US20020152961A1 - Preheat method for EBPVD coating - Google Patents
Preheat method for EBPVD coating Download PDFInfo
- Publication number
- US20020152961A1 US20020152961A1 US10/177,797 US17779702A US2002152961A1 US 20020152961 A1 US20020152961 A1 US 20020152961A1 US 17779702 A US17779702 A US 17779702A US 2002152961 A1 US2002152961 A1 US 2002152961A1
- Authority
- US
- United States
- Prior art keywords
- gas
- coating
- preheat
- chamber
- substrate
- 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
Links
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
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/02—Pretreatment of the material to be coated
- C23C14/024—Deposition of sublayers, e.g. to promote adhesion of the coating
-
- 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
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/10—Oxidising
Definitions
- Thermal barrier coatings are becoming widely used in gas turbine engines.
- the most durable type of TBC coating is that which is deposited by electron beam physical vapor deposition (EBPVD) which consists of a substrate, a bond coat on the substrate and a columnar grain ceramic material adhered to the bond coat (the bond coat may be omitted in certain situations, hereinafter the word bond coat will be used to refer to the bond coat or the substrate if no bond coat is present).
- Adherence of the ceramic coating to the bond coat is critical and this is accomplished through the provision of the thin intermediate layer of a thermally grown oxide (TGO), consistingly essentially of alumina, on the surface of the bond coat prior to the application of the ceramic top coat.
- TGO thermally grown oxide
- TGO thermally grown oxide layer
- the EBPVD process is performed in conditions of relatively high vacuum.
- the TGO layer is developed by thermal oxidation.
- the TGO growth step is performed by heating the part in a vacuum environment, generally less than 10 ⁇ 2 Torr and allow the oxygen which leaks in the vacuum system to react with the part to form the TGO layer. It is also known to controllably bleed oxygen or air into the chamber.
- the TGO growth step is generally performed as part of the preheat cycle used to heat the substrate to the temperature required for the ceramic layer deposition.
- the rate of growth of the TGO layer depends on the oxygen concentration adjacent the part in vacuum chamber, the aluminum activity in the bond coat and time and temperature. TGO growth continues during ceramic coating distribution, but this is unavoidable. Difficulties have been encountered with excessively thick TGO layers in circumstances where the bond coat has particularly high aluminum activity so that the growth of the TGO layer is rapid, and also in circumstances where large part size (high thermal mass) leads to long heat up times and thereby forms an excessively thick TGO.
- This invention relates to the application of coatings to substrates or to substrates that have a coating thereon which contains aluminum. This invention has particular relevance to the controlled formation of thin TGO layers.
- U.S. Pat. Nos. 4,405,659; 4,676,994 and 5,538,796 describe methods for developing TGO layers.
- U.S. Pat. No. 5,087,477 describes a method for assuring stoichometry of the oxide ceramic insulating layer through the injection of oxygen into a chamber which partly surrounds the part being coated.
- U.S. Pat. No. 4,880,614 shows oxygen injection without a chamber surrounding the part.
- U.S. Pat. Nos. 4,405,659; 5,538,796 and 5,514,482 describe the application and utilization of MCrAlY bond coats and diffusion aluminide bond coats.
- U.S. Pat. No. 5,262,245 describes an alloy which can receive a ceramic coating without the requirement of a separate bond coat.
- the part to be coated is maintained at a vacuum level of less than about 10 ⁇ 2 Torr during the preheat process.
- This vacuum level refers to the overall vacuum level within the coating chamber.
- An amount of inert gas is continually flowed into the chamber, preferably immediately adjacent the part, during the preheat process, and most particularly during preheating from above about 1000° F., and preferably above 1200° F., to the substrate temperature desired during coating which is generally on the order of about 1600°-1900° F.
- Significant TGO growth does not occur below 1,000° F. and usually not below 1200° F.
- the gas may be truly inert such as argon, helium, xenon, krypton and the like and mixtures thereof, or may be non reactive with respect to the part to be coated, under the preheat conditions, for example hydrogen and nitrogen and mixtures thereof.
- nitrogen may cause formation of nitride phases in some alloys but this is not anticipated for superalloy substrates and bond coats used for gas turbine engine applications.
- Hydrogen is known to cause embrittlement in some alloys, but again this is not anticipated to occur in the TBC situation.
- the assignee of the present invention prefers argon, but the skilled practitioner will have no difficulty in evaluating and selecting a suitable gas. Mixtures of inert and non reactive gases may also be used.
- the part is surrounded by a cloud of inert or non oxidizing gas which tends to lower the oxygen level adjacent to the part and thereby lowers the rate of TGO growth.
- a cloud of inert or non oxidizing gas which tends to lower the oxygen level adjacent to the part and thereby lowers the rate of TGO growth.
- FIG. 1 of this patent shows an enclosure which partially surrounds the part and which has associated therewith the manifold system for delivering oxygen during the application of the ceramic coating.
- the enclosure serves to increase the oxygen partial pressure (the oxygen activity) of the environment immediately surrounding the part to be coated.
