CN116237542B - In-situ generation and non-original addition method, material and application of reinforcing phase of GH3230 - Google Patents
In-situ generation and non-original addition method, material and application of reinforcing phase of GH3230 Download PDFInfo
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- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 35
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- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 claims 1
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Abstract
The invention discloses a method, a material and application for in-situ generation and non-original addition of an enhancement phase of GH3230, relating to the technical field of metal additive manufacturing, comprising the following steps: selecting GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder to prepare composite powder according to a set proportion; the composite powder is mixed and stirred at high speed by double centrifugation for many times until the mixture is uniform and has no obvious agglomeration, thus forming GH3230-TiB 2-AlSi10 Mg composite powder; SLM forming is carried out on the stirred composite powder by utilizing metal additive manufacturing equipment; carrying out solution heat treatment on the sample piece after the SLM forming, and then carrying out aging heat treatment to realize that an Al element in AlSi 10 Mg powder and a Ni element in GH3230 alloy powder are separated out to form a gamma' reinforcing phase; on the basis of adding (ex-situ adding) TiB 2 reinforcing phase, the gamma' reinforcing phase generated in situ by heat treatment further plays a role in reinforcing, and the synergistic effect of the two reinforcing phases contributes to improving the bearing capacity of the alloy.
Description
Technical Field
The invention relates to the technical field of metal additive manufacturing, in particular to a method, a material and application for in-situ generation and non-original addition of a reinforcing phase of GH 3230.
Background
GH3230 (nickel-based superalloy) is a solid solution strengthening superalloy with Cr, W and Mo as main strengthening elements, and has the service temperature range of 700-1050 ℃, and good strength, thermal stability and oxidation resistance. The alloy is mainly used for manufacturing hot end components such as flame tubes, combustion chambers and the like of advanced aeroengines, high-temperature corrosion-resistant components in the chemical industry and the like. However, the structure of the component is generally complex, and the problems of long research and development period, high processing cost and the like exist when the component is processed by adopting traditional processing modes such as casting, forging, milling and the like. The laser selective melting (SELECTIVE LASER MELTING, SLM) is used as a typical powder-spreading type metal additive manufacturing technology, and can directly form a metal component by spreading powder layer by layer and selectively melting and depositing by laser.
With the development of equipment technology, higher requirements are put on the mechanical properties of GH 3230. The addition of reinforcing particles into the alloy as a reinforcing phase is an effective means for improving the mechanical properties of the alloy, and the improvement of the content of the reinforcing phase in the alloy is mainly divided into two modes of 'non-in-situ addition' and 'in-situ generation'.
It is common to mechanically mix reinforcing phase particles with alloy powder and then SLM form them in an "ex situ addition" manner in the SLM process. However, since the reinforcing particles are added by mechanical mixing, excessive addition tends to cause agglomeration of the reinforcing particles in the alloy powder, thereby affecting SLM forming quality. This limits the proportion of reinforcing phase added and the reinforcing effect "ex situ".
The reinforcing phase is mainly precipitated by heat treatment of the shaped sample, and the heat treatment can also relieve residual stress and anisotropy in the SLM shaped sample. Therefore, heat treatment is an indispensable process step before the SLM-forming sample is put into service. In the nickel-based superalloy, the ' gamma ' -phase ' with the main component of Ni 3 Al is an important reinforcing phase, and can play a good role in reinforcing. However, research shows that the GH3230 formed by the SLM can only precipitate a small amount of carbide particles containing solid solution strengthening elements after heat treatment, the strengthening effect of the particles is weak, and the gamma' phase with better strengthening effect is hardly found in the GH 3230. Secondly, the mechanical properties of the material are reduced after heat treatment due to the reduced dislocation density and increased grain size in the sample.
Disclosure of Invention
Aiming at the defects existing in the prior art, the invention aims to provide a method, a material and application for in-situ generation and non-original addition of a reinforcing phase of GH3230, which can realize in-situ and non-in-situ synergistic reinforcement of the reinforcing phase in manufacturing of GH3230 by an SLM (selective laser deposition) process, thereby improving the mechanical properties of the alloy.
