CN117265338A - High-performance Al-V-Cr-Fe alloy for additive manufacturing - Google Patents
High-performance Al-V-Cr-Fe alloy for additive manufacturing Download PDFInfo
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- CN117265338A CN117265338A CN202311209312.9A CN202311209312A CN117265338A CN 117265338 A CN117265338 A CN 117265338A CN 202311209312 A CN202311209312 A CN 202311209312A CN 117265338 A CN117265338 A CN 117265338A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 54
- 239000000956 alloy Substances 0.000 title claims abstract description 54
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 20
- 229910019589 Cr—Fe Inorganic materials 0.000 title claims abstract description 16
- 239000000654 additive Substances 0.000 title claims abstract description 13
- 230000000996 additive effect Effects 0.000 title claims abstract description 13
- 238000000034 method Methods 0.000 claims abstract description 18
- 238000002844 melting Methods 0.000 claims abstract description 15
- 230000008018 melting Effects 0.000 claims abstract description 15
- 230000008569 process Effects 0.000 claims abstract description 10
- 238000005516 engineering process Methods 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000007639 printing Methods 0.000 claims abstract description 4
- 239000000843 powder Substances 0.000 claims description 14
- 239000012300 argon atmosphere Substances 0.000 claims description 5
- 238000009689 gas atomisation Methods 0.000 claims description 4
- 239000002245 particle Substances 0.000 claims description 3
- 239000000758 substrate Substances 0.000 claims description 3
- 238000002360 preparation method Methods 0.000 claims description 2
- 238000012387 aerosolization Methods 0.000 claims 1
- 238000010438 heat treatment Methods 0.000 abstract description 7
- 229910000838 Al alloy Inorganic materials 0.000 description 13
- 238000002474 experimental method Methods 0.000 description 12
- 238000011056 performance test Methods 0.000 description 12
- 238000009864 tensile test Methods 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 10
- 238000013461 design Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000012216 screening Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- 229910000967 As alloy Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Classifications
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- 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
-
- 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
- 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
- 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
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses a high-performance Al-V-Cr-Fe alloy for additive manufacturing, which comprises, by mass, 4-8% of V and 4-8% of Cr:2-6%, fe:2-8%, and the balance of Al and non-removable impurity elements, wherein the alloy is prepared by adopting a laser selective melting technology. The alloy has high strength and good plasticity in a printing state, the tensile strength is 407-662MPa, the elongation is 1.1-12.9%, the heat treatment is not needed, and the process cost required by the subsequent heat treatment can be saved.
Description
Technical Field
The invention belongs to the technical field of additive manufacturing, and relates to a high-performance Al-V-Cr-Fe alloy for additive manufacturing.
Background
The aluminum alloy has the advantages of low cost, high specific strength, low density, corrosion resistance, repeated use and the like, is a preferred material for realizing light weight, and is widely applied to industries such as aerospace, automobile manufacturing, electronic devices and the like. In recent years, the production requirements of the high-precision tip fields such as aerospace and the like on aluminum alloy components with complex structures are higher and higher, and the requirements of the traditional manufacturing process are difficult to meet. In this case, metal additive manufacturing techniques are widely studied and used, which can produce complex optimized geometries that cannot be manufactured by conventional manufacturing techniques. Selective laser melting technology is one of the most popular metal additive manufacturing technologies at present. Because of the characteristic of high manufacturing precision, the method is very suitable for producing components with complex shapes, and provides a new way for the integration and the light weight of complex aluminum alloy parts.
For the laser selective melting technology of aluminum alloys, the most widely used is near-eutectic Al-Si alloy at present, and the narrow solidification range gives low hot tearing sensitivity and better forming capability. However, the alloy has low strength and poor ductility, cannot meet performance requirements, and needs to develop a high-strength aluminum alloy suitable for selective laser melting technology. At present, most of high-strength aluminum alloys suitable for laser selective melting are mostly ageing-reinforced aluminum alloys, the strength of the printed state of the high-strength aluminum alloys is low, and the high strength is mainly derived from a precipitated phase separated out in the subsequent heat treatment process, so that the process is complicated. In order to simplify the process and reduce the process cost, it is necessary to develop a high strength aluminum alloy that does not require heat treatment.
Disclosure of Invention
In order to solve the problems, the invention provides an Al-V-Cr-Fe alloy for additive manufacturing, which takes transition group elements V, cr and Fe as alloy elements. The alloy has high strength in the printed state without subsequent heat treatment, and the high strength is derived from a large volume fraction second phase generated in the solidification process.
