CN110629075A - High-strength high-elongation aluminum alloy plate and manufacturing method thereof - Google Patents
High-strength high-elongation aluminum alloy plate and manufacturing method thereof Download PDFInfo
- Publication number
- CN110629075A CN110629075A CN201810658850.9A CN201810658850A CN110629075A CN 110629075 A CN110629075 A CN 110629075A CN 201810658850 A CN201810658850 A CN 201810658850A CN 110629075 A CN110629075 A CN 110629075A
- Authority
- CN
- China
- Prior art keywords
- equal
- aluminum alloy
- percent
- strength
- elongation
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
A high-strength high-elongation aluminum alloy plate and a manufacturing method thereof are disclosed, wherein the aluminum alloy plate comprises the following chemical components in percentage by mass: mg is more than or equal to 0.8 percent and less than or equal to 1.5 percent, Si is more than or equal to 0.8 percent and less than or equal to 1.5 percent, Cu is more than or equal to 1.2 percent and less than or equal to 1.5 percent, Mn is more than or equal to 0.1 percent and less than or equal to 0.5 percent, Fe is more than or equal to 0.05 percent and less than or equal to 0.5 percent, Zr is more than or equal to 0.05 percent and less than or equal to 0.2 percent, Ti is more than or equal to 0.01 percent. The invention adopts the two-stage homogenization heat treatment process corresponding to the aluminum alloy component system, improves the grain refinement and dispersion strengthening effects of the alloy, the age hardening rate in the baking finish or short-time artificial aging process, and improves the number density and dispersion distribution of precipitated phases, thereby improving the strength of the final aluminum alloy part and having higher plasticity.
Description
Technical Field
The invention belongs to the field of aluminum alloy plate strip manufacturing, and particularly relates to a high-strength high-elongation aluminum alloy plate and a manufacturing method thereof, which are particularly suitable for automobile structural parts and safety parts with light weight requirements.
Background
In order to respond to the call of governments to energy conservation and emission reduction of automobiles, automobile body lightening is taken as an important task for automobile development by all major automobile manufacturers all over the world. Aluminum alloys are considered to be the most effective materials for automobile weight reduction because of their low density, good formability, impact energy absorption, corrosion resistance, recyclability, and the like. At present, aluminum alloy plates are increasingly widely applied to automobile covering parts such as engine hoods, trunk lids and automobile doors. With increasingly strict oil consumption regulation regulations of governments, the requirement of light weight of automobiles of various large automobile enterprises cannot be met only by adopting the aluminum alloy plates on the covering pieces, and the light weight of the materials for the automobile structural parts is a necessary development trend. In addition, the weight of the power battery of the new energy automobile reaches hundreds of kilograms, and the light weight of the automobile body of the new energy automobile is more urgent in order to compensate for the weight increase of the battery. Therefore, the high-strength aluminum alloy for automobile structural parts and safety parts such as the A column, the B column, the chassis, the collision system and the like has great application potential in both traditional automobiles and new energy automobiles.
Aluminum alloy sheets commonly used in the field of mass transit are 7xxx series, 6xxx series and 5xxx series aluminum alloys. The 7xxx series Al-Zn-Mg-Cu aluminum alloy is a high-strength wrought aluminum alloy and is one of the most important structural materials for aerospace. But because the fatigue resistance and the weldability are poor, the alloy has obvious stress corrosion cracking tendency and higher cost, and still needs time to be applied to automobiles. The 5xxx series Al-Mg series aluminum alloy is heat treatment non-reinforceable aluminum alloy, and the strength is improved mainly by solid solution strengthening and work hardening, and the strength requirement of the automobile structural member is difficult to achieve due to no aging strengthening effect. The 6xxx Al-Mg-Si aluminum alloy is the most popular aluminum alloy plate for the automobile due to good forming property, mechanical property, corrosion resistance and baking hardening property.
At present, the 6xxx series aluminum alloy plates used for automobile covering parts are mainly of conventional brands of 6016, 6111, 6022 and the like, the main alloy elements are Mg and Si, and beta-Mg is mainly formed in the aging process2Si phase metastable phase beta' to realize aging strengthening. The 6xxx series aluminum sheet for automobile covering parts is generally supplied in a solid solution pre-aged (T4P) state, when Mg and Si atoms are dissolved in an aluminum matrix to form an alpha-Al supersaturated solid solution, and the aluminum sheet has lower yield strength and better forming performance so as to meet the requirement of stamping and forming automobile parts. The aluminum plate can be baked after being stamped into the automobile part, which is equivalent to a short artificial aging process. Due to the limitation of baking temperature and time, the beta' strengthening phase can not be completely precipitated, the alloy is still in an underaged state, the yield strength and the tensile strength are still lower, and the strength requirements of automobile structural parts and safety parts can not be met. Therefore, if various material strengthening means are applied to improve the strength of the 6xxx series aluminum alloy, it is the key to promote the wide application of the 6xxx series aluminum alloy in the automobile structural parts and safety parts.
