CN114277325B - Heat treatment process for improving age hardening capacity of Al-Mg-Si-Zn aluminum alloy or composite material thereof - Google Patents
Heat treatment process for improving age hardening capacity of Al-Mg-Si-Zn aluminum alloy or composite material thereof Download PDFInfo
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Abstract
The invention discloses a heat treatment process for improving the age hardening capacity of an Al-Mg-Si-Zn aluminum alloy or a composite material thereof, belonging to the technical field of heat treatment of aluminum alloys and metal matrix composite materials. The heat treatment process comprises the following steps: solution quenchingAnd then, sequentially carrying out high-temperature artificial aging and low-temperature artificial aging treatment on the aluminum alloy or the composite material thereof. In high temperature artificial ageing, mg 2 Si phase and transition phase thereof, and improves the strength and hardness of Al-Mg-Si-Zn series aluminum alloy or composite material thereof. In the low-temperature artificial aging, the Zn element drives the Mg and Si elements to be continuously precipitated, so that the hardening response of the Al-Mg-Si-Zn aluminum alloy or the composite material thereof is further improved. The heat treatment process further excavates the age hardening capacity of the Al-Mg-Si-Zn aluminum alloy or the composite material thereof, and solves the problem that the age hardening capacity of the aluminum alloy or the composite material thereof is insufficient.
Description
Technical Field
The invention relates to the technical field of heat treatment of aluminum alloy and metal matrix composite materials, in particular to a heat treatment process for improving the age hardening capacity of Al-Mg-Si-Zn aluminum alloy or composite materials thereof.
Background
Al-Mg-Si series (6000 series) aluminum alloys have the characteristics of good corrosion resistance, excellent formability and the like. The Al-Mg-Si aluminum alloy is added with a reinforcing phase (such as a ceramic phase, nano carbon and the like) to prepare the aluminum-based composite material, and the strength, the elastic modulus and the fatigue resistance can be further improved. In recent years, novel Al-Mg-Si series aluminum alloys with different grades and composite materials thereof are widely applied to the fields of transportation, aerospace and the like.
In order to further improve the mechanical property, the component regulation and control of Al-Mg-Si series aluminum alloy is always concerned. Among them, diversification of alloy elements is a key point of development in recent ten years. By adding alloy elements such as Cu, ag, zn and the like into the Al-Mg-Si series aluminum alloy, precipitation of a precipitation phase can be promoted during artificial aging, the types of the precipitation phase are enriched, and the strength of the alloy is further improved. Based on the above, quaternary aluminum alloys such as Al-Mg-Si-Cu series, al-Mg-Si-Zn series, al-Mg-Si-Ag series, and the like, and even quinary aluminum alloys such as Al-Mg-Si-Cu-Ag series, al-Mg-Si-Cu-Zn series, and the like have been developed. Among many alloy elements, zn is widely concerned because it accelerates the precipitation of a precipitation phase during artificial aging, thereby rapidly improving the strength and hardness of an alloy through artificial aging in a short time, and thus making the hardening response of the alloy rapid.
Since the amount of Zn added to an Al-Mg-Si aluminum alloy or a composite material thereof is usually small (generally not higher than 3% by mass), the addition of Zn hardly increases the hardness in the naturally aged state. Therefore, the Al-Mg-Si-Zn aluminum alloy or the composite material thereof still has excellent formability in a natural aging state, and can better meet the application strategies of room-temperature plastic deformation processing and service after artificial aging in the natural aging state. Based on the method, the aluminum alloy or aluminum-based composite material can be directly subjected to artificial aging after quenching and then used, can also be stored, transported and subjected to room-temperature plastic deformation processing in a natural aging state after quenching, and then is subjected to artificial aging to improve the strength and the hardness, so that the service use conditions are met.
However, zn does not significantly improve The hardness and strength of Al-Mg-Si based aluminum alloy after artificial aging under The single-stage artificial aging process used in conventional Al-Mg-Si based aluminum alloys, as in The literature "The effect of Zn on The aluminum grading response in an Al-Mg-Si alloy, materials and Design,2015;65, 1229-1235", it was reported that the addition of 3.0wt.% (mass fraction) of Zn to an Al-0.99Mg-0.54Si (mass fraction) alloy does not significantly increase the peak hardness although the early hardening rate of artificial aging is increased. This is because the main precipitated phase in the Al-Mg-Si aluminum alloy is Mg 2 Si phase and transition phase thereof, these precipitated phases being formed at 160 to 190 ℃. In this temperature range, zn is highly soluble in the Al matrix and therefore rarely precipitates. Lowering the artificial aging temperature can lower the solid solubility of Zn, thus promoting Zn precipitation, but is not beneficial to Mg 2 And Si and a transition phase thereof are formed, so that the traditional artificial aging process is difficult to combine the formation of two types of precipitated phases, and the strength and the hardness after artificial aging are not improved after Zn is added.
