WO2019037688A1 - Uranium carbide pellet, preparation method therefor, and fuel rod - Google Patents
Uranium carbide pellet, preparation method therefor, and fuel rod Download PDFInfo
- Publication number
- WO2019037688A1 WO2019037688A1 PCT/CN2018/101376 CN2018101376W WO2019037688A1 WO 2019037688 A1 WO2019037688 A1 WO 2019037688A1 CN 2018101376 W CN2018101376 W CN 2018101376W WO 2019037688 A1 WO2019037688 A1 WO 2019037688A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- uranium carbide
- uranium
- carbide pellet
- pellet
- preparing
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/5158—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on actinide compounds
-
- G—PHYSICS
- G21—NUCLEAR PHYSICS; NUCLEAR ENGINEERING
- G21C—NUCLEAR REACTORS
- G21C3/00—Reactor fuel elements and their assemblies; Selection of substances for use as reactor fuel elements
- G21C3/42—Selection of substances for use as reactor fuel
- G21C3/58—Solid reactor fuel Pellets made of fissile material
- G21C3/62—Ceramic fuel
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3852—Nitrides, e.g. oxynitrides, carbonitrides, oxycarbonitrides, lithium nitride, magnesium nitride
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
- C04B2235/422—Carbon
- C04B2235/424—Carbon black
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
- C04B2235/422—Carbon
- C04B2235/425—Graphite
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/54—Particle size related information
- C04B2235/5418—Particle size related information expressed by the size of the particles or aggregates thereof
- C04B2235/5436—Particle size related information expressed by the size of the particles or aggregates thereof micrometer sized, i.e. from 1 to 100 micron
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/54—Particle size related information
- C04B2235/5418—Particle size related information expressed by the size of the particles or aggregates thereof
- C04B2235/5445—Particle size related information expressed by the size of the particles or aggregates thereof submicron sized, i.e. from 0,1 to 1 micron
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/60—Aspects relating to the preparation, properties or mechanical treatment of green bodies or pre-forms
- C04B2235/608—Green bodies or pre-forms with well-defined density
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
- C04B2235/6562—Heating rate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
- C04B2235/6567—Treatment time
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/658—Atmosphere during thermal treatment
- C04B2235/6581—Total pressure below 1 atmosphere, e.g. vacuum
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/66—Specific sintering techniques, e.g. centrifugal sintering
- C04B2235/661—Multi-step sintering
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/77—Density
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E30/00—Energy generation of nuclear origin
- Y02E30/30—Nuclear fission reactors
Definitions
- the invention relates to the technical field of nuclear reactors, in particular to a uranium carbide pellet, a preparation method thereof and a fuel rod.
- the existing commercial pressurized water reactor nuclear fuel is mainly uranium dioxide (UO 2 ) pellets, but the UO 2 pellets have low thermal conductivity and high centerline temperature. Even in the event of an accident, even if it has been safely shut down, the pellets are still stored. A large amount of decay heat, in the case of loss of coolant, the residual heat is difficult to export, so that the temperature of the fuel rod cladding rapidly rises to a dangerous level. Due to its own chemical properties, the existing zirconium alloy material begins to undergo a significant zirconium-water reaction above 650 °C. This reaction is an exothermic reaction and releases a large amount of hydrogen, which seriously deteriorates the safety of the fuel assembly, which can lead to core melting and severe hydrogen. Explosive and other catastrophic consequences.
- UO 2 uranium dioxide
- uranium carbide (UC) pellets are used, the thermal conductivity is higher and the uranium density is also improved. From the perspective of economy and safety, there are obvious advantages.
- the preparation of the existing uranium carbide pellets is mainly divided into two steps. One is the synthesis of uranium carbide powder, and the uranium carbide powder is usually synthesized by the method of carbothermal reduction of uranium dioxide at high temperature; the second is the compaction and sintering of the pellets. Pressureless sintering with a sintering aid or external field assisted hot press sintering is usually employed.
- the uranium carbide powder is easily dissolved into oxygen atoms, and the dissolution of oxygen atoms stabilizes UC 2 and decomposes U 2 C 3 .
- the concentration of solid dissolved oxygen in uranium carbide can reach 12.5at%, which will cause the thermal conductivity of uranium carbide to decrease.
