CN115679168B - Al-Zn-Mg aluminum alloy with high strength and high stress corrosion resistance, preparation method and application - Google Patents
Al-Zn-Mg aluminum alloy with high strength and high stress corrosion resistance, preparation method and application Download PDFInfo
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- 229910018571 Al—Zn—Mg Inorganic materials 0.000 title claims abstract description 48
- 238000002360 preparation method Methods 0.000 title claims abstract description 7
- 230000007797 corrosion Effects 0.000 title abstract description 38
- 238000005260 corrosion Methods 0.000 title abstract description 38
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 35
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 230000032683 aging Effects 0.000 claims description 33
- 238000001125 extrusion Methods 0.000 claims description 29
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Abstract
The invention discloses an Al-Zn-Mg aluminum alloy with high strength and high stress corrosion resistance, a preparation method and application thereof. The Al-Zn-Mg aluminum alloy comprises the following components ：Zn：5.0％-8.0％,Mg：1.50％-2.50％,Cu：0.10％-0.60％,Mn：0.25％-0.60％,Cr≤0.15％,Zr≤0.20％,Ti≤0.10％,Si≤0.20％,Fe≤0.2％,Al：85.45％-91.80％. by mass percent, and has higher mechanical property and excellent stress corrosion resistance.
Description
Technical Field
The invention relates to the technical field related to aluminum alloy extruded materials, in particular to an Al-Zn-Mg aluminum alloy with high strength and high stress corrosion resistance, a preparation method and application thereof.
Background
The Al-Zn-Mg aluminum alloy is widely applied to the fields of aerospace, rail traffic, high-end automobile manufacturing and the like because of good mechanical property, formability, workability and corrosion resistance. In recent years, with the development of new energy automobiles, the replacement of steel materials with aluminum alloy extruded profiles for automobile body parts has become an important means for realizing the goals of light weight, energy conservation and emission reduction in various large automobile main engine factories.
The aluminum alloy extruded section for the automobile needs to have high strength on one hand and good stress corrosion resistance on the other hand. The Al-Zn-Mg aluminum alloy takes Zn and Mg as main alloy components, has some advantages, such as good plastic deformation capability in a high-temperature (lower than solid solution temperature) state, and can obtain aluminum alloy sections with various cross-section shapes through extrusion; a large amount of MgZn 2 strengthening phases are separated out after on-line solution quenching and subsequent aging treatment, so that the alloy has higher strength. However, the existing Al-Zn-Mg aluminum alloys also have some disadvantages, such as poor matching of the strength of the alloy with the stress corrosion resistance. When the Zn and Mg element contents in the Al-Zn-Mg aluminum alloy are improved, the alloy subjected to the T6 ageing treatment can be ensured to obtain the highest strength, but the stress corrosion cracking sensitivity tendency of the alloy is increased; in the case of T73 aging, the alloy strength is lost although the stress corrosion resistance is improved. Obviously, the existing Al-Zn-Mg aluminum alloy is difficult to achieve the synergistic improvement of the comprehensive performance in terms of strength and stress corrosion resistance, and the existing Al-Zn-Mg aluminum alloy preparation method cannot meet the requirements of automobile parts on the Al-Zn-Mg aluminum alloy with high strength and high stress corrosion resistance.
Based on this, a novel Al-Zn-Mg aluminum alloy is urgently needed to solve the above-mentioned problems.
Disclosure of Invention
The first technical problem to be solved by the invention is as follows:
An Al-Zn-Mg aluminum alloy is provided.
The second technical problem to be solved by the invention is as follows:
A preparation method of the Al-Zn-Mg aluminum alloy is provided.
The third technical problem to be solved by the invention is:
The application of the Al-Zn-Mg aluminum alloy.
In order to solve the first technical problem, the invention adopts the following technical scheme:
the Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Zn：5.0％-8.0％,Mg：1.50％-2.50％,Cu：0.10％-0.60％,Mn：0.25％-0.60％,Cr≤0.15％,Zr≤0.20％,Ti≤0.10％,Si≤0.20％,Fe≤0.2％,Al：85.45％-91.80％.
