CN113981281B - High-strength rapid aging aluminum alloy and preparation method thereof - Google Patents
High-strength rapid aging aluminum alloy and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a high-strength rapid aging aluminum alloy and a preparation method thereof, wherein the aluminum alloy is Mg 2 A 6XXX series aluminum alloy with Si content of 1.09-1.85 wt% and Mg element/Si element mass ratio not less than 1.91; the preparation method comprises the following steps: (1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot; (2) carrying out homogenization annealing; (3) hot rolling; (4) cold rolling; (5) and (6) annealing. The preparation method is simple, the finally prepared aluminum alloy has the characteristic of quick aging response, the mechanical property of the aluminum alloy can reach the peak value in a short time, and the peak aging time is 40-180 min; after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapid aging aluminum alloy is more than or equal to 265MPa, the tensile strength Rm is more than or equal to 307MPa, and the elongation percentage A after fracture 50 ≥5.5％。
Description
Technical Field
The invention belongs to the technical field of aluminum alloy, and relates to a high-strength rapid aging aluminum alloy and a preparation method thereof.
Background
The aluminum alloy is made of pure aluminum with some alloying elements added. The aluminum alloy material has the characteristics of light weight, excellent strength, good heat dissipation and the like. Particularly, with the development of new energy automobiles, the requirement for the lightweight of automobiles is increasingly increased, and the use of aluminum alloys which are high in strength, light, thin and easy to form to replace the original steel materials becomes an important market direction. Wherein the 6XXX series aluminum alloy takes magnesium and silicon as main alloy elements and Mg 2 The Si phase is an aluminum alloy of strengthening phase, belonging to heat treatment strengthening aluminum alloy. The alloy has excellent strength, high corrosion resistance and good processability after aging treatment, and is an aluminum alloy material widely applied at present.
However, Al-Mg-Si alloys require heat treatment for strengthening to the maximum alloy strength, depending on time, as compared with Al-Mn alloys and the like, and it generally takes 6 to 12 hours, or even longer, to treat the Al-Mg-Si alloys to the peak of aging. Based on this, it is desired to develop a high strength, rapidly aging aluminum alloy, thereby reducing the time and energy consumption for machining at the customer site.
Disclosure of Invention
The invention aims to solve the technical problem of low aging response speed of the aluminum alloy in the prior art, and provides a high-strength rapid aging aluminum alloy and a preparation method thereof. The aluminum alloy has high strength and rapid aging response characteristic, and the mechanical property of the aluminum alloy can reach a peak value in a short time.
In order to achieve the purpose, the invention adopts the following technical scheme:
a high-strength quickly aged Al alloy is Mg 2 1.09-1.85 wt% of Si and Mg (including Mg) 2 Mg element in Si) and Si element (including Mg) 2 Si element in Si) is not less than 1.91 in mass ratio.
In Al-Mg-Si alloys, Mg 2 Si content is a key index affecting the strength of aluminum alloys, when Mg 2 When the Si content is less than 1.09 wt%, the strength of the aluminum alloy is insufficient; when Mg 2 When the Si content is more than 1.85wt%, it is difficult to completely dissolve the Mg having a low melting point 2 After the Si crystal phase is subjected to a high-temperature solid solution process, the material is easy to over-fire to cause strength reduction, and the elongation is lower than 4%. For Mg 2 In the Si strengthening system, we found that the aluminum alloy has a rapid aging response characteristic after controlling the Mg element to be excessive within a certain range (the mass ratio of the Mg element to the Si element is not less than 1.91), because the excessive Mg element can cause Mg 2 The solid solubility of Si in aluminum matrix is reduced, and then Mg is more easily precipitated from supersaturated solid solution formed by high-temperature solid solution in the aging process 2 A Si precipitation strengthening phase. The high-strength quick aging aluminum alloy has high strength and quick aging response characteristic, and the mechanical property of the aluminum alloy can reach a peak value in a short time.
As a preferred technical scheme:
the high-strength rapid aging aluminum alloy and Mg in the high-strength rapid aging aluminum alloy 2 The area ratio of Si crystalline phase in the longitudinal section of the aluminum alloy is lower than 0.05 percent so as to ensure that Mg in the aluminum alloy material 2 The Si crystal phase does not generate serious overburning phenomenon when being Mg 2 When the area ratio of the Si crystal phase is more than 0.05%, the elongation after brazing of the material is lowered, and the yield and tensile properties are lowered; mg (magnesium) 2 The melting point of the Si crystalline phase is lower and is 570-579 ℃.
