CN116287871A - Nickel-based superalloy for 650 ℃ and additive manufacturing method thereof - Google Patents

Nickel-based superalloy for 650 ℃ and additive manufacturing method thereof Download PDF

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CN116287871A
CN116287871A CN202310564451.7A CN202310564451A CN116287871A CN 116287871 A CN116287871 A CN 116287871A CN 202310564451 A CN202310564451 A CN 202310564451A CN 116287871 A CN116287871 A CN 116287871A
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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
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    • 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%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
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    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
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    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
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    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y80/00—Products made by additive manufacturing
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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 invention discloses a nickel-based superalloy for 650 ℃ and an additive manufacturing method thereof, wherein the nickel-based superalloy comprises, by mass, 10.0-12.0% Cr;8.0-9.0% Nb;4.0-5.0% Ti;2.0-3.0% Al;3.0-4.0% Fe;4.0-5.0% w;2.0-3.0% mo;1.0-2.0% Ta; the balance Ni. The invention adopts the additive manufacturing mode of selective laser melting for deposition, adopts a multi-stage solid solution treatment system to fully promote element diffusion, and enables the gamma 'and gamma+gamma' eutectic to be completely dissolved in a gamma matrix; and finally, performing two-stage aging treatment, namely firstly preserving heat for 6-10 hours at 750 ℃, cooling to 600 ℃ in a furnace, preserving heat for 6-10 hours, and performing air cooling to finish heat treatment, thereby obtaining the nickel-based superalloy with excellent performance under the service condition of 650 ℃, and meeting the specific service requirement.

Description

Nickel-based superalloy for 650 ℃ and additive manufacturing method thereof
Technical Field
The invention relates to a method for manufacturing nickel-based superalloy by laser additive, in particular to a nickel-based superalloy for 650 ℃ and an additive preparation method thereof.
Background
Nickel-based superalloy is one of the most widely used superalloys and has the strongest high temperature strength. The nickel-based superalloy takes nickel element as a matrix (the content is generally more than 50 percent), and has higher strength and good oxidation resistance and gas corrosion resistance in the range of 650-1000 ℃. The different nickel-base superalloys contain more than ten alloy elements such as Cr, co, W, mo, re, al, ti, C, B, zr, Y and the like, and the different elements play roles of solid solution strengthening, second phase strengthening, grain boundary strengthening and the like for strengthening the alloy. With the progress of science and technology and the rapid development of aerospace industry, the nickel-based superalloy becomes one of blade materials widely applied in the aerospace field due to the strength of the nickel-based superalloy at high temperature and good oxidation resistance and gas corrosion resistance.
When the material is used as a blade material of a turbine engine, the blade bears different extreme environments in different working parts, and the working temperature range is 650-850 ℃ at the root of the turbine blade. Therefore, it is particularly important to provide nickel-base superalloy with more excellent performance at 650-850 ℃.
This requires the continued development and improvement of the composition and processing of nickel-base superalloys. The additive manufacturing is a manufacturing process for accumulating materials from bottom to top, and the specific forming process is as follows: firstly modeling by using computer modeling software, utilizing the principle of discrete, accumulation and lamination, on the basis of slicing data of a three-dimensional solid model of the part CAD, controlling high-power laser to melt metal powder synchronously conveyed by computer programming, melting part of materials on the surface of a base material, mixing the two materials to form a molten pool, and rapidly solidifying the molten pool after a laser beam sweeps, so that the molten pool is deposited on the solidified base material, and accumulating layer by layer, thus finally obtaining the three-dimensional sample. Because the high-energy laser beam melts and covers the powder on the solidified base material, the powder has ultrahigh temperature gradient, unbalanced rapid solidification can be realized, metallurgical bonding is formed, the sample piece has fine structure, high density and good surface quality, and the powder can be arranged between a casting and a forging piece, and has excellent mechanical properties.
Disclosure of Invention
The invention aims to obtain a nickel-based alloy with excellent performance under the service condition of 650 ℃ by innovating nickel-based superalloy components, specifically, determining the microstructure of the superalloy by the content of Cr, nb, ti, al, fe, W, mo and Ta and assisting with additive manufacturing and a unique heat treatment process, thereby meeting specific service requirements.
