CN105112727A - Fused salt corrosion resistant nickel-based deformable high-temperature alloy and preparation method thereof - Google Patents
Fused salt corrosion resistant nickel-based deformable high-temperature alloy and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a fused salt corrosion resistant nickel-based deformable high-temperature alloy which comprises the following chemical components in percentage by weight: 5.0-8.0% of Cr, 15.0-28.0% of W, 0.5-0.55% of Fe, 0.5-0.8% of Mn, 0.1-0.3% of Si, 0.05-0.06% of C, 0-1.0% of Mo, 0-0.2% of Ti and the balance of Ni. The invention further provides a preparation method for the fused salt corrosion resistant nickel-based deformable high-temperature alloy. The fused salt corrosion resistant nickel-based deformable high-temperature alloy has the advantage that the machinable property is excellent, the high-temperature mechanical property and the structure stability are higher, and the tensile strength and the long-term service life are obviously superior to that of Hastelloy N alloy; the alloy is excellent in fused salt corrosion resistance, is suitable for high-temperature structural material of a fused salt nuclear reactor, and is excellent in overall performance at the operating temperature of 800-850 DEG C.
Description
Technical field
The present invention relates to the material being applicable to the component such as molten salt react ion core pressure vessel and heat exchanger, relate more specifically to a kind of ni-base wrought superalloy of resistance to fused salt corrosion and preparation method thereof.
Background technology
Along with the surge of China's energy demand, the energy gap problem faced will be more and more serious, totally, safety, high efficiency advanced nuclear energy is the best method solving China energy problem, greatly develops the important directions that nuclear energy is also following China Energy restructuring and optimization.This century, forth generation nuclear reactor was all greatly developed in countries in the world.Wherein, molten salt reactor (MSR) is liquid fuel reactor unique in forth generation reactor, has the incomparable advantage of other reactors, be subject to the favor of countries in the world in inherent safety, economy, nuclear resource Sustainable development and in preventing nuclear proliferation etc.And as preparing the structured material of molten salt react ion core pressure vessel and heat exchanger, require steady operation under the extreme conditions such as high temperature, high pressure, high radiation, high corrosion for a long time, be one of key issue of restriction molten salt reactor (MSR) development.
When to fluoridize fused salt as the refrigerant of reactor, heap temperature out reaches 700 DEG C, greatly improves the working efficiency of reactor.In the sixties in 20th century, for meeting thorium base molten salt reactor (MSR) demand, U.S.'s Oak Ridge National Laboratory have developed HastelloyN alloy.This alloy has that intensity is high, plasticity and toughness good and processability is good, for neutron radiation, there is good suffertibility, its hot strength is better than ferrous alloy, and in the fluorochemical of melting, corrosion resistance is strong, is successfully applied to the positions such as reactor pot, return, pump for liquid salts, interchanger.But the highest allowable temperature of HastelloyN alloy is 704 DEG C, and in recent years, along with the variation of energy demand, people wish to realize the high-level efficiency Energy conversion such as high temperature for hydrogen production, and this needs MSR to operate in more than 800 DEG C.HastelloyN alloy can not meet the demands, and is badly in need of research and development molten salt reactor (MSR) with holding the higher structured material of warm ability.
Summary of the invention
In order to solve the problem cannot born higher than the fused salt corrosion of 704 DEG C that above-mentioned prior art exists, the present invention aims to provide a kind of ni-base wrought superalloy of resistance to fused salt corrosion and preparation method thereof.
The invention provides a kind of ni-base wrought superalloy of resistance to fused salt corrosion, it is characterized in that, by weight percentage, its chemical composition is: the Cr of 5.0-8.0%, the W of 15.0-28.0%, the Si of the Mn of the Fe of 0.5-0.55%, 0.5-0.8%, 0.1-0.3%, the C of 0.05-0.06%, the Ti of the Mo of 0-1.0%, 0-0.2%, and the Ni of surplus.The ni-base wrought superalloy of resistance to fused salt corrosion provided by the invention, has excellent mechanical behavior under high temperature and structure stability, simultaneously high temperature resistant melt brine corrosion, and resistance to oxidation and radioresistance injury reinforcing, meet the service requirements of molten salt reactor (MSR) to structured material.
