CN114561575A - Preparation method of Er and Zr compositely added high-toughness aluminum alloy - Google Patents
Preparation method of Er and Zr compositely added high-toughness aluminum alloy Download PDFInfo
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- CN114561575A CN114561575A CN202210201014.4A CN202210201014A CN114561575A CN 114561575 A CN114561575 A CN 114561575A CN 202210201014 A CN202210201014 A CN 202210201014A CN 114561575 A CN114561575 A CN 114561575A
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- 229910052726 zirconium Inorganic materials 0.000 title claims abstract description 25
- 229910052691 Erbium Inorganic materials 0.000 title claims abstract description 19
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 15
- 238000002360 preparation method Methods 0.000 title abstract description 4
- 239000000956 alloy Substances 0.000 claims abstract description 44
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 41
- 230000032683 aging Effects 0.000 claims abstract description 33
- 229910018571 Al—Zn—Mg Inorganic materials 0.000 claims abstract description 25
- 238000010438 heat treatment Methods 0.000 claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 13
- 239000006104 solid solution Substances 0.000 claims abstract description 9
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 3
- 238000005098 hot rolling Methods 0.000 claims description 20
- 238000000137 annealing Methods 0.000 claims description 11
- 238000001816 cooling Methods 0.000 claims description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 10
- 238000004321 preservation Methods 0.000 claims description 9
- 229910052725 zinc Inorganic materials 0.000 claims description 7
- 239000002131 composite material Substances 0.000 claims description 2
- 238000000265 homogenisation Methods 0.000 abstract description 7
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 239000000243 solution Substances 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 239000000463 material Substances 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229910052706 scandium Inorganic materials 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
Abstract
A preparation method of a high-toughness aluminum alloy compositely added with Er and Zr relates to the field of aluminum alloys. The mass percentage of the elements is Zn 5.0-5.5%, Mg: 3.0-3.3%, Mn: 0.25 to 0.3 percent of Al, 0.10 to 0.13 percent of micro-alloy element Er, 0.10 to 0.13 percent of Zr, and the balance of Al and inevitable impurities; the invention also discloses a thermal deformation process and a heat treatment process of the high-strength and high-toughness Al-Zn-Mg aluminum alloy added with trace Er and Zr, wherein the thermal deformation process comprises homogenization, thermal deformation, solid solution treatment and aging treatment. The invention has excellent room temperature tensile property, meets the industrial application requirements in the field of rail transit and transportation, and is suitable for production and manufacturing.
Description
Technical Field
The invention belongs to the technical field of metal alloys, and particularly relates to a preparation method of a high-strength and high-toughness Al-Zn-Mg aluminum alloy.
Background
The aluminum alloy has high specific modulus, high specific strength and excellent electrical conductivity, thermal conductivity and corrosion resistance, and the excellent properties enable the aluminum alloy to be widely applied to the fields of pressure vessel manufacturing, automobile manufacturing, aerospace and rail traffic. Currently, an Al-Zn-Mg alloy as an ultra-hard aluminum comprises alloy elements such as Zn, Mg, Cu, Mn, Sc, Zr and the like, wherein Zn and Mg are main alloy elements. The addition of trace rare earth elements in the Al-Zn-Mg alloy can effectively improve the microstructure of the alloy and improve and promote the comprehensive properties of the aluminum alloy, such as obdurability, corrosion resistance, fatigue resistance and the like. In all microalloying elements, the existing research shows that the addition of Er not only obviously improves the material performance, but also reduces the cost of the alloy material. However, Er has a limited solubility in aluminum alloys, Er-containing eutectic phases are precipitated in Al-Zn-Mg alloys at the grain boundaries of the cast structure, and are difficult to eliminate in homogenization treatment, Er has a high diffusion rate in aluminum alloys, and Al is dissolved in a solid solution at high temperatures3The (Er) phase is easy to coarsen and loses the effects of grain refinement, nail rolling dislocation and substructure, thereby greatly reducing the effect of improving the comprehensive mechanical property of the Al-Zn-Mg alloy by microalloying.
