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  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
  • C04B41/50—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials
  • C04B41/5022—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials with vitreous materials
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B64—AIRCRAFT; AVIATION; COSMONAUTICS
  • B64G—COSMONAUTICS; VEHICLES OR EQUIPMENT THEREFOR
  • B64G1/00—Cosmonautic vehicles
  • B64G1/22—Parts of, or equipment specially adapted for fitting in or to, cosmonautic vehicles
  • B64G1/226—Special coatings for spacecraft
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B64—AIRCRAFT; AVIATION; COSMONAUTICS
  • B64G—COSMONAUTICS; VEHICLES OR EQUIPMENT THEREFOR
  • B64G1/00—Cosmonautic vehicles
  • B64G1/22—Parts of, or equipment specially adapted for fitting in or to, cosmonautic vehicles
  • B64G1/52—Protection, safety or emergency devices; Survival aids
  • B64G1/58—Thermal protection, e.g. heat shields
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
  • C03C1/00—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels
  • C03C1/006—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels to produce glass through wet route
  • C03C1/008—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels to produce glass through wet route for the production of films or coatings
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
  • C04B35/16—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on silicates other than clay
  • C04B35/18—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on silicates other than clay rich in aluminium oxide
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  • C04B37/00—Joining burned ceramic articles with other burned ceramic articles or other articles by heating
  • C04B37/003—Joining burned ceramic articles with other burned ceramic articles or other articles by heating by means of an interlayer consisting of a combination of materials selected from glass, or ceramic material with metals, metal oxides or metal salts
  • C04B37/005—Joining burned ceramic articles with other burned ceramic articles or other articles by heating by means of an interlayer consisting of a combination of materials selected from glass, or ceramic material with metals, metal oxides or metal salts consisting of glass or ceramic material
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  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/009—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone characterised by the material treated
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  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
  • C04B41/81—Coating or impregnation
  • C04B41/85—Coating or impregnation with inorganic materials
  • C04B41/86—Glazes; Cold glazes
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
  • C03C2203/00—Production processes
  • C03C2203/20—Wet processes, e.g. sol-gel process
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  • C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
  • C04B2111/00474—Uses not provided for elsewhere in C04B2111/00
  • C04B2111/00982—Uses not provided for elsewhere in C04B2111/00 as construction elements for space vehicles or aeroplanes
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
  • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
  • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
  • C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
  • C04B2235/3201—Alkali metal oxides or oxide-forming salts thereof
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
  • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
  • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
  • C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
  • C04B2235/3205—Alkaline earth oxides or oxide forming salts thereof, e.g. beryllium oxide
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
  • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
  • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
  • C04B2235/44—Metal salt constituents or additives chosen for the nature of the anions, e.g. hydrides or acetylacetonate
  • C04B2235/447—Phosphates or phosphites, e.g. orthophosphate, hypophosphite
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  • C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
  • C04B2237/02—Aspects relating to interlayers, e.g. used to join ceramic articles with other articles by heating
  • C04B2237/04—Ceramic interlayers
  • C04B2237/06—Oxidic interlayers
  • C04B2237/062—Oxidic interlayers based on silica or silicates
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  • C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
  • C04B2237/02—Aspects relating to interlayers, e.g. used to join ceramic articles with other articles by heating
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  • C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
  • C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
  • C04B2237/32—Ceramic
  • C04B2237/34—Oxidic
  • C04B2237/343—Alumina or aluminates
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  • C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
  • C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
  • C04B2237/32—Ceramic
  • C04B2237/34—Oxidic
  • C04B2237/345—Refractory metal oxides
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  • C04B2237/00—Aspects relating to ceramic laminates or to joining of ceramic articles with other articles by heating
  • C04B2237/30—Composition of layers of ceramic laminates or of ceramic or metallic articles to be joined by heating, e.g. Si substrates
  • C04B2237/32—Ceramic
  • C04B2237/36—Non-oxidic
  • C04B2237/365—Silicon carbide

Definitions

• This invention relates to amorphous aluminosilicates stable at high temperature and more particularly relates to amorphous silica-rich aluminosilicates useful as coatings suitable for use at high to extreme temperatures.
