CN117512415A - Low-scandium low-cost high-strength aluminum alloy material for additive manufacturing and preparation method thereof - Google Patents
Low-scandium low-cost high-strength aluminum alloy material for additive manufacturing and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 88
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 47
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 43
- 239000000654 additive Substances 0.000 title claims abstract description 38
- 230000000996 additive effect Effects 0.000 title claims abstract description 38
- 229910052706 scandium Inorganic materials 0.000 title claims abstract description 35
- 238000002360 preparation method Methods 0.000 title claims abstract description 23
- 238000000034 method Methods 0.000 claims abstract description 24
- 239000002245 particle Substances 0.000 claims abstract description 18
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 11
- 230000032683 aging Effects 0.000 claims description 23
- 238000010146 3D printing Methods 0.000 claims description 15
- 239000000843 powder Substances 0.000 claims description 13
- 238000003723 Smelting Methods 0.000 claims description 11
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 claims description 8
- 229910052691 Erbium Inorganic materials 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 239000002994 raw material Substances 0.000 claims description 5
- 238000000889 atomisation Methods 0.000 claims description 4
- 238000010298 pulverizing process Methods 0.000 claims description 4
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 239000000758 substrate Substances 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
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- 229910045601 alloy Inorganic materials 0.000 abstract description 38
- 238000005728 strengthening Methods 0.000 abstract description 8
- 229910018134 Al-Mg Inorganic materials 0.000 abstract description 3
- 229910018467 Al—Mg Inorganic materials 0.000 abstract description 3
- 239000011159 matrix material Substances 0.000 abstract description 3
- 238000007670 refining Methods 0.000 abstract 1
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- 229910000542 Sc alloy Inorganic materials 0.000 description 1
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Classifications
-
- 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- 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
- 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
- B22F9/08—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
- 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
-
- 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
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
-
- 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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to a low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, and a preparation method and application thereof. The invention takes the Al-Mg alloy as the matrix, breaks through the traditional additive manufacturing of the high-strength aluminum alloy and adopts 5nm coarse-grain L12 ordered phase particles Al 3 The concept of (Sc, zr) phase strengthening is to provide a method for greatly refining L12 ordered particles Al by adopting Er-Si clusters 3 (Zr, er) particle size such that the L12 ordered phase Al 3 The particle size of the (Zr, er) particles is thinned to below 2 nm. The invention skillfully utilizes Si-Er clusters and Cu-M-V clusters, thereby not only reducingThe cost of the alloy also greatly improves the comprehensive mechanical property of the alloy, has good formability, and can be widely popularized in the additive manufacturing in the aerospace and civil fields.
Description
Technical Field
The invention belongs to the technical field of additive manufacturing, and particularly relates to a low-scandium low-cost high-strength aluminum alloy material for additive manufacturing and a preparation method thereof.
Background
The additive manufacturing (commonly called 3D printing) Al-Mg-Sc-Zr alloy has wide application in the aerospace field due to excellent corrosion resistance, high plasticity and good cracking resistance. With the rapid development of aerospace industry, higher and higher requirements are put on materials and structures of parts, and the whole structure tends to be complicated. Compared with the traditional casting method, the 3D printing technology has the following advantages: first, being applicable to complicated part formation, aero-engine shows a large amount of complicated part manufacturing of shape owing to the performance requirement, adopts 3D printing can accomplish the product manufacturing under lower cost. Secondly, can reduce the assembly and subtract heavy, through topological structure design, can print combined part, hollow part, reach the lightweight requirement of part. Third, the method is suitable for diversified products, and the 3D printing does not need to modify the die. Fourth, the extremely large cooling rate of 3D printing is easy to form supersaturated solid solution, so that more elements are dissolved in the matrix, and a foundation is provided for the later aging strengthening of the alloy.
