CN115466888B - High-strength low-quenching-sensitivity aluminum alloy and preparation method of aluminum alloy and aluminum alloy profile - Google Patents
High-strength low-quenching-sensitivity aluminum alloy and preparation method of aluminum alloy and aluminum alloy profile Download PDFInfo
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- 238000002360 preparation method Methods 0.000 title claims abstract description 23
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- 238000010791 quenching Methods 0.000 claims abstract description 32
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- 238000010438 heat treatment Methods 0.000 claims abstract description 27
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- 238000000137 annealing Methods 0.000 claims abstract description 14
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- 239000002994 raw material Substances 0.000 claims abstract description 12
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- 238000007670 refining Methods 0.000 claims abstract description 6
- 238000002844 melting Methods 0.000 claims abstract description 4
- 230000008018 melting Effects 0.000 claims abstract description 4
- 238000001125 extrusion Methods 0.000 claims description 19
- 229910052782 aluminium Inorganic materials 0.000 claims description 14
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 14
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- 238000000034 method Methods 0.000 claims description 9
- 229910052804 chromium Inorganic materials 0.000 claims description 8
- 229910052749 magnesium Inorganic materials 0.000 claims description 8
- 238000004321 preservation Methods 0.000 claims description 8
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 230000000694 effects Effects 0.000 abstract description 8
- 239000000956 alloy Substances 0.000 description 28
- 229910045601 alloy Inorganic materials 0.000 description 26
- 230000000052 comparative effect Effects 0.000 description 23
- 239000011777 magnesium Substances 0.000 description 15
- 239000000203 mixture Substances 0.000 description 8
- 239000000463 material Substances 0.000 description 7
- 230000008569 process Effects 0.000 description 6
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- 238000005728 strengthening Methods 0.000 description 6
- 238000000265 homogenisation Methods 0.000 description 5
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- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 3
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- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
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- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
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- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- 229910017639 MgSi Inorganic materials 0.000 description 1
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- 230000004913 activation Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- -1 aluminum titanium boron Chemical compound 0.000 description 1
- 239000010407 anodic oxide Substances 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
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- 238000009864 tensile test Methods 0.000 description 1
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
- C21D9/085—Cooling or quenching
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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
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- 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
- C22C21/04—Modified aluminium-silicon alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—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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Abstract
A high-strength low-quenching-sensitivity aluminum alloy comprises ：Si 0.55~0.95%;Mg 0.75~1.30%;Cu 0.3~1.1%;Mn 0.05~0.15%;Cr 0.05~0.15%;Fe≤0.15%;Ti≤0.05%;Zn≤0.02%;Zr 0.05~0.15%;Er 0~0.45%;Sr 0~0.1%; the balance of Al. The preparation method comprises the following steps: 1. proportioning according to the mass percentage of each component to obtain raw materials; 2. melting and refining raw materials to obtain an aluminum alloy melt; 3. casting the aluminum alloy melt to obtain an ingot semi-finished product; 4. and carrying out homogenizing annealing and cooling on the ingot semi-finished product to obtain an ingot of the aluminum alloy. The preparation method of the profile comprises the following steps: 1. heating, extruding and online air-cooling quenching the cast ingot to obtain a semi-finished product of the section bar; 2. and (3) artificially aging the semi-finished product of the profile to obtain the aluminum alloy profile with high strength and low quenching sensitivity. The aluminum alloy can realize high-strength quenching sensitivity under the air-cooled quenching condition, and has outstanding technical effects.
Description
Technical Field
The invention relates to the technical field of nonferrous metals, in particular to a high-strength low-quenching-sensitivity aluminum alloy and a preparation method of the aluminum alloy and an aluminum alloy profile.
Background
The aluminum alloy has the advantages of high strength, light weight, good heat dissipation, strong corrosion resistance, long service life, easy recovery and the like, and is widely applied to various fields of aerospace, transportation, climbing ladders, home, buildings, photovoltaics and the like.