• Ultra-High Temperature Ceramic UHTC
• material degradation from corrosion which may be accelerated by air, moisture, salt, or other contaminants, poses a serious problem in advanced materials used and being designed for air and space vehicles and other high performance applications.
• Ceramic refractory materials are used in extreme environments such as in glass making, metal production, and others uses which are prone to degradation from sintering (porosity goes down and so does the toughness) or environmental attack.
• a coating acts as a good barrier against sintering or gases that diffuse from external atmospheres, the life of the refractory may be extended significantly and this could save high costs for replacement and/or repair.
• High temperature resistant coatings also would be useful in protecting an article made from a suitable substrate such as a ceramic used in such applications.
• such materials may have engineered porosity (open and/or closed), which is useful in maintaining targeted performance in end-use applications.
• residual porosity in a bulk material is tailored for imparting lower weight while maintaining or improving toughness of an article.
• a beneficial coating system would not significantly decrease or degrade the engineered porosity (and thereby degrade performance characteristics based on such porosity) while protecting a substrate from corrosion/oxidation or other degradation under high temperature conditions such as in excess of 1500 0 C.
• a solid amorphous silica-rich aluminosilicate composition is stable at temperatures up to 1500 0 C or above and is capable of sustained use as a coating and a protective barrier material under high to extreme temperature conditions.
• Amorphous silica-rich aluminosilicates of this invention are stable at extreme temperatures of above 1450 0 C, above 1500 0 C, above 1550 0 C, or above 1600 0 C or above. These aluminosilicates are useful as protective coatings on substrates typically formed into useful articles, which are subject to extreme operating conditions such as experienced in aero or rocket engines. A protective coating typically is incorporated onto such substrate as protection against oxidative degradation of the substrate during operating conditions.
• An amorphous aluminosilicate material of this invention when applied and treated as a coating to a suitable substrate forms a thin, highly conformal film bonded onto the substrate with sufficient density and low through-thickness transport properties to enable the coating to serve as a highly effective surface sealant and environmental barrier for the underlying substrate.
• the nature of the 'glassy' amorphous aluminosilicate material of this invention renders it highly stable in extremely hot environments, and typically is stable and effective as an environmental barrier at temperatures of 1000 °C to 2000 °C.
• Substrates useful in this invention are capable of withstanding a temperature in excess of 1500 0 C without melting or destruction for a time sufficient to form a coating of this invention.
• suitable substrates are ceramic materials, although high melting metallic materials may be useful.
• Ceramics are materials having a glazed or unglazed body of crystalline or partly crystalline structure, or of glass, which body is produced from essentially inorganic, non-metallic substances and either is formed from a molten mass which solidifies on cooling, or is formed and simultaneously or subsequently matured by the action of the heat.
• Ceramics may be metal oxides such as oxides of aluminum (alumina) or zirconium (zirconia) or yttrium (yttria) or combinations thereof and non-oxides such as borides, nitrides, carbides, and suicides.
• Typical ceramics include refractory oxides, silicon carbide, titanium carbide, silicon carbide in carbon or silicon carbide fiber composites, and carbon-carbon fiber composites
• Suitable substrate materials which are used in extreme temperatures are those which are mechanically strong and stable, preferably lightweight, and durable at elevated temperatures. These materials include silicon carbide, silicon nitride, carbon, and composites made from these components, and other nitride, carbide, and oxide-based materials, which have good thermal properties and low weight. Typically, these materials when uncoated are not stable against prolonged contact with environments such as oxygen and/or water vapor at extreme operating temperatures.
• Examples of useful applications of coating materials of this invention include protection of turbine engine components which may be formed from SiC-SiC composites, particularly for materials known as Ml SiC composites, and protection of carbon-to-carbon (C-C), C-SiC, SiC-SiC and other materials used in rocket propulsion and thermal protection systems for space and air vehicles, and hypersonic vehicles.