- Oxygen injection is used during the application of the ceramic layer to ensure that the oxide which is deposited contains the full amount of oxygen required to reach the stoichometric level in the oxide being deposited.
- the oxide being deposited is zirconia stabilized with yttria. Without this oxygen enhancement the zirconia tend to be deficient in oxygen.
- TGO growth continues during ceramic coating application, oxygen is usually added during ceramic deposition and is also present from the disassociated ceramic. In addition to oxygen, it is also known to inject air into the chamber as an oxidizing gas.
- U.S. Pat. No. 4,880,614 illustrates a similar approach to that of U.S. Pat. No. 5,087,477, using one or more nozzles to direct oxygen at the part during coating without the use of a part surrounding enclosure.
- the essence of the present invention is the injection of an inert or non reactive gas in the region surrounding the part using for example the same type of manifold and enclosure is shown in U.S. Pat. No. 5,087,477 or the nozzle arrangement of the type shown in U.S. Pat. No. 4,880,614.
- an amount of inert or non oxidizing gas comparable or greater than to the amount of oxygen which is deposited later in the cycle is sufficient to substantially reduce the rate of TGO growth during the preheat cycle.
- the time and temperature during the preheat cycle effects the TGO growth layer, longer times, and higher temperatures, produce thicker TGO layers, and larger parts take longer to heat up and consequently generally exhibit thicker TGO layers.
- the skilled practitioner will balance these equipment factors, the nature of the bond coat, if any, and the part mass and heat up time (and temperature) to arrive at a process which produces a TGO layer of the desired thickness, usually about 1 micron.
- an amount of oxygen injection/min approximately equal to 0.4 ⁇ 10 ⁇ 3 ⁇ the coating chamber vol.
- an oxygen injection per minute of 10 ⁇ 4 -10 ⁇ 2 of the coating chamber vol. should be suitable.
- the oxygen flow is measured at STP (standard pressure and temperature 760 mm Hg and 25° C.).
- the aluminum activity on the part surface is a function of surface composition and we have found that aluminide type bond coats generally have higher TGO growth rates than MCrAlY bond coats.
- the oxygen activity in the chamber is controlled by the competition between the leakage rate of oxygen of the external atmosphere (air) into the chamber, combined with any oxygen which may have been adsorbed or otherwise retained in the chamber, in competition with the pumping rate of the vacuum system which is used to maintain the vacuum environment.
- Some degree of leakage is inevitable but it should be minimized. Consequently these equipment parameters, leak up rate and pumping efficiency largely control the oxygen activity.
- the production apparatus which is used by the assignee of the present invention comprises a single chamber in which the preheat steps and coating steps are performed sequentially.
- preheating is generally accomplished using the same electron beam system which is subsequently used to evaporate the ceramic.
- the electron beam is used to directly or indirectly preheat the part.
- This coating is porous with a high effective surface area. This porous high surface area coating can contain substantial adsorbed oxygen and water vapor which will slowly be released during the preheat process providing oxygen which can contribute to the excessive TGO growth.
- the other general type of coating equipment uses a separate preheat chamber generally comprise a preheat chamber in which the part is preheated by radiant electrical heaters. Coating is performed in a separate chamber. Consequently the preheat chamber walls do not become ceramic coated.
- This type of apparatus is less prone to cause excessive TGO growth because the amount of oxygen adsorbed in the preheat chamber is reduced compared to the previously described single chamber system. Nonetheless even in the multiple chamber system with separate preheat there may be circumstances under which the use of an inert gas or non oxidizing gas to control TGO growth rate and thickness may be desirable.
- the invention comprises surrounding the part with a quantity of inert or non reactive gas sufficient to moderate, reduce, and control the rate of TGO layer growth.
- inert gases such as argon and helium
- non oxidizing gases such as nitrogen and hydrogen generally contain impurities, such as water vapor, which can cause oxidation.
- impurities such as water vapor, which can cause oxidation.
- a small gas turbine blade having the length of about 4 inches and a weight of about 3 ounces was to be coated with a thermal barrier coating using an aluminide bond coat.
- the use of an aluminide bond coat for thermal barrier coatings is described in U.S. Pat. Nos. 5,403,669 and 5,514,482.
- the coating apparatus was of the single chamber type and had an internal vol. of about 1.4 m 3 and a leak up rate of from about 8-30 microns per hour (with vacuum pumps not evacuating the chamber).
- the thermal barrier coating system After applying the thermal barrier coating system in a single chamber vacuum system wherein the operating chamber pressure was less than about 10 ⁇ 2 Torr and the preheat time from about 1200° F. to about 1600° F. was about 13 min, combined with the ceramic coating cycle time of (during 42 min. which TGO growth occurs) it was found that the TGO layer was about 2.5-5.0 microns thick and the outer oxide ceramic layer (zirconia stabilized with 8% yttria) was generally non-adherent and spalled upon cooling.
