CN110184559B - Thermal barrier coating containing YAG (yttrium aluminum garnet) and Ce as well as preparation method and application thereof - Google Patents

Thermal barrier coating containing YAG (yttrium aluminum garnet) and Ce as well as preparation method and application thereof Download PDF

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CN110184559B
CN110184559B CN201910636353.3A CN201910636353A CN110184559B CN 110184559 B CN110184559 B CN 110184559B CN 201910636353 A CN201910636353 A CN 201910636353A CN 110184559 B CN110184559 B CN 110184559B
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yag
thermal barrier
barrier coating
stress
layer
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CN110184559A (en
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仇巍
张雁恒
亢一澜
曲传咏
张茜
卢宁
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Tianjin University
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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
    • C23C4/04—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
    • 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
    • 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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  • Chemical Kinetics & Catalysis (AREA)
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  • Mechanical Engineering (AREA)
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  • Organic Chemistry (AREA)
  • Coating By Spraying Or Casting (AREA)
  • Investigating, Analyzing Materials By Fluorescence Or Luminescence (AREA)

Abstract

The thermal barrier coating containing YAG to Ce comprises a metal bonding layer, a fluorescent stress sensing layer and a ceramic layer which are sequentially stacked, wherein the metal bonding layer is used for adhering an alloy substrate of a test piece, the fluorescent stress sensing layer is mainly formed by spraying YAG to Ce powder, the technical problem that stress within 0.1GPa cannot be accurately measured due to low sensitivity of a stress-frequency shift factor of a traditional Eu-doped thermal barrier coating is solved, accurate measurement of the stress within 0.1GPa at a key interface in the thermal barrier coating is realized, the measurement accuracy of the internal stress of the thermal barrier coating can be effectively improved, the early monitoring of internal stress evolution is realized, and the comprehensive monitoring, the fluorescent stress sensing layer and the fluorescent stress sensing layer are realized The safe service life of the thermal barrier coating is effectively and accurately predicted.

Description

Thermal barrier coating containing YAG (yttrium aluminum garnet) and Ce as well as preparation method and application thereof
Technical Field
The invention relates to the technical field of thermal barrier coatings, in particular to a thermal barrier coating containing YAG (yttrium aluminum garnet) and Ce, and a preparation method and application thereof.
Background
Turbine blades for aeroengines are core components in the aeronautical field, and the performance of turbine blades, in particular the ability to withstand high and low temperatures, has become a hallmark of the aeronautical industry level. In order to ensure the safety of turbine blades in extremely high temperature service environments, Thermal Barrier Coating (TBC) systems are one of the core leading edge technologies that address the high temperature challenges of blades due to their low thermal conductivity and high stability. However, TBC systems are typically multilayer heterostructures comprising a surface ceramic coating, a superalloy substrate, a metallic bond coat, and a thermally grown oxide layer (TGO) formed between the ceramic and bond coats. Due to the difference of the interlayer thermal expansion coefficients, process stress and service stress are inevitably introduced in the coating preparation and service process, so that cracks are induced, the coating is cracked and even falls off, and finally the failure of the TBC system is caused, and the failure positions of the TBC system are often generated in the interface of the ceramic layer/TGO/bonding layer and the ceramic layer near the interface. Therefore, the experimental detection of the stress distribution characteristics of the key interface in the service process of the TBC system has important significance for the failure mechanism and the life prediction.
The fluorescence spectrum mechanics measuring technology is an effective means for nondestructive testing of the internal stress of a thermal barrier coating system due to high spatial resolution, nondestructive and non-contact, stress characterization in translucent ceramics and monitoring of the service process of a TBC system, the basic principle of the measurement is to measure the stress by utilizing the linear relation between the fluorescence emission spectrum frequency shift of fluorescence activator ions in a matrix material and the stress, the rare earth fluorescence spectrum method can detect the internal stress distribution and evolution of the thermal barrier coating key interface in the preparation and service processes based on the doping of a fluorescence stress sensing layer, but the maximum stress generated at the thermal barrier coating key interface is generally 0.1 GPa-1 GPa, while the stress-frequency shift factor obtained by the traditional rare earth Eu element doping is-5 cm-1The stress within 0.1GPa can not be accurately measured and the fine characterization of the stress at the key interface of the thermal barrier coating can not be realized by considering the self-limit of the resolution of the spectrometer, so that the stress distribution and the evolution in the coating can not be accurately monitored.
In view of the above, the present invention is particularly proposed.