In recent years, with the increasing call for lightweight concepts, aluminum and aluminum alloys are increasingly used in aspects of people's life. The application range of the 6-series Al-Mg-Si alloy is the widest, however, the 6-series aluminum alloy in the national standard is mostly medium strength, and the tensile strength is less than 300MPa (such as 6063, 6061, 6082 and the like), so that the application range is limited. Although the high-strength 2-series, 5-series and 7-series aluminum alloy materials have excellent mechanical properties, the application of the materials in a plurality of fields is limited due to the influences of factors such as poor corrosion resistance, poor oxidation coloring performance, high production cost and the like.
In recent years, some scientific research institutions and enterprises at home and abroad also develop some high-strength 6-series aluminum alloys, for example, chinese patent CN 111647780A discloses a high-strength 6-series aluminum alloy, a preparation method and application thereof, the alloying degree of the alloy is higher, and the requirement can be met only by using high-strength water quenching or off-line quenching after extrusion; also, as disclosed in Chinese patent CN110373583A, an aluminum alloy with high quality and high oxidation effect and a preparation method thereof are disclosed, and online water passing quenching is also required. The aluminum alloy materials disclosed in the two patents have higher quenching sensitivity, and can realize better performance and effect on the premise that the wall thickness of the profile is more than 3mm, however, for some high-precision profiles with thinner wall thickness (such as the wall thickness of less than 1.5 mm), the profile can only be quenched by air cooling after extrusion, because uneven distribution of residual stress generated during quenching can be caused when the cooling strength is too high during online water cooling and offline quenching, the profile deformation such as flatness and bending and twisting in the length direction can be caused, and the use requirements of products can not be met.
Therefore, the development of a 6-series alloy with high strength and low quenching sensitivity, which can be realized under the air-cooled quenching condition, has important significance.
Disclosure of Invention
The invention aims to provide a high-strength low-quenching-sensitivity aluminum alloy and a preparation method of the aluminum alloy and an aluminum alloy profile.
In order to achieve the purpose, the invention adopts the technical scheme that:
The high-strength low-quenching-sensitivity aluminum alloy comprises the following components in percentage by mass:
Si 0.55～0.95％；
Mg 0.75～1.30％；
Cu 0.3～1.1％；
Mn 0.05～0.15％；
Cr 0.05～0.15％；
Fe ≤0.15％；
Ti 0.02～0.05％；
Zn ≤0.02％；
Zr 0.05～0.15％；
Er 0～0.45％；
Sr 0～0.1％；
The balance being Al.
1. The preferable scheme comprises the combination of two or three of Zr, er and Sr, and the total amount after the combination is between 0.2 and 0.4 percent.
2. In a preferred scheme, the mass ratio of Mg to Si is (1.115-1.67): 1.
3. In a preferred embodiment, the total amount of Mg and Si is 1.4 to 2.1%.
4. In a preferred embodiment, the total amount of Mn and Cr is less than or equal to 0.2%.
5. The preferable scheme comprises the following components in percentage by mass:
Si 0.61～0.85％；
Mg 0.85～1.24％；
Cu 0.63～1.05％；
Mn 0.05～0.1％；
Cr 0.05～0.12％；
Fe ≤0.13％；
Ti 0.02～0.05％；
Zn ≤0.015％；
Zr 0.05～0.13％；
Er 0.15～0.25％；
Sr 0.01～0.05％；
The balance being Al.
6. In a preferred embodiment, the content of the single impurity element is less than or equal to 0.05%.
In order to achieve the purpose, the technical scheme adopted in the process level of the invention is as follows:
a preparation method of a high-strength low-quenching-sensitivity aluminum alloy comprises the following steps:
step one, batching according to the mass percentage of each component to obtain raw materials;
step two, melting and refining the raw materials to obtain an aluminum alloy melt;
Step three, casting the aluminum alloy melt to obtain an aluminum alloy ingot semi-finished product;
and step four, carrying out homogenizing annealing and cooling on the aluminum alloy ingot semi-finished product to obtain an aluminum alloy ingot.
