CA2076091A1 - Superalloy component with dispersion-containing protective coatings, and method of preparation - Google Patents
Superalloy component with dispersion-containing protective coatings, and method of preparationInfo
- Publication number
- CA2076091A1 CA2076091A1 CA 2076091 CA2076091A CA2076091A1 CA 2076091 A1 CA2076091 A1 CA 2076091A1 CA 2076091 CA2076091 CA 2076091 CA 2076091 A CA2076091 A CA 2076091A CA 2076091 A1 CA2076091 A1 CA 2076091A1
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- CA
- Canada
- Prior art keywords
- coating
- superalloy
- component
- percent
- nickel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Abandoned
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/12—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the method of spraying
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/18—After-treatment
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Coating By Spraying Or Casting (AREA)
Abstract
SUPERALLOY COMPONENT WITH DISPERSION-CONTAINING
PROTECTIVE COATING, AND METHOD OF PREPARATION
ABSTRACT OF THE DISCLOSURE
A coated superalloy component includes a substrate article formed of a superalloy and an adherent coating over the substrate. The coating is a nickel-base superalloy containing at least about 0.3 volume percent or more of a dispersed oxide of yttrium, hafnium and/or a rare earth, and, preferably, grain boundary strengthening elements such as carbon, zirconium, and boron. The oxide dispersoids improve the performance of the coating in service, reducing the incidence failures due to thermal fatigue, oxidation, and corrosion damage. The dispersoid-containing coating may be formed by directly depositing the oxide-containing coating, or by depositing a metallic coating and then forming the dispersoids by subsequent heat treatment.
PROTECTIVE COATING, AND METHOD OF PREPARATION
ABSTRACT OF THE DISCLOSURE
A coated superalloy component includes a substrate article formed of a superalloy and an adherent coating over the substrate. The coating is a nickel-base superalloy containing at least about 0.3 volume percent or more of a dispersed oxide of yttrium, hafnium and/or a rare earth, and, preferably, grain boundary strengthening elements such as carbon, zirconium, and boron. The oxide dispersoids improve the performance of the coating in service, reducing the incidence failures due to thermal fatigue, oxidation, and corrosion damage. The dispersoid-containing coating may be formed by directly depositing the oxide-containing coating, or by depositing a metallic coating and then forming the dispersoids by subsequent heat treatment.
Description
2 ~7 rJOC3~ 13DV-8682 SUPERALLOY COMPONENT WITH DISPERSION-CONTAINING
PROTECTIVE COATING, AND METHOD OF PREPARATION
CROSS REFERENCE TO RELATED_APPLICATION
This application is related to concurrently filed and commonly assigned application Serial No. (Attorney Docket 13DV-8335), the disclosure of which is hereby incorporated by referen~e.
BACKGROUND O~ THE INVENTION
This invention relates to the protection of superalloys to be used at elevated temperatures, and, more particularly, to superalloy articles protected by coatings.
This invention was made with Government support under Contract No. N-0019-80-C-0017 awarded by the Naval Air Propulsion Center.
One of the most demanding materials applications in current technolo~y is found in ths hot-stage components used in aircraft jet engines. The higher the operating temperature of an engine, the greater its efficiency, and the more power it can produce from each gallon of fuel.
There is therefore an incentive to operate such engines at as high a te~perature as possible. The primary limitation on the operating temperatures of a jet engine is the material-~ used in the hottect regions of the engine, such as gas turbine blades and vanes.
2~7~oQ~1 13DV-8682 There has been much research to develop materials that can be used in high temperature engine applications. The currently most popular and successful of such materials are the nickel-base superalloys~ which are alloys of S nickel with additions of a number of other elements such as, for example, chromium, cobalt, aluminum, and tantalum.
The compositions of these superalloys are carefully engineered to maintain their strength and other mechanical properties even during use at the high temperature of engine operation, which is in the neighborhood of 2000-F
or more.
The materials used in the jet engines must operate at high temperatures, but additionally are subjected to oxidative and corrosive conditions. Oxidation of materials such as nickel and many of its alloys is rapid at engine operating temperatures. The engine components are also subjected to corrosive attack by chemicals in the burned fuel, as well as ingested agents such as salt that might be drawn into the engine as it operates near an ocean. The materials that have the best mechanical properties at high te~peratures often are not as resistant to oxidation and corrosion as other materials, and there is an ongoing search for materials that offer a compromise between the best mechanical properties and the best oxidation and corrosion resistance.
High operating temperatures can also be achieved by other techniques not related directly to the alloy compositions used in the components. For example, control of grain structures and use of single crystals can result in improved properties. Cooling passages may be provided in the components, and cooling air passed through them to lower their actual operating temperature.
2 ~7 rj~ 9~ 13DV-8682 In another approach which is the primary focus of the present invention, a thin protective metallic coating is deposited upon the component. The coatinq protects the substrate from oxidation and corrosion damage. The coating must be adherent to the superalloy substrate and must remain adherent through many cycles of heating to the operating temperature and then cooling back to a lower temperature when the engine is idling or turned off.
Because materials of different compositions have different coefficients of thermal expansion, differential strains develop between the coating and the component.