According to the embodiments of the present invention, one of the technical solutions has at least one of the following advantages or beneficial effects:
1. as main alloy elements, zn and Mg contents have decisive influence on the strength of the alloy, and have extremely profound influence on the corrosion resistance and workability of the alloy, thereby influencing the final application of the alloy. Experiments show that the Zn content and the Mg content jointly determine the strength of the alloy and influence the corrosion resistance of the alloy, and on the other hand, the Zn content has an important influence on the fracture toughness of the alloy, the Mg content influences the workability of the alloy, and the too high Mg content can seriously reduce the extrudability of the material, so that the extrusion defects such as cracking, strain, surface quality reduction and the like are caused. Too high Zn and Mg content corresponds to high strength and low corrosion resistance, and too low Zn and Mg content corresponds to low strength and high corrosion resistance. Based on the above, the proper Zn and Mg contents can be selected to realize the synergistic improvement of the performances of all aspects of the Al-Zn-Mg aluminum alloy.
Cu atoms can obviously improve the stress corrosion cracking resistance of the alloy and improve the toughness of the alloy. However, too much Cu content can not only lead to a significant increase in production costs and a decrease in alloy economy, but also lead to a tendency of the alloy to produce intergranular corrosion and pitting corrosion, and too low Cu content can affect alloy strength.
When the Mn content is too low, the toughness of the alloy is adversely affected; when the Mn content is too high, a large amount of alpha-AlFeMnSi phases are formed in the alloy system, and the toughness and corrosion resistance of the alloy are reduced.
4. The (CrFe) Al 7 and (CrMn) Al 12、Al3 Zr phase particles can be formed by properly adding Cr and Zr elements, can play a role in refining grains, can inhibit nucleation and growth of recrystallization, plays a certain role in improving the strength of the alloy, can improve the toughness of the alloy and reduce the sensitivity of stress corrosion cracking.
5. The content of impurity elements Si and Fe is strictly controlled, the number of coarse AlFeSi crystal phases in the alloy matrix is reduced, and the toughness and corrosion resistance of the alloy are improved.
Ti element is generally used as a melt modifier in aluminum alloy, and Ti and B form a large number of nano TiB 2 particles serving as nucleation cores in the aluminum melt, so that the purpose of grain refinement is achieved in the casting process.
According to one embodiment of the invention, the mass percentage of Zn is as follows: 5.0% -7.0%. When the Zn content exceeds 7 mass%, the stress corrosion resistance and fracture toughness of the alloy drastically decrease, and particularly when the Zn content exceeds 8 mass%, the corrosion resistance and weldability of the alloy are remarkably deteriorated, so that it is preferable that the mass% of Zn is: 5.0% -7.0%.
According to one embodiment of the invention, the mass percentage of the Mg is as follows: 1.50% -2.0%. When the Mg content exceeds 2.5 mass%, the workability of the alloy decreases and the corrosion resistance decreases, so that it is preferable that the Mg mass% is: 1.50% -2.0%.
According to one embodiment of the invention, the Cu comprises the following components in percentage by mass: 0.20% -0.40%. Cu atoms are dissolved into an intragranular metastable eta' phase (MgZn 2 phase) and a grain boundary balance eta phase (MgZn 2 phase), so that the potential difference between a grain boundary and the intragranular can be reduced, the cracking trend along the grain is inhibited, the crack growth rate of the alloy in a corrosion environment is reduced, the stress corrosion cracking resistance of the alloy can be obviously improved, and meanwhile, cu can refine a grain boundary precipitation phase and improve the toughness of the alloy. However, too much Cu content can not only lead to a great increase in production cost and reduce the economical efficiency of the alloy, but also lead to a tendency of intergranular corrosion and pitting corrosion of the alloy, and particularly when the Cu content exceeds 1.5 mass percent, the corrosion resistance of the alloy can be obviously reduced. Based on the consideration of the addition effect and the economic cost, the mass percentages of Cu are preferably as follows: 0.20% -0.40%.