First, the invention provides a nickel-based superalloy for 650 ℃, which is characterized in that: comprises 10.0-12.0% Cr by mass percent; 8.0-9.0% Nb;4.0-5.0% Ti;2.0-3.0% Al;3.0-4.0% Fe;4.0-5.0% w;2.0-3.0% mo;1.0-2.0% Ta; the balance Ni.
Further preferably, the alloy comprises, by mass, 8.0 to 8.5% of Nb, 4.5 to 4.8% of Ti, 2.2 to 2.5% of Al, and 3.0 to 3.5% of Fe.
Further preferably, the Mo/W is 0.45 to 0.6 in mass percent.
Further preferably, al/Ti is greater than 0.5 in mass percent.
Further preferably, the nickel-base superalloy has a tensile strength of greater than 1200MPa, a yield strength of greater than 1050MPa, an elongation after fracture of greater than 14%, and a reduction of area of greater than 25% at 650 ℃.
The invention also provides an additive manufacturing method of the 650 ℃ high-temperature nickel-based alloy, which comprises the following steps:
1) Preparing alloy powder, wherein the components of the alloy powder meet the component requirements of the high-temperature nickel-based alloy;
2) Depositing a high-temperature nickel-based alloy in a protective atmosphere by adopting a laser selective melting additive manufacturing mode;
3) And performing double-stage aging treatment on the high-temperature nickel-based alloy obtained by additive manufacturing.
Still preferably, the preparing alloy powder is to prepare mixed powder of all alloy elements according to the component requirements of the high-temperature nickel-based alloy, and then put the mixed powder into a vacuum smelting furnace for smelting and casting into a solid bar; and then placing the bar into vacuum atomization powder making equipment, adopting vacuum inert gas atomization technology to prepare alloy powder, taking out the cooled powder, and sieving to obtain the alloy powder with the particle size of 25-45 micrometers.
Further preferably, the island scanning with the light spot diameter of 90-100 μm in the additive manufacturing has the laser power of 200-240W, the scanning speed of 950-970mm/s, the scanning interval of 125-135 μm and the layer thickness of 25-35 μm.
Further preferably, the parameters of the two-stage aging treatment are that the nickel-based superalloy is heated to 750 ℃ and then is insulated for 6-10 hours, then is cooled to 600 ℃ and is insulated for 6-10 hours, and then is cooled to room temperature in an air way.
Further preferably, before the two-stage aging treatment, the nickel-based superalloy is heated to 1060-1080 ℃ for heat preservation for 1-2 hours and then air-cooled to room temperature, and then the nickel-based superalloy is heated to 960-980 ℃ for heat preservation for 1-2 hours and then air-cooled to room temperature.
Compared with the prior art, the invention has the beneficial effects that:
firstly, the invention adjusts and improves the component design of the nickel-based superalloy, properly improves the content of Al, and can separate out more Ni through subsequent heat treatment 3 Al, the gamma prime phase, helps to improve the high temperature properties of the alloy. However, too high gamma' can cause the thermoplastic property to be reduced, and cracking is easy to occur in the process of material addition, and the inventor finds that the Al content is better than 2.0-3.0 wt%; the alloy element W is not beneficial to the stabilization of gamma' phase, so the content is lower; the reduction of the Fe element content is also helpful for improving the strength of gamma', and the inventors found that the Fe content is preferably 3.0-4.0 wt%.
Secondly, the invention adopts a box-type resistance furnace to carry out solution aging treatment. The solution treatment system adopts multistage solid solution to fully promote element diffusion and enable the gamma 'and gamma+gamma' eutectic to be completely dissolved in the gamma matrix. The first step of homogenizing heat treatment, firstly, preserving heat for 1-2 hours at 1060-1080 ℃, and air cooling to enable the alloy to fully eliminate residual stress and segregation and reduce the content of residual delta phase. Then carrying out solution heat treatment, preserving heat for 1-2h at 960-980 ℃, and air cooling. And finally, performing two-stage aging treatment, namely firstly preserving heat for 6-10 hours at 750 ℃, cooling to 600 ℃ in a furnace, preserving heat for 6-10 hours, and performing air cooling to finish heat treatment.
