High-thermal-conductivity radiation-resistant ceramic-based neutron absorbing material and preparation method thereof

Abstract

The invention relates to a high-thermal-conductivity radiation-resistant ceramic-based neutron absorbing material and a preparation method thereof. The preparation method of the high-thermal-conductivity radiation-resistant ceramic-based neutron absorbing material comprises the following steps: mixing amorphous ceramic powder with a high-thermal-conductivity material, and performing ultrahigh-pressure sintering to obtain the high-thermal-conductivity radiation-resistant ceramic-based neutron absorbing material. Through preparation of a high-density amorphous structure and doping modification design of a high-thermal-conductivity material, the neutron absorption control material with high thermal conductivity and irradiation resistance is obtained, and the neutron absorption control material is applied to the nuclear fields of nuclear reactivity control, nuclear radiation shielding and the like.

Description

Technical Field

[0001] The invention belongs to the technical field of neutron absorption materials and relates to a high-thermal-conductivity, radiation-resistant ceramic-based neutron absorption material and a preparation method thereof. Background Art

[0002] The startup, shutdown, and power regulation of nuclear power plant reactors are primarily controlled by control rods in the core. Control rod materials for nuclear reactors require a large neutron absorption cross section, long life, radiation resistance, and good mechanical properties. Neutron-absorbing materials containing elements with large thermal neutron absorption cross sections (such as B, In, Cd, Dy, Tm, Hf, Gd, Eu, and Sm) are particularly important.

[0003] Elements with large thermal neutron absorption cross sections are typically distributed within other matrix materials to create composite materials. These include metal-based neutron-absorbing composite materials, such as those based on Mo and Fe, and ceramic-based neutron-absorbing composite materials, such as those based on aluminates, zirconates, and titanates. In pressurized water reactors, neutron-absorbing materials are exposed to a supercritical or subcritical, high-pressure, weakly acidic environment for extended periods of time and must be able to continue serving for at least 15-20 years. Furthermore, nuclear reactors are plagued by a large number of radioactive particles, including neutrons, fission products, and high-energy radiation. Consequently, nuclear reactor neutron-absorbing materials must endure extremely harsh service environments, such as high radiation exposure, high temperature, high humidity, and acid corrosion, for extended periods of time.

[0004] Ceramic materials possess superior corrosion resistance and compressive strength compared to metals. Ceramic neutron absorbers include natural and 10B-enriched boron carbide (B4C), boric acid, dysprosium titanate (Dy2TiO5), rare earth hafnates (Re2HfO5), and lanthanide titanates (Ln2TiO5). Ceramic neutron absorbers, particularly oxide ceramics, have low thermal conductivity, generally below 5W / m·K. This can lead to excessively high core temperatures and severe swelling. Boron-containing ceramic neutron absorbers can release helium (He), forming helium bubbles or helium bubble-vacancy clusters, which are composed of helium and vacancies. This can lead to significant irradiation swelling and cracking of the material.

[0005] Irradiation structural damage is a major problem faced by neutron absorbing materials in the service environment of nuclear reactors. Existing neutron absorbing materials are generally crystalline structure materials. Irradiation will cause the integrity of the crystal structure to be destroyed and amorphization to occur, which will in turn cause swelling and degradation of material performance. The atomic arrangement of amorphous materials is long-range disordered, and the chaotic changes in atomic arrangement caused by irradiation can easily be annihilated in the disordered structure itself. Amorphous materials are a potential radiation-resistant material. In order to avoid the occurrence of crystallization, the forming and densification process of amorphous ceramics should be carried out at a lower temperature, but lower temperatures are not conducive to the discharge of pores. Traditional sintering methods (pressureless sintering, hot pressing sintering, spark plasma sintering, etc.) are difficult to prepare highly dense amorphous structural materials.