The chemical composition of this ni-base wrought superalloy of resistance to fused salt corrosion is preferably: the Fe of the W of the Cr of 6.0-7.0%, 26.0-28.0%, 0.5-0.55%, the C of the Si of the Mn of 0.5-0.8%, 0.1-0.3%, 0.05-0.06%, the Ti of the Mo of 0-1.0%, 0-0.2%, and the Ni of surplus.
The chemical composition of this ni-base wrought superalloy of resistance to fused salt corrosion is preferably: the Cr of 6.0%, the W of 26%, the Fe of 0.5%, the Mn of 0.8%, the Si of 0.1%, the C of 0.05%, the Mo of 1.0%, the Ti of 0.2%, and the Ni of surplus.
This ni-base wrought superalloy of resistance to fused salt corrosion is not containing Al.
This ni-base wrought superalloy of resistance to fused salt corrosion is not containing Co.
This ni-base wrought superalloy of resistance to fused salt corrosion is not containing Cu.
The present invention also provides a kind of preparation method of the above-mentioned ni-base wrought superalloy of resistance to fused salt corrosion, comprises step: S1, adopts vacuum induction furnace casting mother alloy; S2, Homogenization Treatments; And S3, hot-work.
The treatment temp of step S2 is between 1200 DEG C-1300 DEG C.
The treatment time of step S2 is between 15 hours-25 hours.
The processing temperature of step S3 is between 900 DEG C-1200 DEG C.
The hot-work of step S3 is forging, hot rolling or hot extrusion.
By the specific rational proportion of each alloying element, the present invention ensure that alloy obtains good over-all properties.With existing alloy phase ratio, the advantage that the ni-base wrought superalloy of resistance to fused salt corrosion of the present invention has comprises: excellent processability; Higher mechanical behavior under high temperature and structure stability, its tensile strength and creep rupture life will obviously be better than HastelloyN alloy; There is excellent anti-fused salt corrosion performance, be applicable to the high-temperature structural material of fused salt nuclear reactor, under 800-850 DEG C of working temperature, show excellent over-all properties.
Accompanying drawing explanation
Fig. 1 a is the pattern schematic diagram of the as cast condition macrostructure of the ni-base wrought superalloy of resistance to fused salt corrosion according to embodiments of the invention 1;
Fig. 1 b is the pattern schematic diagram of the as cast condition mirco structure of the ni-base wrought superalloy of resistance to fused salt corrosion according to embodiments of the invention 1;
Fig. 1 c is the pattern schematic diagram of the forging state macrostructure of the ni-base wrought superalloy of resistance to fused salt corrosion according to embodiments of the invention 1;
Fig. 2 a is the Cross Section Morphology schematic diagram of the ni-base wrought superalloy of resistance to fused salt corrosion after 800 DEG C/400h fused salt corrosion according to embodiments of the invention 1;
Fig. 2 b is the cross section Cr distribution diagram of element of the ni-base wrought superalloy of resistance to fused salt corrosion after 800 DEG C/400h fused salt corrosion according to embodiments of the invention 1;
Fig. 2 c is the Cross Section Morphology schematic diagram of comparative alloy (HastelloyN) after 800 DEG C/400h fused salt corrosion;
Fig. 2 d is the cross section Cr distribution diagram of element of comparative alloy (HastelloyN) after 800 DEG C/400h fused salt corrosion;
Fig. 3 a is the Cross Section Morphology schematic diagram of the ni-base wrought superalloy of resistance to fused salt corrosion after 850 DEG C/400h fused salt corrosion according to embodiments of the invention 1;
Fig. 3 b is the cross section Cr distribution diagram of element of the ni-base wrought superalloy of resistance to fused salt corrosion after 850 DEG C/400h fused salt corrosion according to embodiments of the invention 1;
Fig. 3 c is the Cross Section Morphology schematic diagram of comparative alloy (HastelloyN) after 850 DEG C/400h fused salt corrosion; And
Fig. 3 d is the cross section Cr distribution diagram of element of comparative alloy (HastelloyN) after 850 DEG C/400h fused salt corrosion.
Embodiment
The % below occurred, unless stated otherwise, is all weight percentage.
The ni-base wrought superalloy of resistance to fused salt corrosion of the present invention is provided according to following preparation method:
S1, adopts vacuum induction furnace casting mother alloy;
S2, Homogenization Treatments; And
S3, hot-work.