Disclosure of Invention
One of the purposes of the invention is to provide a thermal barrier coating containing a fluorescent stress sensing layer mainly formed by YAG and Ce, so as to improve the technical problems that the stress-frequency shift factor sensitivity of the traditional fluorescent stress sensing layer doped with Eu element is low, and due to the self limitation of the resolution of a spectrometer, the stress within 0.1GPa can not be accurately measured, and the fine characterization of the stress at the key interface of the thermal barrier coating can not be realized, so that the stress distribution and the evolution in the coating can not be accurately monitored.
The invention also aims to provide a preparation method of the thermal barrier coating containing the fluorescent stress sensing layer mainly formed by YAG and Ce.
The invention also aims to provide the application of the thermal barrier coating containing the fluorescent stress sensing layer mainly formed by YAG to Ce in the field of stress measurement.
The thermal barrier coating containing YAG and Ce provided by the invention comprises a metal bonding layer, a fluorescent stress sensing layer and a ceramic layer which are sequentially stacked, wherein the metal bonding layer is used for adhering an alloy substrate of a test piece, and the fluorescent stress sensing layer is mainly formed by spraying YAG and Ce powder.
Further, the YAG to Ce powder is mainly prepared from the following raw materials in percentage by mole: y is3Al5O1298-99.5% and CeO20.5-2％；
Preferably, the YAG to Ce powder comprises the following raw materials in percentage by mole: y is3Al5O1299-99.5% and CeO20.5-1％；
Further preferably, the YAG: Ce powder comprises the following raw materials in mole percentage: y is3Al5O1299.5% and CeO20.5％；
Preferably, said Y is3Al5O12The purity of the product is more than or equal to 99 percent;
preferably, the CeO2The purity of the product is more than or equal to 99 percent.
Further, the preparation method of the YAG to Ce powder comprises the following steps: will Y3Al5O12And CeO2After mixed sintering and grinding, YAG and Ce powder is obtained;
preferably, the particle size of the YAG: Ce powder is 300-400 meshes;
preferably, the sintering temperature is 1400-1600 ℃, and the sintering time is 2-4 h.
Further, the thickness of the fluorescence stress sensing layer is 20-50 μm.
Furthermore, the material of the metal bonding layer is NiCoCrAlY, and the thickness of the metal bonding layer is 100-200 μm.
Further, the ceramic layer is made of Y2O3Stabilized ZrO2The thickness of the ceramic layer is 150-200 μm.
The invention provides a preparation method of a thermal barrier coating containing YAG to Ce, which comprises the following steps:
(a) preparing a metal bonding layer on an alloy substrate of a test piece through a spraying process;
(b) preparing a fluorescent stress sensing layer on the metal bonding layer by a spraying process;
(c) preparing a ceramic layer on the fluorescent stress sensing layer by a spraying process;
preferably, the spraying process in step (a), step (b) or step (c) is an atmospheric plasma spraying process.
Further, step(s) is included before step (a): carrying out roughening and purifying treatment on the alloy substrate of the test piece;
preferably, the roughening and cleaning treatment is performed by sandblasting;
preferably, the raw material adopted by the sand blasting treatment is steel grit, and the granularity of the steel grit is 10-20 mu m.
Further, the alloy substrate of the test piece is made of nickel-based superalloy;
preferably, the nickel-based superalloy comprises Ni, Cr, Ti, and Al.
The thermal barrier coating containing YAG to Ce provided by the invention is applied to the field of stress measurement;
preferably, the stress measurement field is the field of nondestructive fine detection of the stress distribution of the internal interface of the thermal barrier coating on the surface of the turbine blade of an aeroengine and/or a gas turbine.
The invention provides a high-performance high-efficiency high-power-consumption: the thermal barrier coating of Ce is provided between a metal bond layer and a ceramic layer by YAG: a fluorescent stress sensing layer formed by spraying Ce powder, since the stress-frequency shift factor sensitivity of the fluorescent stress sensing layer containing Ce element is more than 20 times that of the conventional fluorescent stress sensing layer (e.g. fluorescent stress sensing layer containing Eu element), therefore, the present application provides a YAG: the fluorescence stress sensing layer of Ce can obtain the stress fine distribution at the key interface in the thermal barrier coating, therefore, the accurate measurement of the stress within 0.1GPa at the key interface inside the coating is realized, the measurement accuracy of the internal stress of the thermal barrier coating is effectively improved, and the fluorescent stress sensing layer is favorable for realizing the early monitoring of the internal stress evolution of the thermal barrier coating, so that the safe service life of the thermal barrier coating can be comprehensively, effectively and accurately predicted.
