CN105483477A - High-strength and high-toughness scandium-contained Al-Cu-Mg-Zr alloy and preparation method thereof - Google Patents
High-strength and high-toughness scandium-contained Al-Cu-Mg-Zr alloy and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
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- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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Abstract
The invention discloses a high-strength and high-toughness scandium-contained Al-Cu-Mg-Zr alloy. The high-strength and high-toughness scandium-contained Al-Cu-Mg-Zr alloy consists of the following alloy elements in percentage by mass: 3.0-5.0% of copper, 1.5-2.5% of magnesium, 0.05-0.20% of scandium, 0.1-0.4% of zirconium, and the balance of aluminum. The alloy elements are fed according to the mass ratios, are cast into an ingot after electromagnetic induction smelting, and are rolled into a rolling plate with a thickness of 2.9 mm after pretreatment and homogenization; then, the rolling plate with a thickness of 2.9 mm is subjected to the solid solution treatment, the room-temperature water quenching and the 30% cold deformation rolling to form a rolling plate with a thickness of 2.00 mm; and finally, the peak aging treatment is performed. The preparation method is simple, easy to operate, excellent in alloy strengthening and toughening effects and an economical and efficient alloy strengthening method; the obtained scandium-contained Al-Cu-Mg-Zr alloy is excellent in mechanical performance; and compared with a 2024 alloy having equivalent components in a T6 state after minus 80 DEG C low-temperature rolling in tensile property, the alloy has the advantages that the tensile strength of the alloy is increased by 7.5% and the yield strength of the alloy is increased by 11.4% while keeping higher ductility.
Description
Technical field
The present invention relates to a kind of Al-Cu-Mg-Zr Alloy And Preparation Method containing scandium high-strength and high ductility, belong to nonferrous materials technical field.
Background technology
Al-Cu-Mg alloy, owing to having lower density, higher intensity, good resistance toheat and moulded manufacturability, is widely used in the fields such as automobile, boats and ships, building and aerospace.Along with the development of hi-tech, propose more and more higher performance requriements to structured material, conventional aluminum alloy can not meet the requirement of part high-tech area in mechanical property and processing characteristics etc.But rare earth Sc microalloying improves Al alloy structure at present to improve alloy property comparatively economy, effective means, thus cause the extensive concern of scholar simultaneously.
The main Al with being formed of beneficial effect of rare earth Sc is added in aluminium alloy
3sc particle is relevant.Al
3sc particle is included in the Al that the pyroprocesses such as homogenizing, hot rolling or hot extrusion are formed
3sc disperse phase and the Al formed in ag(e)ing process
3sc precipitated phase.In the present invention containing homogenizing and hot rolling technology, therefore Al
3sc disperse phase can be separated out by abundant forming core in above-mentioned technique.But due to Al
3the aging temp (300 ~ 350 DEG C) of Sc precipitated phase is between Al-Cu-Mg alloy Homogenization Treatments temperature (480 ~ 490 DEG C) and aging temperature (175 ~ 205 DEG C), and the scandium Al-Cu-Mg alloy that contains therefore through normative heat treatment is difficult to form Al
3sc precipitated phase, the beneficial effect thus adding Sc in aluminium alloy is very limited.
Pre-treatment was carried out before timeliness for Al-Cu-Mg alloy and can make metastable GPB district and S " at network of dislocation place forming core; thus facilitate from GPB district or S " transformation of main in opposite directions ageing strengthening phase S ' phase, make in alloy, to separate out tiny, equally distributed ageing strengthening phase, and then improve the performance of alloy.
Found by the data of literatures delivered, the tensile strength of common Al-Cu-Mg alloy, lower than 500MPa, therefore it may be necessary the Al-Cu-Mg alloy that a series of thermal treatment exploitation has more high strength.
Summary of the invention
The object of the present invention is to provide a kind of Al-Cu-Mg-Zr Alloy And Preparation Method of the high-strength and high ductility containing scandium, this alloy has higher intensity and has good unit elongation simultaneously, and it uses equipment simple, and preparation method is easy.