- Uranium carbide is easily oxidized to UO 2 or other uranium oxides at temperatures above 200 ° C or oxygen partial pressures exceeding 20 kPa. Therefore, the milling and mixing of uranium carbide must be carried out in an argon-filled environment, and the purity of argon is also high.
- the sintering aid is added to sinter the uranium carbide pellet, although it is advantageous for densification, the melting point of the pellet is significantly reduced and the safety is lowered.
- the technical problem to be solved by the present invention is to provide a method for preparing a uranium carbide pellet which is one-step reaction synthesis and sintering densification and can be industrially mass-produced, and a prepared uranium carbide pellet and a fuel having the uranium carbide pellet. Baton.
- the technical solution adopted by the present invention to solve the technical problem thereof is to provide a preparation method of a uranium carbide pellet, which comprises the following steps:
- the uranium nitride powder and the carbon source are weighed according to a molar ratio of 1:0.8-1.5 and added to the solvent, and uniformly mixed to form a slurry;
- the uranium nitride powder has a purity greater than 95% and a particle size of 0.1-50 ⁇ m;
- the carbon source is carbon black and/or graphite, the purity is greater than 95%, and the particle size is 0.1-50 ⁇ m.
- the solvent is ethanol or acetone.
- step S3 comprises the following steps:
- step S3.1 the mixed powder is placed in a pellet steel mold for pre-compression molding
- step S3.2 the pre-formed green body is vacuum-sealed with oil paper, and the sealed green body is subjected to high pressure pressing using a cold isostatic press.
- step S4 comprises the following steps:
- step S4.1 the blank obtained in step S3 is placed in a high temperature pressureless furnace, in a vacuum environment, the temperature is raised to 1300 ° C -1600 ° C at a rate of 5-30 ° C / min and held for 0.5-4 h;
- the temperature is raised to 1700 ° C - 2000 ° C at a rate of 5-30 ° C / min and held for 1-14 h to obtain a uranium carbide pellet.
- step S4.2 argon gas is introduced into the high-temperature pressureless furnace and maintained at an atmospheric pressure to form an inert atmosphere.
- the ratio of uranium, carbon and nitrogen atoms in the obtained uranium carbide pellet is 1: (0.8-1.5): (0-0.2).
- the present invention also provides a uranium carbide pellet, which is produced by the preparation method described in any of the above.
- the present invention also provides a fuel rod comprising the above-described uranium carbide pellet.
- the invention has the beneficial effects of using the uranium nitride and carbon source as raw materials to realize the two processes of carbothermal reduction reaction and densification sintering under high temperature pressureless sintering, without using a hot pressing sintering process with low production efficiency, without introducing Sintering aids, avoiding the problem of lowering the melting point of the pellets, can achieve batch sintering, low energy consumption, and is suitable for industrial production of fuel pellets.
- the preparation method of the uranium carbide pellet of the invention comprises the following steps:
- the uranium nitride powder and the carbon source are weighed according to a molar ratio of 1:0.8-1.5 and added to the solvent, and uniformly mixed to form a slurry.
- the uranium nitride (UN) powder has a purity of more than 95% and a particle diameter of 0.1-50 ⁇ m.
- the carbon source (C) is carbon black and/or graphite having a purity of more than 95% and a particle diameter of 0.1 to 50 ⁇ m.
- the solvent can be ethanol or acetone.
- the uranium nitride powder and the carbon source are added to the solvent in order to sufficiently mix and evenly distribute the two.
- the resulting slurry can be dried by rotary evaporation to obtain a dried mixed powder.
- the evaporation drying time is adjusted according to the actual situation.
- the mixed powder is pressed into a green body having a density of 50% or more.
- the step S3 may further include the following steps:
- the holding time can be determined according to the situation, for example, 5 min, and the main purpose is to stabilize the shape of the blank after pressing.
- step S3.1 the mixed powder is placed in a pellet steel mold, and a pressure of 10 MPa may be applied for pre-compression molding.
- step S3.2 the pre-formed green body is vacuum-sealed with oil paper, and the sealed green body is subjected to high-pressure pressing such as 200 MPa using a cold isostatic press.
- Step S4 may further include the following steps:
- step S4.1 the blank obtained in step S3 is placed in a high-temperature pressureless furnace, and heated to a temperature of 1300 ° C - 1600 ° C at a rate of 5-30 ° C / min in a vacuum environment and maintained for 0.5-4 h; vacuum.
