Alloy preparation method for improving mechanical property based on 6110 aluminum alloy component optimization

Abstract

The invention discloses an alloy preparation method for improving mechanical properties based on 6110 aluminum alloy component optimization, and relates to the technical field of 6110 aluminum alloy preparation, and the alloy preparation method comprises the following steps: step 1, the 6110 aluminum alloy component is subjected to optimization design, and the 6110 aluminum alloy comprises the following components in percentage by weight: the balance of Al serving as a matrix element; and 0.05-0.1% of Cr, wherein the Cr is used for refining crystal grains. By controlling the proportion of Si / Mg and Cu / Fe key elements, the strengthening potential and the structure stability of the alloy are optimized, gradient heating smelting and composite refining technologies are combined, the melt purity and the component uniformity are improved, element burning loss is effectively reduced, crystal segregation is fully eliminated through multi-stage homogenization treatment, a uniform microcosmic foundation is laid for follow-up treatment, and the high-strength and high-toughness alloy is obtained. An ultrasonic external field is introduced into the dynamic solid solution process, and the cavitation and acoustic streaming effects of the ultrasonic external field are utilized to promote the dissolution of a strengthening phase, so that a supersaturated solid solution with higher saturation and more uniform components is obtained.

Description

TECHNICAL FIELD

[0001] The application relates to the technical field of 6110 aluminum alloy preparation, and in particular to an alloy preparation method for improving mechanical properties based on composition optimization of a 6110 aluminum alloy. BACKGROUND

[0002] As a key material for vehicle lightening, the traditional preparation process of the 6110 aluminum alloy faces core bottlenecks. Firstly, magnesium element is seriously burned in the conventional smelting process, leading to composition fluctuation and affecting performance stability. Secondly, coarse needle-shaped iron-rich phases are easily formed in the alloy due to unavoidable iron impurities, which seriously cut the matrix and deteriorate the toughness. Finally, the traditional single-stage homogenization and aging system is difficult to fully eliminate micro-segregation and precisely control the dispersion precipitation of nanometer strengthening phases, so that the strength and plasticity are difficult to be simultaneously improved. Although the existing technology can be optimized by adjusting the content of main elements, it cannot fundamentally solve the above problems through key element proportion coordination control and multi-field coupling process. SUMMARY

[0003] In order to solve the above problems, the application provides an alloy preparation method for improving mechanical properties based on composition optimization of a 6110 aluminum alloy.

[0004] The alloy preparation method for improving mechanical properties based on composition optimization of a 6110 aluminum alloy provided by the application adopts the following technical scheme:

[0005] The alloy preparation method for improving mechanical properties based on composition optimization of a 6110 aluminum alloy comprises the following steps:

[0006] Step one, optimizing the composition of the 6110 aluminum alloy, the 6110 aluminum alloy contains the following components in terms of weight percentage:

[0007] Al: balance, Al as a matrix element;

[0008] Cr: 0.05-0.1%, Cr for refining grains;

[0009] Cu: 0.72-0.8%, Cu for participating in the formation of strengthening phases;

[0010] Fe: 0.07-0.35%, Fe for improving high-temperature performance;

[0011] Mg: 0.7-0.75%, Mg for leading aging strengthening;

[0012] Mn: 0.68-0.73%, Mn for inhibiting grain coarsening;

[0013] Ni: Ni≤0.1%, Ni for controlling impurity content;

[0014] Si: 0.98-1.07%, Si is used to promote the formation of strengthening phase;

[0015] Ti: 0.01-0.1%, Ti is used to refine the as-cast structure;

[0016] Zn: 0.1-0.15%, Zn is used for secondary strengthening;

[0017] Step two, gradient temperature melting;

[0018] Step three, composite refining treatment;

[0019] Step four, multi-stage homogenization treatment;

[0020] Step five, dynamic solid solution treatment;

[0021] Step six, graded aging strengthening.

[0022] As a preferred technical solution of the application, in step one, the Si / Mg ratio is 1.31-1.53, and the Cu / Fe ratio is 2.06-11.43;

[0023] In step two, the gradient temperature melting adopts a two-stage temperature rising process, first rapidly rising to an intermediate temperature for holding, and then slowly rising to the final melting temperature, and the residence time of each temperature interval in the rising process is strictly controlled;

[0024] In step three, the composite refining treatment adopts a composite refining method combining gas refining and solid refining agent, and the refining agent is added in batches during refining to ensure the purity of the melt;

[0025] In step four, the multi-stage homogenization treatment is a homogenization process with three temperature stages, and a specific heating rate is used to transition between stages;

[0026] In step five, during the dynamic solid solution treatment, an external physical field is applied during the solid solution holding stage, and the physical field parameters and the solid solution temperature form a synergistic relationship;

[0027] In step six, the graded aging strengthening adopts a graded aging system combining low-temperature pre-aging and high-temperature main aging, and an auxiliary external field is applied during the aging process.