To accommodate the strains imposed by the thermal cycling, the thin coatings have been made of materials that are relatively weak and ductile. Such a coating can plastically deform either in tension or compression to remain adherent to the surface of the substrate as the substrate is heated and cooled. Most coatings for nickel-base superalloys have been made of alloys of nickel, chromium, aluminum, and yttrium, which are termed NiCrAlY alloys, and nickel, cobalt, chromium, aluminum, and yttrium, which are termed NiCoCrAlY alloys. The term MCrAlX, where M represents nickel, cobalt, iron or some combination thereof and X represents yttrium, hafnium, tantalum, silicon or some combination thereof, is a widely used generic description for this type of alloy. While such alloys contain many of the same elements as the substrate materials, the proportions of those elements have been adjusted to enhance oxidation and corrosion resistance rather than mechanical properties. They therefore lack the strength to serve as the structural components themselves, but serve well as protective coatings.
2~7 ~ 1. 13DV-8682 There remains an ongoing need for improved metallic coating materials that can protect the substrates for extended periods of time, against oxidation and corrosion damage. The present invention fulfills this need, and further provides related advantages.
SUMMARY OF T~E INVENTION
The present invention provides a class, and specific alloy compositions, of metallic coating materials useful in protecting high-temperature superalloys. The compositions are compositionally and structurally compatible with the superalloy substrates, protect against oxidation and corrosion damage, and remain adherent, crack-free, and protective for greater periods of time than prior metallic superalloy coatings. The coatings are formulated and applied by conventional techniques~
In accordance with the invention, a coated superalloy component comprises a substrate article formed of a superalloy and an adherent coating over the substrate.
The coating is a nickel-base superalloy additionally containing at least about 0.3 ~olume percent of dispersed particles of an oxide of yttrium, hafnium, a rare earth, or combinations thereof.
It is well known to provide yttrium and/or rare earth elements in superalloys and superalloy coatings to improve their resistance to oxidation. However, these elements are present in s~all amounts or are provided in such a compositional and formation context that a high fraction of their oxide dispersoids is not formed. The approach of the present invention intentionally provides a high fraction of dispersoids distributed in such a way as to improve the properties of the coating.
2~
The coatings of the invention represent a significant departure from conventional thinking in the metallic coating area. Heretofore, metallic superalloy coatings were made weak and ductile, to accommodate the strains imposed by the substrate as the component was repeatedly heated and cooled. The coating is deformed in complex planar strain conditions that are dictated by the deformation of the more massive substrate. The coating must deform plastically and/or in creep to a new set point during the temperature and load cycling of the engine, and a weak coating was deemed most desirable to operate under these constraints.
It was observed in the research underlying this invention that metallic coatings tend to fail in thermal fatigue, and that the weak coatings did not offer sufficient mechanical resistance to such fatigue failure.
The present invention therefore provides an oxide-dispersion containing coating, a coated article, and a method for preparation thereof. The oxide-containing coating is more resistant to thermal fatigue damage than the NiCrAlY or NiCoCrAlY alloys conventionally used as metallic coating materials, without sacrificing oxidation and corrosion resistance.
The present invention provides an important advance in the art of superalloys, as well as a departure from the conventional thought in the field. The coating of the invention permits a controllable improvement to the properties of the coating through selection of the fraction of dispersoid, while retalning the chemical components that lead to oxidation and corrosion resistance. Other features and advantages of the invention will be apparent from the following mor~
2 ~ Q ~1 13DV-8682 detailed description of the preferred embodiment, taken in conjunction with the accompanying drawings which illustrate, by way of example, the principles of the invention.
BRIEF DESCRI~TION OF THE DRAWINGS
Figure 1 is a perspective view of a turbine blade having a metallic protective coating; and Figure 2 is an enlarged sectional view of the turbin~
blade of Figure 1, taken along lines 2-2.
DETAILED ~ESCRIPTION OF THE PREFERRED EMBODIMENT
The coating of the invention is pre~erably used with nickel-base superalloys, in applications such as a jet engine gas turbine blade 10 illustrated in Figure 1, or a gas turbine vane which has a similar appearance in -relevant respects. The blade 10 may be formed of any suitable superalloy such as Rene' 80, a well known nickel-base superalloy which has a nominal composition, in weight percent, of 14 percent chromium, 9.5 percent cobalt, 5 percent titanium, 4 percent tungsten, 4 percent molybdenum, 3 percent aluminum, 0.17 percent carbon, 0.06 percent zirconium, 0.015 percent boron, and the balance nickel. Another example is a more advanced nickel-base superalloy such as Rene' N4, having a composition, in weight percent, of 7.5 cobalt, 9.O chromium, 3.7 aluminum, 4.2 titanium, 1.5 percent molybdenum, 4.0 percent tantalum, 6.0 percent tungsten, 0.5 percent niobium, and balance nickel. These substrate superalloys are presented as exa~ples, and the coatings are not limited for use with these substrates.
2~ ~rQ91 Such a blade 10 includes an airfoil section 12 against which hot combustion gases are directed when the engine operates, and whose surface is subjected to severe oxidation and corrosion attack during service. If the surface of the airfoil section 12 is not protected against oxidation and corrosion in some fashion, it will normally last at most only a-few cycles of operation. The airfoil section 12 is anchored to a turbine dis~ (not shown) through a root section 14. In some cases, cooling passages 16 are present in the airfoil section 12, through which cool bleed air is forced to remove heat from the blade 10. The blade 10 is normally prepared by a casting and solidification procedure well known to those skilled in the art, such as investment casting or, more preferably, directional solidification or single crystal growth.
