CN106636756A - Nickel-base superalloy and gas turbine engine part - Google Patents
Nickel-base superalloy and gas turbine engine part Download PDFInfo
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- CN106636756A CN106636756A CN201611146863.5A CN201611146863A CN106636756A CN 106636756 A CN106636756 A CN 106636756A CN 201611146863 A CN201611146863 A CN 201611146863A CN 106636756 A CN106636756 A CN 106636756A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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Abstract
The invention provides nickel-base superalloy. The nickel-base superalloy is composed of, by mass, 18-20% of Co, 13-15% of Cr, 2.9-3.5% of Al, 3.3-3.7% of Ti, 0.9-1.1% of Ta, 1.8-2.2% of W, 2.5-3.5% of Mo, 0.4-0.6% of Nb, 0.1-0.3% of Hf, 0.02-0.06% of C, 0.003-0.012% of B, 0.02-0.06% of Zr and the balance Ni and inevitable impurities. By optimizing elements of Al, Ti, Nb and Ta, the volume fraction of gamma' is increased, so that the precipitation capacity of harmful phases during the long-time service process at a high temperature of the superalloy material is lowered, and the structure stability of the material is improved. By adjusting the contents of W and Mo, the solution strengthening effect is improved, and the content of TCP phases is lowered. In addition, the contents of Hf and B of the alloy are adjusted, the content of Ta is increased, so that the stability of the gamma' phase and MC phase is improved, and precipitation of a previous particle boundary (PPB) is effectively improved. Accordingly, the harmful phase generation tendency of the nickel-base superalloy during high-temperature long-time service is well eliminated, and the fatigue performance of the alloy material is improved.
Description
Technical field
The present invention relates to technical field of high temperature alloy, more particularly to a kind of nickel base superalloy and gas-turbine unit portion
Part.
Background technology
In general, high temperature alloy refers to the high temperature gold for being capable of long-term work more than 600 DEG C and under certain stress condition
Category material, with excellent elevated temperature strength, good anti-oxidant and hot corrosion resistance, good fatigue behaviour, fracture toughness
Etc. combination property.With the high speed development of industry, high temperature alloy has shown good application prospect in every field, mainly
For manufacturing the high-temperature portion such as turbo blade, guide vane, the turbine disk, high-pressure compressor disk and combustion chamber of gas-turbine unit
Part.
High-temperature alloy material can be divided into wrought superalloy, cast superalloy and powder metallurgy high temperature according to preparation technology
Alloy.High-temperature alloy material can be divided mainly into iron-base superalloy, nickel base superalloy and cobalt base superalloy by matrix element.
Because iron-base superalloy tissue is not sufficiently stable, non-oxidizability is poor, and elevated temperature strength is poor, is not suitable under higher temperature conditions
(>800 DEG C) application, it is typically only capable to used below at 650 DEG C；And cobalt is a kind of important strategic resource, most of states in the world
The scarce cobalt of family so that the development of cobalt-base alloys is restricted.Thus, the Ni-based height of (content is generally higher than 50%) based on nickel
Temperature alloy becomes most widely used in a current high temperature alloy, with fastest developing speed class alloy. and it has in the range of 700-1100 DEG C
There is higher intensity and good non-oxidizability, resistance to combustion gas corrosion ability.Nickel base superalloy has many advantages, such as that one can be
The more alloying element of dissolving, and preferable stability can be kept；Two can be to form orderly L12 structural intermetallic compoundses
γ '-[Ni (Al, Ti, Ta)] makes effectively being strengthened for alloy as hardening constituent, obtains than iron-based, cobalt base superalloy
Higher elevated temperature strength；Three is that the nickel-base alloy containing chromium has more more preferable than iron-base superalloy anti-oxidant and resistance to combustion gas corrosion energy
Power, generally it can contain ten multiple elements, and Cr acts primarily as anti-oxidant and anticorrosive effect, and other elements act primarily as reinforcing and make
With.
Although nickel base superalloy has excellent high-temperature behavior such as：The performance such as antifatigue, corrosion-resistant and anti-oxidant, but
It is that the nickel-base alloy of high temperature long service can go out in terms of the mechanical properties such as fatigue strength, yield strength and ultimate tensile strength
Now it is decreased obviously.