According to one embodiment of the invention, the mass percentage of Mn is as follows: 0.30% -0.50%. At a certain Fe content, too low or too high Mn content adversely affects the alloy. When the Mn content is too low, the acicular beta-AlFeSi phase cannot be fully converted into a spherical alpha-AlFeMnSi phase, so that the adverse effect of the acicular beta-AlFeSi on the alloy toughness is difficult to be completely eliminated; when the Mn content is too high, a large amount of alpha-AlFeMnSi phases are formed, and the toughness and corrosion resistance of the alloy are also reduced. In addition, the Mn content is increased, so that the recrystallization behavior of the material in the extrusion process can be obviously inhibited, the grain structure of the material is fibrous, the difficulty of the stress corrosion crack along the crystal expansion is increased, and the improvement of the stress corrosion resistance of the material is facilitated. In view of the above, there is a possibility of reducing the influence of the corrosion resistance and toughness of the needle-like β -AlFeSi relative to the alloy, and also of keeping the Mn content range of the extruded fibrous structure as much as possible, so that the mass percentages of Mn are preferably: 0.30% -0.50%.
According to one embodiment of the present invention, when the mass percentage of Cr is: 0.05% -0.10%, wherein the mass percentage of Zr is as follows: 0.10% -0.15%. The (CrFe) Al 7、(CrMn)Al12 and Al 3 Zr phase particles can be formed by properly adding Cr and Zr elements, can play a role in refining grains, can inhibit nucleation and growth of recrystallization, plays a certain role in improving the strength of the alloy, and can improve the toughness and stress corrosion cracking sensitivity of the alloy. Therefore, the Cr and Zr contents need to be added in combination so that the two can have a synergistic effect within the addition range. In addition, excessive Cr element can improve the quenching sensitivity of the alloy, increase the cooling strength requirement of on-line quenching and improve the capacity requirement of production equipment, and the addition amount of the Cr element is strictly controlled, and the mass percent of the preferable Cr is as follows: 0.05% -0.10%, wherein the mass percentage of Zr is as follows: 0.10% -0.15%.
According to one embodiment of the invention, the mass percentage of Si is less than or equal to 0.15%, and the mass percentage of Fe is less than or equal to 0.15%. When the content of Si and Fe in the alloy is too high, the quantity of coarse AlFeSi crystal phases in the alloy matrix is increased, and the toughness and corrosion resistance of the alloy are affected, based on the fact that the mass percent of Si is preferably less than or equal to 0.15%, and the mass percent of Fe is preferably less than or equal to 0.15%.
According to one embodiment of the invention, the Ti is in mass percent: 0.02% -0.10%. Ti element is generally used as a melt modifier in aluminum alloy, and Ti and B form a large number of nano TiB 2 particles serving as nucleation cores in the aluminum melt, so that the purpose of grain refinement is achieved in the casting process. However, excessive Ti forms Al 3 Ti particles which are easy to coarsen, and not only can not play a role of refining grains, but also can cause coarsening of the grains. Therefore, the Ti content is not too high, and preferably the mass percentage of Ti is as follows: 0.02% -0.10%.
In order to solve the second technical problem, the invention adopts the following technical scheme:
a method of preparing the Al-Zn-Mg aluminum alloy, comprising the steps of:
and mixing the components, and carrying out smelting, casting and three-stage homogenization treatment to obtain the Al-Zn-Mg aluminum alloy.
Wherein the three-stage homogenization treatment comprises: the homogenization annealing temperature of the first stage is 350-355 ℃, the second stage is 420-425 ℃, and the third stage is 480-485 ℃.
According to an embodiment of the present invention, the method for preparing the Al-Zn-Mg aluminum alloy further includes the steps of: after smelting, casting and three-stage homogenization treatment, extrusion, online quenching and cooling and artificial aging treatment are carried out to obtain the Al-Zn-Mg aluminum alloy extrusion profile.