Aiming at the characteristic that the mechanical property of the Al-Zn-Mg alloy added with rare earth element Er alone is not improved enough, the rare earth element Er and transition group element Zr are added into the Al-Zn-Mg alloy for carrying out tissue modification. Al formation in hot rolling of Al-Zn-Mg alloys3The (Er, Zr) phase has excellent thermal stability, further refines the crystal grains of the whole structure, reduces the growth of epitaxial crystal grains, and finally achieves the purpose of improving the comprehensive mechanical property of the Al-Zn-Mg alloy by adopting an aging process of slowly raising the temperature to the aging temperature.
Disclosure of Invention
The invention aims to provide an Al-Zn-Mg alloy compositely added with trace Er and Zr elements and a thermal mechanical treatment process suitable for improving the strength of the aluminum alloy, so as to obtain an Er-Zr-containing Al-Zn-Mg alloy material with high strength and high toughness.
The Al-Zn-Mg alloy compositely added with trace Er and Zr comprises the following components in percentage by mass: 5.0-5.5% of Zn, Mg: 3.0-3.3%, Mn: 0.25 to 0.3 percent of the master alloy, 0.10 to 0.13 percent of the microalloy element Er, 0.10 to 0.13 percent of Zr, and the balance of Al and inevitable impurities.
The invention provides a heat treatment process suitable for an Al-Zn-Mg alloy compositely added with trace Er and Zr elements, which is characterized by comprising the following steps of:
(1) carrying out homogenizing annealing treatment on the Al-Zn-Mg alloy water-cooled ingot which is compositely added with trace Er and Zr, wherein the single-stage homogenizing annealing temperature is 470-480 ℃, the heat preservation time is 24h, and the ingot is cooled in a door opening furnace;
(2) carrying out hot rolling on the homogenized alloy, wherein the hot rolling temperature is 470 ℃, the heat preservation time of each pass is 20min, the hot rolling pass is 6, and the total deformation is 80%;
(3) carrying out solid solution and aging treatment on the hot rolled plate, wherein the selected solid solution treatment temperature is 470 ℃, the heat preservation time is 1h, and water cooling is adopted; aging treatment: slowly heating from 20-25 ℃ to 120 ℃ of ageing temperature, slowly heating for 5h, ageing treatment for 24h, and cooling with water.
Compared with the prior art, the invention has the beneficial effects that:
1. the invention adopts a single-stage homogenization annealing process, and a reasonable homogenization system is favorable for Al3The dispersion precipitation of (Er, Zr) particles can basically eliminate nonequilibrium phase at the grain boundary of the as-cast alloy, and is particularly more important for the high-alloying Al-Zn-Mg alloy with more complex second phase change. The Al-Zn-Mg alloy has dendrite segregation during solidification, and the nonuniformity of chemical components and structures in the alloy must be reduced or eliminated through homogenizing annealing, and simultaneously, the internal stress generated during solidification is eliminated, the thermal deformation capability of the alloy is improved, and the mechanical property is improved.
2. For the hot extrusion process provided by the invention, although the strength of the Al-Zn-Mg aluminum alloy after hot processing is relatively reduced, the distribution of the structure becomes more uniform, and the plasticity of the alloy is also greatly improved.
3. For the solid solution and aging process provided by the invention, the maximum solute supersaturation degree of the matrix is obtained through reasonable solid solution treatment, and meanwhile, Al is added3The (Er, Zr) particles hinder the growth of recrystallized grains, so that the effect of refining the grains is achieved, and the ductility and toughness of the material are improved; the aging precipitation phase in the matrix is fully nucleated and grows for a long time by slowly raising the temperature to reach the peak aging temperature, so that higher aging strength is obtained.
Detailed Description
The present invention will be described in further detail with reference to examples, but the present invention is not limited to the following examples.