In order to solve the problems of the technologies described above, the Al-Cu-Mg-Zr alloy of a kind of high-strength and high ductility containing scandium that the present invention proposes, is made up of following alloying element and mass percentage thereof: copper: 3.0 ~ 5.0%; Magnesium: 2.5 ~ 3.5%; Scandium: 0.05 ~ 0.20%; Zirconium: 0.1 ~ 0.4%; Surplus is aluminium; Under alloy T6 state, mechanical properties reaches 588MPa, and yield strength reaches 560MPa, and unit elongation is 9.6%, and yield tensile ratio reaches 0.96.
Prepare the preparation method of the Al-Cu-Mg-Zr alloy of the above-mentioned high-strength and high ductility containing scandium, comprise the following steps:
Step one, the aluminium ingot of 99.9wt.% is greater than with massfraction, massfraction is greater than the copper ingot of 99.9wt.%, massfraction is greater than the magnesium ingot of 99.9wt.%, Al-2wt.%Sc master alloy and Al-5wt.%Zr master alloy are melting raw material, by described aluminium ingot, copper ingot, magnesium ingot, the mass ratio of Al-2wt.%Sc intermediate alloy ingot and Al-5wt.%Zr intermediate alloy ingot is (0.8 ~ 0.9): (0.03 ~ 0.05): (0.01 ~ 0.03): (0.03 ~ 0.1): (0.02 ~ 0.08), adopt electromagnetic induction melting method molten alloy, smelting temperature controls at 680 ~ 720 DEG C, and under vacuum atmosphere, water in the mould casting from and be preheated to 200 DEG C, natural air cooling becomes ingot casting,
Step 2, ladle barrow Milling Machining step one obtained are the sheet material that 20mm is thick, are then positioned in chamber type electric resistance furnace and at 345 ~ 355 DEG C, carry out pre-treatment 8h successively, at 475 ~ 485 DEG C, carry out Homogenization Treatments 20h;
Step 3, first the sheet material after Homogenization Treatments is carried out preheating 2h at 450 DEG C of temperature, at 450 DEG C of temperature, be then rolling to that 6.0mm is thick rolls plate, at 400 DEG C, process annealing 2h, naturally cools to room temperature, finally, be cold-rolled to 2.9mm thick roll plate;
Step 4, the plate that rolls thick for 2.9mm is carried out 1h solution treatment at 500 DEG C, in room temperature water, then carry out quench treatment be cooled to room temperature, quenching shift time is 10 ~ 15s, will roll afterwards plate continue cold rolling for 2.0mm thick, rolling treatment time 15min to 60min;
Step 5, the plate that rolls that 2.0mm step 4 rolling obtained is thick carry out peak ageing treatment at temperature is 190 DEG C, obtain the Al-Cu-Mg-Zr alloy of the high-strength and high ductility containing scandium.
Compared with prior art, the invention has the advantages that: use equipment simple, preparation method is easy, easy to operate, obtained contains scandium Al-Cu-Mg-Zr alloy after pre-treatment, the comparatively uniform secondary Al of, distribution comparatively large containing number density
3(Sc, Zr) particle.Under T6 state, alloy main strengthening phase number density is comparatively large, size is more tiny, distribution is comparatively even, and under alloy T6 state, mechanical properties reaches 588MPa, and yield strength reaches 560MPa, and unit elongation is 9.6%, and yield tensile ratio is up to 0.96.Compared with the tensile property of commercial 2024 alloys of the U.S. suitable with composition after-80 DEG C of low temperature rollings under T6 state, alloy of the present invention is while maintenance is compared with high-elongation, and tensile strength improves 7.5%, and yield strength improves 11.4%.
Accompanying drawing explanation
Fig. 1 (a) be comparative example 1 obtained containing the transmission photo after the Al-Cu-Mg-Zr alloy Homogenization Treatments of scandium;
Fig. 1 (b) be obtained by the embodiment of the present invention 1 containing scandium high-strength and high ductility Al-Cu-Mg-Zr alloy Homogenization Treatments after transmission photo;
Fig. 2 (a) is the dark field image transmission photo of precipitated phase after comparative example 2 ageing treatment;
Fig. 2 (b) is the enlarged view of Fig. 2 (a) photo;
Fig. 2 (c) is the dark field image transmission photo of precipitated phase after the embodiment of the present invention 1 ageing treatment;
Fig. 2 (d) is the enlarged view of Fig. 2 (c) photo;
Fig. 3 (a) is the tensile strength properties figure of the embodiment of the present invention 1 and the Al-Cu-Mg-Zr alloy containing scandium obtained by comparative example 1-4;
Fig. 3 (b) is the yield strength performance map of the embodiment of the present invention 1 and the Al-Cu-Mg-Zr alloy containing scandium obtained by comparative example 1-4;
Fig. 3 (c) is the yield tensile ratio performance map of the embodiment of the present invention 1 and the Al-Cu-Mg-Zr alloy containing scandium obtained by comparative example 1-4.
