US20180030584A1 - Thermal barrier coating, turbine member, gas turbine, and manufacturing method for thermal barrier coating - Google Patents
Thermal barrier coating, turbine member, gas turbine, and manufacturing method for thermal barrier coating Download PDFInfo
- Publication number
- US20180030584A1 US20180030584A1 US15/549,862 US201615549862A US2018030584A1 US 20180030584 A1 US20180030584 A1 US 20180030584A1 US 201615549862 A US201615549862 A US 201615549862A US 2018030584 A1 US2018030584 A1 US 2018030584A1
- Authority
- US
- United States
- Prior art keywords
- ceramic layer
- cracks
- thermal
- thermal spray
- barrier coating
- 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
Images
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
- C23C4/12—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
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
- C23C28/32—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer
-
- 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
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
- C23C28/34—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates
- C23C28/345—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates with at least one oxide layer
- C23C28/3455—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates with at least one oxide layer with a refractory ceramic layer, e.g. refractory metal oxide, ZrO2, rare earth oxides or a thermal barrier system comprising at least one refractory oxide layer
-
- 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
-
- 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
- C23C4/10—Oxides, borides, carbides, nitrides or silicides; Mixtures thereof
- C23C4/11—Oxides
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D25/00—Component parts, details, or accessories, not provided for in, or of interest apart from, other groups
- F01D25/005—Selecting particular materials
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
- F01D5/12—Blades
- F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
- F01D5/12—Blades
- F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
- F01D5/288—Protective coatings for blades
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D9/00—Stators
- F01D9/02—Nozzles; Nozzle boxes; Stator blades; Guide conduits, e.g. individual nozzles
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
- F05D2220/00—Application
- F05D2220/30—Application in turbines
- F05D2220/32—Application in turbines in gas turbines
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
- F05D2230/00—Manufacture
- F05D2230/30—Manufacture with deposition of material
- F05D2230/31—Layer deposition
- F05D2230/311—Layer deposition by torch or flame spraying
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
- F05D2300/00—Materials; Properties thereof
- F05D2300/20—Oxide or non-oxide ceramics
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
- F05D2300/00—Materials; Properties thereof
- F05D2300/50—Intrinsic material properties or characteristics
- F05D2300/514—Porosity
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
- F05D2300/00—Materials; Properties thereof
- F05D2300/60—Properties or characteristics given to material by treatment or manufacturing
- F05D2300/611—Coating
Definitions
- the present invention relates to a thermal barrier coating, a turbine member, a gas turbine, and a manufacturing method for a thermal barrier coating.
- a temperature of combustion gas to be used is set high in order to improve efficiency of the gas turbine.
- a thermal barrier coating is applied to surfaces of turbine blade members such as blades and vanes subjected to the combustion gas having a high temperature.
- the thermal barrier coating is a coating of a thermal spraying material having low thermal conductivity (for example, a ceramics-based material having low thermal conductivity) applied by thermal spraying to a surface of a turbine member which is an object to be thermally sprayed. Heat-shielding properties and durability of the turbine member are improved by the thermal barrier coating.
- a thermal barrier coating includes a metal bonding layer which is an undercoat layer and a ceramic layer which is a top coat layer formed on the metal bonding layer, on a surface of a heat-resistant substrate serving as a base material.
- the ceramic layer is formed by thermally spraying a powder mixture of ceramic powder and resin powder onto the undercoat layer.
- the ceramic layer described in PTL 1 is so configured that vertical cracks which are cracks extending in a thickness direction and pores are dispersed in a surface direction.
- a dense coating having the vertical cracks described in PTL 1 is referred to as a DVC (Dense Vertically Crack) coating. Since the DVC coating is a dense structure having a vertically cracked structure, durability is improved. However, since the structure is dense in the DVC coating, porosity decreases, and heat-shielding properties are likely to decrease.
- DVC Den Vertically Crack
- the present invention provides a thermal barrier coating in which heat-shielding properties can be improved while sufficient durability is secured, a turbine member, a gas turbine, and a manufacturing method for a thermal barrier coating.
- the present invention suggests the following means.
- a thermal barrier coating including: a heat-resistant alloy substrate which is used in a turbine member; and a ceramic layer which is formed on the heat-resistant alloy substrate, vertical cracks extending in a thickness direction being dispersed in a surface direction, a plurality of pores being included inside the ceramic layer, wherein thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m are thermally sprayed to form the ceramic layer.
- the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m are used, when the thermal spray particles are thermally sprayed on the heat-resistant alloy substrate to form the ceramic layer, surfaces of the thermal spray particles are melted while cores thereof remain so as not to be melted. Accordingly, in the ceramic layer, a porous structure is formed by the remaining cores of the thermal spray particles while a dense structure is formed by the melted surfaces of the thermal spray particles. Accordingly, it is possible to obtain the ceramic layer having a porous structure including an amount of pores required for securing heat-shielding properties while having a dense structure including vertical cracks required for securing sufficient durability.
- the vertical cracks in the ceramic layer, may be dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction, and the porosity may be 4% to 15%.
- the vertical cracks in the ceramic layer, may be dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction, and the porosity may be 9% to 15%.
- the vertical cracks in the ceramic layer, may be dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction, and the porosity may be 9% to 10%.
- a turbine member on which the thermal barrier coating is formed.
- a gas turbine including the turbine member.
- a manufacturing method for a thermal barrier coating including a ceramic layer forming process of forming a ceramic layer on a heat-resistant alloy substrate used in a turbine member by thermally spraying thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m, wherein in the ceramic layer, vertical cracks extending in a thickness direction are dispersed in a surface direction and a plurality of pores are included inside the ceramic layer.
- the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m are used, when the thermal spray particles are thermally sprayed on the heat-resistant alloy substrate to form the ceramic layer, the surfaces of the thermal spray particles are melted while the cores thereof remain so as not to be melted. Accordingly, in the ceramic layer, a porous structure is formed by the remaining cores of the thermal spray particles while a dense structure is formed by the melted surfaces of the thermal spray particles. Accordingly, it is possible to obtain the ceramic layer having a porous structure including an amount of pores required for securing heat-shielding properties while having a dense structure including vertical cracks required for securing sufficient durability.
- the ceramic layer in the manufacturing method for a thermal barrier coating, may be formed such that the vertical cracks are dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction, and that the porosity is 4% to 15%.
- the ceramic layer in the manufacturing method for a thermal barrier coating, may be formed such that the vertical cracks are dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction, and that the porosity is 9% to 15%.
- the ceramic layer in the manufacturing method for a thermal barrier coating, may be formed such that the vertical cracks are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction, and that the porosity is 9% to 10%.
- the thermal spray particles composed of YbSZ having the particle-size distribution in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m are used, it is possible to improve heat-shielding properties while securing sufficient durability.
- FIG. 1 is a schematic configurational view of a gas turbine according to an embodiment of the present invention.
- FIG. 2 is a schematic view showing an aspect in which a blade is fixed to a jig in the embodiment of the present invention.
- FIG. 3 is a sectional view showing a schematic configuration of a thermal barrier coating in the embodiment of the present invention.
- FIG. 4 is a graph indicating relationships between a 50% particle diameter of thermal spray particles in a cumulative particle-size distribution and various characteristics in the embodiment of the present invention.
- FIG. 4( a ) is a graph indicating a relationship between the 50% particle diameter in the cumulative particle-size distribution and the number of thermal spray passes.
- FIG. 4( b ) is a graph indicating a relationship between the 50% particle diameter in the cumulative particle-size distribution and thermal cycle durability.
- FIG. 4( c ) is a graph indicating a relationship between the 50% particle diameter in the cumulative particle-size distribution and thermal conductivity.
- FIG. 5 is a flowchart of a manufacturing method for thermal spray powder in the embodiment of the present invention.
- FIG. 6 is an enlarged photograph for explaining the thermal barrier coating in the embodiment of the present invention.
