Rare earth oxide doped yttrium oxide stabilized zirconia ceramic material as well as preparation method and application thereof

Abstract

The invention provides a rare earth oxide doped yttrium oxide stabilized zirconia ceramic material as well as a preparation method and application thereof, and belongs to the technical field of ceramic materials and industrial equipment protection. According to the preparation method, yttrium oxide stabilized zirconia is taken as a matrix phase, lanthanum oxide, cerium oxide, gadolinium oxide or neodymium oxide is taken as a doping phase, and the rare earth oxide doped yttrium oxide stabilized zirconia ceramic material is prepared through a solid-phase reaction and a spark plasma sintering technology. Through the microstructure and phase composition of rare earth element doped optimized yttrium oxide stabilized zirconium oxide, the cavitation erosion resistance and mechanical property of the material are remarkably improved, and the material is suitable for preparing fluid equipment runner components such as hydraulic pump impellers and valve elements.

Description

Technical Field

[0001] This invention relates to the field of ceramic materials and industrial equipment protection technology, and in particular to a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material, its preparation method, and its application. Background Technology

[0002] Cavitation erosion is a common and highly destructive failure mode in hydraulic machinery such as propellers, hydraulic pumps, and valves. It is caused by microjet streams or shock waves generated by the collapse of air bubbles in the liquid, accompanied by extremely high instantaneous impact pressure and temperature, ultimately leading to severe vibration, noise, and material damage during the operation of hydraulic machinery. Therefore, there is an urgent need to develop high-performance cavitation erosion resistant materials.

[0003] Yttrium-stabilized zirconia (YSZ), with its excellent mechanical strength and stability, has become a potential candidate material for resisting cavitation corrosion. It significantly improves fracture toughness through ferroelastic domain redirection and reversible phase transformation toughening mechanisms, overcoming the high brittleness of traditional ceramics. However, YSZ still suffers from two interrelated core drawbacks in practical applications, limiting its long-term reliability and protective effect. Firstly, the localized extreme high temperature, high pressure, and water environment generated during cavitation collapse constitute harsh service conditions, easily inducing an irreversible transformation from the metastable tetragonal phase (t' phase) to the monoclinic phase (m phase) in YSZ. This not only consumes the material's phase transformation toughening capacity, but the accompanying volume expansion can also induce microcracks within the material or at grain boundaries, leading to gradual structural relaxation and even overall failure. On the other hand, the large grain size and weak grain boundary bonding commonly found in YSZ exacerbate its damage sensitivity. Under cyclic impact loads caused by cavitation collapse, cracks are very likely to initiate and propagate along the weak grain boundaries. At the same time, the coarse grains also reduce the material's ability to resist local deformation and fracture, resulting in a significant increase in the cavitation erosion rate.

[0004] Therefore, how to further improve the corrosion resistance of yttrium oxide-stabilized zirconium oxide is an urgent problem to be solved. Summary of the Invention

[0005] The purpose of this invention is to provide a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material, its preparation method, and its application. The rare earth oxide doping in the yttrium oxide-doped yttrium oxide-stabilized zirconia ceramic material can further optimize the mechanical properties of yttrium oxide-stabilized zirconia, inhibit grain growth, and adjust the phase transformation critical point. It has excellent resistance to cavitation erosion and shows good application potential in the fields of high-temperature protection and corrosion. It is suitable for manufacturing flow channel components such as water pumps, propellers, and valves that are prone to cavitation erosion.

[0006] To achieve the above-mentioned objectives, the present invention provides the following technical solution: This invention provides a method for preparing rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic materials, comprising the following steps: Yttrium-stabilized zirconium oxide powder was mixed with rare earth oxides and ball-milled in a first dispersion medium to obtain a suspension. After the suspension is first dried, a solid-phase reaction is carried out to obtain a solid solution precursor powder. The solid solution precursor powder is subjected to a second ball milling in a second dispersion medium and then a second drying to obtain rare earth oxide-doped yttrium oxide-stabilized zirconium oxide powder. The rare earth oxide-doped yttrium oxide-stabilized zirconia powder is uniaxially molded, and the resulting initial compact is subjected to spark plasma sintering to obtain a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material. The rare earth oxides include lanthanum oxide, cerium oxide, gadolinium oxide, or neodymium oxide.

