CN110951981B - Method for improving corrosion resistance of 7-series aluminum alloy - Google Patents
Method for improving corrosion resistance of 7-series aluminum alloy Download PDFInfo
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- CN110951981B CN110951981B CN201911339794.3A CN201911339794A CN110951981B CN 110951981 B CN110951981 B CN 110951981B CN 201911339794 A CN201911339794 A CN 201911339794A CN 110951981 B CN110951981 B CN 110951981B
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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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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- 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
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Abstract
The invention discloses a method for improving the corrosion resistance of a 7-series aluminum alloy, which comprises 6 process steps of casting, homogenizing, hot working, solid solution, critical temperature deformation and aging, wherein the core step is the critical temperature deformation process, and the aluminum alloy section subjected to solid solution is subjected to 1-2% of temperature deformation at 95-105 ℃. According to the invention, the aluminum alloy section after solid solution is subjected to critical temperature deformation, so that a deformation induced phase transformation process is generated in the alloy, and the corrosion resistance of the alloy can be improved by improving the distribution of aging precipitation phases in the alloy on the basis of not losing the strength and plasticity of the alloy, thereby providing a safer 7-series aluminum alloy product for practical application; the method has simple process flow, only needs to add a small deformation processing on the basis of the traditional 7-series aluminum alloy production process, does not generate waste materials and environmental harmful substances in the process, and is beneficial to popularization and use.
Description
Technical Field
The invention belongs to the field of preparation of non-ferrous metal materials, and particularly relates to a method for improving corrosion resistance of 7-series aluminum alloy.
Background
The 7 series aluminum alloy is used as the highest-strength aluminum alloy and is often used as a load-bearing part in the fields of airplanes, high-speed rails, automobiles and the like, and particularly, the 7 series aluminum alloy section combines the ultrahigh strength (more than 500MPa) and the excellent plasticity, so that the 7 series aluminum alloy section is increasingly applied to the related fields under the situation that the lightweight manufacturing standard is increasingly strict. The high strength of the 7-series aluminum alloy is derived from the high alloy composition, which brings a significant disadvantage to the 7-series aluminum alloy, namely, the poor corrosion resistance, compared with the 6-series and 5-series aluminum alloys, the 7-series aluminum alloy is often coated with pure aluminum or anodized to improve the corrosion resistance, or the corrosion resistance of the alloy is improved by adding trace alloy elements.
For example, chinese patent No. cn201711256180.x discloses a preparation process of a rare earth aluminum alloy material with good corrosion resistance, and the corrosion resistance of the aluminum alloy is improved by adding rare earth into the alloy. However, rare earth elements are easily oxidized in the casting process, so that special anti-oxidation process equipment is needed when the method is used for preparing the aluminum alloy, the operation process is complex, and the production cost is increased. In addition, the rare earth elements are generally expensive, which also results in the increase of the raw material cost of the aluminum alloy, which is very unfavorable for the popularization and use of the novel aluminum alloy in the civil field. The Chinese patent with the patent number of CN201721632017.4 discloses an anti-corrosion super-weather-resistant aluminum alloy section, and the main method is to realize the anti-corrosion of the aluminum alloy by preparing a multi-layer composite polymer coating on the surface of the aluminum alloy. The method has high production cost and complex process, and can generate some environmental harmful substances in the production process due to the production and the manufacture of the high polymer material, thereby being not beneficial to environmental protection.
Disclosure of Invention
Aiming at the problems of improving the corrosion resistance of the 7-series aluminum alloy, the invention provides a novel method for improving the corrosion resistance of the 7-series aluminum alloy, which has the core principle that the aluminum alloy section after solid solution is subjected to 1-2% of temperature deformation at 95-105 ℃, so that the alloy is subjected to deformation induced phase change precipitation process, and in the process, as the phase change precipitation is performed on the basis of deformation and the deformation is performed at a grain boundary and in a crystal, a precipitation phase in the aluminum alloy can be generated simultaneously at the grain boundary and in the crystal boundary, so that a precipitation-free precipitation zone can be avoided, and the corrosion resistance of the 7-series aluminum alloy is improved; the method has simple process flow, only needs to add a small deformation processing on the basis of the traditional 7-series aluminum alloy production process, does not generate waste materials and environmental harmful substances in the process, and is beneficial to popularization and use.