- Example II In Example II the same equipment, blade type, operating parameters and bond coat were employed except during the preheat process, starting at a temperature of less than about 1200° F., 554 sccm per minute of argon having a dew point in the range of ⁇ 30 to ⁇ 50° F. was flowed in the vicinity of the part using a part surrounding enclosure as described in U.S. Pat. No. 5,087,477. After preheating with this argon addition, at the conclusion of the preheat and coating cycle time of 42 minutes, the TGO layer was 0.5-2.0 microns thick and the columnar zirconia based oxide layer was fully adherent and durable.
- the same equipment and operating parameters were used to deposit a stabilized zirconia TBC on and industrial gas turbine engine part having a length of about 12 inches and a weight of about 8 lbs.
- the preheat time for this part was about 35 minutes and the coating cycle time as about 50 minutes for a total TGO growth time window of about 85 minutes.
- the TGO layer thickness varied from 3.5 to 6 microns, and the TBC longevity was unsatisfactory.
- Argon was flowed adjacent during preheating the TGO thickness ranged from 0.7 to 2.2 microns and the TBC was adherent and long lived.
Landscapes
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
A method is described for reducing surface oxide growth which heating aluminum containing surfaces in a vacuum environment prior to the deposition of a ceramic coating. The method comprises flowing an inert or non reactive gas into the coating apparatus adjacent to the surface to be coated to reduce oxygen reaction with the surface.
Description
- Thermal barrier coatings (TBC) are becoming widely used in gas turbine engines. The most durable type of TBC coating is that which is deposited by electron beam physical vapor deposition (EBPVD) which consists of a substrate, a bond coat on the substrate and a columnar grain ceramic material adhered to the bond coat (the bond coat may be omitted in certain situations, hereinafter the word bond coat will be used to refer to the bond coat or the substrate if no bond coat is present). Adherence of the ceramic coating to the bond coat is critical and this is accomplished through the provision of the thin intermediate layer of a thermally grown oxide (TGO), consistingly essentially of alumina, on the surface of the bond coat prior to the application of the ceramic top coat.
- This process is shown and described for example in U.S. Pat. Nos. 4,405,659 and 5,514,482. The contents of these patents are incorporated herein by reference. U.S. Pat. No. 5,262,245 describes a superalloy which can receive a durable EBPVD coating without the need for a bond coat. This superalloy contains aluminum and forms a TGO layer upon heating.
- The thickness of the thermally grown oxide layer (TGO) has been found to be a significant factor in the coating longevity, excessively thick TGO layers (on the order of 10 microns are generally correlated with non durable ceramic coatings).
- The EBPVD process is performed in conditions of relatively high vacuum. The TGO layer is developed by thermal oxidation. Currently the TGO growth step is performed by heating the part in a vacuum environment, generally less than 10−2 Torr and allow the oxygen which leaks in the vacuum system to react with the part to form the TGO layer. It is also known to controllably bleed oxygen or air into the chamber. The TGO growth step is generally performed as part of the preheat cycle used to heat the substrate to the temperature required for the ceramic layer deposition.
- The rate of growth of the TGO layer depends on the oxygen concentration adjacent the part in vacuum chamber, the aluminum activity in the bond coat and time and temperature. TGO growth continues during ceramic coating distribution, but this is unavoidable. Difficulties have been encountered with excessively thick TGO layers in circumstances where the bond coat has particularly high aluminum activity so that the growth of the TGO layer is rapid, and also in circumstances where large part size (high thermal mass) leads to long heat up times and thereby forms an excessively thick TGO.
- This invention relates to the application of coatings to substrates or to substrates that have a coating thereon which contains aluminum. This invention has particular relevance to the controlled formation of thin TGO layers.
- U.S. Pat. Nos. 4,405,659; 4,676,994 and 5,538,796 describe methods for developing TGO layers. U.S. Pat. No. 5,087,477 describes a method for assuring stoichometry of the oxide ceramic insulating layer through the injection of oxygen into a chamber which partly surrounds the part being coated. U.S. Pat. No. 4,880,614 shows oxygen injection without a chamber surrounding the part. U.S. Pat. Nos. 4,405,659; 5,538,796 and 5,514,482 describe the application and utilization of MCrAlY bond coats and diffusion aluminide bond coats. U.S. Pat. No. 5,262,245 describes an alloy which can receive a ceramic coating without the requirement of a separate bond coat.
- According to the present invention the part to be coated is maintained at a vacuum level of less than about 10−2 Torr during the preheat process. This vacuum level refers to the overall vacuum level within the coating chamber. An amount of inert gas is continually flowed into the chamber, preferably immediately adjacent the part, during the preheat process, and most particularly during preheating from above about 1000° F., and preferably above 1200° F., to the substrate temperature desired during coating which is generally on the order of about 1600°-1900° F. Significant TGO growth does not occur below 1,000° F. and usually not below 1200° F. The gas may be truly inert such as argon, helium, xenon, krypton and the like and mixtures thereof, or may be non reactive with respect to the part to be coated, under the preheat conditions, for example hydrogen and nitrogen and mixtures thereof.
- Theoretically, nitrogen may cause formation of nitride phases in some alloys but this is not anticipated for superalloy substrates and bond coats used for gas turbine engine applications. Hydrogen is known to cause embrittlement in some alloys, but again this is not anticipated to occur in the TBC situation. The assignee of the present invention prefers argon, but the skilled practitioner will have no difficulty in evaluating and selecting a suitable gas. Mixtures of inert and non reactive gases may also be used.