With preparation method's difference of existing alloy be: containing Cr, W, Fe, Mn, Si, C, Ni in the mother alloy in above-mentioned steps S1, also can also have Mo, Ti, not containing Al, Co, Cu.The temperature of above-mentioned steps S2 is between 1200 DEG C-1300 DEG C, and the treatment time is between 15 hours-25 hours.The temperature of above-mentioned steps S3 is between 900 DEG C-1200 DEG C, and hot-work is forging, hot rolling or hot extrusion.
Particularly, mother alloy is preferably with the content of each alloying element in the final ni-base wrought superalloy of resistance to fused salt corrosion formed:
The content of Cr controls between 5.0-8.0%, preferably controls, between 6.0-7.0%, most preferably to be 6.0%.Cr within the scope of this is the key element effectively improving the corrosion resistance nature in oxidizing corrosion medium.If the content of Cr is too large, Cr element may be caused to diffuse in large quantities in fused salt.In addition, if the content of Cr is too large, it can form excessive carbide with C simultaneously, falls low-alloyed structure stability.
The content of W controls between 15.0-28.0%, preferably between 26.0-28.0%, most preferably is 26.0%.W within the scope of this, as strong solution strengthening element, mainly plays the effect of strengthening γ matrix; Meanwhile, W rate of diffusion is in the alloy lower, can put forward heavy alloyed creep strength; In addition, the rate of diffusion of W is only about 1/10 of Mo, and the stability of the fluoride salt of W will be worse than the fluoride salt of other strengthening elements such as Mo, Fe, therefore the corrosion of the more resistance to fluoride salt of W.
The content of Fe controls, between 0.5-0.55%, to be particularly preferably 0.5%.Fe within the scope of this dissolves in nickel as a kind of matrix element, can improve the consistency of other elements and matrix.
The content of Mn controls, between 0.5-0.8%, to be particularly preferably 0.8%; The content of Si controls, between 0.1-0.3%, to be particularly preferably 0.1%; The content of C controls, between 0.05-0.06%, to be particularly preferably 0.05%.Mn, Si and C tend to segregation at grain boundaries, play the effect of strengthening crystal boundary; C partly can also form carbide simultaneously, is distributed in crystal boundary, also can strengthens crystal boundary; And Si can improve grain boundary corrosion resistance energy, the stability of carbide can be improved simultaneously.
The content of Mo controls, between 0-1.0%, to be particularly preferably 1.0%.Mo within the scope of this, as the strong solution strengthening element of one, can significantly improve the creep property of alloy, improves the corrosion resistance nature in reductant simultaneously.If the content of Mo is too large, the antioxidant property of alloy also has disadvantageous effect.
The content of Ti controls, between 0-0.2%, to be particularly preferably 0.2%.Ti within the scope of this, as a kind of carbon stablizer, can improve intergranular corrosion resistance nature.
Al is γ ' phase forming element, is easy to separate out tiny γ ' precipitated phase in heat treatment process.But because γ ' precipitated phase can be grown up inefficacy for a long time under the high temperature conditions, alloy performance is unfavorable, therefore should not add Al element in alloy.Although it should be noted that Ti is also a kind of γ ' phase forming element, be added in alloy due to its carbon stability.
Co, as solution strengthening element, can significantly improve creep strength and the plasticity of alloy.But because this Alloyapplication is in the contour neutron irradiation environment of nuclear reactor main vessel, Co can become 60Co, the radioactive substance long half-lift of a kind of by after neutron irradiation, releases gamma-rays, Co element long-term harm produced to environment, so can not add in the alloy.
Cu is as solution strengthening element, and its solid solution strengthening effect is poor, so do not add in the alloy.If add this Cu element, alloying element kind will be increased, fall low-alloyed structure stability.
Provide 5 embodiments in above-mentioned scope below to be described in detail the ni-base wrought superalloy of resistance to fused salt corrosion provided by the invention further.The chemical composition of the ni-base wrought superalloy of resistance to fused salt corrosion of each embodiment sees table 1.In order to contrast conveniently, in table 1, also list the chemical composition of comparative alloy HastelloyN.
The chemical composition (wt.%) of table 1 embodiment and comparative alloy HastelloyN
For the ni-base wrought superalloy of resistance to fused salt corrosion that embodiment 1 obtains, Fig. 1 a-Fig. 1 c gives its corresponding pattern schematic diagram, wherein, Fig. 1 a and Fig. 1 b represents at the as-cast structure pattern of 1250 DEG C of Homogenization Treatments after 20 hours, can find that the granular carbide in cast alloy is distributed in matrix uniformly; The tissue topography of bar after ingot casting after Fig. 1 c represents Homogenization Treatments forges at the temperature of 1100 DEG C, can find that tiny carbide even dispersion is in the matrix of alloy, alloy structure keeps good homogeneity.