Table 1 shows the tensile properties of the Al-Zn-Mg alloy with trace Er and Zr added in a compounding way from low temperature to aging temperature;
table 2 shows the tensile properties of the Er-added Al-Zn-Mg alloy after solution treatment by slowly raising the temperature from a low temperature to an aging temperature;
table 3 shows the tensile properties of the Al-Zn-Mg alloy compositely added with trace Er and Zr after no slow heating aging treatment;
example 1
The weight percentage of one of the components is as follows: 5.1% of Zn, and Mg: 3.2%, Mn: 0.25 percent of microalloy element Er, 0.10 percent of Zr, the balance of Al and inevitable impurities, performing a single-stage homogenization annealing process on a water-cooled ingot, performing 6 times of hot rolling on the alloy, wherein the hot rolling heat preservation temperature is 470 ℃, the size after hot rolling is 2mm, placing a rolled plate in a high-temperature furnace for solution treatment, the solution treatment process is 470 ℃/1h, immediately placing the rolled plate in an aging furnace after water cooling, slowly heating from 20 ℃ to 120 ℃ of the aging temperature, the heating time is 5h, the aging treatment heat preservation time is 24h, and performing water cooling. The aged material was subjected to tensile testing and the data are given in table 1.
Comparative example 1
The weight percentage of one of the components is as follows: 5.1% of Zn, and Mg: 3.2%, Mn: 0.26 percent of microalloy element Er, 0.10 percent of microalloy element Er, the balance of Al and inevitable impurities, performing a single-stage homogenization annealing process on a water-cooled ingot, performing 6 times of hot rolling on the alloy, performing hot rolling at the hot rolling heat preservation temperature of 470 ℃, performing hot rolling to the size of 2mm, placing a rolled plate in a high-temperature furnace for solution treatment at the solution treatment temperature of 470 ℃/1h, immediately placing the rolled plate in an aging furnace after water cooling, slowly heating from 20 ℃ to the aging temperature of 120 ℃, heating for 5h, performing aging treatment for 24h, and performing water cooling. The aged material was subjected to tensile testing and the data are shown in table 2.
Comparative example 2
The weight percentage of one of the components is as follows: 5.2% of Zn, Mg: 3.2%, Mn: 0.25 percent of microalloy element Er, 0.10 percent of Zr, 0.11 percent of Zr, the balance of Al and inevitable impurities, performing a single-stage homogenization annealing process on the water-cooled ingot, performing 6-pass hot rolling on the alloy, keeping the hot rolling temperature at 470 ℃, performing the hot rolling to the size of 2mm, placing the rolled plate in a high-temperature furnace for solution treatment, performing the solution treatment at 470 ℃/1h, immediately placing the rolled plate in an aging furnace after water cooling, and performing the water cooling with the aging process at 120 ℃/24 h. The aged material was subjected to tensile testing and the data are given in table 3.
Comparing the results of example 1 with those of comparative example 1, the results show that the yield strength, tensile strength and elongation of the alloy are significantly higher than those of comparative example 1 by adding Er and Zr in a small amount in combination, while the holding temperature, time and deformation parameters are the same in both of the single-stage homogenizing annealing, hot rolling and solution aging treatment. The result shows that the composite addition of trace Er and Zr is beneficial to the comprehensive mechanical property of the Al-Zn-Mg alloy.
Comparing the results of example 1 with those of comparative example 2, it is shown that both have the same alloying elements and comprise a single-stage temper and solution treatment with the same holding temperature and holding time and a hot rolling with the same deformation parameters, whereas the aging treatment of example 1 is carried out by slowly raising the temperature to the aging temperature at a low temperature, and the yield strength and tensile strength of the alloy are significantly higher than those of comparative example 2. The result shows that the aging treatment process of slowly heating from low temperature to aging temperature can greatly improve the strength of the Al-Zn-Mg alloy.
