CN116219241A - Titanium diboride particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing - Google Patents

Titanium diboride particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing Download PDF

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CN116219241A
CN116219241A CN202310087790.0A CN202310087790A CN116219241A CN 116219241 A CN116219241 A CN 116219241A CN 202310087790 A CN202310087790 A CN 202310087790A CN 116219241 A CN116219241 A CN 116219241A
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aluminum alloy
alloy powder
electron beam
particle reinforced
tib
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陈哲
黎阳
马思鸣
胡磊
吴一
汪明亮
王浩伟
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Shanghai Jiaotong University
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Abstract

The invention provides titanium diboride particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing. The chemical composition of the aluminum alloy powder comprises 1.8 to 2.7 percent of Cu, 0.8 to 1.4 percent of Ni, 0 to 1.8 percent of Mg, and the weight percentage is as follows,Fe:0.1～1.4％，TiB 2 0.1 to 10 percent of particles and the balance of aluminum. The preparation method mainly comprises the following steps: smelting the particle reinforced aluminum alloy prefabricated ingot and performing gas atomization forming on particle reinforced aluminum alloy powder. The block made of the titanium diboride particle reinforced heat-resistant aluminum alloy powder is free of cracks, uniform in microstructure and fine in grains. The tensile strength obtained after heat treatment is 320MPa, the elongation is more than 10 percent, and the average level of the mechanical properties of the electron beam additive manufactured aluminum alloy is better than that of the electron beam additive manufactured aluminum alloy.

Description

Titanium diboride particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing
Technical Field
The invention belongs to the technical field of metal materials, and particularly relates to titanium diboride particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing, in particular to particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing and a preparation method thereof.
Background
The additive manufacturing of the aluminum alloy combines the advantages of light weight of the material and rapid forming of the parts with complex shapes, and has great application prospect in the key fields of national defense and military industry, aerospace, transportation and the like. At present, the main technology adopted by the additive manufacturing of aluminum alloy is laser additive manufacturing and forming. However, most aluminum alloys, other than a few alloys such as al—si based alloys, are prone to hot cracking and voids during laser additive manufacturing and forming, and have poor printability. In recent years, electron beam additive manufacturing techniques have begun to be applied to aluminum alloys. And the electron beam is used as an energy source, and the preset powder is scanned and heated at a high speed under the vacuum protection, so that the additive manufacturing and shaping are realized. Compared with a laser energy source, the electron beam is used, so that the energy absorption rate is high; oxidation and holes are reduced, and the forming density is high; the method has the advantages of low residual stress, reduced printing cracking and the like, can solve the difficult problem of poor printability of most aluminum alloys, and is currently applied to additive manufacturing of aluminum alloys such as AlSi10Mg, 2024 and the like. Nevertheless, the processing temperature in the electron beam additive manufacturing process is high (300-500 ℃), so that the aluminum alloy is in a high-temperature heat exposure state for a long time in the forming process, the grain structure of the forming material is coarse, the grain size is tens to hundreds of micrometers, the mechanical property of the forming material is seriously influenced, the tensile strength is usually lower than 300MPa, and a small gap exists between the forming material and the forming member manufactured by laser additive manufacturing; and in electron beam additive manufacturing forming materials, significant micro-texture and intensity non-uniformity occurs due to the difference in thermal exposure time along the height direction of the print. It is difficult to meet the service requirements. The above problems are due to poor heat resistance of the eutectic phase (e.g., si phase, al—cu phase) of the aluminum alloy, and coarsening occurs under high temperature exposure. The coarsened eutectic phase cannot inhibit the growth of grains, resulting in coarse grains and a decrease in the strength of the material. Severely limiting the application of electron beam additive manufactured aluminum alloys in industrial production. Therefore, development of the heat-resistant aluminum alloy powder for electron beam additive manufacturing is significant in obtaining high-strength electron beam additive manufacturing aluminum alloy.