The thermal barrier coating containing YAG and Ce provided by the invention has the advantages of simple process, convenience in operation and easiness in realization of industrial mass production.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and other drawings can be obtained by those skilled in the art without creative efforts.
Fig. 1 is a schematic structural diagram of a thermal barrier coating containing YAG: Ce and an alloy substrate layer of a test piece provided in embodiment 1 of the present invention.
Icon: a 100-nickel alloy substrate; 201-metal adhesion layer; 202-fluorescent stress sensing layer; 203-ceramic layer.
Detailed Description
Embodiments of the present invention will be described in detail below with reference to examples, but it will be understood by those skilled in the art that the following examples are only illustrative of the present invention and should not be construed as limiting the scope of the present invention. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The powder reagent or the equipment used is not indicated by the manufacturer, and is a conventional product available by commercial purchase.
It should be noted that:
in the present invention, unless otherwise stated, the numerical range "a-b" represents a shorthand representation of any combination of real numbers between a and b, where a and b are both real numbers. For example, a numerical range of "6 to 22" means that all real numbers between "6 to 22" have been listed herein, and "6 to 22" is simply a shorthand representation of the combination of these values.
The "ranges" disclosed herein may have one or more lower limits and one or more upper limits, respectively, in the form of lower limits and upper limits.
In the present invention, unless otherwise specified, the individual operation steps may be performed sequentially or may not be performed in sequence. Preferably, the steps of the operations herein are performed sequentially.
Unless otherwise defined, technical and scientific terms used herein have the same meaning as is familiar to those skilled in the art. In addition, any methods or materials similar or equivalent to those described herein can also be used in the present invention.
According to one aspect of the invention, the thermal barrier coating containing YAG and Ce comprises a metal bonding layer, a fluorescent stress sensing layer and a ceramic layer which are sequentially stacked, wherein the metal bonding layer is used for adhering an alloy substrate of a test piece, and the fluorescent stress sensing layer is mainly formed by spraying YAG and Ce powder.
In the invention, the fluorescence spectrum detection system emits incident light to the surface of the thermal barrier coating and penetrates through the ceramic layer to reach the fluorescence stress sensing layer, rare earth fluorescence emitted by the fluorescence stress sensing layer before and after stress generation is collected to form rare earth fluorescence spectrum information, the internal stress at the key interface of the thermal barrier coating is calculated by utilizing the linear relation between the frequency shift amount in the fluorescence spectrum information and the internal stress at the key interface of the thermal barrier coating, and the analytical formula of the linear relation is as follows: deltaCe＝ΠCe·σCeWherein, isCeRepresenting the amount of frequency shift, σ, of the fluorescence spectrum before and after the generation of internal stressCeRepresenting the internal stress of the key interface of the thermal barrier coatingCeAs a sensing medium Ce3+The stress-frequency shift factor sensitivity of which is a conventional stress sensing medium (e.g., Eu)3+) Is more than 20 times the stress-frequency shift factor sensitivity.
It should be noted that the description "critical interface of thermal barrier coating" herein refers to the interface formed by the interface between the fluorescence stress sensing layer and the bonding layer.
The invention provides a high-performance high-efficiency high-power-consumption: the thermal barrier coating of Ce is provided with a coating consisting of YAG: a fluorescent stress sensing layer formed by spraying Ce powder, since the stress-frequency shift factor sensitivity of the fluorescence stress sensing layer containing Ce element is more than 20 times that of the conventional fluorescence stress sensing layer (e.g. the fluorescence stress sensing layer containing Eu element), therefore, in the actual use process, the fine distribution of the internal stress of the key interface of the thermal barrier coating can be obtained by measuring the frequency shift amount of the fluorescence spectrum generated before and after the internal stress of the thermal barrier coating is generated, therefore, the accurate measurement of the stress within 0.1GPa at the key interface inside the coating is realized, the measurement accuracy of the internal stress of the thermal barrier coating is effectively improved, and the fluorescent stress sensing layer is favorable for realizing the early monitoring of the internal stress evolution of the thermal barrier coating, so that the safe service life of the thermal barrier coating can be comprehensively, effectively and accurately predicted.