1. In the preferred scheme, in the second step, firstly, the raw materials are melted, stirred, refined, slag removed and stood to obtain an aluminum alloy intermediate melt;
then, adding a grain refiner into the aluminum alloy intermediate melt, and then carrying out online degassing and filtering on the aluminum alloy intermediate melt to obtain the aluminum alloy melt.
2. In the preferred scheme, in the step three, the aluminum alloy melt is transferred to a semi-continuous casting machine through a launder for casting, and the aluminum alloy ingot semi-finished product is obtained.
3. In the fourth step, the homogenization treatment is carried out by adopting three-stage homogenization treatment, wherein the first-stage heating temperature is 380-460 ℃, and the temperature is kept for 1-5 h; the second-stage heating temperature is 500-545 ℃, and the temperature is kept for 1-5 h; the third stage heating temperature is 550-580 ℃, and the temperature is kept for 4-10 h.
4. In the preferred scheme, in the fourth step, cooling is carried out by adopting a mode of air cooling and water cooling, cooling is carried out to below 100 ℃, the cooling rate is not less than 300 ℃/h, and then natural cooling is carried out to room temperature.
5. Preferably, the ingot of the aluminum alloy is a round ingot, but is not limited to this shape.
In order to achieve the above purpose, the invention adopts another technical scheme in the technical layer that:
A preparation method of a high-strength low-quenching-sensitivity aluminum alloy section comprises the following steps:
Heating, extruding and online air-cooling quenching an aluminum alloy ingot to obtain an aluminum profile semi-finished product;
And step two, performing artificial aging treatment on the semi-finished product of the aluminum profile to obtain the aluminum alloy profile with high strength and low quenching sensitivity.
1. In the preferred scheme, in the first step, the heating temperature of the cast ingot of the aluminum alloy is 470-510 ℃, the extrusion speed is 3.0-3.5 mm/s, the outlet temperature of the extruded front beam is more than or equal to 525 ℃, the online quenching adopts strong wind cooling quenching, and the cooling rate from extrusion to cooling to 250 ℃ of the profile is more than or equal to 6 ℃/s.
2. In the second step, the temperature of the artificial aging treatment is 155-185 ℃ and the heat preservation time is 6-15 h.
In conclusion, the invention obtains the 6-series aluminum alloy with high strength and low quenching sensitivity through reasonable alloy component proportion and microalloying by using transition elements and rare earth elements, and solves the problem that the traditional 6-series aluminum alloy cannot produce high-precision products due to insufficient strength or air cooling cannot reach the optimal quenching effect.
Compared with the prior art, the invention has the following advantages and effects:
1. the invention reasonably designs and controls the ratio of Mg to Si in the alloy components to be (1.15-1.67): 1, by making the Si relatively excessive, it can be ensured that after Si preferentially forms Al-Fe-Si phase with unavoidable Fe impurities in the melt, enough Si atoms remain to form Mg 2Si(β)、Mg5Si6 (beta') strengthening phase, so that the final phase composition of the alloy falls in the three-phase region of alpha (Al) +Mg 2 Si+Si, and the strength of the aluminum alloy has a maximum value.
2. The invention can promote the transformation of needle-shaped beta (AlFeSi) phase to spherical alpha- (AlFe (Mn/Cr) Si) phase in the casting structure in the homogenizing annealing process by strictly controlling the addition amount of Mn and Cr elements, and can improve the recrystallization temperature of the aluminum alloy and inhibit the occurrence of recrystallization.
3. According to the invention, the addition amount of Mn and Cr elements is controlled below 0.2%, and Zr element and Er element are added simultaneously, so that the Zr element and Er element can form an Al 3 Zr phase and an Al 3 Er phase with Al, on one hand, the problem of quenching sensitivity increase caused by the addition of Mn and Cr can be avoided, and on the other hand, the effects of improving the recrystallization temperature and inhibiting recrystallization can be achieved when the total amount of Mn and Cr elements is controlled, as shown in figure 1.