Disclosure of Invention
In order to solve the problems, the invention aims to provide titanium diboride particle reinforced heat resistant aluminum alloy powder for electron beam additive manufacturing.
The invention aims at realizing the following technical scheme:
the titanium diboride particle reinforced heat resistant aluminum alloy powder comprises, by mass, 1.8-2.7% of Cu, 0.8-1.4% of Ni, 0-1.8% of Mg, 0.1-1.4% of Fe and 0.1-1.4% of TiB 2 0.1 to 10 percent of particles and the balance of aluminum.
To further increase the high temperature reinforcing phase Al 9 The content of FeNi and reduces the thermal cracking sensitivity of the alloy, preferably, the content of Fe in the aluminum alloy powder is 0.3-0.9%, the content of Ni is 1.2-1.4% and the content of Mg is 0-0.8% by mass percent.
The preparation method of the titanium diboride particle reinforced heat-resistant aluminum alloy powder comprises the following steps:
A. selecting raw materials, calculating and weighing the consumption of each raw material according to the preset alloy components, and casting each raw material to obtain a prefabricated ingot;
B. the titanium diboride particle reinforced aluminum alloy powder is prepared by gas atomization of an alloy ingot or an alloy rod.
The step A specifically comprises the following steps:
a1, al-TiB 2 Melting the Al-Cu intermediate alloy, the Al-Ni intermediate alloy and the Al-Fe intermediate alloy at 600-1000 ℃, and then heating to 850+/-5 ℃ and preserving heat for 15-30 min;
a2, cooling the melt to 680+/-5 ℃, adding Mg into the melt, and standing for 3-4 min to completely melt the Mg;
a3, heating the melt to 760+/-5 ℃, adding a refining agent, refining for 5-10 min, and removing surface scum; and (3) adding a covering agent into the mixture for vacuum degassing for 10 to 15 minutes after refining, removing surface scum again, and casting and air-cooling the mixture to obtain a prefabricated ingot when the temperature of the melt is regulated to 740+/-5 ℃.
The refining agent in the step A3 is selected from JZJ type harmless aluminum alloy refining agents. Other refining agents commonly used in the energy arts may also be used.
The covering agent in the step A3 is selected from JZF-03 type covering agents. Other capping agents commonly used in the energy arts may also be used.
The step B specifically comprises the following steps:
b1, placing the prefabricated ingot into a smelting cavity of an aerosolization device, and replacing air in the smelting cavity with nitrogen;
b2, heating to 800-1000 ℃ to enable the prefabricated ingot to be completely melted, and keeping the temperature at the melting temperature for 5-120 min;
and B3, flowing out the melted precast ingot melt from a nozzle of the gas atomization equipment, crushing into tiny liquid drops under the impact of high-speed nitrogen, solidifying into powder, collecting and vacuum packaging to obtain a titanium diboride particle reinforced aluminum alloy powder finished product.
As still another embodiment of the present invention, the powder preparation method comprises the steps of:
(1) Pure Al, al-TiB 2 The high-purity master batch, al-Cu intermediate alloy blocks, al-Ni intermediate alloy blocks and Al-Fe intermediate alloy blocks are added into a crucible, and are placed into a resistance furnace for heating, and are completely melted at the melting temperature of 600-1000 ℃. Then the temperature is kept at 850+/-5 ℃ for 15min. After heat preservation, removing surface scum.
(2) Cooling the melt to 680+/-5 ℃, rapidly pressing pure Mg blocks into the melt by using a graphite rod, and standing for 3min to completely melt the Mg blocks.
(3) Heating the melt to 760+/-5 ℃, adding a refining agent for refining for 5min, and then removing surface scum. And (3) spreading a covering agent after refining is finished, carrying out vacuum degassing for 10min, then removing surface scum again, measuring the temperature of a melt at 740+/-5 ℃, casting and air-cooling to obtain a prefabricated ingot.