According to the high-strength quick aging aluminum alloy, the content of Mg in the high-strength quick aging aluminum alloy is not more than 1.5 wt%; when the content of the Mg element is higher than 1.5wt%, the Mg element in the alloy is easy to diffuse to the surface of the plate in a large amount in the high-temperature solid solution or other high-temperature treatment processes, and the Mg element on the surface of the plate is easy to oxidize to black in a high-temperature environment, so that the attractiveness of the plate is affected.
According to the high-strength quick aging aluminum alloy, the content of Mn element in the high-strength quick aging aluminum alloy is not more than 0.30 wt%; although Mn has an enhancing effect on the material performance, too much Mn results in massive Al 9 (MnFe) 3 The Si phase begins to appear and increase, and massive Al 9 (MnFe) 3 The Si phase does not change in form after homogenization, and since the phase belongs to a brittle phase during rolling, microcracks are easily generated, and the interface bonding with the matrix is poor, the elongation is reduced, and the aluminum product is easily cracked.
The high-strength rapid aging aluminum alloy also contains 0.40-0.60 wt% of Cu element; generally, a certain amount of Cu element is added into the aluminum alloy, so that the aluminum alloy has a certain solid solution strengthening effect, and in the system, the addition of the certain amount of Cu element is beneficial to further shortening the time of peak aging; in the 6XXX series alloys with Mg excess, reaching a certain amount of Cu element (i.e. Cu element content exceeding 0.40 wt%) was found to modify Mg during ageing 2 Aging precipitation sequence of Si precipitate phase, therebyThe aging strengthening time is further shortened; when the content of Cu element is more than 0.6 wt%, excessive Cu is easy to precipitate at the grain boundary, and the intergranular corrosion resistance of the material is seriously damaged.
According to the high-strength quick aging aluminum alloy, the peak aging time of the high-strength quick aging aluminum alloy is 40-180 min.
After the high-strength rapid aging aluminum alloy is subjected to solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapid aging aluminum alloy is more than or equal to 265MPa, the tensile strength Rm is more than or equal to 307MPa, and the elongation percentage A after fracture is higher than 50 ≥5.5％。
The invention provides a method for preparing the high-strength quick-aging aluminum alloy, which comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein a two-stage system is adopted in the homogenization process, the first stage is heat preservation for 2-6 h at 480-500 ℃, and the second stage is heat preservation for 4-8 h at 500-570 ℃;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 480-520 ℃, performing hot rolling treatment, and rolling to a target thickness to obtain a hot rolled plate;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill to a certain thickness to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (4) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet to obtain the high-strength quick-aging aluminum alloy.
Mg in the invention 2 The Si content is obtained by reasonably regulating and controlling components, and the system is an Mg excess system (the mass ratio of Mg element to Si element is not less than 1.91), and the Mg content is obtained by reasonably regulating and controlling the components 2 The Si content being controlled mainly by Si, Mg 2 Si wt% ═ Z x (24.31 x 2+28.09)/28.09, Z is the mass fraction of Si in the alloy; for Si excess systems, Mg 2 The Si content being controlled mainly by Mg, Mg 2 Si wt% ("S × (24.31 × 2+ 28.09)/48.62), wherein S is the mass fraction of Mg in the alloy.
As a preferred technical scheme:
the method for preparing the high-strength quick aging aluminum alloy comprises the following steps of (2), preserving heat for 6 hours at 480 ℃ in the first stage, and preserving heat for 6 hours at 550 ℃ in the second stage; the process parameters can ensure that Al in the ingot is cast 2 Cu and Mg 2 The Si crystal phase is more fully dissolved in the aluminum matrix, and the crystal grains do not grow obviously.
The method for preparing the high-strength rapid aging aluminum alloy has a certain thickness of 1-2 mm.
Has the advantages that:
(1) the high-strength rapid aging aluminum alloy has the rapid aging response characteristic, the mechanical property of the aluminum alloy can reach the peak value in a short time, the peak value strength can be reached after the heat preservation is carried out at 210 ℃ for about 40-180 min, and compared with the conventional aging time which needs more than 6 hours, the production efficiency of a client side is greatly improved;
(2) the high-strength rapid aging aluminum alloy has high strength, and after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapid aging aluminum alloy is more than or equal to 265MPa, the tensile strength Rm is more than or equal to 307MPa, and the elongation percentage A after fracture is higher than 50 ≥5.5％；
(3) The aluminum alloy provided by the invention has excellent corrosion resistance.
