CN104046933B - A kind of improve high strength alumin ium alloy sheet material plasticity and the deformation heat treatment method of formability - Google Patents
A kind of improve high strength alumin ium alloy sheet material plasticity and the deformation heat treatment method of formability Download PDFInfo
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- 238000000034 method Methods 0.000 title claims abstract description 71
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 41
- 239000000463 material Substances 0.000 title abstract description 17
- 238000010438 heat treatment Methods 0.000 title abstract description 10
- 238000001953 recrystallisation Methods 0.000 claims abstract description 31
- 238000010791 quenching Methods 0.000 claims abstract description 13
- 230000000171 quenching effect Effects 0.000 claims abstract description 13
- 238000005096 rolling process Methods 0.000 claims abstract description 12
- 230000032683 aging Effects 0.000 claims abstract description 10
- 238000004321 preservation Methods 0.000 claims description 30
- 238000005097 cold rolling Methods 0.000 claims description 22
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 18
- 239000000243 solution Substances 0.000 claims description 17
- 230000000930 thermomechanical effect Effects 0.000 claims description 15
- 239000006104 solid solution Substances 0.000 claims description 11
- 238000001816 cooling Methods 0.000 claims description 6
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- 238000005265 energy consumption Methods 0.000 abstract description 2
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- 238000004519 manufacturing process Methods 0.000 abstract description 2
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- 238000009740 moulding (composite fabrication) Methods 0.000 abstract 2
- 239000000956 alloy Substances 0.000 description 27
- 229910045601 alloy Inorganic materials 0.000 description 26
- 239000002245 particle Substances 0.000 description 10
- 238000001556 precipitation Methods 0.000 description 10
- 238000005098 hot rolling Methods 0.000 description 6
- 238000005728 strengthening Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 229910001008 7075 aluminium alloy Inorganic materials 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 229910017708 MgZn2 Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
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- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 229910018569 Al—Zn—Mg—Cu Inorganic materials 0.000 description 1
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Abstract
The present invention relates to a kind of raising 7000 line aluminium alloy sheet material plasticity and deformation heat treatment methods of formability, be embodied as step as follows: (1) solutionizing step；(2) cold roller and deformed step；(3) insulation and continuous rolling deforming step；(4) recrystallization processes step in short-term.Use this processing method that the crystallite dimension of aluminium alloy can refine to more than 200 μm 10 μm and following, it is suitable with the sheet material that conventional thermal roll process obtains that fine grained texture can enable aluminum alloy to sheet material room temperature strength after peak Ageing Treatment, and elongation percentage obtains and is greatly improved.Compared with conventional thermal roll process, improving through the quenching state sheet material room temperature forming property of this processes, annealed state sheet material room temperature formability obtains huge raising, and the warm working performance of peak aging state sheet material also obtains huge raising.Improving the fine grain treatment method of 7000 line aluminium alloy sheet material formings in the present invention, process is simple, the cycle is short, energy consumption is low, has the biggest application potential and value in industrialized production.
Description
Technical Field
The invention relates to a thermomechanical treatment method for improving plasticity and formability of a high-strength aluminum alloy, in particular to a grain refinement treatment method for an aluminum alloy material, and belongs to the technical field of thermomechanical treatment processes for metal materials.
Background
Al-Zn-Mg-Cu (7000) alloy is an important light-weight high-strength structural material, has high strength compared with Al-Mg-Si (6000) alloy, but has poor plasticity and formability. The ductility and toughness and corrosion performance of the 7000 series aluminum alloy with the fine grain structure are also improved, so that the grain refinement becomes a method for improving the comprehensive performance of the aluminum alloy. The stacking fault energy of the aluminum alloy is higher, the recrystallization is more difficult, and the grain refinement of the aluminum alloy is mainly realized by discontinuous recrystallization.