[0006] Neutron absorbers for control rods in high-power pressurized water reactors must not only meet high absorption capacity and long life requirements, but also exhibit good radiation resistance and fault tolerance. Considering these factors, such as neutron absorption capacity, corrosion resistance, structural stability, and radiation resistance, the development of new, highly thermally conductive, radiation-resistant ceramic-based neutron absorbers is of great significance. Summary of the Invention

[0007] In response to the above problems, the purpose of the present invention is to provide a high thermal conductivity and radiation-resistant ceramic-based neutron absorption material and a preparation method thereof. The present invention uses a compensation design of rare earth, ceramic matrix, and high thermal conductivity material, introduces an ultra-high pressure preparation process of a large cavity press, and synthesizes a nano-amorphous neutron absorption material with a higher interface density. Not only does it solve the problem of poor thermal conductivity of ceramic-based neutron absorption materials, but it also uses ultra-high pressure to prepare high-density new amorphous neutron absorption materials, thereby compensating for the poor radiation resistance of existing crystal structure neutron absorption materials. The present invention obtains a neutron absorption control material with high thermal conductivity and radiation resistance through the preparation of a high-density amorphous structure and the doping and modification design of a high thermal conductivity material.

[0008] In a first aspect, the present invention provides a method for preparing a high thermal conductivity and radiation-resistant ceramic-based neutron absorption material, comprising: mixing amorphous ceramic powder with a high thermal conductivity material, and sintering under ultra-high pressure to obtain the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material.

[0009] Preferably, in terms of mass percentage, the content of the amorphous ceramic powder is 80-99.9 wt %, and the content of the high thermal conductivity material is 0.1-20 wt %.

[0010] Preferably, the pressure of the ultra-high pressure sintering is 1 to 10 GPa, the sintering temperature is 300 to 1800° C., the holding time is 5 to 180 minutes, and the holding time is 1 to 120 minutes.

[0011] Preferably, the mixed powder is subjected to compression molding and cold isostatic pressing before ultrahigh pressure sintering; the pressure of the cold isostatic pressing is 100-400 MPa, and the time is 50-180 s.

[0012] Preferably, the high thermal conductivity material is selected from at least one of aluminum nitride, silicon nitride, carbon fiber, carbon nanotubes, graphene, diamond, and fullerene; preferably, the diamond is a coated diamond; more preferably, the coated diamond is at least one of titanium-coated diamond, nickel-coated diamond, boron carbide-coated diamond, graphene-coated diamond, fullerene-coated diamond, titanium carbide-coated diamond, and silicon carbide-coated diamond.

[0013] Preferably, the method for preparing the amorphous ceramic powder comprises: weighing a rare earth compound, ceramic powder, and a sintering aid according to mass percentage; mixing the rare earth compound with nitric acid and dissolving it in deionized water to obtain a rare earth nitrate solution; mixing the ceramic powder with nitric acid and dissolving it in deionized water to obtain a ceramic nitrate solution; adding the rare earth nitrate solution and the ceramic nitrate solution according to the total molar ratio of citric acid to metal cations, stirring to form a colloid, and then drying, crushing, screening, and high-temperature calcining to obtain the amorphous ceramic powder. In the present invention, a sol-gel method is used to obtain a uniformly dispersed ultrafine powder.

[0014] Preferably, the high temperature calcination temperature is 200-1200° C., and the time is 0.1-4 hours.

[0015] Preferably, in terms of mass percentage, the content of rare earth oxide is 8-50 wt %, the content of ceramic powder is 48-90 wt %, and the content of sintering aid is 0.2-5 wt %.

[0016] Preferably, the rare earth compound is a rare earth oxide; preferably, the rare earth oxide is selected from at least one of La2O3, Dy2O3, Tm2O3, Gd2O3, CeO2, Eu2O3, and Tb2O3.

[0017] Preferably, the ceramic powder is selected from at least one of zirconium oxide, titanium oxide, aluminum oxide, hafnium oxide and tungsten oxide.

[0018] Preferably, the sintering aid is selected from at least one of magnesium oxide, yttrium oxide, silicon oxide, calcium oxide, and tetraethyl orthosilicate.

[0019] In a second aspect, the present invention provides a high thermal conductivity and radiation-resistant ceramic-based neutron absorption material prepared according to the above preparation method.

[0020] In a third aspect, the present invention provides applications of the above-mentioned high thermal conductivity and radiation-resistant ceramic-based neutron absorption material in the nuclear field, such as application in nuclear reactivity control and nuclear radiation shielding.

