CN110735073A - high-quality 6-series aluminum alloy extruded casting blank and preparation method thereof - Google Patents
high-quality 6-series aluminum alloy extruded casting blank and preparation method thereof Download PDFInfo
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- CN110735073A CN110735073A CN201911068057.4A CN201911068057A CN110735073A CN 110735073 A CN110735073 A CN 110735073A CN 201911068057 A CN201911068057 A CN 201911068057A CN 110735073 A CN110735073 A CN 110735073A
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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
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C23/00—Extruding metal; Impact extrusion
- B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
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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
- C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
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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
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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
Abstract
Compared with the traditional homogenized casting blank in actual production, the casting blank prepared by the scheme of the invention has the advantages that a large number of dispersed precipitation phases with micron sizes are distributed in a matrix, the structure not only can effectively reduce the extrusion deformation resistance of the casting blank and improve the surface quality of an extruded product, but also can improve the online quenching solid solubility of the extruded product, and provides a good structure foundation for later aging treatment.
Description
Technical Field
The invention belongs to the field of aluminum alloy materials, and particularly relates to high-quality 6-series aluminum alloy extruded casting blanks and a preparation method thereof.
Background
As important members of wrought aluminum alloy, 6-series aluminum alloy is used as an extrusion in large quantity, and the structure of the aluminum alloy has a crucial influence on the extrusion process performance, the surface quality and the final mechanical property of a casting blank, namely if the homogenization subsequent cooling treatment causes excessive solid solution of alloy elements in an aluminum matrix, the remarkable solid solution strengthening effect causes higher hardness of the casting blank so as to be difficult to extrude and deform, and if the homogenization subsequent cooling treatment causes excessive precipitation of the alloy elements to form coarse Mg2The solid solution strengthening effect of the Si phase basically disappears, meanwhile, the strengthening effect of the coarse second phase is very limited, although the overall hardness of the ingot blank material is greatly reduced, the resistance of extrusion deformation is reduced, the coarse precipitated phases are difficult to quickly dissolve back in the extrusion process, a large amount of precipitated phases are remained after on-line quenching, and the precipitated phases cannot participate in precipitation strengthening in the later aging link. In addition, the presence of these coarse precipitates tends to produce surface quality defects during extrusion, and more seriously, these coarse precipitates also melt locally at higher extrusion temperatures to cause cracking. In actual production, the conventional cooling treatment effect is not ideal, and the casting blank subjected to homogenization heat treatment is often difficult to obtain timely cooling treatment, so that a large amount of coarsened Mg is precipitated from the casting ingot2Si, which cannot guarantee the final aging strength, excellent surface quality and high extrusion speed.
In the prior art, in order to solve the problem of slow cooling response, water mist is directly sprayed on a casting blank just discharged from a furnace after homogenization, and although the method can obtain the effect of rapid cooling, serious quenching stress can be caused, and even the casting blank deforms and cracks; the strength of the aluminum alloy is improved by respective corresponding schemes, but special requirements on the temperature reduction of the homogenized cast ingot are not made, and the single solid solution heat treatment is carried out for solving the problem of low solid solubility of the base body after thermal deformation, so that the energy consumption and the production cost are increased by the solid solution link; the method also adopts a three-stage cooling mode after the ingot casting is homogenized, and the aim of accelerating the cooling of the high-temperature ingot casting is expected to be achieved on the premise of not generating quenching stress and size deformation, however, the cooling strength of the adopted method is limited, and mass production data show that the size of precipitated phases in the matrix is still large and cannot be completely dissolved in the extrusion process, so that the aging strength of the final product still has a great promotion space.
In industrial production, an ideal solution is rarely provided for the problem of cooling after homogenization of large-size casting blanks, so that the significance of solving the problem of rapid cooling of large-size cast ingots in an industrial site is great, and Mg in homogenized casting blanks is effectively inhibited2The growth and coarsening of the Si precipitate phase become important problems to be solved.