Thirdly, the invention reasonably designs the additive manufacturing process, and ensures that the nickel-based superalloy has uniform structure and excellent performance.
Drawings
FIG. 1 is a schematic illustration of a heat treatment process according to the present invention.
FIG. 2 is a photograph of a microstructure of a nickel-base superalloy of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be described below with reference to the drawings in the embodiments of the present invention.
The invention mainly comprises the following steps: 1. component design of nickel-base superalloy; 2. preparing powder; 3. forming a component; 4. heat treatment; 5. and (5) performance analysis.
1. Composition design of nickel-base superalloy
Nickel-based superalloy is one of the most widely used superalloys and has the strongest high temperature strength. The nickel-based superalloy which takes nickel element as a matrix, has higher strength and good oxidation resistance and gas corrosion resistance in the temperature range of 650-1000 ℃ has wide application in the aerospace field. Nickel-base superalloys typically contain more than ten alloying elements, such as Cr, co, W, mo, al, ti, which serve to strengthen the alloy by solid solution strengthening, second phase strengthening, grain boundary strengthening, and the like.
Cr: cr in the gamma matrix of the high-temperature alloy causes lattice distortion, so that the gamma solid solution strength is improved, the solid solution strengthening effect is realized, the stacking fault energy of the solid solution is reduced by Cr, and the high-temperature durability is obviously improved. When the Cr content is less than 10wt%, the effect of solid solution strengthening is poor, and the alloy cannot have good mechanical properties and high-temperature durability, and at the same time, oxidation resistance and corrosion resistance are also reduced, whereas when the Cr content is more than 12wt%, a large amount of Ni is precipitated in the alloy 2 The AlTi phase deteriorates the performance, and the higher the Cr content, the greater the influence.
Nb: nb increases the lattice constant significantly over W and Mo, and thus the solid solution strengthening effect of Nb is greater. Nb is mainly dissolved in the Y phase, and usually only about 10wt% of the amount added in the γ phase, and thus Nb is mainly a γ″ phase strengthening element. When Nb is too high, the strengthening phase of the alloy is gamma 'phase different from that of the common nickel-based superalloy, gamma' is the main strengthening phase, aggregation and coarsening can occur under the condition of 650 ℃ long-term use, and finally the alloy is converted into delta phase, so that the strength of the material is reduced.
Al: al is formed into gamma' -Ni 3 The basic constituent elements of the AI phase are added into Al in the high-temperature alloy, and about 20% of the Al enters into gamma solid solution to play a role in solid solution strengthening. While 80% of Al forms Ni with Ni 2 Al, carrying out precipitation strengthening. The effect of increasing the Al content and increasing the amount of Al and Ni entering the gamma 'phase on precipitation strengthening is that the gamma phase is formed first, and the gamma' phase increases in amount with increasing AI content, so that each result shows that when the Al content is lower, the creep rupture time increases with increasing Al content, exceeds the peak value, and the creep rupture time rapidly decreases with increasing Al content. The main reason is that large Laves phase and NiAl phase are separated out from the alloy, so that cracks are easy to nucleate and expand. Thus selecting interval 2-3wt%
Ti: ti is added into the nickel-based and iron-based high-temperature alloy, about 10% of the Ti enters a gamma solid solution to play a certain solid solution strengthening role. About 90% of the phase goes into the gamma' phase and titanium atoms can replace gamma-Ni 3 Aluminum atoms in Al phase to form Ni 3 (Al, ti). Under certain aluminum content conditions, as the Ti content increases, the gamma phase number increases, causing the alloy to increase in temperature and high temperature strength. The precipitation strengthening element is combined with carbon to form carbide, so that intergranular corrosion caused by chromium carbide precipitation during heat treatment is reduced, the aging strengthening of Al with a certain content is promoted, the Ti is favorable for the stability of gamma ', the generation of gamma' is weakened by the excessive high or low content of Al, the certain strength of the Al is maintained, and the strength of the Ti is also ensured. The ratio of Al to Ti is preferably greater than 0.5, and too low a ratio of Al to Ti will result in significant changes in the morphology and ratio of the gamma' and gamma "phases, such that the two phases will not fully complex and precipitate, thereby coarsening the remaining gamma" phase in long-term failure to affect high temperature performance.