The purpose of the invention can be realized by the following technical scheme:
a method for improving the corrosion resistance of a 7-series aluminum alloy comprises 6 working procedures of casting, homogenization, hot working, solid solution, critical temperature deformation and aging, and specifically comprises the following steps:
the first step, the fusion casting process: firstly, smelting pure aluminum, adding alloy elements of Zn, Mg, Cu and Cr after the pure aluminum is completely molten, degassing and deslagging after the alloy elements are completely molten, and finally, casting after the temperature of a melt is stabilized to be 30-50 ℃ (680 and 710 ℃);
step two, a homogenization procedure: homogenizing the alloy ingot at the temperature of 410-420 ℃ for 3-6 hours, fully eliminating dendrites and coarse primary equivalences in the alloy, so as to improve the uniformity of the structure and components of the alloy and improve the hot processing technological performance of the alloy;
step three, a hot working procedure: hot extruding or hot rolling the homogenized alloy ingot at the temperature of 360-380 ℃ to prepare the required 7-series aluminum alloy sections with various cross-sectional shapes, and air cooling the alloy sections after hot processing;
step four, a solid solution process: after the 7-series aluminum alloy section obtained in the last step is subjected to heat preservation at the temperature of 430-435 ℃ for 1 hour, water-cooling quenching is carried out, and full solid solution of each element in the alloy is realized;
it is noted that the alloy transfer time after solution and before quenching does not exceed 20 seconds;
step five, critical temperature deformation process: the 7-series aluminum alloy section after solid solution is subjected to 1-2% of tensile deformation at 95-105 ℃, so that a deformation induced phase transformation precipitation process is generated in the alloy, and in the process, a large amount of dislocation is generated from the grain boundary to the interior of the alloy due to deformation, so that a large amount of deformation induced precipitation phases are generated on the dislocation, and the aging precipitation phases of the alloy are uniformly distributed from the interior of the alloy to the grain boundary, and compared with the method for direct aging after solid solution in the conventional process, the invention can obviously improve the distribution condition of the precipitation phases in the alloy finished product;
sixth step, aging process: aging the aluminum alloy section processed at the critical temperature at 140-150 ℃ for 24 hours to ensure that a precipitated phase grows up by maturity on the basis of the prior deformation induced precipitation of the alloy, thereby forming a dispersed peak aging precipitated phase structure, and after aging treatment, because the aging precipitation mainly depends on a second phase crystal nucleus precipitated by the deformation induced precipitation, the precipitation quantity on a crystal boundary in the alloy is very small, and a precipitation-free precipitation zone is very narrow, thereby obviously improving the corrosion resistance of the alloy on the premise of not losing the strength and the plasticity of the alloy;
the invention has the beneficial effects that:
1. compared with other methods for improving the corrosion performance of the 7-series aluminum alloy, the method does not need surface treatment procedures such as surface coating, anodic oxidation and the like, so that no chemical substances harmful to the environment are generated.
2. The invention does not need to change the alloy components to improve the corrosion resistance of the alloy, has simpler and more feasible process, does not need to add rare earth and other expensive alloy elements, has low process cost, and is beneficial to the popularization and the application of the method.
3. The process can be operated by adopting the pre-stretching machine which is arranged in a common aluminum profile factory without adopting special tooling equipment, and is also beneficial to popularization and application.
Drawings
The invention will be further described with reference to the accompanying drawings.
FIG. 1 is a side corrosion profile of 7-series aluminum alloy extruded profiles obtained in example 1 and comparative example 1 of the present invention.
FIG. 2 is a surface corrosion topography of 7-series aluminum alloy plates prepared according to example 2 and comparative example 2 of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
This example illustrates the preparation of a 7-series aluminum alloy extruded profile.
1. Firstly, smelting pure aluminum, adding alloy elements of Zn, Mg, Cu and Cr after the pure aluminum is melted, degassing and deslagging after the alloy elements are completely melted, and finally, stabilizing the temperature of a melt at 710 ℃ and then casting to obtain a 7-series aluminum alloy cylindrical ingot with the diameter of 400 mm.
2. The alloy cast ingot is homogenized for 5 hours at 420 ℃, so that dendrites in the alloy are fully eliminated, the thickness of the dendrites is equal for the first time, the structure and the component uniformity of the alloy are improved, the hot extrusion technological performance of the alloy is improved, the hot extrusion force is reduced, and the hot extrusion speed is increased.
3. And (3) carrying out hot extrusion on the homogenized alloy cast ingot at the temperature of 380 ℃ to prepare a section with the cross section being I-shaped, and carrying out air cooling on the alloy section at an outlet of an extrusion die after the hot extrusion.
4. After the 7-series aluminum alloy section subjected to hot extrusion is subjected to heat preservation at 435 ℃ for 1 hour, water cooling quenching and solid solution are carried out, so that the full redissolution of each element in the alloy is realized, and the alloy transfer time before quenching after solid solution is not more than 20 seconds.