- According to the invention, the part is surrounded by a cloud of inert or non oxidizing gas which tends to lower the oxygen level adjacent to the part and thereby lowers the rate of TGO growth. It should be noted that the objective is to lower and control the rate of TGO growth (and the final TGO thickness) rather than to eliminate oxidation altogether since a TGO layer is a highly desired feature of a part prior to its receiving ceramic top coat.
- U.S. Pat. No. 5,087,477 describes the addition of oxygen during the application of an EBPVD ceramic top coat layer. FIG. 1 of this patent shows an enclosure which partially surrounds the part and which has associated therewith the manifold system for delivering oxygen during the application of the ceramic coating. The enclosure serves to increase the oxygen partial pressure (the oxygen activity) of the environment immediately surrounding the part to be coated.
- Oxygen injection is used during the application of the ceramic layer to ensure that the oxide which is deposited contains the full amount of oxygen required to reach the stoichometric level in the oxide being deposited. Usually the oxide being deposited is zirconia stabilized with yttria. Without this oxygen enhancement the zirconia tend to be deficient in oxygen. TGO growth continues during ceramic coating application, oxygen is usually added during ceramic deposition and is also present from the disassociated ceramic. In addition to oxygen, it is also known to inject air into the chamber as an oxidizing gas.
- U.S. Pat. No. 4,880,614 illustrates a similar approach to that of U.S. Pat. No. 5,087,477, using one or more nozzles to direct oxygen at the part during coating without the use of a part surrounding enclosure.
- The essence of the present invention is the injection of an inert or non reactive gas in the region surrounding the part using for example the same type of manifold and enclosure is shown in U.S. Pat. No. 5,087,477 or the nozzle arrangement of the type shown in U.S. Pat. No. 4,880,614. We have found that the use of an amount of inert or non oxidizing gas comparable or greater than to the amount of oxygen which is deposited later in the cycle is sufficient to substantially reduce the rate of TGO growth during the preheat cycle.
- Those skilled in the art will recognize the difficulty of being specific with parameter values since the process is partially dependent upon process equipment characteristics and characteristics of the substrate to be coated. The rate of growth of the TGO depends upon the part temperature, the length of the preheat cycle, the aluminum activity of the surface, and upon the oxygen activity in the chamber.
- The time and temperature during the preheat cycle effects the TGO growth layer, longer times, and higher temperatures, produce thicker TGO layers, and larger parts take longer to heat up and consequently generally exhibit thicker TGO layers. Thus the skilled practitioner will balance these equipment factors, the nature of the bond coat, if any, and the part mass and heat up time (and temperature) to arrive at a process which produces a TGO layer of the desired thickness, usually about 1 micron. In my process I used an amount of oxygen injection/min approximately equal to 0.4×10−3×the coating chamber vol. As a broad guideline an oxygen injection per minute of 10−4-10−2 of the coating chamber vol. should be suitable. In these guidelines the oxygen flow is measured at STP (standard pressure and temperature 760 mm Hg and 25° C.).
- The aluminum activity on the part surface is a function of surface composition and we have found that aluminide type bond coats generally have higher TGO growth rates than MCrAlY bond coats.
- The oxygen activity in the chamber is controlled by the competition between the leakage rate of oxygen of the external atmosphere (air) into the chamber, combined with any oxygen which may have been adsorbed or otherwise retained in the chamber, in competition with the pumping rate of the vacuum system which is used to maintain the vacuum environment. Some degree of leakage is inevitable but it should be minimized. Consequently these equipment parameters, leak up rate and pumping efficiency largely control the oxygen activity.
- In addition there are different general types of EBPVD apparatus. The production apparatus which is used by the assignee of the present invention comprises a single chamber in which the preheat steps and coating steps are performed sequentially. In this type of system preheating is generally accomplished using the same electron beam system which is subsequently used to evaporate the ceramic. During the preheat process the electron beam is used to directly or indirectly preheat the part. In this type of arrangement where preheating occurs in the same chamber which the ceramic coating deposition subsequently occurs, after a period of use the chamber walls becomes coated with ceramic. This coating is porous with a high effective surface area. This porous high surface area coating can contain substantial adsorbed oxygen and water vapor which will slowly be released during the preheat process providing oxygen which can contribute to the excessive TGO growth.
- The other general type of coating equipment uses a separate preheat chamber generally comprise a preheat chamber in which the part is preheated by radiant electrical heaters. Coating is performed in a separate chamber. Consequently the preheat chamber walls do not become ceramic coated. This type of apparatus is less prone to cause excessive TGO growth because the amount of oxygen adsorbed in the preheat chamber is reduced compared to the previously described single chamber system. Nonetheless even in the multiple chamber system with separate preheat there may be circumstances under which the use of an inert gas or non oxidizing gas to control TGO growth rate and thickness may be desirable.
