Cr-Ti-based MAX phase ceramic material as well as preparation method and application thereof

Abstract

The invention belongs to the technical field of high-temperature lead-bismuth-corrosion-resistant materials, and particularly relates to a Cr-Ti-based MAX-phase ceramic material and a preparation method and application thereof. According to the invention, Cr2TiAlC2 is used as a matrix, and Mo element is doped to partially replace Cr element and Ti element to prepare the Cr2TiAlC2-based composite material; the chemical expression formula of the Cr < 2-x > Ti < 1-x > Mo < 2-x > Al < 2 > C < 2 > or Cr < Ti > Mo < Al > C < 2 > Wherein 0 lt; x is smaller than or equal to 0.4. According to the Cr-Ti-based MAX-phase ceramic material and the preparation method thereof, the Mo element is introduced on the basis of an existing Cr-Ti-based MAX-phase ceramic material, the Cr-Ti-based MAX-phase ceramic material is prepared by adopting a spark plasma sintering method, the obtained Cr-Ti-based MAX-phase ceramic material shows relatively excellent corrosion resistance in a liquid lead bismuth environment, and the problem that an existing material is corroded and dissolved in a high-temperature liquid metal environment is effectively solved.

Description

Technical Field

[0001] This invention belongs to the technical field of high-temperature lead-bismuth corrosion resistant materials, specifically relating to a Cr-Ti based MAX phase ceramic material, its preparation method, and its application. Background Technology

[0002] Nuclear energy plays an irreplaceable role in ensuring energy supply, promoting economic development, and benefiting the national economy and people's livelihoods. As a stable, reliable, clean, and low-carbon energy source, nuclear energy is an important option for the transition to cleaner and lower-carbon energy. Lead-cooled fast reactors, using liquid metal as a coolant, are one of the preferred reactor types for fourth-generation nuclear power systems. Liquid lead-bismuth alloy (LBE) possesses excellent neutronic properties, superior resistance to radiation damage, good thermal conductivity, and a low melting point and high boiling point, making it an ideal candidate material for coolants and spallation targets. Despite these advantages, LBE can corrode reactor structural components, such as main pump impeller blades or fuel cladding, during high-temperature operation. This corrosion involves various physicochemical processes, such as the dissolution of component elements, erosion of the material by the flowing LBE, migration of component elements in the solid-liquid two-phase system, and chemical reactions of corrosion products and impurities. These corrosive effects can lead to material degradation, thereby threatening the safe operation of the reactor.

[0003] Solving the above problems are key technical issues that urgently need to be addressed in the development of lead-cooled fast reactors. Currently, candidate materials for lead-cooled fast reactor systems include stainless steels such as T91, HT9, 316L, and EP823, as well as ceramic materials. Austenitic stainless steels, represented by 316L and 15-15Ti, possess excellent high-temperature creep resistance, weldability, and radiation damage resistance; however, they are prone to elemental dissolution in high-temperature LBE (Lead-Based Electron) environments, leading to structural strength loss. Ceramic materials exhibit relatively small mass loss during corrosion, demonstrating good corrosion resistance. However, due to the inherent brittleness of ceramic materials and the propagation of surface cracks during corrosion, existing engineering ceramics are difficult to apply directly.

[0004] Max phase ceramics, a novel material combining the ductility and toughness of metals with the corrosion resistance of ceramics, exhibit a thin oxide layer after corrosion, making them a promising class of nuclear-grade materials resistant to liquid lead and bismuth corrosion. However, some commonly reported Ti-based MAX phase ceramics, such as Ti3Al... 1-x Si x C2, where xWhile Si doping of Al sites can suppress surface crack formation to some extent in the range of 0 to 1, the oxide layer rich in Ti oxide remains too porous, making element dissolution unavoidable. Recently developed Cr-Ti-based MAX phases, such as Cr2TiAlC2, have seen some reduction in element dissolution because the Ti transition metal is partially replaced by Cr, allowing for the formation of oxide films even under oxygen-deficient conditions. However, this modification method still cannot guarantee the formation of a continuous, protective oxide layer, thus failing to completely eliminate element dissolution. Summary of the Invention

[0005] To address the shortcomings of the existing technology and further improve the corrosion resistance of MAX phase ceramics in lead-bismuth environments, this invention provides a Cr-Ti based MAX phase ceramic material, its preparation method, and its application, effectively solving the corrosion and dissolution problem of existing materials in high-temperature liquid metal environments.