• the coatings used for environmental protection on these substrate materials according to this invention permit operations under conditions, which are not otherwise possible or degrade very rapidly such that adequate service life is not feasible. Further, coatings of this invention are useful to extend operating lifetimes of current generation high temperature ceramic carbide, nitride, and oxide materials.
• Amorphous aluminosilicate materials of this invention typically may be used for coatings on substrates prone to high temperature oxidation, sintering (such as relevant to refractories), or water vapor degradation, such as refractories, silicon carbide, silicon nitride, or carbon, and various composite materials containing such materials, and include other oxide and metallic constituents, such as zirconium nitride or boron nitride in the form of surface hard coatings, as well as thermal barrier coating (TBC) materials such as stabilized zirconia, barium strontium aluminosilicates, and other thermal or combined thermal and environmental barrier coating (EBC) materials.
• Amorphous aluminosilicate-based coatings of this invention serve to add both performance and lifetime to systems to which they are applied as add-on materials, or such coatings may serve to determine new engine design and performance criteria.
• Amorphous aluminosilicates of this invention may be used as an environmental barrier coating on heat engine components to increase lifetime, efficiency, and thermal performance.
• heat engines include devices which transform heat energy into useful work, and include brayton cycle turbine engines, rocket engines, Carnot engines, rankine engines, and the like.
• An aspect of this invention is a coating capable of protecting an attached substrate against oxidative degradation at operating temperature in excess of 1450 0 C, preferably above 1500 0 C, and more preferably above 1550 °C or 1600 °C.
• Such coating material is characterized as a silica-rich substantially amorphous aluminosilicate.
• the Si/AI ratio of such aluminosilicate is greater than 4.
• Amorphous character of aluminosilicates useful in this invention is determined by X- ray diffraction (XRD) spectra.
• XRD X- ray diffraction
• a substantially amorphous material does not exhibit specific or sharp XRD peaks, which can be attributed to lattice parameters of a crystalline structure. These materials also may be described as a glass.
• An aluminosilicate composition of this invention is amorphous and remains substantially amorphous during extreme temperature operating conditions such as at temperatures of 1500 °C and above, and thus is stable at such temperatures.
• a coating formed from such amorphous aluminosilicate is stable (i.e. remains amorphous) and continues to act as an effective oxidative degradation barrier at such extreme conditions.
• aluminosilicate materials formed by combining aluminum and silicon oxides or sources thereof, which when heated to above 1400 °C or above 1500 °C transform into known crystalline phases depending upon parameters such as composition, temperature, and pressure.
• a conventional aluminosilicate composition having a Si/AI atomic ratio of 3 heated to 1500 °C will convert to a mixture of crystalline phases, including mullite and silica crystalline polymorphs (such as tridyamite or cristobalite), which are not microstructurally stable and will not function as a suitable diffusion barrier coating upon ceramic or metal substrates as an effective environmental barrier coating.
• Silica-rich aluminosilicates of this invention are microstructurally stable at extreme temperatures such as at 1500 °C as well as being capable of retaining barrier properties for extended time periods at elevated temperatures such as above 1000 0 C, 1200 0 C, 1500 0 C, or above. At these elevated temperatures silica-rich aluminosilicates are not transformed to crystalline forms and retain barrier properties.
• Silica-rich aluminosilicates of this invention typically have Si/AI atomic ratios above 4, preferably above 5, more preferably above 6, and may be above 7.
• Typical Si/AI ratios of aluminosilicates useful in this invention may range up to 15 or above and preferably range up to 12.
• Typical Si/AI ratios include 5-15, 6-10, 7-9, and 8-12.
• the amorphous aluminosilicate compositions of this invention typically are prepared from precursor solutions containing phosphorus, which is partially eliminated during a thermal treatment curing process, these compositions may contain residual amounts of phosphorus.