Embodiment
Be described in further detail technical solution of the present invention below in conjunction with the drawings and specific embodiments, described specific embodiment only explains the present invention, not in order to limit the present invention.
Embodiment 1:
Prepare a kind of Al-Cu-Mg-Zr alloy of the high-strength and high ductility containing scandium, comprise the following steps:
The magnesium ingot that step one, the aluminium ingot being greater than 99.9wt.% with massfraction, massfraction are greater than the copper ingot of 99.9wt.%, massfraction is greater than 99.9wt.%, Al-2wt.5Sc and Al-5wt.Zr master alloy are melting raw material, be 85:4:2:5:4 by the mass ratio of aluminium ingot, copper ingot, magnesium ingot, Al-2wt.%Sc intermediate alloy ingot and Al-5wt.%Zr intermediate alloy ingot, adopt electromagnetic induction melting method molten alloy, smelting temperature controls at 700 DEG C, and under vacuum atmosphere, water in the mould casting from and be preheated to 200 DEG C, natural air cooling becomes ingot casting;
Step 2, ladle barrow Milling Machining step one obtained are the sheet material that 20mm is thick; Then this sheet material is positioned in chamber type electric resistance furnace and at temperature 350 DEG C, carries out pre-treatment 8h successively, at 480 DEG C, carry out Homogenization Treatments 20h;
Step 3, first the sheet material after Homogenization Treatments is carried out preheating 2h at 450 DEG C of temperature, at 450 DEG C of temperature, be then rolling to that 6.0mm is thick rolls plate, at 400 DEG C, process annealing 2h, naturally cools to room temperature, finally, be cold-rolled to 2.9mm thick roll plate;
Step 4, the plate that rolls thick for 2.9mm is carried out 1h solution treatment at 500 DEG C, in room temperature water, then carry out quench treatment be cooled to room temperature, quenching shift time is 10 ~ 15s, will roll afterwards plate continue cold rolling for 2.0mm thick, rolling treatment time 20min;
Step 5, the plate that rolls that 2.0mm rolling obtained is thick carry out peak ageing treatment at temperature is 190 DEG C, obtain the high-strength and high ductility Al-Cu-Mg-Zr alloy containing scandium.
The rolling treatment time in step 4 is generally 15-20 minute, as long as but be no more than 1 hour, the physical property of the final Al-Cu-Mg-Zr alloy containing scandium obtained is had an impact hardly.
The Al-Cu-Mg-Zr alloy containing scandium that the present embodiment 1 is obtained, as shown in Fig. 3 (a), Fig. 3 (b) He Fig. 3 (c), under its alloy T6 state, room temperature tensile intensity is 588MPa, and yield strength is 560MPa, unit elongation is 9.6%, and yield tensile ratio is 0.96.In the present invention, T6 is solid solution+ageing treatment, the omnipotent mechanics machine of the CSS-44100 utilizing Changchun Inst of Testing Machine to produce, and rate of extension is that 1mm/min carries out room-temperature mechanical property test to the sample that embodiment 1 and each comparative example obtain; Fig. 1 (b) be obtained by the embodiment of the present invention 1 containing scandium high-strength and high ductility Al-Cu-Mg-Zr alloy Homogenization Treatments after transmission photo; Fig. 2 (c) and Fig. 2 (d) is the dark field image transmission photo of precipitated phase after the embodiment of the present invention 1 ageing treatment.
