A multi-rare earth modified zirconia ceramic material, a preparation method and application thereof

Abstract

This invention provides a multi-rare-earth modified zirconia ceramic material, its preparation method, and its application. The chemical composition of the multi-rare-earth modified zirconia ceramic material is La. x Ce y Gd z Yb s Y t Zr 1‑x‑y‑z‑s‑t O δ , where 0 < x <1;0< y <1;0< z <1;0< s <1;0< t <1;0<1- x - y - z - s - t <1;0< δ <2. This material possesses excellent high-temperature phase stability, high coefficient of thermal expansion, low thermal conductivity, and high fracture toughness, enabling it to meet the higher service temperature requirements of thermal barrier coatings.

Description

Technical Field

[0001] This invention belongs to the field of high-performance ceramic technology, specifically relating to a La ceramic exhibiting excellent high-temperature phase stability, high coefficient of thermal expansion, low thermal conductivity, and high fracture toughness. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Multi-rare earth modified zirconia ceramic materials, and their preparation methods in powder and bulk forms. Background Technology

[0002] To improve the thermal efficiency of gas turbines, it is necessary to continuously increase the turbine inlet temperature. Currently, the turbine inlet temperature of J-class heavy-duty gas turbines, representing the highest international level, typically exceeds 1600℃, posing a more severe challenge to the materials of their hot-end components. Existing gas turbine hot-end components mainly use high-temperature alloys as the base material, and thermal barrier coatings are usually deposited on their surfaces to further enhance their high-temperature performance and durability. Yttria-stabilized zirconia (YSZ) has become the preferred ceramic surface layer material for thermal barrier coatings due to its high melting point, high toughness, thermal expansion coefficient matching that of high-temperature alloys, and excellent high-temperature phase stability. However, with the continuous increase in service temperature, YSZ undergoes phase transformation and sintering during long-term service, severely affecting its reliability and service life at higher temperatures. Therefore, researchers have proposed a strategy of multi-element rare-earth co-doped modified zirconia to obtain ceramic surface layer materials with excellent comprehensive performance. Among these, the rational design of the rare-earth element combination and composition is key to achieving this goal. Summary of the Invention

[0003] To meet the higher service temperature requirements of gas turbines, this invention aims to provide a La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s- t O δ Rare earth-modified zirconia ceramic materials, their preparation methods, and applications. These materials possess excellent high-temperature phase stability, high coefficient of thermal expansion, low thermal conductivity, and high fracture toughness, enabling them to meet the higher service temperature requirements of thermal barrier coatings.

[0004] To meet the application requirements of thermal barrier coatings, this invention designs and prepares a multi-rare-earth modified zirconia ceramic material with the chemical composition La. x Ce y Gd z Yb sY t Zr 1-x-y-z-s-t O δ The ceramic powder is synthesized through a high-temperature solid-state reaction method, while the ceramic bulk is prepared through a hot-pressing sintering process.

[0005] To achieve the above objectives, the present invention adopts the following technical solution: This invention provides a multi-rare-earth modified zirconia ceramic material, wherein the chemical composition of the multi-rare-earth modified zirconia ceramic material is La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ , where 0 < x <1;0< y <1;0< z <1;0< s <1;0< t <1;0<1- x - y - z - s - t <1;0< δ <2.

[0006] Furthermore, the multi-rare-earth modified zirconia ceramic material has a metastable tetragonal structure and a space group of [missing information]. P 42 / nmc.

[0007] The present invention also provides a method for preparing the above-mentioned multi-rare-earth modified zirconia ceramic material. When the multi-rare-earth modified zirconia ceramic material is in powder form, the preparation method includes the following steps: (1) Calcine La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders at temperature T1 for t1 hours to obtain calcined La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders; (2) The calcined La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders are mixed and ball-milled, and then dried to obtain La2O3-CeO2-Gd2O3-Yb2O3-Y2O3-ZrO2 mixed powder; (3) The La2O3-CeO2-Gd2O3-Yb2O3-Y2O3-ZrO2 mixed powder was subjected to a solid-state reaction at temperature T2 for t2 hours to obtain La x Ce y Gd z Yb s Y tZr 1-x-y-z-s-t O δ Ceramic sintered powder; (4) The La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ After ball milling, the sintered ceramic powder is dried to obtain the multi-rare-earth modified zirconia ceramic material, specifically La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic powder. The resulting La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ The ceramic powder has a uniform particle size distribution.