[0021] Beneficial effects: The present invention has the following beneficial effects: (1) Improved radiation resistance: First, amorphous ceramic powder containing rare earths is synthesized, and then high-density amorphous ceramic blocks are prepared using ultra-high pressure. The disordered structure of amorphous ceramics is used to annihilate the chaotic changes in atomic arrangement caused by radiation, thereby improving the radiation resistance of neutron absorbing materials; (2) Improved thermal conductivity: by doping with high thermal conductivity materials, the thermal conductivity of ceramic-based neutron absorbers can be improved; (3) Compared with the existing technology (conventional ceramic sintering), the present invention utilizes an ultrahigh pressure process to prepare neutron-absorbing materials, lowering the sintering temperature and achieving rapid material densification. Simultaneously, the microstructure is refined, and the nucleation, precipitation, and growth of grains are inhibited, resulting in amorphous or nanocrystalline high-temperature structural ceramic materials. BRIEF DESCRIPTION OF THE DRAWINGS

[0022] Figure 1 This is a cross-sectional microstructure photograph of Example 1; Figure 2 is the XRD characterization diagram of Example 1; Figure 3 This is a cross-sectional microstructure photograph of Comparative Example 2. DETAILED DESCRIPTION

[0023] To further illustrate the content, features and practical effects of the present invention, the present invention is described in detail below in conjunction with the embodiments. It should be noted that the modification method of the design of the present invention is not limited to these specific embodiments. Without departing from the spirit and connotation of the design of the present invention, equivalent replacements and modifications made by those skilled in the art based on the content of the present invention are also within the scope of the present invention.

[0024] First, the present invention provides a method for preparing a high-thermal-conductivity, radiation-resistant ceramic-based neutron-absorbing material. Ceramic is used as a matrix, rare earth compounds are uniformly mixed to obtain an amorphous ceramic powder, and then a high-thermal-conductivity material is doped into the amorphous ceramic powder. The resulting mixture is compression-molded and cold isostatically pressed to obtain a green body. The green body is then placed in an ultra-high-pressure device for high-temperature, ultra-high-pressure sintering to obtain a high-thermal-conductivity, radiation-resistant ceramic-based neutron-absorbing material. Amorphous material is a potential radiation-resistant material. The chaotic changes in atomic arrangement caused by radiation are easily annihilated in its own disordered structure. In the present invention, amorphous powder is first prepared, and then ultra-high-pressure, low-temperature, rapid sintering is used to obtain a highly dense amorphous ceramic material, thereby improving the thermal conductivity, radiation resistance, and other comprehensive capabilities of the ceramic-based neutron-absorbing material.

[0025] The ultrahigh-pressure sintering used in the present invention refers to a sintering method for densifying ceramic materials under pressure conditions of ≥1GPa. It has the characteristics of fast pressure and temperature ramp rates, and can achieve an ultrahigh-pressure environment of 5-6GPa in just over ten minutes. Compared with traditional methods such as pressureless sintering, hot pressing sintering, and spark plasma sintering (SPS), the ultrahigh-pressure sintering used in the present invention has the following advantages: (1) lowering the sintering temperature to achieve rapid densification of the material; (2) refining the microstructure and inhibiting the nucleation, precipitation, and growth of grains; (3) ultrahigh pressure changes the crystal structure and even the atomic and electronic states, obtaining a new high-density structural phase or new material; (4) obtaining amorphous or nanocrystalline high-temperature structural materials, giving the material better radiation resistance and mechanical properties.

[0026] The following is an exemplary description of the preparation method of the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material provided by the present invention.

[0027] Preparation of amorphous ceramic powder. A rare earth compound, ceramic powder, and sintering aid are weighed according to mass percentage; the rare earth compound is mixed with excess nitric acid and dissolved in deionized water to obtain a rare earth nitrate solution; the ceramic powder is mixed with excess nitric acid and dissolved in deionized water to obtain a ceramic nitrate solution; the rare earth nitrate solution and the ceramic nitrate solution are added according to the total molar ratio of citric acid to metal cations, stirred to form a colloid, and then dried, crushed, sieved, and calcined at high temperature to obtain the amorphous ceramic powder.

[0028] In an optional embodiment, based on mass percentage, the content of rare earth oxide is 8-50 wt %, the content of ceramic powder is 48-90 wt %, and the content of sintering aid is 0.2-5 wt %.