In order to achieve the above object, the present invention is realized by the following technical scheme:
In a first aspect, a method for in situ generation and non-original addition of an enhancement phase of GH3230 comprises the steps of:
Selecting GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder to prepare composite powder according to a set proportion;
The composite powder is mixed and stirred at high speed by double centrifugation for many times until the mixture is uniform and has no obvious agglomeration, thus forming GH3230-TiB 2-AlSi10 Mg composite powder;
SLM forming is carried out on the stirred composite powder by utilizing metal additive manufacturing equipment;
And carrying out solution heat treatment on the sample piece after the SLM forming, and then carrying out aging heat treatment to realize that an Al element in AlSi 10 Mg powder and a Ni element in GH3230 alloy powder are separated out to form a gamma' reinforcing phase.
As a further implementation manner, the mass fraction of the TiB 2 powder is 0.5-2% of the mass of the GH3230 alloy powder, and the mass fraction of the AlSi 10 Mg powder is 1-3% of the mass of the GH3230 alloy powder.
As a further implementation mode, the SLM forming process condition is that the laser power is 180-200W, the scanning speed is 750-800mm/s, the powder spreading layer is 30-50 mu m, and the scanning interval is 100-120 mu m.
As a further implementation manner, the particle size distribution of the GH3230 alloy powder and the AlSi 10 Mg powder is 15-53 μm, and the average particle size is 30-40 μm; the average grain diameter of the TiB 2 powder is smaller than 1 mu m.
As a further implementation, the stirring speed is 900-1100rpm, each time is 1-2 minutes, the mixture is cooled to room temperature after each mixing, and the next mixing is carried out until the mixture is uniform and no obvious agglomeration exists.
As a further implementation, the method is characterized in that a tubular heat treatment furnace is adopted for heat treatment, the sample is subjected to solution heat treatment for 2 hours at 1100-1200 ℃ and then is subjected to aging heat treatment for 8 hours at 600-650 ℃.
The second aspect is a GH3230 nickel-based superalloy material, which is characterized in that the material is prepared by adopting any of the above methods of in-situ generation and non-original addition of a reinforcing phase of GH3230, and comprises GH3230-TiB 2-AlSi10 Mg composite powder, consisting of GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder;
Wherein the mass fraction of the TiB 2 powder is 0.5-2% of the mass of the GH3230 alloy powder, and the mass fraction of the AlSi 10 Mg powder is 1-3% of the mass of the GH3230 alloy powder.
As a further implementation manner, the GH3230 alloy powder has a elemental composition of ：C 0.05-0.15％,Cr20-24％,Co<5％,W 13-15％,Mo 1-3％,Al 0.2-0.5％,Ti<0.1％,Fe<3％,La0.005-0.05％,B<0.015％,Si 0.25-0.75％,Mn 0.3-1％,S<0.015％,P<0.03％,Cu<0.5％, and the balance of Ni element and unavoidable impurities.
As a further implementation, the AlSi 10 Mg powder element composition is as follows: zn <0.1%, mg0.2-0.45%, cu <0.05%, ni <0.05%, si 9-11%, fe <0.55%, mn <0.45%, and the balance of Al element and unavoidable impurities.
In the third aspect, the application of the method for in-situ generation and non-original addition of the enhancement phase of GH3230 is applied to the fields of aerospace, petrochemical industry and nuclear energy industry.
The beneficial effects of the invention are as follows:
1. According to the invention, GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder are selected to prepare composite powder according to a set proportion, the composite powder is stirred to form GH3230-TiB 2-AlSi10 Mg composite powder and is subjected to SLM forming, gamma' (Ni 3 Al) reinforcing phase can be further generated in situ after heat treatment, and cracking of the material is avoided in the heat treatment process; on the basis of adding (ex-situ adding) TiB 2 reinforcing phase, the gamma' reinforcing phase generated in situ by heat treatment further plays a role in reinforcing, and the synergistic effect of the two reinforcing phases contributes to improving the bearing capacity of the alloy.
2. According to the invention, by externally adding the AlSi 10 Mg alloy, the content of the Al element in the GH3230 alloy can be improved, so that the alloy generates a gamma' reinforcing phase in situ, and compared with the mode of adding an Al simple substance in the powder process, the method has higher efficiency, is convenient for quantitatively controlling the content of the Al element, has strong practicability and is suitable for industrial production.
Drawings
The accompanying drawings, which are included to provide a further understanding of the invention and are incorporated in and constitute a part of this specification, illustrate embodiments of the invention and together with the description serve to explain the invention.