Thus, the mechanical behavior under high temperature of the nickel-base alloy of high temperature long service how is improved, into key urgently to be resolved hurrily
Problem.
The content of the invention
The technical problem to be solved in the present invention is to provide a kind of nickel base superalloy and combustion turbine engine components, this
The nickel base superalloy for providing is invented under conditions of long term high temperature, with preferable mechanical property.
The purpose of the present invention is achieved through the following technical solutions：
A kind of nickel base superalloy, constitute includes by mass percentage：
Co：18-20%；Cr：13-15%；Al：2.9-3.5%；Ti：3.3-3.7%；Ta：0.9-1.1%；W：1.8-
2.2%；Mo：2.5-3.5%；Nb：0.4-0.6%；Hf：0.1-0.3%；C：0.02-0.06%；B：0.003-0.012%；
Zr：0.02-0.06%；Balance of Ni and inevitable impurity.
Preferably, the mass percent of the Co is specially 18.5-19.5%.
Preferably, the mass percent of the Cr is specially 13.5-14.5%.
Preferably, the mass percent of the Al is specially 3.0-3.4%.
Preferably, the mass percent of the Ti is specially 3.4-3.6%.
Preferably, the mass percent of the W is specially 1.9-2.1%.
Preferably, the mass percent of the Mo is specially 2.75-3.25%.
Preferably, the mass percent of the Nb is specially 0.45-0.55%.
Preferably, mass percent therein is specially：Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：
1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：0.2%；C：0.03%；B：0.006%；Zr：0.04%.
Preferably, mass percent therein is specially：Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：
1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：0.2%；C：0.05%；B：0.01%；Zr：0.04%.
A kind of combustion turbine engine components, the material of the part is that as described above a kind of arbitrary described nickel-base high-temperature is closed
Gold.
Nickel base superalloy in the present invention due to constitute by mass percentage including：Co：18-20%；Cr：13-15%；
Al：2.9-3.5%；Ti：3.3-3.7%；Ta：0.9-1.1%；W：1.8-2.2%；Mo：2.5-3.5%；Nb：0.4-0.6%；
Hf：0.1-0.3%；C：0.02-0.06%；B：0.003-0.012%；Zr：0.02-0.06%；Balance of Ni and inevitable
Impurity.Compared with prior art, the present invention improves materials microstructure stability, in particular improve γ ' phases, MC phases it is steady
It is qualitative. and it is effectively improved the precipitation of primary granule border (PPB)；Solving the nickel base superalloy of high temperature long service has
The problem of evil phase, improves the fatigue behaviour of alloy material.Test result indicate that, its indices can be better than existing high temperature
Alloy, especially existing powder metallurgy high-temperature alloy.Using the high temperature alloy designed by the present invention, the article of preparation, especially
Gas-turbine unit is prepared, its crucial hot-end component is particularly prepared, preferable mechanical property is respectively provided with and high temperature is taken for a long time
The structure stability of labour, and preferably alloy temperature capability.
Description of the drawings
Fig. 1 is the alloy 140 and the typical powder metallurgy high-temperature alloy of the second generation in the embodiment of the present invention at 850 DEG C
γ ' hardening constituent content balance figures；
Fig. 2 is that the alloy 140 in the embodiment of the present invention is mutually complete with the γ ' of the typical powder metallurgy high-temperature alloy of the second generation
Solution temperature comparison diagram；
Fig. 3 is the harmful phase σ phases of the alloy 140 in the embodiment of the present invention and the typical powder metallurgy high-temperature alloy of the second generation
Maximum molar content comparison diagram；
Fig. 4 is the solid-liquid phase line of the alloy 140 in the embodiment of the present invention and the typical powder metallurgy high-temperature alloy of the second generation
Difference comparison diagram.
Specific embodiment
It is right below in conjunction with the embodiment of the present invention to make purpose, technical scheme and the advantage of present invention enforcement clearer
Technical scheme is explicitly described, it is clear that described embodiment is a part of embodiment of the invention, rather than
Whole embodiments.Based on the embodiment in the present invention, those of ordinary skill in the art are not making creative work premise
Lower obtained every other embodiment, belongs to the scope of protection of the invention.