According to the present invention, the airfoil section 12 is protected by a metallic protective coating 20, as illustrated in detail in Figure 2, which depicts an enlargement of a section throuqh the surface portion of the blade 10. The nickel-base superalloy of the blade 10 (or of a gas turbine vane or other superalloy component) forms a substrate 22 upon which and over which the coating 20 is deposited. The coating 20 contains at least about 0.3 percent by volume of a dispersion of oxide particles 24 formed by the oxidation of yttrium and/or rare earth elements. These particles are typically equiaxed or roughly spherical in shape, but they could have an elongated shape. (In Figure 2, both the volume fraction of the dispersoid and it~ size are exaggerated for purposes of clarity of illustration.) 2~ Q~l. 13DV-8682 detailed description of the preferred embodiment, taken in conjunction with the accompanying drawings which illustrate, by way of example, the principles of the invention.
S BRIEF DESCRIPTION OF THE DRAWINGS
Figure l is a perspectivQ view of a turbine blade having a metallic protective coating; and Figur~ 2 is an enlarged sectional view of the turbine blade of Figure 1, taken along lines 2-2.
DETAILED DESCRIPTION OF ~E PREFERRED EMBODIMENT
The colting of the invention is pre~erably used with nickel-base superalloys, in applications such as a jet engine gas turbine blad~ 10 illustrated in Fiqure l, or a gas turbine vane which has a similar appearance in relevant respects. The blade 10 may be formed of any suitable superalloy such as Rene' 80, a well known nicXel-base superalloy which has a nominal composition, in weight percent, of 14 percent chromium, 9.5 percent cobalt, 5 percent titanium, 4 percent tungsten, 4 percent molybdenum, 3 percent aluminum, 0.17 percent carbon, 0.06 perc~nt zirconium, 0.015 percent boron, and the balance nickel. Another example is a more advanced nickel-base superalloy such as Rene' N4, having a composition, in wQight percent, o~ 7.5 cobalt, 9.0 chromium, 3.7 aluminum, 4.2 titanium, 1.5 percent molybdenum, 4.0 percent tantalum, 6.0 percent tung~ten, 0.5 pQrcent niobium, and balance nickel. Thes~ substrate superalloys are presented as examples, and the coating~ are not limlted ~or USQ with thes~ substrate~.
Z~7~Q9`1 13DV-8682 In accordance with another approach for preparing the coated component, a method for preparing a coated superalloy component comprises the steps of providing a substrate article formed of a nickel-base superalloy; and applying an adherent coating to the article by a thermal spray process such as vacuum or air plasma spray, the coating being a nickel-base superalloy additionally containing a sufficient amount of an element selected from the group consisting of yttrium, hafniu~, and the rare earths, and combinatione thereof, to form at least about 0.3 volume percent of dispersed oxide particles upon subsequent oxidation heat treatment. In this approach, a metallic alloy is applied to the surface. The superalloy of the coating can be any coating designed for protection of the substrate against oxidation and/or corrosion, but additionally has a sufficient excess amount of yttrium, hafnium or a rare earth to form the oxide dispersoids during a subsequent heat treatment. After the coating is applied, the coated component is heat treated in an oxidizing atmosphere to form the oxide dispersoids within the superalloy matrix. The oxides can be simple oxides or complex oxides containing one or more of the elements yttrium, hafnium and the rare earths.
The coating must contain at least about 0.3 volume percent of the oxide dispersoids, or the individual dispersoid particles will be too widely spaced to have a significant effect on reduction of cracking of the coating during thermal fatigue cycling. Larger amounts are acceptable, as long as they do not lead to brittleness of the coating. From about O.5 to about l.O volume percent of the dispersoids is preferred.
2 ~ 7~ 13DV-8682 As used herein, the term "the rare earths" comprehends those elements of the lanthanide series of the periodic table, atomic numbers 57-71 inclusive. These elements include lanthanum, cerium, praseodymium, neodymium, prometheum, samarium, europium, gadolinium, terbium, dysprosium, holmium, erbium, thuli~m, ytterbium, and lutetium. Although yttrium, atomic number 39, and hafnium, atomic number 72, are sometimes grouped together with the rare earths, they are separately identified herein, and not included among the rare earths.
In a preferred embodiment of the invention, a conventional NiCoCrAlY coating material was modified by adding 0.5 volume percent yttrium oxide and also alloying elements to strengthen the grain boundary regions of the coating. A standard NiCoCrAlY coating alloy has a composition, in weight percent, of about 20-23 percent cobalt, 18 percent chromium, 12.5 percent aluminum, 0~3 percent yttrium, and balance nickel. A satisfactory coating alloy is obtained by leaving the major alloying elements substantially as they are, and adding carbon, boron, or zirconium to strengthen the grain boundaries of the coating, and sufficient yttrium oxide to produce a dispersion of about 0.5 volume percent yttrium oxide (Y203) particles throughout the coating. The grain boundary strengthener is preferably up to about 0.07 weight percent carbon, up to about 0.030 weight percent zirconium, and up to about 0.030 percent boron, or combinations thereof. The preferred minimum contents are about 0.01 percent carbon, about 0.005 percent zirconium, and about 0.005 percent boron. Amounts below those indi~ated do not strengthen the grain boundaries to any appreciable degree, which may lead to premature failure of 2 ~ ~i 13DV-8682 the coating due to grain boundary creep. Amounts above the maximums can lead to grain boundary embrittlement, also a cause of premature failure.
A powder is formed from material of this composition by any convenient known method, such as mechanical alloying, and then applied to the component substrate by vacuum plasma spraying.