Disclosure of Invention
The invention aims to provide a preparation method of high-quality 6-series aluminum alloy extruded billets, which can obtain high-quality extruded billets with excellent technological properties and guaranteed final mechanical properties, wherein the high quality means that:
1. the casting blank prepared by the scheme of the invention has micron-sized Mg dispersed in the matrix2The hardness of the Si precipitated phase is obviously reduced, and the extrusion deformation is facilitated;
2. avoiding the damage of the surface quality of the extruded part by the coarse precipitated phase;
3. the fine micron precipitated phase is quickly redissolved in the later stage of extrusion, and has very high solid solubility after on-line quenching; the aging strength in the later period is ensured.
In order to achieve the purpose, the invention adopts the following technical scheme:
the preparation method of high-quality 6-series aluminum alloy extruded casting blanks comprises the following steps of carrying out subsequent treatment on the 6-series aluminum alloy cast blanks after the homogenization treatment to obtain the high-quality 6-series aluminum alloy extruded casting blanks, wherein the subsequent treatment comprises primary cooling treatment, bath treatment and subsequent cooling treatment.
The invention discloses a preparation method of a high-quality 6-series aluminum alloy extruded casting blank, which is used for sequentially carrying out primary cooling treatment, dipping treatment and subsequent cooling treatment on a cast ingot after homogenization heating, and specifically comprises the following steps:
primary cooling treatment: after the 6 series aluminum alloy cast ingot subjected to the homogenization heat treatment is discharged from the furnace, cooling to the solid solubility line temperature of the 6 series aluminum alloy cast ingot at a set speed;
and (3) dipping treatment: carrying out immersion bath treatment on the 6-series aluminum alloy cast ingot subjected to primary cooling for set time and temperature;
and (4) performing subsequent cooling treatment, namely performing subsequent cooling treatment on the 6-series aluminum alloy ingot after the medium-temperature immersion bath is finished at a set speed.
In the invention, the preparation method of the high-quality 6-series aluminum alloy extruded casting blank mainly aims at cooling treatment after homogenization, does not relate to component blending of the alloy and homogenization temperature rise and heat preservation stages, and the homogenization temperature rise and heat preservation system is reasonable conventional heat treatment.
In the invention, the 6 series aluminum alloy is an aluminum alloy material with any grade with the following elements in percentage by mass: 0.3-1.3% of Si, 0-0.5% of Fe, 0-1.2% of Cu, 0-1.0% of Mn, 0.3-1.3% of Mg, 0-0.4% of Cr, 0-0.2% of Ni0, 0-1.0% of Zn, 0-0.2% of Ti, 0-0.1% of B, 0-0.2% of V, 0-0.3% of Zr, 0-0.2% of Sc, and the balance of aluminum and uncontrollable impurities.
In the invention, the solid solubility line temperature is the lowest temperature required by the solution treatment of the 6-series aluminum alloy cast ingot, and is determined according to different components, and the temperature reduction rate of the primary cooling treatment ranges from 1 to 5 ℃/min, preferably 3 ℃/min.
In the invention, the temperature range of the dipping bath treatment is 300-400 ℃, and the selected temperature can be a certain constant value in the temperature range or a variable value in the temperature range.
The method for the dipping treatment comprises the steps of salt bath treatment, oil bath treatment, other liquid medium dipping treatment and the like, wherein preferably, the dipping treatment adopts the salt bath treatment, and further steps of the preferable method adopt the nitrate salt bath treatment, and the salt bath method can quickly enable the temperature of the material to reach the temperature of the molten salt, so that the tissue transformation behavior of the material is enabled to be around the temperature of the salt bath, and the material is prevented from staying in other temperature ranges too much.
In the invention, the time of the dipping treatment is 5-30 minutes, preferably 15 minutes.
In the invention, the subsequent cooling treatment is that the 6-series aluminum alloy cast ingot after the dipping treatment is cooled to below 150 ℃ at a cooling rate of 2-10 ℃/min; preferably, the cooling rate is 5 deg.C/min. Cooling below 150 ℃ is a routine knowledge in the art, as long as it is below 150 ℃.