- FIGS. 1 to 6 an embodiment of the present invention will be described with reference to FIGS. 1 to 6 .
- a gas turbine 1 of this embodiment includes a compressor 2 , a combustor 3 , a turbine body 4 , and a rotor 5 .
- the compressor 2 takes in a large amount of air and compresses the air.
- the combustor 3 mixes compressed air A compressed by the compressor 2 with a fuel and combusts the mixture.
- the turbine body 4 converts thermal energy of a combustion gas G introduced from the combustor 3 into rotation energy.
- the thermal energy of the combustion gas G is converted into mechanical rotation energy by blowing the combustion gas G to blades (turbine members) 7 provided in the rotor 5 , and power is generated.
- blades (turbine members) 7 provided in the rotor 5 , and power is generated.
- a plurality of vanes (turbine members) 8 are provided on a casing 6 of the turbine body 4 .
- the blades 7 and the vanes 8 are alternately arranged in an axial direction of the rotor 5 .
- the rotor 5 transmits a portion of rotating power of the turbine body 4 to the compressor 2 so as to rotate the compressor 2 .
- the blade 7 of the turbine body 4 will be described as an example of the turbine member of the present invention.
- the blade 7 is a heat-resistant alloy substrate which is formed by a known heat-resistant alloy such as a Ni-based alloy.
- the blade 7 of the present embodiment includes a blade body portion 71 , a platform portion 72 , and a blade root portion (not shown).
- the blade body portion 71 is disposed in a combustion gas flow passage through which the high-temperature combustion gas G inside the casing 6 of the gas turbine 1 flows.
- the platform portion 72 is provided on a base end portion of the blade body portion 71 and has a surface which intersects a direction in which the blade body portion 71 extends.
- the blade root portion protrudes from the platform portion 72 toward a side opposite to the blade body portion 71 .
- a thermal barrier coating 100 is formed to cover the surface of the blade 7 which is the heat-resistant alloy substrate.
- the thermal barrier coating 100 is formed on each of the surface of the blade body portion 71 and the surface of the platform portion 72 on a side connected to the blade body portion 71 .
- the thermal barrier coating 100 of the present embodiment includes a metal bonding layer 200 which is laminated on the surface of the blade 7 and a ceramic layer 300 which is laminated on the surface of the metal bonding layer 200 .
- the metal bonding layer 200 prevents the ceramic layer 300 from being peeled and is formed as a bonding coat layer having excellent corrosion resistance and oxidation resistance.
- the metal bonding layer 200 is formed by thermally spraying metal thermal spray powder of an MCrAlY alloy which is thermal spray particles on the surface of the blade 7 .
- M of the MCrAlY alloy composing the metal bonding layer 200 indicates a metal element, and for example, indicates a single metal element such as NiCo, Ni, or Co, or a combination of two or more of them.
- the metal bonding layer 200 of the present embodiment is integrally laminated to cover each of the surface of the blade body portion 71 and the surface of the platform portion 72 on the side connected to the blade body portion 71 .
- the metal bonding layer 200 of the present embodiment is formed to have a film thickness of approximately 0.05 mm to 0.2 mm.
- the ceramic layer 300 is a top coat layer which is formed by thermally spraying the thermal spray particles toward the surface of the blade 7 on which the metal bonding layer 200 is formed.
- the ceramic layer 300 is a dense DVC (Dense Vertically Crack) coating in which vertical cracks C extending in a thickness direction of the ceramic layer 300 are dispersed in a surface direction in which a surface spreads, and a plurality of pores P are included inside the ceramic layer 300 .
- the vertical cracks C are dispersed such that the vertical cracks C per 1 mm is distributed at a pitch of 0.5 cracks/mm to 40 cracks/mm, and the ceramic layer 300 is formed such that the porosity is within a range of 4% to 15%.
- the ceramic layer 300 is formed to have a film thickness of approximately 0.2 mm to 1 mm.
- the vertical cracks C are dispersed such that the vertical cracks C per 1 mm are distributed at a pitch of 1 crack/mm to 6 cracks/mm, and the ceramic layer 300 is formed such that the porosity is within a range of 9% to 15%.
- the vertical cracks C are dispersed such that the vertical cracks C per 1 mm is distributed at a pitch of 1 crack/mm to 2 cracks/mm, and the ceramic layer 300 is formed such that the porosity is within a range of 9% to 10%.
- the porosity in the present embodiment is not an occupancy ratio of only the pores P per unit volume, and the porosity is an occupancy ratio of the vertical cracks C and the pores P combined. Accordingly, if the range of 9% to 10% in the porosity of the above-described ceramic layer 300 is expressed as the occupancy ratio of only the pores P per unit volume, preferably, the ceramic layer 300 of the present embodiment is formed such that the porosity of the ceramic layer 300 is within a range of 5% to 7%.
- the thermal spray particles forming the ceramic layer 300 are composed of YbS (ytterbia stabilized zirconia) which is ZrO 2 partially stabilized by Yb 2 O 3 .
- the thermal spray particles of the present embodiment are YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m.
- the reason why the 50% particle diameter in the cumulative particle-size distribution is set to 100 ⁇ m or less is because if the particle diameters of the thermal spray particles are too large and exceed 100 ⁇ m, the number of thermal spray passes until the film formation is completed significantly increases when thermal spraying is performed, and it is practically difficult to perform manufacturing.
- another reason is because if the particle diameters of the thermal spray particles exceed the 50% particle diameter in the cumulative particle-size distribution of 100 ⁇ m, it is difficult for the vertical cracks C to be formed in the ceramic layer 300 , and thermal cycle durability decreases.
- the reason why the 50% particle diameter in the cumulative particle-size distribution is set to 40 ⁇ m or more is because if the particle diameters are too small and below the 50% particle diameter in the cumulative particle-size distribution of 40 ⁇ m, the ceramic layer 300 becomes too dense, and porosity decreases. As a result, as shown in FIG. 4( c ) , the thermal conductivity of the ceramic layer 300 increases, and heat-shielding properties decrease.
- the cumulative particle-size distribution is a value which indicates the size of particles as powder, that is, as an aggregate.
- the cumulative particle-size distribution represents a plurality of measurement results by a distribution of an abundance ratio for each particle diameter.
- the 50% particle diameter in the cumulative particle-size distribution is also referred to as a median diameter.
- the 50% particle diameter in the cumulative particle-size distribution is a particle diameter at which the amount of particles having larger diameters becomes equal to the amount of particles having smaller diameters when the powder is divided into two at that particle diameter.
- the distribution of the abundance ratio for each particle diameter of the thermal spray particles can be measured using a laser scattering diffraction type particle-size distribution measuring device or the like.
- the thermal cycle durability for example, a thermal cycle test is performed using a device shown in FIG. 7 or 8 of Japanese Patent No. 4388466. From the viewpoint of the thermal cycle durability, an effective addition amount of Yb 2 O 3 is 4 wt % to 30 wt %.
- the thermal barrier coating 100 of the present embodiment can exert superior thermal cycle durability.
- the thermal cycle durability decreases. This is because the amount of monoclinic phases (m phases) remaining in the ceramic layer 300 increases and thereby the durability decreases in a case where the addition amount is less than 8 wt %, and the ceramic layer 300 easily becomes a tetragonal crystal and a ratio of t′ phases having excellent durability decreases and thereby the durability of the ceramic layer 300 decreases in a case where the addition amount exceeds 25 wt %.
- the addition amount of Yb 2 O 3 is 10 wt % to 25 wt %, and most preferably, the addition amount of Yb 2 O 3 is 12 wt % to 20 wt %. By setting the addition amount to these ranges, the thermal barrier coating 100 can have superior thermal cycle durability.
- the manufacturing method for a thermal barrier coating is performed by fixing the blade 7 on a jig 91 and thermally spraying thermal spray particles to the surface of the blade 7 using a thermal spray gun 92 .