The present invention is raw materials used, it is originated and is not particularly limited, commercially buying or according to art technology
Preparation method is prepared known to personnel.
High temperature alloy of the present invention and its article of preparation, it is no special to the source of its preparation method and other raw materials
Limit, prepare according to preparation method well known to those skilled in the art or commercially buy.
Below in conjunction with the accompanying drawings the invention will be further described with preferred embodiment.
The embodiment of the invention discloses a kind of high temperature alloy, constitute includes by mass percentage：
Co：18～20%；Cr：13～15%；Al：2.9-3.5%；Ti：3.3～3.7%；Ta：0.9～1.1%；W：
1.8～2.2%；Mo：2.5～3.5%；Nb：0.4～0.6%；Hf：0.1～0.3%；C：0.02～0.06%；B：0.003～
0.012%；Zr：0.02～0.06%；Balance of Ni and inevitable impurity.
The embodiment of the present invention usually increases γ ' volume fractions by adopting optimization Al, Ti, Nb, Ta units, so as to reduce high temperature
The precipitation ability of harmful phase of the alloy material during high temperature long-time is on active service, improves materials microstructure stability.By adjusting
The content of whole W, Mo is improving solid solution strengthening effect and reduce TCP (topological Mi Dui phases) phase content.In addition, the alloy have adjusted unit
The content of plain Hf, B, and Ta contents are increased, so as to improve γ ' phases, the stability of MC phases, and it is effectively improved primary granule side
The precipitation on boundary (PPB)；Therefore the tendency that nickel base superalloy after high temperature long service produces harmful phase is reduced, alloy is improved
The problem of the fatigue behaviour of material.Test result indicate that, its indices can be better than existing high temperature alloy, especially existing
Powder metallurgy high-temperature alloy.Using the high temperature alloy designed by the present invention, the article of preparation, especially prepare gas turbine and start
Machine, particularly prepares its crucial hot-end component, is respectively provided with the structure stability of preferable mechanical property and high temperature long service, with
And preferable alloy temperature capability.
High temperature alloy provided in an embodiment of the present invention, i.e., a kind of powder metallurgy nickel alloy, constitutes by mass percentage, described
The mass percentage content of element nb is preferably 0.45～0.55%, and the present embodiment is preferably 0.5%, naturally it is also possible to be
0.4%, or 0.6%；The present invention is not particularly limited to the source of element nb, with element nb well known to those skilled in the art
Source or commercially available element nb；The present invention is not particularly limited to the purity of element nb, is known with those skilled in the art
The purity for preparing the element nb of high temperature alloy.
The embodiment of the present invention is by improving the door that TCP phases (topological Mi Dui phases) are formed using 0.4～0.5% element nb
Threshold value, so as to reduce precipitation of the TCP phases during high temperature long-time is on active service, improves materials microstructure stability.
Constitute by mass percentage, the mass percentage content of Elements C o is preferably 18.5～19.5%, this enforcement
Example is preferably 19%, naturally it is also possible to for 18%, or for 20%；The present invention is not particularly limited to the source of Elements C o, with this
The source of Elements C o known to art personnel or commercially available Elements C o；The present invention is to the purity of Elements C o without special
Limit, with the purity for preparing Elements C o of high temperature alloy well known to those skilled in the art.
The embodiment of the present invention adjusts the solid solubility temperature of γ ' by the content of optimization Elements C o.
Constitute by mass percentage, the mass percentage content of the element Hf is preferably 0.1～0.3%, the present embodiment
Preferably 0.20%, naturally it is also possible to for 0.1%, or for 0.3%；The present invention is not particularly limited to the source of element Hf, with
The source of element Hf well known to those skilled in the art or commercially available element Hf；The present invention is to the purity of element Hf without spy
Do not limit, with the purity for preparing the element Hf of high temperature alloy well known to those skilled in the art.
In the high temperature alloy, alloying element Hf improves the stability of γ ' phases to the embodiment of the present invention, and element Hf not only may be used
Into γ ', MC can also be entered, more stable carbide can be formed in powder particle, be to improve primary granule border (PPB) analysis
The effective way for going out.