[0008] Furthermore, in step (1), the calcination temperature T1 is not lower than 1300℃ and the calcination time t1 is not lower than 3 hours.

[0009] Furthermore, in step (2), the molar ratio of La2O3, CeO2, Gd2O3, Yb2O3, Y2O3, and ZrO2 is 0.5. x : y 0.5 z 0.5 s 0.5 t : (1- x - y - z - s - t ).

[0010] Furthermore, in step (3), the solid-phase reaction temperature T2 is 1500 ~ 1650℃, the solid-phase reaction time t2 is 12 ~ 48 hours, the solid-phase reaction atmosphere is air, and the heating and cooling rate is 5 ~ 10℃ / min.

[0011] Furthermore, the ball milling in steps (2) and (4) includes: using anhydrous ethanol as the medium, wherein the mass ratio of powder to anhydrous ethanol is between 1:1 and 1:1.5, the mass ratio of ball material is between 2:1 and 4:1, the ball milling speed is 150 to 350 rpm, and the ball milling time is 24 to 48 h.

[0012] Furthermore, when the rare earth-modified zirconia ceramic material is in bulk form, the preparation method further includes the following step: (5) placing the La... x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ The ceramic powder was sintered at temperature T3 for t3 hours to obtain La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic blocks.

[0013] Furthermore, in step (5), the sintering temperature T3 is 1500 ~ 1700℃, the sintering time t3 is 1 ~ 3 hours, the sintering pressure is 20 ~ 30 MPa, the sintering atmosphere is argon, and the heating and cooling rates are 5 ~ 10℃ / min.

[0014] This invention also provides the application of the above-mentioned rare earth modified zirconia ceramic materials in the field of thermal barrier coatings.

[0015] Compared with the prior art, the technical solution provided by the present invention has at least the following beneficial effects: 1. This invention utilizes a two-step solid-state reaction method to dope zirconium oxide with rare earth ions of varying sizes and valence states, thereby preparing a pure-phase metastable tetragonal La structure. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic powder.

[0016] 2. This invention prepares La by hot pressing and sintering. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ The ceramic bulk has a density exceeding 97.0% and a grain size of 13.5 ± 0.6 μm.

[0017] 3. In terms of material design, this invention prepares a ceramic surface material with excellent comprehensive performance by doping ZrO2 with La2O3, CeO2, Gd2O3, Yb2O3, and Y2O3: it maintains a metastable tetragonal phase structure without phase transformation after annealing at 1600℃ for 100 hours; and its thermal conductivity ranges from room temperature to 1400℃ is 1.41 ~ 1.65 W·m. -1 ·K -1 The average coefficient of thermal expansion in the range of room temperature to 1300℃ is 9.5 ~ 11.5 × 10⁻⁶. -6 K -1 The fracture toughness is 3.0 ~ 4.0 ± 0.1 MPa·m. 1 / 2 The above performance indicators show that this material can meet the service requirements of thermal barrier coatings. Attached Figure Description

[0018] One or more embodiments are illustrated by way of example with reference to the accompanying drawings. These illustrations do not constitute a limitation on the embodiments, and unless otherwise stated, the figures in the drawings are not to be limited by scale.

[0019] Figure 1 La in Embodiment 1 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 (a) X-ray diffraction pattern and (b) Raman spectrum of ceramic powder; Figure 2 La in Embodiment 1 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 X-ray diffraction pattern of ceramic powder after annealing at 1600℃ for 100 hours; Figure 3 La in Embodiment 2 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 (a) Surface morphology and (b) Statistical results of grain size of ceramic bulk material; Figure 4 La in Embodiment 2 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y0.06 Zr 0.78 O 1.905 Curves showing the changes in (a) heat capacity, (b) thermal diffusivity, and (c) thermal conductivity of a ceramic bulk material with temperature; Figure 5 La in Embodiment 2 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Characterization results of thermal expansion behavior of ceramic bulk: (a) Elongation (ΔL / L) as a function of temperature; (b) Comparison of its average thermal expansion coefficient with that of YSZ material. Detailed Implementation

