CN114752881B - Preparation method of CMAS corrosion resistant thermal barrier coating and thermal barrier coating obtained by preparation method - Google Patents
Preparation method of CMAS corrosion resistant thermal barrier coating and thermal barrier coating obtained by preparation method Download PDFInfo
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- 238000005260 corrosion Methods 0.000 title claims abstract description 82
- 230000007797 corrosion Effects 0.000 title claims abstract description 67
- 239000012720 thermal barrier coating Substances 0.000 title claims abstract description 41
- 238000002360 preparation method Methods 0.000 title claims description 14
- 239000000919 ceramic Substances 0.000 claims abstract description 104
- 239000002243 precursor Substances 0.000 claims abstract description 40
- 238000000034 method Methods 0.000 claims abstract description 24
- 229910052751 metal Inorganic materials 0.000 claims abstract description 23
- 239000002184 metal Substances 0.000 claims abstract description 23
- 238000007750 plasma spraying Methods 0.000 claims abstract description 18
- 239000000758 substrate Substances 0.000 claims abstract description 12
- 239000002105 nanoparticle Substances 0.000 claims abstract description 11
- 239000002245 particle Substances 0.000 claims abstract description 5
- 238000005507 spraying Methods 0.000 claims description 39
- 239000007921 spray Substances 0.000 claims description 29
- 239000000243 solution Substances 0.000 claims description 28
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 15
- 239000002994 raw material Substances 0.000 claims description 13
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 12
- 239000001257 hydrogen Substances 0.000 claims description 12
- 229910052739 hydrogen Inorganic materials 0.000 claims description 12
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 10
- 239000008367 deionised water Substances 0.000 claims description 10
- 229910021641 deionized water Inorganic materials 0.000 claims description 10
- 230000008569 process Effects 0.000 claims description 10
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 7
- 239000007788 liquid Substances 0.000 claims description 7
- 239000011259 mixed solution Substances 0.000 claims description 7
- 229910052726 zirconium Inorganic materials 0.000 claims description 7
- NGDQQLAVJWUYSF-UHFFFAOYSA-N 4-methyl-2-phenyl-1,3-thiazole-5-sulfonyl chloride Chemical compound S1C(S(Cl)(=O)=O)=C(C)N=C1C1=CC=CC=C1 NGDQQLAVJWUYSF-UHFFFAOYSA-N 0.000 claims description 6
- 229910052727 yttrium Inorganic materials 0.000 claims description 6
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 6
- UJVRJBAUJYZFIX-UHFFFAOYSA-N nitric acid;oxozirconium Chemical compound [Zr]=O.O[N+]([O-])=O.O[N+]([O-])=O UJVRJBAUJYZFIX-UHFFFAOYSA-N 0.000 claims description 5
- 229910002077 partially stabilized zirconia Inorganic materials 0.000 claims description 4
- 238000004140 cleaning Methods 0.000 claims description 3
- 229910052769 Ytterbium Inorganic materials 0.000 claims description 2
- NAWDYIZEMPQZHO-UHFFFAOYSA-N ytterbium Chemical compound [Yb] NAWDYIZEMPQZHO-UHFFFAOYSA-N 0.000 claims description 2
- KUBYTSCYMRPPAG-UHFFFAOYSA-N ytterbium(3+);trinitrate Chemical compound [Yb+3].[O-][N+]([O-])=O.[O-][N+]([O-])=O.[O-][N+]([O-])=O KUBYTSCYMRPPAG-UHFFFAOYSA-N 0.000 claims description 2
- SIWVEOZUMHYXCS-UHFFFAOYSA-N oxo(oxoyttriooxy)yttrium Chemical compound O=[Y]O[Y]=O SIWVEOZUMHYXCS-UHFFFAOYSA-N 0.000 claims 1
- UZLYXNNZYFBAQO-UHFFFAOYSA-N oxygen(2-);ytterbium(3+) Chemical compound [O-2].[O-2].[O-2].[Yb+3].[Yb+3] UZLYXNNZYFBAQO-UHFFFAOYSA-N 0.000 claims 1
- 229940075624 ytterbium oxide Drugs 0.000 claims 1
- 229910003454 ytterbium oxide Inorganic materials 0.000 claims 1
- 238000009736 wetting Methods 0.000 abstract description 29
- 239000010410 layer Substances 0.000 description 99
- 238000000576 coating method Methods 0.000 description 41
- 239000011248 coating agent Substances 0.000 description 38
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- 238000012360 testing method Methods 0.000 description 10
- 238000012876 topography Methods 0.000 description 10
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- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- 244000137852 Petrea volubilis Species 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000004506 ultrasonic cleaning Methods 0.000 description 5
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- 239000007789 gas Substances 0.000 description 4
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- DUFCMRCMPHIFTR-UHFFFAOYSA-N 5-(dimethylsulfamoyl)-2-methylfuran-3-carboxylic acid Chemical compound CN(C)S(=O)(=O)C1=CC(C(O)=O)=C(C)O1 DUFCMRCMPHIFTR-UHFFFAOYSA-N 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000005240 physical vapour deposition Methods 0.000 description 3
- 239000011148 porous material Substances 0.000 description 3