Fig. 1 is a flow chart of an in-situ generation and non-original addition method of an enhancement phase of GH3230 according to an embodiment of the present invention.
FIG. 2 is a photograph of GH3230-TiB 2 -AlSi10Mg composite powder in an embodiment of the invention.
Fig. 3 is a photograph of the microstructure of the final shaped material in an embodiment of the present invention.
FIG. 4 shows the results of the normal temperature Vickers hardness test in the examples of the present invention.
FIG. 5 is a graph showing the results of normal temperature tensile stress strain curves in the examples of the present invention.
Detailed Description
It should be noted that the following detailed description is illustrative and is intended to provide further explanation of the invention. Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs.
The term "GH3230": the solid solution strengthening type high-temperature alloy takes Cr, W and Mo as main strengthening elements, has the service temperature ranging from 700 ℃ to 1050 ℃, and has good strength, thermal stability and oxidation resistance.
The term "gamma' phase": the alloy comprises Ni 3 Al as an important constituent element, wherein the gamma '-phase is an important reinforcing phase in the nickel-based superalloy, and can be separated out in the alloy through ageing heat treatment, but the GH3230 alloy after the SLM forming is subjected to heat treatment almost has no separation of the gamma' -phase because of less Al element in the GH3230 alloy, and the mechanical property of the component is weakened due to grain growth and dislocation density reduction caused by heat treatment.
The term "reinforcing phase particles": in the alloy, reinforcing phase particles uniformly distributed in a matrix can play a role in reinforcing the mechanical property of the alloy, and researches show that the smaller the size of the reinforcing phase particles, the more uniform the distribution and the more the number of the reinforcing phase particles, the more remarkable the reinforcing effect is.
Example 1
In a typical embodiment of the present invention, as shown in fig. 1, a method for in-situ generation and non-original addition of a reinforcing phase of GH3230 is used to obtain a GH3230-TiB 2-AlSi10 Mg composite powder, which comprises the following steps:
S101, selecting GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder to prepare composite powder according to a set proportion.
In the step S101, the mass fraction of TiB 2 powder is 0.5-2% of the mass of GH3230 alloy powder, and the mass fraction of AlSi 10 Mg powder is 1-3% of the mass of GH3230 alloy powder. The TiB 2 powder content is not more than 2% because the addition of excessive TiB 2 powder particles by means of externally adding the powder mixture can lead to non-uniformity of the powder mixture and further affect the SLM forming effect.
The grain sizes of GH3230 alloy powder and AlSi 10 Mg powder are distributed between 15 and 53 mu m, and the average grain size is between 30 and 40 mu m; the average grain diameter of the TiB 2 powder is smaller than 1 mu m.
In this example, a GH3230 alloy powder having an average particle diameter of 30.04 μm, a TiB 2 powder having an average particle diameter of 500nm, and an AlSi 10 Mg powder having an average particle diameter of 32.1 μm were selected, according to GH3230: the mass ratio of TiB 2：AlSi10 Mg powder is 97:1:2, and composite powder is prepared.
S102, carrying out double-centrifugation high-speed mixing and stirring on the composite powder for a plurality of times until the mixture is uniformly mixed and no obvious agglomeration exists, so as to form GH3230-TiB 2-AlSi10 Mg composite powder.
The GH3230-TiB 2-AlSi10 Mg composite powder is prepared by a high-speed mixing technology. The requirement is that TiB 2 powder is uniformly adhered to the surfaces of GH3230 alloy powder and AlSi 10 Mg powder, a large amount of aggregation is avoided, alSi 10 Mg powder is randomly distributed in the GH3230 powder, and the composite powder has certain fluidity and can meet the powder laying requirement in the SLM forming process.
And (3) carrying out double-centrifugal high-speed mixing and stirring on the composite powder prepared in the step (S101), wherein the mixing speed of stirring is 900-1100rpm, the time of stirring is 1-2 minutes each time, the preferable mixing speed is 1000rpm, the time of stirring is 1.5 minutes each time, cooling to room temperature after each time of mixing is finished, and then carrying out next mixing until the powder is uniformly mixed and has no obvious agglomeration, thereby forming the GH3230-TiB 2-AlSi10 Mg composite powder.
