CN112695220A - Selective laser melting forming nano TiB2Preparation method of reinforced aluminum-based composite material - Google Patents
Selective laser melting forming nano TiB2Preparation method of reinforced aluminum-based composite material Download PDFInfo
- Publication number
- CN112695220A CN112695220A CN202011375114.6A CN202011375114A CN112695220A CN 112695220 A CN112695220 A CN 112695220A CN 202011375114 A CN202011375114 A CN 202011375114A CN 112695220 A CN112695220 A CN 112695220A
- Authority
- CN
- China
- Prior art keywords
- powder
- tib
- selective laser
- nano
- laser melting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000002131 composite material Substances 0.000 title claims abstract description 34
- 238000002844 melting Methods 0.000 title claims abstract description 29
- 230000008018 melting Effects 0.000 title claims abstract description 28
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 23
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 23
- 238000000034 method Methods 0.000 title claims abstract description 22
- 239000000843 powder Substances 0.000 claims abstract description 67
- 239000002245 particle Substances 0.000 claims abstract description 29
- 239000011159 matrix material Substances 0.000 claims abstract description 24
- 229910033181 TiB2 Inorganic materials 0.000 claims abstract description 23
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 13
- 229910003407 AlSi10Mg Inorganic materials 0.000 claims abstract description 13
- 238000005516 engineering process Methods 0.000 claims abstract description 11
- 230000003014 reinforcing effect Effects 0.000 claims abstract description 9
- 230000001788 irregular Effects 0.000 claims abstract description 8
- 238000002156 mixing Methods 0.000 claims description 24
- 239000011812 mixed powder Substances 0.000 claims description 13
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 12
- 238000002360 preparation method Methods 0.000 claims description 10
- 230000008569 process Effects 0.000 claims description 8
- 229910052786 argon Inorganic materials 0.000 claims description 6
- 239000000463 material Substances 0.000 claims description 6
- 238000010309 melting process Methods 0.000 claims description 4
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 claims description 2
- 238000005728 strengthening Methods 0.000 abstract description 7
- 230000000694 effects Effects 0.000 abstract description 4
- 239000006185 dispersion Substances 0.000 abstract description 3
- 230000002195 synergetic effect Effects 0.000 abstract description 2
- 238000001035 drying Methods 0.000 description 8
- 238000001816 cooling Methods 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000003892 spreading Methods 0.000 description 4
- 230000007480 spreading Effects 0.000 description 4
- 238000010521 absorption reaction Methods 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 238000012356 Product development Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000001678 irradiating effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000002667 nucleating agent Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
Images
Classifications
-
- 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
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- B22F1/0003—
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
Abstract
The embodiment of the invention provides a nano TiB prepared by selective laser melting2A reinforced aluminum matrix composite and a method thereof. The method comprises the following steps: (1) selecting purity>99.9% of high-purity spherical AlSi10Mg powder with a particle size of 15-53 μm; purity of>99.9% of irregular knots with particle size of 50-100nmStructure of TiB2Powder; (2) the two powders are mechanically mixed and uniformly mixed under the condition of not damaging the original characteristics of the matrix powder; (3) and preparing a composite material forming sample with reinforcing phase particles uniform to the aluminum alloy matrix and high density by adopting a selective laser melting forming technology. By adding the nano reinforced particles into the aluminum alloy matrix, the comprehensive mechanical property of the aluminum alloy can be effectively improved under the synergistic strengthening effect of fine grain strengthening and dispersion strengthening.
Description
Technical Field
The invention belongs to the technical field of laser additive manufacturing, and particularly relates to nano TiB2A reinforced aluminum matrix composite material and a preparation method thereof.
Background
Selective Laser Melting (SLM), the leading edge and potential forming technique in the field of additive manufacturing technology, is an important development direction of advanced manufacturing technology. The selective laser melting can shorten the product development period, form parts with complex structures and reduce the personalized customization cost. Meanwhile, due to a rapid fusing mechanism in the selective laser melting process, a microstructure with fine grains can be obtained in the workpiece, and the comprehensive mechanical property of the workpiece is improved.