Provide alloy and the comparative alloy HastelloyN alloy tensile property data under several conditions of embodiments of the invention 1 below, see table 2.
(strain rate is 3 × 10 for table 2 alloy of the present invention (embodiment 1) and comparative alloy HastelloyN tensile strength data under several conditions
-4s
-1)
It can thus be appreciated that the yield strength under the uniform temp of embodiment 1 alloy and tensile strength are all higher than HastelloyN alloy, and the yield strength 238MPa of embodiment 1 alloy at 850 DEG C, higher than the 220MPa of HastelloyN alloy at 700 DEG C.Yield strength is an important parameter of reactor design, and only from the viewpoint of yield strength, this alloy 700 DEG C of being expected to the use temperature of MSR to provide from HastelloyN bring up to 850 DEG C.
Provide the tensile property data of alloy under room temperature to high temperature of embodiments of the invention 2-embodiment 5 below, see table 3.
To high temperature tensile properties, (strain rate is 3 × 10 to the room temperature of table 3 alloy of the present invention (embodiment 2-embodiment 4)
-4s
-1)
It can thus be appreciated that the tensile strength of alloy of the present invention increases along with the increase of W content, when W content is more than 15%, its yield strength at 850 DEG C and tensile strength have been better than HastelloyN alloy.
Provide the alloy of embodiments of the invention 1 and embodiment 5 and the enduring quality data of comparative alloy HastelloyN alloy below, see table 4.
The enduring quality of table 4 alloy of the present invention (embodiment 1 and embodiment 5) and comparative alloy HastelloyN
It can thus be appreciated that the creep rupture life of alloy of the present invention, under 816 DEG C of temperature condition, the creep rupture life of embodiment 1 alloy was more than the twice of HastelloyN alloy higher than comparative alloy HastelloyN; Under 700 DEG C of temperature condition, the creep rupture life of embodiment 5 is more than 4 times of HastelloyN alloy, also suitable with HastelloyN at 816 DEG C.
In fact, the selection of content of element W is a maximum bright spot of the present invention.Comprehensive tensile and enduring quality, in alloy of the present invention, the most preferred content of W element is 26-28%.
The static fused salt corrosion experimental temperature of the alloy of the embodiment of the present invention 1 and comparative alloy (HastelloyN alloy) is 800 DEG C and 850 DEG C, etching time 400h.Concrete etching condition is as follows:
1, plumbago crucible (its detail parameters is in table 5): plumbago crucible inwall and component (peg, lid, bolt and nut) are in ethanol after ultrasonic cleaning, at 700 DEG C of vacuum-drying 24h, after being cooled to room temperature, for subsequent use in fast transfer to glove box.
Table 5 plumbago crucible parameter
2, fused salt prepares: fused salt is ingot casting shape FLiNaK (46.5-11.5-42mol%), and foreign matter content is: acid ion (SO
4 2-+ PO
4 3-+ NO
3 -) be less than 20ppm; Total oxygen content (comprising acid group, oxide compound and water) is less than 200ppm; Metal ion is about 100ppm.Be positioned in glove box.
3, preparation of samples: often kind of alloy prepares 3 parallel samples, and alloy sample is polished to 1200# step by step, oil removing, dewater, cold wind dries up, having marked, is that the scales/electronic balance weighing of 0.01mg is for subsequent use by precision.
4, etching condition corrosion temperature: 800 DEG C and 850 DEG C, etching time: 400 hours.
