CN107630153A - A kind of die material cast Ni-base alloy - Google Patents
A kind of die material cast Ni-base alloy Download PDFInfo
- Publication number
- CN107630153A CN107630153A CN201710828427.4A CN201710828427A CN107630153A CN 107630153 A CN107630153 A CN 107630153A CN 201710828427 A CN201710828427 A CN 201710828427A CN 107630153 A CN107630153 A CN 107630153A
- Authority
- CN
- China
- Prior art keywords
- alloy
- die material
- base alloy
- material cast
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Abstract
The invention discloses a kind of die material cast Ni-base alloy：The composition of the alloy includes：C：0.10‑0.18；Co：9.0‑12.0；Al：5.0‑6.0；Cr：5.5‑7.5；W：13.0‑15.0；Nb：2.0‑3.0；Ta：0.75‑1.75；B：0.01‑0.03；Zr：0.03‑0.15；Ti：0.5‑1.5；Surplus is nickel；Unit is percetage by weight；Die material cast Ni-base alloy provided by the invention, there is provided a kind of die material material used under 950 1050 DEG C of air, while there is good elevated temperature strength, antioxygenic property and moderate cost, meet wrought superalloy ausforming needs.
Description
Technical field
The present invention is a kind of die material cast Ni-base alloy, belongs to metal material field.
Background technology
Isothermal forging is a kind of important moulding process of high-temperature structural material, and first the technology key technology is mould
Material.Such as Isothermal Forging of Titanium Alloy domestic at present, mold temperature are 800 DEG C -950 DEG C.Wrought superalloy isothermal forging, temperature
Generally 950-1050 DEG C.Ni-base P/M Superalloy, isothermal forging temperature are 1050-1100 DEG C.
Isothermal Forging of Titanium Alloy, mold temperature is 800 DEG C -950 DEG C, and because temperature is relatively low, the country is typically made using K403
For mould.Because K403 alloys are after temperature is more than 950 DEG C, drawing by high temperature and creep rupture strength drastically decline, and the alloy does not apply to
In wrought superalloy and Ni-base P/M Superalloy isothermal forging.
By literature query and patent retrieval, a kind of nickel base cast is provided in CN2005100814011.3 patent applications
High temperature alloy, it is mainly used in Ni-base P/M Superalloy forging.It includes following components in percentage by weight：Co 9.0~
12.0%；Al 5.0~6.5%；Cr 2.5~3.5%；Ti 0.5~1.5%；W 13.0~14.5%；Mo 1.5~
2.5%；Nb 0.8~1.5%；Ta 2.0~5.0%；Hf 0.3~1.5%；C 0.07~0.18%；B 0.01~
0.02%；Y≤0.01%, surplus are nickel.The alloy can be used for 1050 DEG C -1100 DEG C.The alloy with the addition of noble element hafnium
(Hf), for Ta contents more than 2%, totle drilling cost is higher.In addition, Cr contents are relatively low, antioxygenic property is relatively poor.
There is document to propose using K21 as 1050 DEG C with isothermal forging mould, according to open source information, 1050 DEG C of the alloy
Tensile strength is relatively low (yield strength 418MPa), while when making large mold, has obvious tearing tendency.For deformation
For high temperature alloy isothermal forging, it is badly in need of that a kind of price used at 1050 DEG C is suitable, the high temperature alloy mould material of excellent performance
Material.
The content of the invention
The present invention is to provide a kind of die material Ni-based cast to solve the technical scheme that above-mentioned technical problem uses
Alloy, wherein, concrete technical scheme is：
The composition of the alloy includes：
C：0.10-0.18；
Co：9.0-12.0；
Al：5.0-6.0；
Cr：5.5-7.5；
W：13.0-15.0；
Nb：2.0-3.0；
Ta：0.75-1.75；
B：0.01-0.03；
Zr：0.03-0.15；
Ti：0.5-1.5；
Surplus is nickel；
Unit is percetage by weight.
The microscopic structure of the alloy is made up of austenite γ matrixes, and in mentioned component, W, Nb, Ta form high-melting-point element
Solution strengthening matrix.
Al, Ti, Nb, Ta form γ ' and mutually strengthened, and Nb, Ta and Ti can generate primary carbide, and C, B, Zr element are carried out
Intercrystalline strengthening.