Detailed Description
The invention will be further illustrated with reference to specific embodiments. It should be understood that these examples are for illustrative purposes only and are not intended to limit the scope of the present invention. Further, it should be understood that various changes or modifications of the present invention may be made by those skilled in the art after reading the teaching of the present invention, and such equivalents may fall within the scope of the present invention as defined in the appended claims.
The concrete processes of the solution treatment and the aging treatment in the following examples and comparative examples are as follows: and cutting the annealed aluminum alloy into corresponding test standard sizes (the length is 240mm, the width is 20mm) along the longitudinal direction, carrying out solution treatment on the sample for 35min at 578 ℃, and then putting the aluminum alloy subjected to solution treatment into a muffle furnace at the temperature of 210 ℃ for carrying out aging treatment until the peak aging strength is reached (namely the time for the aging treatment is equal to the time for the peak aging treatment).
The following examples and comparative examples were tested for some of the parameters as follows:
Mg 2 the area ratio of the Si crystal phase in the longitudinal section of the aluminum alloy is as follows: the method comprises the steps of carrying out complete metallographic polishing on a longitudinal section of an aluminum alloy (the aluminum alloy is not subjected to solution treatment and aging treatment), putting the polished aluminum alloy into a Zeiss field emission scanning electron microscope, setting the magnification factor to be 500x, carrying out picture shooting on different parts of the aluminum alloy by using a back scattering scanning mode, and identifying Mg in a picture by adopting ZEN picture processing software 2 Si crystal phase, and calculating Mg in the region 2 The area of the Si crystal phase accounts for the total area of the region to obtain Mg 2 The area ratio of the Si crystal phase in the longitudinal section of the aluminum alloy.
Peak aging time: and (3) putting the aluminum alloy subjected to the solution treatment into a muffle furnace at the temperature of 210 ℃ for aging treatment, wherein the aging time (namely the aging heat preservation time) is respectively 20min, 40min, 80min, 120min, 180min, 240min, 300min and 360min, and performing tensile property tests on the aluminum alloys with different aging times, wherein the aging time corresponding to the aluminum alloy with the highest yield strength and tensile strength is the peak aging time.
Mechanical properties: according to GB/T228.1-2010 part 1 of the tensile test of metallic materials: the method disclosed in the Room temperature test method carries out mechanical property test on the aluminum alloy (the aluminum alloy is subjected to solution treatment and aging treatment), the test instrument is a ZWICK universal material tester, and the test indexes are specified yield strength Rp0.2, tensile strength Rm and elongation percentage A after fracture 50 。
Intercrystalline corrosion depth: the aluminum alloy (which is subjected to solution treatment and aging treatment) is subjected to an intercrystalline corrosion test by using ASTM G100-92(2015) standard, the experimental time of the sample is 24h, and then the intercrystalline corrosion depth of the aluminum alloy is observed by using an optical microscope.
Example 1
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.09 wt% and a mass ratio of Mg element to Si element of 2.05; wherein, the content of Mg element is 0.82 wt%, the content of Si element is 0.40 wt%, the content of Cu element is 0.55 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.01 percent;
the peak aging time of the high-strength rapid aging aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapidly aged aluminum alloy is 294MPa, the tensile strength Rm is 335MPa, and the elongation percentage A after fracture is 50 10% and the intergranular corrosion depth is 48 μm.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 480 ℃ for 2 hours, and the second stage is heat preservation at 500 ℃ for 4 hours;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 480 ℃, and then carrying out hot rolling treatment to obtain a hot rolled plate with the thickness of 4 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill until the total thickness is 1mm to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 300 ℃, and the annealing time is 5h, so as to obtain the high-strength rapid-aging aluminum alloy.
Comparative example 1
An aluminum alloy Mg 2 Si content of 1.09A 6XXX series aluminum alloy having a weight% ratio of Mg element to Si element of 0.86; wherein, the content of Mg element is 0.69 wt%, the content of Si element is 0.80 wt%, the content of Cu element is 0.55 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.02%; the peak aging time of the aluminum alloy is 180 min; after solution treatment and aging treatment, the yield strength Rp0.2 of the aluminum alloy is 298MPa, the tensile strength Rm is 340MPa, and the elongation percentage A after fracture is 50 6% and the intergranular corrosion depth was 63 μm.