The invention creatively provides a step of homogenizing subsequent dipping bath treatment, overcomes the problem that the prior cooling technology is laggard, and has the beneficial effects that:
1. the heat exchange of the casting blank is carried out in a conduction mode in the post-treatment link, and the heat exchange efficiency is far higher than that of thermal radiation and thermal convection, so that compared with conventional cooling modes such as air cooling and the like, the treatment method disclosed by the invention can obtain a quick cooling effect, and avoids that the precipitated phase is thick due to overlong detention time of the casting blank at a high temperature stage of 500-400 ℃, so that the surface quality problem and extrusion cracks caused by the thick precipitated phase are avoided;
2. the temperature difference between the temperature (solid solubility line temperature) of the casting blank after primary cooling and the dipping bath treatment temperature is not more than 200 ℃, so that the rapid cooling is ensured, and simultaneously, larger quenching stress and size deformation are not generated;
3. the heat released by the casting blank in the bath tank can be collected and recycled, so that the aims of saving energy and reducing consumption are fulfilled;
4. the micron-sized precipitated phases reduce the hardness of the cast ingot, are beneficial to reducing the extrusion energy consumption in the early stage of extrusion and improve the extrusion speed. Along with the extrusion, the precipitated phase is gradually dissolved back in the later stage of extrusion, so that the quenching solid solubility at the extrusion port is ensured, and a good organization foundation is laid for the aging link.
5. After extrusion, a solid solution link is not required to be added, and the solid solubility after on-line quenching can be compared with the effect of single solid solution treatment.
Finally, the casting blank structure obtained by the method has excellent process performance, ensures the surface quality and the final strength index of the product, and has great significance for guiding the regulation and control of the homogenization process in actual production.
Drawings
FIG. 1 shows the surface quality of the product of example ;
FIG. 2 shows the surface quality of the eight products of the examples;
FIG. 3 shows the surface quality of the five products of the examples;
FIG. 4 shows the surface quality of a comparative example ;
FIG. 5 shows the surface quality of the comparative example product;
FIG. 6 shows the surface quality of twenty products of examples;
FIG. 7 shows the surface quality of the product of example twenty .
Detailed Description
In the prior art, a water cooling or strong wind rapid cooling method is adopted for the homogenized aluminum alloy ingot , so that an aluminum alloy ingot with good performance is expected to be obtained, but the extrusion performance of the treated product is still poor, and in the actual industrial production, if the homogenization heat treatment causes excessive solid solution of alloy elements in an aluminum matrix or excessive precipitation of the alloy elements to form coarse Mg2The Si phase causes corresponding process problems or product performance defects. The invention creatively provides the post-treatment step, overcomes the technical prejudice that the prior art needs rapid cooling, realizes the homogenization heat treatment, ensures that the alloy elements are less dissolved in the aluminum matrix in a solid way and the Mg with micron-sized size is precipitated2The Si phase solves the problem of process problems or product performance defects in the prior art, obtains reasonable casting blank tissues, has excellent process performance, ensures the surface quality and the final strength index of products, and aims to guide the homogenization process in actual productionThe regulation and control of (2) have great significance.
A preparation method of high-quality 6-series aluminum alloy extruded casting blanks comprises the steps of carrying out subsequent treatment on 6-series aluminum alloy cast blanks after homogenization treatment to obtain high-quality 6-series aluminum alloy extruded casting blanks, wherein the subsequent treatment comprises primary cooling treatment, bath soaking treatment and subsequent cooling treatment.
Example
The 6063 alloy cast rod with the diameter phi of 178mm comprises the following components in percentage by mass: 0.3 percent of Si, 0.48 percent of Mg, 0.12 percent of Fe, 0.05 percent of Mn0.02 percent of Ti, 0.03 percent of V, 98.9 percent of Al, and the sum of other elements (inevitable impurities) is less than or equal to 0.1 percent.
A process for preparing high-quality 6-series Al alloy castings includes such steps as homogenizing the 6063 alloy casting rod with diameter of 152mm in vacuum heat treating furnace at 580 deg.C for 5 hr, cooling to 460 deg.C by 3 deg.C/min, primary cooling, and putting in 300 deg.C salt bath (KNO) immediately3∶NaNO3The mass ratio of 50 percent to 50 percent, and the temperature of the fused salt is kept constant at 300 ℃ for immersion bath for 15 minutes (a cooling circulation system is adopted to keep the temperature stable); then cooling to below 150 ℃ at a cooling rate of 5 ℃/min (air cooling) to obtain the 6-series aluminum alloy extruded casting blank with high quality.