Fe: fe is added into the nickel-based superalloy, so that the cost can be reduced, the yield strength can be improved, and the effect of solid solution strengthening is achieved.
W: w is 10-13 wt% greater than the atomic radii of nickel, cobalt and iron. The crystal lattice can be obviously expanded in the high-temperature alloy matrix, and the yield strength is improved. Tungsten significantly reduces gamma matrix stacking fault energy to effectively improve creep properties of the superalloy. And the nickel-based alloy is comprehensively solid-solution strengthened together with Mo element. At levels below 4wt%, the nickel-base alloys have poor creep properties and yield strength. When the content is higher than 5wt%, the increase value of the alloy yield strength is not very large, and the distribution of other elements in gamma and gamma' phases is influenced, so that the mechanical properties are influenced.
Mo: mo is one of the most widely used alloying elements in superalloys, as is W. Unlike tungsten, mo atoms are mostly dissolved in the gamma matrix, and the content of Mo is about 1/4 in the gamma 'phase, and since W is unfavorable for the stabilization of the gamma' phase, mo is substituted for W to some extent, preferably 0.45-0.6 Mo/W can be added, more preferably Mo which is nearly half the mass of W is added to reduce the content of W while maintaining the effect of W. Mo can obviously increase the lattice constant of Ni solid solution and obviously increase the yield strength, and meanwhile, by adding Mo, a large amount of M6C carbide is formed in the alloy to form dispersion strengthening. However, when the Mo content is more than 3.0wt%, it has a large negative effect on oxidation resistance and stability of the alloy.
Ta: ta is added in a small amount to strengthen the alloy, so that the hot corrosion resistance can be effectively improved, the strengthening effect of gamma' phase is enhanced, and the instantaneous tensile property, plasticity and creep property are improved, but Ta is expensive, so that 1-2wt% of Ta is added.
Specific components of the nickel-base superalloy designed in the present invention are shown in table 1 below.
Table 1 design composition of nickel-base superalloy (wt.%)
Element(s) Ni Cr Nb Ti Al Fe W Mo Ta Impurity(s)
Content of Allowance of 10.0~12.0 8.0~9.0 4.0~5.0 2.0~3.0 3.0~4.0 4.0~5.0 2.0~3.0 1.0~2.0 ＜0.01
2. Preparation of the powder
In particular to a method for preparing casting bars with the same components and then preparing powder.
Preparing a casting rod:
the elemental materials required for the nickel alloy were first prepared according to the design ingredients as in table 1, and then the prepared materials were placed into a vacuum melting furnace for melting, and cast into solid bars.
Powder preparation:
placing the bar into vacuum atomization powder making equipment for atomization powder making, and introducing the obtained melt into an atomization furnace for gas atomization treatment, wherein the diameter of the gas atomization treatment is 3mn by using an annular conical nozzle; the apex angle of the jet air cone is 55 degrees; the atomization temperature is 400 ℃ above the liquidus temperature; the spraying speed of the air atomization treatment is controlled to be 2kg/min; the pressure in the gas atomization furnace is controlled to be 0.18bar; the pressure of the high-pressure atomizing medium is controlled to be 4MPa; the nickel alloy powder is prepared by vacuum inert gas atomization technology, the cooled powder is taken out, the powder is sieved and classified by vibration sieving equipment, the upper limit and the lower limit are 25 microns and 45 microns respectively, and after sieving is completed, the nickel alloy powder finished product with the particle size of 25-45 microns is obtained.
3. Component shaping
Screening the prepared powder, selecting nickel-based alloy powder with the diameter of 25-45 um for additive manufacturing, selecting nickel-based alloy powder with lower granularity to ensure that the alloy powder is sufficiently heated during additive manufacturing, and the obtained structure is finer, so that defect generation caused by insufficient melting is avoided, but powder caking is not easy to occur if the melting is too low, and thus negative effects are generated on the powder bulk density, the powder fluidity and the final alloy compactness.
The alloy powder is prepared into nickel alloy blocks by a laser selective melting technology (SLM), the diameter of a selected light spot is set to be 90-100 mu m, the laser power is 200-240W, the scanning speed is 950-970mm/s, and the nickel alloy blocks are matched with the melting conditions of the granularity, so that the heat dissipation problem of a molten pool is ensured while the powder is fully melted.