4. According to the invention, by controlling the addition amount of Cu, cu exists in a solid solution form after the Al-Mg-Si alloy is homogenized, and is separated out in a dispersed Q' phase or Q phase in the subsequent artificial aging process, so that the heat treatment strengthening performance of the alloy can be remarkably improved. However, too high Cu content can cause the anodic oxide film of the profile to turn yellow, and simultaneously, the corrosion resistance of the material is reduced due to Cu-containing phases continuously precipitated at the grain boundary during peak aging. Therefore, the invention controls the addition amount of Cu to be 0.3-1.1%, which not only maintains the anodic oxidation performance, but also does not obviously reduce the corrosion resistance.
5. The morphology of the Fe-containing phase can be changed in the ingot homogenization process by adding Sr, so that the acicular beta (AlFeSi) phase is promoted to be converted into the spherical alpha (AlFeSi) phase (see figure 2), and the precipitation activation energy of the beta' phase can be reduced by Sr in the aging process, so that the strengthening phase is finer and dispersed.
6. The invention adopts three-stage homogenization treatment when carrying out homogenization annealing on the semi-finished product of the aluminum alloy ingot, the first-stage heating temperature is 380-460 ℃, and the temperature is kept for 1-5 hours, so that the low-melting-point phase is fully dissolved back, and the dispersed phases such as Al 3Zr、Al3 Er and the like are evenly separated out; the second-stage heating temperature is 500-545 ℃, and the temperature is kept for 1-5 hours, so that the Q phase is fully dissolved back; the third stage heating temperature is 550-580 ℃, and the temperature is kept for 4-10 hours, so that the coarse MgSi phase is fully dissolved back. And cooling the homogenized cast ingot by adopting a mode of air cooling and water cooling, cooling to below 100 ℃, cooling at a cooling rate of not less than 300 ℃/h, and naturally cooling to room temperature. The method has the function of ensuring that the cast ingot is a supersaturated solid solution and coarse Mg 2 Si particles cannot be separated out, so that the cast ingot can be completely dissolved back again in the subsequent extrusion process, and the mechanical property is ensured.
7. The main technological parameters of the extrusion production of the thin-wall aluminum profile are that the heating temperature is 470-510 ℃, the extrusion speed is 3.0-3.5 mm/s, the outlet temperature of the extruded front beam is more than or equal to 525 ℃, the online quenching adopts strong wind cooling quenching, and the cooling rate from extrusion to cooling to 250 ℃ of the profile is more than or equal to 6 ℃/s.
8. The alloy is subjected to artificial aging treatment after extrusion, and a nano-level needle-shaped Mg 2 Si phase which is distributed in a tiny and dispersed way is separated out, so that a precipitation strengthening effect is generated. The artificial aging process parameters of the alloy are 155-185 ℃, and the temperature is kept for 6-15 hours, so that the material has better plasticity while ensuring the strength.
Drawings
FIG. 1 is a back-scattered electron scanning microstructure of an aluminum alloy ingot according to the present invention;
FIG. 2 is a microstructure of the aluminum alloy section of the present invention.
Detailed Description
The present invention will be described in detail with reference to the drawings, wherein modifications and variations are possible in light of the teachings of the present invention, without departing from the spirit and scope of the present invention, as will be apparent to those of skill in the art upon understanding the embodiments of the present invention.
The terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the present disclosure.
The term (terms) as used herein generally has the ordinary meaning of each term as used in this field, in this disclosure, and in the special context, unless otherwise noted. Certain terms used to describe the present disclosure are discussed below, or elsewhere in this specification, to provide additional guidance to those skilled in the art in connection with the description herein.
Example 1:
the alloy compositions of this example are shown in table 1, and the raw materials include:
Aluminum ingot: the aluminum ingot with the mark of Al99.7 which accords with GB/T1196-2008 is adopted, and the mass percentage of Al in the ingot is not less than 99.7 percent.