In a preferred embodiment of the invention, the YAG to Ce powder is mainly prepared from the following raw materials in percentage by mole: y is3Al5O1298-99.5% and CeO20.5-2％；
By controlling Y3Al5O12And CeO2The molar ratio of the rare earth to the Yttrium Aluminum Garnet (YAG) to Ce powder is determined so that the fluorescence spectrum information of the prepared fluorescence stress sensing layer made of YAG to Ce powder measured by a fluorescence spectrum detection system is accurate, and therefore, the stress evolution within 0.1GPa inside the thermal barrier coating can be more comprehensively and effectively predicted; especially when Y is3Al5O12And CeO2When the molar ratio of the rare earth to the yttrium aluminum oxide is 99.5:0.5, the stress-frequency shift factor sensitivity of the fluorescent stress sensing layer made of the YAG: Ce powder in the proportion is higher, the measurement of the stress within 0.1GPa of the critical interface of the thermal barrier coating is more accurate, the generated rare earth fluorescence spectrum information is easier to collect, and in addition, the fluorescent stress sensing layer made of the YAG: Ce powder in the proportion does not influence the use performance of the ceramic layer.
Typically, but not by way of limitation, in the preparation of YAG: Ce powder, Y3Al5O12Is, for example, 98%, 98.1%, 98.2%, 98.3%, 98.4%, 98.5%, 98.6%, 98.7%, 98.8%, 98.9%, 99%, 99.1%, 99.2%, 99.3%, 99.4% or 99.5%; CeO (CeO)2The molar ratio of (a) is, for example, 2%, 1.9%, 1.8%, 1.7%, 1.6%, 1.5%, 1.4%, 1.3%, 1.2%, 1.1%, 1%, 0.9%, 0.8%,0.7%, 0.6% or 0.5%.
It should be noted that the stress-frequency shift factors of the fluorescent stress sensing layer obtained from YAG powder and Ce powder with different raw material ratios are different, so that the stress-frequency shift factor of the fluorescent stress sensing layer needs to be calibrated before use, and the specific operation steps are as follows:
1. the preparation method of the fluorescent stress sensing layer comprises the following steps: firstly, pretreating a high-temperature alloy substrate (such as but not limited to roughening and purifying the surface to be sprayed of the high-temperature alloy substrate), and then preparing a NaCl layer on the surface of the pretreated high-temperature alloy substrate by an APS (advanced plating solution) method spraying process; spraying a fluorescent stress sensing layer containing YAG and Ce on the surface of the NaCl layer by an APS method; finally, placing the whole test piece in a constant-temperature water bath at 60 ℃, and dissolving the NaCl layer to obtain a fluorescence stress sensing layer;
2. adopting 458nm laser of a semiconductor pump as incident light, and receiving a fluorescence spectrum through a fluorescence spectrum detection system;
3. placing a fluorescence stress sensing layer to be calibrated on a microscopic platform of a fluorescence detection system, focusing incident light on the surface of a sample to excite a fluorescence spectrum, and calibrating a characteristic peak of the fluorescence stress sensing layer in a non-pressure state;
4. placing a fluorescence stress sensing layer to be calibrated in a given stress state on a microscope platform of a fluorescence detection system, focusing incident light on the surface of a sample, performing a uniaxial compression experiment on the fluorescence stress sensing layer to be calibrated, measuring a plurality of positions on the surface of the fluorescence stress sensing layer to be calibrated in different load states, respectively collecting fluorescence spectra, comparing the measured fluorescence spectra with the initial characteristic peak, processing data to extract frequency shift information, and using a formula deltaCe＝ΠCe·σCeAnd respectively solving the stress-frequency shift factors, and taking the average result to obtain the stress-frequency shift factor corresponding to the fluorescent stress sensing layer.
In some embodiments of the invention, when measuring a thermal barrier coating containing a calibrated fluorescent stress sensing layer, a thermal barrier coating test piece is placed on a microscopic platform of a fluorescence detection system, and incident light is focused to heatIncident light is emitted to the surface of the thermal barrier coating and penetrates through the ceramic layer to reach the fluorescence stress sensing layer, rare earth fluorescence spectrum information is collected in a back direction, the stress-frequency shift factor corresponding to the fluorescence stress sensing layer is known, the shift of the rare earth fluorescence spectrum peak position before and after the thermal barrier coating is stressed is detected, and a formula delta is utilizedCe＝ΠCe·σCeStress distribution at critical interfaces of the thermal barrier coating can be obtained. In some preferred embodiments of the present invention, the single point detection or the surface scanning detection of the thermal barrier coating can be performed to completely obtain the stress distribution information at the critical interface in a larger area (centimeter magnitude) in the thermal barrier coating and predictably evaluate the service life of the thermal barrier coating.