• Phosphorus content in typical aluminosilicate compositions of this invention range up to 8 mole percent of the total composition. Typical phosphorus content is 0.1 to 4 mole percent.
• Additional elemental components may be present the compositions of this invention such as zirconium or rare earth or alkali or alkaline earth metals (usually in the form of oxides) which impart enhanced thermal durability or chemical compatibility with substrates. Typical concentrations of such other components range up to 5 mole percent of the total composition.
• Many substrates useful as high performance materials have open-cell porosity, which can be measured as average pore volume. Because such porosity is important to the usefulness of such high performance materials (such as heat barriers), a coating that functions to protect the substrate against oxidative degradation, should not significantly affect the porous character of the substrate. Preferably there is less than 10 wt.% (preferably less than 2 wt.% and may be below 1 wt.%) change in pore volume after application of a coating of this invention.
• a superior coating is thin (typically less than 10 microns, preferably less than 5 microns, more preferably less than 1 micron) and is able to coat surfaces within pores of a substrate and protect all surfaces of a porous material against oxidative degradation at extreme operating conditions experienced by such substrate including temperature and moisture and contaminant concentrations.
• Typical coating thicknesses may range from 0.1 ⁇ m (100nm) to over 2000 ⁇ m (2mm).
• the aluminosilicate based coatings used in this manner provide protection from ambient oxygen and water vapor ingress to the underlying component, as well as sintering resistance, protecting from oxidation and chemical attack of the substrate and/or maintaining engineered porosity, allowing higher sustained service temperatures at constant lifetime, or constant service temperatures for longer performance lifetimes, or enabling the use of new generation materials that can be protected in aggressive high temperature environments, which are typified by the existence of temperatures above 1400°C or above 1500°C.
• Solid-state oxide powders mixed in ratios similar to those produced in coatings of this invention and heated to 1500 °C should not form a glassy amorphous aluminosilicate phase as demonstrated in this invention.
• a coating applied to a substrate and formed using a precursor solution according to this invention does show melting and glassification as described in this invention.
• the coating material of this invention conveniently may be prepared by heating a mixture of sources of alumina, silica, and phosphorus oxide under suitable conditions to a temperature at which the material melts and phosphorus-containing compounds substantially are eliminated as a vapor, which leaves a silica-rich aluminosilicate. Some residual phosphorus may remain after the material solidifies (typically less than 1 wt.%), which typically is incorporated into the silicate network. As the phosphorus content of the material decreases, the eutectic temperature at which the remaining aluminosilicate melts increases.
• amorphous aluminosilicate solidifies without a change in temperature and typically retains its solid form when subsequently taken to temperatures above 1550 °C.
• an aluminum-, silicon-, phosphorus-containing starting composition on a substrate is melted at a temperature typically in excess of 1450 °C (preferably 1500 °C and a solid coating is formed on the substrate, which coating remains solid and functions as an effective oxidation barrier coating at temperatures in excess of 1500 0 C.
• Amorphous aluminosilicate compositions of this invention may be made by forming a liquid-containing polymeric network (such as a sol-gel) containing oxidic species of aluminum and phosphorus to which silicon-containing components are incorporated, which is cured by heating to a temperature sufficient to melt and then to form a glass material.
• Sol-gel materials typically are formed in an aqueous or preferably a non-aqueous media such as an alcohol (typically a CrC 8 alcohol or mixtures thereof and preferably ethanol).
• solutions of an aluminum salt such as aluminum nitrate
• a phosphorus oxide such as phosphorus pentoxide (P 2 O 5 ) are combined in the presence of a silicon dioxide (silica) or source thereof.
• a silicon-containing source may be in a substrate (such as silicon carbide), from which silica is produced during formation of a coating, preferably additional silicon-containing material is incorporated into the aluminum- phosphorus-oxygen sol-gel, such as tetraethylorthosilicate (TEOS, Si(OC 2 H 5 ) 4 ).