[0007] Preferably, the purity of the rare earth oxide is 99.99%.

[0008] Preferably, the yttrium-stabilized zirconium oxide powder and the rare earth oxide are dried separately before mixing, and the drying temperature is independently 150~250℃ and the drying time is independently 10~15 h.

[0009] Preferably, the mass of the rare earth oxide is 2-5% of the mass of the yttrium oxide-stabilized zirconium oxide powder; The first dispersion medium includes ethanol, water, or acetone; The first ball mill operates at a speed of 350-450 r / min for 20-25 h. The grinding media of the first ball mill consist of zirconia balls with a purity of 99.9%.

[0010] Preferably, the temperature of the first drying is 150~200℃ and the time is 10~15 h; The solid-phase reaction is carried out at a temperature of 1400~1600℃ for a time of 10~15 h.

[0011] Preferably, the second dispersion medium includes ethanol, water, or acetone; The second ball mill operates at a speed of 350-450 r / min for 20-25 h. The grinding media for the second ball mill is zirconia balls with a purity of 99.9%; The second drying temperature is 80~90℃, and the time is 10~15 h.

[0012] Preferably, the pressure of the uniaxial molding is 20~25 MPa, and the time is 5~10 min.

[0013] Preferably, the vacuum degree of the discharge plasma sintering is 0.8~1 Pa, the heating rate is 100~150℃ / min, the temperature is 1500~1600℃, the time is 10~15 min, and the sintering pressure is 20~25 MPa.

[0014] This invention provides a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material prepared by the above preparation method, wherein the rare earth oxide is the doping phase and the yttrium oxide-stabilized zirconia is the matrix phase.

[0015] This invention provides the application of the above-mentioned rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material in the protection of fluid equipment.

[0016] The beneficial effects of this invention are: This invention uses yttrium oxide-stabilized zirconia polycrystalline structure as the matrix phase and lanthanum oxide, cerium oxide, gadolinium oxide, or neodymium oxide as doping phases. Rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic materials are prepared through solid-state reaction and spark plasma sintering technology. By optimizing the microstructure and phase composition of yttrium oxide-stabilized zirconia through rare earth oxide doping, the cavitation erosion resistance and mechanical properties are significantly improved.

[0017] In the rare-earth oxide-doped yttrium oxide-stabilized zirconia ceramic material prepared by this invention, the doped phase is dissolved in the yttrium oxide-stabilized zirconia lattice. The yttrium oxide-stabilized zirconia matrix phase absorbs cavitation impact energy through the tm phase transformation toughening mechanism, providing basic mechanical strength and resisting microjets. The introduction of rare-earth ions can promote the formation of t' and c phases, which not only enhances the material's dense structure and refines the grains, but also improves microhardness. While adjusting the tm phase transformation critical point and optimizing the phase transformation toughening efficiency, it can also inhibit YSZ grain growth, strengthen grain boundary bonding, and hinder cavitation crack propagation. The special m-phase band existing at the YSZ grain boundaries is the main reason for the first cavitation erosion and peeling of surface grains. In rare-earth oxide-doped YSZ (REYSZ), the segregation of rare-earth elements at the grain boundaries can hinder the formation of the m-phase band, making it exhibit a longer cavitation erosion latency. Thanks to its superior mechanical properties, fine grains, and high density, REYSZ has significantly improved resistance to cavitation erosion compared to YSZ, with NdYSZ exhibiting cavitation erosion resistance that is 12.4 times that of YSZ. Attached Figure Description