The preparation method of the aluminum alloy basically comprises the following steps of example 1, and the difference is only in step (1).
The peak aging time of the aluminum alloy of comparative example 1 is much greater than that of example 1 compared to example 1 because the silicon content in comparative example 1 is much greater than that of example 1.
Comparative example 2
A method for producing an aluminum alloy, substantially as in example 1, except that the first-stage heat-retaining time in step (2) is 1 hour.
Mg in the prepared aluminum alloy 2 The area proportion of the Si crystal phase in the longitudinal section of the aluminum alloy is 0.33%; the peak aging time of the aluminum alloy is 40 min; after solution treatment and aging treatment, the yield strength Rp0.2 of the aluminum alloy is 230MPa, the tensile strength Rm is 251MPa, and the elongation percentage A after fracture is 50 3.8%, and the intergranular corrosion depth was 86 μm.
The aluminum alloy of comparative example 2 has a yield strength Rp0.2, a tensile strength Rm, and a post-fracture elongation A, as compared with example 1 50 Much lower than example 1 because of the reduced homogenizing annealing time of comparative example 2, resulting in more Mg remaining in the ingot 2 Si crystallized phase, resulting in over-firing.
Comparative example 3
A method of making an aluminium alloy substantially as described in example 1, except that the holding time in the second stage of step (2) is 2 hours.
Mg in the prepared aluminum alloy 2 Surface of Si crystal phase in longitudinal section of aluminum alloyThe volume ratio is 0.39%; the peak aging time of the aluminum alloy is 40 min; after solution treatment and aging treatment, the yield strength Rp0.2 of the aluminum alloy is 219MPa, the tensile strength Rm is 230MPa, and the elongation percentage A after fracture is 50 2.7%, and the intergranular corrosion depth was 103 μm.
The aluminum alloy of comparative example 3 has a yield strength Rp0.2, a tensile strength Rm, and a post-fracture elongation A, as compared with example 1 50 Much lower than example 1 because of the reduced homogenizing annealing time of comparative example 3, resulting in more Mg remaining in the ingot 2 Si crystallized phase, resulting in over-firing.
Comparative example 4
An aluminum alloy Mg 2 A 6XXX series aluminum alloy having an Si content of 0.90 wt% and a mass ratio of Mg element to Si element of 2.00; wherein, the content of Mg element is 0.66 wt%, the content of Si element is 0.33 wt%, the content of Cu element is 0.55 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.02%;
the peak aging time of the aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the aluminum alloy is 255MPa, the tensile strength Rm is 287MPa, and the elongation percentage A after fracture is 50 13% and the intergranular corrosion depth was 40 μm.
The preparation method of the aluminum alloy basically comprises the following steps of example 1, and the difference is only in step (1).
The yield strength Rp0.2 and the tensile strength Rm of the aluminum alloy of comparative example 4 are much lower than those of example 1 compared to example 1 because Mg in comparative example 4 2 The lower content of Si strengthening phase results in a decrease in the strength of the final material.
Comparative example 5
An aluminum alloy Mg 2 A 6XXX series aluminum alloy having an Si content of 2.04 wt% and a mass ratio of Mg element to Si element of 2.11; wherein, the content of Mg element is 1.58 wt%, the content of Si element is 0.75 wt%, the content of Cu element is 0.55 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.70%;
the peak aging time of the aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the aluminum alloy is 258MPa, the tensile strength Rm is 286MPa, and the elongation percentage A after fracture is 50 2.1%, and the intergranular corrosion depth was 300. mu.m.
The preparation method of the aluminum alloy basically comprises the following steps of example 1, and the difference is only in step (1).
The aluminum alloy of comparative example 5 has a yield strength Rp0.2, a tensile strength Rm, and an elongation after fracture A, compared to example 1 50 Much lower than example 1 because of the Mg in comparative example 5 2 The Si content far exceeds the maximum solid solubility, so that a large amount of crystalline phases cannot be dissolved into a matrix through a homogenization process, and an overburning phenomenon occurs during high-temperature solid solution at a later stage, so that the strength of a final material is reduced, the elongation is unqualified, and the intercrystalline corrosion is seriously deteriorated.