• TEOS tetraethylorthosilicate
• the aluminum to phosphorous molar ratio in a precursor material may be more than 0.5, and typically is below 1 .5 and preferably is below 2.5.
• the source of silica may be a layer of silica deposited on a substrate such as a ceramic or metal on which a layer of aluminum-containing and phosphorous-containing material (such as a sol-gel). During formation of a coating or composition of this invention, silica may be incorporated into the sol-gel precursor from which the high silica aluminosilicate is formed.
• amorphous aluminosilicate-based material environmental barrier coatings may be applied through precursor solution routes, such as brush or spray painting, flowing the precursor solution onto the surface to be coated, using a dip coating process, thermally spraying, infiltration processing, or vapor deposition to various substrate articles.
• precursor solution routes such as brush or spray painting
• the precursor solution contained in the above-mentioned admixtures can be dried to a gel powder, which subsequently can be applied as a slurry layer by painting, dipping, or spraying.
• Examples of articles on which coatings of this invention may be applied include thermal protection systems used in airframes for space and air transportation, hot exhaust structures in turbine or rocket propulsion systems, turbine engine blades, vanes, shrouds, or combustion housing, and other high temperature components such as cowls, thruster cones and plugs, and the like, rocket thrust chamber components, or combustion engine piston heads and walls.
• thermal protection systems used in airframes for space and air transportation, hot exhaust structures in turbine or rocket propulsion systems, turbine engine blades, vanes, shrouds, or combustion housing, and other high temperature components such as cowls, thruster cones and plugs, and the like, rocket thrust chamber components, or combustion engine piston heads and walls.
• porous refractories are used in metal production, such as in steel plants, in which temperatures above 1300 -1500 °C are used.
• refractory uses in which silica already is present contacting such silica with an aluminophosphate solution formulation may produce a silica-rich aluminosilicate material as described in this invention.
• a polymeric network e.g. a sol-gel initial composition containing Si-Al-O-P structures melts at 1500 °C or above, while phosphorus compounds are substantially eliminated as vapors. With loss of phosphorus, the melting temperature of the remaining aluminosilicate increases and such aluminosilicate solidifies into an amorphous solid state.
• a liquid-containing glassy network such as a sol-gel composition containing oxides of aluminum, phosphorus, and silicon is dried to form a dried precursor typically at elevated temperature (usually 100 to 200 °C) or reduced pressure to remove volatile organics, and then cured by heating to at least the melting temperature of the resulting mixture for a time sufficient to form a flowable fluid.
• a liquid-containing glassy network such as a sol-gel composition containing oxides of aluminum, phosphorus, and silicon is dried to form a dried precursor typically at elevated temperature (usually 100 to 200 °C) or reduced pressure to remove volatile organics, and then cured by heating to at least the melting temperature of the resulting mixture for a time sufficient to form a flowable fluid.
• Such fluid state may form a film or layer on a substrate having a substantially uniform (typically ⁇ 10% variation) composition throughout the layer with excellent conformality to yield a smooth surface layer.
• a relatively smooth layer is obtained which may also provide beneficial low friction and aerodynamic flow properties.
• Typical curing temperatures useful in this invention are above 1450 °C, preferably 1500 °C or above, and may range up to above 1600 °C.
• a typical range of curing temperatures is between 1475 and 1650 0 C, and typically is 1500 to 1600 0 C.
• a suitable curing temperature is below the disintegration temperature of the materials.
• a suitable curing time is about one hour and typically may range up to 3 hours or more. Drying and curing may be conducted in one continuous step.
• an amorphous aluminosilicate coating may be applied to a substrate by surface heating a layer formed from a dried precursor containing oxides of aluminum, phosphorus, and silicon.
• the surface layer is heated to a suitable curing temperature without excess heating of the substrate, thereby permitting substrates with relatively low thermal stability.
• metal substrates such as steel or titanium or superalloy or other nickel- based alloys may not be stable under processing conditions required to form the aluminosilicate material as prescribed above.
• Non-metallic substrates may be used such as plastic materials.