[0018] Figure 1 The XRD patterns (a) and Raman spectra (b) of the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1 are shown. Figure 2 SEM images and grain distribution diagrams of the LaYSZ ceramic material prepared in Example 1; Figure 3SEM images and grain distribution diagrams of the CeYSZ ceramic material prepared in Example 2; Figure 4 SEM images and grain distribution diagrams of the GdYSZ ceramic material prepared in Example 2; Figure 5 SEM images and grain distribution diagrams of the NdYSZ ceramic material prepared in Example 2; Figure 6 SEM images and grain distribution diagrams of the YSZ material prepared in Comparative Example 1; Figure 7 The cumulative mass loss (a) and etching rate (b) of the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1 over time are shown. Figure 8 The hardness results are for the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1. Detailed Implementation

[0019] This invention provides a method for preparing rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic materials, comprising the following steps: Yttrium-stabilized zirconium oxide powder was mixed with rare earth oxides and ball-milled in a first dispersion medium to obtain a suspension. After the suspension is first dried, a solid-phase reaction is carried out to obtain a solid solution precursor powder. The solid solution precursor powder is subjected to a second ball milling in a second dispersion medium and then a second drying to obtain rare earth oxide-doped yttrium oxide-stabilized zirconium oxide powder. The rare earth oxide-doped yttrium oxide-stabilized zirconia powder is uniaxially molded, and the resulting initial compact is subjected to spark plasma sintering to obtain a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material. The rare earth oxides include lanthanum oxide, cerium oxide, gadolinium oxide, or neodymium oxide.

[0020] In this invention, unless otherwise specified, all raw materials required for preparation are commercially available products well known to those skilled in the art.

[0021] In this invention, yttrium-stabilized zirconia (YSZ) powder and rare earth oxides are dried separately, and then the dried yttrium-stabilized zirconia powder and rare earth oxides are mixed and placed in a planetary ball mill for a first ball milling in a first dispersion medium to achieve preliminary mixing and refining of the powders and obtain a suspension.

[0022] In this invention, the yttrium oxide doping ratio in the yttrium oxide stabilized zirconium oxide powder is 8 wt.%, purchased from Oerlikon Microelectronics, Inc.

[0023] In this invention, the rare earth oxide preferably includes lanthanum oxide, cerium oxide, gadolinium oxide or neodymium oxide, and more preferably neodymium oxide; the purity of the rare earth oxide is preferably 99.99%.

[0024] In this invention, the drying temperature is preferably 150~250℃, more preferably 200℃, and the drying time is preferably 10~15 h, more preferably 12 h.

[0025] In this invention, the mass of the rare earth oxide is 2 to 5% of the mass of the yttrium oxide stabilized zirconium oxide powder, more preferably 4 to 5%.

[0026] In this invention, the rotational speed of the first ball mill is preferably 350~450 r / min, more preferably 400 r / min, and the time is preferably 20~25 h, more preferably 24 h; the grinding medium of the first ball mill preferably includes zirconia balls with a purity of 99.9%, and the first dispersion medium preferably includes ethanol, water or acetone, more preferably ethanol. This invention does not have a special limitation on the amount of the first dispersion medium, as long as the first ball milling is carried out smoothly.

[0027] The present invention preferably involves first drying the above suspension to achieve complete drying, followed by a solid-phase reaction to obtain a solid solution precursor powder. The purpose of performing a solid-phase reaction after complete drying of the suspension is to allow the rare earth oxides to fully react chemically with the yttrium-stabilized zirconia matrix, so that rare earth ions enter the zirconia lattice and form a uniform solid solution precursor powder. The rare earth ions introduce a large amount of metastable tetragonal phase (t / t'), which undergoes a phase transition under stress, absorbs energy, and inhibits the formation of easily eroded m-phase. In addition, rare earth elements segregate at the grain boundaries. This structure prevents the formation of brittle m-phase bands on the YSZ grain boundaries, thereby avoiding early spalling and significantly prolonging the cavitation erosion incubation period.

[0028] In this invention, the temperature of the first drying is preferably 150~200℃, more preferably 160℃, and the time is preferably 10~15 h, more preferably 14 h.

[0029] In this invention, the temperature of the solid-phase reaction is preferably 1400~1600℃, more preferably 1500℃, and the time is preferably 10~15 h, more preferably 10 h.

