CN116422880B - High-strength aluminum alloy for 3D printing - Google Patents

High-strength aluminum alloy for 3D printing Download PDF

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CN116422880B
CN116422880B CN202310501635.9A CN202310501635A CN116422880B CN 116422880 B CN116422880 B CN 116422880B CN 202310501635 A CN202310501635 A CN 202310501635A CN 116422880 B CN116422880 B CN 116422880B
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aluminum alloy
powder
printing
strength aluminum
tib
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CN116422880A (en
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茹中赟
张亦杰
叶璋
赵守明
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Dongliang Aluminium Co ltd
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    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/12—Metallic powder containing non-metallic particles
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • B22F1/148—Agglomerating
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
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    • 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
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    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
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    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • 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
    • B33Y10/00—Processes of additive manufacturing
    • 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
    • B33Y70/00—Materials specially adapted for additive manufacturing
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
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    • C23C24/00—Coating starting from inorganic powder
    • C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
    • C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
    • C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
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Abstract

The invention belongs to the technical field of materials for 3D printing, and particularly relates to a high-strength aluminum alloy for 3D printing. The invention provides a high-strength aluminum alloy for 3D printing, which is mixed powder, and comprises aluminum alloy powder and TiB 2 The raw materials of the mixed powder and the aluminum alloy powder comprise Al, cu, mg, sc and TiN doped powder. The high-strength aluminum alloy has the advantages that: 1. the aluminum alloy part printed according to the prior SLM technology has higher fatigue strength, and is not easy to be damaged after multiple alternating load actions; 2. the tensile strength of the aluminum alloy part is obviously more than 550MPa, and the tensile performance is outstanding; 3. the mechanical properties of the aluminum alloy part can meet the use requirements of high-end fields such as an air inlet casing of an aerospace engine.

Description

High-strength aluminum alloy for 3D printing
Technical Field
The invention belongs to the technical field of materials for 3D printing, and particularly relates to a high-strength aluminum alloy for 3D printing.
Background
3D printing technology, also known as additive manufacturing, has the general principle that: the digital model file is used as an instruction, a digital technical material printer is used as equipment, and bondable powder such as metal or plastic is used as a material, so that a part product is quickly constructed and obtained in a layer-by-layer printing mode.
Among them, the laser selective melting technology, namely SLM technology, is one of the most common 3D printing technology implementation modes, and its working mode is: the precisely focused laser light spot is adopted to quickly melt the preset layer-by-layer metal powder, so that the part product with any shape can be directly obtained. SLM technology is widely used in the fields of aerospace, transportation, mechanical construction, etc.
On the other hand, the metal materials of the bondable powder include steel, titanium alloy, aluminum alloy, and the like. Wherein, aluminum alloy powder for 3D printing technique, compare with other several powder materials, the advantage is: high thermal conductivity and good molding performance, but the defects include: the comprehensive mechanical properties are not outstanding, the strength of the part products is not enough, and the like, and the special performance is that: 1. low fatigue strength; 2. the tensile strength is low.
Therefore, some aluminum alloy powders for 3D printing technology newly appeared in the market generally take an improved aluminum alloy formula as a main material and change a heat treatment process as an auxiliary material, so as to improve comprehensive mechanical properties of the final aluminum alloy 3D printed part product.
For example, chinese patent publication No. CN113684403A and publication No. 2021.11.23 disclose a high-strength aluminum alloy powder for 3D printing and a preparation method thereof, wherein the alloy comprises the following components in percentage by mass: mg:3.0 to 8.0 percent of Er:0.1 to 1.2 percent, zr:0.5 to 2.0 percent of Mn:0.3 to 1.0 percent of Si:0.01 to 2.0 percent, the total content of other metal elements except Al is not more than 0.5 weight percent, and the rest is Al.
The aluminum alloy powder in the patent of the invention has the advantages that: the printing process is not easy to generate cracks, has obvious fine grain and precipitation strengthening effects, and has yield strength exceeding 400MPa, tensile strength exceeding 500MPa and elongation exceeding 10 percent after heat treatment.
However, the final 3D printing product of the aluminum alloy powder has relatively low fatigue strength, and the tensile strength is difficult to stably exceed 550MPa, so that the product cannot have good long-term use stability in high-end fields such as an air inlet casing of an aerospace engine.