- the manufacturing method for a thermal barrier coating of the present embodiment includes a metal bonding layer forming process of forming the metal bonding layer 200 on the surface of the blade 7 and a ceramic layer forming process of forming the ceramic layer 300 on the metal bonding layer 200 .
- the metal bonding layer 200 is formed by thermally spraying metal thermal spray powder to the surface of the blade 7 installed on the jig 91 .
- the metal bonding layer forming process of the present embodiment is performed on the surface of the blade body portion 71 of the blade 7 and the surface of the platform portion 72 on the side to which the blade body portion 71 is connected.
- the metal bonding layer 200 is formed by thermally spraying metal thermal spray powder of an MCrAlY alloy to the surface of the blade 7 using the thermal spray gun 92 by an atmospheric plasma thermal spraying method.
- the ceramic layer 300 is formed by thermally spraying thermal spray particles composed of YbSZ from above the metal bonding layer 200 formed in the metal bonding layer forming process toward the surface of the blade 7 .
- the ceramic layer 300 is formed by thermally spraying thermal spray particles composed of YbSZ having the particle-size distribution, in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m, to the metal bonding layer 200 formed on the surface of the blade 7 , by an atmospheric plasma thermal spraying method.
- the ceramic layer forming process is performed with the output of the thermal spray gun 92 set to a current of 500 A to 800 A and a voltage of 55V to 70V.
- a thermal spray distance which is a distance between an outlet of the thermal spray gun 92 and a surface to which the thermal spray particles are thermally sprayed is set to a range from a minimum distance required for the thermal spray to 80 mm or less, and more preferably, is set to 70 mm or less.
- the thermal spray distance is set to 70 mm.
- the thermal spray particles composed of YbSZ used in the present embodiment can be manufactured by the following procedure.
- the thermal spray particles composed of YbSZ, ZrO 2 powder and Yb 2 O 3 powder having a predetermined addition ratio are prepared (first processes S 11 and S 12 ).
- the prepared powders and appropriate binder and dispersant are mixed by a ball mill to prepare slurry (second process S 20 ).
- the prepared slurry is granulated by a spray dryer so as to be dried (third process S 30 ).
- the slurry is solid-solved by a diffusion heat treatment by which the slurry is heated to the range of 1200° C. to 1600° C. (fourth process S 40 ). Accordingly, the thermal spray particles composed of YbSZ having the particle-size distribution in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m are obtained.
- the ceramic layer 300 is formed by the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m.
- the thermal spray particles are thermally sprayed to the blade 7 to form the ceramic layer 300 , the surfaces of the thermal spray particles are melted while the cores thereof remain so as not to be melted. Accordingly, in the ceramic layer 300 , porous structures are partially formed by the remaining cores of the thermal spray particles while dense structures are formed by the melted surfaces of the thermal spray particles.
- the ceramic layer 300 in which the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in a surface direction, and of which the porosity which is an occupancy ratio per unit volume of the vertical cracks C and the pores P combined is approximately 9% to 10%.
- Comparative Example 1 of Table 1 even when YbSZ is the same as that of Example, in the ceramic layer which is formed by thermally spraying the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 30 ⁇ m, the vertical cracks C are dispersed at a pitch of 2 cracks/mm to 40 cracks/mm in the surface direction and the porosity which is an occupancy ratio per unit volume of the vertical cracks C and the pores P combined is approximately 8%.
- the ceramic layer 300 having the structure in which the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction and of which the porosity is approximately 9% to 10%.
- Example of Table 1 As shown in Example of Table 1, as for the characteristics of the ceramic layer 300 which is formed by the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 70 ⁇ m, a ratio of thermal conductivity (with respect to Comparative Example 3) is 1.2 to 1.5, and a ratio of thermal cycle durability (with respect to Comparative Example 3) is approximately 1.5. As is apparent from a comparison between Example and Comparative Example 1 of Table 1, the above-described characteristics are superior to characteristics of the ceramic layer which is formed by the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 30 ⁇ m.
- the thermal conductivity of the ceramic layer 300 of Example is lower than 1.6 to 1.8 which is the ratio of the thermal conductivity of the ceramic layer 300 of Comparative Example 1, and thus the heat-shielding properties of the ceramic layer 300 of Example are superior.
- the thermal cycle durability of the ceramic layer 300 of Comparative Example 1 is the same as 1.5 which is the ratio of the thermal cycle durability of the ceramic layer 300 of Example and thus, the ceramic layer 300 of Example secures sufficient durability.
- the ceramic layer 300 by forming the ceramic layer 300 using the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m, it is possible to obtain the ceramic layer 300 having a porous structure including the amount of pores P required for securing heat-shielding properties while having a dense structure including the vertical cracks C required for securing sufficient durability. Accordingly, in the thermal barrier coating 100 of the present embodiment, it is possible to improve heat-shielding properties while securing sufficient durability.
- the ceramic layer 300 is formed such that the vertical cracks C are dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction and the porosity is approximately 4% to 15%, it is possible to obtain, with high accuracy, the ceramic layer 300 having improved heat-shielding properties while securing sufficient durability. If the ceramic layer 300 is formed such that the vertical cracks C are dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction and the porosity is approximately 9% to 15%, it is possible to obtain higher performance.
- the ceramic layer 300 is formed such that the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction and the porosity is approximately 9% to 10%, it is possible to obtain, with higher accuracy, the ceramic layer 300 having improved heat-shielding properties while securing sufficient durability. Particularly, it is possible to obtain the ceramic layer 300 having higher performance by forming the ceramic layer 300 by thermal spray particles composed of YbSZ.
- Comparative Example 2 of Table 1 even when the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction by the thermal spray particles which are composed of YSZ instead of YbSZ, it is not possible to obtain sufficient heat-shielding properties.
- the thermal conductivity of the ceramic layer 300 of Example is lower than the thermal conductivity of the ceramic layer 300 of Comparative Example 2, and thus the ceramic layer 300 of Comparative Example 1 cannot obtain the heat-shielding properties which are equivalent to those of the ceramic layer 300 of Example.
- Comparative Example 3 of Table 1 if the thermal cycle durability in a case where the porosity of approximately 10% is realized by the porous structure which does not have the vertical cracks C is set as 1 (base), it is understood that the thermal cycle durability of Comparative Example 3 is lower than 1.3 which is the ratio of the thermal cycle durability of Comparative Example 2 having the same YSZ as the thermal spray particles. It is understood that the thermal cycle durability of Comparative Example 3 is lower than 1.5 which is the ratio of the thermal cycle durability of Example which has YbSZ as the thermal spray particles and includes the vertical cracks C, and is lower than 1.5 which is the ratio of the thermal cycle durability of Comparative Example 1 which has YbSZ as the thermal spray particles and includes the vertical cracks C.
- the ceramic layer 300 which is formed by the thermal spray particles composed of YSZ having the structure in which only the vertical cracks C are dispersed at the pitch of 1 crack/mm to 2 cracks/mm in the surface direction and the structure in which only the porosity is approximately 10%, in the ceramic layer 300 of the present embodiment, it is possible to obtain higher performance.
- Example and Comparative Examples 1 to 3 As is apparent from the comparisons between Example and Comparative Examples 1 to 3, it is understood that high-temperature erosion characteristics indicating friction characteristics under a high temperature environment at TBC surface temperature of 1100° C. indicate high performance. Accordingly, it is also possible to secure erosion resistance.
- the ceramic layer 300 by thermal spray particles composed of only YbSZ which hardly includes impurities such as a polyester resin and an acrylic resin. Accordingly, it is possible to include the amount of pores P required for improving the heat-shielding properties inside a dense structure having the vertical cracks C without performing a heat treatment or the like after the thermal spray. Therefore, it is possible to obtain the thermal barrier coating 100 having improved heat-shielding properties while securing sufficient durability using a small number of processes.