The aluminum alloy has the advantages of low density, high specific strength, good heat conduction, electric conduction and corrosion resistance, and the like. The laser absorptivity of the aluminum material is low and is only 9%, and the thermal conductivity of the aluminum material is high and reaches 237Wm-1K-1. The low laser absorption rate and the high thermal conductivity cause the low temperature of a molten pool in the forming process, the high viscosity of a metal solution, poor fluidity and easy generation of defects such as pores, cracks and the like after solidification, thereby restricting the development of the technical field of melting of the aluminum alloy in a laser selection area.
TiB2The laser absorption rate is about 80%, and the thermal conductivity is low and is only 25Wm-1K-1Adding nano TiB into the aluminum alloy matrix2The ceramic powder can effectively improve the laser absorption rate of the material and improve the heat distribution in the forming process of the material, and the nano reinforcing particles can be used as a heterogeneous nucleating agent to play a fine grain reinforcing effect, so that the comprehensive mechanical property of the aluminum alloy material is improved.
Therefore, a method suitable for nano TiB is sought2The forming process of the laser selective melting technology of the reinforced aluminum-based composite material and the improvement of the comprehensive mechanical property of an aluminum alloy matrix are problems to be solved urgently by technical personnel in the field.
Disclosure of Invention
The invention aims to provide a laser selective melting forming nano TiB2The preparation method of the reinforced aluminum-based composite material is characterized by comprising the following steps:
(1) preparing mixed powder: comprises high-purity spherical AlSi10Mg powder and irregular TiB2Powder;
(2) uniformly mixing the two powders under the condition of not damaging the original characteristics of the matrix powder;
(3) and preparing a composite material forming sample with reinforcing phase particles uniform to the aluminum alloy matrix and high density by adopting a selective laser melting forming technology.
Preferably, in step 1: mixing 1-4 wt.% of nano TiB2Formulating a mixed powder with 96-99 wt.% of an AlSi10Mg powder, wherein: purity of AlSi10Mg powder>99.9 percent, the particle size is 15-53 mu m, and the shape is a high-purity sphere; TiB2Purity of the powder>99.9 percent, the particle size is 50-100nm, and the appearance is an irregular structure.
Preferably, the SLM forming technology is adopted, mixed powder mechanically mixed in the step (2) is used as a printing material, and TiB is manufactured by adjusting laser energy density in the SLM forming technology in a laminated mode2a/AlSi 10Mg composite; wherein: the value range of the laser energy density is 43.86-75.75J/mm-3P is laser power, V is laser scanning speed, H is laser scanning interval, and D is powder laying thickness.
Preferably, the adjustment of the laser energy density in the step (3) is realized by adjusting laser power, laser scanning speed and laser scanning interval; wherein: the value range of the laser power P is 375-425W, the value range of the laser scanning speed V is 1100-1500mm/s, and the value range of the scanning interval H is 0.15-0.19 mm.
Preferably, the process parameters of the mechanical mixing are as follows: the powder mixing speed is 12rpm, and the powder mixing time is 120-280 min.
Preferably, in the step (3), high-purity argon is introduced into the forming cavity for protection during selective laser melting forming.
The technical scheme of the invention is based on the selective laser melting forming technology, and compared with the prior art, the selective laser melting forming method has the following effects:
(1) mechanical powder mixing is carried out by adopting a mechanical powder mixing device, and the nano TiB2The reinforcing particles are uniformly dispersed in the aluminum alloy matrix powder without deteriorating the original characteristics of the matrix powder. And irradiating the powder bed by high-energy laser, melting and solidifying the powder, and forming layer by layer to finally realize the formation of the three-dimensional solid component.
(2) In the selective laser melting process, the nano TiB2The reinforced particles become nucleation particles, so that the nucleation rate is improved, and the fine grains are reinforced. In addition, the nano TiB is dispersed and distributed2The reinforcing particles can have a dispersion strengthening effect. The nanometer TiB prepared by selective laser melting is obtained by the synergistic strengthening effect of fine grain strengthening and dispersion strengthening2The reinforced aluminum-based composite material has good comprehensive mechanical properties.
