CN117070787B - Aluminum alloy profile, preparation method and application thereof - Google Patents
Aluminum alloy profile, preparation method and application thereof Download PDFInfo
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- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 238000005260 corrosion Methods 0.000 claims abstract description 39
- 230000007797 corrosion Effects 0.000 claims abstract description 39
- 238000000265 homogenisation Methods 0.000 claims abstract description 35
- 238000011282 treatment Methods 0.000 claims abstract description 31
- 238000010791 quenching Methods 0.000 claims abstract description 26
- 230000000171 quenching effect Effects 0.000 claims abstract description 26
- 229910052691 Erbium Inorganic materials 0.000 claims abstract description 19
- 238000005266 casting Methods 0.000 claims abstract description 13
- 239000000203 mixture Substances 0.000 claims abstract description 13
- 239000002994 raw material Substances 0.000 claims abstract description 9
- 238000001192 hot extrusion Methods 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 239000000956 alloy Substances 0.000 claims description 79
- 238000000034 method Methods 0.000 claims description 69
- 230000008569 process Effects 0.000 claims description 61
- 229910045601 alloy Inorganic materials 0.000 claims description 47
- 238000001125 extrusion Methods 0.000 claims description 43
- 230000032683 aging Effects 0.000 claims description 32
- 238000010438 heat treatment Methods 0.000 claims description 29
- 229910052726 zirconium Inorganic materials 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 15
- 239000012535 impurity Substances 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 3
- 238000012360 testing method Methods 0.000 claims description 3
- 230000002929 anti-fatigue Effects 0.000 abstract 1
- 238000001556 precipitation Methods 0.000 description 15
- 238000005728 strengthening Methods 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 11
- 239000006104 solid solution Substances 0.000 description 11
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- 238000010899 nucleation Methods 0.000 description 4
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- 238000004901 spalling Methods 0.000 description 4
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- 230000015572 biosynthetic process Effects 0.000 description 3
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- 238000000137 annealing Methods 0.000 description 2
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- 229910052746 lanthanum Inorganic materials 0.000 description 2
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- 229910000553 6063 aluminium alloy Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—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 silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—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 copper as the next major constituent
Abstract
The invention provides an aluminum alloy section bar, a preparation method and application thereof. The raw materials are prepared according to the following components: the components of the composition in percentage by weight are: 0.70 to 1.10 percent of Mg, 0.70 to 1.10 percent of Si, 0.50 to 0.80 percent of Cu, 0.20 to 0.80 percent of Mn, less than or equal to 0.40 percent of Fe, 0.10 to 0.15 percent of Er, 0.10 to 0.15 percent of Zr0.15 percent, and the balance of Al; the raw materials are sequentially subjected to casting, two-stage homogenization treatment, sawing, turning, hot extrusion, online quenching and straightening and time-efficient treatment, and the aluminum alloy is obtained. The tensile strength of the prepared section bar is more than or equal to 400MPa, the peeling corrosion resistance is more than or equal to EA grade, the fatigue strength is more than or equal to 200MPa (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ) Can realize the application of the novel high-strength corrosion-resistant anti-fatigue profile in the field of ship industry and ocean engineering equipment.
Description
Technical Field
The invention relates to the technical field of alloys, in particular to an aluminum alloy section bar, a preparation method and application thereof.
Background
The 6-series aluminum alloy is used as one of the aluminum alloys with the largest yield, and is widely applied to important industries such as aerospace, weapon equipment, transportation and the like. The mechanical properties are improved mainly through a solid solution-quenching-aging process, the solid solution process requires precise control of the solid solution temperature to realize sufficient dissolution of alloy elements and ensure the balance between the surface quality of the profile, and meanwhile, the standing time from the quenching to the aging furnace has great influence on the mechanical properties; the aging strengthening phase is easy to be unevenly precipitated along the intergranular, and grain boundary corrosion and peeling corrosion are easy to occur in the use process of the section bar; because each technological parameter is difficult to control, the application of the heat treatment reinforced 6-series profile in the field of ships and marine engineering equipment is limited.