Example 2
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.22 wt% and a mass ratio of Mg element to Si element of 1.93; wherein, the content of Mg element is 0.87 wt%, the content of Si element is 0.45 wt%, the content of Cu element is 0.4 wt%, and the total mass of inevitable impurities is 0.47 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.03%;
the peak aging time of the high-strength rapid aging aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapid aging aluminum alloy is 299MPa, the tensile strength Rm is 330MPa, and the elongation percentage A after fracture is 50 The content was 11%, and the intergranular corrosion depth was 41 μm.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 490 ℃ for 6h, and the second stage is heat preservation at 530 ℃ for 6 h;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 500 ℃, and then carrying out hot rolling treatment to obtain a hot rolled plate with the thickness of 5 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill until the total thickness is 1.5mm to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 400 ℃, and the annealing time is 3h, so as to obtain the high-strength rapid-aging aluminum alloy.
Example 3
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.85wt% and a mass ratio of Mg element to Si element of 2.21; wherein, the content of Mg element is 1.5wt%, the content of Si element is 0.68 wt%, the content of Mn element is 0.3 wt%, the content of Cu element is 0.6 wt%, and the total mass of inevitable impurities is 0.42 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.05 percent;
the peak aging time of the high-strength rapid aging aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapidly aged aluminum alloy is 311MPa, the tensile strength Rm is 345MPa, and the elongation percentage A after fracture is 50 9% and the intergranular corrosion depth was 58 μm.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 500 ℃ for 4 hours, and the second stage is heat preservation at 570 ℃ for 8 hours;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 520 ℃, performing hot rolling treatment, and rolling to obtain a hot rolled plate with the thickness of 6 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill to obtain an aluminum alloy cold rolled plate, wherein the total thickness of the hot rolled plate is 2 mm;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 500 ℃, and the annealing time is 1h, so as to obtain the high-strength rapid-aging aluminum alloy.
Example 4
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.36 wt% and a mass ratio of Mg element to Si element of 2.42; wherein the content of Mg element is 1.21 wt%, the content of Si element is 0.50 wt%, the content of Mn element is 0.15 wt%, the content of Cu element is 0.46 wt%, and the total mass of inevitable impurities is 0.28 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.01 percent;
the peak aging time of the high-strength rapid aging aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapidly aged aluminum alloy is 307MPa, the tensile strength Rm is 355MPa, and the elongation percentage A after fracture is 50 12% and the intergranular corrosion depth is 46 μm.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 480 ℃ for 6h, and the second stage is heat preservation at 550 ℃ for 6 h;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot after milling to 490 ℃, and then carrying out hot rolling treatment to obtain a hot rolled plate with the thickness of 5 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill until the total thickness is 1mm to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 350 ℃, and the annealing time is 4h, so as to obtain the high-strength rapid-aging aluminum alloy.
Example 5
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.09 wt% and a mass ratio of Mg element to Si element of 2.05; wherein, the content of Mg element is 0.82 wt%, the content of Si element is 0.40 wt%, the content of Mn element is 0.5 wt%, the content of Cu element is 0.55 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.01 percent;
the peak aging time of the high-strength rapid aging aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapidly aged aluminum alloy is 213MPa, the tensile strength Rm is 255MPa, and the elongation percentage A after fracture is 50 5.5%, and the intergranular corrosion depth was 45 μm.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 480 ℃ for 2 hours, and the second stage is heat preservation at 500 ℃ for 4 hours;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 480 ℃, and then carrying out hot rolling treatment to obtain a hot rolled plate with the thickness of 4 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill until the total thickness is 1mm to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 300 ℃, and the annealing time is 5h, so as to obtain the high-strength rapid-aging aluminum alloy.
Example 6
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.09 wt% and a mass ratio of Mg element to Si element of 2.05; wherein, the content of Mg element is 0.82 wt%, the content of Si element is 0.40 wt%, the content of Cu element is 0.25 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.01 percent;
the peak aging time of the high-strength rapid aging aluminum alloy is 180 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapidly aged aluminum alloy is 265MPa, the tensile strength Rm is 307MPa, and the elongation percentage A after fracture is 50 12% and the intergranular corrosion depth was 36 μm.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 480 ℃ for 2 hours, and the second stage is heat preservation at 500 ℃ for 4 hours;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 480 ℃, and then carrying out hot rolling treatment to obtain a hot rolled plate with the thickness of 4 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill until the total thickness is 1mm to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 300 ℃, and the annealing time is 5h, so as to obtain the high-strength rapid-aging aluminum alloy.