Weightlessness after the corrosion of material is generally as the index passing judgment on material corrosion performance, and consider that the density of W in alloy of the present invention (embodiment 1) is comparatively large, the weightlessness of unit mol is greater than the Mo in comparative alloy (HastelloyN alloy).Therefore only with weightless be inappropriate as the resistance to fused salt corrosion performance judged between the alloy that component difference is larger.The loss being Cr element in alloy due to the dominant failure main manifestations of alloy in fused salt enters fused salt, therefore adopt the thickness of alloy surface poor Cr layer after fused salt corrosion as the criterion characterizing the resistance to fused salt corrosion performance of alloy, the poor Cr layer thickness of alloy is more shallow, and the corrosion resistance nature of alloy is better.Fig. 2 and Fig. 3 is respectively the cross section Cr distribution diagram of element that the Cross Section Morphology after two kinds of alloy corrosions of 800 DEG C and 850 DEG C and electronic probe characterize.Can find that the poor Cr layer of alloy of the present invention (embodiment 1) is less than the poor Cr layer thickness of comparative alloy (HastelloyN alloy).At 800 DEG C, the poor Cr layer thickness of alloy of the present invention (embodiment 1) is about 10 μm, and comparative alloy (HastelloyN alloy) is about 15 μm; At 850 DEG C, the poor Cr layer thickness of two kinds of alloys is about 25 μm.Prove under 800-850 DEG C of fused salt environment, the resistance to fused salt corrosion performance of alloy of the present invention is better than HastelloyN alloy.In the HastelloyN alloy product Performance Manual of Haynes company, clearly mention HastelloyN alloy can be on active service in 704 DEG C to 871 DEG C high-temperature molten salt environment, illustrates that alloy of the present invention also should have good resistance to fused salt corrosion performance under 800-850 DEG C of high temperature thus.
Above-described, be only preferred embodiment of the present invention, and be not used to limit scope of the present invention, the above embodiment of the present invention can also make a variety of changes.Namely every claims according to the present patent application and description are done simple, equivalence change and modify, and all fall into the claims of patent of the present invention.The not detailed description of the present invention be routine techniques content.
Claims (11)
1. the ni-base wrought superalloy of resistance to fused salt corrosion, it is characterized in that, by weight percentage, its chemical composition is: the Cr of 5.0-8.0%, the W of 15.0-28.0%, the Si of the Mn of the Fe of 0.5-0.55%, 0.5-0.8%, 0.1-0.3%, the C of 0.05-0.06%, the Ti of the Mo of 0-1.0%, 0-0.2%, and the Ni of surplus.
2. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, it is characterized in that, its chemical composition is: the Fe of the W of the Cr of 6.0-7.0%, 26.0-28.0%, 0.5-0.55%, the Mn of 0.5-0.8%, the Mo of the C of the Si of 0.1-0.3%, 0.05-0.06%, 0-1.0%, the Ti of 0-0.2%, and the Ni of surplus.
3. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 2, is characterized in that, its chemical composition is: the Cr of 6.0%, the W of 26%, the Fe of 0.5%, the Mn of 0.8%, the Si of 0.1%, the C of 0.05%, the Mo of 1.0%, the Ti of 0.2%, and the Ni of surplus.
4. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, is characterized in that, this ni-base wrought superalloy of resistance to fused salt corrosion is not containing Al.
5. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, is characterized in that, this ni-base wrought superalloy of resistance to fused salt corrosion is not containing Co.
6. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, is characterized in that, this ni-base wrought superalloy of resistance to fused salt corrosion is not containing Cu.
7. a preparation method for the ni-base wrought superalloy of resistance to fused salt corrosion according to any one of claim 1-6, is characterized in that, comprises step: S1, adopts vacuum induction furnace casting mother alloy; S2, Homogenization Treatments; And S3, hot-work.
8. preparation method according to claim 7, is characterized in that, the treatment temp of step S2 is between 1200 DEG C-1300 DEG C.
9. preparation method according to claim 7, is characterized in that, the treatment time of step S2 is between 15 hours-25 hours.
10. preparation method according to claim 7, is characterized in that, the processing temperature of step S3 is between 900 DEG C-1200 DEG C.
11. preparation methods according to claim 7, is characterized in that, the hot-work of step S3 is forging, hot rolling or hot extrusion.