[0006] To achieve the above objectives, the technical solution of the present invention is as follows.

[0007] The first aspect of this invention provides a Cr-Ti based MAX phase ceramic material, wherein the Cr-Ti based MAX phase ceramic material is prepared by doping Cr2TiAlC2 as a matrix and partially replacing Cr and Ti elements with Mo; the chemical formula of the Cr-Ti based MAX phase ceramic material is: Cr 2-x Ti 1-x Mo 2x AlC2, or CrTiMoAlC2; where 0 <x≤0.4。

[0008] This invention uses Cr2TiAlC2 as a matrix and replaces Cr and Ti elements in equal molar proportions with Mo to prepare Mo-doped Cr-Ti based MAX phase ceramic materials. The introduction of Mo effectively reduces the Gibbs free energy of Al2O3 during corrosion, promotes the formation of a dense Al2O3 protective film on the surface under oxygen-deficient conditions, and enables the matrix material to remain stable for more than 2000 hours in a lead-bismuth corrosion environment, thereby significantly improving the corrosion resistance of Cr-Ti based MAX phase ceramic materials.

[0009] Preferably, the Cr-Ti based MAX phase ceramic material is prepared by ball milling powder containing Cr, Ti, Mo, Al, and C, followed by spark plasma sintering under a protective atmosphere. The spark plasma sintering conditions are: temperature of 1300℃~1500℃, time of 5min~15min, and pressure of 10MPa~40MPa.

[0010] The sintering method used in this invention is spark plasma sintering.

[0011] A second aspect of this invention provides a method for preparing a Cr-Ti based MAX phase ceramic material, comprising the following steps: According to the stoichiometric ratio of the chemical expression of the Cr-Ti based MAX phase ceramic material described in the first aspect, powders containing Cr, Ti, Mo, Al, and C are used as raw materials and ball-milled to obtain a mixed powder; the mixed powder is then subjected to spark plasma sintering under a protective atmosphere to obtain the Cr-Ti based MAX phase ceramic material.

[0012] Preferably, the conditions for spark plasma sintering are: temperature of 1300℃~1500℃, time of 5min~15min, and pressure of 10MPa~40MPa.

[0013] Preferably, the ball milling process is an intermittent ball milling process. Through ball milling, the powders of each element are mixed uniformly.

[0014] In this invention, the ball milling process is intermittent to prevent the powder from sticking together due to excessively high temperature.

[0015] Preferably, the raw material is a mixed powder of Cr powder, Ti powder, Mo powder, Al powder and C powder; the purity of the Cr powder, Ti powder, Mo powder, Al powder and C powder is ≥99%.

[0016] Preferably, the specific operation of spark plasma sintering is as follows: The ball-milled mixed powder was loaded into a graphite mold and placed in a spark plasma sintering furnace. Spark plasma sintering was carried out under an argon atmosphere to obtain a Cr-Ti based MAX phase ceramic material resistant to lead-bismuth corrosion. The conditions for spark plasma sintering were: temperature of 1300℃~1500℃, time of 5min~15min, and pressure of 10MPa~40MPa.

[0017] The third aspect of the present invention provides the application of a Cr-Ti based MAX phase ceramic material in the preparation of lead-bismuth corrosion-resistant materials, wherein the Cr-Ti based MAX phase ceramic material is the Cr-Ti based MAX phase ceramic material described in the first aspect.

[0018] Preferably, the conditions for using lead-bismuth corrosion-resistant materials are: a liquid lead-bismuth environment at 500℃~600℃.

