CN101948970A - Mechanical alloying method for preparing strengthened dispersion alloy of nickel-based oxide - Google Patents
Mechanical alloying method for preparing strengthened dispersion alloy of nickel-based oxide Download PDFInfo
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Abstract
一种机械合金化制备镍基氧化物弥散强化合金的方法，属金属基复合材料领域。其工艺流程为：将FGH96合金元素粉末、氧化物细化元素(Hf)和粒径为20～30nm的氧化物弥散相(Y2O3)预混合均匀，然后在高纯Ar气氛中通过高能球磨将纳米Y2O3颗粒均匀分散在镍基体中，接着将高能球磨后的合金粉末用低碳钢包套并在950～1200℃热等静压。热等静压后的样品进行固溶热处理(950～1200℃)和时效热处理(600～900℃)就能得到最终的纳米相增强的复合材料。本发明的优点主要体现在以FGH96合金的成分为基本成分，添加Hf元素形成Y2Hf2O7复杂氧化物抑制了Y-Al-O复杂氧化物的形成，使弥散相细化到5～13nm。热处理后γ′相的体积百分数高达38％～45％。
The invention discloses a method for preparing a nickel-based oxide dispersion-strengthened alloy by mechanical alloying, which belongs to the field of metal matrix composite materials. The process flow is: pre-mix FGH96 alloy element powder, oxide refining element (Hf) and oxide disperse phase (Y 2 O 3 ) with a particle size of 20-30nm, and then pass high-energy The nanometer Y 2 O 3 particles are evenly dispersed in the nickel matrix by ball milling, and then the alloy powder after high-energy ball milling is covered with a low-carbon steel ladle and hot isostatically pressed at 950-1200°C. The final nano-phase reinforced composite material can be obtained by performing solution heat treatment (950-1200° C.) and aging heat treatment (600-900° C.) on the sample after hot isostatic pressing. The advantages of the present invention are mainly reflected in that the composition of the FGH96 alloy is used as the basic component, and the addition of Hf element to form Y 2 Hf 2 O 7 complex oxides inhibits the formation of Y-Al-O complex oxides and refines the dispersed phase to 5~ 13nm. After heat treatment, the volume percentage of γ' phase is as high as 38%-45%.
Description
Technical field
The invention belongs to field of research of metal, the novel nickel-based oxide dispersion-strengthened of a kind of preparation (Oxide Dispersion Strengthening, ODS) method of alloy are provided especially.
Background technology
The ODS alloy is a kind of important energy high-temperature structural material, and studying maximum at present is the ODS steel.The research and development of ODS alloy are very active in Japan and America and Europe, and China also more and more pays close attention to the fundamental research in this field in recent years.
With the ODS ferritic steel is example, because it has the BCC crystalline structure, under the neutron irradiation condition of 200dpa, still have low-down void swelling rate, add excellent anti-oxidant and corrosion resistance, the ODS ferritic steel can be used for fast reactor and international IV for the clad material in the advanced reactor, first wall material and thermal structure spare.The exploitation of ODS ferritic steel is significant to the thermo-efficiency that improves reactor, the security that reduces environmental pollution, assurance reactor and long lifetime operation.In fusion reactor, the Working environment of first wall/covering is very harsh, not only requires material to have the good high-temperature creep-resistant property, but also extraordinary radioresistance injury reinforcing performance will be arranged.The working temperature of traditional ferrite/martensite steel is the highest can only to reach 550～600 ℃, and the oxide dispersion strengthening ferrite steel can be brought up to working temperature 700 ℃.The stabilized nano oxide particle has been given the high temperature creep property of material excellence.The ODS ferritic steel realizes that the key that breaks through is to utilize Y
2O
3Dissolving/separate out mechanism, usually obtain more tiny oxide compound wild phase by adding Ti unit simultaneously, and can make the distribution of wild phase in matrix more even.In ma process, Y
2O
3Particle dissolves, and separates out with the form of Y-Ti-O complex oxide (2nm) in heat-processed subsequently.Because the particle diameter (3-5nm) of the oxide particle of separating out is less than the Y that adds
2O
3Particle diameter (20-30nm).The high temperature creep property of this particle diameter to wild phase, grain fineness number, martensitic transformation and ODS ferritic steel all has crucial effects.