Constitute by mass percentage, the mass percentage content of the element al is preferably 3.0～3.4%, more preferably
3.1～3.3%, the present embodiment is preferably 3.2%, naturally it is also possible to for 2.9%, or for 3.5%；The present invention comes to element al
Source is not particularly limited, with the source of element al well known to those skilled in the art or commercially available element al；The present invention is right
The purity of element al is not particularly limited, with the purity for preparing the element al of high temperature alloy well known to those skilled in the art
.
Constitute by mass percentage, the mass percentage content of the element ti is preferably 3.4～3.6%, the present embodiment
Preferably 3.5%, naturally it is also possible to for 3.3%, or for 3.7%；The present invention is not particularly limited to the source of element ti, with this
The source of element ti known to art personnel or commercially available element ti；The present invention is to the purity of element ti without special
Limit, with the purity for preparing the element ti of high temperature alloy well known to those skilled in the art.
The embodiment of the present invention adjusts the form and volume of γ ' phases in the high temperature alloy by optimizing Al, Ti, Nb
Fraction, is effectively increased mechanical property, the temperature capability of increase alloy of the alloy during high-temperature service.
Constitute by mass percentage, the mass percentage content of element T a is preferably 0.9～1.1%, the present embodiment
Preferably 1.0%, naturally it is also possible to for 0.9%, or 1.1%；The present invention is not particularly limited to the source of element T a, with ability
The source of element T a known to field technique personnel or commercially available element T a；The present invention is to the purity of element T a without especially limit
System, with the purity for preparing the Ta of high temperature alloy well known to those skilled in the art.
The embodiment of the present invention increases γ ' volume fractions, and stable γ ' phases by increasing Ta in the high temperature alloy,
So as to improve alloying element elevated temperature strength.
Constitute by mass percentage, the mass percentage content of the element W is preferably 1.8～2.2%, more preferably
1.9～2.10%, the present embodiment is preferably 2.0%, naturally it is also possible to for 1.8%, or 2.2%；Source of the present invention to element W
It is not particularly limited, with the source of element W well known to those skilled in the art or commercially available element W；The present invention is to element W
Purity be not particularly limited, with the purity for preparing the element W of high temperature alloy well known to those skilled in the art.
Constitute by mass percentage, the mass percentage content of the elements Mo is preferably 2.5～3.5%, more preferably
2.75～3.25%, the present embodiment is preferably 3.0%, naturally it is also possible to for 2.5%.Or 3.5%；The present invention comes to elements Mo
Source is not particularly limited, with the source of elements Mo well known to those skilled in the art or commercially available elements Mo；The present invention is right
The purity of elements Mo is not particularly limited, with the purity for preparing the elements Mo of high temperature alloy well known to those skilled in the art
.
Constitute by mass percentage, the mass percentage content of the element Cr is preferably 13～15%, more preferably
13.5～14.5%, the present embodiment is preferably 14%, naturally it is also possible to for 13%, or 15%；Source of the present invention to element Cr
It is not particularly limited, with the source of element Cr well known to those skilled in the art or commercially available element Cr；The present invention is to unit
The purity of plain Cr is not particularly limited, with the purity for preparing the element Cr of high temperature alloy well known to those skilled in the art i.e.
Can.
Constitute by mass percentage, the mass percentage content of the Elements C is preferably 0.02～0.06%, more preferably
0.02～0.04%, the present embodiment is preferably 0.03%, or and 0.05%, naturally it is also possible to for 0.02%, or be
0.06%；The present invention is not particularly limited to the source of Elements C, with the source or city of Elements C well known to those skilled in the art
The Elements C sold；The present invention is not particularly limited to the purity of Elements C, with well known to those skilled in the art for preparing
The purity of the Elements C of high temperature alloy.