In accordance with this aspect of the invention, a coated superalloy component comprises a substrate article formed of a superalloy; and an adherent coating over the substrate, the coating being a nickel-base superalloy containing at least one gamma phase ~rain boundary strengthener selected from the group consisting of up to about 0.07 percent carbon, up to about 0.030 percent zirconium, and up to about 0.030 percent boron, and additionally containing at least about 0.3 volume percent of dispersed oxide particles formed of an element selected from the group consisting of yttrium, hafnium, the rare - earths, and combinations thereof.
The presently most preferred coating according to the invention has a metallic matrix composition, in weight percent, of 20 percent cobalt, 18 percent chromium, 12 percent aluminum, 0.95 percent carbon, 0.015 percent boron, 0.015 percent zirconium, 0.3 percent yttrium (present in the metallic ~orm), and 1.0 percent silicon.
About 0.5 percent by volume of yttrium oxide particulate material was mixed with the metallic matrix composition by mechanical alloying. (Yttrium is present in this coating as a metallic alloying element, below its solubility limit, and also as the oxide dispersoid yttriun oxide.) This coating may be applied by any type of plasma spraying, but preferably by vacuum plasma spraying, which was employed in the examples described herein.
2~75~1. . 13DV-8682 The coating of the preceding paragraph was applied to a simulated gas turbine blade made of the Rene' N4 superalloy discussed previously. These simulated blades were comparatively tested against identical simulated S blades of the same Rene' N4 superalloy, except having a CODEP coating prepared by the pack-diffusion process disclosed in U.S. Patent No. 3,540,878. In a burner rig thermal fatigue test, the coated blades were cycled between 970-F and 1800-F for 5000 cycle~, and inspected.
The blades coated with the dispersion-containing coating exhibited approximately the same number of cracks as for the CODEP coated blades, but the severity of the cracks was much less for the dispersion-containing coatings.
In an accelerated burner rig oxidation test at 2075-F
and Mach 1 gas velocity, a set of test specimens with the dispersion-containing coating had an average lifetime of 585 hours, as compared with 125 hours for identical CODEP-coated specimens. In a hot corrosion test at 1700~F
and a 5 ppm (parts per million) salt environment, the ~o dispersion-containing coating had an average life of at least 1600 hours (at which time the test was discontinued), compared to only 550 hours for the CODEP-coated blade.
Thus, the dispersion-containing coating of the invention produces improved results in simulated operating environments as compared with state-of-the-art CODEP
coatings.
Coatings of the present invention are typically stronger than conventional NiCoCrAlY coatings. For example, the rupture life of a conventional NiCoCrAlY
coating, tested at 1600-F and 3,000 pounds per square inch stress, is about 13 hours. As deposited, the coating 2 ~ 7~f~1 described above has a rupture life under the same test conditions of about 23 hours. After heat treating the coating 2 hours at 2310-F, the rupture life was increased to 506 hours. The increased strength is believed to contribute to the observed reduction in severity of cracks in the coating.
Thus, the present approach provides an advancement in the protection of superalloy substrates, and more particularly nickel-base superalloy substrates by metallic protective coatings. Although the present invention has been described in connection with specific examples and embodiments, it will be understood by those skilled in the arts involved, that the present invention is capable of modification without departing from its spirit and scope as represented by the appended claims.
PROTECTIVE COATING, AND METHOD OF PREPARATION
CROSS REFERENCE TO RELATED_APPLICATION
This application is related to concurrently filed and commonly assigned application Serial No. (Attorney Docket 13DV-8335), the disclosure of which is hereby incorporated by referen~e.
BACKGROUND O~ THE INVENTION
This invention relates to the protection of superalloys to be used at elevated temperatures, and, more particularly, to superalloy articles protected by coatings.
This invention was made with Government support under Contract No. N-0019-80-C-0017 awarded by the Naval Air Propulsion Center.
One of the most demanding materials applications in current technolo~y is found in ths hot-stage components used in aircraft jet engines. The higher the operating temperature of an engine, the greater its efficiency, and the more power it can produce from each gallon of fuel.
There is therefore an incentive to operate such engines at as high a te~perature as possible. The primary limitation on the operating temperatures of a jet engine is the material-~ used in the hottect regions of the engine, such as gas turbine blades and vanes.
2~7~oQ~1 13DV-8682 There has been much research to develop materials that can be used in high temperature engine applications. The currently most popular and successful of such materials are the nickel-base superalloys~ which are alloys of S nickel with additions of a number of other elements such as, for example, chromium, cobalt, aluminum, and tantalum.
The compositions of these superalloys are carefully engineered to maintain their strength and other mechanical properties even during use at the high temperature of engine operation, which is in the neighborhood of 2000-F
or more.
The materials used in the jet engines must operate at high temperatures, but additionally are subjected to oxidative and corrosive conditions. Oxidation of materials such as nickel and many of its alloys is rapid at engine operating temperatures. The engine components are also subjected to corrosive attack by chemicals in the burned fuel, as well as ingested agents such as salt that might be drawn into the engine as it operates near an ocean. The materials that have the best mechanical properties at high te~peratures often are not as resistant to oxidation and corrosion as other materials, and there is an ongoing search for materials that offer a compromise between the best mechanical properties and the best oxidation and corrosion resistance.
High operating temperatures can also be achieved by other techniques not related directly to the alloy compositions used in the components. For example, control of grain structures and use of single crystals can result in improved properties. Cooling passages may be provided in the components, and cooling air passed through them to lower their actual operating temperature.