Nickel-base sintered superalloy can be at high-temperature oxidation resistant or anticorrosive more than 600 ℃, and high-temperature material that can long term operation under certain stress, and it is widely used as high temperature structured materials such as engine turbine disk owing to having the excellent high-temperature performance.Nickel-base sintered superalloy has solved traditional casting and has forged superalloy and cause problems such as the serious and hot workability difference of ingotism because of the alloying level height, thereby make the powder metallurgy superalloy turbine disk have more excellent mechanical property and hot workability, the nickel-base high-temperature material is brought up to a brand-new level, thereby become the preferred material of key parts such as high thrust-weight ratio aero-engine turbine disk.China is since the research of late nineteen seventies start powder superalloy, gone through two generation powder metallurgy superalloy research process, be respectively the damage tolerance type FGH96 alloy of 750 ℃ of the high strong type FGH95 alloy of 650 ℃ of first-generation use temperatures and s-generation use temperatures.Compare the high strong type FGH95 of first-generation alloy, the FGH96 alloy has following characteristics on optimizing components: [1] has added more solid solution strength Elements C o, Mo and W, the hot strength of raising alloy; [2] reduced γ ' phase forming element Al, the total amount of Ti makes γ ' phase volume percentage ratio reduce to less than 40% from 50%; [3] element nb content is reduced to 0.8% from 3.5%, the auxiliary γ ' phase volume percentage ratio that reduced of the effect first, and it two is notch sensitivities of improving alloy.In addition, the increase of Cr content can improve the oxidation-resistance of alloy, and the Ce that adds trace is to purify the highly malleablized effect of crystal boundary and raising crystal boundary.This shows that the FGH96 alloy has more excellent comprehensive mechanical properties.
The ODS nickel based super alloy still has excellent high temperature creep property, fatigue property and antioxidant property more than 1000 ℃.Can be used as turning vane or turbine blade in the turbo-jet engine, life-time service at high temperature not only, and can also bear gaseous corrosion, creep and fatigue loading.The high temperature creep property of ODS nickel based super alloy excellence mainly has benefited from dispersion-strengthened, the γ ' [Ni of oxide particle
3(Al, Ti)] precipitation strength and elongate crystal grain and suppress the crystal boundary slippage.The middle temperature of ODS nickel based super alloy (700～900 ℃) strength ratio Ni-based cast superalloy is low, and the interpolation by Al, Ti and Ta has formed FCC (L1
2) ordered structure γ ' phase and keep coherence with the γ matrix, improved medium temperature intensity.When used (T＞1000 ℃) under higher temperature, γ ' was because dissolving loses strengthening effect, and the strengthening effect of steady oxide at this moment accounts for leading.At present, the problem of ODS nickel based super alloy existence is that (15～50nm) than the Y in the iron-based ODS alloy for the particle diameter of dispersed oxide phase
2Ti
2O
7Disperse phase (3nm) is slightly much bigger, and this is because Y
2O
3Al reaction easy and solid solution forms a series of Y-Al-O complex oxide (Al
2Y
4O
9, Al
5Y
3O
12And AlYO
3), and a small amount of Al
2O
3And the generation alligatoring.Therefore, the particle diameter of managing to reduce oxide compound is the key point that guarantees long-term structure stability and further improve mechanical property.
Summary of the invention
The ODS alloy that the objective of the invention is development of new by γ ' phase and the common reinforcement of oxide compound.This method can prepare nano oxide dispersion phase enhanced metal-base composites, has that disperse phase is evenly distributed, the strengthening effect outstanding feature.
