CN110983131B - 7-series aluminum alloy section and manufacturing method thereof - Google Patents
7-series aluminum alloy section and manufacturing method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- 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
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Abstract
The invention belongs to the technical field of aluminum alloy production and manufacturing, and relates to a 7-series aluminum alloy section and a manufacturing method thereof, wherein the 7-series aluminum alloy section is prepared from the following element components in percentage by weight: si is less than or equal to 0.5 percent, Fe is less than or equal to 0.5 percent, Cu: 1.0-3.0%, Mn is less than or equal to 0.3%, Mg: 1.5-4.5%, Cr is less than or equal to 0.3%, Zn: 7.0-12.0%, Zr: 0.05-0.3%, Ti: 0.005-0.5%, the content of other single impurities is less than or equal to 0.05%, the total content of the impurities is less than or equal to 0.15%, and the balance is Al, the preparation method can directly carry out artificial aging without an off-line solid solution process, the product performance can also meet the requirement, 7-series aluminum alloy structural section bars with excellent strength and extensibility can be produced, the efficiency is improved, and the production cost is reduced.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy production and manufacturing, relates to a 7-series aluminum alloy section and a manufacturing method thereof, and particularly relates to an Al-Zn-Mg-Cu aluminum alloy section and a manufacturing method thereof.
Background
The specific gravity of the aluminum alloy is lower than that of a steel material, and the 7-series aluminum alloy has the characteristics of high strength and good heat resistance, and is widely used as structural materials of airplanes, spacecrafts and vehicles. With the wide adoption of the dual-channel airplane, the requirement on the integral processing performance of the airplane is higher and higher, and the aviation structural part is gradually developed towards thick sections and even ultra-thick sections. The 7-series (Al-Zn-Mg-Cu series) aluminum alloy is widely applied to aviation structural parts due to high strength, and thick sectional material products of the 7-series (Al-Zn-Mg-Cu series) aluminum alloy have high requirements on the performances such as fracture toughness, fatigue property, corrosion resistance and the like, particularly the uniformity of the performances in the thickness direction of the sectional material.
However, in order to satisfy the demand for increasing the strength of 7-series aluminum alloys, increasing the strength using conventional production methods causes a problem of reduction in ductility. Low ductility is disadvantageous as a structural material, but if ductility is improved, strength is generally reduced. Therefore, with the conventional production method, it is difficult to produce a 7-series aluminum alloy profile having both high strength and high ductility.
In view of the above, the present invention provides an Al-Zn-Mg-Cu structural aluminum alloy profile having excellent strength and excellent ductility and smaller in-plane anisotropy, and a method for manufacturing the same.
Disclosure of Invention
In view of the above, the present invention provides a 7-series aluminum alloy profile and a manufacturing method thereof, in order to solve the problem that the high strength and the high ductility of the conventional 7-series aluminum alloy profile cannot be obtained at the same time, which affects the application range of the 7-series aluminum alloy profile.
In order to achieve the aim, the invention provides a 7-series aluminum alloy section which is prepared from the following element components in percentage by weight: si is less than or equal to 0.5 percent, Fe is less than or equal to 0.5 percent, Cu: 1.0-3.0%, Mn is less than or equal to 0.3%, Mg: 1.5-4.5%, Cr is less than or equal to 0.3%, Zn: 7.0-12.0%, Zr: 0.05-0.3%, Ti: 0.005-0.5%, the content of other single impurities is less than or equal to 0.05%, the total content of the impurities is less than or equal to 0.15%, and the balance is Al.
Further, the 7-series aluminum alloy section bar raw material is prepared from the following element components in percentage by weight: si is less than or equal to 0.4 percent, Fe is less than or equal to 0.35 percent, Cu: 1.0-2.5%, Mn is less than or equal to 0.2%, Mg: 1.5-3.5%, Cr is less than or equal to 0.2%, Zn: 8.0-11.0%, Zr: 0.05-0.2%, Ti: 0.005-0.35 percent, less than or equal to 0.05 percent of other single impurities, less than or equal to 0.15 percent of impurities in total, and the balance of Al.