[0030] In this invention, the above-mentioned solid solution precursor powder is preferably subjected to a second ball milling in a second dispersion medium and then subjected to a second drying to obtain rare earth oxide-doped yttrium oxide-stabilized zirconium oxide (REYSZ) powder.

[0031] In this invention, the second dispersion medium preferably includes ethanol, deionized water, or acetone, and more preferably ethanol. This invention does not have a special limitation on the amount of the second dispersion medium, as long as the second ball milling is carried out smoothly. The rotation speed of the second ball mill is preferably 350~450 r / min, more preferably 400 r / min, and the time is preferably 20~25 h, more preferably 24 h. The grinding medium of the second ball mill is preferably zirconia balls with a purity of 99.9%.

[0032] In this invention, the temperature of the second drying is preferably 80~90℃, the time is preferably 80℃, the time is preferably 10~15 h, and more preferably 10 h; the purpose of the second drying is to evaporate the ethanol in the ball milling dispersion medium to ensure that it is completely dried into powder.

[0033] The present invention preferably involves uniaxially molding the above-mentioned rare earth oxide-doped yttrium oxide-stabilized zirconia powder to obtain an initial compact; the initial compact is then poured into a standard graphite mold with dimensions of 20mm × 20mm × 5mm and placed in a spark plasma sintering furnace; the furnace cavity is evacuated for spark plasma sintering to obtain rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material; spark plasma sintering technology utilizes plasma generated by pulsed high current to rapidly sinter the powder, combined with high temperature and high pressure, to obtain bulk ceramic materials with fine grains and density close to the theoretical value in a very short time, with a density ≥98.5%. This step effectively inhibits abnormal grain growth and effectively hinders crack propagation, which is the key to obtaining excellent mechanical properties.

[0034] In this invention, the pressure of the uniaxial molding is preferably 20-25 MPa, more preferably 20 MPa, and the time is preferably 5-10 min, more preferably 8 min.

[0035] In this invention, the vacuum degree of the discharge plasma sintering is preferably 0.8~1 Pa, more preferably 1 Pa; the heating rate is preferably 100~150℃ / min, more preferably 150℃ / min; the temperature is preferably 1500~1600℃, more preferably 1600℃; the time is preferably 10~15 min, more preferably 10 min; and the sintering pressure is preferably 20~25 MPa, more preferably 20 MPa.

[0036] This invention provides a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material prepared by the above preparation method, wherein the rare earth oxide is the doping phase and the yttrium oxide-stabilized zirconia is the matrix phase.

[0037] This invention provides the application of the above-mentioned rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material in the protection of fluid equipment.

[0038] The technical solutions provided by the present invention will be described in detail below with reference to the embodiments, but they should not be construed as limiting the scope of protection of the present invention.

[0039] The purity of La2O3, Ce2O3, Gd2O3, and Nd2O3 used in Examples 1-2 and Comparative Example 1 was 99.99%, and they were purchased from Shanghai Aladdin Biochemical Technology Co., Ltd. The yttrium-stabilized zirconium oxide (YSZ) powder used had a yttrium doping ratio of 8 wt.% and was purchased from Oerlikon Microelectronics.

[0040] Example 1

[0041] La2O3 and YSZ powders were baked at 200℃ for 12h to obtain pretreated La2O3 and pretreated YSZ powders, respectively. Pretreated La2O3 and pretreated YSZ powder were mixed at a mass ratio of 4:100 and placed in a planetary ball mill. The grinding media was zirconia balls with a purity of 99.9% and the dispersion medium was ethanol. The mixture was ball-milled at a speed of 400 r / min for 24 h to obtain a suspension. The suspension was dried at 160℃ for 14 h, and then calcined at 1500℃ for 10 h to carry out a solid-phase reaction, thereby obtaining a solid solution precursor powder. The solid solution precursor powder was ball-milled twice at 400 r / min for 24 h. The grinding medium was zirconia balls with a purity of 99.9% and the dispersion medium was ethanol. Then it was dried at 80℃ for 10 h to obtain LaYSZ powder. LaYSZ powder was uniaxially molded under a pressure of 20 MPa to obtain an initial compact. The initial compact was poured into a standard graphite mold with dimensions of 20 mm × 20 mm × 5 mm and placed in a spark plasma sintering furnace. The furnace cavity was evacuated to 1 Pa, and the temperature was raised to 1600 °C at a heating rate of 150 °C / min. The furnace was then sintered at a sintering pressure of 20 MPa for 10 min to obtain the LaYSZ ceramic material.