Chinese patent CN1974814 discloses an Al-Mg-Si-Cu alloy. The Al-Mg-Si-Cu alloy comprises the following components in percentage by mass: mg: 0.4-2 wt%, Si: 0.5 to 1.5 wt%, Cu: 0.01-0.5 wt%, Fe: 0.05-0.15 wt%, Mn: 0.01-0.1 wt%, Cr: 0-0.15 wt%, Zn: 0 to 0.30 wt%, and the ratio of the Si content to the Mg content in the alloy is 1.6 to 2.2: 1. the processing technology of the Al-Mg-Si-Cu alloy comprises the following steps: homogenizing and annealing the cast ingot obtained by casting at 450-600 ℃ for 10-20 hours, then carrying out heat preservation at 400-550 ℃ for 1-2 hours, and carrying out hot rolling; after hot rolling, annealing the plate at 280-560 ℃ for 1-2 hours, and then cold rolling; and after the cold rolling is finished, preserving the heat for 1-2 hours at 530-580 ℃ for solution treatment. After paint baking, the yield strength of the aluminum alloy is more than or equal to 160MPa, the tensile strength is more than or equal to 280MPa, and the strength requirement of an automobile structural part is still not met.
In view of this, the automobile manufacturing industry which is being developed increasingly needs an aluminum alloy plate which has high strength and good plasticity, can realize large-scale industrial production, and can be used for manufacturing automobile parts with high strength requirements, such as automobile structural members, so as to meet the further requirements of automobile light weight.
Disclosure of Invention
The invention aims to provide a high-strength high-elongation aluminum alloy plate and a manufacturing method thereof, wherein the aluminum alloy plate has higher yield strength (Rp) after solid solution and pre-aging treatment0.2: 190-50Not less than 25 percent), is beneficial to stamping and forming automobile parts, can further improve the yield strength by baking finish or short-time artificial aging after forming, is particularly suitable for manufacturing the inner and outer plates, structural members and safety members of automobile covering parts with higher requirements on strength, for example, the yield strength is not less than 320MPa after simulated baking finish treatment, and the yield strength is not less than 360MPa after short-time artificial aging.
In order to achieve the purpose, the technical scheme of the invention is as follows:
after being stamped into an automobile part, the aluminum alloy plate can be baked at 170-205 ℃, which is equivalent to artificial aging treatment, and as the baking time is short (generally about 30 min), the main strengthening phase beta' phase in common 6xxx series aluminum alloy can not be completely precipitated, and peak aging can not be realized.
According to the invention, the Cu content in the alloy is increased, the beta ' precipitated phase precipitation rate is increased during the artificial aging of the aluminum alloy, and extra Q ' and theta ' precipitated phases are formed, so that the number density of the precipitated phases in the baking process is increased, and the aging strengthening effect of the alloy is greatly improved; the grain refinement and dispersion strengthening effects of the alloy are enhanced by adding Zr element, and the yield strength of the alloy is further improved; by reasonably optimizing the manufacturing process of the alloy, the distribution and the size of various dispersed phases and precipitated phases are improved, so that the alloy also has higher elongation.
Specifically, the high-strength high-elongation aluminum alloy plate comprises the following chemical components in percentage by mass: mg is more than or equal to 0.8 percent and less than or equal to 1.5 percent, Si is more than or equal to 0.8 percent and less than or equal to 1.5 percent, Cu is more than or equal to 1.2 percent and less than or equal to 1.5 percent, Mn is more than or equal to 0.1 percent and less than or equal to 0.5 percent, Zr is more than or equal to 0.05 percent and less than or equal to 0.2 percent, Fe is more than or equal to 0.05 percent and less than or equal to 0.5 percent, Ti is more than or equal to 0.01 percent.
Further, the microstructure of the high-strength high-elongation aluminum alloy plate is an alpha (Al) matrix, uniformly distributed granular and/or short rod-shaped crystalline phases and punctiform fine dispersed phases; nano-sized Mg is also present in the material when it is finished into an aluminum alloy part by post-forming paint baking or artificial aging2Metastable phase beta of Si, metastable phase Q' of Q-AlCuMgSi phase and theta-Al2Three precipitated phases of metastable phases theta' of Cu.
Preferably, the average grain size of an alpha (Al) matrix in the microstructure of the high-strength aluminum alloy plate is less than or equal to 30 mu m.
Preferably, the average size of the granular and/or short rod-like crystal phase in the microstructure of the high-strength high-elongation aluminum alloy plate is less than or equal to 3 μm.
Preferably, the point-like fine dispersion precipitated phase in the microstructure of the high-strength high-elongation aluminum alloy plate includes a submicron alpha-Al (Fe, Mn, Cu) Si phase and Al phase3A Zr phase.