Example two
The primary cooling rate in example was changed from 3 ℃/min to 1 ℃/min, and the rest was unchanged, to obtain a high-quality 6-series aluminum alloy extruded casting slab.
EXAMPLE III
The primary cooling rate in example was changed from 3 ℃/min to 5 ℃/min, and the rest was unchanged, to obtain a high-quality 6-series aluminum alloy extruded slab.
Example four
The preliminary cooling rate in example was changed from 3 ℃/min to 10 ℃/min, and the remainder was unchanged, to obtain a comparative 6-series aluminum alloy extruded slab.
EXAMPLE five
A comparative extruded 6-series aluminum alloy slab was obtained by changing the temperature after the primary cooling in example from 460 ℃ to 420 ℃ and leaving the temperature unchanged.
EXAMPLE six
The preliminary cooling treatment, salt bath treatment and subsequent cooling treatment in example were omitted, and the casting was cooled to 150 ℃ or lower at 5 ℃/min after discharging uniformly, to obtain a comparative 6-series aluminum alloy extruded casting slab.
EXAMPLE seven
The preliminary cooling treatment, salt bath treatment and subsequent cooling treatment in example were omitted, and the casting was cooled to 150 ℃ or lower by spraying water mist at 50 ℃/min after discharging the casting homogeneously, to obtain a comparative 6-series aluminum alloy extruded casting.
Example eight
The temperature of the salt bath in example was adjusted to 400 ℃ and the balance was not changed, to obtain a 6-series aluminum alloy extruded slab of high quality.
Example nine
A comparative 6-series aluminum alloy extruded strand was obtained by adjusting the temperature of the salt bath in example to 450 ℃ and leaving the temperature unchanged.
Example ten
A comparative 6-series aluminum alloy extruded strand was obtained by adjusting the temperature of the salt bath in example to 250 ℃ and leaving the temperature unchanged.
Example ten
The cooling circulation system in example was closed, and the temperature of the salt bath was changed from 300 to 400 ℃ while the rest were unchanged, to obtain a high-quality 6-series aluminum alloy extruded slab.
Example twelve
The salt bath time in example was adjusted to 5 minutes, and the remainder was unchanged, to obtain a 6-series aluminum alloy extruded slab of high quality.
EXAMPLE thirteen
The salt bath time in example was adjusted to 30 minutes, and the remainder was unchanged, to obtain a high-quality 6-series aluminum alloy extruded strand.
Example fourteen
A comparative 6-series aluminum alloy extruded strand was obtained by adjusting the salt bath time to 60 minutes in example , and keeping the balance unchanged.
Example fifteen
The molten salt of the dipping medium in the example was changed to cotton oil, and the rest was unchanged, to obtain a high-quality 6-series aluminum alloy extruded strand.
Example sixteen
In example , the cooling rate after the completion of the dipping was changed from 5 ℃/min to 2 ℃/min, and the rest was unchanged, thereby obtaining a high-quality 6-series aluminum alloy extruded slab.
Example seventeen
In example , the cooling rate after the completion of the dipping was changed from 5 ℃/min to 10 ℃/min, and the rest was unchanged, whereby a high-quality 6-series aluminum alloy extruded slab was obtained.
EXAMPLE eighteen
In example , the cooling rate after completion of the dipping was changed from 5 ℃/min to 20 ℃/min, and the remainder was not changed, to obtain a comparative 6-series aluminum alloy extruded cast slab.
Example nineteen
In the sixth example, the extruded product was subjected to off-line solution treatment and aging treatment.
Example twenty
The 6-series aluminum alloy cast rod with the diameter of 178mm comprises the following components in percentage by mass: 0.7 percent of Si, 0.9 percent of Mg, 0.15 percent of Fe, 0.3 percent of Mn0.2 percent of Cr, 0.5 percent of Cu, 0.07 percent of Ti, 0.12 percent of Zr, less than or equal to 0.1 percent of the sum of other impurity elements and the balance of aluminum.
A process for preparing high-quality 6-class Al alloy cast blank includes such steps as homogenizing the 6-class alloy cast rod with diameter of 300mm in electric resistance furnace at 560 deg.C for 10 hr, cooling to 550 deg.C at 2 deg.C/min for primary cooling, and loading in the salt bath (NaNO) at 350 deg.C3100 percent), keeping the temperature of the salt bath within the range of 300-400 ℃, and finishing the dipping for 20 minutes; then cooling to below 150 ℃ at the speed of 5 ℃/min to obtain the 6-series aluminum alloy casting blank with high quality.