The present invention intends by adding Y based on the composition (as shown in table 1) of FGH96 alloy
2O
3Further improve the high temperature creep property of alloy.The Hf energy and the Y that add
2O
3In conjunction with also forming more stable Y
2H
2O
7Complex oxide keeps coherence or half coherence with matrix, and disperse phase is played the effect of refinement, and this will make strengthening effect strengthen.
The present invention adopts high-energy ball milling with Y
2O
3Uniform particles is dispersed in the matrix, then by the heat and other static pressuring processes densification.Y
2O
3Be the most effective strengthening phase, this is because it has and dissolves/separate out mechanism.In ma process, Y
2O
3Particle dissolves, and in the process of postheating with Y-Hf-O, the form of complex oxides such as Y-Al-O is separated out, and makes the particle diameter of the oxide particle of separating out just might be less than the Y of original interpolation
2O
3Particle diameter, this just lays a good foundation for the raising of high temperature creep property.The technical process of novel Ni-based ODS alloy is as shown in Figure 1:
The chemical ingredients (weight %) of table 1FGH96 alloy
At first with Co, Cr, Mo, W, Al, Ti, Nb, B, Zr, C and Ni according to the composition proportion weighing shown in the table 1, add the oxide particle (Y of 0.8～1.5 weight % then in addition
2O
3) and the oxide compound refinement element (Hf) of 1～3 weight %.The Hf element is the crucial alloying element of refinement disperse phase, type, particle diameter and distributing homogeneity that the addition of Hf element can better controlled dispersed oxide phase in the scope of 1～3 weight % the time.Wherein the massfraction of Hf element is in 1.2～1.8% the scope time, and it is to thinning effect the best of disperse phase.Then, this element mixed powder encapsulates in glove box, and protective atmosphere is a high-purity argon gas.By high-energy ball milling with Y
2O
3Uniform particles is dispersed in the Ni substrate; Powder coheres on the ball grinder inwall in the high-energy ball milling process to avoid as process control agent to add 1-3 weight % stearic acid.The rotating speed of ball mill and enough ball milling time be the oxide compound homodisperse and in matrix the dissolved key parameter, the rotating speed of ball mill is controlled in 380～500 rev/mins the scope, the ball milling time is 36-72 hour.Powdered alloy behind the high-energy ball milling carries out vacuum canning with soft steel, carries out densification then on hot isostatic pressing, and temperature is 950～1200 ℃ and is incubated 3 hours, can guarantee that so obvious alligatoring does not take place crystal grain and oxide compound is grown up.The fine and close sample that obtains behind the hot isostatic pressing carries out solution heat treatment at 950～1200 ℃, carries out ageing treatment at 600～900 ℃ at last, and this just obtains novel Ni-based ODS alloy.Figure 2 shows that through the SEM microstructure after solid solution and the timeliness thermal treatment, visible γ ' phase particle diameter tiny and in matrix uniform distribution.Figure 3 shows that the TEM microstructure of novel Ni-based ODS alloy, nano level oxide particle is evenly distributed in the matrix.The volume fraction of γ ' phase, particle diameter and size distribution are controlled by the change of suitable solution treatment, ageing treatment and rate of cooling easily.Optimize Y
2O
3Content can change the strengthening effect of dispersed oxide phase, thereby reach the requirement that improves high temperature creep property.A key of this novel Ni-based ODS alloy is to adopt the interpolation of Hf element to come the disperse of refinement oxide compound is distributed, reduce particle diameter and dwindled average headway between the particle, according to the dispersion-strengthened theory, this motion to effective pinning dislocation under the high temperature will be played more effective effect.