[0019] The beneficial effects of this invention are: 1. This invention uses Cr2TiAlC2 as the matrix and replaces Cr and Ti elements in equal molar proportions with Mo to prepare Mo-doped Cr-Ti based MAX phase ceramic materials. The introduction of Mo effectively reduces the Gibbs free energy of Al2O3 during corrosion, promotes the formation of a dense Al2O3 protective film on the surface under oxygen-deficient conditions, and enables the matrix material to remain stable for 2000 hours in a lead-bismuth corrosion environment, thereby significantly improving the corrosion resistance of Cr-Ti based MAX phase ceramic materials.

[0020] 2. The composition of the Cr-Ti based MAX phase ceramic material of the present invention is easy to control, and the required raw material powder is easy to obtain, all of which are commercially available raw materials; the heat preservation and cooling time during the preparation process is short, and the process is simple.

[0021] 3. Compared with the alloy materials used in existing lead-cooled fast reactors, the mechanical properties of the Cr-Ti based MAX phase ceramic material of the present invention are improved, with a nanohardness of 10GPa to 14GPa, thereby reducing the losses caused by fretting wear and erosion wear during service. Furthermore, because the matrix material contains Ti elements with good ductility, it has little impact on the brittleness of the material.

[0022] 4. This invention utilizes Mo doping to promote the migration of Al elements at the A site during the corrosion process, reducing the Gibbs free energy of Al2O3 during corrosion, enabling the formation of a continuous oxide layer more quickly and protecting the substrate material from corrosion. Attached Figure Description

[0023] Figure 1 The X-ray diffraction patterns are those of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1.

[0024] Figure 2 The curves show the changes in the crystal axis parameters a-axis and c-axis of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1 as a function of Mo content.

[0025] Figure 3The images show cross-sectional scanning electron microscope (SEM) images of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1-3 and Comparative Example 1 after corrosion testing in a liquid lead-bismuth environment at 550°C for 2000 h. Specifically, (a) and (e) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Comparative Example 1 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively; (b) and (f) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Example 1 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively; (c) and (g) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Example 2 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively; and (d) and (h) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Example 3 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively.

[0026] Figure 4 The curves showing the solubility of each element as a function of Mo content after corrosion testing of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1 in a liquid lead-bismuth environment at 550℃ are shown.

[0027] Figure 5 Ellingham diagrams of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1. Detailed Implementation

[0028] To make the objectives, technical solutions, and advantages of this invention clearer, the invention will be further described in detail below with reference to embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the invention.

[0029] Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0030] This invention discloses a Cr-Ti based MAX phase ceramic material resistant to lead-bismuth corrosion, its preparation method, and its applications. Lead-cooled fast reactors using liquid lead-bismuth as a coolant suffer severe corrosion during operation. To improve the structural materials' resistance to corrosion and dissolution caused by liquid lead-bismuth during high-temperature service, this invention introduces Mo into existing Cr-Ti based MAX phase ceramic materials and prepares the target ceramic material using spark plasma sintering. The material prepared by this invention exhibits superior corrosion resistance in a liquid lead-bismuth environment. This method is simple to operate, has a short preparation time, produces a dense material with high phase purity, and exhibits good resistance to lead-bismuth corrosion, effectively solving the corrosion and dissolution problem of materials in high-temperature liquid metal environments.

[0031] In the following embodiments, the conditions for spark plasma sintering during the preparation of the Cr-Ti based MAX phase ceramic material are: temperature of 1300℃~1500℃, time of 5min~15min, and pressure of 10MPa~40MPa. All conditions are acceptable within the above ranges. Using the above conditions, the Cr-Ti based MAX phase ceramic material of the present invention can be prepared, and all conditions can improve the corrosion resistance of the Cr-Ti based MAX phase ceramic material. The Cr-Ti based MAX phase ceramic material of the present invention can be used to prepare lead-bismuth corrosion-resistant materials, and the conditions for using the lead-bismuth corrosion-resistant materials are a liquid lead-bismuth environment of 500℃~600℃.