A manufacturing method of a 7-series aluminum alloy profile comprises the following steps:
A. calculating the using amount of each aluminum alloy raw material, preparing the aluminum alloy raw materials according to the proportion, adding the prepared aluminum alloy raw materials into a smelting furnace, uniformly mixing, smelting to obtain liquid aluminum alloy, casting the liquid aluminum alloy to obtain an aluminum alloy ingot, wherein the diameter range of the aluminum alloy ingot is 358-436 mm;
B. b, carrying out solid solution treatment on the aluminum alloy ingot prepared in the step A, wherein the temperature of the solid solution treatment is 400-480 ℃, and the time of the solid solution heat preservation is 1-10 h;
C. b, placing the aluminum alloy ingot subjected to the solution treatment in the step B into an extruder for extrusion, wherein the temperature of an extrusion cylinder is controlled to be 450-500 ℃, the temperature of an extrusion die is 500-520 ℃, the heating temperature of the aluminum alloy ingot is 380-420 ℃, and the extrusion speed of the aluminum alloy ingot is controlled to be 1.5-2.5 m/min, so that the required aluminum alloy section is obtained;
D. c, performing water quenching on the aluminum alloy section extruded in the step C within 1min in an extremely cold mode to cool the aluminum alloy section to below 90 ℃, wherein the cooling speed of the aluminum alloy section is 500-550 ℃/min, so that magnesium and silicon atoms are fully dissolved;
E. and D, carrying out artificial aging heat treatment on the aluminum alloy section cooled in the step D, wherein the aging temperature is 80-180 ℃, and the aging time is 5-30 h, so as to obtain the aluminum alloy section with excellent comprehensive performance.
Further, the temperature of the solution treatment in the step B is 420-480 ℃, and the solution heat preservation time is 1.5-8 h.
Further, step D cools the extruded aluminum alloy profile 50s to below 80 ℃ in an extremely cold manner.
And furthermore, the artificial aging temperature of the step E is 100-180 ℃, and the aging time is 8-28 h.
The invention has the beneficial effects that:
1. in the 7-series aluminum alloy section disclosed by the invention, Zn plays a role in increasing the strength of the aluminum alloy. When the Zn content in the aluminum alloy is less than 7.0%, the effect of improving the strength of the aluminum alloy cannot be obtained. Also, when the Zn content exceeds 12.0%, Zn-Mg-based crystalline products and precipitates are formed, resulting in a decrease in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Zn content is 7.0% to 12.0%. Further, the Zn content is preferably 8.0% to 11.0%.
Mg plays a role in increasing the strength of the aluminum alloy. When the Mg content in the aluminum alloy is less than 1.5%, the effect of improving the strength of the aluminum alloy cannot be obtained. Further, when the Mg content exceeds 4.5%, Zn-Mg-based and Al-Mg-Cu-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Mg content is 1.5% to 4.5%. Further, the Mg content is preferably 1.5% to 3.5%.
Cu acts to increase the strength of the aluminum alloy. When the Cu content in the aluminum alloy is less than 1.0%, the effect of improving the strength of the aluminum alloy cannot be obtained. Also, when the Cu content exceeds 3.0%, Al-Cu-based and Al-Mg-Cu-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Cu content is 1.0 to 3.0%. Further, the Cu content is preferably 1.0% to 2.5%.
Zr acts to inhibit recrystallization in the aluminum alloy and increase the strength of the aluminum alloy during solution treatment. When the Zr content in the aluminum alloy is less than 0.05%, recrystallization in the aluminum alloy cannot be suppressed, and therefore, the effect of improving the strength of the aluminum alloy cannot be obtained. Also, when the Zr content exceeds 0.30%, Al-Zr-based crystalline products and precipitates are formed, resulting in a decrease in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Zr content is 0.05% to 0.30%. Further, the Zr content is preferably 0.05% to 0.20%.
Ti is a component contained in the refining agent, and is added to refine crystal grains of the ingot. When the Ti content in the aluminum alloy exceeds 0.5%, Al — Ti-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Also, when the Ti content is less than 0.005%, a sufficient ingot grain refinement effect cannot be obtained. Therefore, in the structural aluminum alloy profile of the present embodiment, the Ti content is 0.005% to 0.5%. The Ti content is preferably 0.35% or less.
Si reduces the ductility of the aluminum alloy. When the Si content in the aluminum alloy exceeds 0.5%, Al-Fe-Si-based and Si-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Si content is limited to 0.5% or less. The Si content is preferably 0.4% or less.
Fe reduces the ductility of the aluminum alloy. When the Fe content in the aluminum alloy exceeds 0.5%, Al-Fe-Si-based and Al-Fe-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Fe content is limited to 0.5% or less. The Fe content is preferably 0.35% or less.
Mn reduces the ductility of the aluminum alloy. When the Mn content in the aluminum alloy exceeds 0.3%, Al-Mn-based and Al-Fe-Si-Mn-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Mn content is limited to 0.3% or less. The Mn content is preferably 0.2% or less.
