CN110468305A - 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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- CN110468305A CN110468305A CN201910791888.8A CN201910791888A CN110468305A CN 110468305 A CN110468305 A CN 110468305A CN 201910791888 A CN201910791888 A CN 201910791888A CN 110468305 A CN110468305 A CN 110468305A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0433—Nickel- or cobalt-based alloys
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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
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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Abstract
The present invention provides a kind of nickel base superalloys and preparation method thereof, which includes following component: C:0.05%-0.15%, Cr:20.50%-23.00%, Co:0.50%-2.50%, Mo:8.00%-10.00%, W:0.20%-1.00%, Fe:17.00%-20.00%, Si :≤1.00%, B:0.01%, Mn :≤1.00%, Al:0.60%-3.00%, Ti:1.00%-3.00%, Ni: surplus.Nickel base superalloy of the invention, have both high temperature higher intensity, service temperature it is higher and be suitable for SLM technology.And have the advantages that density is lower, the cost of raw material is lower.
Description
Technical field
The invention belongs to material increasing fields, and in particular, to a kind of nickel-base high-temperature for selective laser smelting technology
Alloy and preparation method thereof.
Background technique
Selective laser smelting technology (SLM) is existing certain in stainless steel, titanium alloy, aluminium alloy and high temperature alloy field at present
The application of degree has shown unique technical advantage.But conventional fabrication processes are compared, SLM technology can be less with alloy species,
This greatly constrains the industrial applications of SLM technology.
The high temperature alloy type for being currently used in SLM technology is concentrated mainly on solid solution high temperature alloy, although this kind of alloy has
Have a preferable high-temperature behavior, but alloy property be difficult to meet higher temperature and it is new the needs of require.
Summary of the invention
In view of the deficiencies of the prior art, the object of the present invention is to which the main object of the present invention is to provide a kind of new be suitble to
SLM technology and the alloy for meeting higher temperature requirement, this is all significant to SLM technology and application field.
Technical solution provided by the invention are as follows: a kind of nickel base superalloy, the nickel base superalloy includes following component:
C:0.05%-0.15%, Cr:20.50%-23.00%, Co:0.50%-2.50%, Mo:8.00%-
10.00%, W:0.20%-1.00%, Fe:17.00%-20.00%, Si :≤1.00%, B:0.01%, Mn :≤1.00%,
Al:0.60%-3.00%, Ti:1.00%-3.00%, Ni: surplus.
In some embodiments of the invention, the nickel base superalloy contains the γ ' phase of 10%-30%.
In some embodiments of the invention, the content of Al is 0.60%-2.00%.
In some embodiments of the invention, the content of Al is 1.50%-2.00%.
In some embodiments of the invention, the content of Ti is 1.00%-2.00%.
In some embodiments of the invention, the content of Ti is 1.50%-2.00%.
The present invention also provides a kind of methods for preparing above-mentioned nickel base superalloy, comprising steps of
Powder processed: superalloy powder is prepared using vacuum induction melting gas atomization；
Sieve powder: the superalloy powder is sieved, the powder of appropriate particle size is chosen；
The powder of selection: being manufactured by molding using selective laser smelting technology, obtains blank alloy；
Heat treatment: the nickel base superalloy is obtained after the blank alloy is carried out solid solution and ageing treatment.
In some embodiments of the invention, what the sieve powder step was chosen is powder of the partial size at 15 μm -45 μm.
In some embodiments of the invention, the temperature of solution treatment is 1100 DEG C -1250 DEG C, time 0.5h-2h.
In some embodiments of the invention, the temperature of ageing treatment is 800 DEG C -950 DEG C, time 1h-3h.
Alloy provided by the invention has the advantages that 900 DEG C, and elevated temperature strength is higher, density is lower, the cost of raw material is lower.
Further, alloy provided by the invention have both high temperature higher intensity, service temperature it is higher and be suitable for SLM skill
Art can more effectively push the exploitation of SLM technology high temperature alloy.
Additional aspect and advantage of the invention will be set forth in part in the description, and will partially become from the following description
Obviously, or practice through the invention is recognized.
Detailed description of the invention
Fig. 1 is the process flow chart that one embodiment of the invention prepares nickel base superalloy.
Specific embodiment
Below in conjunction with drawings and examples, a specific embodiment of the invention is described in more details, so as to energy
The advantages of enough more fully understanding the solution of the present invention and its various aspects.However, specific embodiments described below and reality
It applies example to be for illustrative purposes only, rather than limiting the invention.
Separately specifically, in the present invention, % refers to mass percentage.