[0032] The technical solution of the present invention will be further described below through specific embodiments.

[0033] In the following embodiments, unless otherwise specified, the methods described are conventional methods; and unless otherwise specified, the reagents and materials described are commercially available.

[0034] Example 1 The chemical formula for a Cr-Ti based MAX phase ceramic material is Cr 1.9 Ti 0.9 Mo 0.2 AlC2.

[0035] A method for preparing Cr-Ti based MAX phase ceramic materials includes the following steps: Step 1: Using commercially available Cr powder, Ti powder, Mo powder, Al powder, and C powder as raw materials, prepare the mixture according to a stoichiometric molar ratio of 1.9:0.9:0.2:1.1:1.9. The proportion of C powder needs to be slightly reduced while the proportion of Al powder increases. This is mainly because the sintering process uses a graphite mold, which introduces additional C; and Al will volatilize at high temperatures and react with the graphite mold, therefore additional Al powder is needed to avoid Al deficiency.

[0036] Step 2: Place the prepared raw material powder in a ball mill jar and ball mill twice, each time for 30 minutes, with a 30-minute interval; to obtain a mixed powder.

[0037] Step 3: The ball-milled and uniformly mixed powder is placed in a glove box under argon atmosphere protection, then loaded into a graphite mold. The mold is then placed in a spark plasma sintering furnace for spark plasma sintering at a temperature of 1370℃, a holding time of 15 min, and a pressure of 30 MPa; thus, Cr-Ti based MAX phase ceramic material is prepared.

[0038] Example 2 The chemical formula for a Cr-Ti based MAX phase ceramic material is Cr 1.8 Ti 0.8 Mo 0.4 AlC2.

[0039] A method for preparing Cr-Ti based MAX phase ceramic materials includes the following steps: Step 1: Using commercially available Cr powder, Ti powder, Mo powder, Al powder and C powder as raw materials, the ingredients are prepared according to the stoichiometric molar ratio of Cr powder, Ti powder, Mo powder, Al powder and C powder of 1.8:0.8:0.4:1.1:1.9.

[0040] Step 2: Place the prepared raw material powder in a ball mill jar and ball mill twice, each time for 30 minutes, with a 30-minute interval; to obtain a mixed powder.

[0041] Step 3: The ball-milled and uniformly mixed powder is placed in a glove box under argon atmosphere protection, then loaded into a graphite mold. The mold is then placed in a spark plasma sintering furnace for spark plasma sintering at a temperature of 1370℃, a holding time of 15 min, and a pressure of 30 MPa; thus, Cr-Ti based MAX phase ceramic material is prepared.

[0042] Example 3 The chemical formula for a Cr-Ti based MAX phase ceramic material is CrTiMoAlC2.

[0043] A method for preparing Cr-Ti based MAX phase ceramic materials includes the following steps: Step 1: Using commercially available Cr powder, Ti powder, Mo powder, Al powder and C powder as raw materials, mix the ingredients according to the stoichiometric molar ratio of Cr powder, Ti powder, Mo powder, Al powder and C powder of 1:1:1:1.1:2.

[0044] Step 2: Place the prepared raw material powder in a ball mill jar and ball mill twice, each time for 30 minutes, with a 30-minute interval; to obtain a mixed powder.

[0045] Step 3: The uniformly mixed powder is placed in a glove box under argon atmosphere and loaded into a graphite mold. The mold is then placed in a spark plasma sintering furnace for spark plasma sintering at a temperature of 1365℃ for 15 min and a pressure of 15 MPa to prepare Cr-Ti based MAX phase ceramic material.

[0046] Example 4 The chemical formula for a Cr-Ti based MAX phase ceramic material is Cr 1.6 Ti 0.6 Mo 0.8 AlC2.