Advantage of the present invention is the characteristics of two kinds of strengthening phases of comprehensive utilization: γ ' (700～900 ℃) strengthening effect in intermediate temperature range is more remarkable, Y
2O
3Also has good reinforced effects Deng nano-oxide during greater than 1000 ℃ in temperature.The two has complementarity, they is combined can give play to the mechanical behavior under high temperature of nickel-base alloy to greatest extent.In addition, owing to adopted nickel-base alloy FGH96, help improving fatigue property and damage tolerance performance as basic ingredient with excellent comprehensive mechanical properties.γ ' phase separate out pattern, volume fraction is regulated by thermal treatment process easily, and has the more sophisticated technology can be for reference.Adopt special alloying element Hf that dispersed oxide is played effective refining effect mutually, this will increase substantially its strengthening effect.This novel Ni-based ODS alloy is expected to life-time service at high temperature, and can also bear gaseous corrosion, creep and fatigue loading, in high-temperature material fields such as turbine engine blades good application prospects is arranged.
Description of drawings
Fig. 1 is a process flow sheet of the present invention
Fig. 2 is the pattern of γ ' phase in the novel Ni-based ODS alloy
Fig. 3 is a nano-oxide particles in the novel Ni-based ODS alloy
Embodiment
Comparison example 1: the novel Ni-based ODS alloy that no Hf element adds.
At first Ni-13 weight %Co-15 weight %Cr-4 weight %Mo-4 weight %W-2.2 weight %Al-3.7 weight %Ti-0.8 weight %Nb-0.03 weight %C is carried out weighing according to composition proportion, the particle diameter that adds 1 weight % then is the oxide particle (Y of 20～30nm
2O
3) and the oxide compound refinement element (Hf) of 0 weight %.Then, this element mixed powder encapsulates in glove box, adopts high-purity argon gas (99.999%) as protective atmosphere.By mechanical alloying with Y
2O
3Uniform particles is dispersed in Ni substrate; Powder coheres on the ball grinder inwall in the high-energy ball milling process to avoid as process control agent to add the stearic acid of 1.5 weight % simultaneously.The rotating speed of ball mill is 400 rev/mins, and the ball milling time is 48 hours.Powdered alloy behind the high-energy ball milling carries out vacuum canning with soft steel, carries out densification then on hot isostatic apparatus, and hip temperature is 1050 ℃ and is incubated 3 hours.The fine and close sample that obtains behind the hot isostatic pressing carries out solution heat treatment (shrend) at 960 ℃, carries out timeliness thermal treatment at 760 ℃ at last, and this just obtains novel Ni-based ODS alloy.The volume fraction of γ ' phase is 38%, and the median size of γ ' phase is 1.5 μ m, and the mean sizes of oxide compound is 39nm.
Embodiment 1: the novel Ni-based ODS alloy that adds 1.5 weight %Hf elements.
At first Ni-13 weight %Co-15 weight %Cr-4 weight %Mo-4 weight %W-2.2 weight %Al-3.7 weight %Ti-0.8 weight %Nb-0.03 weight %C is carried out weighing according to composition proportion, the particle diameter that adds 1 weight % then is the oxide particle (Y of 20～30nm
2O
3) and the oxide compound refinement element (Hf) of 1.5 weight %.Then, this element mixed powder encapsulates in glove box, adopts high-purity helium (99.999%) as protective atmosphere.By mechanical alloying with Y
2O
3Uniform particles is dispersed in Ni substrate; Powder coheres on the ball grinder inwall in the high-energy ball milling process to avoid as process control agent to add the stearic acid of 2 weight % simultaneously.The rotating speed of ball mill is 400 rev/mins, and the ball milling time is 48 hours.Powdered alloy behind the high-energy ball milling carries out vacuum canning with soft steel, carries out densification then on hot isostatic apparatus, and hip temperature is 1050 ℃ and is incubated 3 hours.The fine and close sample that obtains behind the hot isostatic pressing 1150 ℃ carry out solution heat treatment and with 25 ℃/minute rate of cooling slow cooling to room temperature, carry out timeliness thermal treatment at 760 ℃ at last, this just obtains novel Ni-based ODS alloy.The volume fraction of γ ' phase is 37%, and the median size of γ ' phase is 230nm, and the median size of oxide compound is 11nm.
