CN106282670A - A kind of nickel base superalloy and preparation method thereof - Google Patents
A kind of nickel base superalloy and preparation method thereof Download PDFInfo
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Abstract
The invention provides a kind of nickel base superalloy and preparation method thereof, a kind of powder metallurgical nickel alloy without element nb, and thus obtained manufacture article, composition includes by mass percentage: Co:12.5～13.5%, Cr:13.75～14.25%, Al:2.8～3.2%, Ti:3.8～4.2%, W:3.75～4.25%, Mo:3.75～4.25%, Ta:2.8～3.2%, Hf:0.17～0.23%, C:0.04～0.06%, B:0.003～0.015%, Zr:0.03～0.07%, surplus is Ni.The high temperature alloy of present invention design has more preferable structure stability and elevated temperature strength, and alloy temperature capability improves further.
Description
Technical field
The present invention relates to technical field of high temperature alloy, particularly relate to a kind of nickel base superalloy and
Preparation method.
Background technology
As a rule, high temperature alloy refers to can grow more than 600 DEG C and under certain stress condition
The high temperature metallic material of phase work, has the elevated temperature strength of excellence, good antioxidation and heat resistanceheat resistant
Corrosive nature, the combination property such as good fatigue behaviour, fracture toughness.High speed along with industry
Development, high temperature alloy has shown good application prospect in every field, is mainly used in system
Make the turbo blade of gas-turbine unit, guide vane, the turbine disk, high-pressure compressor dish and
The high-temperature components such as combustor.
High-temperature alloy material can be divided into wrought superalloy, cast superalloy according to preparation technology
And powder metallurgy high-temperature alloy.High-temperature alloy material can be divided mainly into iron-based high temp by matrix element
Alloy, nickel base superalloy and cobalt base superalloy.Owing to iron-base superalloy tissue is the most steady
Determining non-oxidizability poor, elevated temperature strength is not enough, it is impossible to apply under the conditions of higher temperature, can only
Use under the conditions of moderate temperature (600～800 DEG C)；And cobalt is a kind of important strategic resource,
Most countries lacks cobalt in the world, to such an extent as to, the development of cobalt-base alloys receives the limit of cobalt resource
System.Thus, with nickel as matrix, the nickel base superalloy of (content is generally higher than 50%) becomes
At present most widely used in high temperature alloy, a class alloy that elevated temperature strength is the highest, it is 650～1000
The high temperature in the range of DEG C with intensity relatively and good non-oxidizability, resistance to combustion gas corrosion ability closes
Gold.Nickel base superalloy has plurality of advantages, and one is to dissolve more alloying element, and
Preferable stability can be kept；Two is to form the A3B type intermetallic compound that coherence is orderly
γ '-[Ni (Al, Ti)], as hardening constituent, makes effectively being strengthened of alloy, it is thus achieved that compare iron-based
High temperature alloy and the higher elevated temperature strength of cobalt base superalloy；Three is that the nickel-base alloy containing chromium has
Antioxidation more more preferable than iron-base superalloy and resistance to combustion gas corrosion ability, generally they can be containing ten
Multiple element, and Cr acts primarily as antioxidation and anticorrosive effect, other elements act primarily as strengthening and make
With.
Although powder metallurgy high-temperature alloy have passed through the development course of three generations, first generation feature is high
Intensity, such as Wasploy, Astraloy, FGH97 etc., the second filial generation will improve resistant to damage tolerance limit energy
Power becomes development priority, such as Rene88 (DT), U720Li, FGH96 etc., sending out of the third generation
Open up to merge excellent elevated temperature strength and resistant to damage tolerance limit ability as emphasis, as ME3,
RR1000 etc., but the crucial hot-end component of modern gas turbine engines requires its Ni-based height
Temperature alloy has the performances such as long-term high temperature microstructure stability, resisting fatigue, corrosion-resistant and antioxidation,
And nickel base superalloy during high temperature long service in fatigue strength, yield strength and pole
The limit mechanical property aspect such as tensile strength all there will be and is decreased obviously.
How to improve stability and the mechanical behavior under high temperature of the nickel-base alloy of high temperature long service, be
Key issue the most urgently to be resolved hurrily.
Summary of the invention
The technical problem to be solved in the present invention is to provide a kind of nickel base superalloy and preparation thereof
Method, a kind of metallurgical nickel alloy without element nb.The Ni-based height that the present invention provides
Temperature alloy, under conditions of long term high temperature, has preferable stability and high temperature temperature capability.