- the blade 7 which is the turbine member of the above-described embodiment, it is possible to prevent the blade 7 from being damaged due to exposure to a high temperature for a long period of time. Since intervals between maintenance periods can be extended, it is possible to decrease a frequency of stopping an operation of the gas turbine 1 .
- the metal bonding layer 200 or the ceramic layer 300 may be formed by a method other than that of the present embodiment.
- low pressure plasma spraying which is electrical thermal spraying other than atmospheric pressure plasma spraying may be used, or a flame thermal spraying method and high-speed flame thermal spraying which are gas type thermal spraying may be used.
- the metal bonding layer 200 or the ceramic layer 300 may be formed by a method other than the thermal spraying method and, for example, an electron beam physical vapor deposition method may be used.
- the metal bonding layer 200 and the ceramic layer 300 are each formed to have the same film thickness over the entire region.
- the present invention is not limited to this and the film thickness may be appropriately set according to conditions such as an environment in which these layers are to be used.
- the blade 7 is described as an example of the turbine member.
- the present invention is not limited to this.
- the turbine member may be the vane 8 .
- the output of the thermal spray gun 92 is set to a current of 500 A to 800 A and a voltage of 55V to 70V, and the thermal spray distance is set to 70 mm.
- the present invention is not limited to these conditions. Accordingly, in the ceramic layer forming process, the conditions such as the output or the thermal spray speed may be changed as long as the ceramic layer 300 can be formed such that the vertical cracks C are dispersed in the surface direction at the pitch of 0.5 cracks/mm to 40 cracks/mm and the porosity is 9% to 15%.
- thermal barrier coating 100 since the thermal spray particles composed of YbSZ having the particle-size distribution in which the 50% particle diameter in the cumulative particle-size distribution is 40 ⁇ m to 100 ⁇ m are used, it is possible to improve heat-shielding properties while securing sufficient durability.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- General Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Coating By Spraying Or Casting (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Abstract
A thermal barrier coating (100) includes a heat-resistant alloy substrate which is used in a turbine member and a ceramic layer (300) which is formed on the heat-resistant alloy substrate and in which vertical cracks (C) extending in a thickness direction are dispersed in a surface direction and a plurality of pores (P) are included on the inside. Thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm are thermally sprayed at a thermal spray distance of 80 mm or less, the vertical cracks (C) are dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction, and the ceramic layer (300) of which a porosity attributable to the vertical cracks (C) and the pores (P) combined is 4% to 15% is formed.
Description
- The present invention relates to a thermal barrier coating, a turbine member, a gas turbine, and a manufacturing method for a thermal barrier coating.
- Priority is claimed on Japanese Patent Application No. 2015-025194, filed on Feb. 12, 2015, the content of which is incorporated herein by reference.
- In a gas turbine, a temperature of combustion gas to be used is set high in order to improve efficiency of the gas turbine. A thermal barrier coating (TBC) is applied to surfaces of turbine blade members such as blades and vanes subjected to the combustion gas having a high temperature. The thermal barrier coating is a coating of a thermal spraying material having low thermal conductivity (for example, a ceramics-based material having low thermal conductivity) applied by thermal spraying to a surface of a turbine member which is an object to be thermally sprayed. Heat-shielding properties and durability of the turbine member are improved by the thermal barrier coating.
- For example, as described in
PTL 1, a thermal barrier coating includes a metal bonding layer which is an undercoat layer and a ceramic layer which is a top coat layer formed on the metal bonding layer, on a surface of a heat-resistant substrate serving as a base material. The ceramic layer is formed by thermally spraying a powder mixture of ceramic powder and resin powder onto the undercoat layer. The ceramic layer described inPTL 1 is so configured that vertical cracks which are cracks extending in a thickness direction and pores are dispersed in a surface direction. - [PTL 1] Japanese Unexamined Patent Application, First Publication No. 2013-181192
- A dense coating having the vertical cracks described in
PTL 1 is referred to as a DVC (Dense Vertically Crack) coating. Since the DVC coating is a dense structure having a vertically cracked structure, durability is improved. However, since the structure is dense in the DVC coating, porosity decreases, and heat-shielding properties are likely to decrease. - The present invention provides a thermal barrier coating in which heat-shielding properties can be improved while sufficient durability is secured, a turbine member, a gas turbine, and a manufacturing method for a thermal barrier coating.
- In order to achieve the above-described object, the present invention suggests the following means.
- According to a first aspect of the present invention, there is provided a thermal barrier coating, including: a heat-resistant alloy substrate which is used in a turbine member; and a ceramic layer which is formed on the heat-resistant alloy substrate, vertical cracks extending in a thickness direction being dispersed in a surface direction, a plurality of pores being included inside the ceramic layer, wherein thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm are thermally sprayed to form the ceramic layer.
- According to this configuration, since the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm are used, when the thermal spray particles are thermally sprayed on the heat-resistant alloy substrate to form the ceramic layer, surfaces of the thermal spray particles are melted while cores thereof remain so as not to be melted. Accordingly, in the ceramic layer, a porous structure is formed by the remaining cores of the thermal spray particles while a dense structure is formed by the melted surfaces of the thermal spray particles. Accordingly, it is possible to obtain the ceramic layer having a porous structure including an amount of pores required for securing heat-shielding properties while having a dense structure including vertical cracks required for securing sufficient durability.
- In the thermal barrier coating, in the ceramic layer, the vertical cracks may be dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction, and the porosity may be 4% to 15%.
- In the thermal barrier coating, in the ceramic layer, the vertical cracks may be dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction, and the porosity may be 9% to 15%.
- In the thermal barrier coating, in the ceramic layer, the vertical cracks may be dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction, and the porosity may be 9% to 10%.
- According to these configurations, it is possible to obtain, with high accuracy, the ceramic layer having improved heat-shielding properties while securing sufficient durability.
- According to a second aspect of the present invention, there is provided a turbine member on which the thermal barrier coating is formed.
- According to a third aspect of the present invention, there is provided a gas turbine including the turbine member.
- According to these configurations, it is possible to prevent the turbine member from being damaged due to exposure to a high temperature for a long period of time. Since intervals between maintenance periods can be extended, it is possible to decrease a frequency of stopping an operation of the gas turbine.
- According to a fourth aspect of the present invention, there is provided a manufacturing method for a thermal barrier coating, including a ceramic layer forming process of forming a ceramic layer on a heat-resistant alloy substrate used in a turbine member by thermally spraying thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm, wherein in the ceramic layer, vertical cracks extending in a thickness direction are dispersed in a surface direction and a plurality of pores are included inside the ceramic layer.
- According to this configuration, since the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm are used, when the thermal spray particles are thermally sprayed on the heat-resistant alloy substrate to form the ceramic layer, the surfaces of the thermal spray particles are melted while the cores thereof remain so as not to be melted. Accordingly, in the ceramic layer, a porous structure is formed by the remaining cores of the thermal spray particles while a dense structure is formed by the melted surfaces of the thermal spray particles. Accordingly, it is possible to obtain the ceramic layer having a porous structure including an amount of pores required for securing heat-shielding properties while having a dense structure including vertical cracks required for securing sufficient durability.
- In the manufacturing method for a thermal barrier coating, in the ceramic layer forming process, the ceramic layer may be formed such that the vertical cracks are dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction, and that the porosity is 4% to 15%.
- In the manufacturing method for a thermal barrier coating, in the ceramic layer forming process, the ceramic layer may be formed such that the vertical cracks are dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction, and that the porosity is 9% to 15%.
- In the manufacturing method for a thermal barrier coating, in the ceramic layer forming process, the ceramic layer may be formed such that the vertical cracks are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction, and that the porosity is 9% to 10%.
- According to these configurations, it is possible to obtain, with high accuracy, the ceramic layer having improved heat-shielding properties while securing sufficient durability.