Drawings
FIG. 1 is a micrograph of a mixed powder in example 1;
FIG. 2 shows the preparation of nano TiB by selective laser melting in example 12XOZ optical microscopic picture of the reinforced aluminum matrix composite material sample;
fig. 3 is a flow chart of a method of implementing an embodiment.
Detailed Description
In order to make the aforementioned objects, features and advantages of the present invention comprehensible, embodiments accompanied with figures are described in further detail below.
The technical solutions of the present invention will be described in detail below with reference to the accompanying drawings and various embodiments, but the scope of the present invention is not limited thereto;
example 1
Selective laser melting nano TiB2The preparation method of the particle reinforced aluminum matrix composite material comprises the following steps:
the method comprises the following steps: mixed powder of purity>99.9 percent, the particle size is 15-53 mu m, the morphology is high-purity spherical AlSi10Mg powder, and the purity is>99.9 percent of TiB with particle size of 50-100nm and irregular morphology2Powder composition, mixing of TiB in powder2The mass fraction of (1 wt.%), and fig. 1 shows the morphology of the composite powder after mixing;
step two: and (3) putting the mixed powder obtained in the step (1) into a mixing barrel. The powder mixing is carried out by rotating forward for 30min at the rotation speed of 12rpm, rotating backward for 30min at the rotation speed of 12rpm, repeating the steps once and mixing the powder for 120 min.
Step three: and (3) putting the mixed composite powder into an oven, wherein the powder drying temperature is 120 ℃, the powder drying time is 3 hours, and cooling along with the oven.
Step four: establishing a three-dimensional digital model of a sample to be processed, and performing layered slicing on the model by using layered software;
step five: and taking the composite powder baked in the third step as a raw material for selective laser melting forming, introducing high-purity argon into a forming cavity for protection, wherein the laser power is 400W, the scanning speed is 1500mm/s, the scanning distance is 0.17mm, and the powder spreading thickness is 0.03 mm.
FIG. 2 is a metallographic photograph of an XOZ plane (i.e., a direction perpendicular to a substrate) of a sample under a process with a laser power P of 400W and a scanning speed v of 1500mm/s, and it can be seen that a high-density formed sample can be prepared under the process parameters, and TiB2Reinforcing phase is uniformly distributed in the AlSi101Mg matrix, and finally the obtained nano TiB2The room temperature mechanical properties of the particle reinforced aluminum matrix composite are detailed in table 1.
Example 2
Selective laser melting nano TiB2The preparation method of the particle reinforced aluminum matrix composite material comprises the following steps:
the method comprises the following steps: mixed powder of purity>99.9% and the particle size is 15-53 μmHigh purity spherical AlSi10Mg powder, and purity>99.9 percent of TiB with particle size of 50-100nm and irregular morphology2Powder composition, mixing of TiB in powder2The mass fraction of (a) is 2 wt.%.
Step two: and (3) putting the mixed powder obtained in the step (1) into a mixing barrel. The powder mixing is carried out by rotating forwards for 50min at 12rpm and reversely for 50min at 12rpm, repeating the steps for one time to mix the powder for 200min,
step three: and (3) putting the mixed composite powder into an oven, wherein the powder drying temperature is 120 ℃, the powder drying time is 3 hours, and cooling along with the oven.
Step four: establishing a three-dimensional digital model of a sample to be processed, and performing layered slicing on the model by using layered software;
step five: and taking the composite powder baked in the third step as a raw material for selective laser melting forming, introducing high-purity argon into a forming cavity for protection, wherein the laser power is 400W, the scanning speed is 1300mm/s, the scanning distance is 0.19mm, and the powder spreading thickness is 0.03 mm.
Finally obtained nano TiB2The room temperature mechanical properties of the particle reinforced aluminum matrix composite are detailed in table 1.
Example 3
Selective laser melting nano TiB2The preparation method of the particle reinforced aluminum matrix composite material comprises the following steps:
the method comprises the following steps: mixed powder of purity>99.9 percent, the particle size is 15-53 mu m, the morphology is high-purity spherical AlSi10Mg powder, and the purity is>99.9 percent of TiB with particle size of 50-100nm and irregular morphology2Powder composition, mixing of TiB in powder2The mass fraction of (a) is 3 wt.%.