Therefore, in view of the foregoing, there is an urgent need for a new aluminum alloy powder raw material that has significant improvements in two parameters, namely, fatigue strength and tensile strength, of 3D printed products.
Disclosure of Invention
The invention provides a high-strength aluminum alloy for 3D printing, which is mixed powder, and comprises aluminum alloy powder and TiB 2 The raw materials of the mixed powder and the aluminum alloy powder comprise Al, cu, mg, sc and TiN doped powder. The high-strength aluminum alloy has the advantages that: 1. the aluminum alloy part printed according to the prior SLM technology has higher fatigue strength, and is not easy to be damaged after multiple alternating load actions; 2. the tensile strength of the aluminum alloy part is obviously more than 550MPa, and the tensile performance is outstanding; 3. the mechanical properties of the aluminum alloy part can meet the use requirements of high-end fields such as an air inlet casing of an aerospace engine.
The invention adopts the technical proposal that: the high-strength aluminum alloy for 3D printing is mixed powder, and the mixed powder comprises aluminum alloy powder and TiB 2 The raw material composition of the aluminum alloy powder comprises Al, cu, mg, sc and TiN doped powder.
In the invention, the material essence of the high-strength aluminum alloy is an aluminum alloy-ceramic composite material, and compared with the existing common aluminum alloy material, the aluminum alloy material has the advantages that: 1. the hardness is higher; 2. the yield strength is further improved; 3. the tensile strength is obviously improved.
However, if only the aluminum alloy powder+mixed powder is used, the fatigue strength of the composite material after laser melting and reshaping is generally lower than that of the existing single aluminum alloy powder material for 3D printing, and the following two reasons are possible:
1. the additionally added ceramic material mixed powder can not be melted when the 3D printing part is processed, and can destroy the directional consistency of the internal crystal phase structure of the aluminum alloy powder, so that the 3D printing part prepared from the aluminum alloy-ceramic composite material is processed by (3-5) multiplied by 10 7 After the alternating load, a large number of cracks appear, which is far from sufficient in the field of aerospace engine air inlet casing;
2. in the laser melting step in the SLM technology, it is difficult to heat the aluminum alloy powder and the ceramic mixed powder which are completely separated in the early stage and are simply and mechanically mixed simultaneously, so that the 3D printed part made of the aluminum alloy-ceramic composite material easily generates extremely fine pores inside, which also reduces the fatigue strength of the 3D printed part.
Therefore, more skillfully, the high-strength aluminum alloy also comprises an doping component, namely TiN doping powder, which is mixed with the aluminum alloy powder before 3D printing and atomized together for powder preparation. Wherein, the action of the TiN doped powder and TiB 2 The mixed powder is similar, so that the ceramic composite improvement is carried out on the existing aluminum alloy powder, and the hardness of the final high-strength aluminum alloy is improved.
Furthermore, it is more critical that:
1. TiN doped powder is "in", tiB 2 The mixed powder is outside;
2. both the titanium and the titanium belong to nonmetallic compounds of Ti element, N, B atoms have covalent bond relation to Ti atoms on both sides of the inner side and the outer side after powder laser melting, so that a more integral and uniform ceramic material reinforced skeleton is formed, and finally the titanium and titanium alloy is finally displayed on a 3D printing part of the high-strength aluminum alloy, namely the fatigue strength is obviously improved, the tensile strength is stabilized in a relatively high numerical range, and the tensile strength is at least more than or equal to 550MPa.
The further preferable technical scheme is as follows: the TiB is 2 The addition amount of the mixed powder is 0.6-1.8% of the weight of the mixed powder.
In the prior art, in order to ensure the strengthening effect of the aluminum alloy-ceramic composite material, the adding amount of the ceramic material mixed powder can only be properly increased, for example, the adding amount is kept at the level of 3.0-4.5% by weight, but the contradiction at the moment is that the fatigue strength of a part obtained by 3D printing of the composite material is relatively poor.
Therefore, the existing independent adding mode of the ceramic mixed powder at least greatly limits the application range of the final 3D printing part. Therefore, in the invention, the original ceramic mixed powder is properly distributed to the TiN doped powder. Finally, a more practical and efficient balance is achieved among the hardness, the tensile strength and the fatigue strength of the part product.
The further preferable technical scheme is as follows: the addition amount of Sc is 0.10-0.15% of the weight of the aluminum alloy powder.