- According to the present invention, since the thermal spray particles composed of YbSZ having the particle-size distribution in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm are used, it is possible to improve heat-shielding properties while securing sufficient durability.
-
FIG. 1 is a schematic configurational view of a gas turbine according to an embodiment of the present invention. -
FIG. 2 is a schematic view showing an aspect in which a blade is fixed to a jig in the embodiment of the present invention. -
FIG. 3 is a sectional view showing a schematic configuration of a thermal barrier coating in the embodiment of the present invention. -
FIG. 4 is a graph indicating relationships between a 50% particle diameter of thermal spray particles in a cumulative particle-size distribution and various characteristics in the embodiment of the present invention. -
FIG. 4(a) is a graph indicating a relationship between the 50% particle diameter in the cumulative particle-size distribution and the number of thermal spray passes. -
FIG. 4(b) is a graph indicating a relationship between the 50% particle diameter in the cumulative particle-size distribution and thermal cycle durability. -
FIG. 4(c) is a graph indicating a relationship between the 50% particle diameter in the cumulative particle-size distribution and thermal conductivity. -
FIG. 5 is a flowchart of a manufacturing method for thermal spray powder in the embodiment of the present invention. -
FIG. 6 is an enlarged photograph for explaining the thermal barrier coating in the embodiment of the present invention. - Hereinafter, an embodiment of the present invention will be described with reference to
FIGS. 1 to 6 . - As shown in
FIG. 1 , agas turbine 1 of this embodiment includes acompressor 2, acombustor 3, aturbine body 4, and arotor 5. - The
compressor 2 takes in a large amount of air and compresses the air. - The
combustor 3 mixes compressed air A compressed by thecompressor 2 with a fuel and combusts the mixture. - The
turbine body 4 converts thermal energy of a combustion gas G introduced from thecombustor 3 into rotation energy. In theturbine body 4, the thermal energy of the combustion gas G is converted into mechanical rotation energy by blowing the combustion gas G to blades (turbine members) 7 provided in therotor 5, and power is generated. In theturbine body 4, other than the plurality ofblades 7 provided on therotor 5 side, a plurality of vanes (turbine members) 8 are provided on acasing 6 of theturbine body 4. In theturbine body 4, theblades 7 and thevanes 8 are alternately arranged in an axial direction of therotor 5. - The
rotor 5 transmits a portion of rotating power of theturbine body 4 to thecompressor 2 so as to rotate thecompressor 2. - Hereinafter, in this embodiment, the
blade 7 of theturbine body 4 will be described as an example of the turbine member of the present invention. - As shown in
FIG. 2 , for example, theblade 7 is a heat-resistant alloy substrate which is formed by a known heat-resistant alloy such as a Ni-based alloy. Theblade 7 of the present embodiment includes ablade body portion 71, aplatform portion 72, and a blade root portion (not shown). Theblade body portion 71 is disposed in a combustion gas flow passage through which the high-temperature combustion gas G inside thecasing 6 of thegas turbine 1 flows. Theplatform portion 72 is provided on a base end portion of theblade body portion 71 and has a surface which intersects a direction in which theblade body portion 71 extends. The blade root portion protrudes from theplatform portion 72 toward a side opposite to theblade body portion 71. - As shown in
FIG. 3 , athermal barrier coating 100 is formed to cover the surface of theblade 7 which is the heat-resistant alloy substrate. In the surface of theblade 7, thethermal barrier coating 100 is formed on each of the surface of theblade body portion 71 and the surface of theplatform portion 72 on a side connected to theblade body portion 71. Thethermal barrier coating 100 of the present embodiment includes ametal bonding layer 200 which is laminated on the surface of theblade 7 and aceramic layer 300 which is laminated on the surface of themetal bonding layer 200. - The
metal bonding layer 200 prevents theceramic layer 300 from being peeled and is formed as a bonding coat layer having excellent corrosion resistance and oxidation resistance. For example, themetal bonding layer 200 is formed by thermally spraying metal thermal spray powder of an MCrAlY alloy which is thermal spray particles on the surface of theblade 7. Here, “M” of the MCrAlY alloy composing themetal bonding layer 200 indicates a metal element, and for example, indicates a single metal element such as NiCo, Ni, or Co, or a combination of two or more of them. Themetal bonding layer 200 of the present embodiment is integrally laminated to cover each of the surface of theblade body portion 71 and the surface of theplatform portion 72 on the side connected to theblade body portion 71. Themetal bonding layer 200 of the present embodiment is formed to have a film thickness of approximately 0.05 mm to 0.2 mm. - The
ceramic layer 300 is a top coat layer which is formed by thermally spraying the thermal spray particles toward the surface of theblade 7 on which themetal bonding layer 200 is formed. Theceramic layer 300 is a dense DVC (Dense Vertically Crack) coating in which vertical cracks C extending in a thickness direction of theceramic layer 300 are dispersed in a surface direction in which a surface spreads, and a plurality of pores P are included inside theceramic layer 300. In theceramic layer 300 of the present embodiment, the vertical cracks C are dispersed such that the vertical cracks C per 1 mm is distributed at a pitch of 0.5 cracks/mm to 40 cracks/mm, and theceramic layer 300 is formed such that the porosity is within a range of 4% to 15%. Theceramic layer 300 is formed to have a film thickness of approximately 0.2 mm to 1 mm. - Preferably, in the
ceramic layer 300, the vertical cracks C are dispersed such that the vertical cracks C per 1 mm are distributed at a pitch of 1 crack/mm to 6 cracks/mm, and theceramic layer 300 is formed such that the porosity is within a range of 9% to 15%. Particularly, more preferably, in theceramic layer 300, the vertical cracks C are dispersed such that the vertical cracks C per 1 mm is distributed at a pitch of 1 crack/mm to 2 cracks/mm, and theceramic layer 300 is formed such that the porosity is within a range of 9% to 10%. - The porosity in the present embodiment is not an occupancy ratio of only the pores P per unit volume, and the porosity is an occupancy ratio of the vertical cracks C and the pores P combined. Accordingly, if the range of 9% to 10% in the porosity of the above-described
ceramic layer 300 is expressed as the occupancy ratio of only the pores P per unit volume, preferably, theceramic layer 300 of the present embodiment is formed such that the porosity of theceramic layer 300 is within a range of 5% to 7%. - The thermal spray particles forming the
ceramic layer 300 are composed of YbS (ytterbia stabilized zirconia) which is ZrO2 partially stabilized by Yb2O3. The thermal spray particles of the present embodiment are YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm. - As shown in
FIG. 4(a) , the reason why the 50% particle diameter in the cumulative particle-size distribution is set to 100 μm or less is because if the particle diameters of the thermal spray particles are too large and exceed 100 μm, the number of thermal spray passes until the film formation is completed significantly increases when thermal spraying is performed, and it is practically difficult to perform manufacturing. In addition, as shown inFIG. 4(b) , another reason is because if the particle diameters of the thermal spray particles exceed the 50% particle diameter in the cumulative particle-size distribution of 100 μm, it is difficult for the vertical cracks C to be formed in theceramic layer 300, and thermal cycle durability decreases. - The reason why the 50% particle diameter in the cumulative particle-size distribution is set to 40 μm or more is because if the particle diameters are too small and below the 50% particle diameter in the cumulative particle-size distribution of 40 μm, the
ceramic layer 300 becomes too dense, and porosity decreases. As a result, as shown inFIG. 4(c) , the thermal conductivity of theceramic layer 300 increases, and heat-shielding properties decrease. - In the present embodiment, the cumulative particle-size distribution is a value which indicates the size of particles as powder, that is, as an aggregate. The cumulative particle-size distribution represents a plurality of measurement results by a distribution of an abundance ratio for each particle diameter. The 50% particle diameter in the cumulative particle-size distribution is also referred to as a median diameter. The 50% particle diameter in the cumulative particle-size distribution is a particle diameter at which the amount of particles having larger diameters becomes equal to the amount of particles having smaller diameters when the powder is divided into two at that particle diameter.