[0028] As a preferred technical solution of the application, the specific process of step two is to rise from room temperature to an intermediate temperature range at a first heating rate, hold at the intermediate temperature for a specific time, and then rise to the final melting temperature at a second heating rate, with the final melting temperature controlled within a specific range.

[0029] As the preferred technical solution of the present application, the specific process of step three is to first perform gas refining treatment, then add a specific proportion of composite solid refining agent, and the refining agent is added three times with a fixed time interval, and the refining temperature is controlled within a specific range.

[0030] As the preferred technical solution of the present application, the specific process of step four is that the first stage homogenization treatment temperature is controlled within a first specific range, the second stage homogenization treatment temperature is higher than the first stage by a specific value, and the third stage homogenization treatment temperature is higher than the second stage by a specific value, and the holding time of each stage is distributed in proportion during the treatment.

[0031] As the preferred technical solution of the present application, the specific process of step five is that the solution treatment temperature is controlled within a specific range, the external physical field in step five is an ultrasonic field, the ultrasonic frequency generated by the ultrasonic field is adjusted according to the material thickness, and the ultrasonic amplitude generated by the ultrasonic field and the temperature form a dynamic matching relationship.

[0032] As the preferred technical solution of the present application, the specific process of step six is that the pre-aging temperature is controlled within a first specific range, the main aging temperature is controlled within a second specific range, a specific heating rate is used between pre-aging and main aging, and the auxiliary field in step six is a static magnetic field.

[0033] As the preferred technical solution of the present application, an aluminum alloy includes a 6110 aluminum alloy, a titanium-containing phase with a specific morphology is formed at the grain boundary of the 6110 aluminum alloy, a magnesium-silicon strengthening phase with a specific size is uniformly distributed in the intracrystalline of the 6110 aluminum alloy, the base structure of the 6110 aluminum alloy has no obvious segregation phenomenon, the titanium-containing phase of the 6110 aluminum alloy is in a rod-like structure and the aspect ratio is controlled within a specific range, the magnesium-silicon strengthening phase of the 6110 aluminum alloy is in a spherical shape and the average spacing is controlled within a specific range, and the strengthening phase size of the 6110 aluminum alloy is uniformly distributed within a nanometer range.

[0034] In summary, the present application includes at least the following alloy preparation method which optimizes the mechanical properties based on the composition of the 6110 aluminum alloy:

[0035] The application optimizes the strengthening potential and organizational stability of the alloy by controlling the key element ratio of Si / Mg and Cu / Fe, improves the melt purity and composition uniformity by combining gradient temperature melting and composite refining technology, effectively reduces element burning loss, and fully eliminates intracrystalline segregation by multi-stage homogenization treatment, laying a uniform micro foundation for subsequent treatment. The dynamic solid solution process introduces an ultrasonic field, which uses cavitation and acoustic streaming effects to promote the dissolution of strengthening phases, resulting in a more saturated and uniform supersaturated solid solution. During the staged aging process, the static magnetic field is coupled to control the precipitation behavior of the nano-strengthening phase, resulting in a uniform distribution of the nano-strengthening phase in the crystal. The 6110 aluminum alloy prepared by the application realizes excellent matching of strength and plasticity, and the microstructure characteristics are characterized by the presence of nanoscale spherical Mg2Si strengthening phases in the crystal, regular titanium-containing phases at the grain boundaries, and no significant segregation in the matrix. The comprehensive mechanical properties are improved. BRIEF DESCRIPTION OF DRAWINGS

[0036] Fig. 1 is a schematic diagram of the composition of the 6110 aluminum alloy of the application;

[0037] Fig. 2 is a flowchart of the alloy preparation method based on the composition optimization of the 6110 aluminum alloy to improve the mechanical properties. DETAILED DESCRIPTION

[0038] The following will be described in detail in combination with the accompanying Figs. 1-2 The application will be further described in detail.