Intermediate thermomechanical treatment (ITMT) can achieve grain refinement of aluminum alloys by discontinuous recrystallization. The ITMT process currently used for grain refinement of 7000 series aluminum alloys is the relatively simple RI-ITMT process developed in 1982 by J.Wert et al (J.Wert, et al, Metallurgical transformations A, 1981, 12A: 1267) and comprises the process steps of: solution quenching, 400 ℃/8 hour overaging, medium temperature deformation and solution recrystallization treatment. They refined the 7075 aluminum alloy grains to 10 μm by this process, and the elongation is obviously improved. The core idea of the RI-ITMT process is that large particles are obtained through high-temperature long-time treatment, deformation is carried out at room temperature or medium temperature after the large particles are obtained to form deformation zones around the large particles, and the tissue refinement is realized by utilizing particle-induced recrystallization nucleation during subsequent recrystallization treatment. However, the RI-ITMT process needs long-time high-temperature overaging treatment, has long process period and large energy consumption, and cannot realize continuous production, so that the development of a novel intermediate deformation heat treatment process which is simple to operate, has short process period, can realize industrial production and can improve the plasticity and the formability of 7000 series aluminum alloy is of great significance.
Disclosure of Invention
The invention aims to overcome the defects of the prior art and develop a 7000 series aluminum alloy shape heat treatment structure refining treatment method which is simple, convenient to operate and short in production period, and adopts the steps of solution treatment, cold rolling deformation, heat preservation, continuous deformation and short-time recrystallization. The solid solution aluminum alloy is deformed by cold rolling and then is insulated, so that the precipitation and coarsening of precipitated phases can be greatly accelerated to obtain large-size precipitated phases, and a deformation zone is formed around the large-size precipitated phases (0.5 mu m) after subsequent medium-temperature and room-temperature deformation, so that the recrystallization nucleation can be favorably excited during subsequent recrystallization treatment. The process replaces simple overaging with a mode of combining cold rolling and heat preservation, greatly shortens the period of the classic RI-ITMT process, can obtain a fine grain structure under simple operation, greatly improves the plasticity and toughness of high-strength aluminum alloy, obviously improves the strength and plastic anisotropy, greatly improves the forming performance, and can be widely applied to precipitation strengthening 7000 series aluminum alloy.
The invention relates to a grain refining processing method for improving the plasticity and the formability of 7000 series aluminum alloy plates
A method comprising the steps of:
(1) solid solution
Solution treatment is carried out on 7000 series aluminum alloy, the solution temperature is 460-500 ℃, the heat preservation time is 0.5-24h, and water quenching is carried out at room temperature;
(2) cold rolling
The deformation mode is cold rolling, wherein the deformation amount of R1 is controlled at 30-80%
(3) Thermal insulation and continuous deformation
Performing heat preservation and continuous deformation treatment on the plate obtained in the second step, wherein the heat preservation temperature T is 200-450 ℃, and the heat preservation time T is fixed for 30 min; the continuous deformation mode of R2 is rolling, the deformation is 40-90%, and the deformation process is not re-melting;
(4) short time recrystallization
And (3) rapidly heating the plate obtained in the third step to 460-490 ℃ for recrystallization treatment, and keeping the temperature for 10-60min, wherein the cooling mode is air cooling or room temperature water quenching.
Wherein the cold rolling deformation in the step 2 is controlled to be 40-70%.
Wherein, in the step 3, the heat preservation temperature is controlled to be 400 ℃ in 250-.
Wherein, the better condition of the step 2 and the step 3 is that: step 2, cold rolling deformation is 40-70%, step 3, the heat preservation temperature is 350-450 ℃, the heat preservation time is 30min, and the continuous deformation is 60-80%. The optimal conditions are as follows: step 2, cold rolling deformation is 50-60%, step 3, the heat preservation temperature is 350-400 ℃, the heat preservation time is 30min, and the continuous deformation is 60-80%.
Wherein, in the step 4, the temperature rise rate during recrystallization is more than or equal to 1 ℃/s.
Wherein the short-time recrystallized and water-quenched sheet obtained in step 4 is subjected to T6, T76, T74, T73 or T77 aging treatment.
And testing the room-temperature formability or warm forming of the obtained final plate, wherein the testing method adopts a method described in national standard GB/T4156-2007.