The Al-V-Cr-Fe alloy for additive manufacturing comprises, by mass, 4-8% of V and 4-8% of Cr:2-6%, fe:2-8%, and the balance of Al and non-removable impurity elements.
The preparation method of the Al-V-Cr-Fe alloy comprises the following steps:
preparing master alloy cast ingots according to the alloy ratio, preparing powder by gas atomization, and preparing alloy blocks by the obtained alloy powder by adopting a laser selective melting technology.
Preferably, the master alloy cast ingot is prepared by arc melting according to the alloy proportion.
Preferably, the powder is prepared by gas atomization in an argon atmosphere, and the particle size of the powder is 15-60 mu m.
Preferably, the laser selective melting forming is carried out under argon atmosphere, and the printing process parameters are as follows: the preheating temperature of the substrate is 80 ℃, the laser power is 200-400W, the scanning speed is 1000-3000 mm/s, the scanning interval is 100 mu m, the layer thickness is 10-60 mu m, and the adjacent layers are scanned and rotated by 67 degrees.
Compared with the prior art, the invention has the advantages that: the alloy has high strength and good plasticity in the printing state, the tensile strength is 407-662MPa, and the elongation is 1.1-12.9%. The ultrahigh processing degree of freedom combined with the selective laser melting technology can theoretically form and manufacture parts with any complex shape at one time without heat treatment.
Drawings
FIG. 1 is a diagram showing the morphology of the spherical powder of Al-V-Cr-Fe alloy in example 1 of the present invention.
FIG. 2 is a microstructure of a bulk sample prepared in example 1 of the present invention.
Detailed Description
The present invention will be described in detail with reference to the following examples, which are not intended to limit the scope of the invention.
The Al-V-Cr-Fe alloy for additive manufacturing comprises, by mass, 4-8% of V and 4-8% of Cr:2-6%, fe:2-8%, and the balance of Al and non-removable impurity elements.
The design basis of the components is as follows:
conventionally, V, cr and Fe are all considered as transition group elements, and have low solubility in aluminum alloy, and can react with Al in a metallurgical way in the solidification process to precipitate in the form of a second phase, which is often very coarse and greatly worsens alloy plasticity. And under the condition of high cooling speed of the selective laser, the second phase does not have time to grow up, is of nano scale, and is favorable for improving the toughness of the alloy. The design of the components of the aluminum alloy for selective laser melting has no definite mechanism, and the alloy design mainly depends on experimental screening. The invention determines the selected alloy elements and the corresponding composition ranges on the basis of a large number of experiments, and the experimental results show that the optimal mechanical properties can be obtained only by selecting three alloy elements of V, cr and Fe under the given composition ranges.
Example 1
The Al-V-Cr-Fe alloy powder applied to laser selective melting forming is prepared by adopting an air atomization method, and the prepared alloy raw material powder comprises the following main components in percentage by mass: v3.79 wt%, cr:1.98wt%, fe:3.95wt% of Al and some unavoidable impurities.
The powder prepared by the gas atomization method was screened out alloy powder with a prescribed particle size in the range of 15-60 μm according to a standard screening mesh, as shown in FIG. 1 by a scanning electron microscope.
Based on the aluminum alloy powder composed of the components, the high-performance Al-V-Cr-Fe aluminum alloy block body is prepared by a laser selective melting technology, and the molding parameters are respectively as follows: the laser power is 250W, the scanning speed is 1600mm/s, the scanning interval is 100 mu m, the layer thickness is 30 mu m, the preheating temperature of the substrate is 80 ℃, and the scanning rotation between adjacent layers is 67 degrees. The entire sample manufacturing process was performed under an argon atmosphere with an oxygen content of 200ppm.
A microstructure of a metallographic specimen observation specimen was prepared, and a matrix structure containing a large amount of spherical second phases was shown in fig. 2. The sample has no obvious defects of air holes, unfused holes, cracks and the like, and has good compactness.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of the example 1 has a tensile strength of 462MPa, a yield strength of 329MPa and an elongation of 10.1%.
Example 2
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v5.88 wt%, cr:1.99wt%, fe:3.92wt.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of example 2 has a tensile strength of 620MPa, a yield strength of 492MPa and an elongation of 4.7%.
Example 3
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v7.82 wt%, cr:1.97wt%, fe:3.98wt. .
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of example 3 has a tensile strength of 662Pa, a yield strength of 581MPa, and an elongation of 2.2%.