- This step mainly realizes the carbothermal reduction reaction of the green body, and the reaction is sufficiently carried out by heat preservation to complete the formation of uranium carbide.
- the temperature is raised to 1700 ° C - 2000 ° C at a rate of 5-30 ° C / min and held for 1-14 h to obtain a uranium carbide pellet.
- the uranium carbide pellets can be taken out after cooling to room temperature.
- This step mainly achieves densification of the green body to form a pellet having a predetermined density.
- argon gas may be introduced into the high temperature pressureless furnace and maintained at an atmospheric pressure to form an inert atmosphere.
- the in-situ reaction of uranium nitride and a carbon source is pressureless sintering, and densification is achieved by solid solution and carbon-nitrogen vacancy migration mass transfer.
- the ratio of uranium, carbon and nitrogen atoms is 1: (0.8-1.5): (0-0.2), and the above ratio is adjustable.
- the regulation of uranium carbon atom ratio and solid solution nitrogen includes changing the particle size and group distribution ratio of the raw materials, changing the reaction temperature and reaction holding time, changing the sintering temperature and sintering holding time, and changing the sintering atmosphere.
- the uranium carbide pellet of the present invention is obtained by the above preparation method.
- the fuel rod of the present invention includes the above-described uranium carbide pellet.
- a 98% by weight uranium carbide pellet was prepared and weighed according to a UN:C molar ratio of 1:1.2: 249 g of UN powder and 14.4 g of carbon black.
- the mixture was mixed with Si 3 N 4 balls at a speed of 120 rpm for 24 hours using ethanol as a solvent, and the obtained slurry was dried by rotary evaporation to obtain a uniformly mixed powder.
- the mixed powder is placed in a pellet steel mold, pre-compressed by applying a pressure of 10 MPa, and then the preformed blank is vacuum-sealed with oil paper, and then a cold isostatic press is used to apply a vacuum of 200 MPa to the vacuum-sealed blank of the oil-paper.
- the isostatic load is held at 200 MPa for 5 minutes to achieve an initial density of the core block of 50% or more.
- the green body was taken out and placed in a high temperature pressureless furnace for reaction sintering.
- the heating rate is 10 ° C / min
- the temperature is raised to 1400 ° C and held for 1 hour, which must maintain a vacuum environment.
- the vacuum was stopped, high-purity argon gas was introduced into the furnace and maintained at an atmospheric pressure, and then heated to 1800 ° C at a temperature rising rate of 10 ° C / min and kept for 4 hours. After the end of the heat preservation, cool to room temperature and take out the pellet.
- the sintered core phase was uranium carbide, and the diffraction peaks were not significantly shifted. It was found that the uranium carbide pellets obtained by thermal sintering at 1800 ° C for 4 hours had a density of 98%, a porosity of 2%, a pore diameter of 100 nm, and were open pores.
- a 95% density uranium carbide pellet was prepared.
- the carbon source was changed from carbon black in Example 1 to graphite. Weighed according to the UN:C molar ratio of 1:0.8: 249 g of UN powder and 9.6 g of graphite.
- the green body was prepared in the same manner as in Example 1, and the in-situ reaction temperature was maintained at 1500 ° C for 2 hours, and the sintering temperature was maintained at 1900 ° C for 1 hour.
- the sintered core phase was uranium carbide, and the diffraction peak shifted slightly to the left, indicating the presence of nitrogen solid solution. It was found that the uranium carbide pellet obtained by sintering at 1900 ° C for 1 hour had a density of 95%, a porosity of 5%, a pore diameter of 500 nm, and an open pore.
- a uranium carbide pellet having a density of 99% was prepared. Weighed according to the UN:C molar ratio of 1:1: 249 grams of UN powder, 12 grams of graphite.
- the green body was prepared in the same manner as in Example 1, and the in-situ reaction was carried out, and the pellet was prepared by pressureless sintering at 2000 ° C for 3 hours.
- the sintered core phase was uranium carbide, and the diffraction peaks were not significantly shifted. It was found that the density of uranium carbide pellets produced by heat-sintering at 2000 ° C for 14 hours was 99%, and no open pores were present.
- a 95% density uranium carbide pellet was prepared.