2 ~7 rj~ 9~ 13DV-8682 In another approach which is the primary focus of the present invention, a thin protective metallic coating is deposited upon the component. The coatinq protects the substrate from oxidation and corrosion damage. The coating must be adherent to the superalloy substrate and must remain adherent through many cycles of heating to the operating temperature and then cooling back to a lower temperature when the engine is idling or turned off.
Because materials of different compositions have different coefficients of thermal expansion, differential strains develop between the coating and the component.
To accommodate the strains imposed by the thermal cycling, the thin coatings have been made of materials that are relatively weak and ductile. Such a coating can plastically deform either in tension or compression to remain adherent to the surface of the substrate as the substrate is heated and cooled. Most coatings for nickel-base superalloys have been made of alloys of nickel, chromium, aluminum, and yttrium, which are termed NiCrAlY alloys, and nickel, cobalt, chromium, aluminum, and yttrium, which are termed NiCoCrAlY alloys. The term MCrAlX, where M represents nickel, cobalt, iron or some combination thereof and X represents yttrium, hafnium, tantalum, silicon or some combination thereof, is a widely used generic description for this type of alloy. While such alloys contain many of the same elements as the substrate materials, the proportions of those elements have been adjusted to enhance oxidation and corrosion resistance rather than mechanical properties. They therefore lack the strength to serve as the structural components themselves, but serve well as protective coatings.
2~7 ~ 1. 13DV-8682 There remains an ongoing need for improved metallic coating materials that can protect the substrates for extended periods of time, against oxidation and corrosion damage. The present invention fulfills this need, and further provides related advantages.
SUMMARY OF T~E INVENTION
The present invention provides a class, and specific alloy compositions, of metallic coating materials useful in protecting high-temperature superalloys. The compositions are compositionally and structurally compatible with the superalloy substrates, protect against oxidation and corrosion damage, and remain adherent, crack-free, and protective for greater periods of time than prior metallic superalloy coatings. The coatings are formulated and applied by conventional techniques~
In accordance with the invention, a coated superalloy component comprises a substrate article formed of a superalloy and an adherent coating over the substrate.
The coating is a nickel-base superalloy additionally containing at least about 0.3 ~olume percent of dispersed particles of an oxide of yttrium, hafnium, a rare earth, or combinations thereof.
It is well known to provide yttrium and/or rare earth elements in superalloys and superalloy coatings to improve their resistance to oxidation. However, these elements are present in s~all amounts or are provided in such a compositional and formation context that a high fraction of their oxide dispersoids is not formed. The approach of the present invention intentionally provides a high fraction of dispersoids distributed in such a way as to improve the properties of the coating.
2~
The coatings of the invention represent a significant departure from conventional thinking in the metallic coating area. Heretofore, metallic superalloy coatings were made weak and ductile, to accommodate the strains imposed by the substrate as the component was repeatedly heated and cooled. The coating is deformed in complex planar strain conditions that are dictated by the deformation of the more massive substrate. The coating must deform plastically and/or in creep to a new set point during the temperature and load cycling of the engine, and a weak coating was deemed most desirable to operate under these constraints.
It was observed in the research underlying this invention that metallic coatings tend to fail in thermal fatigue, and that the weak coatings did not offer sufficient mechanical resistance to such fatigue failure.
The present invention therefore provides an oxide-dispersion containing coating, a coated article, and a method for preparation thereof. The oxide-containing coating is more resistant to thermal fatigue damage than the NiCrAlY or NiCoCrAlY alloys conventionally used as metallic coating materials, without sacrificing oxidation and corrosion resistance.
The present invention provides an important advance in the art of superalloys, as well as a departure from the conventional thought in the field. The coating of the invention permits a controllable improvement to the properties of the coating through selection of the fraction of dispersoid, while retalning the chemical components that lead to oxidation and corrosion resistance. Other features and advantages of the invention will be apparent from the following mor~
2 ~ Q ~1 13DV-8682 detailed description of the preferred embodiment, taken in conjunction with the accompanying drawings which illustrate, by way of example, the principles of the invention.
BRIEF DESCRI~TION OF THE DRAWINGS
Figure 1 is a perspective view of a turbine blade having a metallic protective coating; and Figure 2 is an enlarged sectional view of the turbin~
blade of Figure 1, taken along lines 2-2.
DETAILED ~ESCRIPTION OF THE PREFERRED EMBODIMENT
The coating of the invention is pre~erably used with nickel-base superalloys, in applications such as a jet engine gas turbine blade 10 illustrated in Figure 1, or a gas turbine vane which has a similar appearance in -relevant respects. The blade 10 may be formed of any suitable superalloy such as Rene' 80, a well known nickel-base superalloy which has a nominal composition, in weight percent, of 14 percent chromium, 9.5 percent cobalt, 5 percent titanium, 4 percent tungsten, 4 percent molybdenum, 3 percent aluminum, 0.17 percent carbon, 0.06 percent zirconium, 0.015 percent boron, and the balance nickel. Another example is a more advanced nickel-base superalloy such as Rene' N4, having a composition, in weight percent, of 7.5 cobalt, 9.O chromium, 3.7 aluminum, 4.2 titanium, 1.5 percent molybdenum, 4.0 percent tantalum, 6.0 percent tungsten, 0.5 percent niobium, and balance nickel. These substrate superalloys are presented as exa~ples, and the coatings are not limited for use with these substrates.