[0039] Reference should be made to Figs. 1-2 The alloy preparation method based on the composition optimization of the 6110 aluminum alloy to improve the mechanical properties includes the following steps:

[0040] Step one, the composition of the 6110 aluminum alloy is optimized and designed, and the 6110 aluminum alloy contains the following components by weight percentage:

[0041] Al: balance, Al as the matrix element; Cr: 0.05-0.1%, Cr for grain refinement; Cu: 0.72-0.8%, Cu for participating in the formation of strengthening phases; Fe: 0.07-0.35%, Fe for improving high temperature performance; Mg: 0.7-0.75%, Mg for leading aging strengthening; Mn: 0.68-0.73%, Mn for inhibiting grain coarsening; Ni: Ni≤0.1%, Ni for controlling impurity content; Si: 0.98-1.07%, Si for promoting the formation of strengthening phases; Ti: 0.01-0.1%, Ti for refining the as-cast structure; Zn: 0.1-0.15%, Zn for auxiliary strengthening;

[0042] Step two, gradient temperature melting;

[0043] Step three, composite refining treatment;

[0044] Step four, multi-stage homogenization treatment;

[0045] Step five, dynamic solid solution treatment;

[0046] Step six, graded aging strengthening;

[0047] In step one, the Si / Mg ratio is 1.31-1.53, and the Cu / Fe ratio is 2.06-11.43; in step two, the gradient temperature melting adopts a two-stage temperature rising process, first rapidly rising to an intermediate temperature for holding, and then slowly rising to the final melting temperature, and the residence time in each temperature interval is strictly controlled during the temperature rising process; in step three, the composite refining treatment adopts a composite refining method combining gas refining and solid refining agent, and the refining agent is added in batches during refining to ensure the purity of the melt; in step four, the multi-stage homogenization treatment is a homogenization process with three temperature stages, and a specific heating rate is used for transition between stages; in step five, during the dynamic solid solution treatment, an external physical field is applied during the solid solution holding stage, and the physical field parameters and the solid solution temperature form a synergistic relationship; in step six, the graded aging strengthening adopts a graded aging system combining low-temperature pre-aging and high-temperature main aging, and an auxiliary external field is applied during the aging process;

[0048] The present application optimizes the strengthening potential and microstructure stability of the alloy by calculating and balancing the proportions of key elements. The present application introduces two key control parameters, Si / Mg ratio (1.31-1.53) and Cu / Fe ratio (2.06-11.43). During preparation, high-purity aluminum ingots, aluminum-silicon intermediate alloy, aluminum-copper intermediate alloy, pure magnesium ingots, and other element intermediate alloys are used as raw materials. The Si content is controlled at 1.02wt%, the Mg content is controlled at 0.72wt%, the Si / Mg ratio is 1.42, which ensures the formation of sufficient and fine Mg2Si strengthening phase during subsequent aging process, avoids the formation of coarse or other harmful intermetallic compounds due to excessive Si or Mg, thereby maximizing the aging strengthening effect. The Cu content is set to 0.76wt%, the Fe content is set to 0.15wt%, and the Cu / Fe ratio is 5.07, which can effectively inhibit the formation and growth of needle-shaped or flaky iron-rich phases. Cu will preferentially form finer and more rounded α-Al(Fe,Cu,Mn)Si phases with Fe, Al, etc., thereby reducing the harmful effects of iron phases and improving the toughness and high-temperature performance of the alloy. The composition design based on the synergistic control of key proportions lays a good thermodynamic foundation for subsequent all heat treatment processes;

[0049] The specific process of step two is to rise from room temperature to an intermediate temperature range at a first heating rate, hold at the intermediate temperature for a certain time, and then rise to the final melting temperature at a second heating rate. The final melting temperature is controlled within a certain range;

[0050] In the present application, the prepared furnace charge is loaded into a medium-frequency induction melting furnace. First, rapid heating is performed at a first heating rate (set to 280°C / h) to rapidly raise the furnace charge from room temperature to an intermediate temperature range (700±10°C). The furnace charge is held at this temperature for 40 minutes. The purpose of this stage is to fully melt the low-melting-point components (such as magnesium, silicon, etc.) and initiate diffusion, while preliminarily dissolving the high-melting-point components (such as intermetallic compounds) and preliminarily homogenizing the composition using the convection of the melt. Subsequently, the heating rate is switched to a lower second heating rate (120°C / h) to slowly and smoothly raise the melt to the final melting temperature (760±5°C). Through the above process, the violent boiling and rolling of the melt caused by sudden temperature rise are avoided, thereby reducing the evaporation loss of magnesium (boiling point of Mg is only 1090°C, which is easily volatile in high-temperature melt) and the absorption of gases (such as hydrogen) by the melt. During the entire heating process, the temperature control system controls the residence time in each temperature range to ensure that the elements are fully dissolved while the high-temperature exposure time is minimized to protect the quality of the melt. Compared with the traditional one-step melting method, the present method has higher purity and more uniform composition of the melt.