Step two: and (3) putting the mixed powder obtained in the step (1) into a mixing barrel. The powder mixing is carried out by rotating forward for 70min at the rotation speed of 12rpm, rotating backward for 70min at the rotation speed of 12rpm, repeating the steps once and mixing the powder for 280 min.
Step three: and (3) putting the mixed composite powder into an oven, wherein the powder drying temperature is 120 ℃, the powder drying time is 3 hours, and cooling along with the oven.
Step four: establishing a three-dimensional digital model of a sample to be processed, and performing layered slicing on the model by using layered software;
step five: and taking the composite powder baked in the third step as a raw material for selective laser melting forming, introducing high-purity argon into a forming cavity for protection, wherein the laser power is 400W, the scanning speed is 1300mm/s, the scanning distance is 0.19mm, and the powder spreading thickness is 0.03 mm.
Finally obtained nano TiB2The room temperature mechanical properties of the particle reinforced aluminum matrix composite are detailed in table 1.
Comparative example 1
The method comprises the following steps: putting high-purity spherical AlSi10Mg powder with the purity of 99.9 percent and the particle size of 15-53 mu m and the appearance of high-purity spherical AlSi10Mg into an oven, wherein the powder drying temperature is 120 ℃, the powder drying time is 3h, and cooling along with the oven;
step two: establishing a three-dimensional digital model of a sample to be processed, and performing layered slicing on the model by using layered software;
step three: and (3) taking the composite powder baked in the step one as a raw material for selective laser melting forming, introducing high-purity argon into a forming cavity for protection, wherein the laser power is 400W, the scanning speed is 1300mm/s, the scanning distance is 0.19mm, and the powder spreading thickness is 0.03 mm.
The room temperature mechanical properties of the finally obtained AlSi10Mg are detailed in table 1.
TABLE 1 mechanical properties at room temperature of examples and comparative examples
| Parameter(s) | Example 1 | Example 2 | Example 3 | Comparative example 1 |
| Tensile strength | 438 | 440 | 394 | 420 |
| Elongation percentage | 11 | 9.5 | 4.5 | 5.5 |
As can be seen from Table 1, the nano TiB prepared by the embodiment of the invention2Adding nano TiB with proper proportion into particle reinforced aluminum-based composite material2Can obviously improve the comprehensive mechanical property of the aluminum alloy material, and can be used as TiB2When the content is 1 wt.%, the elongation is lower than that without adding the nano TiB2The aluminum alloy is doubled, and the tensile strength is improved slightly. When TiB2At contents up to 3 wt.%, both tensile strength and elongation appear to decrease.
It will be apparent to those skilled in the art that various changes and modifications may be made in the invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (6)
1. Selective laser melting forming nano TiB2The preparation method of the reinforced aluminum-based composite material is characterized by comprising the following steps:
(1) preparing mixed powder: comprises high-purity spherical AlSi10Mg powder and irregular TiB2Powder;
(2) uniformly mixing the two powders under the condition of not damaging the original characteristics of the matrix powder;
(3) and preparing a composite material forming sample with reinforcing phase particles uniform to the aluminum alloy matrix and high density by adopting a selective laser melting forming technology.
2. The selective laser melting nano-TiB as claimed in claim 12The preparation method of the reinforced aluminum matrix composite material is characterized in that in the step 1: mixing 1-4 wt.% of nano TiB2Formulating a mixed powder with 96-99 wt.% of an AlSi10Mg powder, wherein: purity of AlSi10Mg powder>99.9 percent, the particle size is 15-53 mu m, and the shape is a high-purity sphere; TiB2Purity of the powder>99.9 percent, the particle size is 50-100nm, and the appearance is an irregular structure.