In addition, after the high-strength high-elongation aluminum alloy plate is subjected to solid solution and pre-aging treatment, the yield strength is 190-230MPa, and the elongation A50Not less than 25%; the yield strength is more than or equal to 320MPa after 2% pre-stretching and 185 ℃ heat preservation for 20min by simulating baking finish treatment, and the elongation A50More than or equal to 15 percent; the yield strength is more than or equal to 360MPa after the short-time artificial aging treatment is carried out at 190 ℃ for 4h, and the elongation A50≥10％。
The design principle of each chemical element in the aluminum alloy plate is as follows:
mg and Si: the Mg and Si atoms can be combined to form Mg after the aluminum plate is formed and is painted or artificially aged2The metastable phase beta ' phase and the beta ' phase of Si are coherent with an alpha (Al) matrix and have strong precipitation strengthening effect, but due to the limitation of a baking process, the beta ' phase cannot be completely precipitated, so that the yield strength of the baked alloy is still low. When the contents of Mg and Si are less than the defined range, Mg and Si are not combined to form a sufficient beta' strengthening phase upon baking and are not combined with CuCombine to form sufficient Q' phase to meet the desired yield strength requirements. When the Mg and Si contents are above the defined ranges, the plasticity and formability of the alloy are adversely affected. Therefore, the contents of Mg and Si are both limited to 0.8-1.5%.
Cu: as the Cu atoms have strong binding force with the Mg atoms and the Si atoms, the addition of Cu can greatly increase the formation and the dispersion distribution of Cu, Mg and Si atom clusters (GP regions) in the aging process and accelerate the generation of Mg from the GP regions2The transformation rate of metastable phase beta ' of Si improves the precipitation rate of beta ', and increases the number density and the dispersivity of beta ' phase in short-time artificial aging, thereby improving the strength of the alloy. The addition of Cu can also change the precipitation sequence of the Al-Mg-Si alloy after solid solution, and Al can be formed during the artificial aging of the alloy besides a beta' precipitation phase2A metastable phase theta 'phase of Cu and forms a metastable phase Q' phase of Q-AlCuMgSi phase with Mg and Si. The Q 'phase and the theta' phase have strong precipitation strengthening effect, so that the strength of the alloy after aging is greatly improved. When the Cu content is 1.2-1.5%, the aging strengthening effect is most obvious.
Mn: mn element can form a dispersed phase in the homogenization process of the alloy, and plays roles in grain refinement and dispersion strengthening, thereby improving the strength of the aluminum alloy. Mn also reduces the deleterious effects of Fe and improves the plasticity and formability of the alloy. When the Mn content is more than 0.5%, coarse second phases are easily generated, and the plasticity and formability of the aluminum alloy sheet are deteriorated. Therefore, the Mn content is limited to 0.1-0.5%.
Zr: as the difference between the melting points of Zr and Al is large, Zr is easy to serve as a heterogeneous nucleation core of an alpha-Al matrix in the alloy solidification process, and plays a role in refining ingot casting tissues. On the other hand, addition of Zr can form Al together with Al3Zr，Al3The Zr and the alpha-Al matrix are coherent, and can play a strong dispersion strengthening effect, thereby improving the strength of the alloy. And Al3Zr can also be used as a nucleation core of a beta ' phase, a Q ' phase and a theta ' phase in the aging process of the alloy, thereby promoting the precipitation and dispersion distribution of three precipitated phases, improving the aging strengthening effect and further improving the strength of the alloy. Zr content less thanAt 0.05%, Zr is mainly dissolved in Al matrix to form Al3The Zr dispersion phase is less in quantity and weak in strengthening effect. When the Zr content is 0.05-0.2%, the crystal grain refinement, the dispersion strengthening and the precipitation promotion effect on precipitated phases are obvious.
Ti: the addition of Ti mainly plays a role in refining grains, and when the content of Ti is less than 0.01%, the grain refining effect of Ti is not obvious; when the Ti content is more than 0.15%, coarse intermetallic compounds are easily formed, and the formability of the aluminum alloy sheet is deteriorated. Therefore, the Ti content is limited to 0.01-0.15%.
Fe: the invention controls Fe not more than 0.5%, based on: the excessive Fe makes the alloy easy to form coarse crystallized phase during casting, and has adverse effect on the plasticity, forming performance and corrosion resistance of the aluminum alloy plate. In addition, Fe can be combined with Mn to generate alpha-Al (Fe, Mn, Cu) Si dispersed phase, and the alpha-Al dispersed phase plays roles in controlling nucleation and inhibiting grain growth. And the addition of Fe can also make the aluminum alloy utilize the recovered waste aluminum in the production, thereby reducing the cost. Therefore, the Fe content is limited to 0.05-0.5%.
The invention relates to a manufacturing method of a high-strength high-elongation aluminum alloy plate, which mainly comprises the following steps:
1) smelting and casting;
smelting and casting according to the chemical components;
2) homogenization of ingot
Homogenizing at 300-400 ℃ for 5-20 hours, and then homogenizing at 520-570 ℃ for 5-15 hours;
3) hot rolling
Rough rolling: the initial rolling temperature of rough rolling is 450-550 ℃;
finish rolling: the initial rolling temperature of finish rolling is 380-480 ℃, and the final rolling temperature is 250-350 ℃;
the total pass reduction rate of hot rolling is more than 90 percent;
4) cold rolling
5) Solution treatment and cooling
The solution treatment temperature is 500-560 ℃; then quenching and cooling to below 60 ℃;
6) pre-ageing treatment
The pre-aging treatment temperature is 75-180 ℃, and the pre-aging treatment time is 10-45 min.