- the carbon source was changed from carbon black in Example 1 to graphite. Weighed according to the UN:C molar ratio of 1:1.5: 249 grams of UN powder and 18 grams of graphite.
- the green body was prepared in the same manner as in Example 1, and the in-situ reaction temperature was maintained at 1600 ° C for 1.5 hours, and the sintering temperature was maintained at 1700 ° C for 10 hours.
- the sintered core phase was uranium carbide, and the diffraction peak shifted slightly to the right, indicating the presence of carbon. It was found that the uranium carbide pellet obtained by holding and sintering at 1700 ° C for 10 hours has a density of 95%, a porosity of 5%, a pore diameter of 200 nm, and an open pore.
- a 97% dense uranium carbide pellet was prepared. Carbon black is used as a raw material. The molar ratio of UN:C was 1:0.9: 249 g of UN powder and 10.8 g of carbon black.
- the mixture was mixed with SiC balls at a speed of 120 rpm for 12 hours using acetone as a solvent, and the obtained slurry was dried by rotary evaporation to obtain a uniformly mixed powder.
- the mixed powder is placed in a pellet steel mold, and a pressure of 20 MPa is first applied to pre-press, and then the preformed blank is vacuum-sealed with oil paper, and then 250 MPa is applied to the vacuum-sealed blank of the oil paper using a cold isostatic press.
- the isostatic load is held at 250 MPa for 5 minutes to achieve an initial density of the core block of 50% or more.
- the green body was taken out and placed in a high temperature pressureless furnace for reaction sintering.
- the heating rate is 20 ° C / min
- the temperature is raised to 1550 ° C and held for 0.5 hours, which must maintain a vacuum environment.
- the vacuum was stopped, the high-purity argon gas was introduced into the furnace and maintained at an atmospheric pressure, and then heated to 1900 ° C at a temperature increase rate of 20 ° C / min and held for 8 hours. After the end of the heat preservation, cool to room temperature and take out the pellet.
- the sintered core phase was uranium carbide, and the diffraction peaks were not significantly shifted. It was found that the uranium carbide pellet obtained by sintering at 1900 ° C for 8 hours had a density of 97%, a porosity of 3%, a pore diameter of 300 nm, and an open pore.
- a 100% density uranium carbide pellet was prepared. Carbon black is used as a raw material. Weighed according to the UN:C molar ratio of 1:1.1: 249 grams of UN powder and 13.2 grams of carbon black.
- the body was prepared in the same manner as in Example 5, and the in-situ reaction temperature was maintained at 1600 ° C for 2 hours, and the sintering temperature was maintained at 1950 ° C for 12 hours.
- the sintered core phase was uranium carbide, and the diffraction peaks were not significantly shifted. It was found that the density of uranium carbide pellets obtained by holding and sintering at 1950 ° C for 12 hours was 100%, and the porosity was 0%.
- a 95.5% density uranium carbide pellet was prepared. Carbon black is used as a raw material. Weighed according to the UN:C molar ratio of 1:1.5: 249 grams of UN powder and 18 grams of carbon black.
- the mixture was mixed with SiC balls at a speed of 120 rpm for 24 hours using acetone as a solvent, and the obtained slurry was dried by rotary evaporation to obtain a uniformly mixed powder.
- the mixed powder is placed in a pellet steel mold, and a pressure of 15 MPa is applied first to pre-press, and then the preformed blank is vacuum-sealed with oil paper, and then 150 MPa is applied to the vacuum-sealed blank of the oil paper using a cold isostatic press.
- the isostatic load is held at 150 MPa for 5 minutes to achieve an initial density of the core block of 50% or more.
- the green body was taken out and placed in a high temperature pressureless furnace for reaction sintering.
- the heating rate is 30 ° C / min
- the temperature is raised to 1600 ° C and held for 2 hours, which must maintain a vacuum environment.
- the vacuum was stopped, the high-purity argon gas was introduced into the furnace and maintained at an atmospheric pressure, and then heated to 1850 ° C at a temperature increase rate of 30 ° C / min and held for 6 hours. After the end of the heat preservation, cool to room temperature and take out the pellet.
- the sintered core phase was uranium carbide, and the diffraction peak shifted slightly to the right, indicating the presence of carbon. It was found that the density of the uranium carbide pellets obtained by holding and sintering at 1850 ° C for 6 hours was 95.5%, and the porosity was 4.5%.