Selective Laser Melting (SLM) additive manufacturing formed high-performance Al-Mg-Sc-Zr alloy is subjected to solid solution strengthening, fine crystal strengthening and Al precipitation under the influence of a unique rapid solidification mechanism of 3D printing 3 The precipitation strengthening of (Sc, zr) particles and other strengthening mechanisms act together, so that the alloy performance is obviously improved. However, the following problems still exist in the current Al-Mg-Sc-Zr alloy for SLM additive manufacturing:
(1) The strength of the Al-Mg alloy manufactured by the traditional additive is usually improved to more than 500MPa by adding more than 0.6% of Sc element, so that the Al-Mg-Sc-Zr alloy used by the traditional additive manufacturing has high price and high alloy cost;
(2) Al is adopted in the traditional additive manufacturing of Al-Mg-Sc-Zr alloy 3 The (Zr, er) particles are reinforced, the granularity is more than 5nm, the reinforcing effect is still limited, and the particles have a further refinement space;
(3) The traditional additive manufacturing Al-Mg-Sc-Zr alloy reinforced nano particles have fixed size and do not have dynamic strain aging characteristics, so that the stress cannot be absorbed, and the printed part has low work hardening and low fatigue performance.
Disclosure of Invention
This section is intended to outline some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. Some simplifications or omissions may be made in this section as well as in the description summary and in the title of the application, to avoid obscuring the purpose of this section, the description summary and the title of the invention, which should not be used to limit the scope of the invention.
The present invention has been made in view of the above and/or problems occurring in the prior art.
It is therefore an object of the present invention to overcome the deficiencies of the prior art and to provide a low scandium, low cost, high strength aluminum alloy material that can be used in additive manufacturing.
In order to solve the technical problems, the invention provides the following technical proposal, which comprises the following components in percentage by mass,
3.0 to 10.0 percent of Mg,0.05 to 0.25 percent of Sc,0.5 to 1.2 percent of Zr,0.2 to 0.6 percent of Mn,0.02 to 0.5 percent of Cu,0.05 to 0.9 percent of Si,0.1 to 0.8 percent of Er, and the balance of Al and unavoidable impurities.
It is still another object of the present invention to overcome the deficiencies of the prior art and to provide a method for preparing a low scandium high-strength aluminum alloy material for additive manufacturing.
In order to solve the technical problems, the invention provides the following technical proposal, which comprises that,
weighing raw materials according to a formula, uniformly mixing, and vacuum smelting to obtain a prealloy;
atomizing and pulverizing the prealloy by using argon as medium;
the prepared powder is screened, vacuum-dried, 3D printed, and then subjected to post aging treatment to obtain the aluminum alloy material with low scandium, low cost and high strength.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the vacuum smelting is carried out, wherein the smelting temperature is 660-1000 ℃, and the smelting air pressure is 0.55-0.7 MPa.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the atomization pressure of the atomized powder preparation is 5-7.5 MPa.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the particle size of the powder prepared by the atomization powder preparation is 30-240 mu m.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the laser power of the 3D printing is 200-500W.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the 3D printing is performed, wherein the preheating temperature of the substrate is 100-200 ℃, the scanning speed is 500-1400 mm/s, the layer thickness is 0.02-0.08 mm, and the scanning interval is 0.05-0.2 mm.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the temperature of the post aging treatment is 280-425 ℃.
As a preferable scheme of the preparation method of the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, the invention comprises the following steps: the treatment time of the post aging treatment is 0.5-15h.
It is a further object of the present invention to overcome the deficiencies of the prior art and to provide the use of low scandium, low cost, high strength aluminum alloy materials for additive manufacturing in the manufacture of part structures in the aerospace industry.
The invention has the beneficial effects that:
(1) The invention breaks through the design thought of the high Sc content components of the traditional additive manufacturing Al-Mg-Sc-Zr alloy, greatly reduces Sc element, and adds Er-Si and Cu-Mn-V elements to cooperate to form various clusters. Wherein the Sc element and the Er element are used as refiners of alloy reinforcing phases; the Si and Mn elements are used for promoting the Sc and Er elements to exist in a form of cluster atoms and short-range order, so that the generation of cracks of the printed part is effectively inhibited, the defects are reduced, and the mechanical property is improved.