In recent years, there have been few studies on how to improve various properties of 6-series aluminum alloy sections, mainly including:
patent CN110066932B discloses a medium-strength weldable corrosion-resistant 6-series aluminum alloy and a preparation method thereof, wherein the alloy comprises 0.3-0.8% of Zn; meanwhile, the alloy composition of the patent contains 0.01 to 0.06 percent of mixed rare earth elements, wherein the rare earth elements consist of 40 to 60 percent of Er, 25 to 35 percent of La and 5 to 15 percent of Lu according to mass percent. And the medium-strength weldable corrosion-resistant 6-series aluminum alloy is obtained through single-stage homogenization treatment, heat treatment, hot extrusion, quenching treatment and double-stage aging treatment. In this patent, the alloy component contains Zn element, so that the corrosion resistance of the obtained material is low.
Patent CN110923518B discloses a high-strength corrosion-resistant aluminum alloy plate for ships and a preparation method thereof. The aluminum alloy plate comprises 6.1-7.1% of Mg, less than or equal to 0.1% of Cu, 0.55-1.05% of Mn, 0.1-0.2% of Cr, less than or equal to 0.15% of Si, less than or equal to 0.3% of Fe, 0.1-0.2% of Zr and the balance of Al. In the preparation method, part of steps are selected from homogenization, hot rolling, temperature control cooling, primary cold rolling, intermediate annealing, final cold rolling, stabilizing annealing, straightening, slitting and packaging according to the thickness of the sheet material, and the high-strength corrosion-resistant aluminum alloy sheet material for ships is obtained. Er is not added in the alloy components of the patent, and the comprehensive performance of the plate can be improved to a certain extent through the dispersion strengthening effect of Zr element, but the tensile strength is still poor.
Patent CN111575550B discloses a high-strength weldable aluminum alloy and a preparation method thereof, the alloy composition of the patent contains 0.1-0.5% zn and 0.1-0.3% other alloy elements, the other alloy elements comprise Ni, V, ti, zr and rare earth elements, and the rare earth elements comprise: ce. La and Er, wherein Ce accounts for more than 60 percent of the total amount of rare earth elements. In the aspect of the preparation method, the single-stage homogenization technology is adopted in the aspect of homogenization, and the fatigue performance and the corrosion resistance of the obtained alloy are poor, so that the alloy is not suitable for the field of ships and marine engineering equipment.
At present, the 6-series aluminum alloy prepared by the prior art has the problem that the performances such as high strength, corrosion resistance, fatigue resistance and the like are difficult to achieve at the same time, so that the comprehensive performance of the 6-series aluminum alloy is required to be improved, the application requirements in the fields of ship industry and ocean engineering equipment are met, and the development of the ocean engineering equipment and high-technology ships is promoted.
Disclosure of Invention
The invention mainly aims to provide a high-strength corrosion-resistant fatigue-resistant aluminum alloy profile for a ship and a preparation method thereof, which are used for solving the problems that the mechanical property of the 6-series alloy profile for the ship in the prior art is insufficient and falling corrosion is easy to occur in the use process. According to the invention, through the innovative design of alloy components and the accurate control of a processing technology, the tensile strength of the prepared profile is more than or equal to 400MPa, the peeling corrosion resistance performance is more than or equal to EA grade, the fatigue strength is more than or equal to 200MPa (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ) The comprehensive performance is excellent.
In order to achieve the above object, according to an aspect of the present invention, there is provided a method for preparing an aluminum alloy, comprising:
the raw materials are prepared according to the following components: the aluminum alloy profile comprises the following components in percentage by weight: 0.70 to 1.10 percent of Mg, 0.70 to 1.10 percent of Si, 0.50 to 0.80 percent of Cu, 0.20 to 0.80 percent of Mn, less than or equal to 0.40 percent of Fe, 0.10 to 0.15 percent of Er, 0.10 to 0.15 percent of Zr, less than or equal to 0.15 percent of total unavoidable impurities, less than or equal to 0.05 percent of each unavoidable impurity, and the balance of Al;
the raw materials are subjected to casting, double-stage homogenization treatment, sawing, turning, hot extrusion, on-line quenching, straightening and ageing treatment in sequence to obtain the aluminum alloy.
Further, the weight ratio of Mg to Si element in the components of the aluminum alloy profile is (0.74-1.83): 1.