- a 96.5% density uranium carbide pellet was prepared. Carbon black is used as a raw material. Weighed according to the UN:C molar ratio of 1:1.3: 249 grams of UN powder and 15.6 grams of carbon black.
- the mixture was mixed with Si 3 N 4 balls at a speed of 120 rpm for 18 hours using acetone as a solvent, and the obtained slurry was dried by rotary evaporation to obtain a uniformly mixed powder.
- the mixed powder is placed in a pellet steel mold, pre-compressed by applying a pressure of 30 MPa, and then the preformed blank is vacuum-sealed with oil paper, and then 300 MPa is applied to the vacuum-sealed blank of the oil paper using a cold isostatic press.
- the isostatic load is held at 300 MPa for 5 minutes to achieve an initial density of the core block of 50% or more.
- the green body was taken out and placed in a high temperature pressureless furnace for reaction sintering.
- the heating rate is 15 ° C / min
- the temperature is raised to 1450 ° C and held for 2.5 hours, which must maintain a vacuum environment.
- the vacuum was stopped, the furnace was purged with high-purity argon gas and maintained at an atmospheric pressure, and then heated to 1950 ° C at a temperature increase rate of 15 ° C / min and held for 2 hours. After the end of the heat preservation, cool to room temperature and take out the pellet.
- the sintered core phase was uranium carbide, and the diffraction peak shifted slightly to the right, indicating the presence of carbon. It was found that the density of the uranium carbide pellets obtained by holding and sintering at 1950 ° C for 2 hours was 96.5%, and the porosity was 3.5%.
- a 96% density uranium carbide pellet was prepared. Carbon black is used as a raw material. Weighed according to the UN:C molar ratio of 1:0.8: 249 g of UN powder and 9.6 g of carbon black.
- the mixture was mixed with a Si 3 N 4 ball roll at a speed of 120 rpm for 20 hours using acetone as a solvent, and the resulting slurry was dried by rotary evaporation to obtain a uniformly mixed powder.
- the mixed powder is placed in a pellet steel mold, pre-compressed by applying a pressure of 5 MPa, and then the preformed blank is vacuum-sealed with oil paper, and then 150 MPa is applied to the vacuum-sealed blank of the oil paper using a cold isostatic press.
- the isostatic load is held at 150 MPa for 5 minutes to achieve an initial density of the core block of 50% or more.
- the green body was taken out and placed in a high temperature pressureless furnace for reaction sintering.
- the heating rate is 5 ° C / min
- the temperature is raised to 1300 ° C and held for 4 hours, which must maintain a vacuum environment.
- the vacuum was stopped, the high-purity argon gas was introduced into the furnace and maintained at an atmospheric pressure, and then heated to 1850 ° C at a temperature increase rate of 5 ° C / min and held for 5 hours. After the end of the heat preservation, cool to room temperature and take out the pellet.
- the sintered core phase was uranium carbide, and the diffraction peak shifted slightly to the left, indicating the presence of solid solution nitrogen. It was found that the density of uranium carbide pellets obtained by holding and sintering at 1850 ° C for 5 hours was 96% and the porosity was 4%.
- a 98.5% density uranium carbide pellet was prepared. Carbon black is used as a raw material. Weighed according to the UN:C molar ratio of 1:1.1: 249 grams of UN powder and 13.2 grams of carbon black.
- the mixture was mixed with Si 3 N 4 balls at a speed of 240 rpm for 24 hours using acetone as a solvent, and the resulting slurry was dried by rotary evaporation to obtain a uniformly mixed powder.
- the mixed powder is placed in a pellet steel mold, pre-compressed by applying a pressure of 10 MPa, and then the preformed blank is vacuum-sealed with oil paper, and then a cold isostatic press is used to apply a vacuum of 200 MPa to the vacuum-sealed blank of the oil-paper.
- the isostatic load is held at 200 MPa for 5 minutes to achieve an initial density of the core block of 50% or more.
- the green body was taken out and placed in a high temperature pressureless furnace for reaction sintering.
- the heating rate is 10 ° C / min
- the temperature is raised to 1350 ° C and held for 4 hours, which must maintain a vacuum environment.