Further, in the step (4), once intermediate annealing is carried out between adjacent cold rolling passes, wherein the annealing temperature is 360-500 ℃.
In the manufacturing method of the present invention:
in the step (2), the ingot homogenization treatment is helpful to eliminate residual stress in the ingot, reduce dendrite segregation, and promote dissolution of non-equilibrium crystalline phase and precipitation of dispersed phase. Homogenization may be accomplished in the furnace alone or simultaneously with heating prior to hot rolling. The method adopts two-stage homogenization, namely homogenization at 300-400 ℃ for 5-20 hours and then homogenization at 520-570 ℃ for 5-15 hours. Homogenizing at 300-400 deg.C for 5-20 hr to promote dissolution of low-melting-point nonequilibrium crystal phase and form alpha-Al (Fe, Mn, Cu) Si and Al3Zr disperse phase nucleation core, promoting alpha-Al (Fe, Mn, Cu) Si and Al3The precipitation and dispersion distribution of the Zr phase enhance the grain refinement and dispersion strengthening effects of the alloy and improve the strength of the alloy; homogenizing at 520-560 deg.C for 5-15 hr to promote Mg2Si、Q-AlCuMgSi、Al2Dissolution of Cu and other non-equilibrium crystalline phases to reduce the deformation resistance of the alloy.
The hot rolling in the step (3) can be carried out according to conventional methods such as hot rough rolling, hot finish rolling and the like, wherein the initial rolling temperature of rough rolling is controlled to be 450-550 ℃; the start rolling temperature of finish rolling is controlled to be 380-480 ℃, the finish rolling temperature is controlled to be 250-350 ℃, and the total pass reduction rate of hot rolling is more than 90%: so as to completely destroy the aluminum alloy casting structure and obtain a completely recrystallized structure or a recrystallized structure and a small amount of deformed structure.
In the step (5), the solution treatment temperature is controlled to be more than or equal to 500 ℃ based on the following steps: when the solution treatment temperature is less than 500 ℃, Mg in the alloy of the invention2Si, Q-AlCuMgSi and Al2The insufficient solid solution of the second phase such as Cu is unfavorable for the forming performance of the aluminum alloy plate, and the beta ' phase, the Q ' phase and the theta ' phase are not sufficiently separated out in the subsequent baking finish and artificial aging process, so that the strength of the aluminum alloy plate is reduced. When the solution treatment temperature is higher than 560 ℃, the alloy with the composition range is easy to over-fire, so that the elongation of the aluminum alloy plate is reducedTherefore, the solution treatment temperature is limited to 500 to 560 ℃.
In addition, performing pre-aging treatment immediately after quenching, wherein the temperature of the pre-aging treatment is 75-180 ℃, and preserving heat for 10-45 min: the aluminum alloy plate after the solution treatment is easy to generate natural aging in the storage process, so that the strength of the plate is increased, and the plasticity is reduced. The aluminum alloy plate is subjected to pre-aging treatment after solution treatment, so that the stability of the performance of the aluminum alloy plate is maintained, the requirement of an automobile factory on the performance stability of the aluminum alloy plate during storage is met, and the industrial batch stamping production of the aluminum alloy plate is facilitated.
In the microstructure of the high-strength aluminum alloy plate, the average size of the granular and/or short rod-shaped crystalline phase is less than or equal to 3 mu m. Since the fatigue properties and toughness of the aluminum alloy sheet are reduced at a crystal phase of > 3 μm, the average size of the granular and/or short rod-like crystal phase of the aluminum alloy sheet according to the present invention is preferably 3 μm or less.
The invention has the beneficial effects that:
according to the invention, a novel aluminum alloy component system is developed by controlling the content ranges of Si, Mg and Cu elements, particularly obviously improving the Cu content and adding a dispersed phase strengthening element Zr; and a two-stage homogenization heat treatment process corresponding to an aluminum alloy component system is adopted, so that the grain refinement and dispersion strengthening effects of the alloy and the age hardening rate in the baking finish or short-time artificial aging process are improved, and the number density and dispersion distribution of precipitated phases are improved, so that the strength of the final aluminum alloy part is improved, and the final aluminum alloy part has high plasticity.
Drawings
FIG. 1 is a photograph of the EBSD microstructure of the aluminum alloy plate of example 1 of the present invention.
Detailed Description
The aluminum alloy sheet with high strength and high plasticity according to the present invention will be further explained and illustrated with reference to the drawings and specific examples, which, however, should not be construed to unduly limit the technical scope of the present invention.
Table 1 shows the mass percentages of chemical elements of the aluminum alloy sheets of examples 1 to 6 and comparative examples 1 to 2. Table 2 shows the manufacturing process parameters of examples 1 to 6 and comparative examples 1 to 2, and Table 3 shows the results of the performance tests.