(4) Placing the prefabricated ingot obtained in the step (3) into a crucible in a smelting cavity of an air atomizing device, and replacing air in the smelting cavity with nitrogen;
(5) Heating by electromagnetic induction, so that the prefabricated ingot is completely melted and kept at the melting temperature for 5-120 min, and the ingot is completely melted, wherein the melting temperature is 800-1000 ℃;
(6) And enabling the molten precast ingot melt to flow out of a nozzle, breaking into tiny liquid drops under the impact of high-speed nitrogen, solidifying into powder, collecting and vacuum packaging to obtain a titanium diboride particle reinforced aluminum alloy powder finished product.
The invention also provides an electron beam additive preparation method, which comprises the following steps:
and adding materials to the titanium diboride particle reinforced aluminum alloy powder through an electron beam selective melting process to obtain a block.
The voltage used for electron beam material-increasing manufacturing is 60kV, the scanning beam current is 4.5-5.5 mA, the scanning speed is 0.8-1.6 m/s, the scanning mode is layer-by-layer scanning rotated by 90 degrees, and TiB is prepared 2 Block of Al-Cu-Mg-Fe-Ni.
Compared with the prior art, the invention has the following beneficial effects:
(1) Based on Al-Cu-Mg heat-treatable reinforced aluminum alloy, fe and Ni alloy elements are added simultaneously to form Al in the aluminum alloy 9 The FeNi high-temperature heat stable phase effectively inhibits the coarsening of the eutectic phase caused by high-temperature processing in electron beam additive manufacturing, thereby improving the heat resistance of the aluminum alloy matrix. The strength of the printing forming material can be further improved through heat treatment strengthening in the later period;
(2) Autogenously introduced TiB by in situ smelting 2 The particles have small size, uniform distribution, tight combination with an aluminum matrix and obvious particle strengthening effect. And TiB is 2 The particles are used as heterogeneous nucleating agents to refine grains, so that on one hand, the hot crack sensitivity of the aluminum alloy in the rapid solidification of additive manufacturing is reduced, the additive manufacturing formability of the aluminum alloy is improved, and the anisotropism of tissues and performances is eliminated. On the other hand, the fine grain strengthening effect is achieved. TiB located at grain boundary 2 Particles and Al 9 The FeNi and other heat stable eutectic phases are commonly pinned with grain boundaries to inhibit the growth of grains under the high-temperature processing condition of electron beam additive manufacturing.
(3) TiB of the invention 2 The preparation method of the/Al-Cu-Mg-Fe-Ni powder is simple, the process is mature, the added Fe and Ni are common alloy elements, the cost is low, and the large-scale industrial production can be realized.
(4) TiB of the invention 2 The Al-Cu-Mg-Fe-Ni powder can be subjected to electron beam additive manufacturing within a wider component range and an electron beam selective melt processing parameter window, and has good printing forming performance.
Drawings
Other features, objects and advantages of the present invention will become more apparent upon reading of the detailed description of non-limiting embodiments, given with reference to the accompanying drawings in which:
FIG. 1 TiB in example 1 2 Typical particle morphology and typical microstructure of the/Al-Cu-Mg-Fe-Ni powder;
FIG. 2 TiB in example 1 2 Typical microstructure of the printed state of the Al-Cu-Mg-Fe-Ni alloy;
FIG. 3 TiB in example 1 2 Typical grain structure of the Al-Cu-Mg-Fe-Ni alloy in the as-printed state;
FIG. 4 TiB in example 1 2 Al-Cu-Mg-Fe-Ni alloy as-printed and TiB in example 2 2 Typical tensile curve of the Al-Cu-Mg-Fe-Ni alloy after heat treatment;
FIG. 5 TiB in example 3 2 Al-Cu-Mg-Fe-Ni alloy as-printed and TiB in example 4 2 Typical tensile curve of the Al-Cu-Mg-Fe-Ni alloy after heat treatment;
FIG. 6 TiB in example 5 2 Al-Cu-Mg-Fe-Ni alloy forgingTiB in the printing state and example 6 2 Typical tensile curve of the Al-Cu-Mg-Fe-Ni alloy after heat treatment;
FIG. 7Al 9 A variation trend chart of FeNi phase fraction along with Fe and Ni content;
FIG. 8 is a graph showing the trend of thermal cracking sensitivity factor with the content of Mg and Cu;
fig. 9 example 1 and comparative examples 1, 2, 3 print block sample plots.