Further, an alloy cast ingot is obtained through a casting step, and the two-stage homogenization treatment process comprises the following steps: heating the alloy ingot to 280-320 ℃ and preserving heat for 8-10 h, then continuously heating to 545-565 ℃ and preserving heat for 16-24 h, and air-cooling to room temperature to obtain a homogenized ingot; or heating the alloy ingot to 380-420 ℃ at a heating rate of 25 ℃/h, preserving heat for 8-10 h, continuously heating to 545-565 ℃ at a heating rate of 25 ℃/h, preserving heat for 16-24 h, and cooling to room temperature by air to obtain the homogenized ingot.
Further, after the ingot casting subjected to homogenization treatment is subjected to sawing and turning treatment in sequence, a turning ingot casting is obtained, and the heating extrusion process comprises heating the turning ingot casting to 510-550 ℃ and then extrusion molding to obtain a section bar; preferably, in the extrusion molding process, the temperature of the die and the temperature of the extrusion cylinder are 440-460 ℃, the extrusion speed of the profile is 5.1-7.2 m/min, and the extrusion ratio is 26.5-42.8.
Further, in the online quenching process, the quenching temperature of the profile is 480-530 ℃, and the quenching mode is through water cooling.
Further, the straightening treatment process is to stretch-straighten the quenched profile obtained through on-line quenching, and the stretching amount in the stretching straightening process is preferably 0.5-1.5%.
Further, the aging treatment process is artificial aging, preferably the aging treatment temperature is 165-195 ℃ and the aging treatment time is 4-24 hours.
The invention also provides an aluminum alloy section which is prepared by the preparation method, and the tensile strength of the aluminum alloy section is more than or equal to 400MPa, and the peeling corrosion resistance is more than EA grade,fatigue strength of 200MPa or more (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ）。
The invention also provides application of the aluminum alloy section in the fields of ship industry and ocean engineering equipment.
By applying the technical scheme of the invention, submicron/nanometer Al is formed in the homogenization process by compositely adding micro alloying elements Er and Zr into the aluminum alloy profile components 3 The (Er, zr) composite precipitated phase has the advantages of directly causing precipitation strengthening and inhibiting recrystallization nucleation and grain growth in the extrusion process, ensuring good surface quality of the extruded profile, promoting precipitation in the time of artificial aging and achieving the aims of comprehensive balance strength, corrosion resistance and fatigue performance; while the first-stage homogenization of the two-stage homogenization process regime achieves, for example, al 3 (Er，Zr)、Al 6 Precipitation of Mn-like dispersed phases, second-stage homogenization achieving, for example, mg 2 The re-dissolution of Si, Q, and the like, and the intermittent morphology transformation of e.g. AlFeMnSi insoluble phases. The tensile strength of the aluminum alloy section prepared by the method is more than or equal to 400MPa, the peeling corrosion resistance is more than EA grade, the fatigue strength is more than or equal to 200MPa (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ) The comprehensive performance is excellent.
Drawings
The accompanying drawings, which are included to provide a further understanding of the invention and are incorporated in and constitute a part of this specification, illustrate embodiments of the invention and together with the description serve to explain the invention. In the drawings:
FIG. 1 is a uniaxial equilibrium phase diagram calculated by Thermolc ac for example 1 of the present invention.
Detailed Description
It should be noted that, in the case of no conflict, the embodiments and features in the embodiments may be combined with each other. The present invention will be described in detail with reference to examples.
As described in the background art, the 6-series alloy profile for the ship in the prior art has insufficient mechanical properties and is easy to fall and corrode in the use process. In order to solve the technical problems, the application provides a high-strength corrosion-resistant fatigue-resistant aluminum alloy section for a ship and a preparation method thereof, wherein the preparation method comprises the following steps:
the raw materials are prepared according to the following components: the aluminum alloy profile comprises the following components in percentage by weight: 0.70 to 1.10 percent of Mg, 0.70 to 1.10 percent of Si, 0.50 to 0.80 percent of Cu, 0.20 to 0.80 percent of Mn, less than or equal to 0.40 percent of Fe, 0.10 to 0.15 percent of Er, 0.10 to 0.15 percent of Zr, less than or equal to 0.15 percent of total unavoidable impurities, less than or equal to 0.05 percent of each unavoidable impurity, and the balance of Al; the raw materials are subjected to casting, double-stage homogenization treatment, sawing, turning, hot extrusion, on-line quenching, straightening and ageing treatment in sequence to obtain the aluminum alloy.