5. And (3) carrying out 2% critical temperature stretching deformation on the 7-series aluminum alloy section after solid solution at 05 ℃ to enable the alloy to generate a deformation induced phase change precipitation process, so as to prepare an alloy microstructure with the aging precipitation phase uniformly distributed from the inside of the alloy to the grain boundary.
6. Aging the aluminum alloy section bar stretched at the critical temperature for 24 hours at 150 ℃, so that a precipitated phase grows up by maturity on the basis of the previous deformation induced precipitation of the alloy, thereby forming a peak aging precipitated phase structure distributed in a dispersed manner, and after the aging treatment, because the aging precipitation mainly depends on a second phase crystal nucleus precipitated by the deformation induced precipitation, the precipitation quantity on a crystal boundary in the alloy is very small, and a precipitation-free precipitation zone is very narrow, thereby obviously improving the corrosion resistance of the alloy on the premise of not losing the strength and the plasticity of the alloy.
The mechanical properties of the finally obtained 7-series aluminum alloy section bar are yield strength 540MPa, tensile strength 600MPa and elongation 9%, and the alloy is placed in NaCl of 57g/L and H of 10mL/L2O2Soaking in (1.1g/mL) solution for 6h, wherein the cross section intercrystalline corrosion morphology of the corroded alloy is shown in figure 1a, and the maximum corrosion depth of the alloy is 51 microns.
Comparative example 1
As a conventional process for 7-series aluminum alloy to be compared with example 1, the alloy is subjected to aging at 150 ℃ for 24 hours directly without critical temperature stretching after solid solution, the mechanical properties of the finally obtained alloy are yield strength 535MP, tensile strength 590MPa and elongation 9%, and the alloy is placed in NaCl of 57g/L and H of 10mL/L2O2Soaking in (1.1g/mL) solution for 6h, wherein the cross section intercrystalline corrosion morphology of the corroded alloy is shown in figure 1b, and the maximum corrosion depth of the alloy is 180 micrometers;
the results of example 1 and comparative example 1 show that the mechanical properties of the 7-series aluminum alloy section prepared by the method are equivalent to those of the 7-series aluminum alloy prepared by the traditional process, but the corrosion resistance is obviously improved.
Example 2
This example is an example of producing a 7-series aluminum alloy rolled sheet.
1. Firstly, smelting pure aluminum, adding alloy elements of Zn, Mg, Cu and Cr after the pure aluminum is melted, degassing and deslagging after the alloy elements are completely melted, and finally, casting after the melt temperature is stabilized at 690 ℃ to obtain a 7-series aluminum alloy rectangular ingot with the cross section size of 400mm multiplied by 240 mm.
2. The alloy cast ingot is homogenized for 5 hours at 410 ℃, so that dendrites and coarse primary phase in the alloy are fully eliminated, the uniformity of the structure and components of the alloy is improved, the hot rolling process performance of the alloy is improved, and the hot rolling cracking prevention is facilitated.
3. And hot-rolling the homogenized alloy ingot at the temperature of 360 ℃ for multiple times to obtain a plate with the thickness of 20mm, and air-cooling the alloy plate after hot rolling.
4. After the hot-rolled 7-series aluminum alloy plate is subjected to heat preservation at 430 ℃ for 1 hour, water spraying quenching and solid solution are carried out, so that the full redissolution of each element in the alloy is realized, and the alloy transfer time before quenching after solid solution is not more than 20 seconds.
5. And (3) carrying out 1% of critical temperature stretching deformation on the 7-series aluminum alloy plate after solid solution at 95 ℃, so that a deformation induced phase change precipitation process is generated in the alloy, and an alloy microstructure with uniformly distributed alloy aging precipitation phases from the inside of the crystal to the grain boundary is prepared.
6. Aging the aluminum alloy plate stretched at the critical temperature for 24 hours at 140 ℃, so that a precipitated phase grows up by ripening on the basis of the previous deformation induced precipitation of the alloy, thereby forming a peak aging precipitated phase structure distributed in a dispersed manner, and after the aging treatment, because the aging precipitation mainly depends on a second phase crystal nucleus precipitated by the deformation induced precipitation, the precipitation quantity on a crystal boundary in the alloy is small, and a precipitation-free precipitation zone is narrow, thereby obviously improving the corrosion resistance of the alloy on the premise of not losing the strength and the plasticity of the alloy.
The mechanical properties of the finally obtained alloy are 500MPa of yield strength, 560MPa of tensile strength and 10% of elongation, the alloy is soaked in an EXCO solution for 24 hours, and the result of evaluating the surface corrosion of the alloy according to the ASTMG34-2001 standard is shown in figure 2a, and the alloy shows slight peeling corrosion.