The aluminum alloy sheets of examples 1 to 6 and comparative examples 1 to 2 were produced by the following steps:
(1) casting into ingots by a semi-continuous casting method according to the percentage of each chemical element in the table 1;
(2) homogenizing cast ingots: homogenizing the cast ingot at 300-400 ℃ for 5-20 hours, and then homogenizing at 520-560 ℃ for 5-15 hours;
(3) hot rolling: the hot rolling comprises rough rolling and finish rolling, wherein the rough rolling temperature is 450-550 ℃, and the total pass reduction rate of the hot rolling is more than 90%;
(4) cold rolling: cold rolling the hot rolled plate to the required thickness of the finished plate;
(5) the solid solution treatment and the pre-aging treatment are completed on a continuous heat treatment line: the solution treatment temperature is 500-560 ℃, and the solution time is 20-120 s; then quenching and cooling, and cooling to below 60 ℃ by adopting a water cooling mode; and immediately performing pre-aging treatment after quenching, wherein the temperature of the pre-aging treatment is 75-180 ℃, and the temperature is kept for 10-45 min.
The mechanical properties perpendicular to the rolling direction of the aluminum alloy sheets of examples 1-6 and comparative examples 1-2 were measured by sampling after different treatments, and the results of the performance tests are shown in Table 3, wherein T4P represents the state of standing at room temperature for 30 days after solution pre-aging, T8x represents the state after simulated paint baking (pre-stretching by 2% and heating to 185 ℃ for 20 minutes), and T6 represents the state of the aluminum alloy sheets after heating at 190 ℃ for 4 hours.
As can be seen from Table 3, the aluminum alloy sheets of examples 1 to 6 had a yield strength Rp in a tensile property test perpendicular to the rolling direction after being stored at room temperature for 30 days0.2Are all 190-230MPa, the elongation rate A50>25%, indicating that each example has excellent formability; and the yield strength Rp after simulated baking finish (T8x: 2% pre-stretching + heating at 185 ℃ for 20min)0.2Are all made of>320MPa, elongation A50>15% artificially aged T6 State yield strength Rp0.2Are all at>360MPa, elongation A50>10% indicating that examples 1-6 have excellent agingThe hardening performance meets the performance requirements of the high-strength high-elongation aluminum alloy plate.
Combining tables 1 and 3, the Cu content in comparative example 1 is less than 1.2%, resulting in a lower yield strength in the tensile properties test perpendicular to the rolling direction than in the examples of the present invention; in comparative example 2, no Zr is added, so that the yield strength and the elongation rate in the tensile property test perpendicular to the rolling direction are lower than those of the examples in the scheme.
FIG. 1 is a photograph of the EBSD microstructure of the aluminum alloy sheet of example 1 after being left at room temperature for 30 days. As is clear from FIG. 1, the average crystal grain size of the α (Al) matrix is 30 μm or less.
Table 1 units: wt.%
| Mg | Si | Cu | Zr | Mn | Fe | Ti | |
| Example 1 | 1.39 | 1.2 | 1.35 | 0.08 | 0.21 | 0.25 | 0.08 |
| Example 2 | 0.87 | 0.95 | 1.29 | 0.06 | 0.24 | 0.22 | 0.09 |
| Example 3 | 0.82 | 0.85 | 1.24 | 0.12 | 0.32 | 0.19 | 0.12 |
| Example 4 | 1.15 | 1.21 | 1.37 | 0.18 | 0.25 | 0.26 | 0.06 |
| Example 5 | 1.03 | 1.12 | 1.32 | 0.1 | 0.42 | 0.32 | 0.11 |
| Example 6 | 1.2 | 1.06 | 1.41 | 0.14 | 0.26 | 0.41 | 0.07 |
| Comparative example 1 | 0.81 | 1.02 | 0.58 | 0.17 | 0.34 | 0.36 | 0.08 |
| Comparative example 2 | 1.22 | 0.96 | 1.35 | 0 | 0.28 | 0.32 | 0.14 |
TABLE 2
TABLE 3
Claims (13)
1. A high-strength high-elongation aluminum alloy plate comprises the following chemical components in percentage by mass:
mg is more than or equal to 0.8 percent and less than or equal to 1.5 percent, Si is more than or equal to 0.8 percent and less than or equal to 1.5 percent, Cu is more than or equal to 1.2 percent and less than or equal to 1.5 percent, Mn is more than or equal to 0.1 percent and less than or equal to 0.5 percent, Zr is more than or equal to 0.05 percent and less than or equal to 0.2 percent, Fe is more than or equal to 0.05 percent and less than or equal to 0.5 percent, Ti is more than or equal to 0.01 percent.
2. The high-strength high-elongation aluminum alloy sheet according to claim 1, wherein the microstructure of the high-strength high-elongation aluminum alloy sheet is an α (Al) matrix, uniformly distributed granular and/or short rod-like crystalline phases, and a dotted fine dispersed phase; nano-sized Mg is also present in the material when it is finished into an aluminum alloy part by post-forming paint baking or artificial aging2Metastable phase beta of Si, metastable phase Q' of Q-AlCuMgSi phase and theta-Al2Three precipitated phases of metastable phases theta' of Cu.