According to one embodiment of the invention, the casting speed is 60-70mm/min, and water spray cooling is performed.
According to one embodiment of the invention, the three-stage homogenization treatment is carried out for 1-24h, the temperature rising rate of each stage is controlled to be 40-50 ℃/h, and strong wind and spray cooling are adopted after the third-stage treatment is carried out for heat preservation.
According to one embodiment of the invention, the process parameters of the extrusion are: heating the uniformly annealed casting rod to 480-500 ℃, putting the casting rod into an extrusion cylinder, and extruding and forming the casting rod through a preheated die to obtain an aluminum alloy profile semi-finished product. The heating temperature of the die is 460-490 ℃, and the extrusion speed is 4-7m/min.
According to one embodiment of the invention, the online quenching cooling process comprises the following steps: strong wind cooling, strong wind plus water mist cooling or water spray cooling.
According to one embodiment of the invention, the artificial aging treatment regime is: and a two-stage aging process (T73) is adopted, wherein the first-stage aging temperature is 100-105 ℃, the second-stage aging temperature is 150-155 ℃, and the heat preservation time is 1-24h.
In another aspect, the invention also relates to the use of the Al-Zn-Mg aluminum alloy in the manufacture of automobiles. Including the Al-Zn-Mg aluminum alloy described in the embodiment of the 1 st aspect. The application adopts all the technical schemes of the Al-Zn-Mg aluminum alloy of the embodiment, so that the application has at least all the beneficial effects brought by the technical schemes of the embodiment.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention.
Drawings
The foregoing and/or additional aspects and advantages of the invention will become apparent and may be better understood from the following description of embodiments taken in conjunction with the accompanying drawings in which:
FIG. 1 is a graph showing the low-power crack morphology and the cross-sectional high-power crack growth of the alloys prepared in example 1, comparative example 3 and comparative example 4.
Detailed Description
Embodiments of the present invention are described in detail below, examples of which are illustrated in the accompanying drawings, wherein like or similar reference numerals refer to like or similar elements or elements having like or similar functions throughout. The embodiments described below by referring to the drawings are illustrative only and are not to be construed as limiting the invention.
In the description of the present invention, the description of first, second, etc. is for the purpose of distinguishing between technical features only and should not be construed as indicating or implying a relative importance or implicitly indicating the number of technical features indicated or implicitly indicating the precedence of the technical features indicated.
In the description of the present invention, it should be understood that the direction or positional relationship indicated with respect to the description of the orientation, such as up, down, etc., is based on the direction or positional relationship shown in the drawings, is merely for convenience of describing the present invention and simplifying the description, and does not indicate or imply that the apparatus or element referred to must have a specific orientation, be constructed and operated in a specific orientation, and thus should not be construed as limiting the present invention.
In the description of the present invention, unless explicitly defined otherwise, terms such as arrangement, installation, connection, etc. should be construed broadly and the specific meaning of the terms in the present invention can be determined reasonably by a person skilled in the art in combination with the specific content of the technical solution.
The technical solutions of the embodiments of the present invention will be clearly and completely described below in conjunction with the embodiments of the present invention, and it is apparent that the described embodiments are only some embodiments of the present invention, not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to fall within the scope of the invention.
Example 1
The Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Si:0.08%, fe:0.10%, cu:0.25%, mn:0.37%, mg:1.67%, cr:0.08%, zn:6.75%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Example 2
The Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Si:0.08%, fe:0.10%, cu:0.28%, mn:0.40%, mg:1.74%, cr:0.08%, zn:6.95%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Example 3
The Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Si:0.08%, fe:0.10%, cu:0.33%, mn:0.43%, mg:1.81%, cr:0.08%, zn:7.15%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Example 4
The Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Si:0.08%, fe:0.10%, cu:0.25%, mn:0.37%, mg:1.81%, cr:0.08%, zn:7.15%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Example 5
The Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Zn:5.0%, mg:1.50%, cu:0.10%, mn:0.25%, cr:0.15%, zr:0.20%, ti:0.10%, si:0.20%, fe:0.2 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Example 6
The Al-Zn-Mg aluminum alloy comprises the following components in percentage by mass:
Zn:8.0%, mg:2.50%, cu:0.60%, mn:0.60%, cr:0.15%, zr:0.20%, ti:0.10%, si:0.20%, fe:0.2 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Comparative example 1
Comparative example 1 differs from example 1 in that: the amounts of the components varied, wherein example 1 included Cu:0.25%, mn:0.37%, mg:1.67%, zn:6.75%. Comparative example 1 includes Cu:0.15%, mn:0.25%, mg:2.10%, zn:8.30%.