Detailed Description
The present invention will be described in detail with reference to examples. The following examples will assist those skilled in the art in further understanding the present invention, but are not intended to limit the invention in any way. It should be noted that several modifications and improvements can be made by those skilled in the art without departing from the inventive concept. These are all within the scope of the present invention.
Example 1 preparation of titanium diboride particle-reinforced heat resistant aluminum alloy powder for electron beam additive manufacturing
1. Composition design
Proposed to increase Al 9 Alloy design strategies that reduce thermal cracking susceptibility while FeNi high temperature reinforcing phase content. Under the guidance of the strategy, the Al is obtained by adopting phase diagram thermodynamic high-flux calculation 9 The variation trend graph of FeNi phase fraction along with the content of Fe and Ni (figure 7) and the variation trend graph of the thermal cracking sensitivity factor along with the content of Mg and Cu (figure 8) are optimized, so that the content of Fe is 0.3-0.9 wt%, the content of Ni is 1.2-1.4 wt% and the content of Mg is 0-0.8 wt%.
2. Titanium diboride particle reinforced heat resistant aluminum alloy (TiB) 2 Preparation of Al-Cu-Mg-Fe-Ni) powder
Titanium diboride particle reinforced heat resistant aluminum alloy powder for electron beam additive manufacturing, wherein the chemical composition of the aluminum alloy in the powder is w (Cu) =2.60%, w (Ni) =1.12%, w (Mg) =1.60%, w (Fe) =0.63%, tiB 2 The mass fraction of (2) is 5.5wt%, and the balance is aluminum.
The preparation method of the powder comprises the following steps:
(1)TiB 2 smelting of an Al-Cu-Mg-Fe-Ni alloy prefabricated ingot:
a. adding pure Al and Al-TiB2 high-purity master batch, al-Cu intermediate alloy blocks, al-Ni intermediate alloy blocks and Al-Fe intermediate alloy blocks into a crucible, heating in a resistance furnace, and completely melting at 800 ℃. Then preserving the temperature at 850 ℃ for 15min; after heat preservation, removing surface scum.
b. Cooling the melt to 680 ℃, and rapidly pressing pure Mg blocks into the melt by using a graphite rod, and standing for 3min to completely melt the Mg blocks.
c. The melt is heated to 760 ℃, refined for 5min by adding a refining agent, and then the surface scum is removed. And (3) spreading a covering agent after refining is finished, carrying out vacuum degassing for 10min, then removing surface scum again, measuring the temperature of a melt at 740 ℃, casting and air-cooling to obtain a prefabricated ingot.
(2)TiB 2 Aerosolization forming of Al-Cu-Mg-Fe-Ni powder:
a. the TiB obtained is subjected to 2 Placing the Al-Cu-Mg-Fe-Ni prefabricated ingot into a crucible in a smelting cavity of an air atomizing device, and replacing air in the smelting cavity with nitrogen;
b. heating by electromagnetic induction, wherein the target temperature is 800 ℃; preserving heat for 30min to enable the cast ingot to be completely melted;
c. the melt flows out of the nozzle, flows along the nozzle under the action of gravity, is broken into droplets of different sizes under the impact of rapidly moving atomized nitrogen, solidifies into powder in the falling process, and the falling powder is collected at the bottom of the cavity and vacuum-packed.
TiB prepared in this example 2 The typical morphology and typical microstructure of the Al-Cu-Mg-Fe-Ni powder are shown in FIG. 1; the particle size of the powder is 53-105 mu m, and the sphericity is high. The presence of TiB in the powder 2 And (3) particles.
