloy.
In a further embodiment of any of the above, the plasma spraying is air plasma spraying.
In a further embodiment of any of the above, the plasma spraying is suspension plasma spraying.
In a further embodiment of any of the above, the method includes the step of applying a bond coating onto the substrate prior to performing the plasma spraying step. The plasma spraying step includes adhering the ceramic matrix to the bond coat.
In a further embodiment of any of the above, the precursor material contains zirconium.
In a further embodiment of any of the above, the precursor material is at least one of zirconium sulfate, zirconium acetate and zirconia salts.
In a further embodiment of any of the above, the precursor material is an organic polymer.
In a further embodiment of any of the above, the precursor material is at least one of polyvinyl acetate, acrylic, an organo-metallic material and an organic binder.
In a further embodiment of any of the above, the method includes the step of plasma spraying additional ceramic matrix with fibers encapsulated in a precursor material onto a prior ceramic matrix layer.
In a further embodiment of any of the above, the method includes the step of heat treating the coating prior to the additional ceramic matrix plasma spraying step.
In a further embodiment of any of the above, the method includes the step of heat treating the coating subsequent to the additional ceramic matrix plasma spraying step.
In a further embodiment of any of the above, the plasma sprayed ceramic matrix provides a thermal barrier coating and includes the step of heat treating the thermal barrier coating to provide a ceramic matrix composite.
In a further embodiment of any of the above, the heat treating step includes pyrolyzing the precursor material.
In a further embodiment of any of the above, the heat treating step includes calcinating the precursor material.
In a further embodiment of any of the above, the heat treating step includes reducing at least a number or size of voids in the thermal barrier coating.
In a further embodiment of any of the above, the fibers have an aspect ratio of greater than 10:1.
In a further embodiment of any of the above, the fibers are ceramic.
In a further embodiment of any of the above, the fibers are carbon.
The disclosure can be further understood by reference to the following detailed description when considered in connection with the accompanying drawings wherein:
The embodiments, examples and alternatives of the preceding paragraphs, the claims, or the following description and drawings, including any of their various aspects or respective individual features, may be taken independently or in any combination. Features described in connection with one embodiment are applicable to all embodiments, unless such features are incompatible.
The disclosed thermal spray method increases the toughness of the thermal barrier coating. As a result, durability to thermally induced spallation and large particle erosion is improved.
A method of manufacturing a fiber reinforced coating (for example, thermal barrier coating or environmental barrier coating) is shown schematically at 10 in
Fibers, which may be ceramic or carbon, for example, are encapsulated with a precursor material, as indicated at block 16. The fibers have a higher melting temperature than the precursor material. The fibers have an aspect ratio of length to width of greater than 10:1. The encapsulated fibers are plasma-sprayed onto the substrate, as indicated at block 18. The plasma spraying may be air or suspension plasma spraying. The embedded fibers are substantially oriented within the plane of the coating due to the deposition process and provide increased toughness relative to through thickness cracking. Due to coating roughness and local variation in the deposition process, the fibers may vary in orientation in an amount of about plus and minus 30 degrees from the coating plane. This out of plane fiber orientation component contributes to increased toughness relative to planar cracking.
The plasma sprayed coating is formed by a buildup of molten ceramic particles that impact the substrate and form splats. The fracture toughness of the splat boundary is increased by incorporation of fibers during application of the coating to bridge the boundary. The fiber bridges the cracks or splat boundaries and shields them from further stresses through a process known as crack wake bridging. The result is a coating where the splats are more adherent and the coating itself has a higher fracture toughness. Erosion resistance also increases due to improved splat-to-splat adherence.
Fiber structure is maintained, and deposition efficiency achieved, by encapsulating the fibers in a relatively, to the fibers, low melting point material, then co-spraying them with the ceramic matrix material. Encapsulation is with a fugitive or precursor material, the composition and thickness of which influence the deposition and interfacial bonding with the ceramic matrix. Examples of precursors and fugitive binders that may be used individually or in mixtures include zirconium based materials, for example, zirconium sulfate, zirconium acetate, other zirconia salts, or organic polymers, such as PVA, acrylics, organo-metallic compounds and organic binders. The spray process is designed to melt or soften the encapsulation material while substantially leaving retaining the morphology and composition of the fibers.
The ceramic coating may be applied by APS in multiple layers, as indicated a block 20. At this point, the full toughening effect of the fibers may not be realized. The coating and precursor material is then heated to achieve the desired bonding between the fibers and matrix material of the coating. The ceramic coating may be heated during deposition of each layer or once all the ceramic matrix layers have been applied.
Depending on the cladding material and part surface temperature during spray, the decomposition of this layer will affect the adhesion of the next layer of the coating. One example process is that a coating of zirconia acetate is pyrolized and calcined once the fiber adheres to the part surface at approximately 700° C. (1290° F.). Upon return to the spray position with each passage under the torch, the previously deposited fibers become embedded within the coating. The conversion layer on the fibers is not sintered to full density, and can thereby be manipulated to provide the desired bond strength to the matrix coating.
This method may be used in conjunction with conventional powder feed APS or with suspension plasma spray (SPS). With SPS, this method may provide a means to produce fiber or whisker reinforced ceramic composites. The fine particle deposit of SPS may provide a matrix that can be sintered and densified while retaining the fiber reinforcement character. The result is a structure similar to SiC—SiC composites.
Post-calcination includes, for example, a 50% dense fine particulate or web material within the space originally filled with precursor. A post-calcinated coating retains the porosity, micro-crack and splat boundary characteristics of the as-sprayed matrix.
It should also be understood that although a particular component arrangement is disclosed in the illustrated embodiment, other arrangements will benefit herefrom. Although particular step sequences are shown, described, and claimed, it should be understood that steps may be performed in any order, separated or combined unless otherwise indicated and will still benefit from the present invention.
Although the different examples have specific components shown in the illustrations, embodiments of this invention are not limited to those particular combinations. It is possible to use some of the components or features from one of the examples in combination with features or components from another one of the examples.
Although an example embodiment has been disclosed, a worker of ordinary skill in this art would recognize that certain modifications would come within the scope of the claims. For that reason, the following claims should be studied to determine their true scope and content.
This application is a continuation of U.S. application Ser. No. 15/033,153 filed Apr. 29, 2016 which is a U.S. National phase of PCT Application No. PCT/US2014/062387 filed Oct. 27, 2014 which claims priority to U.S. Provisional Application No. 61/904,838, which was filed on Nov. 15, 2013 and is incorporated herein by reference.
| Number | Date | Country | |
|---|---|---|---|
| 61904838 | Nov 2013 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 15033153 | Apr 2016 | US |
| Child | 17471832 | US |