Magnesium ingot: adopts magnesium ingots with the brand name of Mg9990 which conform to GB/T3499-2003, and the mass percent of Mg in the magnesium ingots is not less than 99.9 percent.
Intermediate alloy: aluminum-based master alloys with the designations AlSi20, alCu50, alMn10, alCr2, alZr4, alSr10, alEr which are in accordance with YS/T282-2000 are used.
Smelting, casting and extruding the raw materials to obtain the aluminum alloy section of the embodiment 1, wherein the specific steps and parameters are as follows:
The raw materials are put into a tilting type smelting heat preservation furnace according to a proportion, natural gas is adopted as the raw material, after the raw material is heated to 740 ℃ for melting, an aluminum alloy refining agent is added into the melt for refining for 30min, high-purity argon (99.999%) is used as refining gas for stirring, exhausting and then slagging off the melt, after temperature adjustment is carried out, the melt is kept stand for 30-40 min, and an aluminum alloy intermediate melt is obtained;
Step (2) adding a high-Grade (Grade A) aluminum titanium boron grain refiner into a launder in the process of launder transfer, and then sequentially passing through an online degassing and filtering device, wherein the filtering device uses a 40+60PPI double-stage ceramic foam filter plate to obtain an aluminum alloy melt;
step (3) carrying out semi-continuous casting on the aluminum alloy melt at 730 ℃, wherein a casting machine adopts an oil-gas slip crystallizer, and controls the surface quality of an ingot and the metallurgical quality of a casting rod to obtain an aluminum alloy ingot semi-finished product;
performing three-stage homogenizing annealing on the aluminum alloy ingot semi-finished product, wherein the first-stage heating temperature is 390 ℃, the heat preservation is performed for 4 hours, the second-stage heating temperature is 500 ℃, the heat preservation is performed for 5 hours, the third-stage heating temperature is 560 ℃, the heat preservation is performed for 10 hours, the homogenized ingot is cooled to below 100 ℃ at a cooling rate of 500 ℃/h in a mode of air cooling and then water cooling, and then naturally cooling to room temperature to obtain an aluminum alloy ingot;
Step (5) heating an aluminum alloy cast ingot to 475 ℃, extruding a thin-wall square tube (with the wall thickness of 1.3 mm), wherein the extrusion ratio is 41, the extrusion speed is 3.5mm/s, the temperature of an extruded front beam outlet section is 527 ℃, the extruded section is subjected to online strong wind cooling to below 250 ℃, and then naturally cooled to room temperature to obtain an aluminum section semi-finished product, wherein the cooling speed of a section cooled to 250 ℃ is 7.8 ℃/s;
And (6) carrying out artificial aging treatment on the aluminum profile semi-finished product, wherein the aging system is 155 ℃, and the heat preservation is carried out for 12 hours, so that the aluminum alloy profile of the embodiment 1 can be finally obtained.
Example 2:
the alloy compositions of this example are shown in table 1, and the preparation method of the aluminum alloy section bar of this example is different from that of example 1 in that:
When three-stage homogenizing annealing is carried out on the aluminum alloy ingot semi-finished product in the step (4), the heating temperature is 425 ℃ in the first stage, the heat is preserved for 3 hours, the temperature is 520 ℃ in the second stage, the heat is preserved for 4 hours, the temperature is 570 ℃ in the third stage, the heat is preserved for 8 hours, the homogenized ingot is cooled to 100 ℃ at a cooling speed of 400 ℃/h in a mode of air cooling and then water cooling, and then the ingot is naturally cooled to room temperature, so that the aluminum alloy ingot is obtained;
heating an aluminum alloy cast ingot to 490 ℃ in the step (5), extruding a thin-wall square tube, wherein the extrusion ratio is 41, the extrusion speed is 3.2mm/s, the temperature of an extruded front beam outlet profile is 532 ℃, and naturally cooling the extruded profile to room temperature after on-line strong wind cooling to below 250 ℃ to obtain an aluminum profile semi-finished product, wherein the cooling speed of a section cooled to 250 ℃ is 9.7 ℃/s;
and (3) the aging system in the step (6) is 170 ℃, and the temperature is kept for 8 hours.