[0047] The preparation method of Cr-Ti based MAX phase ceramic material is the same as that of Cr-Ti based MAX phase ceramic material in Example 1; the difference is that the materials are prepared according to the stoichiometric molar ratio of Cr powder, Ti powder, Mo powder, Al powder and C powder of 1.6:0.6:0.8:1.1:1.9.

[0048] Comparative Example 1 The chemical formula for a Cr-Ti based MAX phase ceramic material is Cr2Ti1AlC2.

[0049] A method for preparing Cr-Ti based MAX phase ceramic materials includes the following steps: Step 1: Using commercially available Cr powder, Ti powder, Al powder and C powder as raw materials, mix them according to a stoichiometric molar ratio of 2:1:1.1:2.

[0050] Step 2: Place the prepared raw material powder in a ball mill jar and ball mill twice, each time for 30 minutes, with a 30-minute interval; to obtain a mixed powder.

[0051] Step 3: The ball-milled and uniformly mixed powder is placed in a glove box under argon atmosphere protection, then loaded into a graphite mold. The loaded graphite mold is placed in a spark plasma sintering furnace for spark plasma sintering at a temperature of 1400℃, a holding time of 15min, and a pressure of 40MPa; thus, Cr-Ti based MAX phase ceramic material is prepared.

[0052] The properties of the Cr-Ti based MAX phase ceramic materials prepared in the above embodiments and comparative examples were characterized.

[0053] Figure 1 The X-ray diffraction patterns are those of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1.

[0054] Depend on Figure 1It can be seen that the diffraction peak shapes of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1 are consistent with the diffraction peak shapes of the Cr2Ti1AlC2 standard card and there are no obvious impurity peaks. This indicates that the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1 all have good crystallinity and phase purity.

[0055] Figure 2 The curves show the changes in the crystal axis parameters a-axis and c-axis of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1 as a function of Mo content.

[0056] Depend on Figure 2 It can be seen that, through Mo doping, the crystal axis parameters a-axis and c-axis of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 gradually increase with the Mo content, indicating that a solid solution phase structure is formed.

[0057] To further verify the resistance of Cr-Ti based MAX phase ceramic materials obtained in Examples 1-3 and Comparative Example 1 to lead-bismuth corrosion, the following operations were performed: The Cr-Ti based MAX phase ceramic materials obtained by spark plasma sintering in Examples 1-3 and Comparative Example 1 were processed into 8mm×8mm×2.5mm cuboid samples by wire cutting. The samples were then polished to 3000# sandpaper, ultrasonicated with alcohol for 30 minutes, and dried in a vacuum drying oven for 12 hours to obtain pretreated samples. The pretreated samples were then subjected to corrosion tests in a 550℃ high-temperature box furnace.

[0058] Figure 3 The images show cross-sectional scanning electron microscope (SEM) images of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1-3 and Comparative Example 1 after corrosion testing in a liquid lead-bismuth environment at 550°C for 2000 h. Specifically, (a) and (e) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Comparative Example 1 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively; (b) and (f) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Example 1 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively; (c) and (g) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Example 2 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively; and (d) and (h) are cross-sectional SEM images of the Cr-Ti based MAX phase ceramic material obtained in Example 3 after corrosion testing in a liquid lead-bismuth environment at 550°C for 1000 h and 2000 h, respectively.

[0059] Depend on Figure 3It can be seen that when the Mo content is low, no continuous oxide layer is formed in Comparative Example 1, Example 1 and Example 2. However, when the Mo content is increased to the content of Example 3, it can be observed that the oxide layer gradually becomes continuous and denser, indicating that doping with an appropriate amount of Mo can improve the material's resistance to lead-bismuth corrosion.

[0060] Figure 4 The curves showing the solubility of each element as a function of Mo content after corrosion testing of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1 in a liquid lead-bismuth environment at 550℃ are shown.

[0061] Table 1. Molar solubility of each element in Cr-Ti based MAX phase ceramic materials Note: "-" indicates no data. Molar solubility represents the molar ratio of dissolved atoms of each element.