According to the description of the results, the strength and the elongation of the alloy obtained by the alloy with the addition of trace Er and Zr after single-stage homogenizing annealing, multi-pass hot rolling, high-temperature solid solution and aging treatment from low-temperature slow heating to aging temperature are obviously improved. The alloy of the invention is beneficial to solving the problem of poor comprehensive mechanical property of Al-Zn-Mg alloy
Table 1 example 1 tensile properties
Table 2 tensile properties of comparative example 1
TABLE 3 tensile Properties of comparative example 2
Claims (2)
1. The high-toughness Er and Zr-compounded aluminum alloy is characterized in that the alloy comprises the following components in parts by weight: 5.0-5.5% of Zn, Mg: 3.0-3.3%, Mn: 0.25 to 0.3 percent of Al, 0.10 to 0.13 percent of micro-alloy element Er, 0.10 to 0.13 percent of Zr, and the balance of Al and inevitable impurities.
2. The heat treatment process of the Er and Zr composite added high-strength and high-toughness aluminum alloy according to claim 1, is characterized by comprising the following steps of:
(1) carrying out homogenizing annealing treatment on the Al-Zn-Mg alloy water-cooled ingot which is compositely added with trace Er and Zr, wherein the single-stage homogenizing annealing temperature is 470-480 ℃, the heat preservation time is 24h, and the ingot is cooled in a door opening furnace;
(2) hot rolling the homogenized alloy, wherein the hot rolling temperature is 470 ℃, the heat preservation time of each pass is 20min, the hot rolling passes are 6, and the total deformation is 80%;
(3) carrying out solid solution and aging treatment on the hot rolled plate, wherein the selected solid solution treatment temperature is 470 ℃, the heat preservation time is 1h, and water cooling is adopted; and (3) aging treatment: slowly heating from 20-25 ℃ to 120 ℃ of ageing temperature, slowly heating for 5h, ageing treatment for 24h, and cooling with water.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210201014.4A CN114561575A (en) | 2022-03-02 | 2022-03-02 | Preparation method of Er and Zr compositely added high-toughness aluminum alloy |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210201014.4A CN114561575A (en) | 2022-03-02 | 2022-03-02 | Preparation method of Er and Zr compositely added high-toughness aluminum alloy |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114990396A (en) * | 2022-07-11 | 2022-09-02 | 上海交通大学 | Ultrahigh-strength 7000 series aluminum alloy material and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101413080A (en) * | 2008-11-13 | 2009-04-22 | 苏州有色金属研究院有限公司 | Al-Zn-Mg-Cu-Zr-Er alloy |
| JP2010262991A (en) * | 2009-04-30 | 2010-11-18 | Kobe Steel Ltd | Al alloy film for display device having superior developer resistance, display device, and sputtering target |
| CN107058825A (en) * | 2016-02-11 | 2017-08-18 | 空中客车防务和空间有限责任公司 | The Al Mg Zn alloys with scandium for the unitary construction of ALM structures |
-
2022
- 2022-03-02 CN CN202210201014.4A patent/CN114561575A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101413080A (en) * | 2008-11-13 | 2009-04-22 | 苏州有色金属研究院有限公司 | Al-Zn-Mg-Cu-Zr-Er alloy |
| JP2010262991A (en) * | 2009-04-30 | 2010-11-18 | Kobe Steel Ltd | Al alloy film for display device having superior developer resistance, display device, and sputtering target |
| CN107058825A (en) * | 2016-02-11 | 2017-08-18 | 空中客车防务和空间有限责任公司 | The Al Mg Zn alloys with scandium for the unitary construction of ALM structures |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114990396A (en) * | 2022-07-11 | 2022-09-02 | 上海交通大学 | Ultrahigh-strength 7000 series aluminum alloy material and preparation method and application thereof |
| CN114990396B (en) * | 2022-07-11 | 2023-02-24 | 上海交通大学 | Ultrahigh-strength 7000 series aluminum alloy material and preparation method and application thereof |
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