If the traditional artificial aging process can be improved, the Zn element which is dissolved in the aluminum matrix is precipitated to form a precipitate phase, the function of the Zn element can be fully exerted, and the strength and the hardness of the Al-Mg-Si-Zn series aluminum alloy or the composite material thereof are improved, thereby widening the application range of the alloy and the composite material. However, there is no report on such techniques.
Disclosure of Invention
Aiming at the defect that the traditional artificial aging cannot take account of two precipitated phases, the invention provides a heat treatment process for improving the age hardening capacity of Al-Mg-Si-Zn aluminum alloy or composite material thereof. The heat treatment process is simple in procedure and convenient and fast to operate, and can further improve the strength and hardness of the Al-Mg-Si-Zn aluminum alloy and the composite material thereof after artificial aging on the basis of the traditional single-stage aging.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
a heat treatment process for improving the age hardening capacity of Al-Mg-Si-Zn aluminum alloy or composite material thereof comprises the steps of carrying out solution treatment on the Al-Mg-Si-Zn aluminum alloy or Al-Mg-Si-Zn aluminum matrix composite material, quenching the Al-Mg-Si-Zn aluminum alloy or Al-Mg-Si-Zn aluminum matrix composite material to room temperature, carrying out high-temperature artificial aging at 160-190 ℃, and then carrying out air cooling to the room temperature; and then the air-cooled material is artificially aged at a low temperature of between 110 and 130 ℃.
The Al-Mg-Si-Zn aluminum alloy comprises the following chemical components in percentage by mass: mg:0.3 to 1.8%, si:0.3 to 1.8%, zn:0.5 to 3.0 percent, and the balance of Al and inevitable impurities.
In the chemical components of the Al-Mg-Si-Zn aluminum alloy, the requirements of impurity elements are as follows: fe. Mn, ti and Cr should be such that the content of individual impurity elements is less than or equal to 0.5wt.%, and the total content of impurity elements is less than or equal to 0.8wt.%.
The Al-Mg-Si-Zn aluminum-based composite material is formed by adding a reinforcing phase into an Al-Mg-Si-Zn aluminum alloy matrix, wherein the reinforcing phase is a ceramic phase or a nano carbon material; when the reinforcing phase is a ceramic phase, the volume content of the ceramic phase is 10-40%, preferably 15-30%; when the reinforcing phase is a nano carbon material, the volume content of the nano carbon material is 0.5-10%, preferably 1-5%; the ceramic reinforcing phase is SiC or Al 2 O 3 、B 4 C. TiC or TiB 2 The nano carbon material is carbon nano tube or graphene.
In the process of the solution treatment, when the material is Al-Mg-Si-Zn aluminum alloy, the solution temperature is 530-560 ℃, and the heat preservation time is 20-60 min; when the material is Al-Mg-Si-Zn aluminum-based composite material, the solid solution temperature is 530-560 ℃, and the heat preservation time is 1.5-3 h.
The high-temperature artificial aging can be kept to be in an underaging state, a peak aging state or an overaging state at corresponding temperature according to actual requirements.
The heat preservation time of the low-temperature artificial aging is 24-96 h.
The natural aging can be carried out between the quenching treatment and the high-temperature artificial aging treatment according to the actual requirement, and the natural aging time is not limited.
The design mechanism of the invention is as follows:
the invention provides a novel heat treatment process for improving the artificial age hardening response of Al-Mg-Si-Zn aluminum alloy or a composite material thereof. The heat treatment process comprises the following steps: and after solution quenching or solution quenching and natural aging, sequentially carrying out high-temperature artificial aging and low-temperature artificial aging treatment on the aluminum alloy or the composite material thereof. In the course of high-temperature artificial aging, mg 2 Si phase and transition phase thereof are formed, and the strength and hardness of the Al-Mg-Si-Zn series aluminum alloy or the composite material thereof are improved (the first strengthening is realized). But the element Zn is in Mg 2 At the temperature of Si precipitation by aging, the solid solubility is high, and thus precipitation is difficult. In the process of low-temperature artificial aging in the second stage, the solid solubility of Zn is reduced, so that the precipitation driving force of Zn is increased, a precipitation phase rich in Zn is correspondingly formed, and the strength and the hardness of the Al-Mg-Si-Zn aluminum alloy or the composite material thereof are further improved.