[0042] Example 2

[0043] The only difference from Example 1 is: Replace La2O3 with Ce2O3, Gd2O3, and Nd2O3 respectively; Other parameters remain unchanged; CeYSZ ceramic materials, GdYSZ ceramic materials, and NdYSZ ceramic materials were prepared respectively.

[0044] Comparative Example 1

[0045] The only difference from Example 1 is: No La2O3 powder was added; Other parameters remain unchanged; Pure YSZ material was prepared.

[0046] Characterization and performance testing

[0047] 1. (1) Figure 1 The XRD patterns (a) and Raman spectra (b) of the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1 are shown. Depend on Figure 1 As shown in (a), all synthesized samples possess a pure zirconium dioxide structure; Figure 1 As shown in (b), no peak representing REO was found in the Raman spectrum, indicating that all components formed a solid solution and that rare earth atoms completely entered the zirconium dioxide lattice and replaced some zirconium atoms through chemical reaction.

[0048] (2) The morphology of the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1 were observed using a scanning electron microscope. Based on the obtained SEM micrographs, the grain size distribution was calculated using a Nano Measurer. The results are shown in [Figure 1]. Figures 2-6 ; Figure 2 The images show the SEM images and grain distribution diagrams of the LaYSZ ceramic material prepared in Example 1. Figure 3 The images show the SEM images and grain distribution diagrams of the CeYSZ ceramic material prepared in Example 2. Figure 4 The images show the SEM images and grain distribution diagrams of the GdYSZ ceramic material prepared in Example 2. Figure 5 The images show the SEM images and grain distribution diagrams of the NdYSZ ceramic material prepared in Example 2. Figure 6 SEM images and grain distribution diagrams of the YSZ material prepared in Comparative Example 1; Depend on Figure 2 It can be seen that the grain sizes of the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1 exhibit a normal distribution. The grain size distribution ranges as follows: LaYSZ ceramic material: 0.2-2.6 μm; CeYSZ ceramic material: 0.2-3.4 μm; GdYSZ ceramic material: 0.0-2.4 μm; NdYSZ ceramic material: 0.2-2.8 μm; and YSZ material: 0.6-5.0 μm. YSZ and CeYSZ contain some large grains and have uneven grain size distribution, while LaYSZ, GdYSZ, and NdYSZ have smaller grain sizes and more uniform distribution.

[0049] 2. (1) The cavitation erosion properties of the REYSZ materials prepared in Examples 1 and 2 and the YSZ materials prepared in Comparative Example 1 were tested according to ASTM G 32-10 standard: Before testing, the sample was fixed in distilled water at a depth of 12±4 mm. A 16 mm diameter stainless steel upper sample was used, coaxially mounted with a distance of 0.5±0.01 mm between them. The ultrasonic amplitude transformer tip diameter was 15.9±0.02 mm, the amplitude was 50 μm, and the vibration frequency was 20±0.5 kHz. The total test duration was 15 h. During the test, the distilled water temperature was controlled at 25±2℃ using a cooling water system. The cumulative mass loss of the sample after different cavitation times was measured using an analytical balance with a resolution of 0.1 mg. The results are shown in [Figure number missing]. Figure 7 , Figure 7 In the middle (a), the cumulative mass loss of the REYSZ material prepared in Examples 1-2 and the YSZ material prepared in Comparative Example 1 over time is shown. Figure 7 (b) shows the etching rate of the REYSZ materials prepared in Examples 1-2 and the YSZ materials prepared in Comparative Example 1 as a function of time. like Figure 7 As shown, in the 15-hour cavitation test, NdYSZ had the lowest cumulative mass loss, only 3 mg, which was more than 80% lower than that of pure YSZ (40 mg) in Comparative Example 1. Its resistance to cavitation erosion was 12.4 times that of pure YSZ.