(2) Compared with the traditional additive manufacturing Al-Mg-Sc-Zr alloy, the usage amount of Sc is reduced by more than 67%, and the material cost is reduced by more than 60%: the traditional 500 MPa-level 3D printing high-strength Al-Mg alloy needs to be reinforced by Sc element with the content of more than 0.6wt%, otherwise, the reinforcing effect of 500MPa is not achieved, and the reinforcing effect with the yield strength exceeding 500MPa can be achieved by only using Sc with the content of less than 0.2wt%.
(3) The reinforced nano particles in the alloy are thinned from more than 5nm to less than 2nm in the prior art, so that the yield strength, tensile strength, plasticity and fatigue performance of the material are greatly improved. In addition, the invention adds trace Cu, forms cluster Cu-Mn-V with vacancy (V) and Mn, forms strong dynamic strain aging behavior, greatly improves the work hardening capacity of the alloy, reduces the yield ratio of the alloy, improves the fatigue performance of the alloy and is beneficial to comprehensive mechanical properties.
(4) The Al-Mg-Zr-Er-Mn-Cu-Sc alloy powder which can be used for additive manufacturing is prepared through the scheme, is combined with printing parameter optimization, and the product part obtained after aging treatment has fine and uniform grain structure, no cracks and excellent mechanical properties, wherein the tensile strength can reach 460-550 MPa, the yield strength is 345-536 MPa, the elongation at break is 8.5-14.3%, and the high requirements of aviation parts on light weight, high strength and the like of materials can be met.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings required for the description of the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art. Wherein:
FIG. 1 is a metallographic structure diagram of an alloy prepared in example 1 of the present invention.
FIG. 2 is a high angle annular dark field image-scanning transmission electron image of the alloy prepared in example 1 of the present invention.
FIG. 3 is an SEM photograph of the alloy of example 1 of the present invention.
FIG. 4 is a metallographic structure of the alloy according to example 2 of the present invention.
FIG. 5 is a metallographic structure of an alloy according to example 3 of the present invention.
Detailed Description
In order that the above-recited objects, features and advantages of the present invention will become more apparent, a more particular description of the invention will be rendered by reference to specific embodiments thereof which are illustrated in the appended drawings.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, but the present invention may be practiced in other ways other than those described herein, and persons skilled in the art will readily appreciate that the present invention is not limited to the specific embodiments disclosed below.
Further, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic can be included in at least one implementation of the invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
The material prepared by the embodiment of the invention is subjected to mechanical property test according to the following method:
density: GB/T1423-1996, drainage method.
Tensile strength, yield strength, elongation at break: GB/T228.1-2010, first part of metallic tensile test: room temperature test method.
Hardness: GB/T4340.1-2009, section 1 of Vickers hardness test of metallic materials: test methods.
Example 1:
the embodiment provides a preparation method of a low-scandium low-cost high-strength aluminum alloy material for additive manufacturing, which specifically comprises the following steps:
(1) The following components are weighed in sequence according to mass fraction: mg:7%, sc:0.20%, zr:0.8%, mn:0.5%, cu:0.02%, si:0.7%, er:0.65%, the balance being Al;
(2) Vacuum smelting, namely placing raw materials into a vacuum induction furnace, and heating and smelting the raw materials into prealloy, wherein the smelting temperature is 850 ℃;
(3) Atomizing and pulverizing, namely transferring the prealloy into an atomizing tank, setting the atomizing pressure to be 7.5MPa, and pulverizing by using argon;
(4) Airflow screening, namely, screening the powder by the airflow to obtain metal powder with the particle size range of 15-53 mu m;
(5) And (5) carrying out heat preservation and drying, putting the sieved powder into a drying oven, and carrying out heat preservation for 4 hours at 100 ℃.
(6) 3D printing, wherein 3D printing is carried out on the powder according to the following parameters: the preheating temperature of the substrate is 100 ℃, the laser power is 400W, the scanning speed is 1100mm/s, the layer thickness is 0.03mm, the scanning interval is 0.08mm, and the interlayer rotation angle is 90 degrees.