- For example, the distribution of the abundance ratio for each particle diameter of the thermal spray particles can be measured using a laser scattering diffraction type particle-size distribution measuring device or the like.
- In the
ceramic layer 300 composed of YbSZ, when an addition amount of Yb2O3 which is a stabilizer is increased to 2 wt % or more as an addition ratio of Yb2O3, an improvement in the thermal cycle durability starts. This effect works well until immediately before the addition amount reaches 35 wt %. For the thermal cycle durability, for example, a thermal cycle test is performed using a device shown in FIG. 7 or 8 of Japanese Patent No. 4388466. From the viewpoint of the thermal cycle durability, an effective addition amount of Yb2O3 is 4 wt % to 30 wt %. If the range of the addition amount of Yb2O3 is set to 8 wt % to 27 wt %, thethermal barrier coating 100 of the present embodiment can exert superior thermal cycle durability. In a case where the addition amount of Yb2O3 exceeds the above range, the thermal cycle durability decreases. This is because the amount of monoclinic phases (m phases) remaining in theceramic layer 300 increases and thereby the durability decreases in a case where the addition amount is less than 8 wt %, and theceramic layer 300 easily becomes a tetragonal crystal and a ratio of t′ phases having excellent durability decreases and thereby the durability of theceramic layer 300 decreases in a case where the addition amount exceeds 25 wt %. - More preferably, the addition amount of Yb2O3 is 10 wt % to 25 wt %, and most preferably, the addition amount of Yb2O3 is 12 wt % to 20 wt %. By setting the addition amount to these ranges, the
thermal barrier coating 100 can have superior thermal cycle durability. - Next, a manufacturing method for a thermal barrier coating of laminating the
thermal barrier coating 100 on the surface of theblade 7 will be described. - As shown in
FIG. 2 , the manufacturing method for a thermal barrier coating is performed by fixing theblade 7 on ajig 91 and thermally spraying thermal spray particles to the surface of theblade 7 using athermal spray gun 92. The manufacturing method for a thermal barrier coating of the present embodiment includes a metal bonding layer forming process of forming themetal bonding layer 200 on the surface of theblade 7 and a ceramic layer forming process of forming theceramic layer 300 on themetal bonding layer 200. - In the metal bonding layer forming process, the
metal bonding layer 200 is formed by thermally spraying metal thermal spray powder to the surface of theblade 7 installed on thejig 91. The metal bonding layer forming process of the present embodiment is performed on the surface of theblade body portion 71 of theblade 7 and the surface of theplatform portion 72 on the side to which theblade body portion 71 is connected. For example, in the metal bonding layer forming process, themetal bonding layer 200 is formed by thermally spraying metal thermal spray powder of an MCrAlY alloy to the surface of theblade 7 using thethermal spray gun 92 by an atmospheric plasma thermal spraying method. - In the ceramic layer forming process, the
ceramic layer 300 is formed by thermally spraying thermal spray particles composed of YbSZ from above themetal bonding layer 200 formed in the metal bonding layer forming process toward the surface of theblade 7. In the ceramic layer forming process of the present embodiment, theceramic layer 300 is formed by thermally spraying thermal spray particles composed of YbSZ having the particle-size distribution, in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm, to themetal bonding layer 200 formed on the surface of theblade 7, by an atmospheric plasma thermal spraying method. For example, preferably, the ceramic layer forming process is performed with the output of thethermal spray gun 92 set to a current of 500 A to 800 A and a voltage of 55V to 70V. In order to obtain theceramic layer 300 having a porous structure including the amount of pores P required for securing heat-shielding properties while having a dense structure including vertical cracks C required for securing sufficient durability, preferably, a thermal spray distance which is a distance between an outlet of thethermal spray gun 92 and a surface to which the thermal spray particles are thermally sprayed is set to a range from a minimum distance required for the thermal spray to 80 mm or less, and more preferably, is set to 70 mm or less. For example, in the ceramic layer forming process of the present embodiment, the thermal spray distance is set to 70 mm. - The thermal spray particles composed of YbSZ used in the present embodiment can be manufactured by the following procedure.
- As shown in
FIG. 5 , in the manufacturing method of the thermal spray particles composed of YbSZ, ZrO2 powder and Yb2O3 powder having a predetermined addition ratio are prepared (first processes S11 and S12). The prepared powders and appropriate binder and dispersant are mixed by a ball mill to prepare slurry (second process S20). Next, the prepared slurry is granulated by a spray dryer so as to be dried (third process S30). After the slurry is dried, the slurry is solid-solved by a diffusion heat treatment by which the slurry is heated to the range of 1200° C. to 1600° C. (fourth process S40). Accordingly, the thermal spray particles composed of YbSZ having the particle-size distribution in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm are obtained. - According to the above-described
thermal barrier coating 100 or the above-described manufacturing method for a thermal barrier coating, theceramic layer 300 is formed by the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm. When the thermal spray particles are thermally sprayed to theblade 7 to form theceramic layer 300, the surfaces of the thermal spray particles are melted while the cores thereof remain so as not to be melted. Accordingly, in theceramic layer 300, porous structures are partially formed by the remaining cores of the thermal spray particles while dense structures are formed by the melted surfaces of the thermal spray particles. - Specifically, as shown in Example of the following Table 1 or an enlarged photograph of
FIG. 6 , it is possible to form theceramic layer 300 in which the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in a surface direction, and of which the porosity which is an occupancy ratio per unit volume of the vertical cracks C and the pores P combined is approximately 9% to 10%. -
TABLE 1 Comparative Comparative Comparative Example Example 1 Example 2 Example 3 Thermal spray particle YbSZ YbSZ YSZ YSZ Thermal spray particle 70 30 41 40 diameter (d50) [μm] Micro- Porosity [%] 9 to 10 8 8 10 structure Pitch of vertical 1 to 2 2 to 40 0.8 to 79 Vertical crack crack [crack/mm] is not present Thermal conductivity * 1.2 to 1.5 1.6 to 1.8 2 1 Thermal cycle durability * 1.5 1.5 1.3 1 High-temperature erosion characteristic * 0.3 0.28 0.3 1 * indicate ratio based on Comparative Example 3 - In Comparative Example 1 of Table 1, even when YbSZ is the same as that of Example, in the ceramic layer which is formed by thermally spraying the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 30 μm, the vertical cracks C are dispersed at a pitch of 2 cracks/mm to 40 cracks/mm in the surface direction and the porosity which is an occupancy ratio per unit volume of the vertical cracks C and the pores P combined is approximately 8%. That is, in the case of the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm or less, it is difficult to obtain the
ceramic layer 300 having the structure in which the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction and of which the porosity is approximately 9% to 10%. - As shown in Example of Table 1, as for the characteristics of the
ceramic layer 300 which is formed by the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 70 μm, a ratio of thermal conductivity (with respect to Comparative Example 3) is 1.2 to 1.5, and a ratio of thermal cycle durability (with respect to Comparative Example 3) is approximately 1.5. As is apparent from a comparison between Example and Comparative Example 1 of Table 1, the above-described characteristics are superior to characteristics of the ceramic layer which is formed by the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 30 μm. That is, it is understood that the thermal conductivity of theceramic layer 300 of Example is lower than 1.6 to 1.8 which is the ratio of the thermal conductivity of theceramic layer 300 of Comparative Example 1, and thus the heat-shielding properties of theceramic layer 300 of Example are superior. It is understood that the thermal cycle durability of theceramic layer 300 of Comparative Example 1 is the same as 1.5 which is the ratio of the thermal cycle durability of theceramic layer 300 of Example and thus, theceramic layer 300 of Example secures sufficient durability. - Accordingly, by forming the
ceramic layer 300 using the thermal spray particles composed of YbSZ in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm, it is possible to obtain theceramic layer 300 having a porous structure including the amount of pores P required for securing heat-shielding properties while having a dense structure including the vertical cracks C required for securing sufficient durability. Accordingly, in thethermal barrier coating 100 of the present embodiment, it is possible to improve heat-shielding properties while securing sufficient durability. - If the
ceramic layer 300 is formed such that the vertical cracks C are dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction and the porosity is approximately 4% to 15%, it is possible to obtain, with high accuracy, theceramic layer 300 having improved heat-shielding properties while securing sufficient durability. If theceramic layer 300 is formed such that the vertical cracks C are dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction and the porosity is approximately 9% to 15%, it is possible to obtain higher performance. Particularly, if theceramic layer 300 is formed such that the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction and the porosity is approximately 9% to 10%, it is possible to obtain, with higher accuracy, theceramic layer 300 having improved heat-shielding properties while securing sufficient durability. Particularly, it is possible to obtain theceramic layer 300 having higher performance by forming theceramic layer 300 by thermal spray particles composed of YbSZ. - Specifically, as in Comparative Example 2 of Table 1, even when the vertical cracks C are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction by the thermal spray particles which are composed of YSZ instead of YbSZ, it is not possible to obtain sufficient heat-shielding properties. For example, it is understood that the thermal conductivity of the
ceramic layer 300 of Example is lower than the thermal conductivity of theceramic layer 300 of Comparative Example 2, and thus theceramic layer 300 of Comparative Example 1 cannot obtain the heat-shielding properties which are equivalent to those of theceramic layer 300 of Example. - As in Comparative Example 3 of Table 1, if the thermal cycle durability in a case where the porosity of approximately 10% is realized by the porous structure which does not have the vertical cracks C is set as 1 (base), it is understood that the thermal cycle durability of Comparative Example 3 is lower than 1.3 which is the ratio of the thermal cycle durability of Comparative Example 2 having the same YSZ as the thermal spray particles. It is understood that the thermal cycle durability of Comparative Example 3 is lower than 1.5 which is the ratio of the thermal cycle durability of Example which has YbSZ as the thermal spray particles and includes the vertical cracks C, and is lower than 1.5 which is the ratio of the thermal cycle durability of Comparative Example 1 which has YbSZ as the thermal spray particles and includes the vertical cracks C.