Embodiment 2: the novel Ni-based ODS alloy of inferior solid solution+slow cooling thermal treatment (25 ℃/minute) preparation.
At first Ni-13 weight %Co-15 weight %Cr-4 weight %Mo-4 weight %W-2.2 weight %Al-3.7 weight %Ti-0.8 weight %Nb-0.03 weight %C is carried out weighing according to composition proportion, the particle diameter that adds 1 weight % then is the oxide particle (Y of 20～30nm
2O
3) and the oxide compound refinement element (Hf) of 1.5 weight %.Then, this element mixed powder encapsulates in glove box, adopts high-purity argon gas (99.999%) as protective atmosphere.By mechanical alloying with Y
2O
3Uniform particles is dispersed in Ni substrate; Powder coheres on the ball grinder inwall in the high-energy ball milling process to avoid as process control agent to add the stearic acid of 1 weight % simultaneously.The rotating speed of ball mill is 400 rev/mins, and the ball milling time is 60 hours.Powdered alloy behind the high-energy ball milling carries out vacuum canning with soft steel, carries out densification then on hot isostatic apparatus, and hip temperature is 1050 ℃ and is incubated 3 hours.The fine and close sample that obtains behind the hot isostatic pressing carries out solution heat treatment (rate of cooling is 25 ℃/minute) at 1150 ℃, carries out timeliness thermal treatment at 760 ℃ at last, and this just obtains novel Ni-based ODS alloy.The volume fraction of γ ' phase is 45%, and the median size of γ ' phase is 1.2 μ m, and the median size of oxide compound is 10nm.
Embodiment 3: the novel Ni-based ODS alloy of crossing solid solution+fast cold and hot processing (800 ℃/minute) preparation.
At first Ni-13 weight %Co-15 weight %Cr-4 weight %Mo-4 weight %W-2.2 weight %Al-3.7 weight %Ti-0.8 weight %Nb-0.03 weight %C is carried out weighing according to composition proportion, the particle diameter that adds 1 weight % then is the oxide particle (Y of 20～30nm
2O
3) and the oxide compound refinement element (Hf) of 1.5 weight %.Then, this element mixed powder encapsulates in glove box, adopts high-purity argon gas (99.999%) as protective atmosphere.By mechanical alloying with Y
2O
3Uniform particles is dispersed in Ni substrate; Powder coheres on the ball grinder inwall in the high-energy ball milling process to avoid as process control agent to add the stearic acid of 3 weight % simultaneously.The rotating speed of ball mill is 400 rev/mins, and the ball milling time is 72 hours.Powdered alloy behind the high-energy ball milling carries out vacuum canning with soft steel, carries out densification then on hot isostatic apparatus, and hip temperature is 1050 ℃ and is incubated 3 hours.The fine and close sample that obtains behind the hot isostatic pressing carries out solution heat treatment at 1150 ℃, and controlled chilling speed carries out timeliness thermal treatment at 760 ℃ at last with 800 ℃ of/minute cool to room temperature, and this just obtains novel Ni-based ODS alloy.The volume fraction of γ ' phase is 41%, and the median size of γ ' phase is 0.8 μ m, and the median size of oxide compound is 9nm.
