CN105112727B - 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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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 70
- 239000000956 alloy Substances 0.000 title claims abstract description 70
- 150000003839 salts Chemical class 0.000 title claims abstract description 69
- 238000005260 corrosion Methods 0.000 title claims abstract description 65
- 230000007797 corrosion Effects 0.000 title claims abstract description 65
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 9
- 239000000126 substance Substances 0.000 claims abstract description 11
- 229910000601 superalloy Inorganic materials 0.000 claims description 33
- 229910052799 carbon Inorganic materials 0.000 claims description 9
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- 238000011282 treatment Methods 0.000 claims description 7
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- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 238000005098 hot rolling Methods 0.000 claims description 3
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- 229910000856 hastalloy Inorganic materials 0.000 abstract description 30
- 229910001199 N alloy Inorganic materials 0.000 abstract description 17
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- 229910000967 As alloy Inorganic materials 0.000 description 1
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
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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 it is applied to the material of the parts such as fusedsalt reactor pressure vessel and heat exchanger, more specifically
It is related to a kind of ni-base wrought superalloy of resistance to fused salt corrosion and preparation method thereof.
Background technology
With the surge of China's energy demand, the energy gap problem for facing will be increasingly severe, clean, safety, height
The advanced nuclear energy of efficiency is the best method for solving energy problem of China, and it is also that following China's energy resource structure is adjusted to greatly develop nuclear energy
The important directions of whole and optimization.This century, countries in the world all greatly developed forth generation nuclear reactor.Wherein, fusedsalt reactor is
Unique liquid fuel reactor in forth generation reactor, in inherent safety, economy, nuclear resource sustainable development and anti-
Only the aspect such as nuclear proliferation has the advantages that other reactors are incomparable, is favored by countries in the world.And conduct prepares fused salt
The structural material of reactor pressure vessel and heat exchanger, it is desirable to long-term in extreme bars such as high temperature, high pressure, high radiation, high corrosions
Steady operation under part, is to restrict one of key issue of fusedsalt reactor development.
When the coolant using fluorination fused salt as reactor, heap outlet temperature reaches 700 DEG C, is greatly enhanced reactor
Work efficiency.In the sixties in 20th century, it is to meet thorio fusedsalt reactor demand, U.S.'s Oak Ridge National Laboratory have developed
Hastelloy N alloys.The alloy has that intensity is high, plasticity and toughness are good and processability is good, for neutron irradiation with compared with
Good suffertibility, its elevated temperature strength are better than ferrous alloy, and corrosion resistance is strong in the fluoride of melting, successfully should
For positions such as reactor vessel, return, pump for liquid salts, heat exchangers.But the highest allowable temperature of Hastelloy N alloys
For 704 DEG C, and in recent years, with the variation of energy demand, it is desirable to achieve the high efficiency energy conversion such as high temperature for hydrogen production, this
MSR is needed to operate in more than 800 DEG C.Hastelloy N alloys can not meet requirement, be badly in need of research and development fusedsalt reactor
With the higher structural material of temperature capability.
The content of the invention
In order to solve the problems, such as the fused salt corrosion that cannot withstand greater than 704 DEG C of above-mentioned prior art presence, purport of the present invention
A kind of ni-base wrought superalloy of resistance to fused salt corrosion and preparation method thereof is being provided.
The present invention provides a kind of ni-base wrought superalloy of resistance to fused salt corrosion, it is characterised in that by weight percentage, its
Chemical composition is：The Mn of the Fe of the W of the Cr of 5.0-8.0%, 15.0-28.0%, 0.5-0.55%, 0.5-0.8%, 0.1-
The Ti of the Mo of the C of 0.3% Si, 0.05-0.06%, 0-1.0%, 0-0.2%, and the Ni of surplus.It is resistance to that the present invention is provided
Fused salt corrosion ni-base wrought superalloy, with excellent mechanical behavior under high temperature and structure stability, while high temperature resistant molten salt is rotten
Erosion, resistance to oxidation and radioresistance injury reinforcing, meet use requirement of the fusedsalt reactor to structural material.
The chemical composition of the ni-base wrought superalloy of resistance to fused salt corrosion is preferably：The Cr of 6.0-7.0%, 26.0-
The C of the Si of the Mn of the Fe of 28.0% W, 0.5-0.55%, 0.5-0.8%, 0.1-0.3%, 0.05-0.06%, 0-1.0%'s
The Ti of Mo, 0-0.2%, and the Ni of surplus.