[0050] (2) The hardness of the REYSZ materials prepared in Examples 1-2 and the YSZ material prepared in Comparative Example 1 were tested, and the results are shown in the figure. Figure 8 ; Depend on Figure 8 It is known that REYSZ exhibits higher hardness than YSZ among all materials, with a hardness of 1200~1450HV. In particular, NdYSZ has a microhardness that is 1.5 times higher than that of YSZ.

[0051] As can be seen from the above embodiments, the present invention provides a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material, its preparation method and application. Using a polycrystalline structure of yttrium oxide-stabilized zirconia as the matrix phase and lanthanum oxide, cerium oxide, gadolinium oxide or neodymium oxide as doping phases, the rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material is prepared through solid-state reaction and spark plasma sintering technology. By optimizing the microstructure and phase composition of yttrium oxide-stabilized zirconia through rare earth oxide doping, the cavitation erosion resistance and mechanical properties are significantly improved.

[0052] The above description is only a preferred embodiment of the present invention. It should be noted that for those skilled in the art, several improvements and modifications can be made without departing from the principle of the present invention, and these improvements and modifications should also be considered within the scope of protection of the present invention.

Claims

1. A method for preparing a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material, characterized in that, Includes the following steps: Yttrium-stabilized zirconium oxide powder was mixed with rare earth oxides and ball-milled in a first dispersion medium to obtain a suspension. After the suspension is first dried, a solid-phase reaction is carried out to obtain a solid solution precursor powder. The solid solution precursor powder is subjected to a second ball milling in a second dispersion medium and then a second drying to obtain rare earth oxide-doped yttrium oxide-stabilized zirconium oxide powder. The rare earth oxide-doped yttrium oxide-stabilized zirconia powder is uniaxially molded, and the resulting initial compact is subjected to spark plasma sintering to obtain a rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material. The rare earth oxides include lanthanum oxide, cerium oxide, gadolinium oxide, or neodymium oxide.

2. The preparation method according to claim 1, characterized in that, The purity of the rare earth oxide is 99.99%.

3. The preparation method according to claim 1, characterized in that, The yttrium-stabilized zirconium oxide powder and the rare earth oxide are dried separately before mixing. The drying temperature is 150~250℃ and the drying time is 10~15 h.

4. The preparation method according to claim 1, characterized in that, The mass of the rare earth oxide is 2-5% of the mass of the yttrium oxide-stabilized zirconium oxide powder; The first dispersion medium includes ethanol, water, or acetone; The first ball mill operates at a speed of 350-450 r / min for 20-25 h. The grinding media of the first ball mill consist of zirconia balls with a purity of 99.9%.

5. The preparation method according to claim 1, characterized in that, The first drying temperature is 150~200℃, and the time is 10~15 h; The solid-phase reaction is carried out at a temperature of 1400~1600℃ for a time of 10~15 h.

6. The preparation method according to claim 1, characterized in that, The second dispersion medium includes ethanol, water, or acetone; The second ball mill operates at a speed of 350-450 r / min for 20-25 h. The grinding media for the second ball mill is zirconia balls with a purity of 99.9%; The second drying temperature is 80~90℃, and the time is 10~15 h.

7. The preparation method according to claim 1, characterized in that, The pressure of the uniaxial molding is 20~25 MPa, and the time is 5~10 min.

8. The preparation method according to claim 7, characterized in that, The vacuum degree of the discharge plasma sintering is 0.8~1 Pa, the heating rate is 100~150℃ / min, the temperature is 1500~1600℃, the time is 10~15 min, and the sintering pressure is 20~25 MPa.

9. The rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material prepared by the preparation method according to any one of claims 1 to 8, characterized in that, The rare earth oxide is the doped phase, and the yttrium oxide-stabilized zirconium oxide is the matrix phase.

10. The application of the rare earth oxide-doped yttrium oxide-stabilized zirconia ceramic material according to claim 9 in the protection of fluid equipment.

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