- 238000005488 sandblasting Methods 0.000 description 3
- RUDFQVOCFDJEEF-UHFFFAOYSA-N yttrium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Y+3].[Y+3] RUDFQVOCFDJEEF-UHFFFAOYSA-N 0.000 description 3
- 230000004888 barrier function Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000005328 electron beam physical vapour deposition Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
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- 238000012986 modification Methods 0.000 description 2
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- 239000002086 nanomaterial Substances 0.000 description 2
- 230000035515 penetration Effects 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000013461 design Methods 0.000 description 1
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- 239000012466 permeate Substances 0.000 description 1
- 238000011112 process operation Methods 0.000 description 1
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- 238000005245 sintering Methods 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 230000007480 spreading Effects 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
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- 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
- C23C4/134—Plasma spraying
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y40/00—Manufacture or treatment of nanostructures
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- 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
- C23C18/00—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating
- C23C18/02—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating by thermal decomposition
- C23C18/12—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating by thermal decomposition characterised by the deposition of inorganic material other than metallic material
- C23C18/1204—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating by thermal decomposition characterised by the deposition of inorganic material other than metallic material inorganic material, e.g. non-oxide and non-metallic such as sulfides, nitrides based compounds
- C23C18/1208—Oxides, e.g. ceramics
- C23C18/1216—Metal oxides
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- 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
- C23C18/00—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating
- C23C18/02—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating by thermal decomposition
- C23C18/12—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating by thermal decomposition characterised by the deposition of inorganic material other than metallic material
- C23C18/125—Process of deposition of the inorganic material
- C23C18/1258—Spray pyrolysis
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- 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
- C23C18/00—Chemical coating by decomposition of either liquid compounds or solutions of the coating forming compounds, without leaving reaction products of surface material in the coating; Contact plating
- C23C18/14—Decomposition by irradiation, e.g. photolysis, particle radiation or by mixed irradiation sources
- C23C18/145—Radiation by charged particles, e.g. electron beams or ion irradiation
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
- C23C4/073—Metallic material containing MCrAl or MCrAlY alloys, where M is nickel, cobalt or iron, with or without non-metal elements
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Abstract
本发明涉及一种抗CMAS腐蚀热障涂层的制备方法，其包括在基体上制备金属粘结层；在金属粘结层上制备陶瓷主体层；在陶瓷主体层上采用溶液前驱体等离子喷涂制备抗腐蚀陶瓷顶层，其中，直径为0.2～1.5μm的微纳米颗粒在陶瓷主体层的表面堆叠成直径为10～50μm的半球状或直径为1～10μm的团簇状凸起，半球状或团簇状凸起与其表面的小颗粒共同构成微纳双尺度结构。本发明还涉及一种由此得到的热障涂层，其包括金属粘结层、陶瓷主体层和抗腐蚀陶瓷顶层。根据本发明的抗CMAS腐蚀热障涂层，通过抗腐蚀陶瓷顶层阻碍熔融CMAS在热障涂层表面润湿与附着，使热障涂层与CMAS熔体之间的接触面积达到最小化。
The invention relates to a method for preparing a thermal barrier coating resistant to CMAS corrosion, which includes preparing a metal bonding layer on a substrate; preparing a ceramic body layer on the metal bonding layer; and preparing the ceramic body layer by plasma spraying with a solution precursor. Anti-corrosion ceramic top layer, in which micro-nanoparticles with a diameter of 0.2 to 1.5 μm are stacked on the surface of the main ceramic layer to form hemispheres with a diameter of 10 to 50 μm or cluster-like protrusions with a diameter of 1 to 10 μm, hemispheres or clusters. The clustered protrusions and the small particles on their surface together form a micro-nano dual-scale structure. The invention also relates to a thermal barrier coating thus obtained, which includes a metal bonding layer, a ceramic body layer and a corrosion-resistant ceramic top layer. According to the anti-CMAS corrosion thermal barrier coating of the present invention, the anti-corrosion ceramic top layer prevents the molten CMAS from wetting and adhering to the surface of the thermal barrier coating, thereby minimizing the contact area between the thermal barrier coating and the CMAS melt.