S103, carrying out SLM (selective laser sintering) forming on the mixed GH3230-TiB 2-AlSi10 Mg composite powder by using metal additive manufacturing equipment to obtain a sample.
Carrying out SLM forming on the GH3230-TiB 2-AlSi10 Mg composite powder obtained in the last step by utilizing Concept Laser Mlab R metal additive manufacturing equipment, wherein the laser power is 180-200W, the scanning speed is 750-800mm/s, the powder paving layer thickness is 30-50 mu m, and the scanning interval is 100-120 mu m. Preferred process parameters are as follows: the laser power is 190W, the scanning speed is 800mm/s, the layer thickness is 40 μm, and the scanning interval is 110 μm.
S104, carrying out solution heat treatment on the sample piece after the SLM forming, and then carrying out aging heat treatment to realize that an Al element in the AlSi 10 Mg powder and a Ni element in the GH3230 alloy powder are separated out to form a gamma' reinforcing phase, as shown in figure 2.
Wherein, the heat treatment adopts an NBD-T1500 tubular heat treatment furnace, the sample is firstly subjected to solution heat treatment for 2 hours at 1150 ℃, and then the sample is subjected to aging heat treatment for 8 hours at 620 ℃.
For comparison with GH3230-TiB 2 alloys that were not formed by the present method, comparative example 1:
Comparative example GH3230-1wt.% TiB 2 powder was SLM formed and heat treated using the process in steps (3) and (4).
That is, comparative example 1 differs from this example in that AlSi 10 Mg powder was not added
As shown in fig. 2, in the GH3230-TiB 2-AlSi10 Mg alloy powder of the present invention, tiB 2 particles are uniformly distributed without significant agglomeration, and part of nano-scale TiB 2 particles are attached to the surfaces of GH3230 and AlSi 10 Mg powder; as can be seen from the EDS spectrum sweep profile, the AlSi 10 Mg powder is uniformly distributed, and no agglomeration phenomenon occurs.
As shown in FIG. 3, the GH3230-TiB 2-AlSi10 Mg alloy in the invention has large-sized carbide particles precipitated and a large amount of gamma' (Ni 3 Al) phase with the diameter smaller than 500nm precipitated after heat treatment, while the precipitates in the GH3230-TiB 2 alloy in comparative example 1 are mainly large-sized carbide phases and have a small number.
As shown in FIG. 4, the room temperature tensile properties of the two groups of alloys prepared in the examples and the comparative examples of the present invention are compared, and the result shows that the GH3230-TiB 2-AlSi10 Mg alloy prepared in the first example has a yield strength of 856MPa and a tensile strength of 1214MPa; the GH3230-TiB 2 alloy in comparative example 1 had a yield strength of 503MPa and a tensile strength of 901MPa.
It can be seen that the yield strength of the alloy prepared by the method of the present disclosure is improved by about 70% and the tensile strength is improved by about 35%. This is because, after the method disclosed by the present disclosure is adopted, the content of Al element in the material is greatly improved, and in the aging heat treatment process of the sample piece after SLM forming, the Al element can form γ' (Ni 3 Al) phase with Ni element in the matrix (as shown in fig. 5), and the reinforcing phase is uniformly distributed in the matrix, so that dislocation movement and plastic deformation can be blocked in the stretching process, so that the mechanical properties of the material are improved.
In comparative example 1, alSi 10 Mg was not added, GH3230 was used as a solid solution-strengthened nickel-based superalloy, and the content of Al element in the alloy was small, and even if the sample after molding was subjected to aging heat treatment, a γ' strengthening phase could not be precipitated (as shown in FIG. 3); in addition, long-term heat treatment can also lead to grain growth and reduced dislocation density, thereby affecting alloy performance.
In summary, the alloy member prepared by the method of the embodiment can further generate a gamma' (Ni 3 Al) reinforcing phase in situ after heat treatment, and the material cannot crack in the heat treatment process.
The room temperature hardness of the GH3230-TiB 2-AlSi10 Mg composite powder is improved by about 46% through a sample piece formed by SLM, and the room temperature tensile strength is improved by about 35%, because the gamma' reinforcing phase generated in situ by heat treatment further plays a reinforcing effect on the basis of the reinforcing phase of the externally added (ex-situ added) TiB 2, and the synergistic effect of the two reinforcing phases contributes to the improvement of the bearing capacity of the alloy.