Constitute by mass percentage, the mass percentage content of the element B is preferably 0.003～0.012%, more preferably
For 0.003～0.008%, the present embodiment is preferably 0.006%, or and 0.01%, naturally it is also possible to for 0.003%, or
0.012%；The present invention is not particularly limited to the source of element B, with the source or city of element B well known to those skilled in the art
The element B sold；The present invention is not particularly limited to the purity of element B, with well known to those skilled in the art for preparing
The purity of the element B of high temperature alloy.
Constitute by mass percentage, the mass percentage content of the element Zr is preferably 0.02～0.06%, more preferably
For 0.02～0.04%, the present embodiment is preferably 0.03%, naturally it is also possible to for 0.02%, or 0.06%；The present invention is to element
The source of Zr is not particularly limited, with the source of element Zr well known to those skilled in the art or commercially available element Zr；This
Invention is not particularly limited to the purity of element Zr, with the element Zr for preparing high temperature alloy well known to those skilled in the art
Purity.
The embodiment of the present invention is not particularly limited to the source of element Ni, with element Ni's well known to those skilled in the art
Source or commercially available element Ni；The present invention is not particularly limited to the purity of element Ni, is known with those skilled in the art
The purity for preparing the element Ni of high temperature alloy.
Specifically, mass percent therein is specially：Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：
1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：0.2%；C：0.03%；B：0.006%；Zr：0.04%.According to this
The high temperature alloy of individual proportioning, performance is more excellent.
Specifically, mass percent therein is specially：Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：
1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：0.2%；C：0.05%；B：0.01%；Zr：0.04%.According to this
The high temperature alloy of proportioning, performance is more excellent.
The embodiment of the present invention provides a kind of high temperature alloy, and by mass percentage composition includes：Co：19%；Cr：14%；Al：
3.2%；Ti：3.5%；Ta：1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：0.2%；C：0.03%；B：
0.006%；Zr：0.03%；Balance of Ni and inevitable impurity.
Above-mentioned powder metallurgy high-temperature alloy provided in an embodiment of the present invention, optimizes Al, Ti, Nb content, while adjustment W,
Mo, Co content, and with the addition of Ta and Hf.After testing, compare second generation powder metallurgy high-temperature alloy Rene88, U720Li,
FGH96, its main hardening constituent γ ' phase to be completely dissolved temperature and percent by volume high, thereby increase the elevated temperature strength of alloy
And temperature capability.
The embodiment of the present invention additionally provides another kind of high temperature alloy, and by mass percentage composition includes：Co：19%；Cr：
14%；Al：3.2%；Ti：3.5%；Ta：1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：0.2%；C：0.05%；
B：0.01%；Zr：0.03%；Balance of Ni and inevitable impurity.
The powder metallurgy high temperature nickel alloy provided in an embodiment of the present invention, with respect to second generation powder metallurgy high-temperature alloy tool
There are more preferable elevated temperature strength, the raising further than second generation powder metallurgy high-temperature alloy of alloy temperature capability.
The embodiment of the present invention provides a kind of article, and the article is used for gas-turbine unit, and group by mass percentage
Into comprising the high temperature alloy formed by following element：Co：18～20%；Cr：13～15%；Al：2.9-3.5%；Ti：3.3～
3.7%；Ta：0.9～1.1%；W：1.8～2.2%；Mo：2.5～3.5%；Nb：0.4～0.6%；Hf：0.1～0.3%；C：
0.02～0.06%；B：0.003～0.012%；Zr：0.02～0.06%；Balance of Ni and inevitable impurity.
In article described in the embodiment of the present invention, comprising high temperature alloy in element preferred version and afore-said hot alloy in
Element preferred version it is identical, this is no longer going to repeat them；Article of the present invention is preferred for gas-turbine unit, more excellent
It is selected to the hot-end component of gas-turbine unit.The present invention is not particularly limited to the model of the gas-turbine unit,
With the model of employing high temperature alloy well known to those skilled in the art；The present invention to the gas-turbine unit other
Condition is not particularly limited, with the normal condition of gas-turbine unit well known to those skilled in the art.
Powder nickel base superalloy described in the embodiment of the present invention, it is special as the high-temperature material for gas-turbine unit
Not Shi Yongyu crucial hot-end component Ni based powder metallurgy high temperature alloy, and the associated materials that thus manufacture and its component, this
Invent the high temperature alloy and there is more preferable elevated temperature strength with respect to second generation powder metallurgy high-temperature alloy, alloy temperature capability compares
Two generation powder metallurgy high-temperature alloys are further improved.