The present invention has the advantages that relative to prior art：There is provided and a kind of use under 950-1050 DEG C of air
Die material material, while there is good elevated temperature strength, antioxygenic property and moderate cost, meet wrought superalloy etc.
Warm working needs.
Brief description of the drawings
Fig. 1 is the composition of tested alloys.
Fig. 2 is the mechanical property of tested alloys.
Embodiment
The invention will be further described with reference to the accompanying drawings and examples.
A kind of die material cast Ni-base alloy provided by the invention, it is characterised in that the composition of the alloy includes
(unit is percetage by weight)：C：0.10-0.18；Co：9.0-12.0；Al：5.0-6.0；Cr：5.5-7.5；W：13.0-15.0；
Nb：2.0-3.0；Ta：0.75-1.75；B：0.01-0.03；Zr：0.03-0.15；Ti：0.5-1.5, surplus are nickel and can not kept away
The impurity exempted from.
The microscopic structure of the alloy is made up of austenite γ matrixes.In mentioned component, W, Nb, Ta etc. are high, and melting element is consolidated
Molten reinforcing matrix.Al, Ti, Nb, Ta etc. form γ ' and mutually strengthened.Nb, Ta and Ti can generate a small amount of primary carbide.C、
B, the element such as Zr carries out intercrystalline strengthening.Al and Cr elements are important resistance to high temperature oxidation elements.Co can improve micro- group of alloy
Knit, suppress M6C and separate out, while improve casting character.
There is the reasons why chemical composition and its control range of excellent thermoplasticity nickel base superalloy to make the present invention below
It is as described below：
C：0.10-0.18%
C is the indispensable element that carbide is formed in nickel-base cast superalloy.C controls in 0.10-0.18% be it is necessary,
One will ensure that a number of carbide separates out in crystal boundary, play a part of crystal grain thinning, improve creep rupture strength and plasticity, simultaneously
Casting fluidity can be improved, two will prevent that excessive carbide from causing field trash excessively and segregation is inclined to, and cause crystal grain uneven
Uniform alloy plasticity deteriorates.C content control is considered in 0.10-0.18%.
Cr：5.5-7.5%
The addition of Cr elements considers two factors, first, consider that Cr elements have excellent antioxygenic property, should be appropriate
Addition；It is thought of as improving the elevated temperature strength of alloy, Cr contents need to be suitably reduced, using W, Ta with higher solid solution strengthening effect
Deng element substitution.Consider and control Cr contents in 5.5-7.5%.
Co：9.0-12.0%
Co elements can improve structure stability, reduce harmful phase and separate out, especially for high W alloy, pole during casting
Easily separate out nascent M6C, separate out a large amount of M6C during applied at elevated temperature, decline alloy mechanical property.Co is to suppress M6C to separate out strongly
Important element.Consider and control Co contents in 9.0-12.0%.
Ni：Matrix
Ni-Cr-Fe alloys constitute the matrix of the nickel-base alloy, and Fe additions about 7%.Appropriate Fe is added, and can be replaced
Part Ni is changed, does not significantly affect the performance of alloy, cost of alloy can be significantly reduced.But excessive Fe, for the steady of alloy
It is qualitative unfavorable, consider, Ni contents are necessary >=and 70%.
Al：5.0-6.0%
Al is the required formation element of γ ' phases in nickel-base alloy, and γ ' is mutually most important a kind of reinforcing in nickel-base alloy
Phase.By adding higher Al elements, more γ ' tissues can be separated out, by forming coherence or half altogether with matrix γ solid solution
The relation of lattice, and then formed and strengthened, the back dissolving temperature of γ ' phases increases, and can improve the heat-resisting quantity of alloy.Meanwhile Al addition
It is significantly improved for the antioxygenic property of alloy, Al and O2 reacts at high temperature, forms one layer of fine and close Al2O3 oxidation
Film, alloy is formed and protected.Al content is higher, and the amount of precipitation of γ ' phases is bigger, but Al is too high that cracking can be produced in casting process
Sensitiveness.So Al controls are in 5.0-6.0%.
Ti：0.5-1.5%
Contain certain Ti elements in this alloy, be because alloy in Ti be easy to dissolve in γ ' phases, can replace three/
Two Al atoms.After Ti enters γ ', slow down γ ' precipitations, effectively prevent the effect of overaging, this effect is adapted to alloy
Used for a long time in high-temperature work environment.But Ti, which is added, will excessively generate Ni3Ti (η phases), and Ni3Ti phases are without age-hardening
Ability, this alloy Ti, which contains, measures control range in Ti：0.5-1.5%.