The starting materials and the remaining preparation steps of this example 2 were the same as in example 1.
Example 3:
the alloy compositions of this example are shown in table 1, and the preparation method of the aluminum alloy section bar of this example is different from that of example 1 in that:
When three-stage homogenizing annealing is carried out on the aluminum alloy ingot semi-finished product in the step (4), the heating temperature is 460 ℃ in the first stage, the heat is preserved for 2 hours, the temperature is 545 ℃ in the second stage, the heat is preserved for 3 hours, the temperature is 580 ℃ in the third stage, the homogenized ingot is cooled to 100 ℃ at the cooling speed of 300 ℃/h in a mode of air cooling and then water cooling, and then the ingot is naturally cooled to room temperature, so that the aluminum alloy ingot is obtained;
In the step (5), the cast ingot of the aluminum alloy is heated to 510 ℃ and then extruded into a thin-wall square tube, the extrusion ratio is 41, the extrusion speed is 3.0mm/s, the temperature of the extruded front beam outlet section is 535 ℃, the extruded section is cooled to below 250 ℃ by strong wind on line and then naturally cooled to room temperature, and the aluminum section semi-finished product is obtained, wherein the cooling speed of the section cooled to 250 ℃ is 10.3 ℃/s.
And (3) the aging system in the step (6) is 180 ℃, and the temperature is kept for 6 hours.
The starting materials and the remaining preparation steps of this example 3 were the same as in example 1.
Comparative example 1:
The comparative example is an industrial 6061 alloy, the alloy composition of which is shown in table 1. The preparation method of the aluminum alloy profile of the comparative example is different from that of example 1 in that:
In the step (4), single-stage homogenizing annealing is carried out on the semi-finished product of the aluminum alloy ingot, the heating temperature is 560 ℃, the heat preservation is carried out for 10 hours, the homogenized ingot is cooled to 100 ℃ at the cooling speed of 300 ℃/h in a mode of air cooling and then water cooling, and then the ingot is naturally cooled to room temperature, so that the ingot of the aluminum alloy is obtained;
In the step (5), the cast ingot of the aluminum alloy is heated to 480 ℃ and then extruded, the extrusion ratio is 41, the extrusion speed is 3.5mm/s, the temperature of the extruded front beam outlet profile is 530 ℃, the extruded profile is cooled to below 250 ℃ in strong wind on line and then naturally cooled to room temperature, and the semi-finished product of the aluminum profile is obtained, wherein the cooling speed of the section cooled to 250 ℃ is 9.6 ℃/s.
And (3) the aging system in the step (6) is 175 ℃, and the temperature is kept for 6 hours.
The starting materials and the remaining preparation steps of this comparative example 1 were the same as in example 1.
Comparative example 2:
The comparative example was an industrial 6082 alloy, the alloy composition of which is shown in table 1.
The starting materials and preparation procedure of this comparative example 2 were the same as in comparative example 1.
Comparative example 3:
The comparative example was an industrial 6082 alloy, the alloy composition of which is shown in table 1. The preparation method of the aluminum alloy profile of the comparative example is different from that of comparative example 1 in that:
in this comparative example, after the medium material was extruded in the step (5), an on-line water-cooling quenching was performed at a cooling rate of 18.6 ℃/s in a range of cooling to 250 ℃.
The starting material and the remaining preparation steps of this comparative example 3 were the same as those of comparative example 1.