In the preparation method, the micro-alloying elements Er and Zr are added into the aluminum alloy profile component in a compounding way, so that submicron/nanometer Al is formed in the homogenization process 3 The (Er, zr) composite precipitated phase has the advantages of directly causing precipitation strengthening and inhibiting recrystallization nucleation and grain growth in the extrusion process, ensuring good surface quality of the extruded profile, promoting precipitation in the time of artificial aging and achieving the aims of comprehensive balance strength, corrosion resistance and fatigue performance; while the first-stage homogenization of the two-stage homogenization process regime achieves, for example, al 3 (Er，Zr)、Al 6 Precipitation of Mn-like dispersed phases, second-stage homogenization achieving, for example, mg 2 The re-dissolution of Si, Q, and the like, and the intermittent morphology transformation of e.g. AlFeMnSi insoluble phases. The tensile strength of the aluminum alloy section prepared by the method is more than or equal to 400MPa, the peeling corrosion resistance is more than EA grade, the fatigue strength is more than or equal to 200MPa (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ) The comprehensive performance is excellent.
Further, in the components of the aluminum alloy section, the weight ratio of Mg to Si element is (0.74-1.83): 1, in the preparation process of the 6-series aluminum alloy, the Mg and Si can form a beta reinforcing phase, the weight ratio of Mg to Si element in the beta reinforcing phase is about 0.86, the consumption of other intermetallic compounds such as Q-AlCuMgSi, alFeMnSi on the Mg and Si element is calculated, the proportion of the Mg and Si element is designed, the content of the beta reinforcing phase is improved, and the mechanical property and fatigue resistance of the aluminum alloy are further improved.
The components are subjected to a casting step to obtain alloy ingots, and then two-stage homogenization treatment is carried out, wherein the process comprises the following steps: heating the alloy ingot to 280-320 ℃ and preserving heat for 8-10 h, then continuously heating to 545-565 ℃ and preserving heat for 16-24 h, and air-cooling to room temperature to obtain a homogenized ingot; or heating the alloy ingot to 380-420 ℃ at a heating rate of 25 ℃/h, preserving heat for 8-10 h, continuously heating to 545-565 ℃ at a heating rate of 25 ℃/h, preserving heat for 16-24 h, and cooling to room temperature by air to obtain the homogenized ingot. Controlling the temperature, time and other parameters of the homogenization of the first and second stages within this range is beneficial to controlling the Al formed during the homogenization process 3 (Er，Zr)、Al 6 Mn content is in the optimal range while ensuring Mg 2 The dissolution of soluble phases such as Si and Q is carried out, for example, the intermittent morphology transformation of insoluble phases of AlFeMnSi is carried out, and the mechanical property, the peeling corrosion resistance and the fatigue property of the alloy material are further improved.
Sawing and turning the homogenized cast ingot in sequence to obtain a turning cast ingot, and heating and extruding the turning cast ingot to 510-550 ℃ and then extruding and forming to obtain a section; preferably, in the extrusion molding process, the temperature of the die and the temperature of the extrusion cylinder are 440-460 ℃, the extrusion speed of the profile is 5.1-7.2 m/min, and the extrusion ratio is 26.5-42.8. If the T5-state alloy has good strength, the alloy is used for replacing the T6-state alloy, so that a large amount of energy consumption is saved, and the quenching temperature of an extrusion outlet is required to be higher than the solid solution temperature of an alloy material. And a large amount of heat energy can be generated in the extrusion process, the higher the extrusion speed is, the higher the temperature of the profile in the extrusion process is, and the lower the extrusion speed is, the lower the temperature of the profile in the extrusion process is, the worse the solid solution degree is, so that the mechanical property and the fatigue property of the alloy material are lower. The invention adopts a high-temperature high-speed extrusion process to realize good mechanical properties of the T5-state alloy material.
And carrying out on-line quenching treatment on the extruded profile, wherein the quenching temperature of the profile is 480-530 ℃ in the process, and the quenching mode is through water cooling. Controlling the quenching temperature to be 480-530 ℃ is beneficial to ensuring the solid solution degree of the alloy material, so that the mechanical property and fatigue property of the alloy material are improved; selecting water penetrationCooling is beneficial to improving the cooling speed and reducing Mg 2 The precipitation of Si promotes the solid solubility of the alloy section bar, is beneficial to aging precipitation strengthening, and further improves the T5-state strength performance of the section bar.
The extruded and quenched profile inevitably has a certain degree of curvature, and meanwhile has the defects of twisting, flaring, wellhead, gaps and the like, so that in order to eliminate the defects, the quenched profile obtained through on-line quenching is subjected to stretching straightening treatment, and the stretching amount in the stretching straightening process is preferably 0.5-1.5%, so that the dimensional accuracy of the profile is improved.
Finally, artificial aging treatment is carried out on the profile, and the aging treatment temperature is 165-195 ℃ and the aging treatment time is 4-24 hours in order to realize that the alloy beta' strengthening phase is fully precipitated to reach a peak value, further improve the mechanical property, the fatigue strength and the like.
The invention also provides an aluminum alloy section prepared by the preparation method.
The tensile strength of the 6063 aluminum alloy extrusion profile in the T6 state is generally not higher than 260MPa; the tensile strength of 6061-T6 is also generally less than 290MPa, and the fatigue strength is also less than 160MPa (same test conditions as the invention). The tensile strength of the T5 state of the aluminum alloy section bar prepared by the method is more than or equal to 400MPa, the peeling corrosion resistance is more than or equal to EA level, and the fatigue strength is more than or equal to 200MPa (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ) Compared with the traditional aluminum alloy materials such as 6063, 6061, 6082 and the like, the comprehensive performance is comprehensively improved.
The invention also provides application of the aluminum alloy section in the fields of ship industry and ocean engineering equipment. The novel high-strength, corrosion-resistant and fatigue-resistant marine aluminum alloy profile provided by the application breaks through three key technologies of improving the strength of the novel marine aluminum alloy extrusion profile, improving the peeling corrosion resistance of the extrusion profile and improving the fatigue performance of the extrusion profile through the design of innovative components of the composite microalloying high-solute content 6-series alloy and the accurate control of the processing technology, and further forms a complete set of high-strength corrosion-resistant and fatigue-resistant profile industrialized preparation technology, so that the novel high-strength corrosion-resistant and fatigue-resistant profile is applied to the fields of ship industry and ocean engineering equipment.
The present application is described in further detail below in conjunction with specific embodiments, which should not be construed as limiting the scope of the claims.
It should be noted that, in the case of no conflict, the embodiments and features in the embodiments may be combined with each other. The present invention will be described in detail with reference to examples.
Term interpretation:
t5 state: the method is a state of cooling by a high-temperature forming process and then artificially aging, and is suitable for a product state of cooling by the high-temperature forming process without cold working (straightening and leveling can be performed, but mechanical property limit is not influenced) so as to artificially age.
T6 state: refers to a state of artificial aging after solid-melt heat treatment, and is suitable for a product state of no cold working (straightening and leveling can be performed, but mechanical property limit is not affected) after the solid-melt heat treatment.
Equilibrium phase diagram: is a graph used to represent the relationship between the composition of the phase equilibrium system and some parameters (e.g., temperature, pressure).
Example 1
Mixing and casting the raw materials of the 6-series aluminum alloy according to the component ratio to obtain an aluminum alloy cast ingot; performing two-stage homogenization treatment on the aluminum alloy cast ingot to obtain a homogenized cast ingot, wherein the homogenization process is 300 ℃ multiplied by 10 hours and 555 ℃ multiplied by 20 hours, and air cooling; sawing and turning the homogenized cast ingot; heating the ingot after sawing and turning the steel sheet, and performing hot extrusion to obtain an extruded section, wherein the temperature of the ingot is as follows: 540 ℃; the die temperature and the extrusion barrel temperature are as follows: 450 ℃; the extrusion speed of the profile is as follows: 6.2m/min, the extrusion ratio is: 26.5; carrying out on-line quenching treatment on the extruded profile to obtain a quenched profile, wherein the quenching temperature of the profile is controlled to be 520 ℃, and the quenching mode is through water cooling; straightening the quenched profile, wherein the stretching amount is controlled to be 1%; and (3) aging the straightened profile to obtain an aging profile, wherein the standing time is 1.5h, and the aging process is 190 ℃ multiplied by 5h. The profile was evaluated for its properties after 7 days of standing at room temperature, with a tensile strength of 403MPa and resistance to spalling corrosionThe EA grade has fatigue strength of more than or equal to 200MPa (R=0.1, K) t =1, f=10-200 Hz, cycle number 1.0x10 7 ). The aluminum alloy composition is shown in Table 1, the process parameters are shown in Table 2, the performance evaluation results are shown in Table 3, and the uniaxial equilibrium phase diagram calculated by Thermalcoc is shown in FIG. 1. In fig. 1:
(1) is AlFeMnSi; (2) is Al 3 (ErZr); (3) is Al 8 Cu 4 Er; (4) is AlFeSi; (5) is FCC_Al; (6) is LIQUID; (7) is Mg 2 Si; (8) Q_AlCuMgSi.
Examples 2 to 22
Examples 2 to 22 are different from example 1 in that the aluminum alloy composition and the process parameters are shown in table 1, the process parameters are shown in table 2, and the performance evaluation results are shown in table 3.
Comparative examples 1 to 6
Comparative examples 1 to 6 are different from example 1 in the aluminum alloy composition and the process parameters, the aluminum alloy composition is shown in table 1, the process parameters are shown in table 2, and the performance evaluation results are shown in table 3.
TABLE 1
TABLE 2
TABLE 3 Table 3
Description: fatigue strength test conditions: r=0.1, k t =1, f=10-200 Hz, cycle number 1.0x10 7 。
From the above description, it can be seen that the above embodiments of the present invention achieve the following technical effects:
from the above, the alloy compositions of comparative examples 1 to 5 are greatly different from the present invention, wherein comparative example 5 is a 6-series alloy in which no Er and Zr are added to the alloy composition in the prior art, and the process parameters of comparative example 6 are greatly different from the present invention. Examples 2 to 7 make adjustments to the alloy composition within the scope of the present application, and examples 8 to 22 make adjustments to the process parameters within the scope of the present application. Wherein the performance results of examples 13-22 are less than the most preferred example performance results within the scope of the present application, but still superior to the existing 6-series alloys.
In the comparative example 1, the content of Mg and Si elements is lower, the Mg and Si elements are dissolved back in the homogenization and solid solution process, and the content of the beta '' strengthening phase precipitated in the aging process is lower than that in the examples 1-10, so that the mechanical property and fatigue property of the alloy material are lower.
In comparative example 2, the Cu element content was high, and although the strength was greatly improved, the Cu-containing phase content was increased, and precipitation was likely to occur at the grain boundary, so that the spalling corrosion resistance of the alloy material was lowered.
When the content of Mn element in comparative example 3 is too much, the strengthening effect of Si element is reduced, the formation of intragranular segregation and the reduction of dispersed precipitated phase are realized, so that the extruded product has a coarse grain structure, and the mechanical property, the peeling corrosion resistance and the fatigue property of the alloy material are reduced.
In comparative example 4, the content of Er and Zr elements is low, and Al is formed in the first-stage homogenization process 3 (Er, zr) content was lower than in examples 1-10, al 3 The precipitation strengthening of (Er, zr) and the inhibition of recrystallization nucleation and grain growth in the extrusion process reduce the precipitation effect in the artificial aging promotion process, so that the mechanical property, the peeling corrosion resistance and the fatigue performance of the alloy material are reduced.
The alloy composition of comparative example 5 was not added with Er and Zr elements, and Al was not formed efficiently 3 (Er, zr), cannot exert Al 3 The beneficial effects of (Er, zr) are that the tensile strength is about 350MPa, the peeling corrosion resistance is about EB, and the fatigue strength is less than or equal to 200MPa.
The homogenization process in comparative example 6 was single-stage homogenization, resulting in inefficient Al formation 3 (Er，Zr)、Al 6 Mn, so that the mechanical property, the peeling corrosion resistance and the fatigue property of the alloy material are reduced.