(7) Heat treatment: the aging temperature is 375 ℃, the heat preservation time is 4 hours, and the aluminum alloy material is obtained after air cooling.
Fig. 1 is a microstructure of the alloy prepared in this example, and it can be clearly observed that the alloy structure has no cracks, fewer holes, no obvious large-size holes, and high density.
Fig. 2 shows a high-angle annular dark field image-scanning transmission electron image of the alloy prepared in the embodiment, and can show that elements such as Er-Si, cu-Mn-V and the like added into the alloy are cooperated to form various clusters, si and Mn promote Sc and Er elements to exist in a form of cluster atoms and short-range order, so that the generation of cracks of a printed part is effectively inhibited, defects are reduced, and the mechanical property of the alloy is improved.
FIG. 3 is an SEM image of the alloy produced in this example, showing the mass of reinforcing particles within the material and the contour of the molten pool.
Example 2
The present example was different from example 1 in that the laser power was adjusted to 200W, and the remaining production processes were the same as example 1, to produce an aluminum alloy material.
Fig. 4 is a microstructure of the alloy prepared in this example, and cracks, more holes and lower density of the alloy structure can be clearly observed.
Example 3
The present example was different from example 1 in that the laser power was adjusted to 500W, and the remaining production processes were the same as example 1, to produce an aluminum alloy material.
The mechanical properties of the materials obtained in the above examples were tested, and the results of comparison with example 1 are shown in Table 1.
TABLE 1
| Density of the product | Tensile strength of | Yield strength of | Elongation at break | Hardness of | |
| Example 1 | 99.91％ | 550MPa | 536MPa | 10.4％ | 158Hv |
| Example 2 | 88.26％ | 480MPa | 380MPa | 9.1％ | 101Hv |
| Example 3 | 90.4％ | 460MPa | 345MPa | 8.5％ | 121Hv |
As can be seen from Table 1, adjusting the laser power of 3D printing has an effect on the properties of the alloy material, and too high and too low can reduce the mechanical properties of the alloy material, because the adjustment of the laser power can change the temperature of the molten pool and the solidification rate of the molten pool, thereby affecting the properties such as grain size, phase composition, tissue uniformity, hardness and the like. Excessive laser power causes overheating and too fast solidification, possibly generating excessive thermal stress, air holes and non-uniform tissue structure, and according to the results of table 1, the best technical effect can be obtained when the laser power for 3D printing in the invention is 400W.
Example 4
This example is different from example 1 in that the aging temperature after heat treatment was adjusted to 325 ℃, and the rest of the preparation process was the same as example 1, to prepare an aluminum alloy material.
Example 5
This example is different from example 1 in that the aging temperature after heat treatment was adjusted to 400℃and the remaining production processes were the same as example 1 to produce an aluminum alloy material.
Example 6
This example is different from example 1 in that the aging temperature after heat treatment was adjusted to 425 ℃, and the rest of the preparation process was the same as example 1, to prepare an aluminum alloy material.
The mechanical properties of the materials obtained in the above examples were tested, and the results of comparison with those of example 1 are shown in Table 2.
TABLE 2
| Density of the product | Tensile strength of | Yield strength of | Elongation at break | Hardness of | |
| Example 1 | 99.91％ | 550MPa | 536MPa | 10.4％ | 158Hv |
| Example 4 | 96.92％ | 494MPa | 469MPa | 12.1％ | 130Hv |
| Example 5 | 98.92％ | 496MPa | 471MPa | 12.5％ | 132Hv |
| Example 6 | 97.02％ | 482MPa | 461MPa | 12.6％ | 128Hv |
As can be seen from table 2, adjusting the aging temperature of the heat treatment has an effect on the properties of the alloy material, and too high or too low aging temperature can reduce the mechanical properties of the prepared alloy material, because phase transformation and tissue recrystallization occur inside the alloy during the heat treatment, and the stress in the alloy can be released through the aging treatment, so that the stress relaxation of the alloy assembly during the use process is reduced. Too high or too low an ageing temperature, although increasing the elongation at break of the alloy material, gives better ductility, correspondingly also results in an insufficient hardness of the alloy material. In summary, the preferred aging temperature is 375 ℃.