The 7000 series aluminum alloy plate is treated by adopting the thermomechanical treatment method, the mode of combining cold deformation and heat preservation is used for replacing the mode of simply overaging to accelerate the precipitation of large-size precipitated phase particles, so that a core capable of exciting recrystallization is obtained, in the example operation, a certain number of precipitated phases (with the average size of 0.5 mu m) are obtained after the third step of short-time heat preservation treatment, so that the long-time overaging treatment of RI-ITMT is replaced, and the time of the whole process is greatly shortened. After the recrystallized water-quenched plate is subjected to T6 aging treatment, the strength of the plate is equivalent to that of the plate obtained by the traditional hot rolling process, but the elongation rate can be greatly improved, so that the formability is also improved.
Through the thermomechanical treatment process, namely, the mode of combining cold rolling and heat preservation to obtain large-size precipitation phase MgZn2 particles, deformation bands can be formed around the large particles in the subsequent continuous deformation, and recrystallization grains can be nucleated by taking the precipitation phase as a core in the short-time recrystallization stage, so that a fine recrystallization texture is obtained.
Experiments show that compared with the conventional thermomechanical treatment process, the solution treatment-cold rolling deformation-heat preservation + continuous deformation-short-time solution recrystallization process for the 7000 series aluminum alloy greatly shortens the preparation time, reduces the operation difficulty, greatly improves the elongation while maintaining good strength of the aged 7000 series aluminum alloy plate after obtaining good fine grain structure, obviously improves the room temperature forming performance of the quenched and annealed plate, and greatly improves the temperature forming performance of the quenched and annealed plate after peak aging. The material with good strength and plasticity and toughness has important significance for the development of the fields of aerospace, transportation and the like, and is suitable for industrial application.
Drawings
FIG. 1 is a schematic process flow diagram of the present invention.
FIG. 2 is a recrystallized and water-quenched structure of an initial 7075 alloy.
FIG. 3 is the M of the alloy in solid solution state of example 1 after cold deformation and short-term heat preservationgZn2 profile.
FIG. 4 shows the recrystallized and water-quenched structure of the alloy of example 1.
FIG. 5 is a recrystallized and water quenched structure of the alloy of comparative example I of example 1.
FIG. 6 is a recrystallized and water quenched structure of a conventional hot rolled alloy of comparative example II of example 1.
FIG. 7 shows the recrystallized water-quenched structure of the alloy of example 2.
FIGS. 8(a) and 8(b) show the recrystallized and water-quenched structures of the alloys of example 3 in different processes.
FIG. 9 is the structure of the alloy in example 4 after solid solution recrystallization and water quenching.
FIG. 10 is the recrystallized and water quenched structure of the 7050 alloy of example 5.
Detailed Description
Example 1
According to the process shown in fig. 1, 7075 aluminum alloy was used as a rolled material. In order to make solute atoms dissolved in the matrix, the plate is subjected to solution treatment at 475 ℃/1.5h and water quenching at room temperature, and a metallographic structure of the undeformed initial quenched 7075 alloy is shown in a figure 2. The deformation is realized on a common two-roller rolling mill, the 7075 alloy plate with the thickness of 15mm in a solid solution state is subjected to cold rolling deformation with the deformation amount of 30 percent, the alloy in the cold rolling state is kept at the temperature of 400 ℃ for 30min and then is continuously rolled on the rolling mill for 80 percent, and the rolling process is not returned. And (3) carrying out recrystallization treatment on the final rolled plate at 480 ℃/30min, and respectively adopting water quenching (W state) and air cooling (O state) in cooling modes after recrystallization is finished. FIG. 4 shows the metallographic structure of the alloy after recrystallization and water quenching of the rolled plate, and the average grain size of the alloy was 9.8 μm when measured by the linear intercept method. Two comparative examples were used, i: adopting 7075 aluminum alloy to treat according to the process of J.Wert (RI-ITMT), namely solid solution at-400 ℃/8h for overaging-warm rolling deformation of 90% -recrystallization, II: the conventional Hot Rolling (HR) is carried out at 400 ℃ on 7075 in a solid solution state with the thickness of 15mm, the total deformation is 88 percent, other heat treatment processes are completely the same, and the metallographic structures of the two after recrystallization and water quenching treatment are shown in figures 5 and 6 respectively, so that the grains which are still elongated by 100 mu m and are obtained by the conventional hot rolling are shown. The water quenched sheets of the inventive process and the two comparative processes were then subjected to T6 aging and the mechanical properties of the aged sheets were tested as shown in Table 1. The air-and water-quenched sheets obtained from the three processes were subjected to room temperature formability tests and the peak aged sheets obtained from the three processes were subjected to warm forming tests at 200 ℃ (T6-200 ℃) as shown in table 2. It can be seen that the process of the present invention improves the plasticity of the plate in the peak aged condition compared to the conventional hot rolling process while achieving the same strength. The formability of the plate in three states is higher than that of the traditional hot rolling process and is equivalent to that of an RI-ITMT process, but the plate greatly shortens the process time compared with the RI-ITMT process, and is very beneficial to industrial production.
Example 2
According to the mechanical heat treatment process shown in FIG. 1, 7075 alloy which had been subjected to solution treatment at 475 ℃ for 1.5 hours was used as a rolled material (plate thickness: 7.5 mm). The cold rolling deformation is carried out, the deformation amount is 40%, the cold rolled plate is subjected to heat preservation at 350 ℃ for 30min, then continuous deformation with the deformation amount of 70% is continuously carried out on a rolling mill, and the plate is not returned to the furnace. The final rolled plate was recrystallized and water quenched at 480 deg.C/0.5 h to obtain a fine grain structure as shown in FIG. 7. The final rolled plate was treated with 480 ℃/0.5h solution and T6 aging, at which point the plate strength was comparable to that of example 1, the plate elongation was 16.6% (Table 1), and the 200 ℃ cupping was higher than that of the conventional hot rolling process.
Example 3
According to the mechanical heat treatment process shown in FIG. 1, 7075 alloy which had been subjected to solution treatment at 475 ℃ for 1.5 hours was used as a rolled material (plate thickness: 7.5 mm). The two materials are subjected to 50% deformation on a two-roll mill, and then two cold-rolled plates are subjected to heat preservation at 350 ℃ and 400 ℃ for 30min respectively and then are continuously subjected to continuous deformation with 70% deformation on the mill without returning to the furnace. The final rolled plate was recrystallized and water quenched at 480 ℃/0.5h and treated at 120 ℃/24h to obtain fine crystalline structures as shown in fig. 8a and b, respectively, wherein the plate strength was equivalent to that of example 1, and the plate elongation was 16.5% and 16.7%, respectively, which also resulted in the conditions of grain refinement and improved plate plasticity (table 1) and warm formability (table 2).
Example 4
According to the mechanical heat treatment process shown in FIG. 1, 7075 alloy which had been subjected to solution treatment at 475 ℃ for 1.5 hours was used as a rolled material (plate thickness: 7.5 mm). The steel is subjected to cold rolling deformation for 60 percent, then the steel is subjected to heat preservation for 30min at 350 ℃, and then continuous deformation with the deformation of 60 percent is continuously carried out on a rolling mill without returning. The rolled plate is recrystallized and water quenched at 480 ℃/0.5h to obtain a fine grain structure as shown in figure 9, after 60% of the plate is subjected to cold rolling deformation, heat preservation and continuous deformation, the elongation of the plate with 60% of the plate subjected to continuous deformation reaches 16.6% (table 1) after recrystallization and T6 treatment, and the warm forming performance is still better than that of the traditional hot rolled plate (table 2).
Example 5
According to the mechanical heat treatment process shown in FIG. 1, 7050 aluminum alloy was used as a rolled material (plate thickness: 15mm),
the solution treatment is carried out at 475 ℃/1.5h, and water quenching is carried out at room temperature. Cold rolling and deforming 7050 in a solid solution state by 50-7.5 mm, keeping the temperature of 7.5mm plates at 400 ℃ for 30min, and then performing continuous deformation with deformation amount of 70%, wherein the continuous deformation process is not re-melting. The final rolled plate is processed at 480 ℃/0.5h and 120 ℃/24h,
the average grain size of the obtained structure was 9.6 μm (fig. 10), at which point the plasticity of the alloy was greatly improved, the elongation was as high as 20.9%, and the warm formability was excellent.