3. The selective laser melting nano-TiB as claimed in claim 12The preparation method of the reinforced aluminum-based composite material is characterized in that an SLM forming technology is adopted, mixed powder which is mechanically mixed in the step (2) is used as a printing material, and TiB is manufactured in a laminated mode by adjusting laser energy density in the SLM forming technology2a/AlSi 10Mg composite; wherein: the value range of the laser energy density is 43.86-75.75J/mm-3P is laser power, V is laser scanning speed, H is laser scanning interval, and D is powder laying thickness.
4. The selective laser melting nano-TiB as claimed in claim 32The preparation method of the reinforced aluminum matrix composite is characterized in that the adjustment of the laser energy density in the step (3) is realized by adjusting the laser power, the laser scanning speed and the laser scanning interval; wherein: the value range of the laser power P is 375-425W, the value range of the laser scanning speed V is 1100-1500mm/s, and the value range of the scanning interval H is 0.15-0.19 mm.
5. The selective laser melting process for preparing nano TiB as claimed in claim 32The method for reinforcing the aluminum matrix composite is characterized in that the mechanical mixing process parameters are as follows: the powder mixing speed is 12rpm, and the powder mixing time is 120-280 min.
6. The selective laser melting process for preparing nano TiB as claimed in claim 32The method for reinforcing the aluminum-based composite material is characterized in that in the step (3), high-purity argon is introduced into a forming cavity for protection in the selective laser melting forming process.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011375114.6A CN112695220A (en) | 2020-11-30 | 2020-11-30 | Selective laser melting forming nano TiB2Preparation method of reinforced aluminum-based composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011375114.6A CN112695220A (en) | 2020-11-30 | 2020-11-30 | Selective laser melting forming nano TiB2Preparation method of reinforced aluminum-based composite material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN112695220A true CN112695220A (en) | 2021-04-23 |
Family
ID=75506020
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011375114.6A Pending CN112695220A (en) | 2020-11-30 | 2020-11-30 | Selective laser melting forming nano TiB2Preparation method of reinforced aluminum-based composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112695220A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113798501A (en) * | 2021-08-10 | 2021-12-17 | 西安理工大学 | Nano Al2O3Reinforced 3D printing aluminum-based composite material and preparation method thereof |
| CN114192799A (en) * | 2021-12-07 | 2022-03-18 | 重庆大学 | Selective laser melting forming Inconel718 composite material and preparation method 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 |
| CN114769619A (en) * | 2022-03-08 | 2022-07-22 | 南京理工大学 | Laser additive manufacturing method for high-toughness titanium-based composite material with multiple reaction systems |
| CN116900306A (en) * | 2023-09-14 | 2023-10-20 | 内蒙古工业大学 | AlSi10Mg/ZrO 2 Composite metal powder and forming process thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105014073A (en) * | 2015-08-18 | 2015-11-04 | 上海航天精密机械研究所 | TC4 titanium alloy laser selective melting material additive manufacturing and heat treatment method |
| CN107760933A (en) * | 2017-09-11 | 2018-03-06 | 南京航空航天大学 | A kind of 3D printing strengthens Al alloy powder and preparation method thereof with in-situ nano complex phase ceramic |
| CN107774996A (en) * | 2017-10-11 | 2018-03-09 | 华中科技大学 | A kind of integral forming method of the part of more material gradient lattice structures |
| CN108315577A (en) * | 2018-02-02 | 2018-07-24 | 上海交通大学 | Laser gain material manufacture 7XXX systems in-situ Al-base composition powder and preparation |
| 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 |
| WO2019050973A1 (en) * | 2017-09-05 | 2019-03-14 | University Of Utah Research Foundation | Methods and systems for 3d printing with powders |
-
2020
- 2020-11-30 CN CN202011375114.6A patent/CN112695220A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105014073A (en) * | 2015-08-18 | 2015-11-04 | 上海航天精密机械研究所 | TC4 titanium alloy laser selective melting material additive manufacturing and heat treatment method |
| WO2019050973A1 (en) * | 2017-09-05 | 2019-03-14 | University Of Utah Research Foundation | Methods and systems for 3d printing with powders |