Comparative example
The aluminum alloy cast rod in the nineteenth embodiment has the following enterprise homogenization production flow: keeping the temperature of a conventional 6-series alloy cast rod with the diameter of 300mm at 560 ℃ in a resistance heat treatment furnace for 10 hours to carry out homogenization heat treatment; discharging after homogenization and air cooling for 20 min; cooling for 1-2 hours by adopting an axial flow fan; then spraying water to cool to below 150 ℃. A comparative 6-series aluminum alloy cast slab was obtained.
Example twenty
The 6-series aluminum alloy cast rod with the diameter of 178mm comprises the following components in percentage by mass: 0.95 percent of Si, 0.65 percent of Mg, 0.13 percent of Fe, 0.5 percent of Mn, 0.012 percent of Ti, 0.015 percent of V, 0.12 percent of Zr, less than or equal to 0.15 percent of the sum of other impurity elements and the balance of aluminum.
A process for preparing high-quality 6-class Al alloy cast blank includes such steps as homogenizing the 6-class alloy cast rod with phi 178mm at 570 deg.C for 8 hr, cooling to 530 deg.C at 3 deg.C/min for primary cooling, and loading in a salt bath (NaNO) at 350 deg.C3100 percent), keeping the temperature within the range of 300-400 ℃, and finishing the immersion bath for 15 minutes; then blowing and cooling to below 150 ℃ at the speed of 5 ℃/min. Obtaining the 6 series aluminum alloy casting blank with high quality.
Comparative example No. two
In the aluminum alloy cast bar of example twenty, the enterprise homogenization production flow is as follows: carrying out homogenization heat treatment on a conventional 6-series alloy cast rod with phi of 178mm in a vacuum heat treatment furnace at the temperature of 570 ℃ for 8 hours; discharging after homogenization is finished, and cooling by adopting an axial flow fan for 2h to below 150 ℃; spraying water and cooling to room temperature. A comparative 6-series aluminum alloy cast slab was obtained.
The indexes of cooling stress, precipitated phase size, extrusion force, extrusion surface quality and T5 state strength of the casting blanks in the examples and the comparative examples are shown in Table 1, the test method is conventional technology, for example, extrusion is carried out on an extruder, and stretching is carried out according to the national standard GB/T228-2002; besides, except for nineteen examples, all extruded products are not subjected to off-line solid solution and aging treatment, which shows that the solid solubility after on-line quenching can be comparable to the effect of single solid solution treatment without adding a solid solution link after the extrusion of the aluminum alloy extruded casting blank prepared by the method disclosed by the invention.
TABLE 1 test data in examples and comparative examples
Examples to nineteenth are examples of 6063 alloy, fig. 1 shows the surface quality of the product of example as best, fig. 2 shows the surface quality of the product of example eight as better, fig. 3 shows the surface quality of the product of example five with extrusion cracks, fig. 4 and 5 show the surface quality of the product of comparative examples and two with extrusion streaks, respectively, and fig. 6 and 7 show the surface quality of the product of examples twenty and twenty with optimized surface quality according to the present invention.
Finally, it is noted that the above-mentioned preferred embodiments illustrate rather than limit the invention, and that, although the invention has been described in detail with reference to the above-mentioned preferred embodiments, it will be understood by those skilled in the art that various changes in form and detail may be made therein without departing from the scope of the invention as defined by the appended claims.
Claims (10)
- The preparation method of the high-quality 6-series aluminum alloy extruded casting blank is characterized by comprising the following steps of carrying out subsequent treatment on the homogenized 6-series aluminum alloy cast ingot to obtain the high-quality 6-series aluminum alloy extruded casting blank, wherein the subsequent treatment comprises primary cooling treatment, dipping treatment and subsequent cooling treatment.