• An example of a surface heating technique is laser heating.
• Amorphous aluminosilicate compositions and coatings formed from such compositions are stable at a temperature of 1500 °C. That is, the aluminosilicate material does not transform to a crystalline form such as mullite (or related compositions within the alumina-silica two-phase composition system) at that temperature. Suitably stable coating materials of this invention do not spall or flake from an adhered substrate at operating temperature of 1500 °C.
• coating materials of this invention act as a hermetic barrier to oxygen and resists oxidative corrosion of the substrate.
• Preferable solid coating materials of this invention are suitably stable under extreme conditions of temperature (>1500 °C, preferably >1600 0 C) together with presence of moisture and contaminants such as salt.
• Minor amounts of additional materials may be incorporated into the amorphous aluminosilicate compositions and coatings of this invention. These materials may be considered as dopants and include metals such as sodium, zirconium, lanthanum, and the like (typically in the form of oxides). Such dopants can be utilized to tailor the melting temperature and to suit specific substrate properties.
• An aspect of this invention is used as a health monitoring coating on heat engine components to increase the overall system performance, efficiency, and reliability.
• An amorphous aluminosilicate material of this invention can be applied to heat engine component, with the primary application method targeted at infiltration of the coating material into the internal porous surfaces of high temperature exposed substrate materials.
• This material may be formulated with a small amount of a doping agent that is detectable through non-destructive methods, and also has a characteristic that changes as a function of exposure time to temperatures typically above 1400°C.
• Doping agents used in this manner are readily recognized by those skilled in the state of the art, and are typically diffusion based indicators with time at elevated temperature, such that the concentration gradient as a function of dopant location, in this case, typically depth within the heat engine porous substrate structure, can be conveniently used to determine the thermal aging processes that are occurring in real time to the heat engine substrate and overall component.
• Dopants that display characteristics of this nature are typically highly mobile metallic ions, which are generally located in the transition metal series, and historically include chromium (Cr), europium (Eu), erbium (Er), cerium (Ce), and neodymium (Nd).
• cerium, europium, and neodymium are the florescent properties which they possess, enabling easier concentration gradient detection using non-destructive methods.
• these dopant elements may be incorporated into coatings on a substrate such as an engine part.
• coatings are applied through an infiltration process.
• the coatings containing a dopant element may be used to monitor the thermal aging profile ("health profile") of a coated engine component, which may be used to schedule preventative maintenance, avoid premature part replacement, and the like to increase engine performance, reliability, and efficiency.
• suitable substrates may be joined together using silica-rich, amorphous aluminosilicate described in this invention as an intermediate adhesion layer between such substrates.
• precursor solutions may be applied to one or more surfaces of the substrates, such surfaces placed together, and the resulting combination cured at temperatures and pressures, which permit melting of the aluminum-silicon-phosphorus-containing material to form an intermediate silica-rich, amorphous aluminosilicate layer bonded to both surfaces.
• an aluminum-silicon-phosphorus precursor solution of this invention may be applied to a suitable substrate and dried, but not cured.
• Such a coated substrate may be incorporated into a component, which may be subject to high temperature conditions. If such conditions become higher than the melting temperature of the uncured coating, the coating will be transformed into a silica-rich, amorphous aluminosilicate as described in this invention, and will become a protective barrier coating to the substrate.
• Example 1 Aspects of the invention are illustrated but not limited by the following examples. Example 1
• An aluminosilicate glass material was formed on bulk silicon carbide (SiC) coupons.
• a low viscosity sol-gel precursor solution was prepared by adding 37.51 grams of aluminum nitrate nonahydrate to 250 milliliters of ethanol. In a separate container, 3.55 grams of phosphorus pentoxide were dissolved in 250 milliliters of ethanol. The two solutions were mixed and 1 1 .2 milliliters of 98% tetraethyl orthosilicate were added with further mixing, and the solution then was stirred under reflux for 3 hours.