The invention provides a kind of high temperature alloy, it is characterised in that form bag by mass percentage
Include:
Co:12.5～13.5%；
Cr:13.75～14.25%；
Al:2.8～3.2%；
Ti:3.8～4.2%；
W:3.75～4.25%；
Mo:3.75～4.25%；
Ta:2.8～3.2%；
Hf:0.17～0.23%；
C:0.04～0.06%；
B:0.003～0.015%；
Zr:0.03～0.07%；
Surplus is Ni.
Preferably, including 12.7～the Co of 13.2%.
Preferably, including 13.85～the Cr of 14.15%.
Preferably, including 2.9～the Al of 3.1%.
Preferably, including 3.9～the Ti of 4.1%.
Preferably, including 3.85～the W of 4.15%.
Preferably, including 3.85～the Mo of 4.15%.
Preferably, including 2.9～the Ta of 3.1%.
Preferably, including 0.18～the Hf of 0.22%.
The invention provides a kind of high temperature alloy, it is characterised in that form bag by mass percentage
Include:
Co:13%；
Cr:14%；
Al:3.0%；
Ti:4.0%；
W:4.0%；
Mo:4.0%；
Ta:3.0%；
Hf:0.2%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
Present invention also offers a kind of high temperature alloy, it is characterised in that form by mass percentage
Including:
Co:13%；
Cr:14.1%；
Al:3.05%；
Ti:3.95%；
W:3.9%；
Mo:4.1%；
Ta:3.05%；
Hf:0.19%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
The invention provides a kind of article, it is characterised in that described article are sent out for gas turbine
Motivation, and forming by mass percentage, comprises the high temperature alloy formed by following element:
Co:12.5～13.5%；
Cr:13.75～14.25%；
Al:2.8～3.2%；
Ti:3.8～4.2%；
W:3.75～4.25%；
Mo:3.75～4.25%；
Ta:2.8～3.2%；
Hf:0.17～0.23%；
C:0.04～0.06%；
B:0.003～0.015%；
Zr:0.03～0.07%；
Surplus is Ni.
Preferably, including 12.7～the Co of 13.2%.
Preferably, including 13.85～the Cr of 14.15%.
Preferably, including 2.9～the Al of 3.1%.
Preferably, including 3.9～the Ti of 4.1%.
Preferably, including 3.85～the W of 4.15%.
Preferably, including 3.85～the Mo of 4.15%.
Preferably, including 2.9～the Ta of 3.1%.
Preferably, including 0.18～the Hf of 0.22%.
Preferably, described article are for the hot-end component of gas-turbine unit.
The invention provides a kind of article, it is characterised in that described article are sent out for gas turbine
Motivation, and forming by mass percentage, comprises the high temperature alloy formed by following element:
Co:13%；
Cr:14%；
Al:3.0%；
Ti:4.0%；
W:4.0%；
Mo:4.0%；
Ta:3.0%；
Hf:0.2%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
Preferably, described article are for the hot-end component of gas-turbine unit.
Present invention also offers a kind of article, it is characterised in that described article are used for gas turbine
Electromotor, and forming by mass percentage, comprises the high temperature alloy formed by following element:
Co:13%；
Cr:14.1%；
Al:3.05%；
Ti:3.95%；
W:3.9%；
Mo:4.1%；
Ta:3.05%；
Hf:0.19%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
Preferably, described article are for the hot-end component of gas-turbine unit.
One nickel base superalloy of the present invention and preparation method thereof, especially a kind of powder is without unit
The metallurgical nickel alloy of element Nb, and thus obtained manufacture article, form by mass percentage
Including: Co:12.5～13.5%, Cr:13.75～14.25%, Al:2.8～3.2%, Ti:3.8～4.2%,
W:3.75～4.25%, Mo:3.75～4.25%, Ta:2.8～3.2%, Hf:0.17～0.23%,
C:0.04～0.06%, B:0.003～0.015%, Zr:0.03～0.07%, surplus is Ni.With
Prior art is compared, and the present invention passes through substitute element Nb, and improves the addition of Ta element,
Improve the threshold value that TCP phase is formed, thus reduce high-temperature alloy material and take for a long time at high temperature
Precipitation ability during labour, improves materials microstructure stability.By adding alloying element Hf
Improve the stability of γ ' phase.And, element Hf not only can enter in γ ', MC with γ phase and improve
Its stability, also can be combined with oxygen, purifies crystal boundary, element Hf or strong carbide forms unit
Element, can form more stable carbide in powder particle, effectively improve primary granule border
(PPB) precipitation, thus fundamentally, solve the nickel base superalloy of high temperature long service,
The TCP phase (topology solid matter phase, as equal in sigma phase, μ) produced has a strong impact on alloy material
The problem of the fatigue behaviour of material, and during high-temperature service, the roughening of γ ' phase also can reduce alloy
The yield strength of material and the phenomenon of ultimate tensile strength.Test result indicate that, its indices
Existing high temperature alloy, the most existing powder metallurgy high-temperature alloy, its alloy can be better than
Temperature capability improves about 30 DEG C than second filial generation powder metallurgy high-temperature alloy.