Scanning the substrate with a scanning interval of 125-135 μm and a layer thickness of 25-35 μm, and adding material on the substrate to obtain a block sample. The parameter data are specifically shown in table 2:
TABLE 2 Process parameters for laser Selective melting (SLM) additive manufacturing
Parameters (Unit) Numerical value
Particle size of powder (μm) 15~45
Spot diameter (μm) 90~100
Layer thickness (mum) 25~35
Speed of movement (mm/s) 960
Laser power (W) 220
4. Heat treatment of
The invention adopts a box-type resistance furnace to carry out solution aging treatment, and the heat treatment system is shown in figure 1.
In the selection of the heat treatment temperature, the first-stage homogenization heat treatment is carried out at 1060-1080 ℃, so that elements in the alloy can be subjected to solid diffusion to reduce the non-uniformity (segregation) of chemical components, mainly the non-uniformity (intra-crystal segregation or dendrite segregation) of chemical components in the grain size. The reason is that the heat preservation time is shortened as much as possible in order to accelerate the diffusion of the alloy elements. The homogenizing annealing temperature is typically 0.90-0.95TM (TM is the temperature at which the actual ingot begins to melt). The melting temperature of the alloy phase with the lowest melting point is determined according to DSC experimental data, namely the lowest overburning temperature of the alloy is determined first. For the nickel-based superalloy, if the temperature is too high, the alloy is easy to burn at the temperature of more than 1080 ℃, the alloy quality is difficult to control, and if the temperature is lower than 1060 ℃, the diffusion rate of the alloy element is lower, the heat preservation time is as long as possible, and the nickel-based superalloy is unfavorable for manufacturing.
The second-stage temperature is selected to be 960-980 ℃ for solid solution for 1-2 hours, air cooling is carried out, no obvious grain size change is caused during solid solution, but delta phase precipitation in a grain boundary can be promoted. The number of delta phases decreases with increasing solution temperature. Thus, at lower temperatures, the number of delta phases is excessive, and proper delta phase precipitation is not met, which inhibits dislocation movement and provides resistance to grain boundary creep rupture. The delta phase is largely dissolved at the temperature higher than 980 ℃, so that the pinning effect on the grain boundary is obviously weakened, and the heating and deformation temperature is controlled between 960 and 980 ℃ when the alloy delta phase process is formulated.
Followed by a double aging at 750 ℃ plus 600 ℃. The aging treatment is carried out at 750 ℃ and 600 ℃ in two steps without affecting the grain size and delta phase quantity, but the size and distribution precipitation of gamma 'and gamma'. The main strengthening phase gamma 'starts to precipitate at 750 ℃, while the gamma' phase precipitates above 600 ℃. So that both phases will separate out at 750 deg.c, and after the second stage ageing at 600 deg.c, gamma "will not grow up and gamma' will increase in size. Thus, two temperatures of 750 ℃ and 600 ℃ are selected for the aging treatment.
The incubation time is a range, and is adjusted according to the size and thickness of the sample, and the time for a small sample and a sample with a thin wall thickness should be relatively short.
5. Performance analysis
Examples
(1) Preparing metal powder, wherein the specific chemical composition of the metal powder is 63.10% by weight of Ni, 10% by weight of Cr, 8.5% by weight of Nb, 5% by weight of Ti, 2.4% by weight of Al, 3.5% by weight of Fe, 2% by weight of Mo, 4% by weight of W, 1.5% by weight of Ta and 100% by weight of the total of the components;
(2) Putting the prepared materials into a vacuum smelting furnace for smelting, wherein the smelting temperature is 1500 ℃; and when the vacuum degree of the furnace chamber is higher than 0.1MPa, filling inert gas for protection, smelting for 60min, and degassing to obtain a melt.