- the vacuum was stopped, the high-purity argon gas was introduced into the furnace and maintained at an atmospheric pressure, and then heated to 1750 ° C at a temperature increase rate of 10 ° C / min and held for 13 hours. After the end of the heat preservation, cool to room temperature and take out the pellet.
- the sintered core phase was uranium carbide, and the diffraction peaks were not significantly shifted. It was found that the density of uranium carbide pellets obtained by holding and sintering at 1750 ° C for 13 hours was 98.5%, and the porosity was 1.5%.
Abstract
Description
Claims (10)
- 一种碳化铀芯块的制备方法,其特征在于,包括以下步骤:A method for preparing a uranium carbide pellet, comprising the steps of:S1、按照摩尔比1:0.8-1.5称取氮化铀粉体和碳源并加到溶剂中,混合均匀后形成浆料;S1, the uranium nitride powder and the carbon source are weighed according to a molar ratio of 1:0.8-1.5 and added to the solvent, and uniformly mixed to form a slurry;S2、将所述浆料烘干,获得混合粉体;S2, drying the slurry to obtain a mixed powder;S3、将所述混合粉体压制成密度50%以上的坯体;S3, pressing the mixed powder into a blank having a density of 50% or more;S4、高温无压烧结,获得致密度≥95%的碳化铀芯块。S4, high temperature pressureless sintering, obtaining a uranium carbide pellet with a density of ≥95%.
- 根据权利要求1所述的碳化铀芯块的制备方法,其特征在于,步骤S1中,所述氮化铀粉体纯度大于95%,粒径为0.1-50μm;The method for preparing a uranium carbide pellet according to claim 1, wherein in step S1, the uranium nitride powder has a purity greater than 95% and a particle diameter of 0.1-50 μm;所述碳源为炭黑和/或石墨,纯度大于95%,粒径为0.1-50μm。The carbon source is carbon black and/or graphite, the purity is greater than 95%, and the particle size is 0.1-50 μm.
- 根据权利要求1所述的碳化铀芯块的制备方法,其特征在于,步骤S1中,所述溶剂为乙醇或丙酮。The method for preparing a uranium carbide pellet according to claim 1, wherein in the step S1, the solvent is ethanol or acetone.
- 根据权利要求1所述的碳化铀芯块的制备方法,其特征在于,步骤S3包括以下步骤:The method for preparing a uranium carbide pellet according to claim 1, wherein the step S3 comprises the following steps:S3.1、将所述混合粉体在5-30Mpa的压力下预压成型;S3.1, pre-compressing the mixed powder under a pressure of 5-30 MPa;S3.2、将预压成型的坯体真空密封,以150-300Mpa的压力对密封的坯体进行高压压制,保压后获得密度50%以上的坯体。S3.2, vacuum-sealing the pre-formed blank, pressing the sealed blank at a pressure of 150-300 MPa, and obtaining a green body having a density of 50% or more after the pressure is maintained.
- 根据权利要求4所述的碳化铀芯块的制备方法,其特征在于,步骤S3.1中,将所述混合粉体放入芯块钢模具中进行预压成型;The method for preparing a uranium carbide pellet according to claim 4, wherein in step S3.1, the mixed powder is placed in a pellet steel mold for pre-compression molding;步骤S3.2中,将预压成型的坯体用油纸真空密封,使用冷等静压机对密封的坯体进行高压压制。In step S3.2, the pre-formed green body is vacuum-sealed with oil paper, and the sealed green body is subjected to high pressure pressing using a cold isostatic press.
- 根据权利要求1所述的碳化铀芯块的制备方法,其特征在于,步骤S4包括以下步骤:The method of preparing a uranium carbide pellet according to claim 1, wherein the step S4 comprises the following steps:S4.1、将步骤S3获得的坯体放入高温无压炉中,在真空环境下,以5-30℃/min的速率升温至1300℃-1600℃并保温0.5-4h;S4.1, the blank obtained in step S3 is placed in a high temperature pressureless furnace, in a vacuum environment, the temperature is raised to 1300 ° C -1600 ° C at a rate of 5-30 ° C / min and held for 0.5-4 h;S4.2、在惰性气氛下,以5-30℃/min的速率升温至1700℃-2000℃并保温1-14h,获得碳化铀芯块。S4.2. Under an inert atmosphere, the temperature is raised to 1700 ° C - 2000 ° C at a rate of 5-30 ° C / min and held for 1-14 h to obtain a uranium carbide pellet.
- 根据权利要求6所述的碳化铀芯块的制备方法,其特征在于,步骤S4.2中,往所述高温无压炉通入氩气并保持一个大气压,形成惰性气氛。The method for preparing a uranium carbide pellet according to claim 6, wherein in the step S4.2, argon gas is introduced into the high temperature pressureless furnace and maintained at an atmospheric pressure to form an inert atmosphere.
- 根据权利要求1-7任一项所述的碳化铀芯块的制备方法,其特征在于,获得的碳化铀芯块中,铀、碳、氮原子比例为1:(0.8-1.5):(0-0.2)。 The method for preparing a uranium carbide pellet according to any one of claims 1 to 7, wherein the ratio of uranium, carbon and nitrogen atoms in the obtained uranium carbide pellet is 1: (0.8-1.5): (0) -0.2).
- 一种碳化铀芯块,其特征在于,采用权利要求1-8任一项所述的制备方法制得。A uranium carbide pellet, which is produced by the production method according to any one of claims 1-8.
- 一种燃料棒,其特征在于,包括权利要求9所述的碳化铀芯块。A fuel rod comprising the uranium carbide pellet of claim 9.
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
GB2007032.2A GB2581903B (en) | 2017-08-21 | 2018-08-20 | Uranium carbide pellet, preparation method therefor, and fuel rod |
RO202000363A RO134863A2 (en) | 2017-08-21 | 2018-08-20 | Uranium carbide pellet, preparation method therefor and fuel rod |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201710719413.9A CN107500767B (en) | 2017-08-21 | 2017-08-21 | Uranium carbide pellet and preparation method thereof, fuel rod |
CN201710719413.9 | 2017-08-21 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2019037688A1 true WO2019037688A1 (en) | 2019-02-28 |
Family
ID=60692024
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/CN2018/101376 WO2019037688A1 (en) | 2017-08-21 | 2018-08-20 | Uranium carbide pellet, preparation method therefor, and fuel rod |
Country Status (4)
Country | Link |
---|---|
CN (1) | CN107500767B (en) |
GB (1) | GB2581903B (en) |
RO (1) | RO134863A2 (en) |
WO (1) | WO2019037688A1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112735618A (en) * | 2020-12-30 | 2021-04-30 | 中核北方核燃料元件有限公司 | Preparation method of SiC-based UCO core fuel pellet |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107500767B (en) * | 2017-08-21 | 2019-09-10 | 中广核研究院有限公司 | Uranium carbide pellet and preparation method thereof, fuel rod |
CN109461509B (en) * | 2018-09-29 | 2020-11-10 | 中广核研究院有限公司 | Inert matrix dispersion fuel pellet and preparation method thereof |
CN113012834A (en) * | 2019-12-20 | 2021-06-22 | 中核北方核燃料元件有限公司 | Preparation method of uranium nitride composite uranium trisilicon two-fuel pellet |
CN116655382A (en) * | 2023-05-22 | 2023-08-29 | 中国科学院过程工程研究所 | Method for preparing uranium carbide pellets by spark plasma sintering |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN105469838A (en) * | 2015-12-23 | 2016-04-06 | 中广核研究院有限公司 | Fuel assembly and fuel rod capable of improving reactor security of fuel assembly |
US20170040069A1 (en) * | 2011-08-04 | 2017-02-09 | Francesco Venneri | Dispersion Ceramic Micro-encapsulated (DCM) Nuclear Fuel and Related Methods |
CN107010960A (en) * | 2017-04-13 | 2017-08-04 | 中国工程物理研究院材料研究所 | A kind of preparation method and applications of uranium base double carbide |
CN107500767A (en) * | 2017-08-21 | 2017-12-22 | 中广核研究院有限公司 | Uranium carbide pellet and preparation method thereof, fuel rod |
-
2017
- 2017-08-21 CN CN201710719413.9A patent/CN107500767B/en active Active
-
2018
- 2018-08-20 RO RO202000363A patent/RO134863A2/en unknown
- 2018-08-20 WO PCT/CN2018/101376 patent/WO2019037688A1/en active Application Filing
- 2018-08-20 GB GB2007032.2A patent/GB2581903B/en active Active
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20170040069A1 (en) * | 2011-08-04 | 2017-02-09 | Francesco Venneri | Dispersion Ceramic Micro-encapsulated (DCM) Nuclear Fuel and Related Methods |
CN105469838A (en) * | 2015-12-23 | 2016-04-06 | 中广核研究院有限公司 | Fuel assembly and fuel rod capable of improving reactor security of fuel assembly |