The embodiment of the present invention is further to improve the high-temperature mechanics strength and stability of high temperature alloy, additionally provides use in addition
In manufacture gas-turbine unit, the concrete technical scheme of crucial hot-end component is particularly manufactured, including the embodiment of the present invention is carried
For a kind of article, the article is used for gas-turbine unit, and constitutes by mass percentage, comprising what is formed by following element
High temperature alloy：Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：1.0%；W：2.0%；Mo：3.0%；Nb：
0.5%；Hf：0.2%；C：0.03%；B：0.006%；Zr：0.03%, balance of Ni.
And the embodiment of the present invention also provides another kind of article, the article is used for gas-turbine unit, and by quality
Percentage is constituted, comprising the high temperature alloy formed by following element：Co：18.8%；Cr：13%；Al：3.25%；Ti：
3.45%；Ta：1.0%；W：1.9%；Mo：3.1%；Nb：1.0%；Hf：0.2%；C：0.05%；B：0.010%；Zr：
0.03%, balance of Ni.
Nickel base superalloy provided in an embodiment of the present invention, especially a kind of nickel-base sintered high temperature alloy, Yi Jiyou
This gas-turbine unit for preparing, the particularly crucial hot-end component of gas-turbine unit, for alloy high-temp warm energy is held
Power is not enough, and tired, the primary granule border relatively low with creep ability of high temperature resistance, structure stability etc. directly determine the high temperatures of alloy
Can and component life-span problem, and the harmful phase of powder metallurgy high-temperature alloy middle appearance under arms is that material and component are being grown
Being also easy to produce fatigue crack during phase military service causes one of principal element of failure.
The embodiment of the present invention improves solid solution strengthening effect by adjusting the content of W, Mo, and reduces TCP phase contents；Adjustment
The content of Co can improve γ ' solid solubility temperatures, be effectively increased alloy heat-treatability and by be heat-treated optimized alloy performance can
Row；Increase Ta to improve γ ' phase stabilities.In addition, the alloy have adjusted the content of element Hf, B, so as to improve γ ' phases,
The stability of MC phases, and it is effectively improved the precipitation of primary granule border (PPB)；Therefore high temperature long service is solved well
Nickel base superalloy produces the tendency of harmful phase, improves the problem of the fatigue behaviour of alloy material.The present invention is using advanced
Alloy design method, gives full play to the effect of solution strengthening, precipitation strength, lifts the mechanical behavior under high temperature of alloy, balances respectively
Intensified element W, Mo, Nb, Al, Ti, Ta content in the alloy, through screening, devises the powder smelting containing Ta, medium Co contents
Golden high temperature nickel alloy, test result indicate that, its indices is better than typical second generation powder metallurgy high-temperature alloy.Using this
Bright designed high temperature alloy, the article of preparation especially prepares gas-turbine unit, particularly prepares its crucial hot junction portion
Part, is respectively provided with the stability of preferable mechanical property and high temperature long service, and preferably alloy temperature capability.
In order to further illustrate the embodiment of the present invention, the Ni based powder metallurgy for providing the present invention with reference to embodiments is high
Warm nickel alloy is described in detail.
The embodiment of the present invention prepares two kinds of powder metallurgy high temperature nickel alloys 140 according to certain alloying component proportioning,
Including alloy 140A and alloy 140B, and with existing typical second generation powder metallurgy high-temperature alloy (Rene88 (DT),
U720Li, FGH96) carry out composition contrast, comparing result, referring to table 1, the high temperature alloy that table 1 is obtained for the embodiment of the present invention (is closed
Golden 140A and alloy 140B) with the composition of second generation typical powder metallurgy high temperature alloy (Rene88 (DT), U720Li, FGH96)
Contrast.