- The invention comprises surrounding the part with a quantity of inert or non reactive gas sufficient to moderate, reduce, and control the rate of TGO layer growth. It should be noted that even inert gases such as argon and helium, and non oxidizing gases such as nitrogen and hydrogen generally contain impurities, such as water vapor, which can cause oxidation. Thus the skilled practitioner will recognize the need to measure the water vapor content in the inert or non oxidizing gas being used and factor that into the overall performance of the preheat cycle to arrive at the desired TGO layer thickness. We have used argon having a dew point of between −30 and −50° F. with good success. However different circumstances may require a different dew point.
- The present invention will be better understood by consideration of the following illustrative examples.
- A small gas turbine blade having the length of about 4 inches and a weight of about 3 ounces was to be coated with a thermal barrier coating using an aluminide bond coat. The use of an aluminide bond coat for thermal barrier coatings is described in U.S. Pat. Nos. 5,403,669 and 5,514,482.
- The coating apparatus was of the single chamber type and had an internal vol. of about 1.4 m3 and a leak up rate of from about 8-30 microns per hour (with vacuum pumps not evacuating the chamber).
- After applying the thermal barrier coating system in a single chamber vacuum system wherein the operating chamber pressure was less than about 10−2 Torr and the preheat time from about 1200° F. to about 1600° F. was about 13 min, combined with the ceramic coating cycle time of (during 42 min. which TGO growth occurs) it was found that the TGO layer was about 2.5-5.0 microns thick and the outer oxide ceramic layer (zirconia stabilized with 8% yttria) was generally non-adherent and spalled upon cooling.
- In Example II the same equipment, blade type, operating parameters and bond coat were employed except during the preheat process, starting at a temperature of less than about 1200° F., 554 sccm per minute of argon having a dew point in the range of −30 to −50° F. was flowed in the vicinity of the part using a part surrounding enclosure as described in U.S. Pat. No. 5,087,477. After preheating with this argon addition, at the conclusion of the preheat and coating cycle time of 42 minutes, the TGO layer was 0.5-2.0 microns thick and the columnar zirconia based oxide layer was fully adherent and durable.
- The same equipment and operating parameters were used to deposit a stabilized zirconia TBC on and industrial gas turbine engine part having a length of about 12 inches and a weight of about 8 lbs. The preheat time for this part was about 35 minutes and the coating cycle time as about 50 minutes for a total TGO growth time window of about 85 minutes. Without the use of inert gas injection during preheat the TGO layer thickness varied from 3.5 to 6 microns, and the TBC longevity was unsatisfactory. When Argon was flowed adjacent during preheating the TGO thickness ranged from 0.7 to 2.2 microns and the TBC was adherent and long lived.
- Although this invention has been shown and described with respect to the detailed embodiments thereof, it will be understood by those skilled in the art that various changes in the form and detail thereof may be made without departing from the spirit and scope of the claimed invention.
Claims (14)
1. A method for heating a part in a vacuum environment which comprises: heating said part while simultaneously providing a gas selected from the group comprising inert and non reactive gases and mixtures thereof to the region immediately surrounding the part and maintaining the part in a vacuum environment; whereby oxidation of said part due to oxygen in said vacuum environment is reduced.
2. A method as in claim 1 wherein said part comprises a superalloy substrate having an aluminum containing bond coat.
3. A method as in claim 2 wherein said bond coat comprises an MCrAlY coating.
4. A method as in claim 2 wherein said bond coat comprises an aluminide coating.
5. A method as in claim 1 wherein said part comprises an aluminum containing superalloy substrate without a bond coat.
6. A method as in claim 1 wherein said inert gas is selected from the group consisting of Ar, Ne, Kr, Xe and mixtures thereof.
7. A method as in claim 1 wherein said non reactive gas is selected from the group consisting of N, H and mixtures thereof.
8. A method as in claim 2 wherein said gas is provided during that part of the preheat cycle where the substrate temperature exceeds about 1000° F.
9. A method as in claim 2 wherein said gas is provided during that part of the preheat cycle where the part temperature exceeds about 1200° F.
10. A method as in claim 1 wherein said vacuum environment is maintained at a pressure of less than about 10−2 during the preheat cycle. (unit?)
11. A method as in claim 1 wherein said gas is injected into a chamber which partially surrounds the part to be preheated.
12. A method as in claim 1 wherein said gas is injected into the region immediately surrounding the part through at least one nozzle.
13. A method for preheating a gas turbine component in a vacuum environment prior to the application of a ceramic coating, wherein said gas turbine component has an outer surface which contains aluminum, which comprises: adding a gas selected from the group consisting of Ar, He, N, H, Xe, Kr, and mixtures thereof into the region immediately surrounding the part to reduce the rate of alumina formation during preheating.