In the invention, due to the TiN doped powder and TiB 2 The Sc component originally mainly used for strengthening the mechanical property can be greatly reduced by the combination and the specific addition of the mixed powder. The Sc element is very expensive, so that the high-strength aluminum alloy has a new advantage of relatively low cost.
The further preferable technical scheme is that the raw materials of the aluminum alloy powder comprise the following components in parts by weight, cu:4.0-4.5%, mg:1.6-2.5%, sc:0.10-0.15%, tiN doped powder: 0.5-1.0%, and the balance Al.
The further preferable technical scheme is as follows: the grain diameter of the aluminum alloy powder is 25-60 mu m; the TiB is 2 The particle size of the mixed powder is 30-45 mu m; the particle size of the TiN doped powder is 15-20 mu m.
The further preferable technical proposal is that the preparation method of the high-strength aluminum alloy sequentially comprises the following steps,
s1, melting: adding Al, cu, mg and Sc into a smelting furnace together with TiN doped powder in a pure metal or intermediate alloy mode to carry out smelting operation to obtain a melt;
s2, gas atomization: the melt is still in a smelting furnace and is subjected to vacuum induction gas atomization operation to obtain coarse aluminum alloy powder;
s3, post-processing: sequentially drying and screening the aluminum alloy coarse material powder to obtain the aluminum alloy powder;
s4, mixing and spheroidizing: the TiB is added into the aluminum alloy powder first 2 And mixing the powder, and performing spheroidization operation to obtain the final high-strength aluminum alloy.
The further preferable technical scheme is as follows: in S1, the heating temperature of the smelting furnace is 850-900 ℃, and the melting operation time is 30-50min/100g of TiN doped powder.
In the invention, the heating condition of 850-900 ℃ is only mainly used for melting Al, so that the molten aluminum can be fully wrapped with TiN doped powder.
In addition, the heating time of the melting step is in a proportional relation with the weight of the TiN doped powder, so that the heat required for melting Al can be ensured to be enough, and the problem of insufficient melting of Al caused by a large amount of heat absorption of the TiN doped powder can be avoided. Finally, the aluminum liquid can be fully combined with all other raw material elements of the aluminum alloy powder.
The further preferable technical scheme is as follows: s2, the vacuum degree of the smelting furnace is 10 -3 Pa, and the pressure of the gas atomization operation is 3-6MPa.
The further preferable technical scheme is as follows: and S3, the temperature of the drying operation is 110-150 ℃.
The further preferable technical scheme is as follows: s4, performing spheroidization operation by adopting a radio frequency plasma high-energy spheroidization system until the aluminum alloy powder and TiB 2 The sphericity of the mixed powder is more than or equal to 98 percent.
Detailed Description
The following description is of the preferred embodiments of the invention and is not intended to limit the scope of the invention.
Example 1
The high-strength aluminum alloy for 3D printing is mixed powder, and the mixed powder comprises aluminum alloy powder and TiB 2 The raw material composition of the aluminum alloy powder comprises Al, cu, mg, sc and TiN doped powder.
Wherein the TiB is 2 The addition amount of the mixed powder is 0.6% of the weight of the mixed powder, and the raw material composition of the aluminum alloy powder comprises the following components in parts by weight: 4.0%, mg:1.8%, sc:0.10% of TiN doped powder: 0.5%, and the balance Al.
In addition, the grain diameter of the aluminum alloy powder is 26-32 mu m; the TiB is 2 The particle size of the mixed powder is 32-38 mu m; the particle size of the TiN doped powder is 15-18 mu m.
The preparation method of the high-strength aluminum alloy sequentially comprises the following steps of,
s1, melting: adding Al, cu, mg and Sc into a smelting furnace together with TiN doped powder in a pure metal or intermediate alloy mode to carry out smelting operation to obtain a melt;
s2, gas atomization: the melt is still in a smelting furnace and is subjected to vacuum induction gas atomization operation to obtain coarse aluminum alloy powder;
s3, post-processing: sequentially drying and screening the aluminum alloy coarse material powder to obtain the aluminum alloy powder;
s4, mixing and spheroidizing: the TiB is added into the aluminum alloy powder first 2 And mixing the powder, and performing spheroidization operation to obtain the final high-strength aluminum alloy.