High temperature alloy is as can be with higher in the metalloid material that 600 DEG C or more of high temperature is on active service steadily in the long term
The comprehensive performances such as elevated temperature strength, good anti-oxidant and corrosion resistance, good fatigue behaviour, fracture toughness are widely applied
Under the extreme conditions such as aerospace, gas turbine.
Nickel base superalloy of the invention, including following component:
C:0.05%-0.15%, Cr:20.50%-23.00%, Co:0.50%-2.50%, Mo:8.00%-
10.00%, W:0.20%-1.00%, Fe:17.00%-20.00%, Si :≤1.00%, B:0.01%, Mn :≤1.00%,
Al:0.60%-3.00%, Ti:1.00%-3.00%, Ni: surplus.
The present invention is obtained simultaneous by the synergistic effect of the elements such as Ni, C, Cr, Co, Mo, W, Fe, Si, B, Mn, Al and Ti
Tool high temperature higher intensity, service temperature are higher and are suitable for the novel nickel base superalloy of SLM technology, can more effectively push SLM
The exploitation of technology high temperature alloy.
The effect of element ti and Al in the alloy is introduced below:
γ ' is mutually the main hardening constituent in nickel base superalloy, can effectively improve the intensity under alloy high-temp, but γ '
It is mutually excessively easy to cause plasticity under high temperature to reduce, cracks simultaneously for being easy to cause to print for SLM technology.It is led in increasing material manufacturing
Domain, intensity, plasticity and the high-temperature behavior of alloy must all be taken into account, and the application is controlled by controlling the content of Al and Ti element
γ ' Xiang Hanliang makes alloy that can still remain with preferable plasticity in the case where improving elevated temperature strength, guarantees that SLM is smoothly formed.The present invention
In, γ ' mutually has 10%-30%.Preferably, γ ' phase content is 20%-30%.
In the application, element ti is γ ' phase and carbide former, plays adjustment γ ' phase content and formation in the alloy
Partially carbonized object is with the effect of reinforced alloys.In the application, there are about 2%-5% for carbide.
In the application, element al is γ ' phase formation element, by adjusting the amount of γ ' in the content control alloy of Al, thus
Control the mechanical property of material.In addition, the Al of certain content can improve the high-temperature oxidation resistance of alloy.
Ti content is higher, and the yield strength of alloy can be higher and higher, but with intensity on the contrary, the stretching plastic of alloy, impact
Toughness can be lower and lower.
In general, content≤0.15% of Ti.In the present invention, the content of Ti is 1.00%-3.00%.The present invention more
In preferred embodiment, the content of Ti is 1.00%-2.00%.In the further preferred embodiment of the present invention, the content of Ti is
1.50%-2.00%.
In the present invention, the content of Al is 0.60%-3.00%.In preferred embodiment of the invention, the content of Al is
0.60%-2.00%.In the further preferred embodiment of the present invention, the content of Al is 1.50%-2.00%.
It is rapid cooling process that SLM technique, which prints workpiece, and it is similar with welding that inventor has found it, and rapid cooling is easy to cause in alloy
Fire check is generated, inventors have found that the content of Al+Ti is controlled at≤6%, Ni based high-temperature alloy has medium welding hot tearing
Sensibility, belonging to can be with welding alloy, and printing is not in crackle in increasing material manufacturing, is met the requirements.
The density of nickel base superalloy of the invention is in 7.7g/cm3-8.1g/cm3Range, relative to existing nickel-base high-temperature
The low 3%-7% of the density of alloy GH3536.
Fig. 1 is the method that the present invention prepares above-mentioned nickel base superalloy comprising S1-S4 step:
S1 (powder processed): using has crucible vacuum induction melting gas atomization (VIGA) to prepare superalloy powder, VIGA method
Using crucible for smelting alloy material, aluminium alloy is flow at atomizer through tundish bottom conduit, by supersonic gas impact cutting
It is broken, be atomized into the tiny molten drop of micron order scale, molten drop nodularization is simultaneously frozen into powder, have powder processed low energy consumption, fine powder recovery rate,
The features such as more extensive using raw material.
S2 (sieve powder): superalloy powder is sieved, the powder of appropriate particle size is chosen.
In order to the performance of the alloy after subsequent better molding and guarantee molding, need to choose the powder of appropriate particle size.
In the preferred embodiment of the invention, what sieve powder step was chosen is powder of the partial size at 15 μm -45 μm, this particle size range powder exists
Powdering effect is good in print procedure, splashes that less, print surface finish is higher in print procedure, suitable for aerospace material
Material demand.
The powder of selection: being manufactured by S3 (molding) using selective laser smelting technology, obtains blank alloy.
Novel nickel base superalloy of the invention can be used for because having both high temperature higher intensity and excellent high-temperature behavior
SLM technology.