[0020] This invention addresses the application requirements of thermal barrier coatings for hot-end components in advanced gas turbines, and designs a multi-rare-earth modified zirconia ceramic material with a chemical composition of La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ By controlling the doping concentration and coordination structure of rare earth elements, the formation of a metastable tetragonal phase is effectively promoted, ensuring high fracture toughness while significantly improving the high-temperature phase stability of the material. Based on the significant differences in ion radii between lanthanum, cerium, gadolinium, ytterbium, and yttrium and zirconium ions, introducing several rare earth ions into the zirconium oxide lattice induces significant lattice distortion, achieving synergistic optimization of phonon scattering enhancement and lattice diffusion suppression, simultaneously improving key indicators such as the material's anti-sintering performance and thermal insulation properties. This invention successfully synthesized a pure-phase metastable tetragonal La... x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic powder was used to prepare corresponding ceramic blocks by hot pressing and sintering, and relevant performance tests were completed.

[0021] The performance test information in the following examples is as follows: (1) Morphological observation: Microscopic morphology was observed using field emission scanning electron microscopy (Clara, Tescan, Czech Republic); (2) Phase structure analysis: Phase analysis was performed using an X-ray diffractometer (D8 Advance, Bruker, Germany) and a laser confocal Raman spectrometer (LabRam Odyssey, Horiba, Japan). (3) Density measurement: The apparent density of the bulk sample was measured using the Archimedes displacement method. (4) High-temperature phase stability test: La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ The ceramic was placed in a muffle furnace and annealed at 1600℃ for 100 hours. The phase composition before and after annealing was compared.

[0022] (5) Measurement of thermal diffusivity and calculation of thermal conductivity: The thermal diffusivity of the sintered bulk material was measured using a Netzsch LFA427 laser thermal conductivity meter, and the thermal conductivity was calculated according to formula (1). κ = αC p ρ (1) in, κ For thermal conductivity, α For thermal diffusivity, C p For thermal melting (obtained by Neumann-Kopp rule calculation), ρ The density is the bulk density.

[0023] (6) Measurement of thermal expansion coefficient: The coefficient of thermal expansion of the sintered bulk material was measured using a thermomechanical analyzer (TMA / SDTA 2+, Mettler-Toledo, Switzerland).

[0024] (7) Fracture toughness measurement: The fracture toughness of the material was measured using a mechanical testing machine (C45.105, MTS, America) via the single-sided pre-cracked beam method.

[0025] The present invention will be further described in detail below through embodiments.

[0026] Example 1 In this embodiment, La x Ce y Gd z Yb s Y t Zr1-x-y-z-s-t O δ The specific steps for preparing the powder are as follows: (1) Calcine La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders at 1300℃ for 3 hours to remove the adsorbed water and impurities such as carbon dioxide, and obtain calcined La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders; (2) Using calcined La2O3, CeO2, Gd2O3, Yb2O3, Y2O3, and ZrO2 powders as raw materials and anhydrous ethanol as the medium, the raw materials and anhydrous ethanol were placed in a silicon nitride ball mill jar at a mass ratio of 1:1.2 and ball-milled in a planetary ball mill. The ball-to-material mass ratio was 2:1, the rotation speed was 300 rpm, and the ball-milling time was 24 h. After drying and sieving, a mixed powder of La2O3-CeO2-Gd2O3-Yb2O3-Y2O3-ZrO2 was obtained; the molar ratio of La2O3, CeO2, Gd2O3, Yb2O3, Y2O3, and ZrO2 powders was 1:3:3.5:2:3:78, i.e., 0.5 x= 0.01; y= 0.03; 0.5 z= 0.035; 0.5 s= 0.02; 0.5 t= 0.03: (1- x - y - z - s - t )=0.78 (3) The La2O3-CeO2-Gd2O3-Yb2O3-Y2O3-ZrO2 mixed powder was placed in a zirconia crucible and then placed in a muffle furnace. The temperature was increased to 1500℃ at a rate of 5℃ / min under air atmosphere and held for 12 hours to carry out a complete solid-phase reaction. Then, it was cooled to room temperature at a rate of 5℃ / min to obtain La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Ceramic sintered powder; (4) With La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905Using ceramic sintered powder as raw material and anhydrous ethanol as the medium, the raw material and anhydrous ethanol were placed in a silicon nitride ball mill jar at a mass ratio of 1:1.2 and ball-milled in a planetary ball mill. The ball-to-powder mass ratio was 2:1, the rotation speed was 300 rpm, and the milling time was 24 h. Subsequently, the powder was dried and sieved to obtain La with uniform particle size. 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Ceramic powder.