The invention has the beneficial effects that:
1. the heat treatment process further excavates the hardening capacity of the Al-Mg-Si-Zn aluminum alloy or the composite material thereof on the basis of improving the traditional single-stage artificial aging process, and solves the problem that the Zn element in the aluminum alloy or the composite material thereof does not fully play a strengthening role. Compared with the traditional heat treatment process of solution quenching, natural aging and single-stage artificial aging, the Al-Mg-Si-Zn aluminum alloy and the composite material thereof subjected to heat treatment by the process have the advantages that the strength and the hardness are obviously improved after artificial aging.
2. The heat treatment process disclosed by the invention is simple in procedure and strong in operability, effectively widens the application of the aluminum alloy and the composite material, and is suitable for large-scale application in the actual production process.
Drawings
FIG. 1 shows the morphology of precipitated phases of a composite material according to example 1; wherein: (a) Edge of<001> Al Shooting an image of a crystal belt shaft; (b) Edge of<110> Al The ribbon axis takes an image.
Detailed Description
The present invention will be described in further detail with reference to specific examples, but the embodiments of the present invention are not limited to the scope of the examples. The examples are given solely for the purpose of illustration and are not intended to limit the scope of the invention.
Example 1
A composite material using an Al-Mg-Si-Zn aluminum alloy as a matrix is produced by a powder metallurgy method. The reinforcing phase is SiC particles with the volume fraction of 20% and the average particle size of 5 mu m. Except for SiC particles, the alloy element mix was 1.30wt.% Mg, 0.50wt.% Si, 1.30wt.% Zn, and the balance Al. The powder metallurgy produced ingots were hot extruded at 450 ℃ with an extrusion ratio of 15. Then solid dissolving for 2.5h at 535 +/-5 ℃ and water quenching to room temperature. Transferring the quenched sample to an aging furnace within 1min, and carrying out high-temperature artificial aging at 175 ℃ for 4 h. And taking out the sample for air cooling, and cooling the aging furnace to 125 ℃. After the temperature of the aging furnace is reduced to the temperature, the sample is put into the low-temperature artificial aging furnace for 40 hours at 125 ℃.
FIG. 1 shows the morphology of precipitated phases of the composite material after heat treatment in example 1. The precipitation phase in the Al-Mg-Si-Zn aluminum alloy is Mg under the existing single-stage artificial aging treatment 2 Si phase and transition phase thereof. These precipitated phases are all three equivalent [001 ]] Al A needle-like bar with an elongated direction (as indicated by the arrow in FIG. A, the black dot in the lower right corner is a precipitated phase cross section). When the incident direction of the electron beam is<110> Al In the process, all precipitated phases are strained into needle-like shapes forming a certain angle with each other, and black dot-like phases are not generated. However, many black dotted phases (indicated by arrows in the diagram (b)) are found in the diagram (b), which indicates that new precipitate phases are formed after the artificial aging process treatment of the high and low temperature steps according to the present invention, and the precipitate phases are judged to be the Zn-containing GP zones according to the morphology.
The sample after low temperature aging was subjected to the brinell hardness test, and the result was 145HB. The tensile test was performed on the samples after low temperature aging, and the results were: the tensile strength is 460MPa, the yield strength is 410MPa, and the elongation at break is 6.5%.
Comparative example 1
The composite material prepared in example 1 was subjected to solution quenching treatment in the same manner. Transferring the quenched sample to an aging furnace within 1min, and carrying out high-temperature artificial aging at 175 ℃ for 4 h. The sample after high temperature artificial aging is subjected to Brinell hardness test, and the result is 132HB. And (3) performing tensile test on the sample subjected to high-temperature artificial aging, wherein the result is as follows: the tensile strength is 430MPa, the yield strength is 380MPa, and the elongation at break is 7.5%. Hardness and tensile strength were lower than those in example 1.