3. Electron beam additive manufacturing TiB 2 Block of Al-Cu-Mg-Fe-Ni
TiB prepared by adopting the step 1 2 The Al-Cu-Mg-Fe-Ni powder is subjected to additive manufacturing by an electron beam selective melting process to obtain a block material, wherein the acceleration voltage for the electron beam additive manufacturing is 60kV, the scanning beam current is 5.1mA, the scanning speed is 1.4m/s, and the scanning is carried outIn a layer-by-layer scan rotated 90 degrees.
TiB prepared 2 the/Al-Cu-Mg-Fe-Ni bulk material was free from crack generation, and the presence of a large number of voids was not observed. Its typical micro-solidification structure is shown in FIG. 2, tiB 2 The particles and eutectic phases are distributed uniformly throughout the print mass. Typical grain structure as shown in fig. 3, the average grain size is less than 10 μm, and is reduced by 4-6 times compared with the grain size of the electron beam additive manufacturing aluminum alloy in the industry. TiB in the print state 2 Use of the/Al-Cu-Mg-Fe-Ni block on a stretcher (Zwick/Roell) according to GB/T228.1-2010 Standard 10 -3 s -1 The strain rate was uniaxially stretched to a tensile strength of 256MPa, a yield strength of 135MPa and an elongation of 15.6%.
Example 2
This example is identical to the material composition described in example 1, and the powder is prepared in essentially the same way as in example 1.
The difference is that: in experimental step 2 TiB in print form 2 the/Al-Cu-Mg-Fe-Ni block is subjected to solid solution treatment at 530 ℃ for 2 hours, water quenching at 25 ℃ at room temperature, and then aging treatment at 190 ℃ for 12 hours. The tensile strength was measured to be 320MPa, the yield strength was measured to be 192MPa, and the elongation was measured to be 11.3%.
FIG. 4 is TiB in example 1 2 Al-Cu-Mg-Fe-Ni alloy as-printed and TiB in example 2 2 Typical tensile curve of the Al-Cu-Mg-Fe-Ni alloy after heat treatment;
example 3
A titanium diboride particle reinforced heat resistant aluminum alloy powder for electron beam additive manufacturing, wherein the chemical composition of aluminum alloy in the powder is w (Cu) =2.46%, w (Ni) =1.09%, w (Mg) =1.48%, w (Fe) =0.63%, tiB 2 The mass fraction of (2) was 4.6 wt.%, the balance being aluminum.
The milling process was essentially the same as in example 1.
The difference is that: and 2, the scanning beam current used for electron beam additive manufacturing in the experimental step is 4.5mA, and the scanning speed is 1m/s. The tensile strength was 188MPa, the yield strength was 85MPa, and the elongation was 10.2%.
Example 4
The material composition of this example was the same as that described in example 3, and the pulverizing method was substantially the same as that of example 1.
The difference is that: the scanning beam current used in the electron beam additive manufacturing in the experimental step 2 is 4.5mA, the scanning speed is 1m/s, and the TiB is in a printing state 2 the/Al-Cu-Mg-Fe-Ni block is subjected to solid solution treatment at 530 ℃ for 2 hours, water quenching at 25 ℃ at room temperature, and then aging treatment at 190 ℃ for 12 hours. The tensile strength was 258MPa, the yield strength was 130MPa, and the elongation was 13.0%.
FIG. 5 is TiB in example 3 2 Al-Cu-Mg-Fe-Ni alloy as-printed and TiB in example 4 2 Typical tensile curve of the Al-Cu-Mg-Fe-Ni alloy after heat treatment.
Example 5
A titanium diboride particle reinforced heat resistant aluminum alloy powder for electron beam additive manufacturing, wherein the chemical composition of aluminum alloy in the powder is w (Cu) =2.43%, w (Ni) =1.08%, w (Mg) =1.61%, w (Fe) =0.63%, tiB 2 The mass fraction of (2) was 4.9 wt.%, the balance being aluminum.