An alloy comprising the following components in mass percent:
Si:0.08%, fe:0.10%, cu:0.15%, mn:0.25%, mg:2.10%, cr:0.08%, zn:8.30%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Comparative example 2
Comparative example 2 differs from example 1 in that: the component amounts are different. Wherein the composition of example 1 comprises Fe:0.10%, cu:0.25%, mn:0.37%, mg:1.67%, zn:6.75%. The composition of comparative example 2 includes Fe:0.10%, cu:0.45%, mn:0.35%, mg:2.20%, zn:7.50%.
An alloy comprising the following components in mass percent:
Si:0.08%, fe:0.10%, cu:0.45%, mn:0.35%, mg:2.20%, cr:0.08%, zn:7.50%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Comparative example 3
Comparative example 3 differs from example 1 in that: the component amounts are different. Wherein the composition of example 1 comprises, cu:0.25%, mn:0.37%, mg:1.67%, zn:6.75%. The components of comparative example 3 include: cu:0.65%, mn:0.25%, mg:2.40%, zn:7.6%.
An alloy comprising the following components in mass percent:
si:0.08%, fe:0.10%, cu:0.65%, mn:0.25%, mg:2.40%, cr:0.08%, zn:7.6%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Comparative example 4
Comparative example 4 differs from example 1 in that: the component amounts are different. Wherein the components of example 1 include: cu:0.25%, mn:0.37%, mg:1.67%, zn:6.75%. The components of comparative example 4 include: cu:0.05%, mn:0.45%, mg:2.80%, zn:8.50%.
An alloy comprising the following components in mass percent:
Si:0.08%, fe:0.10%, cu:0.05%, mn:0.45%, mg:2.80%, cr:0.08%, zn:8.50%, zr:0.12%, ti:0.06 percent, the total amount of other elements is less than or equal to 0.15 percent, the balance is Al, and the total mass percentage is 100 percent.
Proportioning according to a set proportion, smelting and alloying at 720 ℃, standing at 700 ℃, and casting the phi 226 aluminum rod at 690 ℃ by adopting a semi-continuous casting method.
The aluminum bar adopts a three-stage homogenizing annealing process: 350 ℃/4h+420 ℃/4h+480 ℃/16h.
After the heat preservation is finished, cooling is performed by a strong wind and spraying mode.
Sawing the homogenized and annealed aluminum bar into 720mm short bars, performing ultrasonic flaw detection to be qualified, transferring into a gas furnace, heating to 490 ℃ in a stepped manner, and setting the heating temperature of the extrusion cylinder to 470 ℃.
The profile was then extruded at a speed of 5m/min with an extrusion ratio of 50, cooled with strong wind on-line.
And (3) finishing T73 artificial aging treatment by adopting a two-stage aging system of 105 ℃/5h and 155 ℃/10h to obtain the Al-Zn-Mg aluminum alloy.
Performance test:
tensile property test: the test is carried out according to the method of room temperature tensile test of GB/T228.1-2010 section 1 of tensile test of metallic materials, 200X 20 mm-sized bars are cut longitudinally along the section bar, CNC is adopted to process the bars into A50 tensile test pieces, the bars are stretched to fracture on a LEGEND 2382 universal tester, the strength value is read, the elongation after fracture is calculated, and the original gauge length is 50mm.