[0029] In an optional embodiment, the rare earth compound is a rare earth oxide; preferably, the rare earth oxide is selected from at least one of La2O3, Dy2O3, Tm2O3, Gd2O3, CeO2, Eu2O3, and Tb2O3. The ceramic powder is selected from at least one of zirconium oxide, titanium oxide, aluminum oxide, hafnium oxide, and tungsten oxide. The sintering aid is selected from at least one of magnesium oxide, yttrium oxide, silicon oxide, calcium oxide, and tetraethyl orthosilicate.

[0030] In an optional embodiment, the high-temperature calcination temperature is 200 to 1200° C., and the time is 0.1 to 4 hours.

[0031] Doping and modification of high thermal conductivity materials: Amorphous ceramic powder is mixed with uniformly dispersed high thermal conductivity materials to obtain a mixed powder.

[0032] In an optional embodiment, the content of the amorphous ceramic powder is 80-99.9 wt %, and the content of the high thermal conductivity material is 0.1-20 wt %, calculated in percentage by mass.

[0033] In an optional embodiment, the high thermal conductivity material is selected from at least one of aluminum nitride, silicon nitride, carbon fiber, carbon nanotubes, graphene, diamond, and fullerene; preferably, the diamond is a coated diamond; more preferably, the coated diamond is at least one of titanium-coated diamond, nickel-coated diamond, boron carbide-coated diamond, graphene-coated diamond, fullerene-coated diamond, titanium carbide-coated diamond, and silicon carbide-coated diamond.

[0034] Ultra-high pressure sintering. After the mixed powder is molded and cold isostatically pressed, it is placed in the cavity of a high-temperature and high-pressure synthesis equipment and sintered under ultra-high pressure to obtain a neutron absorber with a highly dense nano / amorphous structure, that is, the high thermal conductivity and radiation-resistant neutron absorber.

[0035] In an optional embodiment, the ultra-high pressure sintering pressure is 1 to 10 GPa, the sintering temperature is 300 to 1800° C., the holding time is 5 to 180 min, and the holding time is 1 to 120 min.

[0036] In an optional embodiment, the cold isostatic pressing treatment is performed at a pressure of 100 to 400 MPa and for a time of 50 to 180 seconds.

[0037] The following examples are further given to illustrate the present invention in detail. It should also be understood that the following examples are only used to further illustrate the present invention and cannot be understood as limiting the scope of protection of the present invention. Some non-essential improvements and adjustments made by those skilled in the art based on the above content of the present invention all fall within the scope of protection of the present invention. The specific process parameters and the like in the following examples are only examples within a suitable range, that is, those skilled in the art can make selections within a suitable range through the description herein, and are not limited to the specific numerical values ​​exemplified below.

[0038] Example 1

[0039] The preparation process of the high thermal conductivity radiation-resistant ceramic-based neutron absorption material in Example 1 includes: (1) Preparation of amorphous powder. Take 100g of raw material powder, which contains 4wt% of rare earth europium oxide (Eu2O3), 4wt% of rare earth dysprosium oxide (Dy2O3), 90wt% of zirconium oxide, and 2wt% of magnesium oxide. Dissolve the rare earth Dy2O3 in excess HNO3 to obtain a nitrate solution of a certain concentration, add deionized water to dissolve it, and obtain a dysprosium nitrate solution; obtain a europium nitrate solution and a zirconium nitrate solution in the same manner; then, add an aqueous solution of dysprosium nitrate, an aqueous solution of europium nitrate, and an aqueous solution of zirconium nitrate according to the molar ratio of citric acid to total metal cations, stir at a constant temperature until a colloid is formed, place it in a high-temperature box to dry, grind it, sieve it, and then calcine it in a high-temperature furnace at 300°C for 0.5h to obtain an amorphous ceramic powder; (2) Doping and modification of high thermal conductivity materials. Take 100g of mixed powder, wherein 80wt% of amorphous ceramic powder and 20wt% of silicon carbide coated diamond are mixed to obtain a mixed powder; (3) Ultrahigh pressure sintering. The mixed powder was cold isostatically pressed at 200 MPa for 90 seconds and then placed in a six-sided top press for high temperature and ultrahigh pressure sintering to prepare a ceramic-based neutron absorber. The sintering pressure was 10 GPa, the sintering temperature was 1000°C, the holding time was 60 minutes, and the holding time was 120 minutes.