In a preferred embodiment of the present invention, Y is3Al5O12And CeO2Can be obtained by commercial purchase.
In a preferred embodiment of the present invention, Y is3Al5O12Purity of CeO is not less than 99 percent2The purity of the YAG-Ce powder is more than or equal to 99 percent, so that the impurities in the prepared YAG-Ce powder are less, and the fluorescence detection precision of the YAG-Ce powder is effectively ensured.
In a preferred embodiment of the invention, the preparation method of the YAG: Ce powder comprises the following steps: will Y3Al5O12And CeO2Mixing, sintering and grinding to obtain YAG-Ce powder.
In a preferred embodiment of the invention, the particle size of the YAG: Ce powder is 300-400 mesh, so that the YAG: Ce powder can be sprayed uniformly more easily when the fluorescent stress sensing layer is prepared by a spraying process. Compared with the granularity range, when the granularity of YAG (yttrium aluminum garnet) Ce powder is too small, the powder is not easy to be discharged by the used spraying process, so that the coating is not uniform, and the spraying efficiency is low; when the granularity of YAG/Ce powder is too large, the porosity in the coating is high, and the oxidation resistance is low.
Typically, but not by way of limitation, the YAG to Ce powder has a particle size of, for example, 300 mesh, 320 mesh, 350 mesh, 380 mesh or 400 mesh.
In a preferred embodiment of the present invention, Y is3Al5O12And CeO2The sintering temperature after mixing is 1400-1600 ℃, and the sintering time is 2-4h, so that the prepared YAG-Ce powder is more stable, and the fluorescent ion doping is more uniform.
Typically, but not by way of limitation, Y3Al5O12And CeO2The sintering temperature after mixing is 1400 deg.C, 1420 deg.C, 1450 deg.C, 1480 deg.C, 1500 deg.C, 1520 deg.C, 1550 deg.C, 1580 deg.C or 1600 deg.C; the sintering time is 2h, 2.2h, 2.5h, 2.8h, 3h, 3.2h, 3.5h, 3.8h or 4 h.
In a typical but non-limiting embodiment, the YAG: Ce powder is prepared by a process comprising the steps of:
weighing Y according to the proportion3Al5O12And CeO2Putting the mixture into a ball milling tube, carrying out high-speed ball milling for 24h, then carrying out ball milling and drying, putting the ball-milled and dried mixture into a crucible, and putting the crucible into a sintering furnace, wherein the sintering temperature is 1400 ℃ and 1600 ℃, and keeping the temperature for 2 h; then naturally cooling to room temperature; finally, the mixture is put into a ball milling tank for ball milling for 24 hours, and then is taken out for drying and sieving to obtain YAG and Ce powder with the granularity of 300-.
In a preferred embodiment of the invention, the fluorescent stress sensing layer has a thickness of 20-50 μm. Typically, but not by way of limitation, the fluorescent stress sensing layer has a thickness of, for example, 20 μm, 25 μm, 30 μm, 35 μm, 40 μm, 45 μm, or 50 μm.
Multiple tests prove that if the thickness of the fluorescence stress sensing layer is more than 50 mu m, the thermal service reliability of the thermal barrier coating is easily influenced, the thermal mismatch internal stress of the coating is increased, and if the thickness of the fluorescence stress sensing layer is less than 20 mu m, the fluorescence intensity collected by a fluorescence detection system is weaker, and the measurement accuracy is reduced.
In a preferred embodiment of the present invention, the material of the metal adhesion layer is NiCoCrAlY, and the thickness of the metal adhesion layer is 100-200 μm.
The NiCoCrAlY is selected as the metal bonding layer, so that the ceramic layer is connected with the alloy substrate of the test piece more stably and tightly.
Typically, but not by way of limitation, the metal adhesion layer has a thickness of, for example, 100 μm, 110 μm, 120 μm, 130 μm, 140 μm, 150 μm, 160 μm, 170 μm, 180 μm, 190 μm or 200 μm.
If the thickness of the metal bonding layer is greater than 200 μm, the stability of the thermal barrier coating system is easily affected, and if the thickness of the metal bonding layer is less than 100 μm, the ceramic layer and the alloy substrate of the test piece are not easily stably connected through the metal bonding layer.
In a preferred embodiment of the present invention, the material of the ceramic layer is Y2O3Stabilized ZrO2The thickness of the ceramic layer is 150-200 μm.