The chemical composition of the ni-base wrought superalloy of resistance to fused salt corrosion is preferably：6.0% Cr, 26% W, 0.5%
Fe, 0.8% Mn, 0.1% Si, 0.05% C, 1.0% Mo, 0.2% Ti, and the Ni of surplus.
The ni-base wrought superalloy of resistance to fused salt corrosion does not contain Al.
The ni-base wrought superalloy of resistance to fused salt corrosion does not contain Co.
The ni-base wrought superalloy of resistance to fused salt corrosion does not contain 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, including step：S1,
Using vaccum sensitive stove casting foundry alloy；S2, Homogenization Treatments；And S3, hot-working.
The treatment temperature of step S2 is between 1200 DEG C -1300 DEG C.
The process time of step S2 is between -25 hours 15 hours.
The processing temperature of step S3 is between 900 DEG C -1200 DEG C.
The hot-working 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 combination property.With it is existing
Alloy is compared, the present invention the ni-base wrought superalloy of resistance to fused salt corrosion have the advantage that including：Excellent processability；Compared with
High mechanical behavior under high temperature and structure stability, its tensile strength and creep rupture life will be substantially better than Hastelloy N alloys；Tool
There is excellent anti-fused salt corrosion performance, it is adaptable to the high-temperature structural material of fused salt nuclear reactor, under 800-850 DEG C of operating temperature
Show excellent combination property.
Description of the drawings
Fig. 1 a are the as cast condition macrostructures of the ni-base wrought superalloy of resistance to fused salt corrosion of embodiments in accordance with the present invention 1
Pattern schematic diagram；
Fig. 1 b are the as cast condition mirco structures of the ni-base wrought superalloy of resistance to fused salt corrosion of embodiments in accordance with the present invention 1
Pattern schematic diagram；
Fig. 1 c are the forging state macrostructures of the ni-base wrought superalloy of resistance to fused salt corrosion of embodiments in accordance with the present invention 1
Pattern schematic diagram；
Fig. 2 a are the ni-base wrought superalloy of the resistance to fused salt corrosion Jing 800 DEG C/400h fused salts of embodiments in accordance with the present invention 1
Cross Section Morphology schematic diagram after corrosion；
Fig. 2 b are the ni-base wrought superalloy of the resistance to fused salt corrosion Jing 800 DEG C/400h fused salts of embodiments in accordance with the present invention 1
Section Cr distribution diagram of element after corrosion；
Fig. 2 c are Cross Section Morphology schematic diagram of the comparative alloy (Hastelloy N) Jing after 800 DEG C/400h fused salt corrosions；
Fig. 2 d are section Cr distribution diagram of element of the comparative alloy (Hastelloy N) Jing after 800 DEG C/400h fused salt corrosions；
Fig. 3 a are the ni-base wrought superalloy of the resistance to fused salt corrosion Jing 850 DEG C/400h fused salts of embodiments in accordance with the present invention 1
Cross Section Morphology schematic diagram after corrosion；
Fig. 3 b are the ni-base wrought superalloy of the resistance to fused salt corrosion Jing 850 DEG C/400h fused salts of embodiments in accordance with the present invention 1
Section Cr distribution diagram of element after corrosion；
Fig. 3 c are Cross Section Morphology schematic diagram of the comparative alloy (Hastelloy N) Jing after 850 DEG C/400h fused salt corrosions；With
And
Fig. 3 d are section Cr distribution diagram of element of the comparative alloy (Hastelloy N) Jing after 850 DEG C/400h fused salt corrosions.
Specific embodiment
The % for appearing below, unless stated otherwise, is 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, using vaccum sensitive stove casting foundry alloy；
S2, Homogenization Treatments；And
S3, hot-working.
With the preparation method of existing alloy except that：Contain Cr, W, Fe in foundry alloy in above-mentioned steps S1,
Mn, Si, C, Ni, can also also have Mo, Ti, not contain Al, Co, Cu.The temperature of above-mentioned steps S2 between 1200 DEG C -1300 DEG C,
Process time is between -25 hours 15 hours.The temperature of above-mentioned steps S3 between 900 DEG C -1200 DEG C, hot-working be forging,
Hot rolling or hot extrusion.
Specifically, each alloying element in foundry alloy and the ni-base wrought superalloy of resistance to fused salt corrosion that ultimately forms contains
Amount is preferably：
The content of Cr is controlled between 5.0-8.0%, is preferably controlled between 6.0-7.0%, most preferably 6.0%.
Cr in the range of being somebody's turn to do is the key element of the decay resistance being effectively improved in oxidizing corrosion medium.If the content of Cr is too
Greatly, it would be possible to cause Cr elements to be diffused in fused salt in large quantities.In addition, if the content of Cr is too big, which simultaneously can be with C-shaped into mistake
Low-alloyed structure stability, drops in the carbide of degree.