According to the method, the content of the Al element in the GH3230 alloy can be increased by externally adding the AlSi 10 Mg alloy, so that the alloy generates a gamma' reinforcing phase in situ, and compared with the mode of adding the Al element in the powder process, the method is higher in efficiency, convenient to quantitatively control the content of the Al element, high in practicability and suitable for industrial production.
Example two
The GH3230 nickel-based superalloy material is prepared by adopting the reinforcing phase in-situ generation and non-original addition method of GH3230 in the embodiment I, and comprises GH3230-TiB 2-AlSi10 Mg composite powder which consists of GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder;
Wherein the mass fraction of the TiB 2 powder is 0.5-2% of the mass of the GH3230 alloy powder, and the mass fraction of the AlSi 10 Mg powder is 1-3% of the mass of the GH3230 alloy powder.
The GH3230 alloy powder comprises ：C 0.05-0.15％,Cr 20-24％,Co<5％,W 13-15％,Mo 1-3％,Al 0.2-0.5％,Ti<0.1％,Fe<3％,La 0.005-0.05％,B<0.015％,Si0.25-0.75％,Mn 0.3-1％,S<0.015％,P<0.03％,Cu<0.5％, of Ni and unavoidable impurities.
The AlSi 10 Mg powder elements consist of the following: zn <0.1%, mg 0.2-0.45%, cu <0.05%, ni <0.05%, si 9-11%, fe <0.55%, mn <0.45%, and the balance of Al element and unavoidable impurities.
After the composite powder is formed by adding the alloy system and TiB 2 powder, the TiB 2 particles are not decomposed and can be uniformly distributed in the matrix to play a role in reinforcing phases, after the sample piece is subjected to solid solution and aging heat treatment, al element in the AlSi 10 Mg alloy and Ni element in the nickel-based alloy form gamma' (Ni 3 Al) phases, and the phases serve as reinforcing phases generated in situ, so that the effect of reinforcing the mechanical properties of the alloy can be achieved.
Example III
The GH3230-TiB 2-AlSi10 Mg composite powder prepared by the method in the first embodiment is applied to the fields of aerospace, petrochemical industry and nuclear energy industry, and is suitable for hot end parts with complex structures such as gas turbines, aeroengines and the like.
The above description is only of the preferred embodiments of the present invention and is not intended to limit the present invention, but various modifications and variations can be made to the present invention by those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (7)
1. The in-situ generation and non-original addition method of the enhancement phase of GH3230 is characterized by comprising the following steps:
Selecting GH3230 alloy powder, tiB 2 powder and AlSi 10 Mg powder to prepare composite powder according to a set proportion;
The composite powder is mixed and stirred at high speed by double centrifugation for many times until the mixture is uniform and has no obvious agglomeration, thus forming GH3230-TiB 2-AlSi10 Mg composite powder;
SLM forming is carried out on the stirred composite powder by utilizing metal additive manufacturing equipment;
carrying out solution heat treatment on the sample piece after the SLM forming, and then carrying out aging heat treatment to realize that an Al element in AlSi 10 Mg powder and a Ni element in GH3230 alloy powder are separated out to form a gamma' reinforcing phase;
The mass fraction of the TiB2 powder is 0.5-2% of the mass of the GH3230 alloy powder, and the mass fraction of the AlSi 10 Mg powder is 1-3% of the mass of the GH3230 alloy powder;
the SLM forming process conditions are that the laser power is 180-200W, the scanning speed is 750-800mm/s, the powder spreading layer thickness is 30-50 mu m, and the scanning interval is 100-120 mu m;
The heat treatment adopts a tubular heat treatment furnace, wherein the solid solution heat treatment is carried out on the sample for 2 hours at 1100-1200 ℃, and then the aging heat treatment is carried out on the sample for 8 hours at 600-650 ℃.
2. The method for in-situ generation and non-original addition of a reinforcing phase of GH3230 according to claim 1, wherein the particle size distribution of GH3230 alloy powder and AlSi 10 Mg powder is 15-53 μm, and the average particle size is 30-40 μm; the average particle size of the TiB 2 powder is less than 1 mu m.
3. The method for in-situ generation and non-original addition of a reinforcing phase of GH3230 according to claim 1, wherein the stirring and mixing speed is 900-1100rpm, each time is 1-2 minutes, the reinforcing phase is cooled to room temperature after each mixing, and the next mixing is carried out until the mixing is uniform and no obvious agglomeration exists.