14. In an apparatus applying a ceramic coating to a substrate by EBPVD, of the type which includes a vacuum chamber, means for producing a vacuum in said chamber and means to preheat said substrate prior to application of said coating, the improvement which comprises: means to inject a gas selected from the group comprising inert and non reactive gases, and mixtures thereof into the region surrounding the substrate during the preheat step preceding ceramic coating application.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US10/177,797 US20020152961A1 (en) | 1997-12-23 | 2002-06-20 | Preheat method for EBPVD coating |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US08/996,650 US6478888B1 (en) | 1997-12-23 | 1997-12-23 | Preheat method for EBPVD coating |
US10/177,797 US20020152961A1 (en) | 1997-12-23 | 2002-06-20 | Preheat method for EBPVD coating |
Related Parent Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US08/996,650 Division US6478888B1 (en) | 1997-12-23 | 1997-12-23 | Preheat method for EBPVD coating |
Publications (1)
Publication Number | Publication Date |
---|---|
US20020152961A1 true US20020152961A1 (en) | 2002-10-24 |
Family
ID=25543144
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US08/996,650 Expired - Lifetime US6478888B1 (en) | 1997-12-23 | 1997-12-23 | Preheat method for EBPVD coating |
US10/177,797 Abandoned US20020152961A1 (en) | 1997-12-23 | 2002-06-20 | Preheat method for EBPVD coating |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US08/996,650 Expired - Lifetime US6478888B1 (en) | 1997-12-23 | 1997-12-23 | Preheat method for EBPVD coating |
Country Status (5)
Country | Link |
---|---|
US (2) | US6478888B1 (en) |
EP (1) | EP0926257B1 (en) |
JP (1) | JPH11315369A (en) |
DE (1) | DE69823468T2 (en) |
UA (1) | UA68334C2 (en) |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20100081009A1 (en) * | 2008-09-26 | 2010-04-01 | General Electric Company | Spray Application of Liquid Precursors for CMAS Resistant Coatings |
US20110217560A1 (en) * | 2010-03-04 | 2011-09-08 | Ridgeway Neil B | Coated article and coating process therefor |
US20110217464A1 (en) * | 2010-03-08 | 2011-09-08 | United Technologies Corporation | Method for applying a thermal barrier coating |
US20110223354A1 (en) * | 2010-03-12 | 2011-09-15 | United Technologies Corporation | High pressure pre-oxidation for deposition of thermal barrier coating |
US20120196030A1 (en) * | 2009-11-30 | 2012-08-02 | United Technologies Corporation | Coating Methods and Apparatus |
WO2014143259A1 (en) * | 2013-03-14 | 2014-09-18 | United Technologies Corporation | Preheat chamber oxidation process |
US20160326628A1 (en) * | 2014-01-09 | 2016-11-10 | United Technologies Corporation | Coating process using gas screen |
US9581042B2 (en) | 2012-10-30 | 2017-02-28 | United Technologies Corporation | Composite article having metal-containing layer with phase-specific seed particles and method therefor |
US20170197278A1 (en) * | 2016-01-13 | 2017-07-13 | Rolls-Royce Plc | Additive layer manufacturing methods |
CN111893452A (en) * | 2020-07-31 | 2020-11-06 | 中国航空制造技术研究院 | Blade preheating device and method for electron beam physical vapor deposition |
US11866816B2 (en) | 2016-07-06 | 2024-01-09 | Rtx Corporation | Apparatus for use in coating process |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102004052104B3 (en) * | 2004-10-26 | 2006-02-02 | Forschungszentrum Jülich GmbH | Pre-oxidation of articles made from aluminum alloys comprises heating to form stable alpha-aluminum coating in atmosphere comprising e.g. water vapor with specified free oxygen content |
US7838083B1 (en) | 2005-01-28 | 2010-11-23 | Sandia Corporation | Ion beam assisted deposition of thermal barrier coatings |
US8084086B2 (en) * | 2005-06-30 | 2011-12-27 | University Of Virginia Patent Foundation | Reliant thermal barrier coating system and related methods and apparatus of making the same |
US20090162670A1 (en) * | 2007-12-20 | 2009-06-25 | General Electric Company | Method for applying ceramic coatings to smooth surfaces by air plasma spray techniques, and related articles |
US20100247952A1 (en) * | 2009-03-31 | 2010-09-30 | Latour Robert F | Controlled oxidation of bond coat |
US8350180B2 (en) * | 2010-03-12 | 2013-01-08 | United Technologies Corporation | High pressure pre-oxidation for deposition of thermal barrier coating with hood |
WO2015053947A1 (en) | 2013-10-09 | 2015-04-16 | United Technologies Corporation | Thermal barrier coating with improved adhesion |
WO2015116292A2 (en) | 2013-11-11 | 2015-08-06 | United Technologies Corporation | Article with coated substrate |
Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4439248A (en) * | 1982-02-02 | 1984-03-27 | Cabot Corporation | Method of heat treating NICRALY alloys for use as ceramic kiln and furnace hardware |