Comparative example 1:
Prepare a kind of Al-Cu-Mg-Zr alloy containing scandium, the difference of the preparation method of this comparative example 1 and the preparation method of embodiment 1 is, carries out pre-treatment 8h at sheet material temperature in chamber type electric resistance furnace being not 345 ~ 355 DEG C in step 2 wherein; And do not carry out the process being continued to be cold-rolled to 2.0mm by 2.9mm of step 4.The Al-Cu-Mg-Zr alloy containing scandium that comparative example 1 is obtained, as shown in Fig. 3 (a), Fig. 3 (b) He Fig. 3 (c), under its alloy T6 state, room temperature tensile intensity is 436MPa, and yield strength is 334MPa, unit elongation is 18.6%, and yield tensile ratio is 0.76.Fig. 1 (a) be comparative example 1 obtained containing the transmission photo after the Al-Cu-Mg-Zr alloy Homogenization Treatments of scandium.
Comparative example 2:
Prepare a kind of Al-Cu-Mg-Zr alloy containing scandium, the difference of the preparation method of this comparative example 2 and the preparation method of embodiment 1 is, does not carry out the process being continued to be cold-rolled to 2.0mm by 2.9mm of step 4.The Al-Cu-Mg-Zr alloy containing scandium that comparative example 2 is obtained, as shown in Fig. 3 (a), Fig. 3 (b) He Fig. 3 (c), under its alloy T6 state, room temperature tensile intensity is 462MPa, and yield strength is 363MPa, unit elongation is 18.7%, and yield tensile ratio is 0.78.Fig. 2 (a) and Fig. 2 (b) is the dark field image transmission photo of precipitated phase after comparative example 2 ageing treatment.
Comparative example 3
Prepare a kind of Al-Cu-Mg-Zr alloy containing scandium, the difference of the preparation method of this comparative example 3 and the preparation method of embodiment 1 is, in step 4, be by 2.9mm continue to be cold-rolled to 2.6mm thick roll plate.The Al-Cu-Mg-Zr alloy containing scandium that comparative example 3 is obtained, as shown in Fig. 3 (a), Fig. 3 (b) He Fig. 3 (c), under its alloy T6 state, room temperature tensile intensity is 486MPa, and yield strength is 445MPa, unit elongation is 11.8%, and yield tensile ratio is 0.92.
Comparative example 4
Prepare a kind of Al-Cu-Mg-Zr alloy containing scandium, the difference of the preparation method of this comparative example 3 and the preparation method of embodiment 1 is, in step 4, be by 2.9mm continue to be cold-rolled to 2.3mm thick roll plate.The Al-Cu-Mg-Zr alloy containing scandium that comparative example 3 is obtained, as shown in Fig. 3 (a), Fig. 3 (b) He Fig. 3 (c), under its alloy T6 state, room temperature tensile intensity is 517MPa, and yield strength is 495MPa, unit elongation is 10.5%, and yield tensile ratio is 0.95.
Although invention has been described by reference to the accompanying drawings above; but the present invention is not limited to above-mentioned embodiment; above-mentioned embodiment is only schematic; instead of it is restrictive; those of ordinary skill in the art is under enlightenment of the present invention; when not departing from present inventive concept, can also make a lot of distortion, these all belong within protection of the present invention.
Claims (2)
1., containing an Al-Cu-Mg-Zr alloy for the high-strength and high ductility of scandium, it is characterized in that, this alloy is made up of following alloying element and mass percentage thereof: copper: 3.0 ~ 5.0%; Magnesium: 1.5 ~ 2.5%; Scandium: 0.05 ~ 0.20%; Zirconium: 0.1 ~ 0.4%; Surplus is aluminium; Under alloy T6 state, mechanical properties reaches 588MPa, and yield strength reaches 560MPa, and unit elongation is 9.6%, and yield tensile ratio reaches 0.96.