[0040] According to tests, the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material prepared in Example 1 has a thermal conductivity of 20.5 W / m·° C. and a relative density of 98.8%.

[0041] Example 2

[0042] The preparation process of the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material in this Example 2 refers to Example 1, with the only difference being that: in step (1), 100 g of raw material powder is taken, wherein 50 wt% of rare earth terbium oxide (Tb2O3), 48 wt% of aluminum oxide, and 0.2 wt% of silicon oxide are contained; the calcination temperature is 1200°C, and the calcination time is 4 h; in step (2), 100 g of mixed powder is taken, wherein 99.9 wt% of amorphous ceramic powder and 0.1 wt% of carbon nanotubes are contained; in step (3), the sintering pressure is 1 GPa, the sintering temperature is 300°C, the holding time is 5 min, and the pressure holding time is 1 min.

[0043] According to tests, the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material prepared in Example 2 has a thermal conductivity of 12.8 W / m·°C and a relative density of 97.2%.

[0044] Example 3

[0045] The preparation process of the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material in this Example 3 refers to Example 1, with the only difference being: in step (1), 100 g of raw material powder is taken, wherein the rare earth europium oxide (Eu2O3) is 15 wt%, aluminum oxide is 82 wt%, tetraethyl orthosilicate is 1.5 wt%, and yttrium oxide is 1.5 wt%; the calcination temperature is 1000°C, and the calcination time is 2 h; in step (2), 100 g of mixed powder is taken, wherein the amorphous ceramic powder is 90 wt%, diamond is 8 wt%, and carbon fiber is 2 wt%; in step (3), the sintering pressure is 4.5 GPa, the sintering temperature is 1800°C, the holding time is 180 min, and the pressure holding time is 30 min.

[0046] According to tests, the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material prepared in Example 3 has a thermal conductivity of 15.2 W / m·°C and a relative density of 98.5%.

[0047] Example 4

[0048] The preparation process of the high thermal conductivity, radiation-resistant ceramic-based neutron absorber in Example 4 is similar to that in Example 1, except that: in step (1), 100 g of raw material powder is prepared, wherein the raw material powder comprises 10 wt% of rare earth terbium oxide (Tb2O3), 40 wt% of thulium oxide (Tb2O3), 48 wt% of hafnium oxide, 1 wt% of calcium oxide, and 1 wt% of silicon oxide. The calcination temperature is 900°C, and the calcination time is 1.5 h. In step (2), 100 g of mixed powder is prepared, wherein the raw material powder comprises 94 wt% of amorphous ceramic powder, 1 wt% of aluminum nitride, 2 wt% of fullerene, and 3 wt% of carbon nanotubes. In step (3), the sintering pressure is 5.2 GPa, the sintering temperature is 1350°C, the holding time is 15 min, and the holding time is 20 min.

[0049] After testing, the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material prepared in Example 4 had a thermal conductivity of 25.4 W / m·° C. and a relative density of 97.6%.

[0050] Comparative Example 1

[0051] The preparation process of the neutron absorption material in this comparative example 1 refers to that in Example 1, except that the doping of the high thermal conductivity material in step (2) is not performed, and 100 wt% amorphous ceramic powder is used for high temperature and ultrahigh pressure sintering in step (3).

[0052] According to tests, the neutron absorption material prepared in Comparative Example 1 has a thermal conductivity of 4.8 W / m·° C. and a relative density of 95.4%.

[0053] Comparative Example 2

[0054] The preparation process of the neutron absorbing material in this comparative example 2 refers to that in Example 1, with the only difference being that in step (3), pressureless sintering is performed in a conventional vacuum sintering furnace, the sintering temperature is 1000° C., and the holding time is 60 min.

[0055] Testing revealed that the neutron absorber material prepared in Comparative Example 2 had a thermal conductivity of 9.8 W / m·°C and a relative density of 82.6%. Compared to Examples 1-4, the significantly lower thermal conductivity and relative density of Comparative Example 2 are attributed to the ultrahigh-pressure sintering employed in Examples 1-4. This high pressure promotes plastic deformation and fragmentation of particles, resulting in more efficient particle rearrangement and even full densification at temperatures lower than conventional sintering temperatures.