Nb：2.0-3.0%
A certain amount of Nb is added in this alloy, is because Nb and Ni forms γ " hardening constituents, significantly increases the strong of alloy
Degree, in addition, slightly higher Nb can improve the high-temperature stability of alloy, Nb elements are as more precious metal, only appropriate addition.This conjunction
Golden Nb, which contains, measures control range in 2.0-3.0%.
Ta：0.75-1.5%
A certain amount of Ta is added in this alloy, on the one hand Ta elements can be dissolved to matrix, improve the elevated temperature strength of matrix,
On the other hand γ ' phases can be formed, phase amount is strengthened in increase.But Ta elements are expensive metals, consider from control cost of alloy, this
Alloy only adds necessary, appropriate Ta elements.This alloy Nb, which contains, measures control range in 0.75-1.5%.
W：13.0-15.0%
A certain amount of W is added in this alloy, W elements mainly carry out solution strengthening, improve high-temperature substrate intensity, the opposing party
The a small amount of W in face can enter γ ' phases, and phase amount is strengthened in increase.But too high W easily generates the M6C of bulk, infringement is alloy properties
Can, this alloy W content obtains control range in 13.0-15.0%.
Zr：0.03-0.15%
The Zr elements added in this alloy, segregation to crystal boundary, grain boundary defects are reduced, improve crystal boundary adhesion, reduce crystal boundary
Diffusion rate, so as to slow down dislocation climb, strengthen crystal boundary.Meanwhile Zr segregations can reduce interface energy in crystal boundary, improve Grain-Boundary Phase
Form, the size of Grain-Boundary Phase is reduced, improve creep rupture life, improve rupture ductility.This alloy Zr, which contains, measures control range in 0.03-
0.15%.
B：0.01-0.03
The B element added in this alloy, B can reduce grain boundary defects as boundary-strengthening element, improve crystal boundary adhesion,
On the other hand energy microstructure stability, the castability of alloy is improved.This alloy B content control range is in 0.01-0.03%
Ni elements, as this alloy substrate, allotropy transformation does not occur from room temperature to high temperature, there is provided stable austenite
Matrix, while there is very big alloying power
Shown by experimental study, the alloy has good combination property in the range of mentioned component.The alloy exists
1050 tensile yield strengths can be in 500MPa or so, and elongation percentage is up to 4%.The alloy antioxygenic property is superior, 1050 DEG C of oxygen
Change speed is 0.089g/m2h, and according to HB5282-2000 regulation, 1050 DEG C of antioxygenic properties of the alloy reach complete antioxygen
Change level.Meanwhile the alloy has good Castability and processing characteristics, 1050 DEG C of inferior forging molds are completely suitable for.
In alloy manufacturing process of the present invention, smelting uses vacuum induction melting foundry alloy, then under vacuo using mistake wax
Hot investment casting or sand casting process shaping.Casting is subsequently processed into mould, is directly used under as cast condition.
This alloy does not contain noble metal Hf, drastically reduce the area Ta constituent contents, have obvious relative to DM02 alloys
Cost advantage, while at 950-1050 DEG C with better antioxygenic property.Relative to K21 alloys, one side high temperature
Intensity is improved, and on the other hand because composition is optimized, reduces the cracking sensitivity during casting and use, has
More preferable performance.It is that a kind of price that can be used at 1050 DEG C is suitable, the high temperature alloy mold materials of excellent performance.
Details are as follows for the specific embodiment of the present invention：
Needed first using the qualified foundry alloy of vacuum induction melting composition, the process by fusing-refining-drop
Temperature-step of alloying-cast five is completed.In step is melted, nickel, cobalt, tungsten, chromium, carbon are directly loadable into crucible, change clear rear essence
Refining more than 30 minutes, strong agitation molten bath after refining, then have a power failure cooling conjunctiva, then is powered, and adds niobium, tantalum, aluminium, titanium elements,
Melting is stirred after 5 minutes, adds ferro-boron, zr element, is stirred after being further continued for melting 5 minutes, and have a power failure cooling.When molten bath temperature
After degree reaches pouring temperature, you can poured into a mould.
After foundry alloy composition is qualified, can in vaccum sensitive stove using lose wax hot investment casting or sand casting process into
Type, pour into the mould or part of formulation.