In S1, the heating temperature of the smelting furnace is 850 ℃, and the melting operation time is 30min/100g of TiN doped powder.
S2, the vacuum degree of the smelting furnace is 10 -3 Pa, the pressure of the aerosolization operation was 3.5MPa.
In S3, the temperature of the drying operation is 110 ℃.
S4, performing spheroidization operation by adopting a radio frequency plasma high-energy spheroidization system until the aluminum alloy powder and TiB 2 The sphericity of the mixed powder is more than or equal to 98 percent.
The application method of the high-strength aluminum alloy in the field of 3D printing sequentially comprises the following steps,
t1: pouring the powdery high-strength aluminum alloy into a powder supply chamber of 3D printing equipment, and flushing inert gas until the oxygen content in the powder supply chamber is reduced to below 0.1%;
t2: inputting a part model in a system of the 3D printing apparatus;
t3: scanning the substrate by using laser, and spreading the high-strength aluminum alloy on the surface of the substrate;
t4: and 3D printing is carried out according to the part model data, and the final high-strength aluminum alloy 3D printed part is prepared.
The SLM technique in T4 has the parameters: the laser power is 300-500W, the scanning speed is 800-1800mm/s, the scanning interval is 0.10-0.15 mm, and the layer thickness is 0.03-0.05 mm.
Example 2
High-strength aluminum alloy for 3D printing, wherein the high-strength aluminum alloy is mixed powder, and the mixed powder is packagedAluminum alloy powder and TiB 2 The raw material composition of the aluminum alloy powder comprises Al, cu, mg, sc and TiN doped powder.
Wherein the TiB is 2 The addition amount of the mixed powder is 0.8% of the weight of the mixed powder, and the raw material composition of the aluminum alloy powder comprises the following components in parts by weight: 4.2%, mg:1.8%, sc:0.11%, tiN doped powder: 0.9%, and the balance Al.
In addition, the grain diameter of the aluminum alloy powder is 30-55 mu m; the TiB is 2 The particle size of the mixed powder is 33-41 mu m; the particle size of the TiN doped powder is 16-18 mu m.
The preparation method of the high-strength aluminum alloy sequentially comprises the following steps of,
s1, melting: adding Al, cu, mg and Sc into a smelting furnace together with TiN doped powder in a pure metal or intermediate alloy mode to carry out smelting operation to obtain a melt;
s2, gas atomization: the melt is still in a smelting furnace and is subjected to vacuum induction gas atomization operation to obtain coarse aluminum alloy powder;
s3, post-processing: sequentially drying and screening the aluminum alloy coarse material powder to obtain the aluminum alloy powder;
s4, mixing and spheroidizing: the TiB is added into the aluminum alloy powder first 2 And mixing the powder, and performing spheroidization operation to obtain the final high-strength aluminum alloy.
In S1, the heating temperature of the smelting furnace is 880 ℃, and the melting operation time is 40min/100g of TiN doped powder.
S2, the vacuum degree of the smelting furnace is 10 -3 Pa, the pressure of the aerosolization operation was 4.0MPa.
In S3, the temperature of the drying operation is 140 ℃.
S4, performing spheroidization operation by adopting a radio frequency plasma high-energy spheroidization system until the aluminum alloy powder and TiB 2 The sphericity of the mixed powder is more than or equal to 98 percent.
The application method of the high-strength aluminum alloy in the field of 3D printing sequentially comprises the following steps,
t1: pouring the powdery high-strength aluminum alloy into a powder supply chamber of 3D printing equipment, and flushing inert gas until the oxygen content in the powder supply chamber is reduced to below 0.1%;
t2: inputting a part model in a system of the 3D printing apparatus;
t3: scanning the substrate by using laser, and spreading the high-strength aluminum alloy on the surface of the substrate;
t4: and 3D printing is carried out according to the part model data, and the final high-strength aluminum alloy 3D printed part is prepared.
The SLM technique in T4 has the parameters: the laser power is 300-500W, the scanning speed is 800-1800mm/s, the scanning interval is 0.10-0.15 mm, and the layer thickness is 0.03-0.05 mm.
Example 3
The high-strength aluminum alloy for 3D printing is mixed powder, and the mixed powder comprises aluminum alloy powder and TiB 2 The raw material composition of the aluminum alloy powder comprises Al, cu, mg, sc and TiN doped powder.