Accompanying drawing explanation
Fig. 1 is the high temperature alloy CSU-A2 in the embodiment of the present invention 1 and the second filial generation, the third generation
The γ ' of typical powder metallurgy high-temperature alloy is completely dissolved temperature comparisons's figure mutually；
Fig. 2 is the high temperature alloy CSU-A2 in the embodiment of the present invention 1 and the second filial generation, the third generation
γ ' the molal volume mark comparison diagram of typical powder metallurgy high-temperature alloy；
Fig. 3 is the high temperature alloy CSU-A2 in the embodiment of the present invention 1 and the second filial generation, the third generation
The maximum molal volume mark comparison diagram of sigma phase of typical powder metallurgy high-temperature alloy.
Detailed description of the invention
In order to further appreciate that the present invention, below in conjunction with embodiment to the present invention side of being preferable to carry out
Case is described, but it is to be understood that these describe is simply the spy further illustrating the present invention
Advantage of seeking peace rather than the restriction to patent requirements of the present invention.
The present invention is raw materials used, and its source is not particularly limited, that commercially buy or
Prepare according to preparation method well known to those skilled in the art.
High temperature alloy of the present invention and the article of preparation thereof, to its preparation method and other raw material
Source be not particularly limited, prepare according to preparation method well known to those skilled in the art
Or commercially buy.
The invention discloses a kind of high temperature alloy, it is characterised in that form bag by mass percentage
Include:
Co:12.5～13.5%；
Cr:13.75～14.25%；
Al:2.8～3.2%；
Ti:3.8～4.2%；
W:3.75～4.25%；
Mo:3.75～4.25%；
Ta:2.8～3.2%；
Hf:0.17～0.23%；
C:0.04～0.06%；
B:0.003～0.015%；
Zr:0.03～0.07%；
Surplus is Ni.
The high temperature alloy that the present invention provides, a kind of powder metallurgical nickel alloy without element nb,
The present invention uses element T a to replace element nb, forms by mass percentage, described element T a
Mass percentage content be preferably 2.8～3.2%, more preferably 2.9～3.1%, more preferably
2.95～3.05%, most preferably 3.0%；The source of element T a is not particularly limited by the present invention,
Source or commercially available element T a with element T a well known to those skilled in the art；This
The bright purity to element T a is not particularly limited, with well known to those skilled in the art for preparing
The purity of element T a of high temperature alloy.
The present invention replaces element nb to improve the threshold that TCP phase is formed by using element T a
Value, and content is improved to 2.8～3.2%, thus it is long-time at high temperature to reduce high-temperature alloy material
Precipitation ability during military service, improves materials microstructure stability, puies forward heavy alloyed anti-crack
Extended capability.
Forming by mass percentage, the mass percentage content of described element Cr is preferably
13.75～14.25%, more preferably 13.85～14.25%, more preferably 13.85～14.15%, more
It is preferably 13.95～14.05%, most preferably 14%；The source of element Cr is not had by the present invention
It is particularly limited to, with source or the commercially available element Cr of element Cr well known to those skilled in the art
?；The purity of element Cr is not particularly limited by the present invention, knows with those skilled in the art
The purity of element Cr for preparing high temperature alloy.
The present invention is to balance each element ratio in alloy further, reduces containing of element Cr
Amount.
Forming by mass percentage, the mass percentage content of described element Hf is preferably
0.17～0.23%, more preferably 0.18～0.22%, more preferably 0.19～0.21%, most preferably
0.20%；The source of element Hf is not particularly limited by the present invention, ripe with those skilled in the art
The source of the element Hf known or commercially available element Hf；The present invention purity to element Hf
It is not particularly limited, with the element Hf for preparing high temperature alloy well known to those skilled in the art
Purity.
The present invention, in described high temperature alloy, adds alloying element Hf and improves the stability of γ ' phase,
Element Hf not only can enter and improve its stability in γ ', MC with γ phase, also can be combined with oxygen,
Purify crystal boundary, and Hf is carbide, can be formed more steady in powder particle
Fixed carbide, is to improve the effective way that primary granule border (PPB) separates out, thus has
Imitate puies forward heavy alloyed elevated temperature strength and resistance to crack extension ability.