Description
Technical Field
The invention relates to corrosion and protection of a thermal barrier coating, in particular to a preparation method of a CMAS corrosion resistant thermal barrier coating and the thermal barrier coating obtained by the preparation method.
Background
Advanced gas turbine engines are the core power devices of various aerospace vehicles and large ocean vessels, and are also the main conversion devices of power plants and energy industries. The turbine front inlet temperature of the primary aeroengine with the thrust weight ratio of 10 is 1850-1988K at present, and the turbine front design inlet temperature of the primary aeroengine with the thrust weight ratio of 12-15 reaches 2100-2200K, which is far higher than the limit temperature which can be born by the high-temperature alloy materials used for the turbine blades at present. In order to solve the problem, a coating with a thermal barrier function, namely a thermal barrier coating (Thermal Barrier Coatings, TBCs), can be sprayed on the surface of the high-temperature alloy to reduce the surface temperature of the high-temperature alloy and provide guarantee for the normal operation of the engine at a higher service temperature.
The TBCs are prepared by various methods, and the coatings prepared by different preparation processes also have different structures and performances. Common fabrication processes are atmospheric Plasma spray process (Atmospheric Plasma Spraying, APS), electron beam physical vapor deposition process (Electron Beam Physical Vapor Deposition, EB-PVD), plasma spray-physical vapor deposition process (PS-PVD), and the like. The coating prepared by the APS process has a layered structure, has more pores and microcracks and is parallel to the substrate; the coating prepared by the EB-PVD process has a typical columnar crystal structure, and gaps between columnar crystals are vertical to substrates; the coating prepared by the PS-PVD process has a dish-shaped columnar crystal. In addition, solution precursor plasma spraying (Solution Precursor Plasma Spray, SPPS) uses a solution precursor instead of a powder material in conventional plasma spraying, and can produce a coating layer having a nanostructure composed of a large number of fine particles, which has attracted attention in recent years.
With increasing engine operating temperature, a major component is CaO, mgO, al 2 O 3 And SiO 2 Will melt and adhere to the TBC surface and pose a serious hazard to the TBC. On one hand, CMAS is adsorbed and deposited on the surface of the coating, so that air film cooling holes on the surface of the coating are easily blocked, the cooling effect is reduced, and the temperature field and the stress field of the coating are further changed; on the other hand, the molten CMAS at high temperature permeates into the thermal barrier coating, accelerates the sintering and phase change instability of the coating, and greatly reduces the service life and the heat insulation capacity of the coating. The most commonly used ceramic materials of the current thermal barrier coating systems, 6-8wt% yttria partially stabilized zirconia (6-8 YSZ), are not resistant to CMAS corrosion.
CMAS protection methods can be classified into three types, namely, sacrificial type, dense impermeable type and non-wetting type, depending on the corrosion protection mechanism. Certain components within the sacrificial protective coating will react with environmental deposits to produce more difficult to penetrate materials. The impermeable coating is characterized by a continuous, dense, crack-free, direct barrier to melt penetration by physical features. The non-wetting protection method is to obtain a non-wetting surface to the molten CMAS by adopting a coating material which is non-wetting to the interface of the molten CMAS or changing the microstructure of the surface layer of TBCs, so that the contact between the coating and the melt is minimized.
At present, the sacrificial type and compact impermeable type protection methods are more, and corresponding patents are available at home and abroad. However, there is a thermal mismatch problem between the material of the sacrificial protection method and the YSZ material, and the structure of the dense impermeable protection method results in a low strain tolerance of the coating, and the thermal cycle performance of the coating is poor, which limits the large-scale application of the coating. The non-wetting type protection method is less common, and the published patent (patent number: CN 201610590053.2) adopts a PS-PVD process to prepare the CMAS corrosion resistant coating, so that the surface of the CMAS corrosion resistant coating has a nano structure, and has good CMAS adhesion resistance and wetting property. However, the PS-PVD coating has vertical pores, provides a channel for molten CMAS penetration, and is relatively expensive to manufacture.
Disclosure of Invention
In order to solve the problems that the thermal barrier coating in the prior art cannot effectively resist CMAS corrosion and the like, the invention provides a preparation method of the CMAS corrosion resistant thermal barrier coating and the thermal barrier coating obtained by the preparation method.