2~ ~rQ91 Such a blade 10 includes an airfoil section 12 against which hot combustion gases are directed when the engine operates, and whose surface is subjected to severe oxidation and corrosion attack during service. If the surface of the airfoil section 12 is not protected against oxidation and corrosion in some fashion, it will normally last at most only a-few cycles of operation. The airfoil section 12 is anchored to a turbine dis~ (not shown) through a root section 14. In some cases, cooling passages 16 are present in the airfoil section 12, through which cool bleed air is forced to remove heat from the blade 10. The blade 10 is normally prepared by a casting and solidification procedure well known to those skilled in the art, such as investment casting or, more preferably, directional solidification or single crystal growth.
According to the present invention, the airfoil section 12 is protected by a metallic protective coating 20, as illustrated in detail in Figure 2, which depicts an enlargement of a section throuqh the surface portion of the blade 10. The nickel-base superalloy of the blade 10 (or of a gas turbine vane or other superalloy component) forms a substrate 22 upon which and over which the coating 20 is deposited. The coating 20 contains at least about 0.3 percent by volume of a dispersion of oxide particles 24 formed by the oxidation of yttrium and/or rare earth elements. These particles are typically equiaxed or roughly spherical in shape, but they could have an elongated shape. (In Figure 2, both the volume fraction of the dispersoid and it~ size are exaggerated for purposes of clarity of illustration.) 2~ Q~l. 13DV-8682 detailed description of the preferred embodiment, taken in conjunction with the accompanying drawings which illustrate, by way of example, the principles of the invention.
S BRIEF DESCRIPTION OF THE DRAWINGS
Figure l is a perspectivQ view of a turbine blade having a metallic protective coating; and Figur~ 2 is an enlarged sectional view of the turbine blade of Figure 1, taken along lines 2-2.
DETAILED DESCRIPTION OF ~E PREFERRED EMBODIMENT
The colting of the invention is pre~erably used with nickel-base superalloys, in applications such as a jet engine gas turbine blad~ 10 illustrated in Fiqure l, or a gas turbine vane which has a similar appearance in relevant respects. The blade 10 may be formed of any suitable superalloy such as Rene' 80, a well known nicXel-base superalloy which has a nominal composition, in weight percent, of 14 percent chromium, 9.5 percent cobalt, 5 percent titanium, 4 percent tungsten, 4 percent molybdenum, 3 percent aluminum, 0.17 percent carbon, 0.06 perc~nt zirconium, 0.015 percent boron, and the balance nickel. Another example is a more advanced nickel-base superalloy such as Rene' N4, having a composition, in wQight percent, o~ 7.5 cobalt, 9.0 chromium, 3.7 aluminum, 4.2 titanium, 1.5 percent molybdenum, 4.0 percent tantalum, 6.0 percent tung~ten, 0.5 pQrcent niobium, and balance nickel. Thes~ substrate superalloys are presented as examples, and the coating~ are not limlted ~or USQ with thes~ substrate~.
Z~7~Q9`1 13DV-8682 In accordance with another approach for preparing the coated component, a method for preparing a coated superalloy component comprises the steps of providing a substrate article formed of a nickel-base superalloy; and applying an adherent coating to the article by a thermal spray process such as vacuum or air plasma spray, the coating being a nickel-base superalloy additionally containing a sufficient amount of an element selected from the group consisting of yttrium, hafniu~, and the rare earths, and combinatione thereof, to form at least about 0.3 volume percent of dispersed oxide particles upon subsequent oxidation heat treatment. In this approach, a metallic alloy is applied to the surface. The superalloy of the coating can be any coating designed for protection of the substrate against oxidation and/or corrosion, but additionally has a sufficient excess amount of yttrium, hafnium or a rare earth to form the oxide dispersoids during a subsequent heat treatment. After the coating is applied, the coated component is heat treated in an oxidizing atmosphere to form the oxide dispersoids within the superalloy matrix. The oxides can be simple oxides or complex oxides containing one or more of the elements yttrium, hafnium and the rare earths.
The coating must contain at least about 0.3 volume percent of the oxide dispersoids, or the individual dispersoid particles will be too widely spaced to have a significant effect on reduction of cracking of the coating during thermal fatigue cycling. Larger amounts are acceptable, as long as they do not lead to brittleness of the coating. From about O.5 to about l.O volume percent of the dispersoids is preferred.
2 ~ 7~ 13DV-8682 As used herein, the term "the rare earths" comprehends those elements of the lanthanide series of the periodic table, atomic numbers 57-71 inclusive. These elements include lanthanum, cerium, praseodymium, neodymium, prometheum, samarium, europium, gadolinium, terbium, dysprosium, holmium, erbium, thuli~m, ytterbium, and lutetium. Although yttrium, atomic number 39, and hafnium, atomic number 72, are sometimes grouped together with the rare earths, they are separately identified herein, and not included among the rare earths.
In a preferred embodiment of the invention, a conventional NiCoCrAlY coating material was modified by adding 0.5 volume percent yttrium oxide and also alloying elements to strengthen the grain boundary regions of the coating. A standard NiCoCrAlY coating alloy has a composition, in weight percent, of about 20-23 percent cobalt, 18 percent chromium, 12.5 percent aluminum, 0~3 percent yttrium, and balance nickel. A satisfactory coating alloy is obtained by leaving the major alloying elements substantially as they are, and adding carbon, boron, or zirconium to strengthen the grain boundaries of the coating, and sufficient yttrium oxide to produce a dispersion of about 0.5 volume percent yttrium oxide (Y203) particles throughout the coating. The grain boundary strengthener is preferably up to about 0.07 weight percent carbon, up to about 0.030 weight percent zirconium, and up to about 0.030 percent boron, or combinations thereof. The preferred minimum contents are about 0.01 percent carbon, about 0.005 percent zirconium, and about 0.005 percent boron. Amounts below those indi~ated do not strengthen the grain boundaries to any appreciable degree, which may lead to premature failure of 2 ~ ~i 13DV-8682 the coating due to grain boundary creep. Amounts above the maximums can lead to grain boundary embrittlement, also a cause of premature failure.