The high temperature alloy (alloy 140A and alloy 140B) that the present embodiment of table 1 is obtained and second generation typical powder metallurgy high temperature
Composition contrast (numeral is mass percent in table) of alloy (Rene88 (DT), U720Li, FGH96)
| Alloy 140A | Alloy 140B | Rene88(DT) | U720Li | FGH96 | |
| Ni | Surplus | Surplus | Surplus | Surplus | Surplus |
| Co | 19 | 19 | 13 | 15 | 13 |
| Cr | 14 | 14 | 16 | 16 | 16 |
| Al | 3.2 | 3.2 | 2.1 | 2.5 | 2.2 |
| Ti | 3.5 | 3.5 | 3.7 | 5.0 | 3.7 |
| W | 2.0 | 2.0 | 4.0 | 1.25 | 4.0 |
| Mo | 3.0 | 3.0 | 4.0 | 3.0 | 4.0 |
| Ta | 1.0 | 1.0 | 0 | 0 | 0.02 |
| Nb | 0.5 | 0.5 | 0.75(0.7) | 0 | 0.8 |
| Hf | 0.2 | 0.2 | 0 | 0 | 0 |
| C | 0.03 | 0.05 | 0.04(0.03) | 0.025 | 0.03 |
| B | 0.006 | 0.01 | 0.02(0.015) | 0.018 | 0.01 |
| Zr | 0.03 | 0.03 | 0.04(0.03) | 0.05 | 0.04 |
As it can be seen from table 1 the alloy 140A and 140B of embodiment of the present invention design is closed with second generation powder metallurgy high temperature
Gold compares with following characteristics：Compared with Rene88, Al/Ti increased Elements C o than improving, Hf, Ta；With U720Li phases
Than, Al/Ti than improving, and Elements C o is increased, Nb, Ta and element Hf；Compared with domestic FGH96, the quality of Elements C o is improved,
And increased element al, Hf, Ta.
Performance inspection is carried out with the second generation typical powder metallurgy high-temperature alloy to the alloy 140 of embodiment of the present invention design
Survey.
Referring to Fig. 1, Fig. 1 is 140A and 140B and the typical powder metallurgy high-temperature alloy of the second generation in the embodiment of the present invention
γ ' hardening constituent content balance figures at 850 DEG C.
As shown in Figure 1, under 850 DEG C of hot conditions, the high temperature alloy 140A and 140B of embodiment of the present invention design, its
γ ' hardening constituents content is suitable higher than Rene88, FGH96, and U720Li.
Referring to Fig. 2, Fig. 2 is alloy 140A and 140B and the typical powder metallurgy high temperature of the second generation in the embodiment of the present invention
The γ ' of alloy is mutually completely dissolved temperature comparisons' figure.
As shown in Figure 2, the embodiment of the present invention design high temperature alloy 140A and 140B, its γ ' phases solid solubility temperature with
U720Li quite, than Rene88 about 40 DEG C is improved, and than FGH96 about 30 DEG C are improved.This shows the high temperature alloy of present invention design
High-Temperature Strengthening phase -- the stability of γ ' phases is substantially better than second generation powder metallurgy high-temperature alloy.
Referring to Fig. 3, Fig. 3 is alloy 140A and 140B and the typical powder metallurgy high temperature of the second generation in the embodiment of the present invention
The maximum molar content comparison diagram of the harmful phase σ phases of alloy.
From the figure 3, it may be seen that the high temperature alloy 140A and 140B of embodiment of the present invention design, the total amount that its σ phase can be formed is less,
This shows that the high temperature alloy of present invention design has bright certain advantage to the formation for suppressing and controlling σ phases.
Referring to Fig. 4, Fig. 4 is that the freezing range of the alloy 140A and 140B in the embodiment of the present invention is typical more than the second generation
The scope of the solid-liquid phase line of powder metallurgy high-temperature alloy.
The powder metallurgy high temperature nickel alloy of embodiment of the present invention design is can be seen that from above-mentioned testing result and explanation,
Compare original two generations powder metallurgy high-temperature alloy.Elevated temperature strength is improve, the stability of γ ' phases is improve, so as to improve
The high-temperature behavior of alloy, and the precipitation ability of harmful phase is reduced, materials microstructure stability also increases, and its item refers to
Mark is better than typical second generation powder metallurgy high-temperature alloy.