[0027] For La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The powder underwent performance testing, and the results are as follows: like Figure 1 As shown, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The X-ray diffraction pattern and Raman spectrum of the ceramic powder show that the powder has a pure-phase metastable tetragonal structure with space group [space group number missing]. P 42 / nmc.

[0028] like Figure 2 As shown, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The X-ray diffraction pattern of ceramic powder after annealing at 1600℃ for 100 hours shows that the annealed powder still maintains a metastable tetragonal single-phase structure and has excellent high-temperature phase stability.

[0029] Example 2 In this embodiment, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The specific steps for preparing ceramic blocks are as follows: In this embodiment, steps (1), (2), (3) and (4) are completely consistent with steps (1), (2), (3) and (4) in embodiment 1; It also includes: (5) La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Ceramic powder was loaded into a 50 mm diameter graphite mold and placed in a hot-press sintering furnace. Under an argon protective atmosphere, the temperature was increased to 1500 °C at a rate of 10 °C / min, and sintered at 30 MPa for 2 hours. The powder was then cooled to room temperature at a rate of 10 °C / min to obtain dense La. 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Ceramic blocks. For La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The ceramic block underwent performance testing, and the results are as follows: like Figure 3 As shown, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The scanning electron microscope image of the ceramic bulk shows that the bulk has a high density and uniform grains with a size of 13.5 ± 0.6 μm.

[0030] Table 1. La in Embodiment 2 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Apparent density, theoretical density, and compactness of ceramic blocks

[0031] As shown in Table 1, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr0.78 O 1.905 The apparent density of the ceramic block is 6.31 g / cm³. 3 The density is 97.0%.

[0032] like Figure 4 As shown, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The curves showing the changes in heat capacity, thermal diffusivity, and thermal conductivity of the ceramic bulk as a function of temperature, from room temperature to 1400℃, show that the heat capacity increases from 0.429 mm² / s². 2 ·s -1 Increased to 0.616 mm 2 ·s -1 The thermal diffusivity is 0.531 mm. 2 ·s -1 Reduced to 0.434 mm 2 ·s -1 Thermal conductivity from 1.41 W·m -1 ·K -1 Increased to 1.65 W·m -1 ·K -1 Compared to the reported YSZ material, the reduction is 35-45%.

[0033] like Figure 5 As shown, La 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 The curve showing the elongation (ΔL / L) of the ceramic bulk as a function of temperature. The average linear expansion coefficient of this bulk is approximately 10.6 × 10⁻⁶ over the range of room temperature to 1300℃. -6 / K, which is similar to the reported YSZ material.

[0034] Table 2. La in Embodiment 2 of the present invention 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Fracture toughness of ceramic blocks

[0035] As shown in Table 2, La 0.02 Ce 0.03 Gd 0.07 Yb0.04 Y 0.06 Zr 0.78 O 1.905 The fracture toughness of the ceramic bulk is 3.6 ± 0.1 MPa·m. 1 / 2 .

[0036] In summary, the experimental examples of this application successfully prepared La via a solid-state reaction method. 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 La was successfully prepared from ceramic powder by hot pressing and sintering. 0.02 Ce 0.03 Gd 0.07 Yb 0.04 Y 0.06 Zr 0.78 O 1.905 Ceramic bulk. This ceramic material exhibits excellent high-temperature phase stability (maintaining a metastable tetragonal phase without phase transformation after annealing at 1600℃ for 100 hours) and low thermal conductivity (1.41 ~ 1.65 W·m from room temperature to 1400℃). -1 ·K -1 Compared to reported YSZ materials, it is reduced by approximately 35-45%, and has a higher coefficient of thermal expansion (an average of 10.6 × 10⁻⁶ from room temperature to 1300℃). -6 / K, similar to YSZ material) and high fracture toughness (3.6 ± 0.1 MPa·m 1 / 2 With its characteristics such as heat barrier coating, it is a potential surface material for thermal barrier coatings.