4. A GH3230 nickel-based superalloy material prepared by an in situ generation and non-original addition method of a reinforcing phase of GH3230 as claimed in any one of claims 1 to 3.
5. The GH3230 nickel-based superalloy material according to claim 4, wherein the elemental composition of the GH3230 alloy powder is ：C 0.05-0.15%,Cr 20-24%,Co < 5%, W 13-15%, Mo 1-3%,Al 0.2-0.5%,Ti<0.1%, Fe<3%, La 0.005-0.05%, B < 0.015%, Si 0.25-0.75%, Mn 0.3-1%, S <0.015%, P<0.03%, Cu<0.5%, balance Ni and unavoidable impurities.
6. The GH3230 nickel-based superalloy material according to claim 5, wherein the AlSi 10 Mg powder elements consist of: zn <0.1%, mg 0.2-0.45%, cu <0.05%, ni <0.05%, si 9-11%, fe <0.55%, mn <0.45%, and the balance of Al element and unavoidable impurities.
7. Use of the enhanced phase in situ generation and non-original addition method of GH3230 according to any one of claims 1-3, characterized by application in the fields of aerospace, petrochemical, nuclear energy industry.
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| CN202310265411.2A CN116237542B (en) | 2023-03-15 | 2023-03-15 | In-situ generation and non-original addition method, material and application of reinforcing phase of GH3230 |
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| CN202310265411.2A CN116237542B (en) | 2023-03-15 | 2023-03-15 | In-situ generation and non-original addition method, material and application of reinforcing phase of GH3230 |
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| CN116237542B true CN116237542B (en) | 2024-08-13 |
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| CN113061782A (en) * | 2021-03-16 | 2021-07-02 | 山东大学 | GH3230 nickel-based superalloy material, method for eliminating micro-cracks formed by selective laser melting and application thereof |
| CN114350998A (en) * | 2021-12-01 | 2022-04-15 | 华南理工大学 | High-performance two-phase hybrid reinforced aluminum matrix composite and preparation method thereof |
| CN115369276A (en) * | 2022-08-15 | 2022-11-22 | 哈尔滨工业大学（威海） | SiC and TiB 2 Double-phase reinforced aluminum-based composite material and preparation method thereof |
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| JP5843291B2 (en) * | 2013-03-18 | 2016-01-13 | トーカロ株式会社 | Composite sprayed coating |
| FR3008014B1 (en) * | 2013-07-04 | 2023-06-09 | Association Pour La Rech Et Le Developpement De Methodes Et Processus Industriels Armines | METHOD FOR THE ADDITIVE MANUFACTURING OF PARTS BY FUSION OR SINTERING OF POWDER PARTICLES BY MEANS OF A HIGH ENERGY BEAM WITH POWDERS SUITABLE FOR THE PROCESS/MATERIAL TARGETED COUPLE |
| US20190032175A1 (en) * | 2017-02-01 | 2019-01-31 | Hrl Laboratories, Llc | Aluminum alloys with grain refiners, and methods for making and using the same |
| CN107737941A (en) * | 2017-11-02 | 2018-02-27 | 长沙新材料产业研究院有限公司 | TiB for increasing material manufacturing2Strengthen the preparation method of Al alloy powder |
| CN108330347A (en) * | 2018-02-05 | 2018-07-27 | 上海交通大学 | The preparation method of aluminum matrix composite is prepared based on selective laser fusing |
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| CN113881868B (en) * | 2021-12-07 | 2022-03-04 | 天津大学 | Improved method for eliminating solid solution strengthening type nickel-based alloy solidification cracks formed by SLM (selective laser melting) |
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| CN113061782A (en) * | 2021-03-16 | 2021-07-02 | 山东大学 | GH3230 nickel-based superalloy material, method for eliminating micro-cracks formed by selective laser melting and application thereof |
| CN114350998A (en) * | 2021-12-01 | 2022-04-15 | 华南理工大学 | High-performance two-phase hybrid reinforced aluminum matrix composite and preparation method thereof |
| CN115369276A (en) * | 2022-08-15 | 2022-11-22 | 哈尔滨工业大学（威海） | SiC and TiB 2 Double-phase reinforced aluminum-based composite material and preparation method thereof |
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