3. The high strength, high elongation aluminum alloy sheet of claim 2 wherein the high strength aluminum alloy sheet has a microstructure having an average grain size of the alpha (Al) matrix of 30 μm or less.
4. The high-strength high-elongation aluminum alloy sheet according to claim 2, wherein the high-strength high-elongation aluminum alloy sheet has a microstructure in which the average size of granular and/or short-rod-like crystal phases is 3 μm or less.
5. The high strength, high elongation aluminum alloy sheet of claim 2 wherein said microstructure of said high strength, high elongation aluminum alloy sheet has point-like fine dispersion precipitates comprising submicron alpha-Al (Fe, Mn, Cu) Si phase and Al phase3A Zr phase.
6. The high strength, high elongation aluminum alloy of any one of claims 1-5The plate is characterized in that the yield strength of the high-strength high-elongation aluminum alloy plate is 190-230MPa, and the elongation A is50Not less than 25%; the yield strength is more than or equal to 320MPa after 2% pre-stretching and 185 ℃ heat preservation for 20min by simulating baking finish treatment, and the elongation A50More than or equal to 15 percent; after the short-time artificial aging treatment is carried out at 190 ℃ for 4h, the yield strength is more than or equal to 360MPa, and the elongation A50≥10％。
7. The method for producing a high-strength high-elongation aluminum alloy sheet as claimed in any one of claims 1 to 6, comprising the main steps of:
1) smelting and casting;
smelting and casting the chemical composition according to claim 1;
2) homogenization of ingot
Homogenizing at 300-400 ℃ for 5-20 hours, and then homogenizing at 520-570 ℃ for 5-15 hours;
3) hot rolling
Rough rolling: the initial rolling temperature of rough rolling is 450-550 ℃;
finish rolling: the initial rolling temperature of finish rolling is 380-480 ℃, and the final rolling temperature is 250-350 ℃;
the total pass reduction rate of hot rolling is more than 90 percent;
4) cold rolling
5) Solution treatment and cooling
The solution treatment temperature is 500-560 ℃; then quenching and cooling to below 60 ℃;
6) pre-ageing treatment
The pre-aging treatment temperature is 75-180 ℃, and the pre-aging treatment time is 10-45 min.
8. The method for manufacturing the high-strength high-elongation aluminum alloy plate as claimed in claim 7, wherein in the step (4), an intermediate annealing is performed between adjacent cold rolling passes, and the annealing temperature is 360-500 ℃.
9. The method of claim 7 or 8, wherein the microstructure of the high-strength high-elongation aluminum alloy sheet is an α (Al) matrix, bothUniformly distributed granular and/or short rod-shaped crystalline phase and punctiform fine disperse phase; nano-sized Mg is also present in the material when it is finished into an aluminum alloy part by post-forming paint baking or artificial aging2Metastable phase beta of Si, metastable phase Q' of Q-AlCuMgSi phase and theta-Al2Three precipitated phases of metastable phases theta' of Cu.
10. The method of claim 9, wherein the average grain size of the alpha (Al) matrix in the microstructure of the high strength aluminum alloy sheet is 30 μm or less.
11. The method of claim 9, wherein the average size of the granular and/or short rod-like crystal phases in the microstructure of the high-strength high-elongation aluminum alloy sheet is 3 μm or less.
12. The method of claim 9, wherein the point-like fine dispersion precipitated phase of the microstructure of the high-strength high-elongation aluminum alloy sheet comprises a submicron alpha-Al (Fe, Mn, Cu) Si phase and Al phase3A Zr phase.