Forming by mass percentage, the mass percentage content of described element al is preferably
2.8～3.2%, more preferably 2.85～3.15%, more preferably 2.9～3.1%, more preferably
2.95～3.05%, most preferably 3.0%；The source of element al is not particularly limited by the present invention,
Source or commercially available element al with element al well known to those skilled in the art；This
The bright purity to element al is not particularly limited, with well known to those skilled in the art for preparing
The purity of the element al of high temperature alloy.
Forming by mass percentage, the mass percentage content of described element ti is preferably
3.8～4.2%, more preferably 3.85～4.15%, more preferably 3.9～4.1%, more preferably
3.95～4.05%, most preferably 4.0%；The source of element ti is not particularly limited by the present invention,
Source or commercially available element ti with element ti well known to those skilled in the art；This
The bright purity to element ti is not particularly limited, with well known to those skilled in the art for preparing
The purity of the element ti of high temperature alloy.
Forming by mass percentage, the mass percentage content of described element W is preferably
3.75～4.25%, more preferably 3.85～4.15%, more preferably 3.88～4.13%, more preferably
3.95～4.05%, most preferably 4.0%；The source of element W is not particularly limited by the present invention,
Source or commercially available element W with element W well known to those skilled in the art；This
The bright purity to element W is not particularly limited, with well known to those skilled in the art for preparing
The purity of the element W of high temperature alloy.
Forming by mass percentage, the mass percentage content of described elements Mo is preferably
3.75～4.25%, more preferably 3.85～4.15%, more preferably 3.88～4.13%, more preferably
3.95～4.05%, most preferably 4.0%；The source of elements Mo is not particularly limited by the present invention,
Source or commercially available elements Mo with elements Mo well known to those skilled in the art；This
Invent and the purity of elements Mo be not particularly limited, with well known to those skilled in the art for
Prepare the purity of the elements Mo of high temperature alloy.
Forming by mass percentage, the mass percentage content of described Elements C o is preferably
12.5～13.5%, more preferably 12.6～13.4%, more preferably 12.7～13.3%, more preferably
12.8～13.2%, most preferably 13%；The source of Elements C o is not particularly limited by the present invention,
Source or commercially available Elements C o with Elements C o well known to those skilled in the art；This
The bright purity to Elements C o is not particularly limited, with well known to those skilled in the art for making
The purity of Elements C o of standby high temperature alloy.
Forming by mass percentage, the mass percentage content of described Elements C is preferably
0.04～0.06%, more preferably 0.042～0.057%, more preferably 0.045～0.055%, more excellent
Elect 0.047～0.053%, most preferably 0.05% as；The present invention does not has spy to the source of Elements C
Do not limit, with source or the commercially available Elements C of Elements C well known to those skilled in the art；
The purity of Elements C is not particularly limited by the present invention, with well known to those skilled in the art for
Prepare the purity of the Elements C of high temperature alloy.
Forming by mass percentage, the mass percentage content of described element B is preferably
0.003～0.015%, more preferably 0.005～0.012%, more preferably 0.007～0.011%, more
It is preferably 0.008～0.01%, most preferably 0.009%；The source of element B is not had by the present invention
Being particularly limited to, source or commercially available element B with element B well known to those skilled in the art are
Can；The purity of element B is not particularly limited by the present invention, with well known to those skilled in the art
For preparing the purity of the element B of high temperature alloy.
Forming by mass percentage, the mass percentage content of described element Zr is preferably
0.03～0.07%, more preferably 0.035～0.065%, more preferably 0.04～0.06%, more preferably
It is 0.045～0.055%, most preferably 0.05%；The present invention is the most special to the source of element Zr
Limit, with source or the commercially available element Zr of element Zr well known to those skilled in the art；
The purity of element Zr is not particularly limited by the present invention, with well known to those skilled in the art for
Prepare the purity of the element Zr of high temperature alloy.
The source of element Ni is not particularly limited by the present invention, knows with those skilled in the art
The source of element Ni or commercially available element Ni；The purity of element Ni is not had by the present invention
Limit especially, pure with the element Ni for preparing high temperature alloy well known to those skilled in the art
Spend.