Cr reduces the ductility of the aluminum alloy. When the Cr content in the aluminum alloy exceeds 0.3%, Al — Cr-based crystalline products and precipitates are formed, resulting in a reduction in ductility of the aluminum alloy. Therefore, in the structural aluminum alloy profile of the present embodiment, the Cr content is limited to 0.3% or less. The Cr content is preferably 0.2% or less.
2. According to the manufacturing method of the 7-series aluminum alloy section, the temperature of the solution treatment is lower than 400 ℃, the material cannot be fully dissolved, so that the strength and the ductility of the aluminum alloy cannot be fully obtained; if the temperature exceeds 480 ℃, which means that the temperature exceeds the solidus temperature of the material, partial melting occurs. Therefore, in the production method of the present embodiment, the temperature of the solution treatment is specified to be in the range of 400 ℃ to 480 ℃. In order to further improve the strength and ductility of the resulting structural aluminum alloy profile, the temperature of the solution treatment is preferably specified in the range of 420 ℃ to 480 ℃.
In the solution treatment, if the treatment time is less than 1 hour, the material cannot be sufficiently dissolved, and thus the strength and ductility of the aluminum alloy cannot be sufficiently obtained. In addition, in the solution treatment, if the treatment time exceeds 10 hours, recrystallization occurs in the metal structure of the material. The in-plane anisotropy of the aluminum alloy is large, and therefore, the desired strength of the aluminum alloy cannot be obtained. Therefore, in the production method of the present embodiment, the solution treatment time is specified in the range of 1 hour to 10 hours. In order to further improve the strength and ductility of the resulting structural aluminum alloy profile, the solution treatment time is preferably 1.5 hours to 8 hours.
And putting the extruded aluminum alloy section into water for rapid cooling. In quenching, unless the aluminum alloy profile is cooled to have a temperature of 90 ℃ or less in one minute, precipitation occurs during quenching. In this case, the dissolution cannot be sufficiently achieved, and the necessary strength and ductility of the aluminum alloy cannot be obtained. The main reasons are as follows: the 7-series aluminum alloy is low in quenching rate and can be precipitated, so that solute atoms in interstitial solid solution are separated out at first, the solid solution strengthening effect is reduced, and the subsequent performance is improved less. In addition, compared with the nanoscale second phase precipitated by aging, the second phase precipitated first is a micron-scale phase, which can reduce the dispersion strengthening effect of the alloy elements. 7 series aluminum alloy aging precipitation phase sequence: supersaturated solid solution-GP zone- η' (MgZn2) - η (MgZn 2). After the peak value aging treatment is adopted, a large number of fine coherent/semi-coherent GP zones and eta' phases are separated out from the crystal, and the strength of the alloy is highest.
To further improve the strength and ductility of the resulting structural aluminum alloy sections, it is more preferred to cool the material to a temperature of 80 ℃ or less within 50 seconds.
The temperature of the artificial aging treatment is lower than 80 c, precipitation does not occur, and therefore, the effect of improving the strength of the aluminum alloy by enhanced precipitation cannot be obtained. Further, if the temperature of the artificial aging treatment exceeds 180 ℃, coarse precipitates are formed, and therefore, the effect of improving the strength of the aluminum alloy by strengthening the precipitation cannot be obtained. Therefore, in the manufacturing method of the present embodiment, the temperature of the artificial aging treatment is specified to be in the range of 80 ℃ to 180 ℃. Furthermore, in order to further improve the strength of the resulting structural aluminium alloy section, it is preferred that the temperature of the artificial ageing treatment is in the range of 100 ℃ to 180 ℃.
If the artificial aging treatment time is less than 5 hours, precipitation does not sufficiently occur, and therefore, the effect of improving the strength of the aluminum alloy by strengthening the precipitation cannot be obtained. Further, if the artificial aging treatment time exceeds 30 hours, coarse precipitates are generated, and therefore the effect of improving the strength of the aluminum alloy cannot be obtained. Therefore, in the production method of the present embodiment, the artificial aging treatment time is specified in the range of 5 to 30 hours. In addition, in order to further improve the strength of the structural aluminum alloy profile obtained, the artificial aging treatment time is preferably 8 to 28 hours.
3. The manufacturing method of the 7-series aluminum alloy section disclosed by the invention can be used for producing the 7-series aluminum alloy structural section with excellent strength and extension, can be used for directly carrying out artificial aging without an off-line solid solution process, and can also meet the requirements on product performance, thereby improving the efficiency and reducing the production cost.
Additional advantages, objects, and features of the invention will be set forth in part in the description which follows and in part will become apparent to those having ordinary skill in the art upon examination of the following or may be learned from practice of the invention. The objectives and other advantages of the invention may be realized and attained by the means of the instrumentalities and combinations particularly pointed out hereinafter.