| CN107760933A (en) * | 2017-09-11 | 2018-03-06 | 南京航空航天大学 | A kind of 3D printing strengthens Al alloy powder and preparation method thereof with in-situ nano complex phase ceramic |
| CN107774996A (en) * | 2017-10-11 | 2018-03-09 | 华中科技大学 | A kind of integral forming method of the part of more material gradient lattice structures |
| CN108315577A (en) * | 2018-02-02 | 2018-07-24 | 上海交通大学 | Laser gain material manufacture 7XXX systems in-situ Al-base composition powder and preparation |
| 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 |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113798501A (en) * | 2021-08-10 | 2021-12-17 | 西安理工大学 | Nano Al2O3Reinforced 3D printing aluminum-based composite material and preparation method 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 |
| CN114192799A (en) * | 2021-12-07 | 2022-03-18 | 重庆大学 | Selective laser melting forming Inconel718 composite material and preparation method thereof |
| CN114769619A (en) * | 2022-03-08 | 2022-07-22 | 南京理工大学 | Laser additive manufacturing method for high-toughness titanium-based composite material with multiple reaction systems |
| CN114769619B (en) * | 2022-03-08 | 2024-04-05 | 南京理工大学 | High-strength and high-toughness titanium-based composite material multi-reaction system laser additive manufacturing method |
| CN116900306A (en) * | 2023-09-14 | 2023-10-20 | 内蒙古工业大学 | AlSi10Mg/ZrO 2 Composite metal powder and forming process thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112695220A (en) | Selective laser melting forming nano TiB2Preparation method of reinforced aluminum-based composite material | |
| CN108330344B (en) | 3D printing 7xxx aluminum alloy and preparation method thereof | |
| US20240060156A1 (en) | Method for preparing nano-phase reinforced nickel-based high-temperature alloy using micron ceramic particles | |
| CN111957967B (en) | Method for preparing multi-scale ceramic phase reinforced metal composite material through 3D printing | |
| CN109022920B (en) | Crack-free 4D printing titanium-nickel shape memory alloy and preparation method thereof | |
| CN111940723A (en) | Nano ceramic metal composite powder for 3D printing and application | |
| CN111872386B (en) | 3D printing process method of high-strength aluminum-magnesium alloy | |
| CN111235417A (en) | High-performance aluminum-based composite material based on selective laser melting and forming and preparation method thereof | |
| CN112191854B (en) | Cemented carbide powder for 3D printing and application thereof | |
| CN113600812B (en) | Metal powder and preparation method thereof, metal alloy and preparation method thereof | |
| CN113426996B (en) | Shape memory alloy-based composite intelligent material and preparation method thereof | |
| CN112251646A (en) | Titanium alloy powder of endogenous nano composite ceramic particles and preparation method and application thereof | |
| CN109365810B (en) | Method for preparing copper-based shape memory alloy in any shape in situ by laser and product | |
| CN110744058A (en) | Preparation method for in-situ synthesis of copper-based composite material | |
| CN112191843A (en) | Method for preparing Ti-1Al-8V-5Fe alloy material by selective laser melting | |
| CN110976845A (en) | Powder modification method for eliminating thermal cracks of 7075 aluminum alloy formed by laser 3D printing | |
| CN113201664A (en) | In-situ synthesized titanium-based composite material and additive manufacturing and forming method and component thereof | |
| CN111500905A (en) | High-silicon aluminum alloy modified based on selective laser melting nano ceramic | |
| CN114351029A (en) | SLM CoCrNi alloy based on grain boundary segregation enhancement and preparation method thereof | |
| CN113881873B (en) | High-density trans-scale solid solution ceramic reinforced aluminum matrix composite and preparation method thereof | |
| CN112974842B (en) | Nano multiphase reinforced aluminum matrix composite material and preparation method thereof | |
| CN113210627A (en) | Preparation method of carbide-reinforced TiAl-based nanocomposite | |
| CN111961926A (en) | 3D printed nanoparticle reinforced aluminum-based composite powder and preparation method thereof | |
| CN111842914A (en) | 3D printing process method of high-strength aluminum-copper alloy | |
| CN113755739B (en) | Method for improving mechanical property of additive manufactured austenitic steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20210423 |