The present invention provides a kind of high temperature alloy, it is characterised in that composition includes by mass percentage:
Co:13%；
Cr:14%；
Al:3.0%；
Ti:4.0%；
W:4.0%；
Mo:4.0%；
Ta:3.0%；
Hf:0.2%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
The above-mentioned powder metallurgy high-temperature alloy without element nb that the present invention provides, uses element
Ta replaces element nb, and improves the addition of Ta element to about 3%, reduces simultaneously
The content of Cr is to about 14wt%, and with the addition of the element Hf of about 0.2wt%.After testing,
Comparing the second filial generation powder metallurgy high-temperature alloy Rene88, U720Li, FGH96, it is mainly strengthened
Phase γ ' phase to be completely dissolved temperature and percent by volume high, meanwhile, the analysis of harmful phase sigma phase
Going out temperature to improve and weight percent content reduction, the high temperature microstructure thereby increasing alloy is stable
Property and intensity, improve the precipitation strength ability of alloy.
The present invention also provides for a kind of high temperature alloy, it is characterised in that form bag by mass percentage
Include:
Co:13%；
Cr:14.1%；
Al:3.05%；
Ti:3.95%；
W:3.9%；
Mo:4.1%；
Ta:3.05%；
Hf:0.19%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
The described powder metallurgy high temperature nickel alloy without element nb that the present invention provides, relative the
Secondary powder metallurgy high-temperature alloy has more preferable structure stability and elevated temperature strength, and alloy holds temperature
Can improve further by force rate second filial generation powder metallurgy high-temperature alloy.
The present invention provides a kind of article, it is characterised in that described article start for gas turbine
Machine, and forming by mass percentage, comprises the high temperature alloy formed by following element:
Co:12.5～13.5%；
Cr:13.75～14.25%；
Al:2.8～3.2%；
Ti:3.8～4.2%；
W:3.75～4.25%；
Mo:3.75～4.25%；
Ta:2.8～3.2%；
Hf:0.17～0.23%；
C:0.04～0.06%；
B:0.003～0.015%；
Zr:0.03～0.07%；
Surplus is Ni.
In article of the present invention, the element preferred version in the high temperature alloy comprised and aforementioned height
Element preferred version in temperature alloy is identical, and this is no longer going to repeat them；Article of the present invention
It is preferred for gas-turbine unit, is more preferably used for the hot-end component of gas-turbine unit,
It is most preferably for the high-pressure turbine dish of gas-turbine unit.Described gas turbine is sent out by the present invention
The model of motivation is not particularly limited, with employing high temperature alloy well known to those skilled in the art
Model；Other conditions of described gas-turbine unit are not particularly limited by the present invention,
Normal condition with gas-turbine unit well known to those skilled in the art.
High temperature alloy without element nb of the present invention, as gas-turbine unit
High-temperature material, be particularly well-suited to the Ni based powder metallurgy high temperature alloy of crucial hot-end component, with
And the associated materials that thus manufactures and component thereof, high temperature alloy of the present invention is relative to second filial generation powder
End metallurgy high temperature alloy has more preferable structure stability and elevated temperature strength, alloy temperature capability ratio
Second filial generation powder metallurgy high-temperature alloy improves further, carries than second filial generation powder metallurgy high-temperature alloy
High about 30 DEG C.
The present invention is to improve the high-temperature mechanics strength and stability of high temperature alloy further, also provides for
It is additionally useful for manufacturing gas-turbine unit, particularly manufactures the concrete skill of crucial hot-end component
Art scheme, including,
The present invention provides a kind of article, it is characterised in that described article start for gas turbine
Machine, and form by mass percentage, comprise the high temperature alloy formed by following element: Co:13%,
Cr:14%, Al:3.0%, Ti:4.0%, W:4.0%, Mo:4.0%, Ta:3.0%,
Hf:0.2%, C:0.05%, B:0.009%, Zr:0.05%, surplus is Ni.
And the present invention also provides for a kind of article, it is characterised in that described article are used for combustion gas whirlpool
Turbine, and forming by mass percentage, comprises the high temperature alloy formed by following element:
Co:13%, Cr:14.1%, Al:3.05%, Ti:3.95%, W:3.9%, Mo:4.1%,
Ta:3.05%, Hf:0.19%, C:0.05%, B:0.009%, Zr:0.05%, surplus
For Ni.
Nickel base superalloy that the present invention provides and preparation method thereof, especially a kind of powder does not contains
The metallurgical nickel base superalloy of element nb, and the gas-turbine unit thus prepared, special
It not the crucial hot-end component of gas-turbine unit, be powder metallurgy for primary granule border
One of big defect of the three of high temperature alloy, corresponding powder injection molding and structure stability directly determine to close
The high-temperature behavior of gold and the problem in the life-span of component, and the typical case in powder metallurgy high-temperature alloy
Harmful phase (as equal in sigma phase, μ) is material and component easily produces during long service
One of raw fatigue crack principal element causing inefficacy, strengthening based on powder metallurgy high-temperature alloy
Mode is mainly solution strengthening mode and precipitation strength mode.