S4 (heat treatment): nickel base superalloy is obtained after blank alloy is carried out solid solution and ageing treatment.
In the preferred embodiment of the invention, the temperature of solution treatment is 1100 DEG C -1250 DEG C, time 0.5h-2h, Gu
The solid solubility temperature of the selection Primary Reference γ ' phase of molten time, generally at 1100 DEG C~1250 DEG C.
In the preferred embodiment of the invention, the temperature of ageing treatment is 800 DEG C -950 DEG C, time 1h-3h, timeliness
Effect mainly so that γ ' mutually uniformly be precipitated, therefore aging temp selection it is lower, while aging temp can refer to alloy be on active service temperature
It is more stable to may make that alloy is on active service for degree.
Below with reference to specific embodiment, the present invention will be described.Institute's taking technique condition value is in following embodiments
Illustratively, it can use numberical range as shown in foregoing summary, for not specifically specified technological parameter, can refer to often
Rule technology carries out.Detection method used in following embodiments is the detection method of industry routine.It should be pointed out that following
The calculation of Tensile Strength of embodiment is obtained using the simulation of JMatPro software.
Embodiment 1
Superalloy powder is prepared using vacuum induction melting gas atomization first, the ingredient of alloy powder is as shown in table 1.
Then superalloy powder is sieved, chooses powder of the partial size at 15 μm -45 μm.
The powder of selection is manufactured using selective laser smelting technology, obtains blank alloy.
Nickel base superalloy is obtained after blank alloy is carried out solid solution and ageing treatment.
The temperature of solution treatment is 1100 DEG C, time 2h；The temperature of ageing treatment is 900 DEG C, time 3h.
The density of nickel base superalloy prepared is tested and in 900 DEG C of tensile strength, as a result see table 2.
Embodiment 2
Superalloy powder is prepared using vacuum induction melting gas atomization first, the ingredient of alloy powder is as shown in table 1.
Then superalloy powder is sieved, chooses powder of the partial size at 20 μm -35 μm.
The powder of selection is manufactured using selective laser smelting technology, obtains blank alloy.
Nickel base superalloy is obtained after blank alloy is carried out solid solution and ageing treatment.
The temperature of solution treatment is 1175 DEG C, time 1h；The temperature of ageing treatment is 900 DEG C, time 3h.
The density of nickel base superalloy prepared is tested and in 900 DEG C of tensile strength, as a result see table 2.
Embodiment 3
Superalloy powder is prepared using vacuum induction melting gas atomization first, the ingredient of alloy powder is as shown in table 1.
Then superalloy powder is sieved, chooses powder of the partial size at 30 μm -45 μm.
The powder of selection is manufactured using selective laser smelting technology, obtains blank alloy.
Nickel base superalloy is obtained after blank alloy is carried out solid solution and ageing treatment.
The temperature of solution treatment is 1200 DEG C, time 1.5h；The temperature of ageing treatment is 900 DEG C, time 3h.
The density of nickel base superalloy prepared is tested and in 900 DEG C of tensile strength, as a result see table 2.
Embodiment 4
Superalloy powder is prepared using vacuum induction melting gas atomization first, the ingredient of alloy powder is as shown in table 1.
Then superalloy powder is sieved, chooses powder of the partial size at 15 μm -30 μm.
The powder of selection is manufactured using selective laser smelting technology, obtains blank alloy.
Nickel base superalloy is obtained after blank alloy is carried out solid solution and ageing treatment.
The temperature of solution treatment is 1225 DEG C, time 2h；The temperature of ageing treatment is 900 DEG C, time 3h.
The density of nickel base superalloy prepared is tested and in 900 DEG C of tensile strength, as a result see table 2.
Embodiment 5
Superalloy powder is prepared using vacuum induction melting gas atomization first, the ingredient of alloy powder is as shown in table 1.
Then superalloy powder is sieved, chooses powder of the partial size at 15 μm -35 μm.
The powder of selection is manufactured using selective laser smelting technology, obtains blank alloy.
Nickel base superalloy is obtained after blank alloy is carried out solid solution and ageing treatment.
The temperature of solution treatment is 1125 DEG C, time 2h；The temperature of ageing treatment is 900 DEG C, time 3h.
The density of nickel base superalloy prepared is tested and in 900 DEG C of tensile strength, as a result see table 2.