Table 1 alloy chemical composition table (wt.%)
| Numbering device | Si | Mg | Cu | Mn | Cr | Fe | Ti | Zn | Zr | Er | Sr | Impurity(s) | Allowance of |
| Example 1 | 0.61 | 0.85 | 0.63 | 0.05 | 0.05 | 0.12 | 0.02 | 0.013 | 0.05 | 0.15 | 0.03 | 0.012 | Al |
| Example 2 | 0.85 | 0.98 | 0.7 | 0.05 | 0.12 | 0.13 | 0.02 | 0.011 | 0.1 | 0.25 | 0.01 | 0.009 | Al |
| Example 3 | 0.84 | 1.24 | 1.05 | 0.1 | 0.05 | 0.13 | 0.02 | 0.015 | 0.13 | 0.15 | 0.05 | 0.011 | Al |
| Comparative example 1 | 0.67 | 0.92 | 0.23 | 0.08 | 0.05 | 0.17 | 0.02 | 0.016 | - | - | - | 0.016 | Al |
| Comparative example 2 | 1.02 | 0.88 | 0.03 | 0.52 | 0.09 | 0.13 | 0.02 | 0.013 | - | - | - | 0.014 | Al |
| Comparative example 3 | 1.02 | 0.88 | 0.03 | 0.52 | 0.09 | 0.13 | 0.02 | 0.013 | - | - | - | 0.014 | Al |
The aluminum alloy profile products obtained in the above examples 1 to 3 and comparative examples 1 to 3 were subjected to the metal material tensile test part 1 according to GB/T228.1-2021: room temperature test method mechanical properties of the product were tested and the deformation of the profile was checked, the test results are shown in table 2, wherein Rm represents tensile strength (MPa), rp0.2 represents yield strength (MPa), i.e. strength at a non-proportional elongation of 0.2%, and a50 represents elongation after break (%), i.e. elongation at a gauge length of 50 mm.
TABLE 2
According to the test and detection results in Table 2, the mechanical properties of the alloy disclosed by the invention are far better than those of 6-series aluminum alloy in national standard, so that the alloy disclosed by the invention has lower quenching sensitivity, good solute effect of solute atoms can be realized under the condition of strong air cooling, the precipitation strengthening effect is maximized by matching with a reasonable aging system, the residual stress of the material is smaller under the condition of strong air cooling, higher precision can be kept, the requirements that the plane gap is smaller than 0.2mm and the twisting degree is smaller than 0.5mm/m are met (see fig. 1 and 2), and the alloy quenching sensitivity is reduced under the microalloying action of Zr, er and Sr, and meanwhile, the optimized Mg, si and Cu ratio ensures that the material has higher strength. In comparative example 1, the quenching sensitivity was reduced by optimizing and reducing the Mn and Cr contents, but the recrystallization temperature was lowered to coarsen the crystal grains, and the number of the strengthening phases of the Q' phase was inferior to that of the present invention, so that the performance was slightly inferior. Comparative examples 2 and 3 are 6082 alloys, the alloy components form Al 6 Mn phase due to the existence of Mn, al 6 Mn can fix grain boundaries to play a role in inhibiting recrystallization, however, mg 2 Si phase and Mg 5Si6 phase can be preferentially attached to Al 6 Mn phase to form nuclei, so that quenching sensitivity is increased, and the strength of comparative example 3 is higher than that of comparative example 2, however, residual stress generated when thin walls are formed into water cooling can deform materials, such as flatness, bending in the length direction and twisting, and the use requirements of products cannot be met.
In summary, the invention prepares the 6-series alloy with high strength and low quenching sensitivity which can be realized under the air cooling quenching condition by adjusting the Mg/Si ratio, controlling the total amount of Mg and Si, the total amount of Mn and Cr and carrying out microalloying by using transition elements and rare earth elements and reasonably setting the control of the technological process and the parameters thereof.
The above embodiments are provided to illustrate the technical concept and features of the present invention and are intended to enable those skilled in the art to understand the content of the present invention and implement the same, and are not intended to limit the scope of the present invention. All equivalent changes or modifications made in accordance with the spirit of the present invention should be construed to be included in the scope of the present invention.