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Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106077997A (en) * | 2016-07-15 | 2016-11-09 | 中国科学院上海应用物理研究所 | A kind of solder for anti-fused salt corrosion nickel base superalloy melting |
| CN106181131A (en) * | 2016-07-15 | 2016-12-07 | 中国科学院上海应用物理研究所 | Solid core welding wire preparation method for the welding of anti-fused salt corrosion nickel base superalloy |
| CN109055879A (en) * | 2018-09-14 | 2018-12-21 | 中国科学院上海应用物理研究所 | A method of improving the anti-tellurium corrosive nature of UNS N10003 alloy |
| CN110273085A (en) * | 2019-04-15 | 2019-09-24 | 上海大学 | Reactor spentnuclear fuel storing rich gadolinium nickel-bass alloy material and preparation method thereof |
| CN110373573A (en) * | 2019-08-13 | 2019-10-25 | 上海大学 | Nuclear screening rich gadolinium nickel tungsten alloy material and preparation method thereof |
| CN112322939A (en) * | 2020-11-04 | 2021-02-05 | 中国科学院上海应用物理研究所 | Nickel-based high-temperature alloy and preparation method thereof |
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| CN115595470A (en) * | 2022-10-26 | 2023-01-13 | 西安稀有金属材料研究院有限公司（Cn） | Molten salt corrosion resistant nickel-based alloy for spent fuel aftertreatment and preparation method thereof |
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| CN115786771A (en) * | 2021-09-09 | 2023-03-14 | 中国科学院上海应用物理研究所 | High-strength corrosion-resistant deformation-resistant high-temperature alloy for molten salt reactor and preparation method thereof |
| CN116179896A (en) * | 2023-01-16 | 2023-05-30 | 散裂中子源科学中心 | High-strength high-plasticity corrosion-resistant nickel-based alloy and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1591548A1 (en) * | 2004-04-27 | 2005-11-02 | Daido Steel Co., Ltd. | Method for producing of a low thermal expansion Ni-base superalloy |
| EP1867740A1 (en) * | 2006-06-13 | 2007-12-19 | Daido Tokushuko Kabushiki Kaisha | Low thermal expansion Ni-base superalloy |
| JP2011125874A (en) * | 2009-12-15 | 2011-06-30 | Daido Steel Co Ltd | Method of producing welding wire |
| CN103882266A (en) * | 2014-03-26 | 2014-06-25 | 中国科学院上海应用物理研究所 | Nickel-based alloy for fused salt reactor and preparation method of nickel-based alloy |
| CN104791017A (en) * | 2011-03-30 | 2015-07-22 | 三菱重工业株式会社 | High intermediate pressure turbine |
-
2015
- 2015-09-23 CN CN201510612608.4A patent/CN105112727B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1591548A1 (en) * | 2004-04-27 | 2005-11-02 | Daido Steel Co., Ltd. | Method for producing of a low thermal expansion Ni-base superalloy |
| EP1867740A1 (en) * | 2006-06-13 | 2007-12-19 | Daido Tokushuko Kabushiki Kaisha | Low thermal expansion Ni-base superalloy |
| JP2011125874A (en) * | 2009-12-15 | 2011-06-30 | Daido Steel Co Ltd | Method of producing welding wire |
| CN104791017A (en) * | 2011-03-30 | 2015-07-22 | 三菱重工业株式会社 | High intermediate pressure turbine |
| CN103882266A (en) * | 2014-03-26 | 2014-06-25 | 中国科学院上海应用物理研究所 | Nickel-based alloy for fused salt reactor and preparation method of nickel-based alloy |
Non-Patent Citations (2)
| Title |
|---|
| VICTOR IGNATIEV等: "Intergranular tellurium cracking of nickel-based alloys in molten Li，Be，Th，U/F salt mixture", 《JOURNAL OF NUCLEAR MATERIALS》 * |
| 马国印等: "镍和镍合金耐腐蚀性分析", 《化工装备技术》 * |
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| CN114457261A (en) * | 2020-11-10 | 2022-05-10 | 中国科学院上海应用物理研究所 | Corrosion-resistant nickel-based wrought superalloy for molten salt reactor and preparation method thereof |
| CN115786771A (en) * | 2021-09-09 | 2023-03-14 | 中国科学院上海应用物理研究所 | High-strength corrosion-resistant deformation-resistant high-temperature alloy for molten salt reactor and preparation method thereof |
| CN115747536A (en) * | 2022-10-11 | 2023-03-07 | 散裂中子源科学中心 | Vanadium-nickel alloy for neutron scattering experiments and preparation method and application thereof |
| CN115595470A (en) * | 2022-10-26 | 2023-01-13 | 西安稀有金属材料研究院有限公司（Cn） | Molten salt corrosion resistant nickel-based alloy for spent fuel aftertreatment and preparation method thereof |
| CN115595470B (en) * | 2022-10-26 | 2023-09-12 | 西安稀有金属材料研究院有限公司 | Molten salt corrosion resistant nickel-based alloy for spent fuel aftertreatment and preparation method thereof |
| CN116179896A (en) * | 2023-01-16 | 2023-05-30 | 散裂中子源科学中心 | High-strength high-plasticity corrosion-resistant nickel-based alloy and preparation method thereof |
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