- Accordingly, compared to the
ceramic layer 300 which is formed by the thermal spray particles composed of YSZ having the structure in which only the vertical cracks C are dispersed at the pitch of 1 crack/mm to 2 cracks/mm in the surface direction and the structure in which only the porosity is approximately 10%, in theceramic layer 300 of the present embodiment, it is possible to obtain higher performance. - As is apparent from the comparisons between Example and Comparative Examples 1 to 3, it is understood that high-temperature erosion characteristics indicating friction characteristics under a high temperature environment at TBC surface temperature of 1100° C. indicate high performance. Accordingly, it is also possible to secure erosion resistance.
- It is possible to form the
ceramic layer 300 by thermal spray particles composed of only YbSZ which hardly includes impurities such as a polyester resin and an acrylic resin. Accordingly, it is possible to include the amount of pores P required for improving the heat-shielding properties inside a dense structure having the vertical cracks C without performing a heat treatment or the like after the thermal spray. Therefore, it is possible to obtain thethermal barrier coating 100 having improved heat-shielding properties while securing sufficient durability using a small number of processes. - According to the
blade 7 which is the turbine member of the above-described embodiment, it is possible to prevent theblade 7 from being damaged due to exposure to a high temperature for a long period of time. Since intervals between maintenance periods can be extended, it is possible to decrease a frequency of stopping an operation of thegas turbine 1. - Hereinbefore, the embodiment of the present invention is described in detail with reference to the drawings. However, configurations and combinations thereof in the embodiment are merely examples, and addition, omission, replacement, and other modifications of the configurations can be made within a scope which does not depart from the gist of the present invention. In addition, the present invention is not limited to the embodiment and is limited by only the claims.
- In addition, the
metal bonding layer 200 or theceramic layer 300 may be formed by a method other than that of the present embodiment. For example, low pressure plasma spraying which is electrical thermal spraying other than atmospheric pressure plasma spraying may be used, or a flame thermal spraying method and high-speed flame thermal spraying which are gas type thermal spraying may be used. Themetal bonding layer 200 or theceramic layer 300 may be formed by a method other than the thermal spraying method and, for example, an electron beam physical vapor deposition method may be used. - In the present embodiment, the
metal bonding layer 200 and theceramic layer 300 are each formed to have the same film thickness over the entire region. However, the present invention is not limited to this and the film thickness may be appropriately set according to conditions such as an environment in which these layers are to be used. - In the present embodiment, the
blade 7 is described as an example of the turbine member. The present invention is not limited to this. For example, the turbine member may be thevane 8. - In the ceramic layer forming process of the present embodiment, the output of the
thermal spray gun 92 is set to a current of 500 A to 800 A and a voltage of 55V to 70V, and the thermal spray distance is set to 70 mm. However, the present invention is not limited to these conditions. Accordingly, in the ceramic layer forming process, the conditions such as the output or the thermal spray speed may be changed as long as theceramic layer 300 can be formed such that the vertical cracks C are dispersed in the surface direction at the pitch of 0.5 cracks/mm to 40 cracks/mm and the porosity is 9% to 15%. - According to the above-described
thermal barrier coating 100 and the manufacturing method for a thermal barrier coating, since the thermal spray particles composed of YbSZ having the particle-size distribution in which the 50% particle diameter in the cumulative particle-size distribution is 40 μm to 100 μm are used, it is possible to improve heat-shielding properties while securing sufficient durability. -
-
- 1: gas turbine
- 2: compressor
- 3: combustor
- 4: turbine body
- 5: rotor
- A: compressed air
- G: combustion gas
- 6: casing
- 7: blade
- 71: blade body portion
- 72: platform portion
- 8: vane
- 100: thermal barrier coating
- 200: metal bonding layer
- 300: ceramic layer
- C: vertical crack
- P: pore
- 91: jig
- 92: thermal spray gun
- S11, S12: first process
- S20: second process
- S30: third process
- S40: fourth process
Claims (4)
1-5. (canceled)
6. A manufacturing method for a thermal barrier coating, comprising a ceramic layer forming process of forming a ceramic layer on a heat-resistant alloy substrate used in a turbine member by thermally spraying thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm at a thermal spray distance of 80 mm or less, wherein in the ceramic layer, vertical cracks extending in a thickness direction are dispersed in a surface direction, wherein the vertical cracks are dispersed at a pitch of 0.5 cracks/mm to 40 cracks/mm in the surface direction, wherein a plurality of pores are included inside the ceramic layer, and wherein a porosity of the ceramic layer attributable to the vertical cracks and the pores combined is 4% to 15%.
7. A manufacturing method for a thermal barrier coating, comprising a ceramic layer forming process of forming a ceramic layer on a heat-resistant alloy substrate used in a turbine member by thermally spraying thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm at a thermal spray distance of 80 mm or less, wherein in the ceramic layer, vertical cracks extending in a thickness direction are dispersed in a surface direction, wherein the vertical cracks are dispersed at a pitch of 1 crack/mm to 6 cracks/mm in the surface direction, wherein a plurality of pores are included inside the ceramic layer, and wherein a porosity of the ceramic layer attributable to the vertical cracks and the pores combined is 9% to 15%.