The milling process was essentially the same as in example 1.
The difference is that: the scanning beam current used in the electron beam additive manufacturing in the experimental step 2 is 4.8mA, and the scanning speed is 1.2m/s. The tensile strength was 198MPa, the yield strength was 97MPa, and the elongation was 10.0%.
Example 6
This example was identical to the material composition described in example 5, and the milling process was essentially identical to example 1.
The difference is that: the scanning beam current used in the electron beam additive manufacturing in the experimental step 2 is 4.8mA, the scanning speed is 1.2m/s, and the TiB is in a printing state 2 the/Al-Cu-Mg-Fe-Ni block is subjected to solid solution treatment at 530 ℃ for 2 hours, water quenching at 25 ℃ at room temperature, and then aging treatment at 190 ℃ for 12 hours. The tensile strength was 287MPa, the yield strength was 174MPa, and the elongation was 13.8%.
FIG. 6 is TiB in example 5 2 Al-Cu-Mg-Fe-Ni alloy as-printed and TiB in example 6 2 Typical tensile curve of the Al-Cu-Mg-Fe-Ni alloy after heat treatment;
example 7
A titanium diboride particle reinforced heat resistant aluminum alloy powder for electron beam additive manufacturing, wherein the aluminum alloy powder has the chemical composition of w (Cu) =1.86%, w (Ni) =1.25%, w (Mg) =0.78%, w (Fe) =0.88%, tiB 2 The mass fraction of (2) is 1wt%, and the balance is aluminum.
The milling process was essentially the same as in example 1. The tensile strength of the printed state is 242MPa, the yield strength is 115MPa, and the elongation is 18.2%.
Example 8
The difference from example 7 is that the chemical composition of the aluminum alloy powder is w (Cu) =2.30%, w (Ni) =1.36%, w (Mg) =0.5%, w (Fe) =0.78%, tiB 2 The mass fraction of (2) is 0.1wt% with the balance being aluminum.
The tensile strength in the printed state is 238MPa, the yield strength is 109MPa, and the elongation is 19.0%.
Example 9
The difference from example 7 is that the chemical composition of the aluminum alloy powder is w (Cu) =1.81%, w (Ni) =1.21%, w (Mg) =0.3%, w (Fe) =0.35%, tiB 2 9.5wt% of the balance aluminum.
Experimental steps 1, 2 were identical to example 1. The tensile strength in the printed state is 268MPa, the yield strength is 144MPa, and the elongation is 7.5%.
Comparative example 1
Comparative example 1 differs from example 1 in that no TiB was added to the alloy composition 2 。
The chemical composition of the aluminum alloy in the powder was w (Cu) =2.62%, w (Ni) =1.12%, w (Mg) =1.68%, w (Fe) =0.63%, but TiB was not added 2 The balance being aluminum.
Since TiB is not added 2 Grain refinement is carried out on the particles, a large number of holes and pits appear on a formed sample manufactured by electron beam additive manufacturing, and the formed sample cannot be printedA sample of the block.
Comparative example 2
This comparative example was identical to the alloy composition described in example 1, and the milling process was essentially identical to example 1.
The difference is that: in the experimental step 2, the scanning beam current used for electron beam additive manufacturing is 5.9mA, and is larger than the scanning beam current in the protection range of the application, and the surface of the printed block sample is severely bulged, so that 3D printing accurate forming cannot be realized.
Comparative example 3
The comparative example was essentially identical to the material composition described in example 1 and the milling process was essentially identical to example 1.
The difference is that: in the experimental step 2, the size of the scanning beam current used for electron beam additive manufacturing is 3.6mA, which is smaller than the scanning beam current in the protection range of the application, and obvious concave phenomenon appears on the surface of the printed block sample, so that 3D printing and accurate forming cannot be realized.
Fig. 9 example 1 and comparative examples 1, 2, 3 print block sample plots.