According to one aspect of the invention, there is provided a method of preparing a CMAS corrosion resistant thermal barrier coating comprising the steps of: s1, preparing a metal bonding layer on a substrate; s2, preparing a ceramic main body layer on the metal bonding layer; s3, preparing an anti-corrosion ceramic top layer by adopting solution precursor plasma spraying (Solution Precursor Plasma Spray, SPPS) on the ceramic main body layer, wherein micro-nano particles with the diameter of 0.2-1.5 mu m are stacked on the surface of the ceramic main body layer to form hemispherical protrusions with the diameter of 10-50 mu m or clustered protrusions with the diameter of 1-10 mu m, and the hemispherical protrusions or clustered protrusions and small particles on the surface of the hemispherical protrusions or clustered protrusions form a micro-nano double-scale structure.
Preferably, the step S1 further comprises sand blasting pretreatment and ultrasonic cleaning of the substrate before preparing the metal bonding layer.
Preferably, the material of the matrix is a high temperature nickel-based alloy IN738.
Preferably, the step S1 prepares the metal bonding layer using Atmospheric Plasma Spraying (APS).
Preferably, the material of the metal bonding layer is NiCrAlY.
Preferably, the step S2 prepares the ceramic body layer using Atmospheric Plasma Spraying (APS).
Preferably, the material of the ceramic body layer is YSZ.
Preferably, the step S3 comprises the following sub-steps: s31, dissolving a precursor raw material in a mixed solution of deionized water and absolute ethyl alcohol to prepare a solution precursor; and S32, spraying the solution precursor on the surface of the ceramic main body layer to form the corrosion-resistant ceramic top layer.
Preferably, the substep S31 is preceded by sanding and ultrasonic cleaning of the ceramic body layer. In a preferred embodiment, the ceramic body layer is sanded on 1000# sandpaper and 2000# sandpaper in sequence.
Preferably, the ceramic body layer is polished to a roughness of 1.0 to 4.5 μm. In a preferred embodiment, the surface roughness is controlled to be about 1.8 to 2.5 μm.
Preferably, the material of the corrosion resistant ceramic top layer is yttria partially stabilized zirconia (YSZ) or ytterbia yttria partially stabilized zirconia (YbYSZ). When the material of the top layer of the anti-corrosion ceramic is YSZ, the yttrium source of the precursor raw material is yttrium nitrate, and the zirconium source is zirconyl nitrate or zirconium acetate. When the material of the anti-corrosion ceramic top layer is YbYSZ, the yttrium source of the precursor raw material is yttrium nitrate, the zirconium source is zirconyl nitrate, and the ytterbium source is ytterbium nitrate.
Preferably, the volume ratio of deionized water to absolute ethyl alcohol of the mixed solution is 3:7-7:3. In a preferred embodiment, the volume ratio of deionized water to absolute ethanol of the mixed solution is 1:1.
Preferably, the concentration of Zr element in the solution precursor is 0.75mol/L to 1.5mol/L. In a preferred embodiment, the Zr element concentration of the solution precursor is 0.75mol/L.
Preferably, the micro-nano particles of the corrosion resistant ceramic top layer are stacked as hemispherical protrusions on the surface of the ceramic body layer by shadow effect. In a preferred embodiment, the hemispherical protrusions have a diameter of 17 to 30 μm. In a preferred embodiment, the hemispherical shape has a diameter of 19 to 35 μm.
It should be appreciated that the micro-nano particles of the corrosion resistant ceramic top layer are deposited in clusters on the surface of the ceramic body layer by shadow effect to form protrusions. In a preferred embodiment, the cluster-shaped projections have a diameter of less than 10 μm.
Preferably, said substep S32 comprises: the ceramic main body layer is preheated to 380-420 ℃ by a spray gun and then sprayed, the spraying voltage is 38-42V, the spraying current is 770-830A, the main air pressure is 0.4-0.5 MPa, the hydrogen pressure is 0.2-0.3 MPa, the moving speed of the spray gun is 200-600 mm/s, the spraying distance is 30-50 mm, and the liquid feeding flow is 25-35 ml/min. In a preferred embodiment, the ceramic body layer is preheated to 400 ℃ by a spray gun, then sprayed, the spraying voltage is 40V, the spraying current is 800A, the main air pressure is 0.47MPa, the hydrogen pressure is 0.25MPa, the moving speed of the spray gun is 400-600 mm/s, the spraying distance is 30-40 mm, and the liquid feeding flow is 30ml/min.