US4880614A (en) * | 1988-11-03 | 1989-11-14 | Allied-Signal Inc. | Ceramic thermal barrier coating with alumina interlayer |
US5004721A (en) * | 1988-11-03 | 1991-04-02 | Board Of Regents, The University Of Texas System | As-deposited oxide superconductor films on silicon and aluminum oxide |
US5087477A (en) * | 1990-02-05 | 1992-02-11 | United Technologies Corporation | Eb-pvd method for applying ceramic coatings |
US5238752A (en) * | 1990-05-07 | 1993-08-24 | General Electric Company | Thermal barrier coating system with intermetallic overlay bond coat |
US5262245A (en) * | 1988-08-12 | 1993-11-16 | United Technologies Corporation | Advanced thermal barrier coated superalloy components |
US5432151A (en) * | 1993-07-12 | 1995-07-11 | Regents Of The University Of California | Process for ion-assisted laser deposition of biaxially textured layer on substrate |
US5556472A (en) * | 1991-12-09 | 1996-09-17 | Sumitomo Electric Industries, Ltd | Film deposition apparatus |
US5652044A (en) * | 1992-03-05 | 1997-07-29 | Rolls Royce Plc | Coated article |
US5667663A (en) * | 1994-12-24 | 1997-09-16 | Chromalloy United Kingdom Limited | Method of applying a thermal barrier coating to a superalloy article and a thermal barrier coating |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4405659A (en) | 1980-01-07 | 1983-09-20 | United Technologies Corporation | Method for producing columnar grain ceramic thermal barrier coatings |
US4449714A (en) * | 1983-03-22 | 1984-05-22 | Gulf & Western Industries, Inc. | Turbine engine seal and method for repair thereof |
US4676994A (en) | 1983-06-15 | 1987-06-30 | The Boc Group, Inc. | Adherent ceramic coatings |
US5514482A (en) | 1984-04-25 | 1996-05-07 | Alliedsignal Inc. | Thermal barrier coating system for superalloy components |
JPS63161156A (en) * | 1986-12-24 | 1988-07-04 | Shinko Seiki Kk | Thin hard blue film and its production |
DE8717392U1 (en) * | 1987-03-16 | 1989-05-18 | Emitec Gesellschaft für Emissionstechnologie mbH, 5204 Lohmar | Catalyst carrier body |
JPH0248404A (en) * | 1988-08-10 | 1990-02-19 | Fujitsu Ltd | Method for forming superconducting thin film and apparatus therefor |
US4944858A (en) * | 1988-12-08 | 1990-07-31 | United Technologies Corporation | Method for applying diffusion aluminide coating |
US5601652A (en) | 1989-08-03 | 1997-02-11 | United Technologies Corporation | Apparatus for applying ceramic coatings |
US5451366A (en) * | 1992-07-17 | 1995-09-19 | Sumitomo Light Metal Industries, Ltd. | Product of a halogen containing Ti-Al system intermetallic compound having a superior oxidation and wear resistance |
US5538796A (en) | 1992-10-13 | 1996-07-23 | General Electric Company | Thermal barrier coating system having no bond coat |
US5716720A (en) * | 1995-03-21 | 1998-02-10 | Howmet Corporation | Thermal barrier coating system with intermediate phase bondcoat |
JP2934599B2 (en) * | 1996-02-16 | 1999-08-16 | 三菱重工業株式会社 | High temperature corrosion resistant composite surface treatment method |
GB9715175D0 (en) * | 1997-07-19 | 1997-09-24 | Univ Birmingham | Method of case hardening |
-
1997
- 1997-12-23 US US08/996,650 patent/US6478888B1/en not_active Expired - Lifetime
-
1998
- 1998-12-11 DE DE69823468T patent/DE69823468T2/en not_active Expired - Lifetime
- 1998-12-11 EP EP98310157A patent/EP0926257B1/en not_active Expired - Lifetime
- 1998-12-17 JP JP10358763A patent/JPH11315369A/en active Pending
- 1998-12-17 UA UA98126677A patent/UA68334C2/en unknown
-
2002
- 2002-06-20 US US10/177,797 patent/US20020152961A1/en not_active Abandoned
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4439248A (en) * | 1982-02-02 | 1984-03-27 | Cabot Corporation | Method of heat treating NICRALY alloys for use as ceramic kiln and furnace hardware |
US5262245A (en) * | 1988-08-12 | 1993-11-16 | United Technologies Corporation | Advanced thermal barrier coated superalloy components |
US4880614A (en) * | 1988-11-03 | 1989-11-14 | Allied-Signal Inc. | Ceramic thermal barrier coating with alumina interlayer |
US5004721A (en) * | 1988-11-03 | 1991-04-02 | Board Of Regents, The University Of Texas System | As-deposited oxide superconductor films on silicon and aluminum oxide |
US5087477A (en) * | 1990-02-05 | 1992-02-11 | United Technologies Corporation | Eb-pvd method for applying ceramic coatings |
US5238752A (en) * | 1990-05-07 | 1993-08-24 | General Electric Company | Thermal barrier coating system with intermetallic overlay bond coat |
US5556472A (en) * | 1991-12-09 | 1996-09-17 | Sumitomo Electric Industries, Ltd | Film deposition apparatus |
US5652044A (en) * | 1992-03-05 | 1997-07-29 | Rolls Royce Plc | Coated article |
US5432151A (en) * | 1993-07-12 | 1995-07-11 | Regents Of The University Of California | Process for ion-assisted laser deposition of biaxially textured layer on substrate |