Claims (5)
1. the method for a prepared by mechanical alloy nickel-based oxide strengthened dispersion alloy is characterized in that:
A, design of alloy, the basic ingredient quality percentage composition of nickel-based oxide strengthened dispersion alloy is: Co is 12～14%, Cr is 15～17%, Mo is 3～5%, W is 3～5%, Al is 1.5～3%, Ti is 3～5%, Nb is 0.5～1.0%, C is 0.03～0.05%, surplus is Ni; The interpolation massfraction is 0.8～1.5% Y in basic ingredient
2O
3As the dispersed oxide phase, add massfraction and be 1～3% Hf element as disperse phase refinement element; With alloying constituent uniform mixing in proportion;
B, high-energy ball milling make Y in the mixture by high-energy ball milling in high-purity protective atmosphere
2O
3Uniform particles is dispersed in the Ni matrix; The rotating speed of ball mill is controlled in 380～500 rev/mins the scope, and the ball milling time is 36～72 hours;
C, hot isostatic pressing, the mixed powder behind the high-energy ball milling adopt the stainless steel jacket to carry out soldering and sealing, and then at 950～1200 ℃ of hot isostatic pressings, soaking time is 1-3 hour;
D, solid solution and timeliness thermal treatment can be controlled γ ' particle diameter and size distribution mutually by solid solution and timeliness thermal treatment, and its strengthening effect is optimized; The solution heat treatment temperature scope is 950～1200 ℃, and timeliness thermal treatment is carried out in 600～900 ℃ temperature range.
2. the method for prepared by mechanical alloy nickel-based oxide strengthened dispersion alloy as claimed in claim 1, it is characterized in that: in the described high-energy ball milling process, the stearic acid of the 1-3% of interpolation alloy total mass is as process control agent, to avoid powder agglomates in the high-energy ball milling process.
3. the method for prepared by mechanical alloy nickel-based oxide strengthened dispersion alloy as claimed in claim 1 is characterized in that: described high-purity protective atmosphere is argon gas or the helium of purity more than 99.999%.
4. the method for prepared by mechanical alloy nickel-based oxide strengthened dispersion alloy as claimed in claim 1 is characterized in that: described Y
2O
3Particle diameter be 20～30nm.
5. the method for prepared by mechanical alloy nickel-based oxide strengthened dispersion alloy as claimed in claim 1 is characterized in that: the massfraction of described Hf element is 1.2～1.8%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201010512712 CN101948970A (en) | 2010-10-13 | 2010-10-13 | Mechanical alloying method for preparing strengthened dispersion alloy of nickel-based oxide |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102251131A (en) * | 2011-06-30 | 2011-11-23 | 北京科技大学 | Method for preparing injection-molding nickel-base ODS (oxide dispersion strengthened) alloy |
| CN103060586A (en) * | 2013-01-15 | 2013-04-24 | 北京科技大学 | Preparation method for complex-shape niobium-based ODS (oxide dispersion strengthening) alloy |
| CN104404418A (en) * | 2014-12-09 | 2015-03-11 | 中南大学 | Thermal treatment method for nickel-base high temperature alloy |
| RU2563084C1 (en) * | 2014-11-14 | 2015-09-20 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Production of high-temperature nickel-based composite |
| CN104959624A (en) * | 2015-06-17 | 2015-10-07 | 北京科技大学 | Nanoscale oxide dispersion strengthened nickel base composite powder preparing method |
| CN105821359A (en) * | 2016-04-11 | 2016-08-03 | 西安欧中材料科技有限公司 | Heat-treatment technology of high-plasticity nickel base alloy |