[0051] The specific process of step three is to perform gas refining treatment first, then add a specific proportion of composite solid refining agent, and the refining agent is added three times with a fixed time interval. The refining temperature is controlled within a specific range during refining;

[0052] In the present application, after the melt reaches the final temperature (760°C) and is stationary for 10 minutes, high-purity argon gas is first introduced into the bottom of the melt at a flow rate of 5 L / min through a graphite rotary lance, with a rotary speed of 400 rpm, and the treatment is continued for 20 minutes. The argon bubbles can effectively adsorb hydrogen atoms (H) and oxidized inclusions in the melt during the floating process and carry them to the liquid surface. After gas refining is completed, a covering agent is scattered on the surface of the melt and is stationary for 5 minutes to allow the inclusions to float and gather. Then, a specific proportion of composite refining agent (composed of 40% Na2SiF6, 30% K2TiF6, 20% C2Cl6, and 10% Na3AlF6) is added. This formulation not only efficiently removes gas and inclusions, but also supplements Ti elements to refine grains. The refining agent is added in three batches, with each batch accounting for 1 / 3 of the total refining agent amount, and each addition is separated by a fixed time interval (8 minutes). After each addition, the melt is slowly stirred for 2 minutes using a graphite paddle to ensure sufficient reaction. The entire refining process ensures that the refining temperature is strictly controlled within a specific range of 755-765°C. The refining agent has the highest activity and the best refining effect in this temperature range. The batch addition method avoids the temperature drop caused by single large addition and the melt splashing caused by violent reaction, ensuring thorough and stable refining.

[0053] The specific process of step four is that the temperature of the first stage of homogenization treatment is controlled in a first specific range, the temperature of the second stage of homogenization treatment is increased by a specific value compared with the first stage, and the temperature of the third stage of homogenization treatment is increased by a specific value compared with the second stage, and the holding time of each stage is ensured to be proportionally distributed;

[0054] In the application, the alloy ingot obtained by casting is placed in a precision circulating air heat treatment furnace for three-stage treatment.

[0055] The temperature of the first stage of homogenization treatment is controlled in the range of 500-520°C, and the low-melting-point non-equilibrium phase (such as Mg-Si phase, Al-Cu phase, etc.) is first dissolved into the α-Al matrix at this temperature for 8 hours, and then slowly heated to the temperature of the second stage of homogenization treatment (535-545°C) at a specific heating rate (50°C / h), and the holding time in this stage is 10 hours, the purpose is to further spheroidize and dissolve the high-melting-point iron-rich phase (such as AlFeSi phase) and AlCu phase which are more difficult to dissolve, and then slowly heated to the temperature of the third stage of homogenization treatment (555-565°C) at a rate of 50°C / h, and the holding time at this highest temperature is 6 hours, which maximizes the elimination of intragranular segregation and makes the remaining difficult-to-dissolve phase smaller and more rounded, and the holding time of each stage is proportionally distributed (about 4:5:3), and the total time is 24 hours, and the multi-stage progressive heating method avoids the risk of excessive grain growth or overburning caused by single high-temperature homogenization, and realizes sufficient and safe atomic diffusion.

[0056] The specific process of step five is that the solid solution treatment temperature is controlled in a specific range, the external physical field in step five is an ultrasonic field, the ultrasonic frequency generated by the ultrasonic field is adjusted according to the thickness of the material, and the ultrasonic amplitude generated by the ultrasonic field forms a dynamic matching relationship with the temperature;

[0057] In the application, the cavitation effect and acoustic streaming effect are used to greatly promote the dissolution kinetics of the strengthening phase, and dynamic solid solution is realized. The plate sample after homogenization and hot rolling is placed in a special ultrasonic assisted heat treatment furnace, and the solid solution treatment temperature is strictly controlled at the upper limit of the solid solution window (545±3°C) of the alloy. When the furnace temperature reaches the set value and stabilizes, the ultrasonic generator is started, the ultrasonic frequency is adjusted according to the thickness of the material, and the ultrasonic field is ensured to generate effective standing wave field in the thickness direction of the sample, and the energy distribution is uniform.