(3) Putting the bar into vacuum atomization powder making equipment, atomizing the bar to obtain powder, and introducing the obtained melt into an atomization furnace to perform gas atomization treatment, wherein the gas atomization treatment uses an annular conical nozzle with the diameter of 3mn; the apex angle of the jet air cone is 55 degrees; the atomization temperature is 400 ℃ above the liquidus temperature; the spraying speed of the air atomization treatment is controlled to be 2kg/min; the pressure in the gas atomization furnace is controlled to be 0.18bar; the pressure of the high-pressure atomizing medium is controlled to be 4MPa; the nickel alloy powder is prepared by vacuum inert gas atomization technology, the cooled powder is taken out, the powder is sieved and classified by vibration sieving equipment, the upper limit and the lower limit are 25 microns and 45 microns respectively, and after sieving is completed, the nickel alloy powder finished product with the particle size of 25-45 microns is obtained.
(4) According to the national standard of tensile test, the block is made into a tensile test sample conforming to the national standard, and the tensile test is carried out. From the experimental results shown in table 3, it can be seen that:
TABLE 3 alloy compositions and performance test results for each example at 650℃
No. Cr Nb Ti Al Fe Mo W Ta Heat treatment of Rm Rp A Z
1 10 8.5 5 2.4 3.5 2 4 1.5 Whether or not 1180 1150 10 19
2 10 8.5 5 2.4 3.5 2 4 1.5 Is that 1220 1080 16 30
3 12 8 4.4 2.5 3.3 2.2 4.1 1.4 Whether or not 1160 1100 9.3 18.4
4 12 8 4.4 2.5 3.3 2.2 4.1 1.4 Is that 1200 1060 16.2 28.7
5 9 8.5 4.4 2.5 3.2 2.2 4.4 1.8 Whether or not 1050 1000 8.4 17.2
6 9 8.5 4.4 2.5 3.2 2.2 4.4 1.8 Is that 1100 1000 15.2 28.2
7 13 8 4.7 2.5 3 2.2 4 1.5 Whether or not 1060 1020 9 18
8 13 8 4.7 2.5 3 2.2 4 1.5 Is that 1150 1020 15.8 28.4
9 10 10 4.5 2.6 3.5 2.3 4 1.4 Whether or not 1100 1080 8.4 17.2
10 10 10 4.5 2.6 3.5 2.3 4 1.4 Is that 1140 1040 14.7 26.2
11 10 9 4.4 2.3 3 2.1 4.3 1.6 Whether or not 1160 1120 9.7 18.4
12 10 9 4.4 2.3 3 2.1 4.3 1.6 Is that 1180 1060 15 28.4
13 10 7 4.1 2.4 3.2 2.3 4 1.5 Whether or not 1100 1040 9 17.3
14 10 7 4.1 2.4 3.2 2.3 4 15 Is that 1120 1050 15.2 27.4
15 10 8.5 4.5 2 3.4 2.1 4.2 1.5 Whether or not 1080 1060 8.4 16.4
16 10 8.5 4.5 2 3.4 2.1 4.2 1.5 Is that 1150 1020 15.2 26.7
17 10 8.5 6 2.3 3.1 2.5 4.3 1.5 Whether or not 1140 1120 9.5 18.2
18 10 8.5 6 2.3 3.1 2.5 4.3 1.5 Is that 1180 1040 14 28.1
19 10 8.5 3 1.5 3.2 2.2 4.6 1.6 Whether or not 1040 1020 8.7 18.2
20 10 8.5 3 1.5 3.2 2.2 4.6 1.6 Is that 1100 1000 12 25.1
The room temperature tensile strength, the yield strength, the elongation after fracture and the area shrinkage of the additive body in the direction parallel to the substrate are 1430MPa, 1180MPa, 8% and 16% respectively, the tensile strength at 650 ℃, the yield strength and the elongation after fracture are 1180MPa, 1150MPa, 10% and 19% respectively, and the room temperature tensile strength, the yield strength and the elongation after fracture and the area shrinkage of the additive body in the direction parallel to the substrate are 1500MPa, 1300MPa, 12%, 25% and 650 ℃, the yield strength and the elongation after fracture and the area shrinkage are 1220MPa, 1080MPa, 16% and 30% respectively. As shown in the picture of the structure morphology of the alloy in FIG. 2, the size of the gamma' -phase is about 0.2 mu m, the volume fraction is about 52%, meanwhile, the heat treatment can effectively improve the tensile property of the alloy, and the comparison with a GH4169 forge piece which is widely applied can prove that the tensile strength and the yield strength of the alloy after the heat treatment are superior to those of the GH4169 forge piece.