Each embodiment alloying component content of table 1
| Ingredient | C (%) | Cr (%) | Co (%) | Mo (%) | W (%) | Fe (%) |
| Embodiment 1 | 0.07 | 23.00 | 2.50 | 8.00 | 0.20 | 20.00 |
| Embodiment 2 | 0.07 | 21.50 | 1.50 | 9.00 | 0.80 | 18.00 |
| Embodiment 3 | 0.07 | 23.00 | 0.50 | 10.00 | 1.00 | 17.00 |
| Embodiment 4 | 0.07 | 22.50 | 2.00 | 8.50 | 0.60 | 17.50 |
| Embodiment 5 | 0.07 | 21.00 | 1.20 | 9.50 | 0.40 | 19.00 |
| Ingredient | Si (%) | B (%) | Mn (%) | Al (%) | Ti (%) | Ni (%) |
| Embodiment 1 | < 0.2 | 0.01 | < 0.01 | 0.6 | 1.25 | Surplus |
| Embodiment 2 | < 0.2 | 0.01 | < 0.01 | 1.75 | 2.00 | Surplus |
| Embodiment 3 | < 0.2 | 0.01 | < 0.01 | 1.00 | 1.50 | Surplus |
| Embodiment 4 | < 0.2 | 0.01 | < 0.01 | 2.50 | 2.50 | Surplus |
| Embodiment 5 | < 0.2 | 0.01 | < 0.01 | 1.25 | 3.00 | Surplus |
Each embodiment alloy property of table 2
From above-described embodiment it is found that nickel base superalloy of the invention, have both high temperature higher intensity, service temperature it is higher and
Suitable for SLM technology.And have the advantages that density is lower, the cost of raw material is lower.
Obviously, the above embodiment is merely an example for clearly illustrating the present invention, and not to embodiment
It limits.For those of ordinary skill in the art, other different forms can also be made on the basis of the above description
Variation or variation.There is no necessity and possibility to exhaust all the enbodiments.And it thus amplifies out apparent
Variation or variation be still in the protection scope of this invention.
Claims (10)
1. a kind of nickel base superalloy, which is characterized in that including following component:
C:0.05%-0.15%, Cr:20.50%-23.00%, Co:0.50%-2.50%, Mo:8.00%-10.00%, W:
0.20%-1.00%, Fe:17.00%-20.00%, Si :≤1.00%, B:0.01%, Mn :≤1.00%, Al:0.60%-
3.00%, Ti:1.00%-3.00%, Ni: surplus.
2. nickel base superalloy according to claim 1, which is characterized in that the nickel base superalloy contains 10%-
30% γ ' phase.
3. nickel base superalloy according to claim 1, which is characterized in that the content of Al is 0.60%-2.00%.
4. nickel base superalloy according to claim 3, which is characterized in that the content of Al is 1.50%-2.00%.
5. nickel base superalloy according to claim 1, which is characterized in that the content of Ti is 1.00%-2.00%.
6. nickel base superalloy according to claim 5, which is characterized in that the content of Ti is 1.50%-2.00%.
7. a kind of method for preparing any nickel base superalloy in claim 1-6, which is characterized in that comprising steps of
Powder processed: superalloy powder is prepared using vacuum induction melting gas atomization；
Sieve powder: the superalloy powder is sieved, the powder of appropriate particle size is chosen；
The powder of selection: being manufactured by molding using selective laser smelting technology, obtains blank alloy；
Heat treatment: the nickel base superalloy is obtained after the blank alloy is carried out solid solution and ageing treatment.
8. the method according to the description of claim 7 is characterized in that the sieve powder step selection is partial size at 15 μm -45 μm
Powder.
9. the time is the method according to the description of claim 7 is characterized in that the temperature of solution treatment is 1100 DEG C -1250 DEG C
0.5h-2h。
10. the time is the method according to the description of claim 7 is characterized in that the temperature of ageing treatment is 800 DEG C -950 DEG C
1h-3h。
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Cited By (4)
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| CN113061783A (en) * | 2021-03-23 | 2021-07-02 | 江苏图南合金股份有限公司 | High-temperature alloy seamless special pipe and production method thereof |
| CN113814411A (en) * | 2021-08-13 | 2021-12-21 | 南京国重新金属材料研究院有限公司 | Additive manufacturing method of high-aluminum-titanium K418B alloy |
| CN113927044A (en) * | 2021-09-24 | 2022-01-14 | 南昌航空大学 | A solution treatment method for laser additive manufacturing of superalloys |
| CN117230347A (en) * | 2023-11-13 | 2023-12-15 | 北京科技大学 | Nickel-based superalloy with reduced additive manufacturing cracks and preparation method thereof |
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| CN117230347A (en) * | 2023-11-13 | 2023-12-15 | 北京科技大学 | Nickel-based superalloy with reduced additive manufacturing cracks and preparation method thereof |
| CN117230347B (en) * | 2023-11-13 | 2024-01-30 | 北京科技大学 | A nickel-based high-temperature alloy with reduced cracks produced by additive manufacturing and its preparation method |
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