Compared with the prior art, the embodiment of the invention can meet the requirements of tensile strength, peeling corrosion resistance and fatigue strength by the design of innovative components of the composite microalloying high-solute-content 6-series alloy and the accurate control of the processing technology. The precipitation-strengthened phase beta '' is fully acted without a large amount of excess Mg and Si by the weight ratio of Mg to Si of (0.74-1.83): 1. And proper Cu element is added to promote the formation of beta' phase in the aging process, so that the aging hardening performance is improved. The proper amount of Mn element can inhibit the recrystallization process, obviously refine recrystallized grains in the final stage of recrystallization, and also contribute to the improvement of the dispersion strengthening relative strength formed by Mn. Micro-alloying elements Er and Zr are added in a compound way, and submicron/nanometer Al is formed in the homogenization process 3 The (Er, zr) composite precipitated phase has the purposes of directly causing precipitation strengthening and inhibiting recrystallization nucleation and grain growth in the extrusion process, promoting precipitation in the time of artificial aging and achieving comprehensive balance strength, corrosion resistance and fatigue performance. The invention designs a two-stage homogenization process system, and realizes the first-stage homogenization of, for example, al 3 (Er，Zr)、Al 6 Precipitation of Mn-like dispersed phases, second-stage homogenization achieving, for example, mg 2 The re-dissolution of Si, Q, and the like, and the intermittent morphology transformation of e.g. AlFeMnSi insoluble phases. The high-temperature high-speed extrusion process is realized by improving the heating temperature of the cast ingot, the extrusion speed and the quenching temperature, so that a more sufficient solid solution effect is achieved. And a reasonable aging process is adopted to realize that the strength of the alloy material reaches a peak value.
In example 13, the temperature of the first-stage homogenized ingot was 270℃and Al was formed 3 (Er，Zr)、Al 6 The Mn amount is less, so that the mechanical property, the peeling corrosion resistance and the fatigue property of the alloy material are reduced, but the alloy material is still superior to the existing 6-series alloy.
In the embodiment 14, the temperature of the cast ingot is 560 ℃, the material temperature is higher in the whole extrusion process, the surface quality of the extruded profile is poorer, the surface coarse grain layer is thicker, and the grains of the coarse grain layer are coarse, so that the mechanical property, the peeling corrosion resistance and the fatigue performance of the alloy material are reduced, but the alloy material is still superior to the existing 6-series alloy.
In example 15, the mold temperature was 430 ℃, the mold temperature was lower, the surface of the product was uneven, defects were increased, and at the same time, the mold abrasion was increased, the energy consumption was increased, and the production was unfavorable for the factory, so that the mechanical properties, the spalling corrosion resistance and the fatigue properties of the alloy material were reduced, but the alloy material was still superior to the existing 6-series alloy.
In example 16, the mold temperature was 470 ℃, and the mold temperature was too high, which resulted in defects of unsmooth surface, deformation, occurrence of weld lines or bubbles, etc., so that the mechanical properties, spalling corrosion resistance and fatigue properties of the alloy material were reduced, but the alloy material was still superior to the existing 6-series alloy.
In the embodiment 17, the pre-ageing temperature is 160 ℃, the time is 5 hours, the ageing temperature is lower, the time is shorter, the quantity of Mg and Si precipitated is insufficient, the content of the precipitated beta' strengthening phase is less, the mechanical property and the fatigue property of the alloy material are reduced, and the alloy material is still superior to the existing 6-series alloy.
In example 18, the first homogenization stage was performed for a short period of time, and Al was formed during the first homogenization stage 3 (Er，Zr)、Al 6 The Mn content is lower, so that the mechanical property, the peeling corrosion resistance and the fatigue property of the alloy material are reduced, but the alloy material is still superior to the existing 6-series alloy.
The technological route of the invention is on-line quenching, the full solid solution is realized in the extrusion process, the heating temperature of the cast ingot in the embodiment 19 is lower, the temperature of the alloy material in the whole extrusion process is lower, the solid solution degree is poorer, the mechanical property and fatigue property of the alloy material are lower, and the alloy material is still better than the existing 6-series alloy.
The extrusion process can generate a large amount of heat energy, the higher the extrusion speed is, the higher the temperature of the profile in the extrusion process is, the lower the extrusion speed of the profile in the embodiment 20 is, the lower the temperature of the profile in the extrusion process is, the worse the solid solution degree is, so that the mechanical property and fatigue property of the alloy material are lower, but the alloy material is still superior to the existing 6-series alloy.
The section bar in the embodiment 21 has lower quenching temperature and poorer solid solution degree, so that the mechanical property and fatigue property of the alloy material are lower, but are still better than those of the prior 6-series alloy.
The aging temperature of the profile in example 22 is lower, the precipitation strengthening effect is weakened, so that the mechanical property and fatigue property of the alloy material are lower, but are still better than those of the existing 6-series alloy.
It should be noted that the terms "first," "second," and the like in the description and in the claims of the present application are used for distinguishing between similar objects and not necessarily for describing a particular sequential or chronological order. It is to be understood that the terms so used are interchangeable under appropriate circumstances such that the embodiments of the application described herein are, for example, capable of operation in sequences other than those described herein.