The long-lasting life of the alloy of the invention is 200 hours under the condition of 650 ℃/700MPa after detection and known selective laser melting, and the alloy has excellent service duration.
TABLE 4 comparison of tensile Property test of Selective laser melting alloy No. 1 and existing commonly used alloys
Status of Test temperature/. Degree.C Rm/MPa Rp0.2/MPa A/% Z/%
SLM 23 1430 1180 8 16
SLM 650 1180 1050 10 19
SLM+HT 23 1500 1300 12 25
SLM+HT 650 1220 1080 16 30
GH4169 forging 23 1440 1220 20 34
GH4169 forging 650 1160 1000 21 39
The present invention is not limited to the above-mentioned embodiments, and any changes or substitutions that can be easily understood by those skilled in the art within the technical scope of the present invention are intended to be included in the scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the claims.

Claims (10)

1. A nickel-base superalloy for 650 ℃ comprising: comprises 10.0-12.0% Cr by mass percent; 8.0-9.0% Nb;4.0-5.0% Ti;2.0-3.0% Al;3.0-4.0% Fe;4.0-5.0% w;2.0-3.0% mo;1.0-2.0% Ta; the balance Ni.
2. The nickel-base superalloy for 650 ℃ according to claim 1, wherein:
according to mass percentage, nb is 8.0-8.5%, ti is 4.5-4.8%, al is 2.2-2.5%, and Fe is 3.0-3.5%.
3. The nickel-base superalloy for 650 ℃ according to claim 1, wherein:
the mass percentage of Mo/W is 0.45-0.6.
4. The nickel-base superalloy for 650 ℃ according to claim 1, wherein:
the Al/Ti is more than 0.5 in mass percent.
5. A nickel-base superalloy for use at 650 ℃ according to any of claims 1 to 4, wherein:
the nickel-based superalloy has tensile strength of more than 1200MPa, yield strength of more than 1050MPa, elongation after fracture of more than 14% and area shrinkage of more than 25% at 650 ℃.
6. The additive manufacturing method of a high temperature nickel base alloy for 650 ℃ according to any of claims 1-5, comprising the steps of:
1) Preparing alloy powder, wherein the components of the alloy powder meet the component requirements of the high-temperature nickel-based alloy;
2) Depositing a high-temperature nickel-based alloy in a protective atmosphere by adopting a laser selective melting additive manufacturing mode;
3) And performing double-stage aging treatment on the high-temperature nickel-based alloy obtained by additive manufacturing.
7. The method of additive manufacturing of a high temperature nickel-base alloy for 650 ℃ according to claim 6, wherein: preparing alloy powder, namely preparing mixed powder of all alloy elements according to the component requirements of the high-temperature nickel-based alloy, and then placing the mixed powder into a vacuum smelting furnace for smelting and casting into a solid bar; and then placing the bar into vacuum atomization powder making equipment, adopting vacuum inert gas atomization technology to prepare alloy powder, taking out the cooled powder, and sieving to obtain the alloy powder with the particle size of 25-45 micrometers.
8. The method of additive manufacturing of a high temperature nickel-base alloy for 650 ℃ according to claim 6, wherein: island scanning with the diameter of the light spot of 90-100 mu m, laser power of 200-240W, scanning speed of 950-970mm/s, scanning interval of 125-135 mu m and layer thickness of 25-35 mu m.
9. The method of additive manufacturing of a high temperature nickel-base alloy for 650 ℃ according to claim 6, wherein: the parameters of the two-stage aging treatment are that the nickel-based superalloy is heated to 750 ℃ and then is insulated for 6-10 hours, then is cooled to 600 ℃ and is insulated for 6-10 hours, and then is cooled to room temperature.
10. The method of additive manufacturing of a high temperature nickel-base alloy for 650 ℃ according to claim 9, wherein: before the two-stage aging treatment, heating the nickel-based superalloy to 1060-1080 ℃ for heat preservation for 1-2h, then air-cooling to room temperature, and then heating the nickel-based superalloy to 960-980 ℃ for heat preservation for 1-2h, and then air-cooling to room temperature.
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