A kind of combustion turbine engine components are also disclosed in the present embodiment, the material of the part for as described above any
Nickel base superalloy.
A kind of nickel base superalloy that the present invention is provided is described in detail above, it is used herein specifically individual
Example is set forth to the principle and embodiment of the present invention, and the explanation of above example is only intended to help understand the present invention's
Method and its core concept, including best mode, and also cause any person skilled in the art to put into practice the present invention,
Including manufacture and using any device or system, and the method for implementing any combination.It should be pointed out that general for the art
For logical technical staff, under the premise without departing from the principles of the invention, some improvement and modification can also be carried out to the present invention, this
A little improvement and modification are also fallen into the protection domain of the claims in the present invention.The scope of patent protection of the present invention passes through claim
To limit, and may include those skilled in the art it is conceivable that other embodiment.If these other embodiments have
Different from the structural element of claim character express, or if they are included with the character express of claim without substantive poor
Different equivalent structural elements, then these other embodiments also should be comprising within the scope of the claims.
Claims (11)
1. a kind of nickel base superalloy, it is characterised in that by mass percentage composition includes：
Co：18-20%；Cr：13-15%；Al：2.9-3.5%；Ti：3.3-3.7%；Ta：0.9-1.1%；W：1.8-2.2%；
Mo：2.5-3.5%；Nb：0.4-0.6%；Hf：0.1-0.3%；C：0.02-0.06%；B：0.003-0.012%；Zr：0.02-
0.06%；Balance of Ni and inevitable impurity.
2. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the Co is specially
18.5-19.5%.
3. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the Cr is specially
13.5-14.5%.
4. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the Al is specially
3.0-3.4%.
5. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the Ti is specially
3.4-3.6%.
6. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the W is specially
1.9-2.1%.
7. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the Mo is specially
2.75-3.25%.
8. a kind of nickel base superalloy according to claim 1, it is characterised in that the mass percent of the Nb is specially
0.45-0.55%.
9. a kind of nickel base superalloy according to claim 1, it is characterised in that mass percent therein is specially：
Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：
0.2%；C：0.03%；B：0.006%；Zr：0.04%.
10. a kind of nickel base superalloy according to claim 1, it is characterised in that mass percent therein is specially：
Co：19%；Cr：14%；Al：3.2%；Ti：3.5%；Ta：1.0%；W：2.0%；Mo：3.0%；Nb：0.5%；Hf：
0.2%；C：0.05%；B：0.01%；Zr：0.04%.
11. a kind of combustion turbine engine components, it is characterised in that the material of the part is such as the arbitrary institute of claim 1-10
A kind of nickel base superalloy stated.
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Cited By (2)
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| CN113481413A (en) * | 2021-05-24 | 2021-10-08 | 深圳市万泽中南研究院有限公司 | Directional solidification nickel-based high-temperature alloy, turbine blade and gas turbine |
| CN114737081A (en) * | 2022-04-06 | 2022-07-12 | 暨南大学 | Ni-Al-Ti-based high-temperature alloy with layered microstructure and preparation method thereof |
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|---|---|---|---|---|
| JP2002020849A (en) * | 2000-07-05 | 2002-01-23 | Fukui Prefecture | Method for working/heat-treating superelastic alloy |
| CN104120307A (en) * | 2013-04-23 | 2014-10-29 | 通用电气公司 | Cast nickel-based superalloy including iron |
-
2016
- 2016-12-13 CN CN201611146863.5A patent/CN106636756B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002020849A (en) * | 2000-07-05 | 2002-01-23 | Fukui Prefecture | Method for working/heat-treating superelastic alloy |
| CN104120307A (en) * | 2013-04-23 | 2014-10-29 | 通用电气公司 | Cast nickel-based superalloy including iron |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113481413A (en) * | 2021-05-24 | 2021-10-08 | 深圳市万泽中南研究院有限公司 | Directional solidification nickel-based high-temperature alloy, turbine blade and gas turbine |
| CN114737081A (en) * | 2022-04-06 | 2022-07-12 | 暨南大学 | Ni-Al-Ti-based high-temperature alloy with layered microstructure and preparation method thereof |
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