The content of W is controlled between 15.0-28.0%, preferably between 26.0-28.0%, and most preferably 26.0%.
W in the range of being somebody's turn to do primarily serves the effect of reinforcing γ matrixes as strong solution strengthening element；Meanwhile, W diffusion speed in the alloy
Rate is relatively low, can put forward heavy alloyed creep strength；In addition, the diffusion rate of W is only the 1/10 or so of Mo, and the fluoride salt of W
Stability less than other intensified elements such as Mo, Fe fluoride salt, therefore W is more resistant to the corrosion of fluoride salt.
The content of Fe is controlled between 0.5-0.55%, and particularly preferably 0.5%.Fe within the range is used as a kind of base
Element of volume is dissolved in nickel, can improve the compatibility of other elements and matrix.
The content of Mn is controlled between 0.5-0.8%, and particularly preferably 0.8%；Si content control 0.1-0.3% it
Between, particularly preferably 0.1%；The content of C is controlled between 0.05-0.06%, and particularly preferably 0.05%.Mn, Si and C incline
Act on to reinforcing crystal boundary in grain boundaries, is played in segregation；C can also partly form carbide simultaneously, be distributed in crystal boundary, can also strengthen crystalline substance
Boundary；And Si can improve grain boundary corrosion resistance energy, while the stability of carbide can be improved.
The content of Mo is controlled between 0-1.0%, and particularly preferably 1.0%.Mo within the range is strong as one kind
Molten intensified element, can significantly improve the croop property of alloy, while improving the decay resistance in reductant.If Mo
Content it is too big, the antioxygenic property of alloy is also adversely affected.
The content of Ti is controlled between 0-0.2%, and particularly preferably 0.2%.Ti within the range is steady as a kind of carbon
Determine agent, it is possible to increase intergranular decay resistance.
Al is γ ' phase formation elements, is easy to separate out tiny γ ' precipitated phases in heat treatment process.But due to γ ' precipitated phases
Long-time can be grown up failure under the high temperature conditions, unfavorable to alloy property, therefore should not add Al elements in alloy.Should note
Meaning, although Ti is also a kind of γ ' phases formation element, but is added in alloy due to its carbon stability.
Co can significantly improve the creep strength and plasticity of alloy as solution strengthening element.But due to this Alloyapplication
In the high neutron irradiation environment such as nuclear reactor primary tank, by can be changed into 60Co after neutron irradiation, a kind of long half-lift puts Co
Penetrating property material, releases gamma-rays, produces long-term harm to environment, so Co elements can not add in the alloy.
, used as solution strengthening element, its solid solution strengthening effect is poor for Cu, thus in the alloy without.If adding the Cu
Element, will increase alloying element species, drop low-alloyed structure stability.
Resistance to fused salt corrosion Ni-based deformation of 5 embodiments in above range further to provide to the present invention is given below
High temperature alloy is described in detail.The chemical composition of the ni-base wrought superalloy of resistance to fused salt corrosion of each embodiment is referring to table 1 below.
In order to contrast conveniently, the chemical composition of comparative alloy Hastelloy N in table 1, is also listed.
The chemical composition (wt.%) of 1 embodiment of table and comparative alloy Hastelloy N
By taking the ni-base wrought superalloy of resistance to fused salt corrosion obtained by embodiment 1 as an example, it is corresponding that Fig. 1 a- Fig. 1 c give which
Pattern schematic diagram, wherein, Fig. 1 a and Fig. 1 b represent the as-cast structure pattern after 1250 DEG C of Homogenization Treatments 20 hours, can be with
It was found that the granular carbide in cast alloy is uniformly distributed in matrix；Fig. 1 c represent that the ingot casting after Homogenization Treatments exists
The tissue topography of bar after being forged at a temperature of 1100 DEG C, it can be found that tiny carbide even dispersion is in the base of alloy
In body, alloy structure keeps good uniformity.
The alloy and comparative alloy Hastelloy N alloys of embodiments of the invention 1 is given below under several conditions
Tensile property data, referring to table 2 below.
2 alloy of the present invention of table (embodiment 1) and comparative alloy Hastelloy N tensile strength number under several conditions
According to (strain rate is 3 × 10-4s-1)
It follows that the yield strength and tensile strength at the identical temperature of 1 alloy of embodiment is above Hastelloy N
Alloy, yield strength 238MPa of 1 alloy of embodiment at 850 DEG C, higher than Hastelloy N alloys at 700 DEG C
220MPa.Yield strength is an important parameter of reactor design, and only from from the aspect of yield strength, this alloy is expected to will be molten
There is provided from Hastelloy N 700 DEG C of the use temperature of salt heap bring up to 850 DEG C.