A powder is formed from material of this composition by any convenient known method, such as mechanical alloying, and then applied to the component substrate by vacuum plasma spraying.
In accordance with this aspect of the invention, a coated superalloy component comprises a substrate article formed of a superalloy; and an adherent coating over the substrate, the coating being a nickel-base superalloy containing at least one gamma phase ~rain boundary strengthener selected from the group consisting of up to about 0.07 percent carbon, up to about 0.030 percent zirconium, and up to about 0.030 percent boron, and additionally containing at least about 0.3 volume percent of dispersed oxide particles formed of an element selected from the group consisting of yttrium, hafnium, the rare - earths, and combinations thereof.
The presently most preferred coating according to the invention has a metallic matrix composition, in weight percent, of 20 percent cobalt, 18 percent chromium, 12 percent aluminum, 0.95 percent carbon, 0.015 percent boron, 0.015 percent zirconium, 0.3 percent yttrium (present in the metallic ~orm), and 1.0 percent silicon.
About 0.5 percent by volume of yttrium oxide particulate material was mixed with the metallic matrix composition by mechanical alloying. (Yttrium is present in this coating as a metallic alloying element, below its solubility limit, and also as the oxide dispersoid yttriun oxide.) This coating may be applied by any type of plasma spraying, but preferably by vacuum plasma spraying, which was employed in the examples described herein.
2~75~1. . 13DV-8682 The coating of the preceding paragraph was applied to a simulated gas turbine blade made of the Rene' N4 superalloy discussed previously. These simulated blades were comparatively tested against identical simulated S blades of the same Rene' N4 superalloy, except having a CODEP coating prepared by the pack-diffusion process disclosed in U.S. Patent No. 3,540,878. In a burner rig thermal fatigue test, the coated blades were cycled between 970-F and 1800-F for 5000 cycle~, and inspected.
The blades coated with the dispersion-containing coating exhibited approximately the same number of cracks as for the CODEP coated blades, but the severity of the cracks was much less for the dispersion-containing coatings.
In an accelerated burner rig oxidation test at 2075-F
and Mach 1 gas velocity, a set of test specimens with the dispersion-containing coating had an average lifetime of 585 hours, as compared with 125 hours for identical CODEP-coated specimens. In a hot corrosion test at 1700~F
and a 5 ppm (parts per million) salt environment, the ~o dispersion-containing coating had an average life of at least 1600 hours (at which time the test was discontinued), compared to only 550 hours for the CODEP-coated blade.
Thus, the dispersion-containing coating of the invention produces improved results in simulated operating environments as compared with state-of-the-art CODEP
coatings.
Coatings of the present invention are typically stronger than conventional NiCoCrAlY coatings. For example, the rupture life of a conventional NiCoCrAlY
coating, tested at 1600-F and 3,000 pounds per square inch stress, is about 13 hours. As deposited, the coating 2 ~ 7~f~1 described above has a rupture life under the same test conditions of about 23 hours. After heat treating the coating 2 hours at 2310-F, the rupture life was increased to 506 hours. The increased strength is believed to contribute to the observed reduction in severity of cracks in the coating.
Thus, the present approach provides an advancement in the protection of superalloy substrates, and more particularly nickel-base superalloy substrates by metallic protective coatings. Although the present invention has been described in connection with specific examples and embodiments, it will be understood by those skilled in the arts involved, that the present invention is capable of modification without departing from its spirit and scope as represented by the appended claims.
Claims (18)
1. A coated superalloy component, comprising:
a substrate article formed of a superalloy: and an adherent coating over the substrate, the coating being a nickel-base superalloy additionally containing at least about 0.3 volume percent of dispersed particles of an oxide of an element selected from the group consisting of yttrium, hafnium, the rare earths, and combinations thereof.
a substrate article formed of a superalloy: and an adherent coating over the substrate, the coating being a nickel-base superalloy additionally containing at least about 0.3 volume percent of dispersed particles of an oxide of an element selected from the group consisting of yttrium, hafnium, the rare earths, and combinations thereof.
2. The component of claim 1, wherein the oxide-forming element is yttrium.
3. The component of claim 1, wherein more than one oxide-forming element selected from the group consisting of yttrium, hafnium and the rare earths is present.
4. The component of claim 1, wherein the component is a turbine vane.
5. The component of claim 1, wherein the component is a turbine blade.
6. The component of claim 1, wherein the coating contains from about 0.5 to about 1.0 volume percent of dispersed particles.
7. A coated superalloy component, comprising:
a substrate article formed of a superalloy; and an adherent coating over the substrate, the coating being a nickel-base superalloy containing at least one gamma phase grain boundary strengthener selected from the group consisting of up to about 0.07 percent carbon, up to about 0.030 percent zirconium, and up to about 0.030 percent boron, and additionally containing at least about 0.3 volume percent of dispersed oxide particles formed of an element selected from the group consisting of yttrium, hafnium, the rare earths, and combinations thereof.
a substrate article formed of a superalloy; and an adherent coating over the substrate, the coating being a nickel-base superalloy containing at least one gamma phase grain boundary strengthener selected from the group consisting of up to about 0.07 percent carbon, up to about 0.030 percent zirconium, and up to about 0.030 percent boron, and additionally containing at least about 0.3 volume percent of dispersed oxide particles formed of an element selected from the group consisting of yttrium, hafnium, the rare earths, and combinations thereof.