Example 7
The present example was different from example 4 in that the Mg content was adjusted to 4%, and the rest of the preparation process was the same as example 4, to prepare an aluminum alloy material.
Example 8
The present example was different from example 4 in that the Mg content was adjusted to 9%, and the rest of the production process was the same as example 4, to obtain an aluminum alloy material.
Example 9
The difference between this example and example 4 is that the Er content was adjusted to 0.75%, and the remaining preparation processes were the same as in example 4, to obtain an aluminum alloy material.
Example 10
The difference between this example and example 4 is that the Er content was adjusted to 0.25%, and the remaining preparation processes were the same as in example 4, to prepare an aluminum alloy material.
The mechanical properties of the materials obtained in the above examples were tested, and the results of comparison with those of example 1 are shown in Table 3.
TABLE 3 Table 3
| Density of the product | Tensile strength of | Yield strength of | Elongation at break | Hardness of | |
| Example 1 | 99.91％ | 550MPa | 536MPa | 10.4％ | 158Hv |
| Example 7 | 90.92％ | 481MPa | 465MPa | 9.5％ | 138Hv |
| Example 8 | 90.85％ | 520MPa | 422MPa | 9.8％ | 146Hv |
| Example 9 | 98.92％ | 538MPa | 529MPa | 9.1％ | 152Hv |
| Example 10 | 95.62％ | 478MPa | 466MPa | 14.3％ | 138Hv |
As can be seen from Table 3, adjusting the content of the elements in the raw materials has an effect on the performance of the alloy material, because the Mg and Er elements are cooperated with other elements to generate various cluster atoms, the cluster atoms exist in a short-range ordered form, the crack generation of the printed part is effectively inhibited, the mechanical property is improved, and according to the results of Table 3, the best technical effect can be obtained when the content of Mg is 7% and the content of Er is 0.65%.
Comparative example 1
The comparative example provides a method for preparing a conventional Al-Mg-Sc-Zr alloy, which is different from the example 1 in that the formula is adjusted as Mg:4%, sc:0.6%, zr:0.25%, mn:0.3%, si:0.15%, mo:0.02% of Al and the balance of the preparation process are the same as in example 1.
Comparative example 2
The present example was different from example 1 in that the Er content was adjusted to 0.05%, and the remaining preparation processes were the same as example 1, to prepare an aluminum alloy material.
Comparative example 3
The present example was different from example 1 in that the laser power was adjusted to 100W, and the remaining production processes were the same as example 1, to produce an aluminum alloy material.
Comparative example 4
The present example was different from example 1 in that the Si content was adjusted to 3%, and the remaining production process was the same as example 1, to obtain an aluminum alloy material.
The mechanical properties of the materials obtained in the above comparative examples were measured, and the results of comparison with example 1 are shown in Table 3.
TABLE 4 Table 4
| Density of the product | Tensile strength of | Yield strength of | Elongation at break | Hardness of | |
| Example 1 | 99.91％ | 550MPa | 536MPa | 10.4％ | 158Hv |
| Comparative example 1 | 78.81％ | 210MPa | 180MPa | 2.1％ | 100Hv |
| Comparative example 2 | 79.93％ | 350MPa | 281MPa | 2.4％ | 88Hv |
| Comparative example 3 | 80.51％ | 398MPa | 320MPa | 5.1％ | 103Hv |
| Comparative example 4 | 83.68％ | 458MPa | 353MPa | 6.1％ | 105Hv |
Compared with the traditional Al-Mg-Sc-Zr alloy, the alloy material prepared by the invention has both ductility and strength and excellent mechanical property. And when the element content is out of the scope of the present invention, it has a significant effect on the properties of the alloy. This is because various elements in my invention produce a composite effect to form various clusters which effectively improve the mechanical properties of the alloy material, and the Sc content of my invention is far less than that of the conventional alloy, but a strengthening effect with yield strength exceeding 500MPa is obtained.