8. A manufacturing method for a thermal barrier coating, comprising a ceramic layer forming process of forming a ceramic layer on a heat-resistant alloy substrate used in a turbine member by thermally spraying thermal spray particles composed of YbSZ having a particle-size distribution in which a 50% particle diameter in a cumulative particle-size distribution is 40 μm to 100 μm at a thermal spray distance of 80 mm or less, wherein in the ceramic layer, vertical cracks extending in a thickness direction are dispersed in a surface direction, wherein the vertical cracks are dispersed at a pitch of 1 crack/mm to 2 cracks/mm in the surface direction, wherein a plurality of pores are included inside the ceramic layer, and wherein a porosity of the ceramic layer attributable to the vertical cracks and the pores combined is 9% to 10%.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2015-025194 | 2015-02-12 | ||
JP2015025194 | 2015-02-12 | ||
PCT/JP2016/053506 WO2016129521A1 (en) | 2015-02-12 | 2016-02-05 | Heat-shielding coating, turbine member, gas turbine, and manufacturing method for heat-shielding coating |
Publications (1)
Publication Number | Publication Date |
---|---|
US20180030584A1 true US20180030584A1 (en) | 2018-02-01 |
Family
ID=56614359
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US15/549,862 Abandoned US20180030584A1 (en) | 2015-02-12 | 2016-02-05 | Thermal barrier coating, turbine member, gas turbine, and manufacturing method for thermal barrier coating |
Country Status (6)
Country | Link |
---|---|
US (1) | US20180030584A1 (en) |
JP (1) | JPWO2016129521A1 (en) |
KR (1) | KR20170102962A (en) |
CN (1) | CN107208246A (en) |
DE (1) | DE112016000738T5 (en) |
WO (1) | WO2016129521A1 (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10808308B2 (en) * | 2016-06-08 | 2020-10-20 | Mitsubishi Heavy Industries, Ltd. | Thermal barrier coating, turbine member, and gas turbine |
CN113929474A (en) * | 2021-12-16 | 2022-01-14 | 矿冶科技集团有限公司 | Particulate matter for thermal barrier coating, preparation method of particulate matter, thermal barrier coating and engine |
US20220389835A1 (en) * | 2020-03-30 | 2022-12-08 | Mitsubishi Heavy Industries, Ltd. | Ceramic coating, turbine component, and gas turbine |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN110520599A (en) * | 2017-03-28 | 2019-11-29 | 三菱重工业株式会社 | Heat insulating coat film and turbine component |
US20210087695A1 (en) * | 2017-12-19 | 2021-03-25 | Oerlikon Metco (Us) Inc. | Erosion and cmas resistant coating for protecting ebc and cmc layers and thermal spray coating method |
CN109161889B (en) * | 2018-07-19 | 2020-05-22 | 西安交通大学 | Anti-sintering dual-mode composite structure thermal barrier coating and preparation process thereof |
CN117072253B (en) * | 2023-10-16 | 2024-01-09 | 西安交通大学 | Thermal barrier coating for high-temperature blade of heavy-duty gas turbine and design, manufacture and evaluation methods thereof |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3631982B2 (en) * | 2000-06-16 | 2005-03-23 | 三菱重工業株式会社 | Manufacturing method of thermal barrier coating material |
WO2002103074A1 (en) * | 2001-06-15 | 2002-12-27 | Mitsubishi Heavy Industries, Ltd. | Thermal barrier coating material and method for production thereof, gas turbine member using the thermal barrier coating material, and gas turbine |
JP2003160852A (en) * | 2001-11-26 | 2003-06-06 | Mitsubishi Heavy Ind Ltd | Thermal insulating coating material, manufacturing method therefor, turbine member and gas turbine |
CN101723667B (en) * | 2009-11-18 | 2012-09-05 | 北京航空航天大学 | Multielement rare earth oxide doped zirconia thermal barrier coating with craze crack structure and preparing method thereof |
EP2514850B1 (en) * | 2009-12-17 | 2017-07-26 | Mitsubishi Hitachi Power Systems, Ltd. | Method for producing a heat-shielding coating, turbine member provided with said heat-shielding coating, and gas turbine |
JP5705627B2 (en) * | 2011-04-18 | 2015-04-22 | 三菱重工業株式会社 | Heat-resistant member repair method, repair heat-resistant member |
-
2016
- 2016-02-05 US US15/549,862 patent/US20180030584A1/en not_active Abandoned
- 2016-02-05 JP JP2016574778A patent/JPWO2016129521A1/en not_active Withdrawn
- 2016-02-05 WO PCT/JP2016/053506 patent/WO2016129521A1/en active Application Filing
- 2016-02-05 CN CN201680008590.XA patent/CN107208246A/en active Pending
- 2016-02-05 DE DE112016000738.8T patent/DE112016000738T5/en not_active Withdrawn
- 2016-02-05 KR KR1020177022004A patent/KR20170102962A/en active Search and Examination
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10808308B2 (en) * | 2016-06-08 | 2020-10-20 | Mitsubishi Heavy Industries, Ltd. | Thermal barrier coating, turbine member, and gas turbine |
US20220389835A1 (en) * | 2020-03-30 | 2022-12-08 | Mitsubishi Heavy Industries, Ltd. | Ceramic coating, turbine component, and gas turbine |
US11970950B2 (en) * | 2020-03-30 | 2024-04-30 | Mitsubishi Heavy Industries, Ltd. | Ceramic coating, turbine component, and gas turbine |
CN113929474A (en) * | 2021-12-16 | 2022-01-14 | 矿冶科技集团有限公司 | Particulate matter for thermal barrier coating, preparation method of particulate matter, thermal barrier coating and engine |
Also Published As
Publication number | Publication date |
---|---|
WO2016129521A1 (en) | 2016-08-18 |
CN107208246A (en) | 2017-09-26 |
KR20170102962A (en) | 2017-09-12 |
DE112016000738T5 (en) | 2017-11-02 |
JPWO2016129521A1 (en) | 2017-12-21 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US20180030584A1 (en) | Thermal barrier coating, turbine member, gas turbine, and manufacturing method for thermal barrier coating | |
WO2017213113A1 (en) | Heat shielding coating, turbine member and gas turbine | |
JP2003160852A (en) | Thermal insulating coating material, manufacturing method therefor, turbine member and gas turbine | |
US6916551B2 (en) | Thermal barrier coating material, gas turbine parts and gas turbine | |
JP2006193828A (en) | Heat-shielding coating material, heat-shielding member, heat-shielding coating member, and method for production of the heat-shielding coating member | |
US20130202912A1 (en) | Process for producing thermal barrier coating, turbine member provided with thermal barrier coating, and gas turbine | |
JP2010235415A (en) | Material for thermal barrier coating, thermal barrier coating, turbine member, and gas turbine and method for producing material for thermal barrier coating | |
US20230082214A1 (en) | Coating method, coating layer, and turbine shroud | |
JP5656528B2 (en) | High temperature resistant member and gas turbine | |
JP5657048B2 (en) | High temperature resistant member and gas turbine | |
US20190119172A1 (en) | Coating structure, turbine part having same, and method for manufacturing coating structure | |
US20200048751A1 (en) | Thermal barrier coating formation method, thermal barrier coating, and high-temperature member | |
US20180023178A1 (en) | Production method for thermal spray particles, turbine member, gas turbine, and thermal spray particles | |
JP4388466B2 (en) | Gas turbine, thermal barrier coating material, manufacturing method thereof, and turbine member | |
US20170226620A1 (en) | Heat shielding coating and turbine member | |
US20190277143A1 (en) | High-temperature component for gas turbine, gas turbine blade and gas turbine | |
JP5693631B2 (en) | High temperature resistant member and gas turbine | |
JP2018172731A (en) | Thermal barrier coating, turbine blade, and production method of thermal barrier coating | |
US10947615B2 (en) | Thermal barrier coating film, turbine member, and thermal barrier coating method | |
CN116536611A (en) | Composition and method for producing the same |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: MITSUBISHI HITACHI POWER SYSTEMS, LTD., JAPAN Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:INOUE, YOSHIYUKI;TORIGOE, TAIJI;KUDO, DAISUKE;AND OTHERS;REEL/FRAME:043247/0475 Effective date: 20170626 |
|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |