CN112708811A - Aluminum alloy and preparation method and application thereof - Google Patents
Aluminum alloy and preparation method and application thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
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- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
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- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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- 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
- C22F1/047—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 magnesium as the next major constituent
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
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Abstract
The invention belongs to the technical field of alloys, and particularly relates to an aluminum alloy and a preparation method and application thereof. The aluminum alloy provided by the invention comprises the following elements in percentage by mass: 0.08 to 0.12 percent of Cu, 0.07 to 0.10 percent of Mn, 0.08 to 0.12 percent of Si, 0.15 to 0.20 percent of Mg, 0.02 to 0.06 percent of Li, 0.005 to 0.008 percent of Ti, and the balance of Al and inevitable impurities; li + Mn is more than or equal to 0.12 wt% and less than or equal to 0.15 wt%. The embodiment shows that the tensile strength of the aluminum alloy provided by the invention is 152-170 MPa; the extruded product after extrusion has smooth surface, no tearing and excellent extrusion performance, and can meet the requirements of the section bar for the thin-wall small cavity structure on tensile strength and extrusion performance.
Description
Technical Field
The invention belongs to the technical field of alloys, and particularly relates to an aluminum alloy and a preparation method and application thereof.
Background
Heat exchangers (also known as heat exchangers or heat exchange apparatus) are used to transfer heat from a fluid to a fluidAn apparatus for transferring heat from a hot fluid to a cold fluid to meet specified process requirements is an industrial application of convective and conductive heat transfer having a plurality of rectangular parallel channels. In order to improve the heat transfer effect, the rectangular parallel channels of the heat exchanger are smaller and smaller so as to increase the specific surface area and improve the heat dissipation area; meanwhile, the wall thickness of the aluminum alloy section of the heat exchanger is thinner and thinner. For example, the current heat exchanger has rectangular parallel channels with a minimum area of 2mm2The wall thickness is 0.5mm, and the thin-wall small-cavity structure puts higher and higher requirements on the extrudability of aluminum alloy used for the heat exchanger.
In the existing aluminum alloy, the 1000 series aluminum alloy has the advantages of high purity and easy extrusion because the strength is too low, but the basic strength requirement of the heat exchanger cannot be met; when 3000 series aluminum alloy is used for producing heat exchanger aluminum alloy sections with small rectangular cavities and thin walls, the shape resistance is large, and the aluminum alloy is very easy to adhere to an extrusion die working belt, so that the cavities are scraped and scraped, and a thin-wall heat exchanger with many and small heat dissipation channels is difficult to extrude, so that the problem that extrusion cannot be performed generally exists. The conventional aluminum alloy can not realize the production of a thin-wall small cavity structure on the basis of ensuring good strength and extrusion performance, and can not meet the production and use requirements of a heat exchanger.
Disclosure of Invention
In view of the above, the present invention provides an aluminum alloy and a preparation method thereof, and the aluminum alloy provided by the present invention has the characteristics of excellent extrusion performance and high tensile strength, and can meet the requirements of thin-wall small-cavity structures on strength and extrusion performance.
In order to achieve the purpose of the invention, the invention provides the following technical scheme:
the invention provides an aluminum alloy which comprises the following elements in percentage by mass:
0.08 to 0.12 percent of Cu, 0.07 to 0.10 percent of Mn, 0.08 to 0.12 percent of Si, 0.15 to 0.20 percent of Mg, 0.02 to 0.06 percent of Li, 0.005 to 0.008 percent of Ti, and the balance of Al and inevitable impurities;
0.12wt.％≤Li+Mn≤0.15wt.％。
preferably, the inevitable impurities comprise Fe and non-Fe impurities, wherein the mass percentage content of Fe is less than or equal to 0.08%, the content of a single element in the non-Fe impurities is less than or equal to 0.05%, and the total content of the non-Fe impurities is less than or equal to 0.15%.
Preferably, the tensile strength of the aluminum alloy is 150-170 MPa.
Preferably, the aluminum alloy is extruded under extrusion conditions: the limiting wall thickness is 0.5 mm; the limiting cross-sectional area of a single small cavity is 2mm when the small cavity profile is extruded2The number of the small cavities is 5-50.
The invention also provides a preparation method of the aluminum alloy in the technical scheme, which comprises the following steps:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot; the smelting comprises melting, refining, online grain refinement treatment and online degassing and filtering which are sequentially carried out;
and carrying out homogenization treatment, deformation treatment, quenching and aging treatment on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
Preferably, the melting temperature is 740 to 760 ℃;
the refining temperature is 730-780 ℃, and the refining time is 10-40 min;
the temperature of the grain refining treatment is 710-750 ℃;
the on-line degassing and filtering comprises degassing tank filtering, foamed ceramic filter plate filtering and tubular filter tank filtering which are sequentially carried out.
Preferably, the heat preservation temperature of the homogenization treatment is 520-540 ℃, and the heat preservation time is 4-8 h.
Preferably, the temperature of the deformation treatment is 450-500 ℃.
Preferably, the heat preservation temperature of the aging treatment is 200-210 ℃, and the heat preservation time is 1-3 h.
The invention also provides application of the aluminum alloy in the technical scheme or the aluminum alloy prepared by the preparation method in the technical scheme as a thin-wall small-cavity structural section in a heat exchanger.
The invention provides an aluminum alloy which comprises the following elements in percentage by mass: 0.08 to 0.12 percent of Cu, 0.07 to 0.10 percent of Mn, 0.08 to 0.12 percent of Si, 0.15 to 0.20 percent of Mg, 0.02 to 0.06 percent of Li, 0.005 to 0.008 percent of Ti, and the balance of Al and inevitable impurities; li + Mn is more than or equal to 0.12 wt% and less than or equal to 0.15 wt%.
In the present invention, Al provides a base alloying element; cu, Si and Mg have solid solution strengthening effect, and Mg can be precipitated from Si and Mg2Si strengthening phase for strengthening the strength of the aluminum alloy; mn and Li are microalloying elements, and Mn and Li can perform a phase change reaction Al + Mn → MnAl6And Al + Li → Al3Li, Al produced3Li and MnAl6Is a thermodynamically stable fine disperse phase, which is beneficial to inhibiting the recrystallization and grain growth of the aluminum alloy; the addition of Mn is beneficial to the spheroidization of hard particles containing inevitable impurities, promotes the spheroidization of needle-like Fe-containing phases, can eliminate the negative influence of Fe impurity elements and is beneficial to improving the extrusion processing performance of the alloy; ti is beneficial to refining the crystal grains of the cast ingot and improving the structural component uniformity of the aluminum alloy.
In addition, the invention controls Si, Mg and Cu in the corresponding content range, which is beneficial to ensuring the strength of the aluminum alloy, simultaneously avoids the large extrusion deformation resistance of the aluminum alloy, prevents the deterioration of the extrusion performance, can also reduce the potential difference between the grain boundary and the inside of the grain, and avoids the increase of stress corrosion and the corrosion sensitivity of the grain boundary; the content and the mutual content relation of Li and Mn are controlled, so that the aluminum alloy after extrusion is ensured to have a fine recrystallized structure with the grain grade above 5 grade, a coarse recrystallized structure is effectively prevented, or the size of intermetallic compounds is coarse, a mixed grain structure with the coexistence of the coarse recrystallized structure and fibrous crystal structure is formed, and the deterioration of the strength and the extrusion performance of the aluminum alloy is avoided; controlling Ti in a corresponding content range is beneficial to refining grains, preventing Ti-containing particles in the cast ingot from aggregating and growing, preventing the extruded product from having white line stripe defects and discontinuously scratching thin-walled regions so as to be difficult to continuously produce, preventing the cast ingot from having overlarge grains (more than 500 mu m) and uneven components and structures of the cast ingot, and avoiding the deterioration of the extrusion processing performance and the mechanical property of the aluminum alloy.
The test result of the embodiment shows that the tensile strength of the aluminum alloy provided by the invention is 152-170 MPa; the extruded product after extrusion has smooth surface, no tearing and excellent extrusion performance.
The invention also provides a preparation method of the aluminum alloy in the technical scheme, which comprises the following steps: smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot; the smelting comprises melting, refining, online grain refinement treatment and online degassing and filtering which are sequentially carried out; and carrying out homogenization treatment, deformation treatment, quenching and aging treatment on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy. The molten aluminum alloy is subjected to deep purification through refining, degassing and impurity removal and online degassing and filtering, so that the cleanliness of the molten aluminum alloy is greatly improved, impurities in the aluminum alloy are reduced, and the root of scratching and tearing of the aluminum alloy section during extrusion application is radically reduced; the homogenization treatment is favorable for eliminating macro-micro segregation of alloy elements in the ingot, so that the alloy elements and coarse compounds are fully dissolved in a solid manner, the spheroidization rate of impurity phases (Fe) is improved, and fine dispersoids are formed at the same time; the aging treatment is beneficial to separating out the strengthening phase in the aluminum alloy and improving the strength of the aluminum alloy.
Drawings
FIG. 1 is a flow chart of a method of making an aluminum alloy according to the present invention;
FIG. 2 is a metallographic image of an aluminum alloy according to example 1 of the present invention;
fig. 3 is a schematic view of a heat exchanger extruded profile.
Detailed Description
The invention provides an aluminum alloy which comprises the following elements in percentage by mass:
0.08 to 0.12 percent of Cu, 0.07 to 0.10 percent of Mn, 0.08 to 0.12 percent of Si, 0.15 to 0.20 percent of Mg, 0.02 to 0.06 percent of Li, 0.005 to 0.008 percent of Ti, and the balance of Al and inevitable impurities;
0.12wt.％≤Li+Mn≤0.15wt.％。
the aluminum alloy comprises, by mass, 0.08-0.12% of Cu, preferably 0.085-0.115%, and more preferably 0.09-0.11%. In the invention, Cu has the function of solid solution strengthening, which is beneficial to improving the strength of the aluminum alloy; the Cu is controlled within the content range, so that the strength of the aluminum alloy is favorably ensured, the large extrusion deformation resistance of the aluminum alloy is avoided, and the deterioration of the extrusion performance is prevented.
The aluminum alloy comprises 0.07-0.10% of Mn by mass percentage, preferably 0.075-0.095% and more preferably 0.08-0.09%. In the invention, Mn and Al form MnAl6 phase, and the addition of Mn is beneficial to spheroidizing Fe phase hard particles, can eliminate the negative influence of Fe impurity elements and is beneficial to improving the extrusion processing performance of the alloy; the Mn content is controlled to be 0.07-0.10 wt.%, so that the improvement of the plasticity, the weldability, the heat resistance and the corrosion resistance of the aluminum alloy is facilitated, meanwhile, the large extrusion deformation resistance is avoided, and the severe deterioration of the extrusion performance is prevented.
The aluminum alloy comprises, by mass, 0.08-0.12% of Si, preferably 0.085-0.115%, and more preferably 0.09-0.11%. In the present invention, Si has a solid-solution strengthening effect.
The aluminum alloy comprises, by mass, 0.15-0.20% of Mg, preferably 0.155-0.195%, and more preferably 0.16-0.19%. In the invention, Mg has the function of solid solution strengthening, and is beneficial to refining the grain size of the aluminum alloy and improving the strength; furthermore, Si and Mg may precipitate Mg2The Si strengthening phase is beneficial to enhancing the strength of the aluminum alloy; the Si and the Mg are controlled in the corresponding content range, so that the strength of the aluminum alloy is favorably ensured, the large extrusion deformation resistance of the aluminum alloy is avoided, and the deterioration of the extrusion performance is prevented.
The aluminum alloy of the invention comprises 0.02-0.06% of Li by mass percentage, preferably 0.025-0.055%, and more preferably 0.03-0.05%. In the invention, Mn and Li can generate phase change reaction Al + Mn → MnAl6 and Al + Li → Al3Li, and the generated Al3Li and MnAl6 are thermodynamically stable fine dispersed phases, which is beneficial to inhibiting the recrystallization and the grain growth of the aluminum alloy.
The aluminum alloy comprises, by mass, 0.005-0.008% of Ti, preferably 0.0055-0.0075%, and more preferably 0.006-0.007%. In the invention, Ti is beneficial to refining the crystal grains of the cast ingot and improving the structural component uniformity of the aluminum alloy; controlling Ti in a corresponding content range is beneficial to refining grains, preventing Ti-containing particles in the cast ingot from aggregating and growing, preventing the extruded product from having white line stripe defects and discontinuously scratching thin-walled regions so as to be difficult to continuously produce, preventing the cast ingot from having overlarge grains (more than 500 mu m) and uneven components and structures of the cast ingot, and avoiding the deterioration of the extrusion processing performance and the mechanical property of the aluminum alloy.
The aluminum alloy of the present invention includes, in mass percentage, the balance of Al and inevitable impurities.
In the present invention, Al is a base alloy element.
In the present invention, the inevitable impurities include Fe and non-Fe impurities. In the present invention, the content of Fe in the inevitable impurities is preferably 0.08% or less, more preferably 0.07% or less, and still more preferably 0.05% or less, by mass%. In the invention, the impurity element Fe may form a hard and brittle acicular AlFeSi intermetallic compound, which is hard, can improve the extrusion difficulty, and often becomes a root cause of scratching and tearing of the section bar in the extrusion process, thus deteriorating the extrusion property of the aluminum alloy. Therefore, the method needs to strictly control the content of Fe, and the combination of controlling the addition of 0.07-0.10% of Mn in the aluminum alloy promotes the nodularization of the needle-like Fe-containing phase, and eliminates the negative influence of Fe impurity elements.
In the invention, the content of a single element in the non-Fe impurity is preferably less than or equal to 0.05 percent, and more preferably less than or equal to 0.04 percent in percentage by mass; the total content of said non-Fe impurities is preferably less than or equal to 0.15%, more preferably less than or equal to 0.13%, still more preferably less than or equal to 0.1%. In the present invention, the non-Fe impurities preferably include one or more of Na, Ca, V and B.
In the present invention, Li and Mn are required to satisfy 0.12 wt.% or more and 0.15 wt.% or less, preferably 0.125 wt.% or more and 0.145 wt.% or less, more preferably 0.13 wt.% or more and 0.14 wt.% or less. The invention controls the content relation of Li and Mn, is favorable for ensuring that the aluminum alloy has a fine recrystallization structure after extrusion, has a grain grade above 5 grade, effectively prevents a coarse recrystallization structure above 5 grade or a mixed grain structure with coarse recrystallization structure and fibrous crystal structure coexisting due to coarse intermetallic compound size, avoids the deterioration of the strength and the extrusion performance of the aluminum alloy, is favorable for balancing the relation between the strength and the extrusion performance of the aluminum alloy, and meets the requirements of a thin-wall small-cavity structure on the strength and the extrusion performance.
In the invention, the tensile strength of the aluminum alloy is preferably 150-170 MPa. In the present invention, the aluminum alloy is extruded under conditions of: the limiting wall thickness is preferably 0.5 mm; the limiting cross-sectional area of the single small cavity is preferably 2mm when extruding the small cavity profile2The number of the small cavities is preferably 5-50.
The invention also provides a preparation method of the aluminum alloy in the technical scheme, which comprises the following steps:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot; the smelting comprises melting, refining, online grain refinement treatment and online degassing and filtering which are sequentially carried out;
and carrying out homogenization treatment, deformation treatment, quenching and aging treatment on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
Fig. 1 is a flow chart of a method for preparing an aluminum alloy according to the present invention, and the method for preparing an aluminum alloy according to the present invention is described in detail below with reference to fig. 1.
The method comprises the following steps of sequentially smelting and casting alloy raw materials to obtain an aluminum alloy ingot; the smelting comprises the steps of melting, refining, online grain refinement treatment and online degassing and filtering which are sequentially carried out.
The method comprises the following steps of smelting an alloy raw material to obtain an aluminum alloy ingot; the smelting comprises the steps of melting, refining, online grain refinement treatment and online degassing and filtering which are sequentially carried out.
The alloy raw materials are not particularly limited, and any alloy raw materials which can meet the composition of the aluminum alloy elements can be adopted.
In the invention, the melting temperature is preferably 740-760 ℃, and more preferably 745-755 ℃; the melting time is preferably 1 to 5 hours, and more preferably 3 to 4 hours. In the present invention, the melting apparatus is preferably a tilting melting furnace. The first aluminum alloy melt is obtained through melting.
In the present invention, the refining is preferably performed by mixing the first aluminum alloy melt, a refining agent, and a slag former, and refining the mixture under an argon gas flow condition to obtain a second aluminum alloy melt. In the present invention, the refining agent is preferably a 6AB refining agent; the 6AB refining agent preferably comprises, by mass, K15-25%, Na 15-25%, Al 0-10%, Si 2-10%, Cl 10-30%, F5-20% and the balance of impurities. In the invention, the amount of the refining agent used relative to the first aluminum alloy melt is preferably 0.5-1 kg/t, and more preferably 0.6-0.9 kg/t. In the present invention, the slag removing agent is preferably one or more of K, Al, Si, Cl, F, Ni, Pb, Sn, B, Be, Ca, Na and V. In the embodiment of the invention, the slag-removing agent is preferably a D4 slag-removing agent; the D4 slagging agent preferably comprises, by mass, 8-12% of K, 10-20% of Na, 0-10% of Al, 3-15% of Si, 20-30% of Cl and 20-30% of F. In the invention, the amount of the slag removing agent relative to the first aluminum alloy melt is preferably 0.5-1 kg/t, and more preferably 0.6-0.9 kg/t. In the invention, the preferable introducing speed of the argon is 1-2 m3More preferably 1.2 to 2m3H is used as the reference value. In the invention, the refining temperature is preferably 730-780 ℃, and more preferably 740-760 ℃; the time is preferably 10 to 40min, and more preferably 15 to 30 min.
After the refining, the invention preferably further comprises slagging off and standing the second aluminum alloy melt. The slag skimming method is not particularly limited, and the slag skimming method known by the skilled person can be adopted. In the invention, the standing time is preferably 10-40 min, and more preferably 15-30 min. According to the invention, the second aluminum alloy solution is subjected to degassing and impurity removal primarily by refining under the condition of introducing argon.
In the present invention, the online grain refinement treatment is preferably performed by mixing the second aluminum alloy melt with a grain refiner, and performing online grain refinement treatment to obtain a third aluminum alloy melt. In the invention, the grain refiner is preferably an aluminum-titanium-boron wire, and the chemical composition of the aluminum-titanium-boron wire is preferably Al-3 Ti-1B. In the invention, the aluminum-titanium-boron wire is preferably added into the second aluminum alloy melt; the addition rate of the aluminum-titanium-boron wire is preferably determined according to the calculation formula of the following formula:
adding speed (m/min) ([ the number of casting holes of the aluminum alloy ingot multiplied by the meter weight of the aluminum alloy ingot multiplied by the casting speed x (the target value content of Ti in the aluminum alloy-the content of Ti in the raw material aluminum ingot) ]/(the content of Ti in the aluminum-titanium-boron line multiplied by the meter weight of the aluminum-titanium-boron line);
wherein the unit of the meter weight of the aluminum alloy ingot and the meter weight of the aluminum-titanium-boron wire is kg, the unit of the casting speed is m/min, and the absolute value of each parameter in the calculation formula is taken.
In the present invention, the on-line degassing filtration preferably includes degassing tank filtration, ceramic foam filter plate filtration and tubular filter tank filtration, which are sequentially performed. In the invention, the online degassing and filtering is preferably performed by sequentially flowing the third aluminum alloy melt through a degassing tank, a foamed ceramic filter plate and a tubular filter tank which are arranged on a chute to obtain a fourth aluminum alloy melt. In the invention, the rotating speed of the rotor in the degassing box is preferably 400-500 rpm, and more preferably 420-480 rpm; the preferred flow rate of argon gas is 2.0-2.55 m3More preferably 2.05 to 2.4 m/h3H is used as the reference value. In the present invention, the porosity of the ceramic foam filter plate is preferably 80 ppi. In the invention, the temperature of the tubular filter in the tubular filter box is preferably 810-880 ℃, and more preferably 820-870 ℃.
In the invention, the casting temperature is preferably 700-730 ℃, and more preferably 705-725 ℃. In the present invention, the casting speed is preferably 0.150 to 0.250m/min, and more preferably 0.170 to 0.230 m/min. The number of the aluminum alloy casting holes in the casting is not particularly limited in the invention, and the number of the casting holes known to those skilled in the art can be adopted.
After an alloy ingot is obtained, homogenizing treatment, deformation treatment, quenching and aging treatment are sequentially carried out on the aluminum alloy ingot to obtain the aluminum alloy.
The aluminum alloy ingot is subjected to homogenization treatment to obtain a homogenized ingot.
In the invention, the heat preservation temperature of the homogenization treatment is preferably 520-540 ℃, and more preferably 525-535 ℃; the heat preservation time is preferably 4-8 h, and more preferably 4.5-7.5 h. In the invention, the homogenization treatment is beneficial to eliminating macro-micro segregation of alloy elements in the ingot, so that the alloy elements and coarse compounds are fully dissolved in a solid manner, and fine dispersoids are formed at the same time.
After the homogenization treatment, the obtained homogenized cast ingot is preferably cooled to room temperature; the cooling is preferably air cooling.
After the homogenized cast ingot is obtained, the homogenized cast ingot is sequentially subjected to deformation treatment and quenching to obtain the wrought aluminum alloy.
In the invention, the temperature of the deformation treatment is preferably 450-500 ℃, and more preferably 455-495 ℃. In the present invention, the temperature of the deformation treatment is preferably obtained by raising the temperature to room temperature; the heating rate is preferably 6-9 ℃/min, and more preferably 8-9 ℃/min. In the present invention, the deformation treatment is preferably extrusion. In the present invention, the apparatus for the deformation treatment is preferably a forward extruder. In the present invention, the extrusion speed is preferably 20 to 25m/min, and more preferably 21 to 24 m/min. In the present invention, the extrusion ratio of the extrusion is preferably 50 to 100, and more preferably 55 to 95. In the invention, the temperature of the die in extrusion is preferably 450-480 ℃, and more preferably 455-475 ℃. In the invention, the deformation treatment is beneficial to realizing solid solution of the alloy strengthening phase, simultaneously obtains the expected product prototype and is beneficial to realizing the accurate process control of the product.
Before the extrusion, 1050 pure aluminum cast ingot drainage is preferably carried out in the invention; and the 1050 pure aluminum cast ingot is drained, preferably, the extrusion of the homogenized cast ingot is carried out after the pure aluminum cast ingot is extruded. In the invention, the number of pure aluminum ingots in the 1050 pure aluminum ingot drainage is preferably 1-3; the extrusion speed is preferably 10-15 m/min, and more preferably 11-14 m/min; the temperature of the pure aluminum ingot is preferably 500-520 ℃, and more preferably 505-515 ℃. The 1050 pure aluminum cast ingot with small deformation resistance is adopted for drainage, so that smooth deformation of the aluminum alloy with higher strength is facilitated.