The above description is only of the preferred embodiments of the present invention and is not intended to limit the present invention, but various modifications and variations can be made to the present invention by those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (7)
1. The preparation method of the aluminum alloy is characterized by comprising the following steps of:
the raw materials are prepared according to the following components: the aluminum alloy section consists of the following components in percentage by weight: 0.70 to 1.10 percent of Mg, 0.70 to 1.10 percent of Si, 0.50 to 0.80 percent of Cu, 0.20 to 0.80 percent of Mn, less than or equal to 0.40 percent of Fe, 0.10 to 0.15 percent of Er, 0.10 to 0.15 percent of Zr, less than or equal to 0.15 percent of total unavoidable impurities, less than or equal to 0.05 percent of each unavoidable impurity, and the balance of Al;
sequentially carrying out casting, double-stage homogenization treatment, sawing, turning, hot extrusion, on-line quenching, straightening and ageing treatment on the raw materials to obtain the aluminum alloy;
and obtaining an alloy cast ingot through the casting step, wherein the two-stage homogenization treatment process comprises the following steps of: heating the alloy ingot to 280-320 ℃ and preserving heat for 8-10 h, then continuously heating to 545-565 ℃ and preserving heat for 16-24 h, and air-cooling to room temperature to obtain a homogenized ingot; or heating the alloy cast ingot to 380-420 ℃ at a heating rate of 25 ℃/h, preserving heat for 8-10 h, continuously heating to 545-565 ℃ at a heating rate of 25 ℃/h, preserving heat for 16-24 h, and air-cooling to room temperature to obtain a homogenized cast ingot;
and after the ingot casting subjected to homogenization treatment is subjected to sawing and wagon treatment in sequence, a wagon ingot casting is obtained, and the hot extrusion process comprises the following steps:
heating the wagon ingot to 510-550 ℃ and then carrying out extrusion molding to obtain a section bar;
in the extrusion molding process, the temperature of the die and the temperature of the extrusion cylinder are 440-460 ℃, the extrusion speed of the profile is 5.1-7.2 m/min, and the extrusion ratio is 26.5-42.8.
2. The method according to claim 1, wherein the weight ratio of Mg to Si element in the composition of the aluminum alloy profile is (0.74-1.83): 1.
3. The method for preparing aluminum alloy according to claim 1, wherein in the on-line quenching process, the quenching temperature of the profile is 480-530 ℃, and the quenching mode is through water cooling.
4. The method for producing an aluminum alloy according to claim 3, wherein the straightening treatment process is a stretching and straightening process for a quenched profile obtained by the on-line quenching, and the stretching amount in the stretching and straightening process is 0.5 to 1.5%.
5. The method of producing an aluminum alloy according to claim 1, wherein the aging treatment process is artificial aging.
6. An aluminum alloy profile, characterized in that the aluminum alloy profile is produced by the production method according to any one of claims 1 to 5, and the tensile strength of the aluminum alloy profile is not less than 400MPa, and the flaking corrosion resistance is not less than EA level, where r=0.1, k t =1, f=10-200 Hz, cycle number 1.0x10 7 The fatigue strength under the test condition is more than or equal to 200MPa.
7. An application of the aluminum alloy section bar in the fields of ship industry and ocean engineering equipment.
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| JPH11323472A (en) * | 1998-05-12 | 1999-11-26 | Sumitomo Light Metal Ind Ltd | Al-mg-si alloy extrusion material excellent in machinability and its production |
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| CN112941377A (en) * | 2021-01-28 | 2021-06-11 | 北京工业大学 | Er-containing cast heat-resistant Al-Si-Cu-Mg alloy |
| CN114058885A (en) * | 2021-11-16 | 2022-02-18 | 中铝材料应用研究院有限公司 | 6XXX series aluminum alloy plate and preparation method and welding method thereof |
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| JPH11323472A (en) * | 1998-05-12 | 1999-11-26 | Sumitomo Light Metal Ind Ltd | Al-mg-si alloy extrusion material excellent in machinability and its production |
| JP2019151918A (en) * | 2018-03-05 | 2019-09-12 | 昭和電工株式会社 | Al-Mg-Si-BASED ALUMINUM ALLOY HOLLOW EXTRUSION MATERIAL AND MANUFACTURING METHOD THEREFOR |
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