Wherein the TiB is 2 The addition amount of the mixed powder is 1.2% of the weight of the mixed powder, and the raw material composition of the aluminum alloy powder comprises the following components in parts by weight: 4.2%, mg:2.0%, sc:0.13% of TiN doped powder: 0.9%, and the balance Al.
In addition, the grain diameter of the aluminum alloy powder is 26-50 mu m; the TiB is 2 The particle size of the mixed powder is 37-45 mu m; the particle size of the TiN doped powder is 16-20 mu m.
The preparation method of the high-strength aluminum alloy sequentially comprises the following steps of,
s1, melting: adding Al, cu, mg and Sc into a smelting furnace together with TiN doped powder in a pure metal or intermediate alloy mode to carry out smelting operation to obtain a melt;
s2, gas atomization: the melt is still in a smelting furnace and is subjected to vacuum induction gas atomization operation to obtain coarse aluminum alloy powder;
s3, post-processing: sequentially drying and screening the aluminum alloy coarse material powder to obtain the aluminum alloy powder;
s4, mixing and spheroidizing: the TiB is added into the aluminum alloy powder first 2 And mixing the powder, and performing spheroidization operation to obtain the final high-strength aluminum alloy.
In S1, the heating temperature of the smelting furnace is 900 ℃, and the melting operation time is 40min/100g of TiN doped powder.
S2, the vacuum degree of the smelting furnace is 10 -3 Pa, the pressure of the aerosolization operation was 5.0MPa.
In S3, the temperature of the drying operation is 125 ℃.
S4, performing spheroidization operation by adopting a radio frequency plasma high-energy spheroidization system until the aluminum alloy powder and TiB 2 The sphericity of the mixed powder is more than or equal to 98 percent.
The application method of the high-strength aluminum alloy in the field of 3D printing sequentially comprises the following steps,
t1: pouring the powdery high-strength aluminum alloy into a powder supply chamber of 3D printing equipment, and flushing inert gas until the oxygen content in the powder supply chamber is reduced to below 0.1%;
t2: inputting a part model in a system of the 3D printing apparatus;
t3: scanning the substrate by using laser, and spreading the high-strength aluminum alloy on the surface of the substrate;
t4: and 3D printing is carried out according to the part model data, and the final high-strength aluminum alloy 3D printed part is prepared.
The SLM technique in T4 has the parameters: the laser power is 300-500W, the scanning speed is 800-1800mm/s, the scanning interval is 0.10-0.15 mm, and the layer thickness is 0.03-0.05 mm.
Comparative example 1
The high strength aluminum alloy of this comparative example, and the method of preparing and using the same, differs from example 1 only in the following 1 point:
the aluminum alloy powder in the high-strength aluminum alloy is free of TiN doped powder.
Comparative example 2
The high strength aluminum alloy of this comparative example, and the method of preparing and using the same, differs from example 1 only in the following 1 point:
in the high-strength aluminum alloy, no TiB2 mixed powder exists, namely the aluminum alloy powder is independently used.
Comparative example 3
The high strength aluminum alloy of this comparative example, and the method of preparing and using the same, differs from example 1 only in the following 1 point:
TiB is mixed with the aluminum alloy powder in the high-strength aluminum alloy 2 The mixed powder and the TiN doped powder are added into the raw materials of the aluminum alloy powder.
Comparative example 4
The high strength aluminum alloy of this comparative example, and the method of preparing and using the same, differs from example 1 only in the following 1 point:
the aluminum alloy powder in the high-strength aluminum alloy has no TiN doped powder, but is mixed with TiB 2 The mixed powder is directly mixed with the aluminum alloy powder.
Comparative example 5
The high strength aluminum alloy of this comparative example, and the method of preparing and using the same, differs from example 1 only in the following 1 point:
in the high-strength aluminum alloy, no TiB exists 2 The mixed powder is also free of TiN doped powder in the aluminum alloy powder.
Performance testing
The high strength aluminum alloys of the 3 examples and 5 comparative examples were printed according to the conventional SLM technique to obtain 10 tensile bars each. A total of 8 groups of 80 tensile bars are subjected to mechanical property test according to the GB/T228.1-2010 standard, and the test items comprise: yield strength, elongation, tensile strength, fatigue strength, and density, the final data were averaged for each group and the results are given in table 1 below.
TABLE 1
From table 1 above, the following conclusions can be drawn.