The present invention use element T a replace element nb to improve the threshold value that TCP phase is formed,
Thus reduce high-temperature alloy material precipitation ability during high temperature is on active service for a long time, improve
The resistance to crack extension ability of alloy.Addition element Hf can improve precipitation strength principal element γ ' phase
Stability, reduce the formation on primary granule border, thus put forward heavy alloyed high-temperature behavior.Should
By advanced alloy design method, give full play to the effect of precipitation strength, reduce the shape of harmful phase
Become tendency, existence range and content, reduce the content of element Cr, balance each intensified element
W, Mo, Al, Ti content in the alloy, through screening, devises containing element T a, adds
The powder metallurgy high temperature nickel alloy without element nb of Hf, test result indicate that, its every finger
Mark is better than typical second filial generation powder metallurgy high-temperature alloy, and its alloy temperature capability is than second filial generation powder
End metallurgy high temperature alloy improves about 30 DEG C.Use the high temperature alloy designed by the present invention, preparation
Article, especially prepare gas-turbine unit, particularly prepare its crucial hot-end component, all have
There are preferable mechanical property and the structure stability of high temperature long service, and preferably anti-crack
Extended capability.
In order to further illustrate the present invention, below in conjunction with embodiment, offer of the present invention is not contained unit
The powder metallurgy high temperature nickel alloy of element Nb is described in detail.
Embodiment 1
Its source, to raw materials used in embodiment, is not particularly limited, commercially by the present invention
Buy or prepare according to preparation method well known to those skilled in the art.
The system of the present invention powder metallurgy high temperature nickel alloy to not containing element nb described in embodiment
The source of Preparation Method and other raw material is not particularly limited, according to well known to those skilled in the art
Preparation method prepares or commercially buys.
The present invention prepares powder metallurgy high temperature nickel alloy according to certain alloying component proportioning
CSU-A2, and become with the existing typical second filial generation, third generation powder metallurgy high-temperature alloy
Dividing contrast, comparing result, see table 1, table 1 is that the high temperature that the embodiment of the present invention 1 obtains closes
Gold and the second filial generation, the composition contrast of third generation typical powder metallurgy high temperature alloy.
The high temperature alloy that table 1 embodiment 1 obtains and the second filial generation, third generation typical powder
The composition contrast of metallurgy high temperature alloy
| CSU-A2 | FGH96 | FGH98I | Rene88(DT) | U720Li | RR1000 | ME3 | |
| Ni | Surplus | Surplus | Surplus | Surplus | Surplus | Surplus | Surplus |
| Co | 13 | 13 | 20.83 | 13 | 15 | 18.5 | 18.2 |
| Cr | 14 | 16 | 12.92 | 16 | 16 | 15 | 13.1 |
| Al | 3.0 | 2.2 | 2.64 | 2.1 | 2.5 | 3.0 | 3.5 |
| Ti | 4.0 | 3.7 | 3.53 | 3.7 | 5.0 | 3.6 | 3.5 |
| W | 4.0 | 4.0 | 3.85 | 4.0 | 1.25 | 0 | 1.9 |
| Mo | 4.0 | 4.0 | 4.0 | 4.0 | 3.0 | 5.0 | 3.8 |
| Ta | 3.0 | 0.02 | 1.65 | 0 | 0 | 2.0 | 2.7 |
| Nb | 0 | 0.8 | 1.51 | 0.75(0.7) | 0 | 1.1 | 1.4 |
| Hf | 0.2 | 0 | 0.2 | 0 | 0 | 0.5 | 0 |
| C | 0.05 | 0.03 | 0.048 | 0.04(0.03) | 0.025 | 0.027 | 0.03 |
| B | 0.009 | 0.01 | 0.027 | 0.02(0.015) | 0.018 | 0.015 | 0.03 |
| Zr | 0.05 | 0.04 | 0.043 | 0.04(0.03) | 0.05 | 0.06 | 0.05 |
As it can be seen from table 1 the alloy CSU-A2 of present invention design and second filial generation powder metallurgy
High temperature alloy compares and has the feature that substitute element Nb；Close with third generation powder metallurgy high temperature
Gold compares and has the feature that the mass percent about 50% that improve element T a, and increases
Element Hf.