In summary, the invention prepares the low scandium, low cost and high strength aluminum alloy material which can be used for additive manufacturing, and the invention proposes to adopt Er-Si elementThe composite effect causes Er-Si elements to form clusters which are used as a refiner to refine L12 ordered particles Al greatly 3 (Zr, er) particle size such that the L12 ordered phase Al 3 The grain size of the (Zr, er) particles is thinned to below 2nm, compared with L12 ordered Al above 5nm obtained by adopting high Sc element in the prior art 3 The (Sc, zr) particles have more strengthening advantage and cost advantage when the ultra-fine particles below 2nm are used.
The alloy prepared by the invention is in a supersaturated solid solution state, and after aging treatment, er, si, zr, sc element and Al can also generate Al- (Si, er and Zr) clusters, and can further refine matrix grains, effectively pin grain boundaries, have aging hardening characteristics and further improve alloy performance after aging treatment.
The Mn and Si elements in the alloy are used for inhibiting the precipitation of Zr, sc and Er element-containing particles, and the Zr, sc and Er element-containing particles exist in the form of cluster atoms and short-range order. The Er-Si, si-Zr and Si-Sc clusters can delay the generation of fatigue cracks and improve the static and dynamic mechanical properties of the alloy.
The trace Cu element is added to form a cluster Cu-Mn-V with the vacancy and Mn, so that strong dynamic strain aging behavior is formed, the work hardening capacity of the alloy is greatly improved, the yield ratio of the alloy is reduced, the fatigue performance of the alloy is improved, and the comprehensive mechanical property is facilitated.
It should be noted that the above embodiments are only for illustrating the technical solution of the present invention and not for limiting the same, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that the technical solution of the present invention may be modified or substituted without departing from the spirit and scope of the technical solution of the present invention, which is intended to be covered in the scope of the claims of the present invention.
Claims (10)
1. The utility model provides a low scandium low-cost high strength aluminum alloy material that can be used to additive manufacturing which characterized in that: the aluminum alloy comprises the following components in percentage by mass,
3.0 to 10.0 percent of Mg,0.05 to 0.25 percent of Sc,0.5 to 1.2 percent of Zr,0.2 to 0.6 percent of Mn,0.02 to 0.5 percent of Cu,0.05 to 0.9 percent of Si,0.1 to 0.8 percent of Er, and the balance of Al and unavoidable impurities.
2. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 1, wherein the method comprises the following steps: comprising the steps of (a) a step of,
weighing raw materials according to a formula, uniformly mixing, and vacuum smelting to obtain a prealloy;
atomizing and pulverizing the prealloy by using argon as medium;
the prepared powder is screened, vacuum-dried, 3D printed, and then subjected to post aging treatment to obtain the aluminum alloy material with low scandium, low cost and high strength.
3. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the vacuum smelting is carried out, wherein the smelting temperature is 660-1000 ℃, and the smelting air pressure is 0.55-0.7 MPa.
4. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the atomization pressure of the atomized powder preparation is 5-7.5 MPa.
5. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the particle size of the powder prepared by the atomization powder preparation is 30-240 mu m.
6. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the laser power of the 3D printing is 200-500W.
7. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the 3D printing is performed, wherein the preheating temperature of the substrate is 100-200 ℃, the scanning speed is 500-1400 mm/s, the layer thickness is 0.02-0.08 mm, and the scanning interval is 0.05-0.2 mm.
8. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the temperature of the post aging treatment is 280-425 ℃.
9. The method for preparing the low-scandium low-cost high-strength aluminum alloy material for additive manufacturing according to claim 2, wherein the method comprises the following steps of: the treatment time of the post aging treatment is 0.5-15h.
10. Use of the low scandium low-cost high strength aluminium alloy material produced by the production method according to any one of claims 2 to 9 for producing part structures in the aerospace industry.
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