According to another aspect of the invention, there is provided a CMAS corrosion resistant thermal barrier coating comprising a metallic bond coat, a ceramic body layer, and a corrosion resistant ceramic top layer. Particularly, according to the CMAS corrosion resistant thermal barrier coating provided by the invention, the spreading and wetting of molten CMAS can be effectively prevented, the wetting diameter can be reduced to 50% of that of a conventional APS thermal barrier coating, and the CMAS corrosion resistant performance of the thermal barrier coating is improved.
Preferably, the ceramic body layer has a thickness of 250 to 350 μm.
Preferably, the thickness of the corrosion resistant ceramic top layer is 20 to 80 μm. In a preferred embodiment, the thickness of the corrosion resistant ceramic top layer is controlled to be around 50 μm.
According to the preparation method of the CMAS corrosion resistant thermal barrier coating, the solution precursor plasma spraying is adopted to prepare the corrosion resistant ceramic top layer, the solution precursor is adopted to replace the powder material in the traditional plasma spraying, and the prepared corrosion resistant ceramic top layer is formed by stacking a large number of tiny micro-nano particles. The anti-CMAS corrosion resistant thermal barrier coating corrosion resistant ceramic top layer has a non-wetting corrosion resistant mechanism, is non-wetting to molten CMAS, and prevents the molten CMAS from wetting and adhering to the surface of the thermal barrier coating, so that the contact area between the thermal barrier coating and CMAS melt is minimized. That is, the micro-nano particles of the anti-corrosion ceramic top layer enable the coating to have good hydrophobic property and CMAS wetting property, the contact angle of water and the anti-corrosion ceramic top layer can reach 150 degrees at normal temperature, compared with the conventional APS coating at 1300 ℃, the steady-state contact angle of the anti-corrosion ceramic top layer surface melting CMAS is increased by about 3 times, and the wetting diameter is reduced to 50%. In addition, according to the CMAS corrosion resistant thermal barrier coating, the corrosion resistant ceramic top layer prepared by solution precursor plasma spraying has loose structure, fine pores, uniform distribution and larger strain tolerance, and can effectively relieve thermal stress during thermal cycle and prolong the service life of the coating. Moreover, the preparation method of the CMAS corrosion resistant thermal barrier coating has the advantages of simple and accurate process operation and lower cost.
Drawings
FIG. 1 is a schematic structural view of a CMAS corrosion resistant thermal barrier coating made in accordance with the present invention;
FIG. 2A is a graph (500 times magnification) of the topography of the top layer of the corrosion resistant ceramic prepared in example 1;
FIG. 2B is a graph (at 2500 Xmagnification) of the topography of the top layer of the corrosion resistant ceramic prepared in example 1;
FIG. 2C is a cross-sectional profile (500 x magnification) of the corrosion resistant ceramic top layer prepared in example 1;
FIG. 3A is a macroscopic top view of the coating prepared in example 1 after 5 minutes CMAS wetting test;
FIG. 3B is a macroscopic top view of the coating prepared in example 1 after 10 minutes CMAS wetting test;
FIG. 3C is a macroscopic top view of the coating prepared in example 1 after 20 minutes CMAS wetting test;
FIG. 4A is a macroscopic top view of a conventional APS coating after 5 minutes CMAS wetting test;
FIG. 4B is a macroscopic top view of a conventional APS coating after 10 minutes CMAS wetting test;
FIG. 4C is a macroscopic top view of a conventional APS coating after 20 minutes CMAS wetting test;
FIG. 5 is a schematic view showing the contact angle of the surface of the top layer of the corrosion-resistant ceramic prepared in example 1 with water;
FIG. 6A is a graph (500 times magnification) of the topography of the top layer of the corrosion resistant ceramic prepared in example 2;
FIG. 6B is a graph (1700 times magnification) of the topography of the top layer of the corrosion resistant ceramic prepared in example 2;
FIG. 7A is a graph (1000 times magnified) of the topography of the top layer of the corrosion resistant ceramic prepared in example 3;
FIG. 7B is a graph (magnification 5000 times) of the topography of the top layer of the corrosion resistant ceramic prepared in example 3;
FIG. 8 is a CMAS contact angle comparison of a conventional APS coating with a corrosion resistant ceramic top layer;
fig. 9 is a CMAS wet-out diameter comparison of a conventional APS coating with a corrosion resistant ceramic top layer.
Detailed Description
Preferred embodiments of the present invention will be described in detail with reference to the accompanying drawings.
Example 1
The matrix of the high temperature nickel-base alloy IN738 (see fig. 1) was grit blasted and ultrasonically cleaned.