13. The method as claimed in any one of claims 7 to 12, wherein the yield strength of the high-strength high-elongation aluminum alloy sheet after the solution treatment and the pre-aging treatment is 190 MPa and 230MPa, and the elongation A is50Not less than 25%; the yield strength is more than or equal to 320MPa after 2% pre-stretching and 185 ℃ heat preservation for 20min by simulating baking finish treatment, and the elongation A50More than or equal to 15 percent; the yield strength is more than or equal to 360MPa after the short-time artificial aging treatment is carried out at 190 ℃ for 4h, and the elongation A50≥10％。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810658850.9A CN110629075A (en) | 2018-06-25 | 2018-06-25 | High-strength high-elongation aluminum alloy plate and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810658850.9A CN110629075A (en) | 2018-06-25 | 2018-06-25 | High-strength high-elongation aluminum alloy plate and manufacturing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN110629075A true CN110629075A (en) | 2019-12-31 |
Family
ID=68966803
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810658850.9A Pending CN110629075A (en) | 2018-06-25 | 2018-06-25 | High-strength high-elongation aluminum alloy plate and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN110629075A (en) |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112410692A (en) * | 2020-11-28 | 2021-02-26 | 四川航天长征装备制造有限公司 | 2219 aluminum alloy grain refining process |
| CN113355616A (en) * | 2021-06-03 | 2021-09-07 | 苏州大学 | Heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains |
| CN113770180A (en) * | 2021-08-19 | 2021-12-10 | 山东理工大学 | Hot rolling method for refining 7000 series aluminum alloy thick plate grains |
| CN114107766A (en) * | 2020-08-26 | 2022-03-01 | 宝山钢铁股份有限公司 | Preparation method of novel high-performance 7XXX aluminum alloy thin strip |
| CN114101610A (en) * | 2020-08-26 | 2022-03-01 | 宝山钢铁股份有限公司 | Preparation method of particle-reinforced novel 6XXX aluminum alloy plate strip |
| EP3981893A1 (en) * | 2020-10-07 | 2022-04-13 | AMAG rolling GmbH | Plate made of a rolled aluminium alloy and production of such a plate |
| CN114411002A (en) * | 2022-01-25 | 2022-04-29 | 西安交通大学 | Preparation method of aluminum alloy |
| CN114807794A (en) * | 2021-01-28 | 2022-07-29 | 宝山钢铁股份有限公司 | Aluminum alloy product, manufacturing method thereof and automobile structural part |
| CN114807696A (en) * | 2021-01-28 | 2022-07-29 | 宝山钢铁股份有限公司 | Aluminum alloy plate, preparation method thereof and automobile component |
| CN115305394A (en) * | 2022-08-17 | 2022-11-08 | 上海锴朴机电有限公司 | Aluminum alloy material for high-pressure gas cylinder and preparation method thereof |
| CN115652151A (en) * | 2022-12-14 | 2023-01-31 | 中铝材料应用研究院有限公司 | 6xxx series aluminum alloy plate suitable for hot stamping forming integrated process, and preparation method and application thereof |
| CN115927983A (en) * | 2022-12-23 | 2023-04-07 | 苏州宇上实业有限公司 | Preparation method of 6 series aluminum alloy plate |
| CN116288085A (en) * | 2023-02-08 | 2023-06-23 | 常州工学院 | Heat treatment method for improving high-temperature strength of Al-Cu-Mn-Zr aluminum alloy |
| CN117867342A (en) * | 2024-01-15 | 2024-04-12 | 南京工业大学 | QP-II-based aluminum alloy with main strengthening phase and preparation method and application thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101851715A (en) * | 2009-03-31 | 2010-10-06 | 株式会社神户制钢所 | Aluminium alloy plate for battery case and battery case |
| CN101880805A (en) * | 2010-07-30 | 2010-11-10 | 浙江巨科铝业有限公司 | Al-Mg-Si aluminum alloy for automobile body panel and method for producing same |
| CN104745902A (en) * | 2013-12-30 | 2015-07-01 | 鼎镁（昆山）新材料科技有限公司 | High strength Al-Mg-Si-Cu alloy for bicycles and processing technology thereof |
| CN108118206A (en) * | 2016-11-30 | 2018-06-05 | 宝山钢铁股份有限公司 | Aluminum alloy plate materials and its manufacturing method with high natrual ageing stability and high baking hardenability |
-
2018
- 2018-06-25 CN CN201810658850.9A patent/CN110629075A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101851715A (en) * | 2009-03-31 | 2010-10-06 | 株式会社神户制钢所 | Aluminium alloy plate for battery case and battery case |
| CN101880805A (en) * | 2010-07-30 | 2010-11-10 | 浙江巨科铝业有限公司 | Al-Mg-Si aluminum alloy for automobile body panel and method for producing same |
| CN104745902A (en) * | 2013-12-30 | 2015-07-01 | 鼎镁（昆山）新材料科技有限公司 | High strength Al-Mg-Si-Cu alloy for bicycles and processing technology thereof |
| CN108118206A (en) * | 2016-11-30 | 2018-06-05 | 宝山钢铁股份有限公司 | Aluminum alloy plate materials and its manufacturing method with high natrual ageing stability and high baking hardenability |
Cited By (19)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114101610B (en) * | 2020-08-26 | 2023-01-20 | 宝山钢铁股份有限公司 | Preparation method of particle-reinforced 6XXX aluminum alloy plate strip |
| CN114107766A (en) * | 2020-08-26 | 2022-03-01 | 宝山钢铁股份有限公司 | Preparation method of novel high-performance 7XXX aluminum alloy thin strip |
| CN114101610A (en) * | 2020-08-26 | 2022-03-01 | 宝山钢铁股份有限公司 | Preparation method of particle-reinforced novel 6XXX aluminum alloy plate strip |