Y2O3Stabilized ZrO2YSZ for short, which has good thermal insulation properties. If the thickness of the ceramic layer is less than 150 μm, it is difficult to achieve good heat insulation performance, and if the thickness of the ceramic layer is more than 200 μm, the penetration of fluorescence is affected, and the measurement accuracy is affected.
Typically, but not by way of limitation, the ceramic layer has a thickness of, for example, 150 μm, 155 μm, 160 μm, 165 μm, 170 μm, 175 μm, 180 μm, 185 μm, 190 μm, 195 μm or 200 μm.
According to a second aspect of the present invention, the present invention provides a method for preparing the thermal barrier coating containing YAG: Ce, comprising the following steps:
(a) preparing a metal bonding layer on an alloy substrate of a test piece through a spraying process;
(b) preparing a fluorescent stress sensing layer on the metal bonding layer by a spraying process;
(c) and preparing a ceramic layer on the fluorescent stress sensing layer by a spraying process.
The thermal barrier coating containing YAG and Ce provided by the invention is formed by plasma spraying, and has the advantages of simple process, convenience in operation, easiness in industrial production and cost reduction.
In a preferred embodiment of the present invention, the spraying process in step (a), step (b) or step (c) is an atmospheric plasma spraying process.
Atmospheric plasma spray, also known as APS spray, allows for precise control of coating thickness and surface characteristics without affecting area or part distortion and with greater adhesion between the coating and the substrate.
In a preferred embodiment of the present invention, before the step (a) of preparing the thermal barrier coating containing YAG: Ce, a step(s) of: and carrying out roughening and purification treatment on the alloy substrate of the test piece so as to enable the combination between the alloy substrate of the test piece and the metal bonding layer to be more stable and compact.
In a preferred embodiment of the invention, the roughening and cleaning treatment is performed by blasting.
The alloy substrate of the test piece is roughened and purified by sand blasting, and the raw materials are low in price and easy to control.
In a further preferred embodiment of the invention, the blasting is performed with steel grit as the raw material, the steel grit having a particle size of 10 to 20 μm.
The steel grit with the granularity of 10-20 mu m is selected for sand blasting treatment, so that the alloy substrate of the test piece is more easily combined with the metal bonding layer stably and firmly.
Typical but non-limiting steel grit has a particle size of, for example, 10 μm, 11 μm, 12 μm, 13 μm, 14 μm, 15 μm, 16 μm, 17 μm, 18 μm, 19 μm or 20 μm.
In a preferred embodiment of the present invention, the alloy substrate of the test piece is made of a nickel-based superalloy.
The nickel-based superalloy is used as an alloy substrate of a test piece, so that the high-temperature resistance of the test piece is stronger.
In a further preferred embodiment of the present invention, the nickel-base superalloy comprises the elements Ni, Cr, Ti and Al.
According to a third aspect of the invention, the invention provides the use of a thermal barrier coating comprising YAG: Ce as described above in the field of stress measurement.
In a preferred embodiment of the invention, the field of stress measurement is the field of nondestructive fine detection of the stress distribution of the internal interface of a thermal barrier coating on the surface of a turbine blade of an aeroengine and/or a gas turbine.
In a typical but non-limiting embodiment of the present invention, a method for performing non-destructive testing of internal stresses at critical interfaces of a thermal barrier coating containing YAG: Ce comprises the following steps (it should be noted that the stress-frequency shift factor of a fluorescent stress sensing layer in the thermal barrier coating has been calibrated):
(1) laser beams with specific wavelengths are emitted to the surface of the thermal barrier coating containing YAG Ce, the laser beams are emitted to the fluorescence stress sensing layer to excite a fluorescence spectrum, and the initial characteristic peak R of the thermal barrier coating containing YAG Ce in a non-pressure state is calibrated0；
(2) Applying known stress to the thermal barrier coating containing YAG to Ce by uniaxial compression, adopting a laser beam with the same wavelength as that in the step (1), enabling the laser beam to be incident to the surface of the thermal barrier coating containing YAG to Ce, enabling the laser beam to be incident to a fluorescence stress sensing layer, exciting a fluorescence spectrum, and calibrating a specific characteristic peak R of the thermal barrier coating containing YAG to Ce under specific pressure1。
(3) Measuring characteristic fluorescence spectrum R of fluorescence spectrum detection system1And R0By using a linear expression of ΔCe＝ΠCe·σCeCalculating to obtain the internal stress sigma at the key interface of the thermal barrier coatingCe。
The technical solution provided by the present invention is further described below with reference to examples and comparative examples.