An NiCrAlY metallic bond coat was prepared on the substrate using Atmospheric Plasma Spray (APS) (see fig. 1). Specifically, after preheating a substrate to 400 ℃ by using a spray gun, niCrAlY powder is sprayed to prepare a metal bonding layer. The spraying voltage and current are respectively 60V and 500A, the main air pressure is 0.47MPa, and the hydrogen pressure is 0.25MPa. The moving speed of the spray gun is set to be 500mm/s, the spraying distance is 100mm, the powder feeding rotating speed is controlled to be 1.2r/min, and the thickness of the metal bonding layer is controlled to be about 100 mu m.
YSZ ceramic bulk layers were prepared on the metallic bond coat using Atmospheric Plasma Spray (APS) (see fig. 1). Specifically, a ceramic body layer was prepared by spraying YSZ powder after preheating the metal bond coat to 500 ℃ using a spray gun. The spraying voltage and current were 62V and 650A, respectively, the main gas pressure was 0.47MPa, and the hydrogen pressure was 0.25MPa. The moving speed of the spray gun is set to 150mm/s, the spraying distance is 80mm, the powder feeding rotating speed is controlled to 1.5r/min, and the thickness of the ceramic main body layer is controlled to about 300 mu m.
The method for preparing the corrosion-resistant ceramic top layer with the micro-nano double-scale structure by adopting Solution Precursor Plasma Spraying (SPPS) on the ceramic main body layer comprises the following specific steps:
sequentially polishing the ceramic main body layer on 1000# sand paper and 2000# sand paper, controlling the surface roughness to be about 2.5 mu m, and ultrasonically cleaning;
dissolving raw materials into a mixed solution of deionized water and absolute ethyl alcohol to prepare a solution precursor, wherein a yttrium source of a YSZ solution precursor raw material is yttrium nitrate, a zirconium source is zirconyl nitrate, wherein the concentration of Zr element in the precursor is 0.75mol/L, and the volume ratio of the deionized water to the absolute ethyl alcohol is 1:1;
and spraying the solution precursor on the surface of the ceramic main body layer to form the corrosion-resistant ceramic top layer. Specifically, the ceramic main body layer is preheated to 400 ℃ by using a spray gun, then is sprayed, the spraying voltage is 40V, the spraying current is 800A, the main air pressure is 0.47MPa, the hydrogen pressure is 0.25MPa, the moving speed of the spray gun is 400mm/s, the spraying distance is 30mm, the liquid feeding flow is 30ml/min, and the thickness of the anti-corrosion ceramic top layer is controlled to be about 50 mu m.
Fig. 2A and 2B are surface topography diagrams of the prepared anti-corrosion ceramic top layer, and fig. 2C is a cross-sectional topography diagram of the prepared anti-corrosion ceramic top layer, which can be seen from the figure, the anti-corrosion ceramic top layer is formed by stacking micro-nano particles with the diameter of 0.2-1.5 μm, the thickness is about 50 μm, and due to the shadow effect, the micro-nano particles are stacked into hemispheres on the surface of the ceramic main body layer, and the diameter is 19-35 μm.
CMAS powder was pressed into a cylinder of depth and diameter 1mm to form small cylindrical blocks, which were placed on the surface of the coating. The samples were placed in a 1300 ℃ ceramic fiber oven, and removed after heat treatment for various times (5 min, 10min, and 20 min), the results are shown in fig. 3A-3C. As can be seen from comparison of the conventional APS coating test results in FIGS. 4A-4C, the wetting diameter of the molten CMAS on the surface of the top layer of the corrosion-resistant ceramic is obviously reduced, the contact angle is increased, the wetting state is stabilized earlier, and the CMAS wetting resistance of the coating is obviously improved.
The water contact angle measurements were carried out on the corrosion resistant ceramic top layer, and the results were all between 152 and 159 degrees, as shown in fig. 5.
Example 2
The high-temperature nickel-based alloy IN738 matrix is subjected to sand blasting pretreatment and ultrasonic cleaning.
And preparing the NiCrAlY metal bonding layer on the substrate by adopting atmospheric plasma spraying. Specifically, after preheating a substrate to 400 ℃ by using a spray gun, niCrAlY powder is sprayed to prepare a metal bonding layer. The spraying voltage and current are respectively 60V and 500A, the main air pressure is 0.47MPa, and the hydrogen pressure is 0.25MPa. The moving speed of the spray gun is set to be 500mm/s, the spraying distance is 100mm, the powder feeding rotating speed is controlled to be 1.2r/min, and the thickness of the metal bonding layer is controlled to be about 100 mu m.