1. In the high strength aluminum alloy, tiB 2 As a direct mix, tiN as an admixture in aluminum alloy powders, both of these points are indispensable, otherwise the overall mechanical properties of the 3D printed parts corresponding to the high strength aluminum alloy are significantly reduced, such as comparative examples 1 and 2.
2. Comparative example 5 is the most common aluminum alloy powder for 3D printing in the prior art, and compared with the aluminum alloy, the aluminum alloy with high strength in the invention has the following items that the performance is improved most obviously: fatigue strength and tensile strength, which are extremely important for the environment in which the aerospace engine intake case is used.
3. In the high strength aluminum alloy, tiB 2 As direct mixed powder and TiN as an admixture in the aluminum alloy powder, the two materials are used alternatively, and only the mechanical property of the final part is not obviously improved, and the two materials are also comparative examples 1 and 2.
4. In the high strength aluminum alloy, tiB, which is originally directly mixed 2 TiN, which was also used as a charge, was also directly mixed, both of which were comparative examples 3 and 4 described above, which were reduced in the overall mechanical properties as compared with example 5, and thus had no beneficial effect at all, and were even detrimental.
The embodiments of the present invention have been described in detail, but the present invention is not limited to the above embodiments, and various modifications may be made without departing from the spirit of the present invention within the knowledge of those skilled in the art. These are all non-inventive modifications which are intended to be protected by the patent laws within the scope of the appended claims.

Claims (9)

1. The utility model provides a high strength aluminum alloy that 3D printed usefulness which characterized in that: the high-strength aluminum alloy is mixed powder, and the mixed powder comprises aluminum alloy powder and TiB 2 The raw materials of the mixed powder comprise Al, cu, mg, sc and TiN doped powder,
the preparation method of the high-strength aluminum alloy sequentially comprises the following steps of,
s1, melting: adding Al, cu, mg and Sc into a smelting furnace together with TiN doped powder in a pure metal or intermediate alloy mode to carry out smelting operation to obtain a melt;
s2, gas atomization: the melt is still in a smelting furnace and is subjected to vacuum induction gas atomization operation to obtain coarse aluminum alloy powder;
s3, post-processing: sequentially drying and screening the aluminum alloy coarse material powder to obtain the aluminum alloy powder;
s4, mixing and spheroidizing: the TiB is added into the aluminum alloy powder first 2 And mixing the powder, and performing spheroidization operation to obtain the final high-strength aluminum alloy.
2. The high strength aluminum alloy for 3D printing of claim 1, wherein: the TiB is 2 The addition amount of the mixed powder is 0.6-1.8% of the weight of the mixed powder.
3. The high strength aluminum alloy for 3D printing of claim 1, wherein: the addition amount of Sc is 0.10-0.15% of the weight of the aluminum alloy powder.
4. A high strength aluminum alloy for 3D printing according to claim 3, wherein the raw material composition of the aluminum alloy powder comprises the following components by weight, cu:4.0-4.5%, mg:1.6-2.5%, sc:0.10-0.15%, tiN doped powder: 0.5-1.0%, and the balance Al.
5. The high strength aluminum alloy for 3D printing of claim 1, wherein: the grain diameter of the aluminum alloy powder is 25-60 mu m; the TiB is 2 The particle size of the mixed powder is 30-45 mu m; the particle size of the TiN doped powder is 15-20 mu m.
6. The high strength aluminum alloy for 3D printing of claim 1, wherein: in S1, the heating temperature of the smelting furnace is 850-900 ℃, and the melting operation time is 30-50min/100g of TiN doped powder.
7. The high strength aluminum alloy for 3D printing of claim 1, wherein: s2, the vacuum degree of the smelting furnace is 10 -3 Pa, and the pressure of the gas atomization operation is 3-6MPa.
8. The high strength aluminum alloy for 3D printing of claim 1, wherein: and S3, the temperature of the drying operation is 110-150 ℃.
9. The high strength aluminum alloy for 3D printing of claim 1, wherein: s4, performing spheroidization operation by adopting a radio frequency plasma high-energy spheroidization system until the aluminum alloy powder and TiB 2 The sphericity of the mixed powder is more than or equal to 98 percent.
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CN114182129A (en) * 2021-12-16 2022-03-15 国网福建省电力有限公司 High-strength aluminum-based composite material and preparation method thereof
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