[0058] In the initial stage of solution heat preservation (first 10 minutes), a higher amplitude (15 pm) is adopted to break the unsolved coarse second phase particles by using strong cavitation effect, in the middle stage of solution heat preservation (10-30 minutes), the amplitude is adjusted to medium (10 pm) to continuously promote phase dissolution and composition homogenization, in the later stage of solution heat preservation (last 10 minutes), a low amplitude (5 pm) is adopted to mainly use acoustic streaming effect to maintain the uniformity of the melt and prevent grain growth, so as to reduce the time required for solution, and the obtained supersaturated solid solution has higher saturation and more uniform composition, which improves the strengthening potential of subsequent aging and refines the grains.

[0059] The specific process of step six is that the pre-aging temperature is controlled in a first specific range, the main aging temperature is controlled in a second specific range, a specific heating rate is adopted between the pre-aging and the main aging, and the auxiliary external field in step six is a static magnetic field.

[0060] In the present application, the precipitation behavior of the strengthening phase is accurately controlled through the coupling of space-time and field to obtain the best mechanical property matching. After solution water quenching, the sample is immediately transferred to an aging furnace, pre-aging treatment is first performed, the temperature is controlled at 80±2°C, and a 0.5 T vertical static magnetic field is applied. The static magnetic field exists for 10 hours at this low temperature stage, and the diffusion of solute atoms is affected by the static magnetic field, which promotes the formation of GP zones or pre-precipitation clusters with extremely high density, providing a large number of uniform nucleation sites for subsequent precipitation. Then, the temperature is slowly increased to the main aging treatment temperature (175±2°C) at a specific heating rate (25°C / h). Slow heating avoids the dissolution or coarsening of the fine pre-precipitation phase formed due to rapid heating. The static magnetic field is continuously applied during the main aging at the temperature, and the static magnetic field can effectively inhibit the preferential precipitation and growth of the strengthening phase along the grain boundaries and other unfavorable positions by affecting the Lorentz force of charged atoms and their diffusion paths, and promote the uniform precipitation of the strengthening phase in the grains, and make the size of the strengthening phase more fine and the distribution more dispersed. Finally, the size of the strengthening phase of the obtained alloy is uniformly distributed in the nanometer range, realizing the excellent combination of strength and plasticity.

[0061] An aluminum alloy includes a 6110 aluminum alloy, a titanium-containing phase with a specific morphology is formed at the grain boundary of the 6110 aluminum alloy, a magnesium-silicon strengthening phase with a specific size is uniformly distributed in the grain of the 6110 aluminum alloy, the matrix structure of the 6110 aluminum alloy has no obvious segregation phenomenon, the titanium-containing phase of the 6110 aluminum alloy is in a rod-like structure and the aspect ratio is controlled in a specific range, the magnesium-silicon strengthening phase of the 6110 aluminum alloy is in a spherical shape and the average spacing is controlled in a specific range, and the size of the strengthening phase of the 6110 aluminum alloy is uniformly distributed in the nanometer range.

[0062] The application optimizes the strengthening potential and microstructure stability of the alloy by controlling the Si / Mg and Cu / Fe key element ratios (1.42 and 5.07 respectively), improves the melt purity and composition uniformity by combining gradient temperature melting and composite refining technology, effectively reduces the element burning loss, fully eliminates the intracrystalline segregation by multi-stage homogenization treatment, lays a uniform microstructure foundation for subsequent processing, introduces an ultrasonic field in the dynamic solid solution process, uses the cavitation and acoustic streaming effect to promote the dissolution of the strengthening phase, and obtains a supersaturated solid solution with higher saturation and more uniform composition, and the nanometer strengthening phase is uniformly distributed in the intracrystalline by coupling the static magnetic field in the staged aging process, so that the application realizes the excellent matching of strength and plasticity of the 6110 aluminum alloy, the microstructure characteristics of which are that the nanometer spherical Mg2Si strengthening phase is distributed in the intracrystalline, the regular titanium-containing phase is at the grain boundary, and the matrix has no significant segregation, so that the comprehensive mechanical properties are improved.

[0063] The above are preferred embodiments of the application, and are not intended to limit the protection scope of the application, therefore: any equivalent changes made on the structure, shape and principle of the application shall be covered within the protection scope of the application.