• the SiC substrate was removed from the solution with a controlled retraction velocity of 1 cm/second and resulted in a wet film on the surface of the SiC substrate.
• the film was dried and then cured in air in an oven by ramping the temperature at 10°C/minute to 1500°C, holding at 1500 °C for 1 hour, and then cooled to room temperature at 10°C/minute.
• the result was an approximately two micrometer thick film of primarily aluminosilicate glass formed having a Si/AI ratio of 5 and containing 1 wt% phosphorus.
• An aluminosilicate glass material formed on SiC using a low viscosity sol- gel precursor solution was prepared according to Example 1 .
• the aluminosilicate glass was formed by placing about 2 milliliters of the precursor solution onto a SiC substrate coupon. While the solution was still wet, the substrate was spun at 7000 rpm for 10 seconds, creating a thin wet film which was dried at 120 9 C for 5 minutes. The film was then treated under ambient conditions in air using the procedure described in Example 1 . The result was a approximately two micrometers thick film of aluminosilicate glassy material on the silicon carbide substrate.
• Aluminosilicate glass material was formed on alumina (99.5% pure AI 2 O 3 having a density of 3.9 g/cc) using a precursor solution.
• the precursor solution was prepared by adding 37.51 grams of aluminum nitrate nonahydrate to 166 milliliters of ethanol. In a separate container, 3.55 grams of phosphorus pentoxide was dissolved in 164 milliliters of ethanol. The two solutions were mixed and 169.2 milliliters of 98% tetraethyl orthosilicate was added with further mixing. The solution then was stirred overnight for about 16 hours.
• the precursor solution was applied to an alumina substrate by immersing the substrate in the solution for one minute and removing the sample with a controlled retraction velocity of 1 .5 cm/second. Following removal from the precursor solution, the sample and resulting wet film were dried 120°C for 10 minutes. The dipping and drying procedure was repeated three times on each sample. Following the dipping/drying steps, the sample was cured in air by ramping at 10°C/minute to 1500°C, held at that temperature for one hour, and then cooled to room temperature at 10°C/minute. The result was a glassy aluminosilicate materia on the surface of the AI 2 O 3 substrate.
• Example 4 A precursor solution was prepared by adding 34.51 grams of aluminum nitrate nonahydrate to 173 milliliters of ethanol. In a separate container, 6.55 grams of phosphorus pentoxide was dissolved in 174 milliliters of ethanol. The two solutions were mixed and 152.7 milliliters of 98% tetraethyl orthosilicate was added with further mixing. The solution was then stirred overnight, about 16 hours. The precursor solution was applied to an alumina substrate by dipping/submerging the substrate in the solution for one minute and removing the sample with a controlled retraction velocity of 1.5 cm/second. Following removal from the precursor solution, the sample and resulting wet film were dried 120°C for 10 minutes.
• the dipping and drying procedure was repeated three times on each sample. Following the dipping/drying steps, the sample was cured in air by ramping at I CO/minute to 1500 9 C where it was held for one hour and then cooled to room temperature at 10°C/minute. The result was a glassy aluminosilicate material on the surface of the AI 2 O 3 substrate.
• a precursor solution was prepared by adding 36.30 grams of aluminum nitrate nonahydrate to 170 milliliters of ethanol. In a separate container, 18.31 grams of phosphorus pentoxide was dissolved in 170 milliliters of ethanol. The two solutions were mixed and a colloid formed within a few minutes of initial mixing resulting in a hazy solution. 160.1 milliliters of 98% tetraethyl orthosilicate was then added with further mixing. After one hour of stirring, the solution returned to clear and white precipitate was present. The solution was then stirred overnight for about 16 hours.
• the precursor solution was applied to an alumina substrate by dipping/submerging the substrate in the solution for one minute and removing the sample with a controlled retraction velocity of 1 .5 cm/second. Following removal from the precursor solution, the sample and resulting wet film were dried 120°C for 10 minutes. The dipping and drying procedure was repeated three times on each sample. Following the dipping/drying steps, the sample was cured in air by ramping at I CO/minute to 1500°C where it was held for one hour and then cooled to room temperature at 10°C/minute. The result was a glassy aluminosilicate material on the surface of the AI 2 O 3 substrate.