The foregoing describes specific embodiments of the present invention. It is to be understood that the invention is not limited to the particular embodiments described above, and that various changes and modifications may be made by one skilled in the art within the scope of the claims without affecting the spirit of the invention.

Claims (9)

1. The titanium diboride particle reinforced heat-resistant aluminum alloy powder is characterized by comprising, by mass, 1.8-2.7% of Cu, 0.8-1.4% of Ni, 0-1.8% of Mg, 0.1-1.4% of Fe and 0.1-1.4% of TiB 2 0.1 to 10 percent of particles and the balance of aluminum.
2. The aluminum alloy powder according to claim 1, wherein the content of Fe in the aluminum alloy powder is 0.3 to 0.9%, the content of Ni is 1.2 to 1.4%, and the content of Mg is 0 to 0.8% by mass percent.
3. A method for producing the aluminum alloy powder according to claim 1 or 2, characterized by comprising the steps of:
A. selecting raw materials, calculating and weighing the consumption of each raw material according to the preset alloy components, and casting each raw material to obtain a prefabricated ingot;
B. the titanium diboride particle reinforced aluminum alloy powder is prepared by gas atomization of an alloy ingot or an alloy rod.
4. The method of producing an aluminum alloy powder according to claim 3, wherein the step a specifically comprises the steps of:
a1, al-TiB 2 Melting the Al-Cu intermediate alloy, the Al-Ni intermediate alloy and the Al-Fe intermediate alloy at 600-1000 ℃, and then heating to 850+/-5 ℃ and preserving heat for 15-30 min;
a2, cooling the melt to 680+/-5 ℃, adding Mg into the melt, and standing for 3-4 min to completely melt the Mg;
a3, heating the melt to 760+/-5 ℃, adding a refining agent, refining for 5-10 min, and removing surface scum; and (3) adding a covering agent into the mixture for vacuum degassing for 10 to 15 minutes after refining, removing surface scum again, and casting and air-cooling the mixture to obtain a prefabricated ingot when the temperature of the melt is regulated to 740+/-5 ℃.
5. The method of producing an aluminum alloy powder according to claim 4, wherein the refining agent in step A3 is selected from the group consisting of JZJ-type harmless aluminum alloy refining agents.
6. The method of producing an aluminum alloy powder according to claim 4, wherein the covering agent in step A3 is selected from the group consisting of JZF-03 type covering agents.
7. The method of producing an aluminum alloy powder according to claim 3, wherein the step B specifically comprises the steps of:
b1, placing the prefabricated ingot into a smelting cavity of an aerosolization device, and replacing air in the smelting cavity with nitrogen;
b2, heating to 800-1000 ℃ to enable the prefabricated ingot to be completely melted, and keeping the temperature at the melting temperature for 5-120 min;
and B3, flowing out the melted precast ingot melt from a nozzle of the gas atomization equipment, crushing into tiny liquid drops under the impact of high-speed nitrogen, solidifying into powder, collecting and vacuum packaging to obtain a titanium diboride particle reinforced aluminum alloy powder finished product.
8. An electron beam additive manufacturing method is characterized by comprising the following steps:
the titanium diboride particle reinforced aluminum alloy powder of claim 1 or 2, or the titanium diboride particle reinforced aluminum alloy powder produced by the production method of any one of claims 3 to 7, is additively produced by an electron beam selective melting process to obtain a bulk material.
9. The method for preparing the electron beam additive according to claim 8, wherein the voltage used for manufacturing the electron beam additive is 60kV, the scanning beam current is 4.5-5.5 mA, the scanning speed is 0.8-1.6 m/s, and the scanning mode is layer-by-layer scanning rotated by 90 degrees, so as to prepare the TiB 2 Block of Al-Cu-Mg-Fe-Ni.
CN202310087790.0A 2023-01-30 2023-01-30 Titanium diboride particle reinforced heat-resistant aluminum alloy powder for electron beam additive manufacturing Pending CN116219241A (en)

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