Detailed Description
The embodiments of the present invention are described below with reference to specific embodiments, and other advantages and effects of the present invention will be easily understood by those skilled in the art from the disclosure of the present specification. The invention is capable of other and different embodiments and of being practiced or of being carried out in various ways, and its several details are capable of modification in various respects, all without departing from the spirit and scope of the present invention.
Example 1
A manufacturing method of a 7-series aluminum alloy profile comprises the following steps:
A. calculating the using amount of each aluminum alloy raw material and preparing the aluminum alloy raw material according to the mixture ratio, wherein the 7-series aluminum alloy raw material comprises the following elements in percentage by mass:
| element(s) | Si | Fe | Cu | Mn | Mg | Cr | Zn | Zr | Ti | Impurities | Al |
| Content (wt.) | 0.5 | 0.5 | 2.0 | 0.3 | 4.0 | 0.3 | 8.0 | 0.2 | 0.03 | 0.05 | Balance of |
Adding the prepared aluminum alloy raw material into a smelting furnace, uniformly mixing, smelting into liquid aluminum alloy, and casting the liquid aluminum alloy into an aluminum alloy ingot, wherein the aluminum alloy smelting process is a semi-continuous casting method of melting, stirring, slagging off, degassing and impurity removing, filtering and casting, and the diameter of the aluminum alloy ingot is 400 mm;
B. b, carrying out solid solution treatment on the aluminum alloy ingot prepared in the step A, wherein the temperature of the solid solution treatment is 450 ℃, and the solid solution heat preservation time is 6 hours;
C. b, placing the aluminum alloy ingot subjected to the solution treatment in the step B into an extruder for extrusion, wherein the temperature of an extrusion cylinder is controlled to be 450-500 ℃, the temperature of an extrusion die is 500-520 ℃, the heating temperature of the aluminum alloy ingot is 380-420 ℃, and the extrusion speed of the aluminum alloy ingot is controlled to be 1.5-2.5 m/min, so that the required aluminum alloy section is obtained;
D. c, performing water quenching on the aluminum alloy section extruded in the step C in 50s in an extremely cold mode to cool the aluminum alloy section to below 80 ℃, wherein the cooling speed of the aluminum alloy section is 540 ℃/min, so that magnesium and silicon atoms are fully dissolved;
E. and D, carrying out artificial aging heat treatment on the aluminum alloy section cooled in the step D, wherein the aging temperature is 120 ℃, and the aging time is 24h, so that the aluminum alloy section with excellent comprehensive performance is obtained.
Example 2
The difference between the embodiment 2 and the embodiment 1 is that the mass percent ratio of each element of the 7 series aluminum alloy raw material in the step A is as follows:
| element(s) | Si | Fe | Cu | Mn | Mg | Cr | Zn | Zr | Ti | Impurities | Al |
| Content (wt.) | 0.4 | 0.35 | 2.0 | 0.2 | 3.0 | 0.2 | 8.0 | 0.1 | 0.03 | 0.05 | Balance of |
Example 3
The difference between the example 3 and the example 2 is that the temperature of the solution treatment in the step B is 430 ℃ and the solution heat preservation time is 6 h.
Example 4
Example 4 differs from example 2 in that step D cools the extruded aluminum alloy profile 50s to below 50 ℃ in an extremely cold manner.
Comparative example 1
The difference between the comparative example 1 and the example 1 is that the mass percent ratio of each element of the 7 series aluminum alloy raw material in the step A is as follows:
| element(s) | Si | Fe | Cu | Mn | Mg | Cr | Zn | Zr | Ti | Impurities | Al |
| Content (wt.) | 0.55 | 0.35 | 1.5 | 0.25 | 4.0 | 0.3 | 8.0 | 0.15 | 0.03 | 0.05 | Balance of |
Comparative example 2
The difference between the comparative example 2 and the comparative example 1 is that the solution treatment temperature in the step B is 320 ℃, and the solution heat preservation time is 20 h.
Comparative example 3
The difference between the comparative example 3 and the comparative example 1 is that the solution treatment temperature in the step B is 500 ℃, and the solution heat preservation time is 4 h.
Comparative example 4
The difference between the comparative example 4 and the comparative example 1 is that the extruded aluminum alloy section in the step D is cooled to be below 80 ℃ by water quenching, and the cooling speed of the aluminum alloy section is 100 ℃/min.
Comparative example 5
Comparative example 5 differs from comparative example 1 in that step E has an ageing temperature of 60 ℃ and an ageing time of 32 h.