Example 4
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.88 wt%, cr:3.98wt%, fe:3.99wt%.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of example 4 has a tensile strength of 557MPa, a yield strength of 382MPa and an elongation of 6.9%.
Example 5
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.78 wt%, cr:6.04wt%, fe:3.89wt%.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of example 5 has a tensile strength of 592Pa, a yield strength of 411MPa, and an elongation of 4.5%.
Example 6
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.99 wt%, cr:1.97wt%, fe:2.05wt%.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, the sample of example 6 has a tensile strength of 407MPa, a yield strength of 301MPa and an elongation of 12.9%.
Example 7
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.85 wt%, cr:1.87wt%, fe:6.04wt%.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of example 7 has a tensile strength of 602MPa, a yield strength of 408MPa and an elongation of 4.8%.
Example 8
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.86 wt%, cr:1.82wt%, fe:8.22wt%.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the sample of example 8 has tensile strength up to 655MPa, yield strength 562MPa and elongation 1.1%.
Comparative example 1
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v10.22 wt%, cr:1.98wt%, fe:3.95wt.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the tensile strength of the sample in comparative example 1 reaches 488MPa, and the tensile piece is brittle and free from yielding phenomenon and elongation.
Comparative example 2
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.78 wt%, cr:8.02wt%, fe:3.98wt. .
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, the tensile strength of the sample of comparative example 2 reaches 522MPa, the yield strength is 501MPa, and the elongation is 0.7%.
Comparative example 3
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.95 wt%, cr:1.97wt%, fe:10.80wt%.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the tensile strength of the sample in comparative example 3 reaches 518MPa, and the tensile piece is brittle and free from yielding phenomenon and elongation.
Comparative example 4
The experimental procedure is substantially the same as in example 1, except that the components are changed as follows in mass percent: v3.91 wt%, cr:1.97wt% and 3.90wt% of Ni.
Tensile specimens were processed according to GB/T228.1-2010 standard and room temperature tensile tests were performed. The alloy performance test results are as follows, and the tensile strength of the sample in comparative example 4 reaches 452MPa, and the tensile member is brittle and free from yielding phenomenon and elongation.
From the above examples, it can be seen that the alloy has high strength and good plasticity in the printed state, and does not need heat treatment, thereby contributing to the reduction of the process cost.
The ingredients and test results of each example and comparative example are given in tables 1 and 2, respectively.
Table 1 the composition table (wt.%) of each example and comparative example
Note that: the balance being Al.
Table 2 actual measured values of various properties
Claims (7)
1. An Al-V-Cr-Fe alloy for additive manufacturing, which is characterized by comprising, by mass, 4-8% of V, cr:2-6%, fe:2-8%, and the balance of Al and non-removable impurity elements.
2. An Al-V-Cr-Fe alloy for additive manufacturing according to claim 1, wherein the alloy is prepared using a laser selective melting technique.
3. The Al-V-Cr-Fe alloy for additive manufacturing according to claim 1, wherein the tensile strength of the alloy is 407-662MPa and the elongation is 1.1-12.9%.
4. A preparation method of an Al-V-Cr-Fe alloy is characterized in that the alloy comprises, by mass, 4-8% of V and 4-8% of Cr:2-6%, fe:2-8%, and the balance of Al and non-removable impurity elements, including the following steps:
preparing a master alloy ingot according to the alloy ratio, and preparing powder by gas atomization, wherein the obtained alloy powder is prepared into an Al-V-Cr-Fe alloy block by adopting a laser selective melting technology.
5. The method of claim 4, wherein the master alloy ingot is prepared by arc melting in the alloy ratio.
6. The method of claim 4, wherein the powder is prepared by aerosolization under an argon atmosphere, the powder having a particle size of 15-60 μm.
7. The method of claim 4, wherein the laser selective melt forming is performed under an argon atmosphere, and the printing process parameters are as follows: the preheating temperature of the substrate is 80 ℃, the laser power is 200-400W, the scanning speed is 1000-3000 mm/s, the scanning interval is 100 mu m, the layer thickness is 10-60 mu m, and the adjacent layers are scanned and rotated by 67 degrees.
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| Application Number | Priority Date | Filing Date | Title |
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| CN202311209312.9A CN117265338A (en) | 2023-09-19 | 2023-09-19 | High-performance Al-V-Cr-Fe alloy for additive manufacturing |
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| CN202311209312.9A CN117265338A (en) | 2023-09-19 | 2023-09-19 | High-performance Al-V-Cr-Fe alloy for additive manufacturing |
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