Using the above method, 5 stove the technology of the present invention alloys are smelted, composition is as shown in Figure 1.Wherein 1050 DEG C of mechanical property
Can be as shown in Figure 2.
Can be seen that from the result of these embodiments, according to present invention provide that the nickel-base alloy that is produced of composition range,
Final finished obtains higher tensile strength at 1050 DEG C, good plasticity, good antioxygenic property, is before one kind has very much
The high temperature alloy mold materials on way.
Although the present invention is disclosed as above with preferred embodiment, so it is not limited to the present invention, any this area skill
Art personnel, without departing from the spirit and scope of the present invention, when a little modification and perfect, therefore the protection model of the present invention can be made
Enclose to work as and be defined by what claims were defined.
Claims (3)
1. a kind of die material cast Ni-base alloy, it is characterised in that the composition of the alloy includes：
C：0.10-0.18；
Co：9.0-12.0；
Al：5.0-6.0；
Cr：5.5-7.5；
W：13.0-15.0；
Nb：2.0-3.0；
Ta：0.75-1.75；
B：0.01-0.03；
Zr：0.03-0.15；
Ti：0.5-1.5；
Surplus is nickel；
Unit is percetage by weight.
2. die material cast Ni-base alloy as claimed in claim 1, it is characterised in that：The microscopic structure of the alloy is by Austria
Family name body γ matrixes form, and in mentioned component, W, Nb, Ta form high-melting-point element solid solution and strengthen matrix.
3. die material cast Ni-base alloy as claimed in claim 2, it is characterised in that：Al, Ti, Nb, Ta form γ ' phases
Strengthened, Nb, Ta and Ti can generate primary carbide, and C, B, Zr element carry out intercrystalline strengthening.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710828427.4A CN107630153A (en) | 2017-09-14 | 2017-09-14 | A kind of die material cast Ni-base alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710828427.4A CN107630153A (en) | 2017-09-14 | 2017-09-14 | A kind of die material cast Ni-base alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN107630153A true CN107630153A (en) | 2018-01-26 |
Family
ID=61099873
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710828427.4A Pending CN107630153A (en) | 2017-09-14 | 2017-09-14 | A kind of die material cast Ni-base alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN107630153A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109023347A (en) * | 2018-08-21 | 2018-12-18 | 西安国宏天易智能科技有限公司 | A kind of isothermal forging mold laser repair method |
| CN110951997A (en) * | 2019-12-23 | 2020-04-03 | 上海金甸机电设备成套有限公司 | Casting high-temperature alloy die material for 950-1050 ℃ isothermal forging |
| WO2021223759A1 (en) * | 2020-05-08 | 2021-11-11 | 华能国际电力股份有限公司 | High-strength and corrosion-resistant nickel-based polycrystalline high-temperature alloy and preparation method therefor |
| CN114032420A (en) * | 2021-11-10 | 2022-02-11 | 中国航发北京航空材料研究院 | High-performance cast high-temperature alloy |
| CN115287575A (en) * | 2022-07-21 | 2022-11-04 | 中国航发成都发动机有限公司 | Method for spraying high-bonding-strength coating by supersonic flame |
| CN115595469A (en) * | 2022-10-18 | 2023-01-13 | 深圳市钢昱碳晶科技有限公司（Cn） | Apparatus material contacting melt in refining aluminum alloy melt and manufacturing method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1079995A (en) * | 1993-01-06 | 1993-12-29 | 冶金工业部钢铁研究总院 | Heat and corrosion resistant cast nickel-base alloy |
| KR19980022301U (en) * | 1996-10-26 | 1998-07-15 | 양재신 | Vibration Reduction Device for Automobile Exhaust System |
| CN1570171A (en) * | 2003-03-24 | 2005-01-26 | 大同特殊钢株式会社 | Nickel base heat resistant cast alloy and turbine wheels made thereof |
| CN1718803A (en) * | 2005-07-15 | 2006-01-11 | 中国航空工业第一集团公司北京航空材料研究院 | Nickel base casting high temperature alloy for high temperature mould |
-
2017
- 2017-09-14 CN CN201710828427.4A patent/CN107630153A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1079995A (en) * | 1993-01-06 | 1993-12-29 | 冶金工业部钢铁研究总院 | Heat and corrosion resistant cast nickel-base alloy |