• a precursor solution was prepared by adding 37.51 grams of aluminum nitrate nonahydrate to 170 milliliters of ethanol. In a separate container, 9.46 grams of phosphorus pentoxide was dissolved in 170 milliliters of ethanol. The two solutions were mixed and 160.0 milliliters of 98% tetraethyl orthosilicate was added with further mixing. The solution was then stirred overnight, about 16 hours.
• the precursor solution was applied to an alumina substrate by dipping/submerging the substrate in the solution for one minute and removing the sample with a controlled retraction velocity of 1.5 cm/second. Following removal from the precursor solution, the sample and resulting wet film were dried 120°C for 10 minutes.
• the inventive aluminosilicate glass material was also formed as a bulk powder.
• a precursor solution was prepared by adding 36.30 grams of aluminum nitrate nonahydrate to 170 milliliters of ethanol. In a separate container, 18.31 grams of phosphorus pentoxide was dissolved in 170 milliliters of ethanol. The two solutions were mixed and a colloid formed within a few minutes of initial mixing resulting in a hazy solution. 160.1 milliliters of 98% tetraethyl orthosilicate was then added with further mixing. After one hour of stirring the solution returned to clear and white precipitated was present. The solution was then stirred overnight, about 16 hours.
• Example 8 Approximately 15 milliliters of the solution was then dried at 120°C for 16 hours to form a gel powder. This gel powder was placed on a zirconia-containing substrate and cured in air by ramping at 10°C/minute to 1500°C where it was held for one hour and then cooled to room temperature at 10°C/minute. The result was a transparent and glassy powder of aluminosilicate material.
• Example 8
• a solution was prepared by adding 37.51 grams of aluminum nitrate nonahydrate to 170 milliliters of ethanol. In a separate container, 9.46 grams of phosphorus pentoxide was dissolved in 170 milliliters of ethanol. The two solutions were mixed and 160.0 milliliters of 98% tetraethyl orthosilicate was added with further mixing. The solution was then stirred overnight, about 16 hours. Approximately 2 milliliters of the precursor solution was then placed on a zirconia-containing substrate using a dropper. The wet solution was cured in air by ramping at 10°C/minute to 1500°C where it was held for one hour and then cooled to room temperature at 10°C/minute. The result was the formation of aluminosilicate glassy material on the ZrO 2 substrate.
• the oxidation protection provided by the aluminosilicate glassy material described in this invention as a coating on SiC was determined based on oxide scale thickness.
• a coating of the inventive aluminosilicate glass was formed on SiC as described in Example 1 .
• An aluminosilicate glass coated SiC substrate and an uncoated SiC substrate alongside each other were both heated in air to 1500°C at a ramp rate of 10°C/minute.
• the samples were held at 1500°C for 42.5 hours and then cooled to room temperature at 10°C/minute.
• the samples were mounted in epoxy in cross-section and polished to a finish of 0.1 microns. Scanning electron microscopy was used to determine the thickness of the oxide scales that formed on the coated and uncoated samples. These scales were measured to be 7 microns and 70 micron for the coated and uncoated samples, respectively indicating a 10-fold improvement in oxidation resistance of SiC as a result of the presence of the inventive aluminosilicate glass coating material
• aluminosilicate glassy coating material of this invention on surface roughness of a substrate to which it is applied was examined.
• An aluminosilicate glass coating of an amorphous aluminosilicate material was formed on a SiC coupon substrate as described in example 1 .
• the root mean squared (RMS) surface roughness value of the coated SiC coupon, alongside an otherwise identical uncoated SiC substrate, were measured by atomic force microscopy (AFM) to be 2.7 nanometers and 1 micron, respectively. This indicates almost an order of magnitude improvement in the surface roughness due to application of the aluminosilicate glassy material coating.

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