| CN105983703A (en) * | 2014-11-21 | 2016-10-05 | 北京有色金属研究总院 | Thermal treatment method for molding automobile turbo by powder injection |
| CN106825587A (en) * | 2016-12-05 | 2017-06-13 | 北京科技大学 | A kind of method for preparing oxide dispersion intensifying ferrous alloy |
| CN108161275A (en) * | 2018-01-08 | 2018-06-15 | 河北工业大学 | A kind of nickel-base alloy seam organization crystal fining method and its application |
| CN108330408A (en) * | 2017-01-18 | 2018-07-27 | 天津大学 | A kind of high intensity alferric ferritic ODS steel and preparation method thereof |
| CN109207765A (en) * | 2018-10-31 | 2019-01-15 | 中国科学院金属研究所 | The method that power forging prepares oxide-dispersed alloy |
| CN109332680A (en) * | 2018-11-07 | 2019-02-15 | 南京航空航天大学 | A nano-oxide particle/nickel-based superalloy composite spherical powder for high-energy beam 3D printing and preparation method thereof |
| CN110527856A (en) * | 2019-09-20 | 2019-12-03 | 无锡市东杨新材料股份有限公司 | A kind of preparation method of great surface quality, high-intensity nickel alloy band |
| CN110863126A (en) * | 2019-12-30 | 2020-03-06 | 临沂鑫海新型材料有限公司 | High-performance nickel-based heat-resistant alloy |
| CN111979469A (en) * | 2020-07-31 | 2020-11-24 | 青岛理工大学 | A kind of preparation method of oxide dispersion strengthened steel based on powder forging |
| CN112033163A (en) * | 2020-09-03 | 2020-12-04 | 昆明理工大学 | High-temperature-resistant corrosion-resistant long-life alloy spray gun for smelting of pizza furnace and preparation method thereof |
| CN112534073A (en) * | 2018-08-02 | 2021-03-19 | 西门子能源环球有限责任两合公司 | Metal composite |
| CN114505479A (en) * | 2022-02-15 | 2022-05-17 | 中南大学 | ODS alloy composition design method based on diffusion multi-element technology |
| CN115537625A (en) * | 2021-06-29 | 2022-12-30 | 通用电气公司 | Oxide dispersion strengthened refractory base alloy |
| CN115609009A (en) * | 2022-09-20 | 2023-01-17 | 天津大学 | Method for eliminating printing cracks of solid solution strengthened nickel-based superalloy in additive manufacturing |
| CN115608999A (en) * | 2022-10-17 | 2023-01-17 | 合肥工业大学 | A kind of W-Y2O3-HfO2 composite powder and its preparation method |
| CN116287872A (en) * | 2023-05-19 | 2023-06-23 | 北京煜鼎增材制造研究院有限公司 | Particle reinforced nickel-based superalloy and additive preparation method thereof |
| CN116555630A (en) * | 2022-01-27 | 2023-08-08 | 中南大学深圳研究院 | ODS nickel-based superalloy and its preparation method and application |
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| CN102251131B (en) * | 2011-06-30 | 2012-11-28 | 北京科技大学 | Method for preparing injection-molding nickel-base ODS (oxide dispersion strengthened) alloy |
| CN102251131A (en) * | 2011-06-30 | 2011-11-23 | 北京科技大学 | Method for preparing injection-molding nickel-base ODS (oxide dispersion strengthened) alloy |
| CN103060586A (en) * | 2013-01-15 | 2013-04-24 | 北京科技大学 | Preparation method for complex-shape niobium-based ODS (oxide dispersion strengthening) alloy |
| CN103060586B (en) * | 2013-01-15 | 2014-09-17 | 北京科技大学 | Preparation method for complex-shape niobium-based ODS (oxide dispersion strengthening) alloy |
| RU2563084C1 (en) * | 2014-11-14 | 2015-09-20 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Production of high-temperature nickel-based composite |
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| CN104404418A (en) * | 2014-12-09 | 2015-03-11 | 中南大学 | Thermal treatment method for nickel-base high temperature alloy |
| CN104959624A (en) * | 2015-06-17 | 2015-10-07 | 北京科技大学 | Nanoscale oxide dispersion strengthened nickel base composite powder preparing method |