[0037] Those skilled in the art will understand that the above embodiments are specific examples of implementing the present invention, and in practical applications, various changes in form and detail can be made without departing from the spirit and scope of the present invention. Any person skilled in the art can make their own modifications and alterations without departing from the spirit and scope of the present invention; therefore, the scope of protection of the present invention should be determined by the scope defined in the claims.

Claims

1. A multi-rare-earth modified zirconia ceramic material, characterized in that, The chemical composition of the multi-rare-earth modified zirconia ceramic material is La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ , where 0 < x < 1; 0 < y < 1; 0 < z < 1; 0 < s < 1; 0 < t < 1; 0 < 1- x - y - z - s - t < 1; 0 < δ < 2.

2. The multi-rare-earth modified zirconia ceramic material according to claim 1, characterized in that, The multi-rare-earth modified zirconia ceramic material has a metastable tetragonal structure and a space group of [space group number missing]. P 42 / nmc.

3. A method for preparing multi-rare-earth modified zirconia ceramic material according to claim 1 or 2, characterized in that, When the rare earth-modified zirconia ceramic material is in powder form, the preparation method includes the following steps: (1) Calcine La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders at temperature T1 for t1 hours to obtain calcined La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders; (2) The calcined La2O3, CeO2, Gd2O3, Yb2O3, Y2O3 and ZrO2 powders are mixed and ball-milled, and then dried to obtain La2O3-CeO2-Gd2O3-Yb2O3-Y2O3-ZrO2 mixed powder; (3) The La2O3-CeO2-Gd2O3-Yb2O3-Y2O3-ZrO2 mixed powder was subjected to a solid-state reaction at temperature T2 for t2 hours to obtain La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic sintered powder; (4) The La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ After ball milling, the sintered ceramic powder is dried to obtain the multi-rare-earth modified zirconia ceramic material, specifically La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic powder.

4. The method for preparing multi-rare-earth modified zirconia ceramic material according to claim 3, characterized in that, In step (1), the calcination temperature T1 is not lower than 1300℃ and the calcination time t1 is not lower than 3 hours.

5. The method for preparing multi-rare-earth modified zirconia ceramic material according to claim 3, characterized in that, In step (2), the molar ratio of La₂O₃, CeO₂, Gd₂O₃, Yb₂O₃, Y₂O₃, and ZrO₂ is 0.

5. x : y 0.5 z 0.5 s 0.5 t : (1- x - y - z - s - t ).

6. The method for preparing multi-rare-earth modified zirconia ceramic material according to claim 3, characterized in that, In step (3), the solid-phase reaction temperature T2 is 1500 ~ 1650℃, the solid-phase reaction time t2 is 12 ~ 48 hours, the solid-phase reaction atmosphere is air, and the heating and cooling rate is 5 ~ 10℃ / min.

7. The method for preparing multi-rare-earth modified zirconia ceramic material according to claim 3, characterized in that, The ball milling in steps (2) and (4) includes: using anhydrous ethanol as the medium, wherein the mass ratio of powder to anhydrous ethanol is between 1:1 and 1:1.5, the mass ratio of ball material is between 2:1 and 4:1, the ball milling speed is 150 to 350 rpm, and the ball milling time is 24 to 48 h.

8. The method for preparing multi-rare-earth modified zirconia ceramic material according to claim 3, characterized in that, When the rare earth-modified zirconia ceramic material is in bulk form, the preparation method further includes the following steps: (5) The La x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ The ceramic powder was sintered at temperature T3 for t3 hours to obtain La. x Ce y Gd z Yb s Y t Zr 1-x-y-z-s-t O δ Ceramic blocks.

9. The method for preparing multi-rare-earth modified zirconia ceramic material according to claim 8, characterized in that, In step (5), the sintering temperature T3 is 1500 ~ 1700℃, the sintering time t3 is 1 ~ 3 hours, the sintering pressure is 20 ~ 30 MPa, the sintering atmosphere is argon, and the heating and cooling rates are 5 ~ 10℃ / min.

10. The application of a multi-rare-earth modified zirconia ceramic material according to claim 1 or 2 in the field of thermal barrier coatings.

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