High temperature alloy CSU-A2 and the second filial generation, third generation allusion quotation to the embodiment of the present invention 1 design
The powder metallurgy high-temperature alloy of type carries out performance detection.
Seeing Fig. 1, Fig. 1 is the high temperature alloy CSU-A2 and second in the embodiment of the present invention 1
Generation, the γ ' of the typical powder metallurgy high-temperature alloy of the third generation are completely dissolved temperature comparisons's figure mutually.
As shown in Figure 1, the high temperature alloy of embodiment 1 design, it is bright that its γ ' is completely dissolved temperature mutually
Aobvious higher than second filial generation powder metallurgy high-temperature alloy, suitable with the 3rd powder metallurgy high-temperature alloy.This
Show the high temperature alloy that the present invention designs High-Temperature Strengthening phase--the stability of γ ' phase is substantially better than
Secondary powder metallurgy high-temperature alloy, alloy high-temp intensity is significantly improved.
Seeing Fig. 2, Fig. 2 is the high temperature alloy CSU-A2 and second in the embodiment of the present invention 1
Generation, γ ' the molal volume mark comparison diagram of the typical powder metallurgy high-temperature alloy of the third generation.
As shown in Figure 2, the high temperature alloy of embodiment 1 design, its γ ' phase volume fraction ratio second
High for powder metallurgy high-temperature alloy FGH96, Rene88, U720Li and third generation powder metallurgy
Temperature alloy RR1000 is the highest, more lower slightly than third generation powder metallurgy high-temperature alloy ME3, and this shows,
The high temperature alloy precipitation strength ability of present invention design gets a promotion.
Seeing Fig. 3, Fig. 3 is the high temperature alloy CSU-A2 and second in the embodiment of the present invention 1
Generation, the maximum molal volume mark pair of sigma phase of the typical powder metallurgy high-temperature alloy of the third generation
Than figure.
From the figure 3, it may be seen that the high temperature alloy of embodiment 1 design, than third generation powder metallurgy high temperature
The maximum molal volume mark of the sigma phase of alloy substantially reduces, and this shows, present invention design
The harmful phase volume fraction of alloy substantially reduces, and improves the structure stability of alloy.
From above-mentioned testing result and explanation it can be seen that the embodiment of the present invention 1 design do not contain
The powder metallurgy high temperature nickel alloy of element nb, compares original secondary powder metallurgy high-temperature alloy,
Reduce the precipitation ability during high temperature is on active service for a long time, improve materials microstructure stability,
Improve the extended capability of anti-crack, improve elevated temperature strength, improve the stability of γ ' phase,
Decrease the formation on primary granule border, thus improve the high-temperature behavior of alloy, its every finger
Mark is better than typical second filial generation powder metallurgy high-temperature alloy.
As used herein, with odd number the unit that is described with word " " or " a kind of "
Element or step are interpreted as being not excluded for the element of plural form or step, unless clearly described so
Eliminating.It addition, mention that " the single embodiment " of the present invention should not be construed as eliminating and exist also
Other embodiments including described feature.
Above a kind of nickel base superalloy that the present invention provides and preparation method thereof is carried out in detail
Thin introduction, principle and the embodiment of the present invention are carried out by specific case used herein
Illustrating, the explanation of above example is only intended to help to understand that the method for the present invention and core thereof are thought
Think, including best mode, and also make any person skilled in the art can put into practice this
Invention, including manufacturing and using any device or system, and the method implementing any combination.Should
When pointing out, for those skilled in the art, without departing from the principle of the invention
On the premise of, it is also possible to the present invention is carried out some improvement and modification, and these improve and modify also
Fall in the protection domain of the claims in the present invention.The scope of patent protection of the present invention passes through right
Require limit, and those skilled in the art can be included it is conceivable that other embodiments.If
These other embodiments have the structural element being not different from claim character express, or
If they include the equivalent structural elements without essence difference of the character express with claim, that
These other embodiments also should comprise within the scope of the claims.
Claims (25)
1. a high temperature alloy, it is characterised in that composition includes by mass percentage:
Co:12.5～13.5%；
Cr:13.75～14.25%；
Al:2.8～3.2%；
Ti:3.8～4.2%；
W:3.75～4.25%；
Mo:3.75～4.25%；
Ta:2.8～3.2%；
Hf:0.17～0.23%；
C:0.04～0.06%；
B:0.003～0.015%；
Zr:0.03～0.07%；
Surplus is Ni.
High temperature alloy the most according to claim 1, it is characterised in that include 12.7～13.2%
Co.