TABLE 1 room temperature mechanical properties of alloy T6 prepared in accordance with the invention
TABLE 2 Room temperature formability and warm formability of sheet materials
As seen from FIG. 3, the solid solution alloy is cold rolled and held at a medium temperature for a short period of time to obtain a large amount of large-sized MgZn2 particles of 0.5 μm, and strong deformation zones are formed around the particles in the subsequent continuous rolling deformation, which induce the formation of fine recrystallized grains as the nuclei of recrystallization in the solution treatment. Compared with the traditional RI-ITMT process, the process of the invention can greatly shorten the preparation time while refining the crystal grains. The aluminum alloy processed by the process can obtain a fine grain structure of 6-20 mu m, and the process can obtain the fine grain structure with the grain size equivalent to that of the RI-ITMT process.
As can be seen from the comparison of the three processes of the example 1 in the tables 1 and 2, the plasticity and the formability of the alloy plate can be greatly improved while the grain refinement is realized by the simple process of the invention. The 7000 series aluminum alloy strengthening mode mainly depends on precipitation strengthening, so the strength of the 7000 series aluminum alloy is not greatly influenced by grain refinement, but the plasticity can be greatly improved by grain refinement, thereby being beneficial to improving the formability.
The 7000 series aluminum alloy with precipitation strengthening characteristics can accelerate precipitation of precipitation strengthening phases through cold deformation and medium-temperature heat preservation, simultaneously can further promote coarsening or growth of the precipitation phases, and large particles can be used as a recrystallization core for grain refinement and can be used for improving plasticity and formability. Therefore, the process provided by the invention can effectively improve the ductility, toughness and formability of the high-strength 7075 and 7050 aluminum alloys after crystal grains are refined. Meanwhile, the process principle provided by the invention is applicable to all 7000 series aluminum alloys, namely the process realizes the structure refinement and improves the plasticity and the formability, and is not limited to 7075 and 7050 aluminum alloys.
Claims (8)
1. A thermomechanical treatment method for improving plasticity and formability of a high-strength aluminum alloy plate is characterized by comprising the following steps of: the method comprises the following steps:
(1) a solid solution treatment step; (2) cold rolling deformation; (3) heat preservation and continuous rolling deformation; (4) a short-time recrystallization treatment step; (5) carrying out aging treatment on T6, T76, T74, T73 or T77; (6) carrying out room temperature formability or warm forming test; wherein,
in the step (1), solution treatment is carried out on 7000 series aluminum alloy to ensure that solute atoms are fully dissolved in a matrix, wherein the solution temperature is 460-500 ℃, the heat preservation time is 0.5-24h, and water quenching is carried out at room temperature after solution treatment;
in the step (2), cold rolling deformation is carried out on the solid solution state plate, wherein the cold rolling deformation is controlled to be 30-80%;
in the step (3), the plate obtained in the step (2) is subjected to heat preservation and continuous rolling deformation, wherein the heat preservation temperature is 200-;
in the step (4), the plate obtained in the step (3) is rapidly heated to 460-490 ℃ for recrystallization treatment, the heat preservation time is 10-60min, and then air cooling or immediate room temperature water quenching is carried out;
in the step (5), the short-time recrystallized and quenched plate obtained in the step (4) is subjected to aging treatment of T6, T76, T74, T73 or T77;
and (6) testing the room-temperature formability or warm forming of the plate obtained in the step (5) after the low-temperature aging treatment.
2. The thermomechanical treatment method for improving the plasticity and the formability of the high-strength aluminum alloy plate is characterized in that the cold rolling deformation in the step (2) is controlled to be 40-70%.
3. The thermomechanical treatment method for improving the plasticity and the formability of the high-strength aluminum alloy plate, as recited in claim 1, wherein the temperature in the step (3) is controlled to be 400 ℃ at 250 ℃ for 30 min.