Claims

1. A method for preparing an alloy based on the composition of 6110 aluminum alloy to optimize the mechanical properties, characterized in that: The method comprises the following steps: Step one, optimizing the composition of 6110 aluminum alloy, the 6110 aluminum alloy comprises the following components in percentage by weight: Al: balance, Al as a base element; Cr: 0.05-0.1%, Cr for grain refinement; Cu: 0.72-0.8%, Cu for participating in the formation of strengthening phase; Fe: 0.07-0.35%, Fe for improving high-temperature performance; Mg: 0.7-0.75%, Mg for leading aging strengthening; Mn: 0.68-0.73%, Mn for inhibiting grain coarsening; Ni: Ni≤0.1%, Ni for controlling impurity content; Si: 0.98-1.07%, Si for promoting the formation of strengthening phase; Ti: 0.01-0.1%, Ti for refining as-cast structure; Zn: 0.1-0.15%, Zn for auxiliary strengthening; Step two, gradient temperature melting; Step three, composite refining treatment; Step four, multi-stage homogenization treatment; Step five, dynamic solid solution treatment; Step six, graded aging strengthening.

2. The method for preparing an alloy based on the 6110 aluminum alloy component to optimize the mechanical properties according to claim 1, characterized in that: In step one, the Si / Mg ratio is 1.31-1.53, and the Cu / Fe ratio is 2.06-11.43; In step two, the gradient temperature melting adopts a two-stage temperature rising process, first rapidly rising to an intermediate temperature for holding, and then slowly rising to the final melting temperature, and the residence time at each temperature interval is strictly controlled during the temperature rising process; In step three, the composite refining treatment adopts a composite refining method combining gas refining and solid-state refining agent, and the refining agent is added in batches to ensure the purity of the melt; In step four, the multi-stage homogenization treatment is a homogenization process with three temperature stages, and a specific temperature rising rate is used for transition between stages; In step five, during the dynamic solid solution treatment, an external physical field is applied during the solid solution holding stage, and the physical field parameters and the solid solution temperature form a synergistic relationship; In step six, the graded aging strengthening adopts a graded aging system combining low-temperature pre-aging and high-temperature main aging, and an auxiliary external field is applied during the aging process.

3. The method according to claim 2, wherein the method is characterized by: The specific process of step two is to rise from room temperature to the intermediate temperature interval at a first temperature rising rate, hold at the intermediate temperature for a specific time, and then rise to the final melting temperature at a second temperature rising rate, with the final melting temperature controlled within a specific range.

4. The method according to claim 3, wherein the method is characterized by: The specific process of step three is to first perform gas refining treatment, then add a specific proportion of composite solid-state refining agent, and the refining agent is added in three batches with a fixed time interval, and the refining temperature is controlled within a specific range during refining.

5. The method according to claim 4, wherein the method is characterized by: The specific process of step four is that the first stage homogenization treatment temperature is controlled within a first specific range, the second stage homogenization treatment temperature is increased by a specific value compared to the first stage, and the third stage homogenization treatment temperature is increased by a specific value compared to the second stage, and the holding time of each stage is distributed proportionally during the treatment.

6. The method according to claim 5, wherein the method is characterized by: The specific process of step five is to control the solid solution treatment temperature within a specific range, and the external physical field in step five is an ultrasonic field, the ultrasonic frequency generated by the ultrasonic field is adjusted according to the material thickness, and the ultrasonic amplitude generated by the ultrasonic field forms a dynamic matching relationship with the temperature.

7. The method according to claim 6, wherein the method is characterized by: The specific process of step six is that the pre-aging temperature is controlled in a first specific range, the main aging temperature is controlled in a second specific range, a specific heating rate is adopted between the pre-aging and the main aging, and the auxiliary external field in step six is a static magnetic field.

8. An aluminum alloy, prepared by the method of claim 7, wherein the alloy is based on the composition of 6110 aluminum alloy and is optimized to improve mechanical properties. The 6110 aluminum alloy includes a titanium-containing phase with a specific morphology formed at a grain boundary, a magnesium-silicon strengthening phase with a specific size uniformly distributed in a grain, a base structure without obvious segregation, a rod-shaped titanium-containing phase with a specific aspect ratio, a spherical magnesium-silicon strengthening phase with a specific average interval, and a strengthening phase with a size uniformly distributed in a nanometer range.

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