And preparing the YSZ ceramic main body layer on the metal bonding layer by adopting atmospheric plasma spraying. Specifically, a ceramic body layer was prepared by spraying YSZ powder after preheating the metal bond coat to 500 ℃ using a spray gun. The spraying voltage and current were 62V and 650A, respectively, the main gas pressure was 0.47MPa, and the hydrogen pressure was 0.25MPa. The moving speed of the spray gun is set to 150mm/s, the spraying distance is 80mm, the powder feeding rotating speed is controlled to 1.5r/min, and the thickness of the ceramic main body layer is controlled to about 250 mu m.
The method for preparing the corrosion-resistant ceramic top layer with the micro-nano double-scale structure by adopting solution precursor plasma spraying on the ceramic main body layer comprises the following specific steps:
sequentially polishing the ceramic main body layer on 1000# sand paper and 2000# sand paper, controlling the surface roughness to be about 1.8 mu m, and ultrasonically cleaning;
dissolving raw materials into a mixed solution of deionized water and absolute ethyl alcohol to prepare a solution precursor, wherein a yttrium source of a YSZ solution precursor raw material is yttrium nitrate, a zirconium source is zirconyl nitrate, wherein the concentration of Zr element in the precursor is 1mol/L, and the volume ratio of the deionized water to the absolute ethyl alcohol is 7:3;
and spraying the solution precursor on the surface of the ceramic main body layer to form the corrosion-resistant ceramic top layer. Specifically, the ceramic main body layer is preheated to 380 ℃ by using a spray gun, then is sprayed, the spraying voltage is 38V, the spraying current is 830A, the main air pressure is 0.5MPa, the hydrogen pressure is 0.2MPa, the moving speed of the spray gun is 200mm/s, the spraying distance is 40mm, the liquid feeding flow is 25ml/min, and the thickness of the anti-corrosion ceramic top layer is controlled to be about 80 mu m.
FIGS. 6A and 6B are surface topography diagrams of the prepared corrosion-resistant ceramic top layer, and it can be seen that the corrosion-resistant ceramic top layer is also formed by stacking micro-nano particles with diameters of 0.2-1.5 μm and is stacked into a hemispherical shape with diameters of 17-30 μm.
The resulting coating was subjected to CMAS wetting test, again with a smaller wetting diameter and a larger contact angle. The contact angles with water were measured to be between 150 and 156 degrees.
Example 3
The high-temperature nickel-based alloy IN738 matrix is subjected to sand blasting pretreatment and ultrasonic cleaning.
And preparing the NiCrAlY metal bonding layer on the substrate by adopting atmospheric plasma spraying. Specifically, after preheating a substrate to 400 ℃ by using a spray gun, niCrAlY powder is sprayed to prepare a metal bonding layer. The spraying voltage and current are respectively 60V and 500A, the main air pressure is 0.47MPa, and the hydrogen pressure is 0.25MPa. The moving speed of the spray gun is set to be 500mm/s, the spraying distance is 100mm, the powder feeding rotating speed is controlled to be 1.2r/min, and the thickness of the metal bonding layer is controlled to be about 100 mu m.
And preparing the YSZ ceramic main body layer on the metal bonding layer by adopting atmospheric plasma spraying. Specifically, a ceramic body layer was prepared by spraying YSZ powder after preheating the metal bond coat to 500 ℃ using a spray gun. The spraying voltage and current were 62V and 650A, respectively, the main gas pressure was 0.47MPa, and the hydrogen pressure was 0.25MPa. The moving speed of the spray gun is set to 150mm/s, the spraying distance is 80mm, the powder feeding rotating speed is controlled to be 1.5r/min, and the thickness of the ceramic main body layer is controlled to be about 350 mu m.
The method for preparing the corrosion-resistant ceramic top layer with the micro-nano double-scale structure by adopting solution precursor plasma spraying on the ceramic main body layer comprises the following specific steps:
the ceramic main body layer is polished on 1000# sand paper and 2000# sand paper in sequence, the surface roughness is controlled to be about 4.5 mu m, and ultrasonic cleaning is carried out.
And dissolving the raw materials in a mixed solution of deionized water and absolute ethyl alcohol to prepare a solution precursor. The source of yttrium serving as a precursor raw material of the YSZ solution is yttrium nitrate, and the source of zirconium is zirconium acetate. The concentration of Zr element in the precursor is 1.5mol/L; the volume ratio of deionized water to absolute ethyl alcohol is 3:7.
And spraying the solution precursor on the surface of the ceramic main body layer to form the corrosion-resistant ceramic top layer.