Tensile property data of the alloy of embodiments of the invention 2- embodiments 5 under room temperature to high temperature are given below, are joined
See the table below 3.
To high temperature tensile properties, (strain rate is 3 × 10 to the room temperature of 3 alloy of the present invention of table (embodiment 2- embodiment 4)- 4s-1)
It follows that the tensile strength of the alloy of the present invention increases with the increase of W content, when W content 15% with
When upper, its yield strength and tensile strength at 850 DEG C has been better than Hastelloy N alloys.
Be given below embodiments of the invention 1 and embodiment 5 alloy and comparative alloy Hastelloy N alloys it is lasting
Performance data, referring to table 4 below.
The enduring quality of 4 alloy of the present invention of table (embodiment 1 and embodiment 5) and comparative alloy Hastelloy N
It follows that the creep rupture life of alloy of the present invention is higher than comparative alloy Hastelloy N, in 816 DEG C of temperature conditionss
Under, the creep rupture life of 1 alloy of embodiment is more than the twice of Hastelloy N alloys；Under 700 DEG C of temperature conditionss, embodiment 5
Creep rupture life be more than 4 times of Hastelloy N alloys, it is also suitable with Hastelloy N 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 elements is 26-28%.
The alloy of the embodiment of the present invention 1 and the static fused salt corrosion experimental temperature of comparative alloy (Hastelloy N alloys)
For 800 DEG C and 850 DEG C, etching time 400h.Concrete etching condition is as follows：
1st, graphite crucible (its detail parameters is shown in Table 5)：Graphite crucible inwall and parts (peg, lid, bolt and nut)
After being cleaned by ultrasonic in ethanol, 24h is vacuum dried at 700 DEG C, it is after being cooled to room temperature, standby in fast transfer to glove box.
5 graphite crucible parameter of table
2nd, fused salt prepares：Fused salt is ingot casting shape FLiNaK (46.5-11.5-42mol%), and impurity content is：Acid ion
(SO4 2-+PO4 3-+NO3 -) less than 20ppm；Total oxygen content (including acid group, oxide and water) is less than 200ppm；Metal ion is about
100ppm.It is positioned in glove box.
3rd, preparation of samples：Every kind of alloy prepares 3 parallel samples, and alloy sample is polished to 1200# step by step, oil removing, removes
Water, cold wind are dried up, and labelling is complete, standby with the scales/electronic balance weighing that precision is 0.01mg.
4th, 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 for passing judgment on material corrosion performance, it is contemplated that alloy of the present invention is (real
In applying example 1), the density of W is larger, and the weightlessness of unit mol is greater than the Mo in comparative alloy (Hastelloy N alloys).Therefore only
It is inappropriate with the resistance to fused salt corrosion performance between the weightlessness alloy larger as component difference is judged.As alloy is in fused salt
In dominant failure be mainly shown as that the loss of Cr elements in alloy enters fused salt, it is therefore lean using alloy surface after fused salt corrosion
, used as the criterion for characterizing the resistance to fused salt corrosion performance of alloy, the lean Cr thickness degree of alloy is more shallow for the thickness of Cr layers, alloy it is corrosion-resistant
Performance is better.What the Cross Section Morphology and electron probe after two kinds of alloy corrosions that respectively 800 DEG C and 850 DEG C of Fig. 2 and Fig. 3 was characterized
Section Cr distribution diagram of element.It can be found that the lean Cr layers of alloy (embodiment 1) of the present invention are less than comparative alloy (Hastelloy N
Alloy) lean Cr thickness degree.At 800 DEG C, the lean Cr thickness degree of alloy (embodiment 1) of the present invention is 10 μm or so, and contrasts and close
Golden (Hastelloy N alloys) is for 15 μm or so；At 850 DEG C, the lean Cr thickness degree of two kinds of alloys is 25 μm or so.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 Hastelloy N alloys.In Haynes
Hastelloy N alloys are specifically mentioned in the Hastelloy N alloy product Performance Manuals of company can be served in 704 DEG C and arrive
871 DEG C of high-temperature molten salt environment, thus illustrate that alloy of the present invention should also have good resistance to fused salt corrosion under 800-850 DEG C of high temperature
Performance.
Above-described, only presently preferred embodiments of the present invention is not limited to the scope of the present invention, and the present invention's is upper
State embodiment to make a variety of changes.What i.e. every claims and description according to the present patent application were made
Simply, equivalence changes and modification, fall within the claims of patent of the present invention.Of the invention not detailed description is
Routine techniquess content.