US5667663A (en) * | 1994-12-24 | 1997-09-16 | Chromalloy United Kingdom Limited | Method of applying a thermal barrier coating to a superalloy article and a thermal barrier coating |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20100081009A1 (en) * | 2008-09-26 | 2010-04-01 | General Electric Company | Spray Application of Liquid Precursors for CMAS Resistant Coatings |
US20120196030A1 (en) * | 2009-11-30 | 2012-08-02 | United Technologies Corporation | Coating Methods and Apparatus |
US9133542B2 (en) * | 2009-11-30 | 2015-09-15 | United Technologies Corporation | Coating methods and apparatus |
US9315905B2 (en) * | 2010-03-04 | 2016-04-19 | United Technologies Corporation | Coated article and coating process therefor |
US20110217560A1 (en) * | 2010-03-04 | 2011-09-08 | Ridgeway Neil B | Coated article and coating process therefor |
US8481117B2 (en) | 2010-03-08 | 2013-07-09 | United Technologies Corporation | Method for applying a thermal barrier coating |
US20110217464A1 (en) * | 2010-03-08 | 2011-09-08 | United Technologies Corporation | Method for applying a thermal barrier coating |
US20110223354A1 (en) * | 2010-03-12 | 2011-09-15 | United Technologies Corporation | High pressure pre-oxidation for deposition of thermal barrier coating |
US9581042B2 (en) | 2012-10-30 | 2017-02-28 | United Technologies Corporation | Composite article having metal-containing layer with phase-specific seed particles and method therefor |
WO2014143259A1 (en) * | 2013-03-14 | 2014-09-18 | United Technologies Corporation | Preheat chamber oxidation process |
US20160326628A1 (en) * | 2014-01-09 | 2016-11-10 | United Technologies Corporation | Coating process using gas screen |
US10233533B2 (en) * | 2014-01-09 | 2019-03-19 | United Technologies Corporation | Coating process using gas screen |
EP3092324B1 (en) * | 2014-01-09 | 2020-07-15 | United Technologies Corporation | Coating process using gas screen |
US20170197278A1 (en) * | 2016-01-13 | 2017-07-13 | Rolls-Royce Plc | Additive layer manufacturing methods |
US11866816B2 (en) | 2016-07-06 | 2024-01-09 | Rtx Corporation | Apparatus for use in coating process |
CN111893452A (en) * | 2020-07-31 | 2020-11-06 | 中国航空制造技术研究院 | Blade preheating device and method for electron beam physical vapor deposition |
Also Published As
Publication number | Publication date |
---|---|
EP0926257A1 (en) | 1999-06-30 |
US6478888B1 (en) | 2002-11-12 |
UA68334C2 (en) | 2004-08-16 |
EP0926257B1 (en) | 2004-04-28 |
JPH11315369A (en) | 1999-11-16 |
DE69823468D1 (en) | 2004-06-03 |
DE69823468T2 (en) | 2004-09-09 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US6478888B1 (en) | Preheat method for EBPVD coating | |
US5624721A (en) | Method of producing a superalloy article | |
US5942337A (en) | Thermal barrier coating for a superalloy article and a method of application thereof | |
US6284323B1 (en) | Thermal barrier coating systems and materials | |
US5236745A (en) | Method for increasing the cyclic spallation life of a thermal barrier coating | |
US6123997A (en) | Method for forming a thermal barrier coating | |
US6440496B1 (en) | Method of forming a diffusion aluminide coating | |
EP1321542B1 (en) | Thermal barrier coating systems and materials | |
US7214409B1 (en) | High strength Ni-Pt-Al-Hf bondcoat | |
US6730413B2 (en) | Thermal barrier coating | |
US20100196615A1 (en) | Method for forming an oxidation-resistant film | |
US20070231589A1 (en) | Thermal barrier coatings and processes for applying same | |
JP2005313644A (en) | Peeling resistance metal articles and peeling reduction method of metal article | |
JPH10507230A (en) | Protective layer for protecting members against corrosion, oxidation and thermal overload, and method of manufacturing the same | |
JP2001225411A (en) | Method for forming ceramic coating comprising porous layer, and coated article | |
KR20040014223A (en) | Thermal barrier coating utilizing a dispersion strengthened metallic bond coat | |
US6495271B1 (en) | Spallation-resistant protective layer on high performance alloys | |
US7282271B2 (en) | Durable thermal barrier coatings | |
US6492038B1 (en) | Thermally-stabilized thermal barrier coating and process therefor | |
US20060057418A1 (en) | Alluminide coatings containing silicon and yttrium for superalloys and method of forming such coatings | |
US20130327271A1 (en) | Vapor deposition process and apparatus therefor | |
US20080292873A1 (en) | Method for Providing a Thermal Barrier Coating and Substrate Having Such Coating | |
JP2000080464A (en) | Low thermal conductivity and heat barrier type ceramic coating, method for depositing ceramic coating and metallic parts protected by this ceramic coating | |
US6790486B2 (en) | Vapor deposition process | |
US6342278B1 (en) | Method for forming a thermal barrier coating by electron beam physical vapor deposition |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |