WO2014021600A1 - Matériau absorbant les neutrons et son procédé de préparation - Google Patents

Matériau absorbant les neutrons et son procédé de préparation Download PDF

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WO2014021600A1
WO2014021600A1 PCT/KR2013/006810 KR2013006810W WO2014021600A1 WO 2014021600 A1 WO2014021600 A1 WO 2014021600A1 KR 2013006810 W KR2013006810 W KR 2013006810W WO 2014021600 A1 WO2014021600 A1 WO 2014021600A1
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neutron absorbing
absorbing material
carbon
boron
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Korean (ko)
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최용
문병문
손동성
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단국대학교 천안캠퍼스 산학협력단
국립대학법인 울산과학기술대학교 산학협력단
한국생산기술연구원
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Priority to KR1020157003590A priority Critical patent/KR102061839B1/ko
Publication of WO2014021600A1 publication Critical patent/WO2014021600A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D23/00—Casting processes not provided for in groups B22D1/00 - B22D21/00
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a neutron absorbing material and a manufacturing method thereof, and more particularly, to a neutron absorbing material having excellent strength and corrosion resistance containing gadolium (Gd) and boron (B) having excellent neutron absorbing ability and a method for producing the same. .
  • Gd gadolium
  • B boron
  • Conventional techniques for neutron absorbing materials include Korean Patent No. 10-0147082, Austenitic steel having excellent odor resistance to neutron irradiation, and Aluminum composite having neutron absorbing performance and a method of manufacturing the same.
  • Cermet and composite materials containing boron carbide (Al alloy-B 4 C) in commercial aluminum alloys have the advantage of being lightweight and easy to manufacture, but due to the characteristics of the material, the melting point of aluminum is low and the welding area is weak. And, there is a disadvantage that the corrosion resistance of the aluminum-boron carbide interface is weak.
  • the austenitic single-phase structure containing boron (B) has superior strength, corrosion resistance, and weldability as compared with aluminum alloy-boron carbide composites, but has a low solubility of boron for iron (Fe) and grain boundary segregation during firing.
  • boron (B) reacts with neutrons to form helium gas, it is disadvantageous in comparison with gadolium (Gd) in neutron absorbing materials used for a long time. Meanwhile, gadolium (Gd) has a problem in that it is expensive in terms of price compared to boron (B).
  • the present invention is to propose a neutron absorbing material having a neutron absorbing ability, excellent strength and corrosion resistance, and a method of manufacturing the same by using a combination of gadolium (Gd) and boron (B) having excellent neutron absorbing ability.
  • Gd gadolium
  • B boron
  • Gd gadolium
  • B boron
  • Mo molybdenum
  • Mo molybdenum
  • a neutron absorbing material having high strength and high corrosion resistance it is possible to provide a neutron absorbing material having high strength and high corrosion resistance, and to suppress grain boundary segregation by a two-stage solidification heat treatment which is quenched by quenching during the production by the melt casting process.
  • a neutron absorbing material having improved machinability can be manufactured.
  • FIG. 1 is an analysis diagram showing the distribution of the Gd component of 2.5% Gd-containing SUS ingot prepared by pressure sintering by area mapping with EPMA according to an embodiment of the present invention.
  • FIG. 1 (a) is an SEM image
  • FIG. 1 (b) is an image in which the position of Gd is represented as a spot.
  • FIG. 2 is an analysis showing the component analysis of 2.5% Gd-containing SUS prepared by vacuum magnetic buoyancy dissolution method analyzed by EPMA according to an embodiment of the present invention.
  • FIG. 2 (a) is an SEM image
  • FIG. 2 (b) is an image in which the position of Gd is represented as a spot.
  • FIG. 3 is a SEM image (a) of a Gd-duplex stainless steel and a distribution map of Cr (b), Ni (c), and Gd (d) that are area mapped with EDX according to an embodiment of the present invention. .
  • FIG. 5 is a graph showing the solution heat treatment conditions according to an embodiment of the present invention.
  • FIG. 6 is a photograph of a neutron absorbing material after hot rolling according to an embodiment of the present invention.
  • FIG. 7 is a microstructure photograph of a neutron absorbing material according to an embodiment of the present invention.
  • gadolium (Gd) and boron (B) are excellent in neutron absorbing ability and can be added to aluminum or stainless steel to be used as neutron absorbers or shielding materials.
  • B boron
  • the composition of the steel used as a neutron absorber or shield and the microstructure of the steel are not properly adjusted, it is difficult to secure corrosion resistance and strength suitable for the application.
  • the present inventors maintain the neutron absorption capability provided by these elements by appropriately adding the amounts of gadolium and boron, and at the same time, reduce the amount of expensive gadolium, and use duplex stainless steel as a neutron absorbing material. It has been devised to devise a proper corrosion resistance and strength.
  • Cr, Mo, W, N in the above formula means the weight% value of these elements, respectively.
  • gadolium When gadolium (Gd) is added at less than 0.1%, the effect of neutron absorption is not sufficiently obtained. Also, when it is more than 2.5%, the oxidative property between the atmosphere and the melt is high in a high temperature liquid molten state, which greatly reduces the flowability of the molten metal. ) To form an intermetallic compound and greatly reduce the formability can be limited to the above range.
  • boron When boron is added in less than 0.3%, it is difficult to express the neutron absorbing remarkably, and in the case of more than 0.8%, boron may cause brittleness of the material, thereby making it difficult to mold in the solid state of the alloy, and thus it may be limited to the above range.
  • Molybdenum (Mo) may be added to improve the alloy surface stability, that is, corrosion resistance in harsh corrosive environments, but may not be added in a relatively harsh general environment.
  • Molybdenum ( ⁇ ) phase which is very fragile in a two-phase (duplex) alloy is formed, and thus has an adverse effect. Therefore, it is good to add at 4.0% or less (including 0%).
  • Tungsten (W) is an expensive alloying element that positively affects the corrosion resistance, and when added in large amounts, it can promote the formation of intermetallic compounds, and therefore, in terms of phase stability, mechanical properties and corrosion resistance, the content of tungsten (6.5% or less) is less than 6.5% (including 0%). Is added.
  • Nitrogen is a useful element that improves the resistance to formulas, and its effect is about 30 times more than chromium.
  • the synergistic effect greatly improves the corrosion resistance.
  • the carbon content is lowered for the purpose of improving the intergranular corrosion resistance, it is possible to obtain the compensation of mechanical properties by adding nitrogen, inhibiting the formation of chromium carbide and increasing the tensile strength and the yield strength without reducing the elongation.
  • Carbon is preferably contained as little as possible because it improves the flowability of the molten metal during melt casting of the alloy, but has a very bad effect on corrosion resistance.
  • it is preferable to contain 0.05% or less, but when it exceeds 0.1%, the corrosion resistance may be extremely deteriorated.
  • impurities which are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art, all of them are not specifically mentioned in the present specification.
  • Cr, Mo, W, N means the weight% value of these elements, respectively. If the equivalent index value is less than 30, sufficient corrosion resistance cannot be secured, and the higher the equivalent index value, the higher the corrosion resistance, so no particular upper limit is set.
  • the neutron absorbing material of the present invention additionally contains at least one of vanadium (V): 10 times or less of carbon (C) and 10 times or less of niobium (Nb): carbon (C). It may include.
  • V Vanadium (V): 10 times or less of carbon (C) content
  • Nb Niobium (Nb): 10 times or less of carbon (C) content
  • Vanadium and niobium typically contain 0.1 to 0.5% for heat treatment and high temperature phase stability.
  • the alloy reacts with carbon, which has a great influence on corrosion resistance, to form carbides, thereby suppressing the adverse effect of carbon, each is added at 10 times or less of the carbon content.
  • the amount of vulnerable carbides increases and there is a fear that the corrosion resistance is rather deteriorated due to excessive carbide extraction. It is better not to add carbon when it is lower than 0.03%.
  • nickel (Ni): 0.4-8.0%, silicon (Si): 0.8% or less (except 0%), manganese (Mn): 1.2% or less (except 0%), phosphorus (P): 0.08% or less (including 0%), sulfur (S): 0.08% or less (including 0%) may be further included.
  • Nickel is an austenite stabilizing element and is a useful element that increases the overall corrosion resistance in terms of corrosion resistance, and therefore it needs to contain at least 0.4% or more. Considering the relationship with the ordinary ratio and the expensive material, it is limited to 8.0% or less.
  • Silicon is an element that stabilizes the ferrite structure, which has deoxidation effect during dissolution and refining, increases acid resistance and increases molten steel fluidity during casting, and decreases surface defects. Can increase, and the toughness and ductility of the steel is lowered. In view of corrosion resistance, 0.8% or less is preferable.
  • Manganese is an austenite stabilizing element that can replace expensive nickel, an element that increases the solubility of nitrogen and lowers the resistance to high temperature deformation. In order to improve the corrosion resistance by increasing the nitrogen content, an appropriate amount of manganese is an essential element. Corrosion resistance is degraded when a large amount is added, and the upper limit thereof is limited to 1.2% or less since it promotes the formation of highly brittle intermetallic phases.
  • Phosphorus (P) is not artificially added for the manufacture of alloys, but it is inevitably contained in steel as it is naturally present in iron, alloy iron, and various non-ferrous metal elements used as raw materials while the alloy is industrially manufactured. Phosphorus is an element that causes brittleness of materials and deteriorates corrosion resistance, so the maximum allowable value is controlled to 0.08%. On the other hand, since no more phosphorus is contained, a lower limit is not set.
  • Sulfur is not artificially added for the manufacture of alloys, but it is inevitably contained in steel as trace amounts are naturally present in iron, ferroalloy, and various non-ferrous metal elements used as raw materials while the alloy is industrially manufactured.
  • the maximum allowable value is controlled to 0.08% as it may cause cracking or deterioration of ductility after completion of the product, causing material brittleness.
  • sulfur is so good that it does not contain, a lower limit is not set.
  • the microstructure of the steel having the composition as described above is a mixture of two phases of austenite and ferrite
  • the present invention can target a duplex stainless steel having such a two-phase structure.
  • Duplex stainless steel has a fine combination of austenite ( ⁇ ) phase, which provides excellent processability, and ferrite ( ⁇ ) phase, which provides excellent corrosion resistance, so that the strength is at least 1.7 times higher than that of austenitic stainless steel. Excellent stress corrosion cracking resistance.
  • gadolium Gd
  • gadolium oxide Gd 2 O 3
  • boron B
  • a boron compound e.g., FeB, FeB 2 , CrB, CrB 2
  • nano size 100nm or less (except 0nm)
  • Such materials present on the microstructure of the austenite-ferrite biphasic phase can produce an effect of enhancing strength and simultaneously neutron absorbing ability in the neutron absorbing material.
  • FIG. 1 is an analysis diagram showing the component analysis of 2.5% Gd-containing stainless steel (SUS) ingot prepared by pressure sintering analyzed by EPMA according to an embodiment of the present invention
  • Figure 2 is an embodiment of the present invention It is the analysis figure which showed the component analysis of the 2.5% Gd containing SUS prepared by the vacuum magnetic buoyancy melt
  • 1 (a) and 2 (a) show a BSE image
  • FIGS. 1 (b) and 2 (b) show a Gd distribution.
  • the supersaturated Gd compounds are distributed relatively homogeneously in the upper and lower portions of the ingot.
  • Gd-duplex stainless steel shows the results of area mapping with EDX of Gd-duplex stainless steel. Cr, Ni, and Gd are uniformly distributed throughout the mother phase. 4 is a result of analyzing the components of the precipitate by EDX.
  • Supersaturated Gd is a precipitate, such as gadolium oxide (Gd 2 O 3 ), present in grains and at grain boundaries.
  • the raw material is prepared by dissolving in a melting furnace of inert atmosphere using pure iron, pure metal, iron alloy having a composition as shown in Table 1. (Standard composition range of alloy)
  • the steel constituting the neutron-absorbing material is in weight percent, including at least one of gadolium (Gd): 0.1 to 2.5% and boron (B): 0.3 to 0.8%, and molybdenum.
  • Gd gadolium
  • B boron
  • Mo molybdenum
  • Mo 4.0% or less (including 0%)
  • Cr chromium
  • one or more of 10 times or less of vanadium (V): carbon (C) content and 10 times or less of niobium (Nb): carbon (C) content is further added. It may include.
  • nickel (Ni): 0.4-8.0%, silicon (Si): 0.8% or less (except 0%), manganese (Mn): 1.2% or less (except 0%), phosphorus (P): 0.08% or less ( 0%), sulfur (S): 0.08% or less (including 0%) may be further included.
  • a neutron absorbing material having a composition as shown in Table 1 above is an example, and an equivalent index (PREN) value defined as follows satisfies 30 or more.
  • the solubility of boron (B) to iron (Fe) is increased by adding so that the atomic ratio of niobium (Nb) and carbon (C) is 1: 0.8 to 1: 1.2.
  • a small amount of titanium (Ti) may be added, but in this case, the atomic ratio of titanium (Ti) and carbon (C) is 1: 0.8 to 1: 1.2.
  • the solubility of boron (B) during casting reaches 0.5% by weight, but after cooling, there is a problem of lowering to 0.05% by weight for reasons such as oxidation.
  • chromium (Cr), molybdenum (Mo), and vanadium (V) having a larger lattice constant than iron (Fe) are added during melting in the form of oxide or pure metal.
  • Boron (B) and gadolium (Gd) may be initially used as raw materials in the form of borides (eg FeB, FeB 2 , CrB, CrB 2 ), and gadolium oxide (Gd 2 O 3 ).
  • nanoparticles (100 nm or less (except 0 nm)) are added at a ratio of below their melting temperature in a ratio of these compounds (e.g., Gd 2 B 5 , GdB 2 , GdB). 4 , GdB 6 , GdB 12 , GdB 66 ) can be manufactured and used.
  • alloying elements Cr, Ni, Mo, Si, N, etc.
  • alloying elements are appropriately blended based on Table 1 above.
  • buoyant melting using electromagnetic force may be applied to prevent the inflow of impurities through the ceramic crucible.
  • High frequency may be applied for uniform mixing of alloying elements during dissolution.
  • the solution is quenched by solution treatment around the ferrite decomposition temperature in the cooling stage after casting.
  • solution treatment can be performed in any alloy system in which a single-phase solid solution region exists on the state diagram, and can perform solution treatment of carbon strength.
  • the solution treatment temperature refers to an operation of heating to an austenite region in an iron-carbon state diagram.
  • FIG. An example of the solution treatment condition of this invention is shown in FIG. According to this, the temperature was raised at a constant rate during the initial 80 minutes, and then maintained at 1070 ° C. for 50 minutes, followed by rapid water quenching.
  • the neutron absorbing material manufactured by the melt casting method is capable of mass production and economical, the disadvantage is that various phases are generated during solidification due to high melting temperature and various alloying elements, and that boron and gadolium are oxidized and difficult to control. There are disadvantages, and in particular, it is difficult to accurately control the amount of gadolium and boron in the final product.
  • the present invention sought to improve the powder metallurgy method.
  • the steel constituting the neutron absorbing material is by weight, and includes at least one of gadolium (Gd): 0.1 to 2.5% and boron (B): 0.3 to 0.8%.
  • one or more of 10 times or less of vanadium (V): carbon (C) content and 10 times or less of niobium (Nb): carbon (C) content is further added. It may include.
  • nickel (Ni): 0.4-8.0%, silicon (Si): 0.8% or less (except 0%), manganese (Mn): 1.2% or less (except 0%), phosphorus (P): 0.08% or less ( 0%), sulfur (S): 0.08% or less (including 0%) may be further included.
  • a neutron absorbing material having a composition as shown in Table 2 is an example, and an equivalent index (PREN) value defined as follows satisfies 30 or more.
  • the compound of gadolium (Gd) and boron (B) added to the neutron absorbing material is a compound of porous boride boride (Bd) by burning synthesis by heating the gadolium (Gd) and boron (B) in an inert atmosphere at 2500 ° C. or more ( Example: Gd 2 B 5 , GdB 2 , GdB 4 , GdB 6 , GdB 12 , GdB 66 ), and the porous boride is mechanically pulverized to obtain a nano-sized powdery porous boride.
  • the raw material is a porous boride which is a compound of gadolium (Gd) and boron (B) of pure iron, pure metal, nano-sized (100 nm or less (excluding 0 nm)) in a powder state of micro size with the composition shown in Table 2 above.
  • Blend powder of thorium eg Gd 2 B 5 , GdB 2 , GdB 4 , GdB 6 , GdB 12 , GdB 66 ).
  • porous gadolium boride eg Gd 2 B 5 , GdB 2 , GdB 4 , GdB
  • Gd porous gadolium boride
  • Gd a compound of raw metal and nanoscale (less than 100 nm but less than 0 nm) of gadolium (Gd) and boron (B) 6 , GdB 12 , GdB 66 ) by the mechanical alloying (mechanical alloying) to prepare a master alloy powder in which the presence of nano-sized gallium boride in the base material.
  • the master alloy powder in which the nano-sized gadolium boride is present is molded under pressure at a pressure of 100-600 MPa.
  • the microstructures are characterized by the presence of gadolium (Gd), gadolium oxide (Gd 2 O 3 ), boron (B) and boron compounds (e.g. FeB, FeB 2 , CrB, A complex structure in which CrB 2 ) is finely precipitated or distributed in a second phase, or in an austenitic-ferritic composite stainless alloy, gadolium (Gd), gadolium oxide (Gd 2 O 3 ), boron (B), and boron Compound boron (eg FeB, FeB 2 , CrB, CrB 2 ) is a complex structure in which a fine precipitate or second phase is distributed, and at the same time, a compound of gadolium (Gd) and boron (B) Gd 2 B 5 , GdB 2 , GdB 4 , GdB 6 , GdB 12 , and GdB 66 ) are composite tissues that exist in nanoscale (less than 100 nm (excluding 0
  • austenite-ferritic composite stainless alloys include gadolium boride, which is a compound of gadolium (Gd) and boron (B) (e.g., Gd 2 B 5 , GdB 2 , GdB 4 , GdB 6 , GdB 12 , GdB 66 ) are made of composite tissue with nanoscale ( ⁇ 100nm (excluding 0nm)).
  • Gd gadolium
  • B boron
  • the improved machinability is achieved by having a superstructure of boron supersaturated and nanoscale fine boron compounds, or a microstructure of supersaturated superoxide and nanosize microgadal compounds.
  • the steel of the austenitic-ferrite composite structure has a high strength and high corrosion resistance compared to the steel of the austenitic single phase structure.
  • the strength can be varied according to manufacturing conditions such as work hardening and annealing heat treatment, and cast steel shows the following ranges. It has a yield strength of about 2.2 times that of commercial single phase austenitic steel and about 2 times better corrosion resistance. Moreover, its yield strength and corrosion resistance are similar to those of commercial austenitic-ferrite two phase tissue steel, but it is strengthened by using precipitation hardening and foreign material dispersion strengthening. Is improved by more than 20%.
  • Gd gadolium
  • B boron
  • austenite-ferritic composite stainless alloys may contain a mixture of gadolium (Gd) and boron (B), which is a compound of boride (e.g., Gd 2 B 5 , GdB 2 , GdB 4 , GdB 6 , GdB 12 , GdB 66 ) are nano-sized (100 nm or less (except 0 nm)) and are mostly dissolved in doped boride and relatively low in oxides (eg Gd 2 O 3 , B 2 O 5 ) Compared with the material produced by the casting method, the shielding efficiency per unit volume is high.
  • Gd gadolium
  • B boron
  • W and Mo may be present at appropriate ratios to improve the structure control and weldability of the heat affected zone after welding.

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Abstract

L'invention concerne un matériau absorbant les neutrons et son procédé de préparation. Le matériau absorbant les neutrons est un acier comprenant 0,1 à 2,5 % en poids de Gd et/ou 0,3 à 0,8 % en poids de B, et comprenant en outre 4,0 % en poids ou moins de Mo (y compris 0 % en poids), 6,5 % en poids ou moins de W (y compris 0 % en poids), 0,4 % en poids ou moins de N (y compris 0 % en poids), 16 à 34 % en poids de Cr, 0,1 % en poids ou moins de C (y compris 0 % en poids), et Fe, et deux phases d'austénite et de ferrite sont mélangées dans la microstructure de l'acier et une valeur d'indice équivalente du matériau absorbant les neutrons (PREN = Cr + 3,3(Mo + 0,5W) + 30N) atteint 30 ou plus. Le matériau absorbant les neutrons selon la présente invention a une résistance mécanique, une résistance à la corrosion et une faculté de mise en œuvre excellentes.
PCT/KR2013/006810 2012-07-30 2013-07-30 Matériau absorbant les neutrons et son procédé de préparation WO2014021600A1 (fr)

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CN113798487A (zh) * 2021-08-27 2021-12-17 四川大学 一种新型Fe基球形屏蔽合金粉末及其制备方法
CN115491530A (zh) * 2022-10-18 2022-12-20 西安工业大学 一种含钆不锈钢中子吸收复合板及其制备方法
CN117512474A (zh) * 2023-10-24 2024-02-06 四川大学 一种结构/功能一体化核辐射防护用Fe基屏蔽合金及其制备方法

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CN113798487A (zh) * 2021-08-27 2021-12-17 四川大学 一种新型Fe基球形屏蔽合金粉末及其制备方法
CN113798487B (zh) * 2021-08-27 2022-07-08 四川大学 一种Fe基球形屏蔽合金粉末及其制备方法
CN115491530A (zh) * 2022-10-18 2022-12-20 西安工业大学 一种含钆不锈钢中子吸收复合板及其制备方法
CN115491530B (zh) * 2022-10-18 2023-05-16 西安工业大学 一种含钆不锈钢中子吸收复合板及其制备方法
CN117512474A (zh) * 2023-10-24 2024-02-06 四川大学 一种结构/功能一体化核辐射防护用Fe基屏蔽合金及其制备方法
CN117512474B (zh) * 2023-10-24 2024-05-07 四川大学 一种结构/功能一体化核辐射防护用Fe基屏蔽合金及其制备方法

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