In the present invention, the quenching is preferably an in-line air-cooled quenching. In the invention, the cooling rate of quenching is preferably not less than 100 ℃/min, and more preferably 100-200 ℃/min. In the invention, the quenching is beneficial to forming supersaturated solid solution, and lays a foundation for subsequent aging.
After the wrought aluminum alloy is obtained, the invention carries out aging treatment on the wrought aluminum alloy to obtain the aluminum alloy.
In the invention, the heat preservation temperature of the aging treatment is preferably 200-210 ℃, and more preferably 202-208 ℃; the heat preservation time is preferably 1-3 h, and more preferably 1.5-2.5 h. In the present invention, the temperature of the aging treatment is preferably obtained by raising the temperature to room temperature; the heating rate is preferably 2-10 ℃/min, and more preferably 3-5 ℃/min. In the invention, the aging treatment is beneficial to separating out the strengthening phase in the aluminum alloy and improving the strength of the aluminum alloy; within the condition range of the aging treatment, the invention is beneficial to simultaneously ensuring the strength and the extrusion performance of the aluminum alloy and preventing the strength reduction or the extrusion difficulty of the aluminum alloy.
The invention also provides application of the aluminum alloy in the technical scheme or the aluminum alloy prepared by the preparation method in the technical scheme as a thin-wall small-cavity structural section in a heat exchanger.
In the present invention, the application is preferably that the aluminum alloy is directly subjected to heat exchanger molding treatment, and the thin-walled small-cavity profile obtained by the molding treatment is used as a main body member of the heat exchanger. The heat exchanger forming process of the present invention is not particularly limited, and a heat exchanger forming process known to those skilled in the art may be used.
In order to further illustrate the present invention, the following examples are provided to describe an aluminum alloy and its preparation method and application in detail, but they should not be construed as limiting the scope of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
Designing the element composition of the aluminum alloy to be 0.08 percent of Cu, 0.08 percent of Mn, 0.08 percent of Si, 0.15 percent of Mg, 0.04 percent of Li, 0.005 percent of Ti, the balance of Al and inevitable impurities according to the mass percentage; fe 0.067% of inevitable impurities, the content of single non-Fe impurities is less than or equal to 0.05%, and the total amount of non-Fe impurities is less than or equal to 0.15%;
preparing an aluminum alloy: melting alloy raw materials conforming to the composition of design elements at 750 ℃ for 3h to obtain a first aluminum alloy melt, wherein the dosage of the first aluminum alloy melt is 1kg/t, adding a 6AB refining agent and a D4 slagging agent into the first aluminum alloy melt, refining at 740 ℃ for 30min, slagging off, and standing for 30min to obtain a second aluminum alloy melt; introducing the obtained second aluminum alloy melt into a chute, and adding a grain refiner Al-3Ti-1B into the second aluminum alloy melt for online grain refinement treatment to obtain a third aluminum alloy melt; the obtained third aluminum alloy melt is sequentially subjected to the rotation speed of a rotor on a launder of 450rpm and the flow of argon of 2.05m3H, a degassing box, a foamed ceramic filter plate with the porosity of 80ppi and a tubular filter box with the temperature of 850 ℃ of a tubular filter, so as to obtain a fourth aluminum alloy melt;
casting the obtained fourth aluminum alloy melt at 700-730 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy ingot to 530 ℃ at the speed of 4 ℃/min, preserving the heat at 530 ℃ for 5 hours, and air-cooling to room temperature to obtain a homogenized ingot; heating the obtained homogenized cast ingot to 480-490 ℃, extruding at the extrusion speed of 22m/min, performing on-line air cooling quenching at the cooling rate of 120 ℃/min to obtain a wrought aluminum alloy, draining 2 1050 pure aluminum cast ingots before extrusion, wherein the temperature of the pure aluminum cast ingots is 520 ℃, and the extrusion speed of the pure aluminum cast ingots is 12 m/min; and heating the obtained wrought aluminum alloy to 200 ℃ at the speed of 5 ℃/min, and preserving heat at 200 ℃ for 2h for aging treatment to obtain the aluminum alloy.
Metallographic observations were made of the aluminum alloy obtained in this example, and the obtained metallographic image is shown in FIG. 2. As can be seen from FIG. 2, the aluminum alloy provided by the invention is recrystallized grains with more than 5 grades, which is beneficial to the aluminum alloy having good extrusion performance.