2. press the preparation method containing the Al-Cu-Mg-Zr alloy of the high-strength and high ductility of scandium described in claim 1, it is characterized in that, comprise the following steps:
Step one, the aluminium ingot of 99.9wt.% is greater than with massfraction, massfraction is greater than the copper ingot of 99.9wt.%, massfraction is greater than the magnesium ingot of 99.9wt.%, Al-2wt.%Sc master alloy and Al-5wt.%Zr master alloy are melting raw material, by described aluminium ingot, copper ingot, magnesium ingot, the mass ratio of Al-2wt.%Sc intermediate alloy ingot and Al-5wt.%Zr intermediate alloy ingot is (0.8 ~ 0.9): (0.03 ~ 0.05): (0.01 ~ 0.03): (0.03 ~ 0.1): (0.02 ~ 0.08), adopt electromagnetic induction melting method molten alloy, smelting temperature controls at 680 ~ 720 DEG C, and under vacuum atmosphere, water in the mould casting from and be preheated to 200 DEG C, natural air cooling becomes ingot casting,
Step 2, ladle barrow Milling Machining step one obtained are the sheet material that 20mm is thick, are then positioned in chamber type electric resistance furnace and at 345 ~ 355 DEG C, carry out pre-treatment 8h successively, at 475 ~ 485 DEG C, carry out Homogenization Treatments 20h;
Step 3, first the sheet material after Homogenization Treatments is carried out preheating 2h at 450 DEG C of temperature, at 450 DEG C of temperature, be then rolling to that 6.0mm is thick rolls plate, at 400 DEG C, process annealing 2h, naturally cools to room temperature, finally, be cold-rolled to 2.9mm thick roll plate;
Step 4, the plate that rolls thick for 2.9mm is carried out 1h solution treatment at 500 DEG C, in room temperature water, then carry out quench treatment be cooled to room temperature, quenching shift time is 10 ~ 15s, will roll afterwards plate continue cold rolling for 2.0mm thick, rolling treatment time 15min to 60min;
Step 5, the plate that rolls that 2.0mm step 4 rolling obtained is thick carry out peak ageing treatment at temperature is 190 DEG C, obtain the high-strength and high ductility Al-Cu-Mg-Zr alloy containing scandium.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106513638A (en) * | 2016-11-18 | 2017-03-22 | 喀左金牛铸造有限公司 | 2Al2 aluminum alloy casting process |
| CN111057921A (en) * | 2019-12-20 | 2020-04-24 | 山东南山铝业股份有限公司 | High-temperature-resistant high-strength aluminum alloy and preparation method thereof |
| CN112646997A (en) * | 2020-12-17 | 2021-04-13 | 东北轻合金有限责任公司 | Scandium-containing ultrahigh-strength aluminum alloy for aerospace and manufacturing method thereof |
| CN115323294A (en) * | 2022-06-30 | 2022-11-11 | 广西科技大学 | Strong plastic deformation method of Al-Cu-Mg alloy |
| CN115558827A (en) * | 2022-10-18 | 2023-01-03 | 中国航发北京航空材料研究院 | Al-Cu-Mg-Ag-Si-Sc-Mn-Zr high-strength high-heat-resistance aluminum alloy and preparation method thereof |
| CN115786787A (en) * | 2022-07-18 | 2023-03-14 | 山东浩信机械有限公司 | High-strength and high-toughness Al-Cu cast aluminum alloy and preparation method thereof |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106513638A (en) * | 2016-11-18 | 2017-03-22 | 喀左金牛铸造有限公司 | 2Al2 aluminum alloy casting process |
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| CN112646997A (en) * | 2020-12-17 | 2021-04-13 | 东北轻合金有限责任公司 | Scandium-containing ultrahigh-strength aluminum alloy for aerospace and manufacturing method thereof |
| CN115323294A (en) * | 2022-06-30 | 2022-11-11 | 广西科技大学 | Strong plastic deformation method of Al-Cu-Mg alloy |
| CN115786787A (en) * | 2022-07-18 | 2023-03-14 | 山东浩信机械有限公司 | High-strength and high-toughness Al-Cu cast aluminum alloy and preparation method thereof |
| WO2024017085A1 (en) * | 2022-07-18 | 2024-01-25 | 山东浩信股份有限公司 | High-strength and high-toughness al-cu series cast aluminum alloy, preparation method therefor, and use of same in wheel hub manufacturing |
| CN115786787B (en) * | 2022-07-18 | 2024-02-23 | 山东浩信机械有限公司 | High-strength and high-toughness Al-Cu cast aluminum alloy and preparation method thereof |
| CN115558827A (en) * | 2022-10-18 | 2023-01-03 | 中国航发北京航空材料研究院 | Al-Cu-Mg-Ag-Si-Sc-Mn-Zr high-strength high-heat-resistance aluminum alloy and preparation method thereof |
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Application publication date: 20160413 |