Example 7
A high-strength quickly aged Al alloy is Mg 2 A 6XXX series aluminum alloy having an Si content of 1.09 wt% and a mass ratio of Mg element to Si element of 2.05; wherein, the content of Mg element is 0.82 wt%, the content of Si element is 0.40 wt%, the content of Cu element is 0.7 wt%, and the total mass of inevitable impurities is 0.35 wt%;
mg in high-strength quick aging aluminum alloy 2 The area percentage of the Si crystalline phase in the longitudinal section of the aluminum alloy is 0.01 percent;
the peak aging time of the high-strength rapid aging aluminum alloy is 40 min;
after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapidly aged aluminum alloy is 301MPa, the tensile strength Rm is 350MPa, and the elongation percentage A after fracture is 50 The content of the corrosion inhibitor is 7 percent, the intergranular corrosion depth is 280 mu m, and the material has poor corrosion resistance and can only be used in the field of high-strength aluminum alloy with low requirement on corrosion resistance.
The preparation method of the high-strength rapid aging aluminum alloy comprises the following specific steps:
(1) preparing materials according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein the homogenization process adopts a two-stage system, the first stage is heat preservation at 480 ℃ for 2 hours, and the second stage is heat preservation at 500 ℃ for 4 hours;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 480 ℃, and then carrying out hot rolling treatment to obtain a hot rolled plate with the thickness of 4 mm;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill until the total thickness is 1mm to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (3) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet, wherein the annealing temperature is 300 ℃, and the annealing time is 5h, so as to obtain the high-strength rapid-aging aluminum alloy.
Claims (6)
1. High strength fast aging aluminum alloy, characterized by: is Mg 2 A 6XXX series aluminum alloy with Si content of 1.09-1.85 wt% and Mg element/Si element mass ratio not less than 1.91; mg in high-strength quick aging aluminum alloy 2 The area ratio of the Si crystalline phase in the longitudinal section of the aluminum alloy is lower than 0.05 percent; the peak aging time of the high-strength rapid aging aluminum alloy is 40-180 min; after solution treatment and aging treatment, the yield strength Rp0.2 of the high-strength rapid aging aluminum alloy is more than or equal to 265MPa, the tensile strength Rm is more than or equal to 307MPa, and the elongation percentage A after fracture 50 ≥5.5%。
2. The high strength rapidly aged aluminum alloy of claim 1, wherein the content of Mg element in the high strength rapidly aged aluminum alloy is not more than 1.5 wt.%.
3. The high strength rapidly aged aluminum alloy according to claim 1, wherein the content of Mn element in the high strength rapidly aged aluminum alloy is not more than 0.30 wt%.
4. The high strength rapidly aged aluminum alloy according to claim 1, wherein the high strength rapidly aged aluminum alloy further contains 0.40 to 0.60wt% of Cu element.
5. The method for preparing the high-strength rapidly aged aluminum alloy according to any one of claims 1 to 4, which comprises the following specific steps:
(1) burdening according to the element composition of the high-strength rapid aging aluminum alloy, and casting to obtain an ingot;
(2) carrying out homogenization annealing;
carrying out high-temperature homogenization treatment on the cast ingot, wherein a two-stage system is adopted in the homogenization process, the first stage is heat preservation for 2-6 h at 480-500 ℃, and the second stage is heat preservation for 4-8 h at 500-570 ℃;
(3) hot rolling;
cutting and milling the cast ingot subjected to high-temperature homogenization treatment, heating the cast ingot subjected to surface milling to 480-520 ℃, performing hot rolling treatment, and rolling to a target thickness to obtain a hot rolled plate;
(4) cold rolling;
cooling the hot rolled plate to room temperature, and rolling the hot rolled plate on a cold rolling mill to a certain thickness to obtain an aluminum alloy cold rolled plate;
(5) annealing;
and (4) carrying out complete annealing treatment on the aluminum alloy cold-rolled sheet to obtain the high-strength quick-aging aluminum alloy.
6. The method of claim 5, wherein in step (2), the first stage is at 480 ℃ for 6 hours and the second stage is at 550 ℃ for 6 hours.
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