Stress corrosion resistance: and fixing a 100X 20mm sample by adopting a three-point bending tool in a pressure applying mode, and placing the sample in a LY-FH-120L composite alternating circulating salt spray testing machine. The inclination angle of the sample is 20+/-5 degrees, the concentration of sodium chloride salt water is 0.5wt.%, the test environment temperature is 25 ℃, the test is repeatedly circulated for 100 cycles, each cycle is respectively subjected to the condition test of spraying, introducing external air, wetting and drying, the sample is observed every 10 cycles, and the existence of cracking cracks on the surface of the sample is judged by adopting a visual inspection method. If cracks are observed on the surface of the sample, the depth of the cracks is recorded on the cut side, and a picture of the cracks is shown in fig. 1. Wherein (a) of fig. 1 is a low-power crack morphology of example 3, and (b) of fig. 1 is a cross-sectional high-power crack propagation diagram of example 3; FIG. 1 (c) shows the low-power crack morphology of comparative example 1, and FIG. 1 (d) shows the cross-sectional high-power crack propagation diagram of comparative example 1;
FIG. 1 (e) shows the low-power crack morphology of comparative example 3, and FIG. 1 (f) shows the cross-sectional high-power crack propagation map of comparative example 3; FIG. 1 (g) shows the low-power crack morphology of comparative example 4, and FIG. 1 (h) shows the cross-sectional high-power crack propagation diagram of comparative example 4.
Table 1 shows the results of the tensile properties at room temperature and the stress corrosion resistance.
TABLE 1
The foregoing is merely exemplary embodiments of the present invention and are not intended to limit the scope of the present invention, and all equivalent modifications made by the present invention or direct or indirect application in the relevant art are intended to be included in the scope of the present invention.
Claims (5)
1. An Al-Zn-Mg aluminum alloy characterized in that: the composite material comprises the following components in percentage by mass:
Zn：6.75%-7.15%,Mg：1.67%-1.81%,Cu：0.25%-0.33%,Mn：0.37%-0.43%,Cr≤0.15%,Zr≤0.20%,Ti≤0.10%,Si≤0.20%,Fe≤0.2%,Al：85.45%-91.80%, The total amount of other elements is less than or equal to 0.15 percent; the sum of the mass percentages of the elements is 100 percent;
The preparation of the Al-Zn-Mg aluminum alloy comprises the following steps:
Mixing the components, smelting, casting, three-stage homogenization treatment, extrusion, online quenching and cooling and artificial aging treatment to obtain the Al-Zn-Mg aluminum alloy;
wherein the three-stage homogenization treatment comprises: the first-stage homogenizing annealing temperature is 350 ℃ and the time is 4 hours; the second-stage homogenizing annealing temperature is 420 ℃, the time is 4 hours, and the third-stage homogenizing annealing temperature is 480 ℃ and the time is 16 hours;
The temperature rising rate of each stage is controlled to be 40-50 ℃/h, and strong wind and spray cooling are adopted after the third stage treatment and heat preservation are finished;
The online quenching cooling process comprises the following steps: strong wind cooling, strong wind plus water mist cooling or water spray cooling;
the artificial aging treatment is as follows: and a two-stage aging process is adopted, wherein the first-stage aging temperature is 105 ℃, the time is 5 hours, and the second-stage aging temperature is 155 ℃ and the time is 10 hours.
2. An Al-Zn-Mg aluminum alloy according to claim 1, wherein: when the mass percentage of Cr is as follows: 0.05% -0.10%, wherein the mass percentage of Zr is as follows: 0.10% -0.15%.
3. An Al-Zn-Mg aluminum alloy according to claim 1, wherein: the mass percentage of Si is less than or equal to 0.15 percent, and the mass percentage of Fe is less than or equal to 0.15 percent.
4. An Al-Zn-Mg aluminum alloy according to claim 1, wherein: the Ti comprises the following components in percentage by mass: 0.02% -0.10%.
5. Use of the Al-Zn-Mg aluminum alloy of any one of claims 1 to 4 in automotive manufacturing.
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