| EP3981893A1 (en) * | 2020-10-07 | 2022-04-13 | AMAG rolling GmbH | Plate made of a rolled aluminium alloy and production of such a plate |
| WO2022074153A1 (en) * | 2020-10-07 | 2022-04-14 | Amag Rolling Gmbh | Plate made of a rolled aluminium alloy and a method for producing said plate |
| CN112410692A (en) * | 2020-11-28 | 2021-02-26 | 四川航天长征装备制造有限公司 | 2219 aluminum alloy grain refining process |
| CN114807794A (en) * | 2021-01-28 | 2022-07-29 | 宝山钢铁股份有限公司 | Aluminum alloy product, manufacturing method thereof and automobile structural part |
| CN114807696A (en) * | 2021-01-28 | 2022-07-29 | 宝山钢铁股份有限公司 | Aluminum alloy plate, preparation method thereof and automobile component |
| CN113355616A (en) * | 2021-06-03 | 2021-09-07 | 苏州大学 | Heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains |
| CN113770180A (en) * | 2021-08-19 | 2021-12-10 | 山东理工大学 | Hot rolling method for refining 7000 series aluminum alloy thick plate grains |
| CN113770180B (en) * | 2021-08-19 | 2023-01-10 | 山东理工大学 | Hot rolling method for refining 7000 series aluminum alloy thick plate grains |
| CN114411002A (en) * | 2022-01-25 | 2022-04-29 | 西安交通大学 | Preparation method of aluminum alloy |
| CN115305394A (en) * | 2022-08-17 | 2022-11-08 | 上海锴朴机电有限公司 | Aluminum alloy material for high-pressure gas cylinder and preparation method thereof |
| CN115652151A (en) * | 2022-12-14 | 2023-01-31 | 中铝材料应用研究院有限公司 | 6xxx series aluminum alloy plate suitable for hot stamping forming integrated process, and preparation method and application thereof |
| CN115927983A (en) * | 2022-12-23 | 2023-04-07 | 苏州宇上实业有限公司 | Preparation method of 6 series aluminum alloy plate |
| CN116288085A (en) * | 2023-02-08 | 2023-06-23 | 常州工学院 | Heat treatment method for improving high-temperature strength of Al-Cu-Mn-Zr aluminum alloy |
| CN116288085B (en) * | 2023-02-08 | 2024-01-05 | 常州工学院 | Heat treatment method for improving high-temperature strength of Al-Cu-Mn-Zr aluminum alloy |
| CN117867342A (en) * | 2024-01-15 | 2024-04-12 | 南京工业大学 | QP-II-based aluminum alloy with main strengthening phase and preparation method and application thereof |
| CN117867342B (en) * | 2024-01-15 | 2024-07-19 | 南京工业大学 | QP-II-based aluminum alloy with main strengthening phase and preparation method and application thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110629075A (en) | High-strength high-elongation aluminum alloy plate and manufacturing method thereof | |
| CN110885942B (en) | Medium-strength 7xxx series aluminum alloy plate suitable for hot stamping forming-quenching integrated process | |
| CN100453671C (en) | Al-Mg-Si-Cu alloy for automobile and its production process | |
| WO2015109893A1 (en) | Al-mg-si-cu-zn series alloy of fast ageing response type and preparation method therefor | |
| WO2015127805A1 (en) | High temperature baking hardened aluminum alloy material used for automobile body and preparation method thereof | |
| CN111575548B (en) | 6-series aluminum alloy automobile outer plate with excellent comprehensive performance and preparation method thereof | |
| CN109897995B (en) | High-strength high-plasticity aluminum alloy plate and manufacturing method thereof | |
| WO2014169585A1 (en) | Aluminum alloy material suitable for manufacturing of automobile sheet, and preparation method therefor | |
| CN111593239B (en) | Low-cost high-formability aluminum alloy plate for vehicle body structure and preparation method thereof | |
| CN106521253A (en) | High-formability Al-Mg-Si alloy and manufacturing method thereof | |
| CN109055698B (en) | 6XXX aluminum alloy suitable for automobile body and preparation process of automobile body plate | |
| CN112458344B (en) | High-strength corrosion-resistant aluminum alloy and preparation method and application thereof | |
| CN110983129B (en) | Integrated process regulation and control method for improving automobile aluminum alloy plate flanging performance | |
| CN111057980A (en) | Process control method for high-formability aluminum alloy heterogeneous structure for automobile | |
| WO2024183265A1 (en) | Lightweight, high-strength, corrosion-resistant aluminum alloy material and preparation method thereof | |
| JPWO2019167469A1 (en) | Al-Mg-Si based aluminum alloy material | |
| CN103255323B (en) | Al-Mg-Zn-Cu alloy and preparation method thereof | |
| CN114438356A (en) | Preparation method of high-strength, corrosion-resistant and high-toughness Al-Mg-Zn-Ag (-Cu) aluminum alloy | |
| JP2024010058A (en) | High-strength, highly formable aluminum alloys and methods of making the same | |
| CN111074121B (en) | Aluminum alloy and preparation method thereof | |
| US6344096B1 (en) | Method of producing aluminum alloy sheet for automotive applications | |
| WO2023246736A1 (en) | Method for manufacturing al-zn-mg-cu series aluminum alloy plate, and aluminum alloy plate | |
| WO2024124736A1 (en) | 6xxx-series aluminum alloy plate suitable for hot stamping forming and formability integrated process, and preparation method therefor and use thereof | |
| CN112877554A (en) | Preparation method of high-strength and high-toughness easy-welding corrosion-resistant Al-Mg-Zn-Cu alloy | |
| CN112626384A (en) | Aluminum alloy with medium strength and high plasticity as well as preparation method and application thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20191231 |