Comparative example 2
As the conventional process of the 7 series aluminum alloy for comparison in example 2, the alloy is directly aged at 140 ℃ for 24 hours without critical temperature stretching after solid solution, the mechanical property indexes of the alloy are 505MPa of yield strength, 560MPa of tensile strength and 10 percent of elongation, and the result of evaluating the surface corrosion of the alloy according to the ASTMG34-2001 standard after the alloy is soaked in an EXCO solution for 24 hours is shown in FIG. 2b, which shows that the alloy shows serious spalling corrosion.
Fig. 2 and the above experimental results show that the mechanical properties of the 7-series aluminum alloy plate prepared by the method of the present invention are equivalent to those of the 7-series aluminum alloy prepared by the conventional process, but the spalling corrosion resistance is significantly improved.
In conclusion, the corrosion resistance of the alloy can be obviously improved by adopting the method disclosed by the invention on the premise of not losing the mechanical property of the 7-series aluminum alloy by combining the examples 1-2 and the comparative examples 1-2.
The foregoing is merely exemplary and illustrative of the present invention and various modifications, additions and substitutions may be made by those skilled in the art to the specific embodiments described without departing from the scope of the invention as defined in the following claims.
Claims (1)
1. The method for improving the corrosion resistance of the 7-series aluminum alloy is characterized by comprising 6 process steps of casting, homogenizing, hot working, solid solution, critical temperature deformation and aging, and specifically comprises the following steps:
the first step, the fusion casting process: firstly, smelting pure aluminum, adding alloy elements after the pure aluminum is completely molten, degassing and deslagging after the alloy elements are completely molten, and finally casting the melt to obtain an alloy ingot;
the alloy elements comprise Zn, Mg, Cu and Cr alloy elements; the concrete mode of the casting is as follows: stabilizing the temperature of the melt at 30-50 ℃ higher than the alloy liquidus line, and then casting;
step two, a homogenization procedure: homogenizing the alloy ingot at the temperature of 410-420 ℃ for 3-6 hours;
step three, a hot working procedure: hot extruding or hot rolling the homogenized alloy ingot at the temperature of 360-380 ℃ to prepare the required 7-series aluminum alloy sections with various cross-sectional shapes, and air cooling the alloy sections after hot processing;
step four, a solid solution process: after the 7-series aluminum alloy section obtained in the last step is subjected to heat preservation at the temperature of 430-435 ℃ for 1 hour, water-cooling quenching is carried out, and full solid solution of each element in the alloy is realized;
the alloy transfer time after solid solution and before quenching is not more than 20 seconds;
step five, critical temperature deformation process: carrying out 1% -2% tensile deformation on the solid-dissolved 7-series aluminum alloy section at 95-105 ℃;
sixth step, aging process: aging the aluminum alloy section subjected to critical temperature processing at the temperature of 140 ℃ and 150 ℃ for 24 hours.
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101037748A (en) * | 2007-04-29 | 2007-09-19 | 东北轻合金有限责任公司 | Aviation aluminum alloy pre-stretching plate and production method thereof |
| CN102978544A (en) * | 2012-11-21 | 2013-03-20 | 中南大学 | Method for multilevel creep age forming of Al-Zn-Mg-Cu series aluminium alloy plate |
| CN103614597A (en) * | 2013-11-22 | 2014-03-05 | 中南大学 | Anti-exfoliation corrosion high-strength aluminum-zinc-magnesium-copper alloy and heat treatment process |
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101037748A (en) * | 2007-04-29 | 2007-09-19 | 东北轻合金有限责任公司 | Aviation aluminum alloy pre-stretching plate and production method thereof |
| CN102978544A (en) * | 2012-11-21 | 2013-03-20 | 中南大学 | Method for multilevel creep age forming of Al-Zn-Mg-Cu series aluminium alloy plate |
| CN103614597A (en) * | 2013-11-22 | 2014-03-05 | 中南大学 | Anti-exfoliation corrosion high-strength aluminum-zinc-magnesium-copper alloy and heat treatment process |
Non-Patent Citations (2)
| Title |
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| Effect of large cold deformation after solution treatment on precipitation characteristic and deformation strengthening of 2024 and 7A04 aluminum alloys;Ning Ailin etal;《Transaction of Nonferrous Metals Society of China》;20061231;1341-1347 * |
| 最终形变热处理工艺对 Al-5.2Mg-3.1Zn铝合金组织性能的影响;丁清伟等;《稀有金属材料与工程》;20190831;2661-2666 * |
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