The ceramic main body layer is preheated to 420 ℃ by a spray gun, then is sprayed, the spraying voltage is 42V, the spraying current is 770A, the main air pressure is 0.4MPa, the hydrogen pressure is 0.3MPa, the moving speed of the spray gun is 600mm/s, the spraying distance is 50mm, the liquid feeding flow is 35ml/min, and the thickness of the corrosion-resistant ceramic top layer is controlled to be about 20 mu m.
Fig. 7A and 7B are surface topography diagrams of the prepared corrosion-resistant ceramic top layer, and it can be seen that the corrosion-resistant ceramic top layer is also formed by stacking micro-nano particles with diameters of 0.2-1.5 μm, however, no obvious hemispherical protrusions are formed, and the small particles are stacked in a cluster form, and the diameter is less than 10 μm. The reason is that the precursor with zirconium acetate as a zirconium source has larger viscosity, so that liquid drops are larger in the spraying process, a strong shadow effect cannot be generated, and small particles cannot form hemispherical bulges due to the smaller thickness. The resulting coatings were subjected to CMAS wetting tests and water contact angle tests, resulting in contact angles between 145 and 153 degrees, similar to examples 1 and 2.
Fig. 8 is a CMAS contact angle comparison of a conventional APS coating with a corrosion resistant ceramic top layer prepared in examples 1-3, and fig. 9 is a CMAS wetting diameter comparison of a conventional APS coating with a corrosion resistant ceramic top layer prepared in examples 1-3, it being observed that the anti-CMAS wetting performance of all examples is significantly improved over conventional APS coatings.
Compared with the conventional APS coating, the CMAS corrosion-resistant micro-nano double-scale structure thermal barrier coating provided by the invention has better CMAS wetting resistance, and can prevent the adhesion of molten CMAS on the surface of the coating, so that the corrosion resistance of the coating is improved, and the preparation cost is low, the preparation method is simple, and the industrial production and application are easy to realize.
The foregoing description is only a preferred embodiment of the present invention, and is not intended to limit the scope of the present invention, and various modifications can be made to the above-described embodiment of the present invention. All simple, equivalent changes and modifications made in accordance with the claims and the specification of this application fall within the scope of the patent claims. The present invention is not described in detail in the conventional art.
Claims (5)
1. The preparation method of the CMAS corrosion resistant thermal barrier coating is characterized by comprising the following steps:
s1, preparing a metal bonding layer on a substrate;
s2, preparing a ceramic main body layer on the metal bonding layer;
s3, preparing an anti-corrosion ceramic top layer on the ceramic main body layer by adopting solution precursor plasma spraying,
the step S3 includes the following sub-steps:
s31, dissolving a precursor raw material into a mixed solution of deionized water and absolute ethyl alcohol to prepare a solution precursor, wherein an yttrium source of the precursor raw material is yttrium nitrate, a zirconium source of the precursor raw material is zirconium oxynitrate, an ytterbium source of the precursor raw material is ytterbium nitrate, and the concentration of Zr element in the solution precursor is 0.75 mol/L-1.5 mol/L;
s32, preheating a ceramic main body layer to 380-420 ℃ by using a spray gun, spraying a solution precursor onto the surface of the ceramic main body layer, wherein the spraying voltage is 38-42V, the spraying current is 770-830A, the main air pressure is 0.4-0.5 MPa, the hydrogen pressure is 0.2-0.3 MPa, the moving speed of the spray gun is 200-600 mm/S, the spraying distance is 30-50 mm, the liquid feeding flow is 25-35 ml/min, and an anti-corrosion ceramic top layer of ytterbium oxide and yttrium oxide partially stabilized zirconia is formed, wherein micro-nano particles with the diameter of 0.2-1.5 mu m are stacked on the surface of the ceramic main body layer to form hemispherical protrusions with the diameter of 10-50 mu m or cluster protrusions with the diameter of 1-10 mu m, and the hemispherical protrusions and small particles on the surface form a micro-nano double-scale structure together.
2. The method of claim 1, further comprising sanding and ultrasonically cleaning the ceramic body layer prior to substep S31.
3. The method of claim 2, wherein the ceramic body layer is polished to a roughness of 1.0 to 4.5 μm.
4. A CMAS corrosion resistant thermal barrier coating obtained by the process of any one of claims 1 to 3, wherein the CMAS corrosion resistant thermal barrier coating comprises a metallic bond coat, a ceramic bulk layer, and a corrosion resistant ceramic top layer.
5. The CMAS corrosion resistant thermal barrier coating of claim 4, wherein the thickness of the corrosion resistant ceramic top layer is 20-80 μm.
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