Claims (11)
1. a kind of ni-base wrought superalloy of resistance to fused salt corrosion, it is characterised in that by weight percentage, its chemical composition is：
The Si of the Mn of the Fe of the W of the Cr of 6.0-8.0%, 26.0-28.0%, 0.5-0.55%, 0.5-0.8%, 0.1-0.3%, 0.05-
The Ti of the Mo of 0.06% C, 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 characterised in that its chemical composition is：
The Si of the Mn of the Fe of the W of the Cr of 6.0-7.0%, 26.0-28.0%, 0.5-0.55%, 0.5-0.8%, 0.1-0.3%, 0.05-
The Ti of the Mo of 0.06% C, 0-1.0%, 0-0.2%, and the Ni of surplus.
3. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 2, it is characterised in that its chemical composition is：
6.0% Cr's, 26% W, 0.5% Fe, 0.8% Mn, 0.1% Si, 0.05% C, 1.0% Mo, 0.2%
Ti, and the Ni of surplus.
4. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, it is characterised in that the nickel of resistance to fused salt corrosion
Base wrought superalloy does not contain Al.
5. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, it is characterised in that the nickel of resistance to fused salt corrosion
Base wrought superalloy does not contain Co.
6. the ni-base wrought superalloy of resistance to fused salt corrosion according to claim 1, it is characterised in that the nickel of resistance to fused salt corrosion
Base wrought superalloy does not contain Cu.
7. a kind of preparation method of the ni-base wrought superalloy of resistance to fused salt corrosion according to any one of claim 1-6, its
It is characterised by, including step：S1, using vaccum sensitive stove casting foundry alloy；S2, Homogenization Treatments；And S3, hot-working.
8. preparation method according to claim 7, it is characterised in that the treatment temperature of step S2 is at 1200 DEG C -1300 DEG C
Between.
9. preparation method according to claim 7, it is characterised in that the process time of step S2 was at -25 hours 15 hours
Between.
10. preparation method according to claim 7, it is characterised in that the processing temperature of step S3 is at 900 DEG C -1200 DEG C
Between.
11. preparation methoies according to claim 7, it is characterised in that the hot-working of step S3 is forging, hot rolling or heat
Extruding.
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| Application Number | Priority Date | Filing Date | Title |
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| CN201510612608.4A CN105112727B (en) | 2015-09-23 | 2015-09-23 | Fused salt corrosion resistant nickel-based deformable high-temperature alloy and preparation method thereof |
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| CN201510612608.4A CN105112727B (en) | 2015-09-23 | 2015-09-23 | Fused salt corrosion resistant nickel-based deformable high-temperature alloy and preparation method thereof |
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| CN105112727B true CN105112727B (en) | 2017-05-03 |
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|---|---|---|---|---|
| CN106181131B (en) * | 2016-07-15 | 2018-05-29 | 中国科学院上海应用物理研究所 | For the solid core welding wire preparation method of anti-fused salt corrosion nickel base superalloy welding |
| CN106077997B (en) * | 2016-07-15 | 2018-02-09 | 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 fusion welding |
| CN109055879B (en) * | 2018-09-14 | 2019-11-22 | 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 |
| CN110273085B (en) * | 2019-04-15 | 2022-01-07 | 上海大学 | Gadolinium-rich nickel-based alloy material for reactor spent fuel storage and preparation method thereof |
| CN110373573B (en) * | 2019-08-13 | 2021-06-04 | 上海大学 | Gadolinium-rich nickel-tungsten-based alloy material for nuclear shielding and preparation method thereof |
| CN113005379A (en) * | 2019-12-20 | 2021-06-22 | 佛山科学技术学院 | Heat treatment method of nickel-based single crystal superalloy |
| 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 |
| 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 |
| 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 |
Citations (4)
| 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 |
| 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 |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5381677B2 (en) * | 2009-12-15 | 2014-01-08 | 大同特殊鋼株式会社 | Manufacturing method of welding wire |
-
2015
- 2015-09-23 CN CN201510612608.4A patent/CN105112727B/en active Active
Patent Citations (4)
| 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 |
| 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 |
|---|
| Intergranular tellurium cracking of nickel-based alloys in molten Li，Be，Th，U/F salt mixture;Victor Ignatiev等;《Journal of Nuclear Materials》;20130516;第440卷(第1-3期);第243页摘要部分及第244页实验部分 * |
| 镍和镍合金耐腐蚀性分析;马国印等;《化工装备技术》;20070210;第28卷(第1期);第72页表2 * |
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