Claims (4)
1. A high-strength low-quenching-sensitivity aluminum alloy is characterized in that: comprises the following components in percentage by mass:
Si 0.55~0.95%；
Mg 0.75~1.30%；
Cu 0.3~1.1%；
Mn 0.05~0.15%；
Cr 0.05~0.15%；
Fe ≤0.15%；
Ti 0.02~0.05%；
Zn ≤0.02%；
Zr 0.05~0.15%；
Er 0~0.45%；
Sr 0~0.1%；
The balance of Al;
The mass ratio of Mg to Si is (1.115-1.67): 1, a step of;
The total amount of Mg and Si is 1.4-2.1%;
The total amount of Mn and Cr is less than or equal to 0.2 percent;
comprises the combination of two or three of Zr, er and Sr, and the total amount after the combination is 0.2-0.4 percent;
The aluminum alloy is obtained after homogenizing annealing and cooling, wherein the homogenizing annealing adopts three-stage homogenizing treatment, the first-stage heating temperature is 380-460 ℃, and the temperature is kept for 1-5 hours; the second-stage heating temperature is 500-545 ℃, and the temperature is kept for 1-5 h; the third-stage heating temperature is 550-580 ℃, and the temperature is kept for 4-10 h;
And after homogenizing annealing, cooling by adopting a mode of air cooling and water cooling, cooling to below 100 ℃, wherein the cooling rate is not less than 300 ℃/h, and then naturally cooling to room temperature.
2. The high strength low quench sensitivity aluminum alloy of claim 1, wherein:
Comprises the following components in percentage by mass:
Si 0.61~0.85%；
Mg 0.85~1.24%；
Cu 0.63~1.05%；
Mn 0.05~0.1%；
Cr 0.05~0.12%；
Fe ≤0.13%；
Ti 0.02~0.05%；
Zn ≤0.015%；
Zr 0.05~0.13%；
Er 0.15~0.25%；
Sr 0.01~0.05%；
The balance being Al.
3. A preparation method of high-strength low-quenching-sensitivity aluminum alloy is characterized by comprising the following steps: the method for preparing the high-strength low-quenching-sensitivity aluminum alloy according to any one of claims 1-2, comprising the following steps:
step one, batching according to the mass percentage of each component to obtain raw materials;
step two, melting and refining the raw materials to obtain an aluminum alloy melt;
Step three, casting the aluminum alloy melt to obtain an aluminum alloy ingot semi-finished product;
Step four, carrying out homogenizing annealing and cooling on the aluminum alloy ingot semi-finished product to obtain an aluminum alloy ingot, wherein the homogenizing annealing adopts three-stage homogenizing treatment, the first-stage heating temperature is 380-460 ℃, and the temperature is kept for 1-5 h; the second-stage heating temperature is 500-545 ℃, and the temperature is kept for 1-5 h; the third-stage heating temperature is 550-580 ℃, and the temperature is kept for 4-10 h;
And after homogenizing annealing, cooling by adopting a mode of air cooling and water cooling, cooling to below 100 ℃, wherein the cooling rate is not less than 300 ℃/h, and then naturally cooling to room temperature.
4. A preparation method of a high-strength low-quenching-sensitivity aluminum alloy section bar is characterized by comprising the following steps of: preparation by the aluminum alloy of claim 3, the preparation method comprising:
heating, extruding and online air-cooling quenching an aluminum alloy ingot to obtain an aluminum profile semi-finished product; the heating temperature of the cast ingot of the aluminum alloy is 470-510 ℃, the extrusion speed is 3.0-3.5 mm/s, the outlet temperature of the extruded front beam is more than or equal to 525 ℃, the online quenching adopts strong wind cooling quenching, and the cooling rate from extrusion to cooling to 250 ℃ of the profile is more than or equal to 6 ℃/s and less than or equal to 10.3 ℃/s;
And secondly, carrying out artificial aging treatment on the aluminum profile semi-finished product to obtain the aluminum alloy profile with high strength and low quenching sensitivity, wherein the temperature of the artificial aging treatment is 155-185 ℃, and the heat preservation time is 6-15 h.
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