- 2. The high-quality 6-series aluminum alloy extruded strand according to claim 1, wherein: the mass percentages of all elements in the 6-series aluminum alloy are within the following ranges: 0.3-1.3% of Si, 0-0.5% of Fe, 0-1.2% of Cu, 0-1.0% of Mn, 0.3-1.3% of Mg, 0-0.4% of Cr, 0-0.2% of Ni, 0-1.0% of Zn, 0-0.2% of Ti, 0-0.1% of B, 0-0.2% of V, 0-0.3% of Zr, 0-0.2% of Sc0, and the balance of aluminum and uncontrollable impurities.
- 3. The high-quality 6-series aluminum alloy extruded strand according to claim 1, wherein: the preliminary cooling treatment is to reduce the temperature of the homogenized 6-series aluminum alloy ingot to the solid solubility line temperature at a cooling rate of 1-5 ℃/min.
- 4. The high-quality 6-series aluminum alloy extruded strand according to claim 1, wherein: the temperature range of the dipping bath treatment is 300-400 ℃, and the time is 5-30 minutes.
- 5. The high-quality 6-series aluminum alloy extruded strand according to claim 1, wherein: the immersion bath comprises salt bath and oil bath.
- 6. The high-quality 6-series aluminum alloy extruded strand according to claim 1, wherein: and the subsequent cooling treatment is to cool the 6 series aluminum alloy cast ingot after the dipping treatment to below 150 ℃ at a cooling rate of 2-10 ℃/min.
- 7. The high-quality 6-series aluminum alloy extruded strand according to claim 1, wherein: the primary cooling treatment, the dipping bath treatment and the subsequent cooling treatment are carried out in sequence.
- 8. Use of the high-quality 6-series aluminum alloy extruded strand according to claim 1 for producing an aluminum alloy extruded product.
- The preparation method of the 9 and high-quality 6-series aluminum alloy extruded billets is characterized by comprising the following steps of carrying out subsequent treatment on the 6-series aluminum alloy cast ingots subjected to the homogenization treatment to obtain the high-quality 6-series aluminum alloy extruded billets, wherein the subsequent treatment comprises primary cooling treatment, dipping treatment and subsequent cooling treatment.
- 10. The method of producing a high-quality 6-series aluminum alloy extruded slab according to claim 9, wherein the preliminary cooling treatment, the dipping treatment and the subsequent cooling treatment are performed in this order; the mass percentages of all elements in the 6-series aluminum alloy are within the following ranges: 0.3-1.3% of Si, 0-0.5% of Fe, 0-1.2% of Cu, 0-1.0% of Mn, 0.3-1.3% of Mg, 0-0.4% of Cr, 0-0.2% of Ni, 0-1.0% of Zn, 0-0.2% of Ti, 0-0.1% of B, 0-0.2% of V, 0-0.3% of Zr, 0-0.2% of Sc, and the balance of aluminum and uncontrollable impurities.
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| CN114086040B (en) * | 2021-08-20 | 2022-06-28 | 中国航发北京航空材料研究院 | Aluminum-magnesium-silicon-scandium-zirconium alloy and preparation method thereof |
| CN113667863A (en) * | 2021-08-30 | 2021-11-19 | 安徽华深铝业有限公司 | Aluminum bar homogenization heat treatment process before extrusion of industrial aluminum profile |
| CN114058889A (en) * | 2021-10-29 | 2022-02-18 | 上海工程技术大学 | Preparation method of high-strength high-toughness ultrafine-grained aluminum alloy |
| CN114058889B (en) * | 2021-10-29 | 2022-09-16 | 上海工程技术大学 | Preparation method of high-strength high-toughness ultrafine-grained aluminum alloy |
| CN114892050A (en) * | 2022-05-23 | 2022-08-12 | 江苏亚太航空科技有限公司 | High-strength Al-Mg-Si aluminum alloy and preparation process and application thereof |
| CN114892051A (en) * | 2022-05-27 | 2022-08-12 | 大为材料(包头)有限公司 | Aluminum alloy automobile transmission shaft tube and manufacturing method thereof |
| CN114892051B (en) * | 2022-05-27 | 2023-06-09 | 大为材料(包头)有限公司 | Aluminum alloy automobile transmission shaft tube and manufacturing method thereof |
| CN114752824A (en) * | 2022-06-02 | 2022-07-15 | 山东南山铝业股份有限公司 | Rapid extrusion aluminum alloy profile with low rare earth content and preparation process thereof |
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