CN107010960A (en) * | 2017-04-13 | 2017-08-04 | 中国工程物理研究院材料研究所 | A kind of preparation method and applications of uranium base double carbide |
CN107500767A (en) * | 2017-08-21 | 2017-12-22 | 中广核研究院有限公司 | Uranium carbide pellet and preparation method thereof, fuel rod |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112735618A (en) * | 2020-12-30 | 2021-04-30 | 中核北方核燃料元件有限公司 | Preparation method of SiC-based UCO core fuel pellet |
CN112735618B (en) * | 2020-12-30 | 2022-06-28 | 中核北方核燃料元件有限公司 | Preparation method of SiC-based UCO core fuel pellet |
Also Published As
Publication number | Publication date |
---|---|
GB2581903B (en) | 2022-03-23 |
CN107500767A (en) | 2017-12-22 |
GB202007032D0 (en) | 2020-06-24 |
CN107500767B (en) | 2019-09-10 |
GB2581903A (en) | 2020-09-02 |
RO134863A2 (en) | 2021-03-30 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2019037688A1 (en) | Uranium carbide pellet, preparation method therefor, and fuel rod | |
US5942455A (en) | Synthesis of 312 phases and composites thereof | |
CN109553419B (en) | Pneumatic solid-phase sintered boron carbide complex-phase ceramic and preparation method thereof | |
WO1997018162A9 (en) | Synthesis of 312 phases and composites thereof | |
CN110156475B (en) | Microwave synthesis method of uranium zirconium carbonitride powder | |
CN105967691B (en) | The method that hot pressed sintering prepares SiC/C ceramic composite | |
CN110484796B (en) | Transition metal carbide high-entropy ceramic particles and preparation method thereof | |
CN106116593B (en) | Preparation method of tungsten tetraboride ceramic powder | |
WO2020042949A1 (en) | Highly oriented nanometer max phase ceramic and preparation method for max phase in-situ autogenous oxide nanocomposite ceramic | |
US3953556A (en) | Method of preparing uranium nitride or uranium carbonitride bodies | |
KR20090064565A (en) | Low cte highly isotropic graphite | |
CN113943159B (en) | Preparation method of boron carbide composite ceramic | |
CN110668821B (en) | Method for preparing MAX phase ceramic under no pressure | |
US4332755A (en) | Sintered silicon carbide - aluminum nitride articles and method of making such articles | |
JPH0260633B2 (en) | ||
JPS6042187B2 (en) | Method of manufacturing silicon nitride objects | |
CN108409328B (en) | Preparation method of boron carbide ceramic composite material | |
CN112125315A (en) | Low-cost high-purity silicon hexaboride production process | |
CN108417278B (en) | Preparation method of metal type fuel pellet with high irradiation stability | |
CN115896495A (en) | Method for rapidly sintering high-uranium-density high-thermal-conductivity composite core block | |
JPH0312316A (en) | Boron nitride powder and its sintered body | |
CN110370176B (en) | Composite binder and preparation method thereof, polycrystalline cubic boron nitride composite sheet and preparation method and application thereof | |
CN108447576B (en) | Preparation method of MAX phase improved uranium dioxide pellet | |
JPS6337067B2 (en) | ||
JPS62876B2 (en) |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 18849083 Country of ref document: EP Kind code of ref document: A1 |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 202007032 Country of ref document: GB Kind code of ref document: A Free format text: PCT FILING DATE = 20180820 |
|
ENP | Entry into the national phase |
Ref document number: 202000363 Country of ref document: RO Kind code of ref document: A |
|
32PN | Ep: public notification in the ep bulletin as address of the adressee cannot be established |
Free format text: NOTING OF LOSS OF RIGHTS PURSUANT TO RULE 112(1) EPC (EPO FORM 1205 DATED 24/09/2020) |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 18849083 Country of ref document: EP Kind code of ref document: A1 |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 18849083 Country of ref document: EP Kind code of ref document: A1 |