High temperature alloy the most according to claim 1, it is characterised in that include
13.85～the Cr of 14.15%.
High temperature alloy the most according to claim 1, it is characterised in that include 2.9～3.1%
Al.
High temperature alloy the most according to claim 1, it is characterised in that include 3.9～4.1%
Ti.
High temperature alloy the most according to claim 1, it is characterised in that include 3.85～4.15%
W.
High temperature alloy the most according to claim 1, it is characterised in that include 3.85～4.15%
Mo.
High temperature alloy the most according to claim 1, it is characterised in that include 2.9～3.1%
Ta.
High temperature alloy the most according to claim 1, it is characterised in that include 0.18～0.22%
Hf.
10. a high temperature alloy, it is characterised in that composition includes by mass percentage:
Co:13%；
Cr:14%；
Al:3.0%；
Ti:4.0%；
W:4.0%；
Mo:4.0%；
Ta:3.0%；
Hf:0.2%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
11. 1 kinds of high temperature alloys, it is characterised in that composition includes by mass percentage:
Co:13%；
Cr:14.1%；
Al:3.05%；
Ti:3.95%；
W:3.9%；
Mo:4.1%；
Ta:3.05%；
Hf:0.19%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
12. 1 kinds of article, it is characterised in that described article are used for gas-turbine unit, and
Form by mass percentage, comprise the high temperature alloy formed by following element:
Co:12.5～13.5%；
Cr:13.75～14.25%；
Al:2.8～3.2%；
Ti:3.8～4.2%；
W:3.75～4.25%；
Mo:3.75～4.25%；
Ta:2.8～3.2%；
Hf:0.17～0.23%；
C:0.04～0.06%；
B:0.003～0.015%；
Zr:0.03～0.07%；
Surplus is Ni.
13. article according to claim 12, it is characterised in that include 12.7～13.2%
Co.
14. article according to claim 12, it is characterised in that include 13.85～14.15%
Cr.
15. article according to claim 12, it is characterised in that include 2.9～3.1%
Al.
16. article according to claim 12, it is characterised in that include 3.9～4.1%
Ti.
17. article according to claim 12, it is characterised in that include 3.85～4.15%
W.
18. article according to claim 12, it is characterised in that include 3.85～4.15%
Mo.
19. article according to claim 12, it is characterised in that include 2.9～3.1%
Ta.
20. article according to claim 12, it is characterised in that include 0.18～0.22%
Hf.
21. article according to claim 12, it is characterised in that described article are used for
The hot-end component of gas-turbine unit.
22. 1 kinds of article, it is characterised in that described article are used for gas-turbine unit, and
Form by mass percentage, comprise the high temperature alloy formed by following element:
Co:13%；
Cr:14%；
Al:3.0%；
Ti:4.0%；
W:4.0%；
Mo:4.0%；
Ta:3.0%；
Hf:0.2%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
23. article according to claim 22, it is characterised in that described article are used for
The hot-end component of gas-turbine unit.
24. 1 kinds of article, it is characterised in that described article are used for gas-turbine unit, and
Form by mass percentage, comprise the high temperature alloy formed by following element:
Co:13%；
Cr:14.1%；
Al:3.05%；
Ti:3.95%；
W:3.9%；
Mo:4.1%；
Ta:3.05%；
Hf:0.19%；
C:0.05%；
B:0.009%；
Zr:0.05%；
Surplus is Ni.
25. article according to claim 24, it is characterised in that described article are used for
The hot-end component of gas-turbine unit.
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2153845A (en) * | 1984-02-07 | 1985-08-29 | Inco Alloys Products Limited | Production of superalloy sheet |
| EP2769802A1 (en) * | 2013-02-22 | 2014-08-27 | Siemens Aktiengesellschaft | Improved welding material with regard to weldability and grain stabilisation, method and component |
| CN104120307A (en) * | 2013-04-23 | 2014-10-29 | 通用电气公司 | Cast nickel-based superalloy including iron |
-
2015
- 2015-06-12 CN CN201510322934.1A patent/CN106282670B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2153845A (en) * | 1984-02-07 | 1985-08-29 | Inco Alloys Products Limited | Production of superalloy sheet |
| EP2769802A1 (en) * | 2013-02-22 | 2014-08-27 | Siemens Aktiengesellschaft | Improved welding material with regard to weldability and grain stabilisation, method and component |
| CN104120307A (en) * | 2013-04-23 | 2014-10-29 | 通用电气公司 | Cast nickel-based superalloy including iron |
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