Comparative example 6
Comparative example 6 differs from comparative example 1 in that step E has an ageing temperature of 200 ℃ and an ageing time of 4 h.
Mechanical property tests are carried out on the 7-series aluminum alloy sections obtained in the examples 1 to 4 and the comparative examples 1 to 6, the mechanical properties of the aluminum alloy sections after extrusion, 24 hours after extrusion standing and artificial aging are respectively tested, and the test results are shown in a table I:
table one:
the table shows that after the section extruded by the conventional method in the comparative example is stored for 24 hours, the yield strength and tensile strength are basically reduced by 10-20 MPa, the 7-series aluminum alloy section prepared by the preparation method of the 7-series aluminum alloy section increases the processes of rapid water quenching and artificial aging, after the section is stored for 24 hours, the yield strength and tensile strength change is small, the yield strength, tensile strength and elongation after artificial aging are greatly improved, and the production requirements of customers are completely met.
Finally, the above embodiments are only intended to illustrate the technical solutions of the present invention and not to limit the present invention, and although the present invention has been described in detail with reference to the preferred embodiments, it will be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions, and all of them should be covered by the claims of the present invention.
Claims (5)
1. A manufacturing method of a 7-series aluminum alloy profile is characterized by comprising the following steps:
A. calculating the using amount of each aluminum alloy raw material, preparing the aluminum alloy raw materials according to the proportion, adding the prepared aluminum alloy raw materials into a smelting furnace, uniformly mixing, smelting to obtain liquid aluminum alloy, casting the liquid aluminum alloy to obtain an aluminum alloy ingot, wherein the diameter range of the aluminum alloy ingot is 358-436 mm, and each element component in the aluminum alloy raw materials is prepared according to the weight percentage: si is less than or equal to 0.5 percent, Fe is less than or equal to 0.5 percent, Cu: 1.0-3.0%, Mn is less than or equal to 0.3%, Mg: 1.5-4.5%, Cr is less than or equal to 0.3%, Zn: 7.0-12.0%, Zr: 0.05-0.3%, Ti: 0.005-0.5%, the content of other single impurities is less than or equal to 0.05%, the total content of the impurities is less than or equal to 0.15%, and the balance is Al;
B. b, carrying out solid solution treatment on the aluminum alloy ingot prepared in the step A, wherein the temperature of the solid solution treatment is 400-480 ℃, and the time of the solid solution heat preservation is 1-10 h;
C. b, placing the aluminum alloy ingot subjected to the solution treatment in the step B into an extruder for extrusion, wherein the temperature of an extrusion cylinder is controlled to be 450-500 ℃, the temperature of an extrusion die is 500-520 ℃, the heating temperature of the aluminum alloy ingot is 380-420 ℃, and the extrusion speed of the aluminum alloy ingot is controlled to be 1.5-2.5 m/min, so that the required aluminum alloy section is obtained;
D. c, quenching the aluminum alloy section extruded in the step C in a quenching mode within 1min and cooling the aluminum alloy section to be below 90 ℃, wherein the cooling speed of the aluminum alloy section is 500-550 ℃/min, so that magnesium and silicon atoms are fully dissolved;
E. and D, carrying out artificial aging heat treatment on the aluminum alloy section cooled in the step D, wherein the aging temperature is 80-180 ℃, and the aging time is 5-30 h, so as to obtain the aluminum alloy section with excellent comprehensive performance.
2. The method for manufacturing the 7-series aluminum alloy section bar according to claim 1, wherein the aluminum alloy raw material in the step A is prepared from the following element components in percentage by weight: si is less than or equal to 0.4 percent, Fe is less than or equal to 0.35 percent, Cu: 1.0-2.5%, Mn is less than or equal to 0.2%, Mg: 1.5-3.5%, Cr is less than or equal to 0.2%, Zn: 8.0-11.0%, Zr: 0.05-0.2%, Ti: 0.005-0.35 percent, less than or equal to 0.05 percent of other single impurities, less than or equal to 0.15 percent of impurities in total, and the balance of Al.
3. The method of manufacturing a 7-series aluminum alloy profile according to claim 1, wherein the temperature of the solution treatment in the step B is 420 to 480 ℃, and the solution heat preservation time is 1.5 to 8 hours.
4. The method of producing a 7-series aluminum alloy profile according to claim 1, wherein the step D is a step of rapidly cooling the extruded aluminum alloy profile to 80 ℃ or lower within 50 s.
5. The method for manufacturing a 7-series aluminum alloy profile according to claim 1, wherein the artificial aging temperature in the step E is 100 to 180 ℃, and the aging time is 8 to 28 hours.
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