[0056] Figure 1 This is a cross-sectional microstructure photograph of Example 1. As can be seen from the figure, the grain size is at the submicron and nanometer level. Ultra-high pressure refines the microstructure, inhibits the nucleation, precipitation and growth of grains, and obtains nanocrystalline high-temperature structural ceramic materials.

[0057] Figure 2This is the XRD characterization diagram of Example 1. As can be seen from the figure, the diffraction peaks of the ceramic match well with the standard card of pyrochlore, and the peaks do not have obvious shifts, indicating that the lattice parameters change little after doping by the method of the present invention, and the pyrochlore ceramic with high solid solubility is obtained by sintering.

[0058] Figure 3 This is a cross-sectional microstructure photograph of Comparative Example 2. As can be seen from the figure, the grain size of the ceramics produced by conventional pressureless sintering is relatively large, ranging from 30 to 80 microns.

Claims

1. A method for preparing a high thermal conductivity and radiation-resistant ceramic-based neutron absorption material, characterized in that: include: The amorphous ceramic powder is mixed with a high thermal conductivity material, and subjected to ultra-high pressure sintering to obtain the high thermal conductivity and radiation-resistant ceramic-based neutron absorption material.

2. The preparation method according to claim 1, characterized in that Calculated by mass percentage, the content of the amorphous ceramic powder is 80-99.9 wt %, and the content of the high thermal conductivity material is 0.1-20 wt %.

3. The preparation method according to claim 1 or 2, characterized in that The ultra-high pressure sintering has a pressure of 1 to 10 GPa, a sintering temperature of 300 to 1800° C., a heat preservation time of 5 to 180 minutes, and a pressure preservation time of 1 to 120 minutes.

4. The preparation method according to any one of claims 1 to 3, characterized in that The mixed powder is subjected to compression molding and cold isostatic pressing before ultrahigh pressure sintering; the pressure of the cold isostatic pressing is 100-400 MPa and the time is 50-180 seconds.

5. The preparation method according to any one of claims 1 to 4, characterized in that The high thermal conductivity material is selected from at least one of aluminum nitride, silicon nitride, carbon fiber, carbon nanotubes, graphene, diamond, and fullerene; preferably, the diamond is a coated diamond; more preferably, the coated diamond is at least one of titanium coated diamond, nickel coated diamond, boron carbide coated diamond, graphene coated diamond, fullerene coated diamond, titanium carbide coated diamond, and silicon carbide coated diamond.

6. The preparation method according to any one of claims 1 to 5, characterized in that The preparation method of the amorphous ceramic powder includes: weighing a rare earth compound, ceramic powder and a sintering aid according to mass percentage; mixing the rare earth compound with nitric acid and dissolving the mixture in deionized water to obtain a rare earth nitrate solution; mixing the ceramic powder with nitric acid and dissolving the mixture in deionized water to obtain a ceramic nitrate solution; adding the rare earth nitrate solution and the ceramic nitrate solution according to the total molar ratio of citric acid to metal cations, stirring to form a colloid, and then drying, crushing, screening and high-temperature calcining to obtain the amorphous ceramic powder.

7. The preparation method according to claim 6, characterized in that The high-temperature calcination temperature is 200-1200° C., and the time is 0.1-4 hours.

8. The preparation method according to claim 6 or 7, characterized in that Calculated by mass percentage, the content of rare earth oxide is 8-50wt%, the content of ceramic powder is 48-90wt%, and the content of sintering aid is 0.2-5wt%.

9. The preparation method according to any one of claims 6 to 8, characterized in that The rare earth compound is a rare earth oxide; preferably, the rare earth oxide is selected from at least one of La2O3, Dy2O3, Tm2O3, Gd2O3, CeO2, Eu2O3, and Tb2O3; The ceramic powder is selected from at least one of zirconium oxide, titanium oxide, aluminum oxide, hafnium oxide, and tungsten oxide; The sintering aid is selected from at least one of magnesium oxide, yttrium oxide, silicon oxide, calcium oxide, and tetraethyl orthosilicate.

10. A high thermal conductivity and radiation-resistant ceramic-based neutron absorption material prepared according to the preparation method according to any one of claims 1 to 9.

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