| KR19980022301U (en) * | 1996-10-26 | 1998-07-15 | 양재신 | Vibration Reduction Device for Automobile Exhaust System |
| CN1570171A (en) * | 2003-03-24 | 2005-01-26 | 大同特殊钢株式会社 | Nickel base heat resistant cast alloy and turbine wheels made thereof |
| CN1718803A (en) * | 2005-07-15 | 2006-01-11 | 中国航空工业第一集团公司北京航空材料研究院 | Nickel base casting high temperature alloy for high temperature mould |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109023347A (en) * | 2018-08-21 | 2018-12-18 | 西安国宏天易智能科技有限公司 | A kind of isothermal forging mold laser repair method |
| CN110951997A (en) * | 2019-12-23 | 2020-04-03 | 上海金甸机电设备成套有限公司 | Casting high-temperature alloy die material for 950-1050 ℃ isothermal forging |
| WO2021223759A1 (en) * | 2020-05-08 | 2021-11-11 | 华能国际电力股份有限公司 | High-strength and corrosion-resistant nickel-based polycrystalline high-temperature alloy and preparation method therefor |
| CN114032420A (en) * | 2021-11-10 | 2022-02-11 | 中国航发北京航空材料研究院 | High-performance cast high-temperature alloy |
| CN114032420B (en) * | 2021-11-10 | 2023-03-14 | 中国航发北京航空材料研究院 | High-performance cast high-temperature alloy |
| CN115287575A (en) * | 2022-07-21 | 2022-11-04 | 中国航发成都发动机有限公司 | Method for spraying high-bonding-strength coating by supersonic flame |
| CN115595469A (en) * | 2022-10-18 | 2023-01-13 | 深圳市钢昱碳晶科技有限公司（Cn） | Apparatus material contacting melt in refining aluminum alloy melt and manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107630153A (en) | A kind of die material cast Ni-base alloy | |
| CN111235434B (en) | Preparation method of nickel-based deformed superalloy wheel disc forging used at high temperature | |
| JP5869034B2 (en) | Nickel superalloys and parts made from nickel superalloys | |
| CN106636707B (en) | A kind of smelting process of nickel base superalloy GH4720Li | |
| JP5478601B2 (en) | Ni-based forged alloy and gas turbine using the same | |
| CN100396806C (en) | Nickel base casting high temperature alloy for high temperature mould | |
| CN104630597B (en) | A kind of iron nickel and chromium high temperature alloy and its manufacture method | |
| CN108384992A (en) | A kind of high-strength corrosion-resisting nickel base superalloy and its manufacturing method | |
| CN105268973A (en) | Additive manufacturing method for functional material part based on TiNi memory alloy wire | |
| CN110512116A (en) | A kind of high Nb-TiAl intermetallic compound of multicomponent high-alloying | |
| CN108385010A (en) | A kind of cobalt base superalloy and preparation method thereof of low-density, high structure stability | |
| CN106676299B (en) | A kind of method of raising GH4720Li alloy W elemental composition uniformities | |
| CN115821117B (en) | GH4141 high-temperature alloy and preparation method thereof | |
| CN105695799A (en) | High-temperature structural material of Ti-Al-Nb series intermetallic compound | |
| CN105543568B (en) | A kind of platiniferous non-rhenium nickel base single crystal superalloy and its preparation method and application | |
| CN110268078A (en) | High temperature resistant to damage superalloy, the product manufactured by the alloy and the method for manufacturing the alloy | |
| JP2019537665A (en) | Titanium-free superalloys, powders, methods and components | |
| CN114082876A (en) | High-temperature-resistance and high-durability alloy turbine disc forging and preparation method thereof | |
| CN109022923A (en) | A kind of alloying component and preparation method thereof of low cobalt high temperature alloy charging turbine | |
| CN108531773A (en) | A kind of Ti3Al intermetallic compound high-temperature structural materials | |
| CN105483446A (en) | Method for vacuum smelting and casting for Mar-M246 alloy | |
| CN108950273A (en) | A kind of intermediate alloy and its preparation method and application | |
| CN109554580A (en) | A kind of nickel-base alloy, preparation method and manufacture article | |
| CN106191527B (en) | Nickel-base alloy and the article formed by alloy | |
| CN109554579A (en) | A kind of nickel-base alloy, preparation method and manufacture article |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20180126 |
|
| RJ01 | Rejection of invention patent application after publication |