4. The thermomechanical treatment method for improving the plasticity and the formability of the high-strength aluminum alloy plate, as recited in claim 1, wherein the temperature in the step (3) is controlled to be 350-400 ℃ and the holding time is 30 min.
5. The thermomechanical treatment method for improving the plasticity and the formability of the high-strength aluminum alloy plate according to claim 1, wherein the continuous rolling deformation in the step (3) is 50-90%.
6. The thermomechanical treatment method for improving the plasticity and the formability of the high-strength aluminum alloy plate according to claim 1, wherein the conditions of the step (2) and the step (3) are matched with each other: the cold rolling deformation of the step (2) is 40-70%, the heat preservation temperature of the step (3) is 350-450 ℃, the heat preservation time is 30min, and the continuous deformation is 60-80%.
7. The thermomechanical treatment method for improving the plasticity and the formability of the high-strength aluminum alloy plate according to claim 1, wherein the conditions of the step (2) and the step (3) are matched with each other: 50-60% of cold rolling deformation in the step (2), 350-400 ℃ of heat preservation temperature in the step (3), 30min of heat preservation time and 60-80% of continuous deformation.
8. A thermomechanical treatment method capable of improving the plasticity and the formability of the high-strength aluminum alloy plate according to claim 1, wherein in the step (4), the temperature rise rate during the recrystallization treatment is not less than 1 ℃/s, and air cooling or immediate room temperature water quenching is performed after the recrystallization is completed.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4486244A (en) * | 1982-12-17 | 1984-12-04 | Reynolds Metals Company | Method of producing superplastic aluminum sheet |
| US5181969A (en) * | 1990-06-11 | 1993-01-26 | Sky Aluminum Co., Ltd. | Rolled aluminum alloy adapted for superplastic forming and method for making |
| US6743308B2 (en) * | 2001-02-16 | 2004-06-01 | Kabushiki Kaisha Kobe Seiko Sho. | Aluminum alloy structural plate excelling in strength and corrosion resistance and method of manufacturing same |
| CN102828131A (en) * | 2012-09-12 | 2012-12-19 | 北京科技大学 | Thermo-mechanical treatment process based on ultrahigh-strength and high-toughness aluminum alloy board |
| CN103343306A (en) * | 2013-07-17 | 2013-10-09 | 北京科技大学 | Treatment method for obviously improving deformability and mechanical property of high-strength aluminum alloy |
| CN103572179A (en) * | 2013-11-18 | 2014-02-12 | 北京科技大学 | Grain refinement method of 7000 series aluminum alloy |
-
2014
- 2014-05-26 CN CN201410223778.9A patent/CN104046933B/en not_active Expired - Fee Related
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4486244A (en) * | 1982-12-17 | 1984-12-04 | Reynolds Metals Company | Method of producing superplastic aluminum sheet |
| US5181969A (en) * | 1990-06-11 | 1993-01-26 | Sky Aluminum Co., Ltd. | Rolled aluminum alloy adapted for superplastic forming and method for making |
| US6743308B2 (en) * | 2001-02-16 | 2004-06-01 | Kabushiki Kaisha Kobe Seiko Sho. | Aluminum alloy structural plate excelling in strength and corrosion resistance and method of manufacturing same |
| CN102828131A (en) * | 2012-09-12 | 2012-12-19 | 北京科技大学 | Thermo-mechanical treatment process based on ultrahigh-strength and high-toughness aluminum alloy board |
| CN103343306A (en) * | 2013-07-17 | 2013-10-09 | 北京科技大学 | Treatment method for obviously improving deformability and mechanical property of high-strength aluminum alloy |
| CN103572179A (en) * | 2013-11-18 | 2014-02-12 | 北京科技大学 | Grain refinement method of 7000 series aluminum alloy |
Non-Patent Citations (1)
| Title |
|---|
| 铝合金先进形变热处理研究进展;霍望图等;《材料科学与工程学报》;20140430;第32卷(第2期);第283-292页 * |
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