Comparative example 2
The composite material prepared in example 1 was subjected to solution quenching treatment by the same process. Transferring the quenched sample to an aging furnace within 1min, and carrying out low-temperature artificial aging at 125 ℃ for 40 h. The sample after low-temperature artificial aging is subjected to Brinell hardness test, and the result is 138HB. And (3) performing a tensile test on the sample subjected to low-temperature artificial aging, wherein the result is as follows: the tensile strength is 460MPa, the yield strength is 370MPa, and the elongation at break is 8.0%. Although the hardness and tensile strength were close to those of example 1, the yield strength was significantly lower than those of example 1.
Comparative example 3
The same raw materials and powder metallurgy process as in example 1 were used to prepare a composite material. The hot extrusion and solution process was also the same as in example 1. The difference is that in this example, siC particles were removed, and the alloy element ratio was 1.30wt.% Mg content and 0.50wt.% Si content. Transferring the quenched sample to an aging furnace within 1min, and carrying out high-temperature artificial aging at 175 ℃ for 4 h. And taking out the sample for air cooling, and cooling the aging furnace to 125 ℃. After the temperature of the aging furnace is reduced to the temperature, the sample is put into the low-temperature artificial aging furnace for 40 hours at 125 ℃. The results of Brinell hardness tests on the samples after low-temperature aging are 133HB, which is lower than the results in example 1, but are close to the results in comparative example 1, and show that the improvement of the response of the high-temperature and low-temperature two-step artificial aging process to the aging hardening is mainly caused by the precipitation of Zn during low-temperature artificial aging.
Example 2
The composite material prepared in example 1 was subjected to solution quenching treatment in the same manner. The quenched sample is naturally aged for two weeks at room temperature, and then artificially aged at high temperature of 175 ℃ for 4 hours. And taking out the sample for air cooling, and cooling the aging furnace to 125 ℃. After the temperature of the aging furnace is reduced to the temperature, the sample is put into the low-temperature artificial aging furnace for 40 hours at 125 ℃. The sample after low temperature aging is subjected to tensile test, and the result is as follows: the tensile strength is 425MPa, the yield strength is 365MPa, and the elongation at break is 6.5 percent.
Comparative example 4
The composite material prepared in comparative example 3 was subjected to solution quenching treatment in the same process. The quenched sample is naturally aged at room temperature for two weeks, and then artificially aged at high temperature of 175 ℃ for 4 hours. And taking out the sample for air cooling, and cooling the aging furnace to 125 ℃. After the temperature of the aging furnace is reduced to the temperature, the sample is put into the low-temperature artificial aging furnace for 40 hours at 125 ℃. The tensile test was performed on the samples after low temperature aging, and the results were: the tensile strength is 400MPa, the yield strength is 345MPa, and the breaking elongation is 8.0 percent. The tensile strength is lower than that of the example 2, which shows that the Zn element still can show better strengthening effect under the high-temperature and low-temperature two-step ageing treatment even if the natural ageing is carried out before the artificial ageing.
Example 3
Al-Mg-Si-Zn alloy is prepared by a casting method, and the alloy element mixture ratio is that the Mg content is 0.9wt%, the Si content is 0.75wt%, and the Zn content is 2.0wt%. The ingot was hot forged at 450 ℃ at a forging ratio of 10. Then stress annealing is carried out for 2h at 480 ℃. And (3) carrying out solid solution on the annealed forged cake at 550 +/-5 ℃ for 0.5h and carrying out water quenching to room temperature. Transferring the quenched sample to an aging furnace within 1min, and carrying out high-temperature artificial aging at 170 ℃ for 10 h. And taking out the sample for air cooling, and cooling the aging furnace to 120 ℃. After the temperature of the aging furnace is reduced to the temperature, the sample is put into the low-temperature artificial aging furnace for 60 hours at the temperature of 120 ℃. The sample after low temperature aging is subjected to tensile test, and the result is as follows: the tensile strength is 344MPa, the yield strength is 280MPa, and the elongation at break is 18%.
Comparative example 5
The Al-Mg-Si-Zn alloy forged cake prepared in example 3 was subjected to solution quenching treatment by the same procedure. Transferring the quenched sample to an aging furnace within 1min, and carrying out single-stage artificial aging at 170 ℃ for 10 h. The aged sample was subjected to a tensile test, and the results were: tensile strength of 310MPa, yield strength of 255MPa and elongation at break of 18 percent. The strength is lower than in example 3.