Example 1
The embodiment provides a test piece of a thermal barrier coating containing YAG and Ce, the structure of which is shown in FIG. 1, the test piece comprises a nickel alloy substrate 100 and the thermal barrier coating which is adhered to the nickel alloy substrate 100 and contains YAG and Ce, the thermal barrier coating containing YAG and Ce comprises a metal bonding layer 201, a fluorescent stress sensing layer 202 and a ceramic layer 203 which are sequentially arranged from bottom to top, the metal bonding layer 201 is made of NiCoCrAlY and has the thickness of 150 mu m, the fluorescent stress sensing layer 202 is formed by spraying YAG and Ce powder and has the thickness of 20 mu m, and the ceramic layer 203 is made of Y powder2O3Stabilized ZrO2The thickness is 180 mu m, the fluorescent stress sensing layer is formed by spraying YAG and Ce powder with the granularity of 300 meshes, and the preparation raw material of the YAG and Ce powder is Y3Al5O12And CeO2The molar ratio of the two is 99.5:0.5, and the purity of the two raw materials is more than or equal to 99 percent.
Example 2
This example provides a container comprisingThe structure of the test piece with the thermal barrier coating of YAG and Ce is the same as that of the test piece in the embodiment 1, and the description is omitted, and the difference from the embodiment 1 is that in the raw material for preparing YAG and Ce powder, Y is3Al5O12And CeO2In a molar ratio of 99: 1.
Example 3
This example provides a test piece of a thermal barrier coating containing YAG: Ce, the structure of the test piece is the same as that of example 1, and details are not repeated here, and the difference from example 1 is that in the raw material for preparing YAG: Ce powder, Y is3Al5O12And CeO2Is 99.2: 0.8.
Example 4
This example provides a test piece of a thermal barrier coating containing YAG: Ce, the structure of the test piece is the same as that of example 1, and details are not repeated here, and the difference from example 1 is that in the raw material for preparing YAG: Ce powder, Y is3Al5O12And CeO2Is 95: 5.
Example 5
This example provides a test piece of a thermal barrier coating containing YAG: Ce, the structure of the test piece is the same as that of example 1, and details are not repeated here, and the difference from example 1 is that in the raw material for preparing YAG: Ce powder, Y is3Al5O12And CeO2Is 99.9: 0.1.
Comparative example 1
The embodiment provides a test piece with a thermal barrier coating, which comprises a nickel alloy substrate of the test piece, wherein a metal bonding layer, an Eu-doped 8YSZ (8YSZ: Eu) ceramic layer and an 8YSZ ceramic layer are sequentially arranged on the nickel alloy substrate from bottom to top, the metal bonding layer is made of NiCoCrAlY and is 150 microns thick, the Eu-doped 8YSZ ceramic layer is 20 microns thick, and in the Eu-doped YSZ ceramic layer, the molar content of Eu is 1%, and the thickness of the 8YSZ ceramic layer is 180 microns.
Test examples
Stress-frequency shift factors of the fluorescent stress sensing layers containing YAG: Ce provided in examples 1 to 5 and the Eu-doped 8YSZ (8YSZ: Eu) ceramic layer provided in comparative example 1 were measured by laser beams, respectively, and fluorescence spectra were collected at a plurality of measurement positions on the surface of each sample when a test was performed, and the frequency shift information was extracted by processing test data, and an average value was calculated to obtain the stress-frequency shift factors, wherein examples 1 to 5 were irradiated with a laser beam having a wavelength of 458nm and comparative example 1 was irradiated with a laser beam having a wavelength of 532nm, and the results are shown in table 1 below.
TABLE 1
Figure BDA0002130468080000141
As can be seen from Table 1, examples 1-5 provide Π of fluorescent stress sensing layers comprising YAG to CeCeAre all higher than 80cm-1A stress-frequency shift factor of 4cm, both significantly higher than that of the Eu-doped 8YSZ (8YSZ: Eu) ceramic layer provided in comparative example 1-1The stress test sensitivity of the test pieces of the thermal barrier coatings containing YAG: Ce provided in examples 1-5 was more than 20 times higher than the test piece sensitivity provided in comparative example 1.
The thermal barrier coating containing YAG and Ce provided by the invention is provided with the fluorescent stress sensing layer formed by spraying YAG and Ce powder between the metal bonding layer and the ceramic layer, so that the sensitivity of stress measurement is improved by more than 20 times, the accurate measurement of the stress within 0.1GPa at the key interface in the coating is realized, the internal stress measurement accuracy of the thermal barrier coating is effectively improved, the early monitoring of the internal stress evolution is realized, and the safe service life of the thermal barrier coating can be comprehensively, effectively and accurately predicted.