| CN105821359A (en) * | 2016-04-11 | 2016-08-03 | 西安欧中材料科技有限公司 | Heat-treatment technology of high-plasticity nickel base alloy |
| CN106825587A (en) * | 2016-12-05 | 2017-06-13 | 北京科技大学 | A kind of method for preparing oxide dispersion intensifying ferrous alloy |
| CN106825587B (en) * | 2016-12-05 | 2018-09-14 | 北京科技大学 | A method of preparing oxide dispersion intensifying ferrous alloy |
| CN108330408A (en) * | 2017-01-18 | 2018-07-27 | 天津大学 | A kind of high intensity alferric ferritic ODS steel and preparation method thereof |
| CN108330408B (en) * | 2017-01-18 | 2019-10-01 | 天津大学 | A kind of high intensity alferric ferritic ODS steel and preparation method thereof |
| CN108161275A (en) * | 2018-01-08 | 2018-06-15 | 河北工业大学 | A kind of nickel-base alloy seam organization crystal fining method and its application |
| CN112534073A (en) * | 2018-08-02 | 2021-03-19 | 西门子能源环球有限责任两合公司 | Metal composite |
| US11773469B2 (en) | 2018-08-02 | 2023-10-03 | Siemens Energy Global GmbH & Co. KG | Metal composition |
| CN109207765A (en) * | 2018-10-31 | 2019-01-15 | 中国科学院金属研究所 | The method that power forging prepares oxide-dispersed alloy |
| CN109332680A (en) * | 2018-11-07 | 2019-02-15 | 南京航空航天大学 | A nano-oxide particle/nickel-based superalloy composite spherical powder for high-energy beam 3D printing and preparation method thereof |
| CN110527856A (en) * | 2019-09-20 | 2019-12-03 | 无锡市东杨新材料股份有限公司 | A kind of preparation method of great surface quality, high-intensity nickel alloy band |
| CN110527856B (en) * | 2019-09-20 | 2021-04-30 | 无锡市东杨新材料股份有限公司 | Preparation method of high-surface-quality and high-strength nickel alloy strip |
| CN110863126B (en) * | 2019-12-30 | 2020-11-06 | 临沂鑫海新型材料有限公司 | High-performance nickel-based heat-resistant alloy |
| CN110863126A (en) * | 2019-12-30 | 2020-03-06 | 临沂鑫海新型材料有限公司 | High-performance nickel-based heat-resistant alloy |
| CN111979469A (en) * | 2020-07-31 | 2020-11-24 | 青岛理工大学 | A kind of preparation method of oxide dispersion strengthened steel based on powder forging |
| CN111979469B (en) * | 2020-07-31 | 2021-07-27 | 青岛理工大学 | A kind of preparation method of oxide dispersion strengthened steel based on powder forging |
| CN112033163A (en) * | 2020-09-03 | 2020-12-04 | 昆明理工大学 | High-temperature-resistant corrosion-resistant long-life alloy spray gun for smelting of pizza furnace and preparation method thereof |
| CN115537625A (en) * | 2021-06-29 | 2022-12-30 | 通用电气公司 | Oxide dispersion strengthened refractory base alloy |
| CN116555630A (en) * | 2022-01-27 | 2023-08-08 | 中南大学深圳研究院 | ODS nickel-based superalloy and its preparation method and application |
| CN114505479A (en) * | 2022-02-15 | 2022-05-17 | 中南大学 | ODS alloy composition design method based on diffusion multi-element technology |
| CN114505479B (en) * | 2022-02-15 | 2024-07-16 | 中南大学 | ODS alloy component design method based on diffusion multi-section technology |
| CN115609009A (en) * | 2022-09-20 | 2023-01-17 | 天津大学 | Method for eliminating printing cracks of solid solution strengthened nickel-based superalloy in additive manufacturing |
| CN115608999A (en) * | 2022-10-17 | 2023-01-17 | 合肥工业大学 | A kind of W-Y2O3-HfO2 composite powder and its preparation method |
| CN116287872A (en) * | 2023-05-19 | 2023-06-23 | 北京煜鼎增材制造研究院有限公司 | Particle reinforced nickel-based superalloy and additive preparation method thereof |
| CN116287872B (en) * | 2023-05-19 | 2023-08-04 | 北京煜鼎增材制造研究院股份有限公司 | Particle reinforced nickel-based superalloy and additive preparation method thereof |
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