Example 2
The aluminum alloy is designed to have the element composition of 0.12 percent of Cu, 0.10 percent of Mn, 0.12 percent of Si, 0.20 percent of Mg, 0.05 percent of Li, 0.008 percent of Ti, and the balance of Al and inevitable impurities according to the mass percentage; the content of Fe in the inevitable impurities is 0.08 percent, the content of single non-Fe impurities is less than or equal to 0.05 percent, and the total content of the non-Fe impurities is less than or equal to 0.15 percent;
preparing an aluminum alloy: melting alloy raw materials conforming to the composition of design elements at 750 ℃ for 4 hours to obtain a first molten aluminum alloy, wherein the dosage of the first molten aluminum alloy is 0.8kg/t, adding a 6AB refining agent and a D4 slagging agent into the first molten aluminum alloy, refining at 750 ℃ for 18min, slagging off, and standing for 30min to obtain a second molten aluminum alloy; introducing the obtained second aluminum alloy melt into a chute, and adding a grain refiner Al-3Ti-1B into the second aluminum alloy melt for online grain refinement treatment to obtain a third aluminum alloy melt; the obtained third aluminum alloy melt is sequentially subjected to the rotation speed of a rotor on a launder of 450rpm and the flow of argon of 2.05m3H, a degassing box, a foamed ceramic filter plate with the porosity of 80ppi and a tubular filter box with the temperature of 850 ℃ of a tubular filter, so as to obtain a fourth aluminum alloy melt;
casting the obtained fourth aluminum alloy melt at 700-730 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy ingot to 530 ℃ at the speed of 5 ℃/min, preserving the heat at 530 ℃ for 5h, and air-cooling to room temperature to obtain a homogenized ingot; heating the obtained homogenized cast ingot to 480-490 ℃, extruding at the extrusion speed of 22m/min, performing on-line air cooling quenching at the cooling rate of 120 ℃/min to obtain a wrought aluminum alloy, draining 2 1050 pure aluminum cast ingots before extrusion, wherein the temperature of the pure aluminum cast ingots is 520 ℃, and the extrusion speed of the pure aluminum cast ingots is 12 m/min; and heating the obtained wrought aluminum alloy to 200 ℃ at the speed of 5 ℃/min, and preserving heat at 200 ℃ for 2h for aging treatment to obtain the aluminum alloy.
Example 3
Designing the element composition of the aluminum alloy to be 0.10 percent of Cu, 0.10 percent of Mn, 0.10 percent of Si, 0.17 percent of Mg, 0.02 percent of Li, 0.005 percent of Ti, and the balance of Al and inevitable impurities according to the mass percentage; the content of Fe in the inevitable impurities is 0.06 percent, the content of single non-Fe impurities is less than or equal to 0.05 percent, and the total content of the non-Fe impurities is less than or equal to 0.15 percent;
preparing an aluminum alloy: melting alloy raw materials conforming to the composition of the design elements at 740 ℃ for 3h to obtain a first aluminum alloy melt, wherein the dosage of the first aluminum alloy melt is 1kg/t, adding a 6AB refining agent and a D4 slagging agent into the first aluminum alloy melt, refining at 760 ℃ for 39min, slagging off, and standing for 30min to obtain a second aluminum alloy melt; introducing the obtained second aluminum alloy melt into a chute, and adding a grain refiner Al-3Ti-1B into the second aluminum alloy melt for online grain refinement treatment to obtain a third aluminum alloy melt; the obtained third aluminum alloy melt is sequentially subjected to the rotation speed of a rotor on a launder of 450rpm and the flow of argon of 2.05m3H, a degassing box, a foamed ceramic filter plate with the porosity of 80ppi and a tubular filter box with the temperature of 850 ℃ of a tubular filter, so as to obtain a fourth aluminum alloy melt;
casting the obtained fourth aluminum alloy melt at 700-730 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy ingot to 530 ℃ at the speed of 5 ℃/min, preserving the heat at 530 ℃ for 5h, and air-cooling to room temperature to obtain a homogenized ingot; heating the obtained homogenized cast ingot to 480-490 ℃, extruding at the extrusion speed of 22m/min, performing on-line air cooling quenching at the cooling rate of 120 ℃/min to obtain a wrought aluminum alloy, draining 2 1050 pure aluminum cast ingots before extrusion, wherein the temperature of the pure aluminum cast ingots is 520 ℃, and the extrusion speed of the pure aluminum cast ingots is 12 m/min; and heating the obtained wrought aluminum alloy to 200 ℃ at the speed of 3 ℃/min, and preserving heat at 200 ℃ for 2h for aging treatment to obtain the aluminum alloy.
Comparative example 1
The elemental composition was consistent with example 3;
in the preparation method of the aluminum alloy, the homogenization treatment is to keep the temperature at 545 ℃ for 9h, and the other technical means are the same as those in the embodiment 3 to obtain the aluminum alloy.
Comparative example 2
The elemental composition was consistent with example 3;
in the preparation method of the aluminum alloy, the homogenization treatment is to keep the temperature at 520 ℃ for 3 hours, and the other technical means are the same as those in the embodiment 3 to obtain the aluminum alloy.
Comparative example 3
Designing the element composition of the aluminum alloy to be 0.10 percent of Cu, 0.12 percent of Mn, 0.10 percent of Si, 0.17 percent of Mg, 0.08 percent of Li, 0.01 percent of Ti, and the balance of Al and inevitable impurities according to the mass percentage; the content of Fe in the inevitable impurities is 0.10 percent, the content of single non-Fe impurities is less than or equal to 0.05 percent, and the total content of the non-Fe impurities is less than or equal to 0.15 percent;
the preparation method of the aluminum alloy was the same as that of example 1 to obtain an aluminum alloy.
The extruded products of the aluminum alloys obtained in examples 1 to 3 and comparative examples 1 to 3 were observed under a standard light source D65 at a distance of about 600mm from the eyes of the examiner, and a schematic view of the sample of the heat exchanger section in the extrusion test is shown in FIG. 3, wherein the extruded product has a wall thickness of 0.5mm and a small cavity cross-sectional diameter of 2.5mm2A heat exchanger profile of 12.3mm in length; the tensile strength of the aluminum alloys obtained in examples 1 to 3 and comparative examples 1 to 3 was measured by a universal material testing machine according to the room temperature test method of part 1 of the tensile test of the metal material of GB T228.1, and the test results are shown in Table 1.
TABLE 1 test results of Performance of aluminum alloys obtained in examples 1 to 3 and comparative examples 1 to 3
Note: in Table 1, "/" indicates that no extrusion property was essential because it was not extrudable, and no subsequent extrusion production test and extrudate test were conducted.
As can be seen from Table 1, the aluminum alloy provided by the invention has good extrudability and good performance of continuous extrusion production; the tensile strength can reach 152-170 MPa, and the tensile strength is high.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. The aluminum alloy is characterized by comprising the following elements in percentage by mass:
0.08 to 0.12 percent of Cu, 0.07 to 0.10 percent of Mn, 0.08 to 0.12 percent of Si, 0.15 to 0.20 percent of Mg, 0.02 to 0.06 percent of Li, 0.005 to 0.008 percent of Ti, and the balance of Al and inevitable impurities;
0.12wt.％≤Li+Mn≤0.15wt.％。
2. the aluminum alloy of claim 1, wherein the unavoidable impurities include Fe and non-Fe impurities, Fe ≦ 0.08%, a content of a single element in the non-Fe impurities ≦ 0.05%, and a total content of the non-Fe impurities ≦ 0.15%, in mass%.
3. The aluminum alloy of claim 1 or 2, wherein the aluminum alloy has a tensile strength of 150 to 170 MPa.
4. The aluminum alloy of claim 1 or 2, wherein the aluminum alloy is extruded under extrusion conditions: the limiting wall thickness is 0.5 mm; the limiting cross-sectional area of a single small cavity is 2mm when the small cavity profile is extruded2The number of the small cavities is 5-50.
5. A method for producing an aluminum alloy as recited in any one of claims 1 to 4, characterized by comprising the steps of:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot; the smelting comprises melting, refining, online grain refinement treatment and online degassing and filtering which are sequentially carried out;
and carrying out homogenization treatment, deformation treatment, quenching and aging treatment on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
6. The preparation method according to claim 5, wherein the melting temperature is 740 to 760 ℃;
the refining temperature is 730-780 ℃, and the refining time is 10-40 min;
the temperature of the grain refining treatment is 710-750 ℃;
the on-line degassing and filtering comprises degassing tank filtering, foamed ceramic filter plate filtering and tubular filter tank filtering which are sequentially carried out.
7. The preparation method according to claim 5, wherein the homogenization treatment is carried out at a holding temperature of 520 to 540 ℃ for 4 to 8 hours.
8. The method according to claim 5, wherein the temperature of the deformation treatment is 450 to 500 ℃.
9. The preparation method according to claim 5, wherein the temperature of the aging treatment is 200-210 ℃, and the holding time is 1-3 h.
10. Use of the aluminium alloy according to any one of claims 1 to 4 or the aluminium alloy prepared by the preparation method according to any one of claims 5 to 9 as a thin-walled small-cavity structural profile in a heat exchanger.
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