As can be seen from the comparison of examples 1-3 and examples 4-5, when the YAG to Ce powder used to prepare the fluorescent stress sensing layer is Y3Al5O12And CeO2And the molar ratio of the two is (99-99.5): (1-0.5) preparing the resultant fluorescent stress sensing layerCeAnd the detection sensitivity is higher.
Finally, it should be noted that: the above embodiments are only used to illustrate the technical solution of the present invention, and not to limit the same; while the invention has been described in detail and with reference to the foregoing embodiments, it will be understood by those skilled in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some or all of the technical features may be equivalently replaced; and the modifications or the substitutions do not make the essence of the corresponding technical solutions depart from the scope of the technical solutions of the embodiments of the present invention.

Claims (20)

1. The thermal barrier coating containing YAG and Ce is characterized by comprising a metal bonding layer, a fluorescent stress sensing layer and a ceramic layer which are sequentially stacked, wherein the metal bonding layer is used for adhering an alloy substrate of a test piece, and the fluorescent stress sensing layer is mainly formed by spraying YAG and Ce powder;
the YAG-Ce powder is mainly prepared from the following raw materials in percentage by mole: y is3Al5O1298-99.5% and CeO20.5-2％。
2. The YAG Ce-containing thermal barrier coating according to claim 1, wherein the YAG Ce powder comprises in mole percent: y is3Al5O1299-99.5% and CeO20.5-1％。
3. The YAG Ce-containing thermal barrier coating according to claim 2, wherein the YAG Ce powder comprises in mole percent: y is3Al5O1299.5% and CeO20.5％。
4. Ce-containing YAG thermal barrier coating according to claim 1, wherein Y is3Al5O12The purity of the product is more than or equal to 99 percent.
5. Ce-containing YAG thermal barrier coating according to claim 1, wherein the CeO2The purity of the product is more than or equal to 99 percent.
6. The YAG Ce-containing thermal barrier coating according to claim 1, wherein the preparation method of the YAG Ce powder comprises the following steps: will Y3Al5O12And CeO2Mixing, sintering and grinding to obtain YAG-Ce powder.
7. The YAG Ce-containing thermal barrier coating as claimed in claim 6, wherein the particle size of the YAG Ce powder is 300-400 mesh.
8. The thermal barrier coating comprising YAG: Ce as claimed in claim 6, wherein the sintering temperature is 1400 ℃ and 1600 ℃ and the sintering time is 2-4 h.
9. The YAG: Ce-containing thermal barrier coating of claim 1, wherein the fluorescent stress sensing layer has a thickness of 20-50 μm.
10. The thermal barrier coating containing YAG to Ce as claimed in claim 1, wherein the material of the metal bonding layer is NiCoCrAlY, and the thickness of the metal bonding layer is 100-200 μm.
11. The YAG to Ce containing thermal barrier coating as claimed in claim 1, wherein the ceramic layer is Y2O3Stabilized ZrO2The thickness of the ceramic layer is 150-200 μm.
12. Method for the production of a thermal barrier coating comprising YAG: Ce according to any of the claims 1 to 11, characterized in that it comprises the following steps:
(a) preparing a metal bonding layer on an alloy substrate of a test piece through a spraying process;
(b) preparing a fluorescent stress sensing layer on the metal bonding layer by a spraying process;
(c) and preparing a ceramic layer on the fluorescent stress sensing layer by a spraying process.
13. The method of claim 12, wherein the spraying process in step (a), step (b) or step (c) is an atmospheric plasma spraying process.
14. The method of claim 12, further comprising, before step (a), step(s): and carrying out roughening and purifying treatment on the alloy substrate of the test piece.
15. The method of claim 14, wherein the roughening and cleaning are performed by sand blasting.
16. The method according to claim 15, wherein the grit blasting is performed using steel grit having a particle size of 10 to 20 μm as a raw material.
17. The method according to claim 12, wherein the alloy substrate of the test piece is made of a nickel-based superalloy.
18. The method of making according to claim 17, wherein the nickel-based superalloy comprises Ni, Cr, Ti, and Al.
19. Use of a thermal barrier coating comprising YAG: Ce according to any of claims 1-11 in the field of stress measurement.
20. Use according to claim 19, wherein the field of stress measurement is the field of non-destructive fine inspection of the stress distribution of the internal interface of a thermal barrier coating on the surface of a turbine blade of an aeroengine and/or gas turbine.
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