[0062] As shown in Table 1 and Figure 4 After normalization, the molar solubility rates of Cr, Ti, and Al in Comparative Example 1 were 0.0077%, 0.0217%, and 0.6867%, respectively; the molar solubility rates of Cr, Ti, Mo, and Al in Example 1 were 0.0484%, 0.0594%, 0.0215%, and 1.2733%, respectively; the molar solubility rates of Cr, Ti, Mo, and Al in Example 2 were 0.0218%, 0.1239%, 0.0053%, and 1.0277%, respectively; and the molar solubility rates of Cr, Ti, Mo, and Al in Example 3 were 0.0098%, 0.041%, 0.0053%, and 1.0255%, respectively. In Example 3, except for Al, the molar solubility rates of the other elements were relatively similar. The molar solubility rate of Al was higher than that in Comparative Example 1, indicating that the doping of Mo promoted the migration of Al during the corrosion process.

[0063] Figure 5 Ellingham diagrams of the Cr-Ti based MAX phase ceramic materials obtained in Examples 1 to 3 and Comparative Example 1.

[0064] Depend on Figure 5 It can be seen that at a temperature of 550℃, the Cr-Ti based MAX phase ceramic material in Example 3 has the lowest Gibbs free energy required to generate Al2O3, indicating that Mo doping reduces the energy required to generate Al2O3 and promotes the migration of Al during the corrosion process.

[0065] The above are merely preferred embodiments of the present invention and are not intended to limit the present invention. Any modifications, equivalent substitutions, and improvements made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A Cr-Ti based MAX phase ceramic material, characterized in that, The Cr-Ti based MAX phase ceramic material is prepared by doping Cr2TiAlC2 as a matrix and partially replacing Cr and Ti elements with Mo; the chemical formula of the Cr-Ti based MAX phase ceramic material is: Cr 2-x Ti 1-x Mo 2x AlC2, or CrTiMoAlC2; Among them, 0 <x≤0.4。 2. The Cr-Ti based MAX phase ceramic material according to claim 1, characterized in that, The Cr-Ti based MAX phase ceramic material is prepared by ball milling powder containing Cr, Ti, Mo, Al, and C, followed by spark plasma sintering under a protective atmosphere. The conditions for spark plasma sintering are: temperature of 1300℃~1500℃, time of 5min~15min, and pressure of 10MPa~40MPa.

3. A method for preparing a Cr-Ti based MAX phase ceramic material, characterized in that, Includes the following steps: According to the stoichiometric ratio of the chemical expression of the Cr-Ti based MAX phase ceramic material as described in claim 1, powders containing Cr, Ti, Mo, Al, and C are used as raw materials and ball-milled to obtain a mixed powder. Under a protective atmosphere, the mixed powder was subjected to spark plasma sintering to obtain Cr-Ti based MAX phase ceramic materials.

4. The method for preparing Cr-Ti based MAX phase ceramic material according to claim 3, characterized in that, The conditions for spark plasma sintering are: temperature of 1300℃~1500℃, time of 5min~15min, and pressure of 10MPa~40MPa.

5. The method for preparing Cr-Ti based MAX phase ceramic material according to claim 3, characterized in that, The ball milling process is performed using intermittent ball milling.

6. The method for preparing Cr-Ti based MAX phase ceramic material according to claim 3, characterized in that, The raw material is a mixture of Cr powder, Ti powder, Mo powder, Al powder and C powder; the purity of the Cr powder, Ti powder, Mo powder, Al powder and C powder is ≥99%.

7. The application of a Cr-Ti based MAX phase ceramic material in the preparation of lead-bismuth corrosion-resistant materials, characterized in that, The Cr-Ti based MAX phase ceramic material is the Cr-Ti based MAX phase ceramic material as described in claim 1 or 2.

8. The application of the Cr-Ti based MAX phase ceramic material according to claim 7 in the preparation of lead-bismuth corrosion-resistant materials, characterized in that, The operating conditions for lead-bismuth resistant materials are: a liquid lead-bismuth environment at 500℃~600℃.

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