8. The component of claim 7, wherein the coating contains from about 0.5 to about 1.0 volume percent of dispersed particles.
9. A method for preparing a coated superalloy component, comprising the steps of:
providing a substrate article formed of a nickel-base superalloy; and applying an adherent coating to the article by a thermal spray process, the coating being a nickel-base superalloy additionally containing at least about 0.3 volume percent of dispersed oxide particles formed of an element selected from the group consisting of yttrium and a rare earth.
providing a substrate article formed of a nickel-base superalloy; and applying an adherent coating to the article by a thermal spray process, the coating being a nickel-base superalloy additionally containing at least about 0.3 volume percent of dispersed oxide particles formed of an element selected from the group consisting of yttrium and a rare earth.
10. The method of claim 9, wherein the step of applying is performed by vacuum plasma spraying.
11. The method of claim 9, wherein the step of applying is performed by air plasma spraying.
12. The method of claim 9, wherein the coating contains from about 0.5 to about 1.0 volume percent of dispersed particles.
13. A method for preparing a coated superalloy component, comprising the steps of:
providing a substrate article formed of a nickel-base superalloy; and applying an adherent coating to the article by a thermal spray process, the coating being a nickel-base superalloy additionally containing a sufficient amount of an element selected from the group consisting of yttrium, hafnium, the rare earths, and combinations thereof, to form at least about 0.3 volume percent of dispersed oxide particles upon subsequent oxidation heat treatment.
providing a substrate article formed of a nickel-base superalloy; and applying an adherent coating to the article by a thermal spray process, the coating being a nickel-base superalloy additionally containing a sufficient amount of an element selected from the group consisting of yttrium, hafnium, the rare earths, and combinations thereof, to form at least about 0.3 volume percent of dispersed oxide particles upon subsequent oxidation heat treatment.
14. The method of claim 13, including the additional step, after the step of applying, of heat treating the coated article to form an oxide dispersion in the coating.
15. The method of claim 13, wherein the step of applying is performed by vacuum plasma spraying.
16. The method of claim 13, wherein the step of applying is performed by air plasma spraying.
17. The method of claim 13, wherein the coating contains from about 0.5 to about 1.0 volume percent of dispersed particles.
18. The invention as defined in any of the preceding claims including any further features of novelty disclosed.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US75694791A | 1991-09-09 | 1991-09-09 | |
| US756,947 | 1991-09-09 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2076091A1 true CA2076091A1 (en) | 1993-03-10 |
Family
ID=25045734
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA 2076091 Abandoned CA2076091A1 (en) | 1991-09-09 | 1992-08-13 | Superalloy component with dispersion-containing protective coatings, and method of preparation |
Country Status (3)
| Country | Link |
|---|---|
| EP (1) | EP0532252A1 (en) |
| JP (1) | JPH05195186A (en) |
| CA (1) | CA2076091A1 (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5455119A (en) * | 1993-11-08 | 1995-10-03 | Praxair S.T. Technology, Inc. | Coating composition having good corrosion and oxidation resistance |
| TW383233B (en) * | 1995-01-31 | 2000-03-01 | Rieter Ag Maschf | Thread guiding elements |
| US6168874B1 (en) | 1998-02-02 | 2001-01-02 | General Electric Company | Diffusion aluminide bond coat for a thermal barrier coating system and method therefor |
| CA2301092A1 (en) * | 1998-06-15 | 1999-12-23 | Mitsubishi Heavy Industries, Ltd. | Ni-based single crystal alloy having coating film for preventing recrystallization fracture |
| US7341758B2 (en) * | 2003-04-24 | 2008-03-11 | General Electric Company | Method for preparing and ultrasonically testing a thermal-spray coated article |
| US8313810B2 (en) | 2011-04-07 | 2012-11-20 | General Electric Company | Methods for forming an oxide-dispersion strengthened coating |
| FR3096690B1 (en) * | 2019-05-27 | 2021-07-23 | Safran | Corrosion protection process |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CH599352A5 (en) * | 1976-10-15 | 1978-05-31 | Bbc Brown Boveri & Cie | |
| US4230748A (en) * | 1979-08-15 | 1980-10-28 | Eutectic Corporation | Flame spray powder mix |
| US4447503A (en) * | 1980-05-01 | 1984-05-08 | Howmet Turbine Components Corporation | Superalloy coating composition with high temperature oxidation resistance |
| CA1233998A (en) * | 1984-04-05 | 1988-03-15 | Subramaniam Rangaswamy | Aluminum and yttrium oxide coated thermal spray powder |
| WO1987006273A2 (en) * | 1986-04-10 | 1987-10-22 | MTU MOTOREN- UND TURBINEN-UNION MüNCHEN GMBH | Coating to protect against wear and fretting corrosion of, in particular, metal mechanical components held together by frictional adherence |
-
1992
- 1992-08-13 CA CA 2076091 patent/CA2076091A1/en not_active Abandoned
- 1992-09-08 JP JP23874692A patent/JPH05195186A/en not_active Withdrawn
- 1992-09-08 EP EP92308099A patent/EP0532252A1/en not_active Withdrawn
Also Published As
| Publication number | Publication date |
|---|---|
| EP0532252A1 (en) | 1993-03-17 |
| JPH05195186A (en) | 1993-08-03 |
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