Example 4
Al-Mg-Si-Zn alloy is prepared by a casting method, and the alloy element mixture ratio is that the Mg content is 0.8wt%, the Si content is 1.1wt%, and the Zn content is 1.5wt%. The billet was hot extruded at 450 ℃ with an extrusion ratio of 16. The extruded bar is subjected to solid solution for 0.5h at 550 +/-5 ℃ and water quenching to room temperature. Naturally aging the quenched extrusion rod for 10 days at room temperature, and then artificially aging at the high temperature of 170 ℃ for 20 hours. And taking out the sample for air cooling, and cooling the aging furnace to 125 ℃. After the temperature of the aging furnace is reduced to the temperature, the sample is put into the low temperature artificial aging furnace for 80 hours at 125 ℃. The sample after low temperature aging is subjected to tensile test, and the result is as follows: the tensile strength is 300MPa, the yield strength is 245MPa, and the elongation at break is 19 percent.
Example 5
The Al-Mg-Si-Zn extrusion rod prepared in example 4 was subjected to solution quenching and natural aging treatment in the same process. And carrying out single-stage artificial aging at 170 ℃ for 20h on the sample after natural aging. The aged sample was subjected to a tensile test, and the results were: the tensile strength is 270MPa, the yield strength is 210MPa, and the elongation at break is 20%. The intensity is lower than in example 4.
Claims (5)
1. A heat treatment process for improving the age hardening capacity of Al-Mg-Si-Zn aluminum alloy or a composite material thereof is characterized in that: the process comprises the steps of carrying out solid solution treatment on the Al-Mg-Si-Zn series aluminum alloy or the Al-Mg-Si-Zn series aluminum matrix composite material, quenching the Al-Mg-Si-Zn series aluminum alloy or the Al-Mg-Si-Zn series aluminum matrix composite material to room temperature, carrying out high-temperature artificial aging at 160 to 190 ℃, and then carrying out air cooling to room temperature; then, carrying out low-temperature artificial aging on the air-cooled material at 110-130 ℃;
in the solution treatment process, when the material is Al-Mg-Si-Zn aluminum alloy, the solution temperature is 530 to 560 ℃, and the heat preservation time is 20 to 60min; when the material is an Al-Mg-Si-Zn aluminum-based composite material, the solid solution temperature is 530 to 560 ℃, and the heat preservation time is 1.5 to 3h;
the Al-Mg-Si-Zn aluminum alloy comprises the following chemical components in percentage by mass: mg:0.3 to 1.8%, si:0.3 to 1.8%, zn:0.5 to 3.0 percent, and the balance of Al and inevitable impurities;
the Al-Mg-Si-Zn aluminum-based composite material is formed by adding a reinforcing phase into an Al-Mg-Si-Zn aluminum alloy matrix, wherein the reinforcing phase is a ceramic phase or a nano carbon material; when the reinforcing phase is a ceramic phase, the volume content of the ceramic phase is 10 to 40 percent; when the reinforcing phase is a nano carbon material, the volume content of the nano carbon material is 0.5 to 10 percent; the ceramic reinforcing phase is SiC or Al 2 O 3 、B 4 C. TiC or TiB 2 The nano carbon material is carbon nano tube or graphene.
2. The heat treatment process for improving the age hardening ability of an Al-Mg-Si-Zn based aluminum alloy or a composite material thereof according to claim 1, wherein: in the chemical components of the Al-Mg-Si-Zn aluminum alloy, the requirements of impurity elements are as follows: fe. Mn, ti and Cr should be such that the content of individual impurity elements is less than or equal to 0.5wt.%, and the total content of impurity elements is less than or equal to 0.8wt.%.
3. The heat treatment process for improving the age hardening ability of an Al-Mg-Si-Zn aluminum alloy or a composite material thereof according to claim 1, wherein: the high-temperature artificial aging is under-aging, peak aging or over-aging state when the temperature is kept to the corresponding temperature.
4. The heat treatment process for improving the age hardening ability of an Al-Mg-Si-Zn based aluminum alloy or a composite material thereof according to claim 1, wherein: the heat preservation time of the low-temperature artificial aging is 24 to 96h.
5. The heat treatment process for improving the age hardening ability of an Al-Mg-Si-Zn based aluminum alloy or a composite material thereof according to claim 1, wherein: natural aging is carried out between quenching treatment and high-temperature artificial aging treatment, and the natural aging time is not limited.
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