CN114351014B - Aluminum alloy and preparation method and application thereof - Google Patents
Aluminum alloy and preparation method and application thereof Download PDFInfo
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Abstract
The invention discloses an aluminum alloy and a preparation method and application thereof, wherein the aluminum alloy comprises the following components in percentage by weight: 0.05 to 0.30 percent of Cu, 0.25 to 0.35 percent of Mn, 0.10 to 0.13 percent of Cr, 0.02 to 0.08 percent of La, 0.02 to 0.08 percent of Zr, 0.78 to 0.88 percent of Si, 0.62 to 0.82 percent of Mg, 0.010 to 0.04 percent of Ti and the balance of Al. The aluminum alloy of the invention has small resistance to extrusion deformation and smooth extrusion. Meanwhile, certain strength is obtained, and the method is suitable for manufacturing complex multi-cavity thin-wall aluminum alloy sections.
Description
Technical Field
The invention relates to the technical field of aluminum alloy, in particular to an aluminum alloy and a preparation method and application thereof.
Background
The aluminum alloy is a non-ferrous metal structural material which is most widely applied in industry, and can be processed into various sectional materials due to low density, high strength and good plasticity; aluminum alloys also have excellent electrical conductivity, thermal conductivity, corrosion resistance, and the like, and are widely used in the machine manufacturing, transportation machinery, power machinery, and aviation industry.
At present, the length of an aluminum alloy section for vehicles, such as an aluminum alloy section for a new energy battery box, is mostly between 1000 and 2500mm, and because the aluminum alloy section needs to meet the matching requirements between the sections and other parts, the section of the section is mostly in a complex multi-cavity thin-wall structure, and the aluminum alloy section has strict requirements on shape and position and size precision. At present, the yield strength of the aluminum alloy is mostly about 260MPa, so that no method is provided for further improving the related performance, meeting the requirements of wall reduction and realizing the purposes of light weight and production of complex multi-cavity thin-wall aluminum alloy sections.
It is therefore desirable to provide a thin-walled aluminum alloy suitable for the manufacture of complex multi-cavities.
Disclosure of Invention
The present invention is directed to solving at least one of the problems of the prior art described above. Therefore, the aluminum alloy provided by the invention has the advantages that through the compounding of the raw materials, the aluminum alloy has high strength, excellent thermal stability, stress corrosion resistance, spalling corrosion resistance, fatigue strength and high strength of a welded joint, has low quenching sensitivity, and is suitable for manufacturing complex multi-cavity thin-wall aluminum alloys.
The invention also provides a preparation method of the aluminum alloy.
The invention also provides an application of the aluminum alloy in the automotive section.
According to one aspect of the invention, the aluminum alloy comprises the following components in percentage by weight: 0.05 to 0.30 percent of Cu, 0.25 to 0.35 percent of Mn, 0.10 to 0.13 percent of Cr, 0.02 to 0.08 percent of La, 0.02 to 0.08 percent of Zr, 0.78 to 0.88 percent of Si, 0.62 to 0.82 percent of Mg, 0.010 to 0.04 percent of Ti, and the balance of Al and impurities;
the aluminum alloy of the invention has at least the following beneficial effects:
1. the invention solves the contradiction between the strength, the extrusion performance and the comprehensive performance of the aluminum alloy by designing the specific alloy composition, so that the aluminum alloy has certain strength and excellent extrusion and comprehensive application performance. The tensile strength of the aluminum alloy provided by the invention is 300-400MPa, and the requirement of complex multi-cavity thin-wall aluminum alloy is met.
2. In aluminum alloys, si and Mg are the main alloying elements forming the strengthening phase, and both form Mg when present together 2 Si as an equivalent strengthening phase, mg 2 The Si precipitation phase is easy to dissolve in a solid state, so the solid solution heat treatment is simple, the solid solution effect can be achieved by adopting an on-line quenching mode, and the tensile strength is increased along with the increase of the contents of Si and Mg. The aluminum alloy contains proper amount of Si element, so that Mg is fully utilized to form Mg 2 When the Si precipitates a strengthening phase, the residual Si not only can improve the age hardening effect of the material, but also can improve the extrusion performance of the material and increase the high-temperature fluidity of the alloy, so that the difficulty of extruding the hollow thin-wall profiled bar by the material is greatly reduced. Meanwhile, the extrusion is carried out on-line quenching (such as strong air cooling, water mist cooling and water cooling) without sacrificing the mechanical property, so that the dimensional precision and the mechanical property of the final product can be ensured.
The Cu can improve the dispersion degree of a precipitation phase in the aluminum alloy and also can play a role in solid solution strengthening, the application range of the invention is controlled to be 0.05-0.30%, so that the alloy has good comprehensive performance, and the addition amount of the Cu is controlled on the premise of ensuring high strength.
4.Mn can play a certain strengthening effect in the alloy, and simultaneously can also be MnAl in the homogenization treatment process 6 The dispersed phase is precipitated, and the phase can effectively prevent the recrystallization of crystal grains in the process of hot working or heat treatment, thereby promoting the material to form fibrous structures.
La can effectively refine the crystal grains of the cast rod in the casting stage, the strength and the toughness of the material, the processing performance of the material is improved, the material is not easy to crack in the extrusion process, and the formed Al-La compound can also become Mg 2 The Si precipitates the nucleation points of the strengthening phase, further improves the strength of the material, can effectively refine the grains of the welding line in the welding process, and improves the welding strength of the material. However, excessive La is agglomerated with Ti to affect the casting grains and acts with Si to affect the strengthening phase, and is concentrated on the grain boundary to affect the corrosion resistance of the material, so the addition amount is strictly controlled.
6. The composite addition of Zr can effectively reduce the cost while ensuring the favorable effect of a dispersed phase, and more importantly, the composite addition of Zr can better control the crystal grains of the material and improve the strength of the material through experimental verification.
The main function of Ti is to refine the grain structure of the welding seam, reduce the welding crack tendency and improve the welding seam strength.
In some embodiments of the invention, the sum of the weight percentages of La and Zr is not higher than 0.12% of the total weight, in weight percentages.
In some embodiments of the invention, the sum of the weight percentages of Mn, cr, la, and Zr is no more than 0.48% of the total weight.
In some embodiments of the present invention, the weight ratio of the Mn to the Cr is 2.2 to 3.
The composite addition of Cr and Mn can more effectively inhibit the crystal grain nucleation and recrystallization of the material in the hot working or heat treatment process, can promote the material to form a fibrous structure besides precipitation strengthening, and can greatly improve the fatigue strength and other properties of the material, but Cr can greatly improve the quenching sensitivity of the material, so that the Cr and Mn need to be added in a matching way, and the addition ratio of Mn to Cr is set to be 2.2-3 in the invention, so that the benefits and the brought negative effects of Cr elements can be better balanced.
In some embodiments of the invention, the aluminum alloy section is a multi-cavity thin-walled structure.
In some embodiments of the invention, the impurities comprise: fe.
In some embodiments of the invention, the weight percent of iron is not greater than 0.2% by weight percent.
Mn can effectively promote spheroidization of Fe phase into spherical alpha (Fe, mn) Al 6 And the adverse effects of the original needle-shaped Fe on the properties of materials such as extrusion, welding, fatigue, machinery and the like are improved.
In some embodiments of the invention, the aluminum alloy has a tensile strength of 300 to 400MPa.
The second aspect of the invention provides a preparation method of an aluminum alloy, which comprises the following steps:
s1: melting and casting an aluminum ingot and a preparation raw material containing Cu, mn, cr, la, zr, si, mg and Ti to obtain an aluminum alloy ingot;
s2: carrying out three-stage homogenization treatment on the aluminum alloy ingot obtained in the step S1;
s3: extruding the aluminum alloy ingot obtained in the step S2;
s4: and (4) carrying out artificial aging treatment on the cast ingot obtained in the step (S3).
The preparation method of the aluminum alloy at least has the following beneficial effects:
1. the aluminum alloy has small extrusion deformation resistance and smooth extrusion. Meanwhile, certain strength is obtained, and the method is suitable for the requirement of manufacturing complex multi-cavity thin-wall aluminum alloy sections.
In some embodiments of the invention, step S1 comprises the steps of:
s1a: heating and melting Al;
s1b: adding Al-Si intermediate alloy, mg, al-La, al-Zr intermediate alloy, cu, mn, cr and Al-Ti intermediate alloy into the melt obtained in the step S1a, and controlling the mass content of Ti to be 0.005-0.025%;
s1c: adding a refining agent into the melt obtained in the S1b for refining;
s1d: then Ti is added in an Al-Ti-B wire rod mode, and the mass content of the Ti is controlled to be 0.010-0.04%.
S1e: the melt obtained in step S1d is subjected to a purification.
S1f: and casting the melt IV obtained in the step S1 e.
In some embodiments of the invention, the temperature of the melting in step S1a is 750 to 800 ℃.
In some embodiments of the invention, the temperature of step S1b is from 750 to 800 ℃.
In some embodiments of the invention, the temperature of the refining in step S1c is 730 to 750 ℃.
In some embodiments of the invention, the refining time in step S1c is 20 to 45min.
In some embodiments of the invention, in step S1c, the refining is performed under an inert gas atmosphere.
In some embodiments of the invention, the inert atmosphere comprises argon.
In some embodiments of the invention, in step S1e, the purifying comprises at least one of degassing purifying and filtering purifying.
In some preferred embodiments of the invention, the degassing purification is performed in a box degassing unit.
In some preferred embodiments of the invention, the filtration purification is performed in an 80 mesh ceramic foam filter panel and an RD tube filter.
In some embodiments of the invention, the temperature of the casting in step S1f is 680 to 700 ℃.
In some embodiments of the invention, the time interval in steps S1e and S1f is within 10 min.
In some embodiments of the invention, in step S1f, the casting is performed under an inert gas atmosphere.
In some embodiments of the invention, the inert atmosphere comprises argon.
High-purity argon is introduced into the aluminum melt through the furnace bottom air brick for stirring, casting and stirring, so that the uniformity of the system can be kept, and the effect of a dispersed phase is ensured.
In the invention, the dispersed phase mainly refers to compounds of trace elements, such as Mn, cr, zr and La, and the phases formed by the elements in the aluminum alloy can effectively control material grains, so that the grains of the material in the extrusion processing process are fine and uniform and cannot grow abnormally, which is beneficial to improving the performance.
According to the invention, al-Ti intermediate alloy with a certain content is added in the furnace in advance, so that the content of Ti element is higher, and due to the thinning principle of Ti-B, the thinning effect of more Ti elements is more obvious, and the welding strength is more favorably improved.
In some embodiments of the present invention, the three-stage homogenization treatment process of step S2 includes a first-stage homogenization treatment, a second-stage homogenization treatment, and a third-stage homogenization treatment.
The reason why the three-stage homogenization treatment process adopts multi-stage homogenization treatment is that a large amount of microelements such as Mn, cr, zr and La are added in the processThe effective precipitation temperature of the trace elements is in the range of 300-450 ℃, so the first-stage homogenization treatment adopts the temperature near the temperature for treatment, and the second-stage homogenization treatment mainly plays the role of solid solution of Mg 2 The Si strengthening phase avoids the high-temperature eutectic reaction from overburning, the homogenization treatment temperature can be increased to a higher temperature, and the third-stage homogenization treatment mainly has the functions of better eliminating the intragranular segregation, the casting stress and the spheroidization of the Fe-containing phase.
In some preferred embodiments of the present invention, in step S2, the time of the first-stage homogenization treatment is 2 to 4 hours.
In some preferred embodiments of the present invention, the temperature of the first-stage homogenization treatment in step S2 is 400 to 450 ℃.
In some preferred embodiments of the present invention, the temperature of the second-stage homogenization treatment in step S2 is 550 to 560 ℃.
In some preferred embodiments of the present invention, in step S2, the time of the second-stage homogenization treatment is 2 to 3 hours.
In some preferred embodiments of the present invention, in step S2, the temperature of the third stage homogenization treatment is 560 to 570 ℃.
In some preferred embodiments of the present invention, in step S2, the time of the third-stage homogenization treatment is 6 to 8 hours.
In some embodiments of the invention, the temperature of the extrusion in step S3 is 480 to 530 ℃.
In some embodiments of the present invention, the temperature of the heat treatment in step S4 is 165 to 185 ℃.
In some embodiments of the present invention, in step S4, the heat treatment time is 6 to 10 hours.
The third aspect of the invention provides the application of the aluminum alloy in the vehicle section bar.
In some preferred embodiments of the invention, a rail transit profile is provided, and the preparation raw material comprises the aluminum alloy.
The aluminum alloy has high strength, moderate extrusion difficulty, moderate process requirement and excellent comprehensive performance, and can be used for producing high-strength structural products with complex and multi-cavity sections and strict requirements on the dimensional precision of the aluminum alloy.
Drawings
The invention is further described with reference to the following figures and examples, in which:
FIG. 1 shows an aluminum alloy obtained in step S3 of example 2.
Detailed Description
The concept and technical effects of the present invention will be clearly and completely described below in conjunction with the embodiments to fully understand the objects, features and effects of the present invention. It is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments, and those skilled in the art can obtain other embodiments without inventive effort based on the embodiments of the present invention, and all embodiments are within the protection scope of the present invention.
Example 1
This embodiment provides an aluminum alloy, and specific content is:
according to the weight percentage: preparing 0.05% of Cu, 0.18% of Fe, 0.25% of Mn, 0.78% of Si, 0.62% of Mg0.03%, 0.03% of Zr, 0.10% of Cr0.05% of La, 0.01% of Ti and the balance of Al, wherein 0.005% of Ti is provided by an Al-Ti intermediate alloy, and the rest 0.005% of Ti adopts an on-line Al-Ti-B wire rod.
Aluminum ingot: an aluminum ingot with the grade of Al99.7 is adopted, the mass percent of Al in the aluminum ingot is more than 99.70 percent, and the aluminum ingot meets the standard GB/T1196-2008 aluminum ingot for remelting;
magnesium ingot: adopting a magnesium ingot with the mark of Mg9990, wherein the mass percent of Mg in the magnesium ingot is more than 99.9 percent, and the magnesium ingot meets the standard GB/T3499-2003 primary magnesium ingot;
alloying additive (aluminum silicon): with AlSi1 2 The quality of the master alloy meets YS/T282-2000 standard;
aluminum copper: adopting AlCu40 intermediate alloy, the quality of which meets YS/T282-2000 standard;
aluminum lanthanum: adopting AlLa intermediate alloy with the content of 10 percent;
aluminum zirconium: adopting an AlZr intermediate alloy with the content of 4 percent;
example 2
The embodiment prepares an aluminum alloy, and the specific process is as follows:
s1a, filling Al in the raw materials in the embodiment 1 into a smelting furnace (a regenerative energy-saving furnace), controlling the temperature in the furnace at 750-800 ℃, and completely melting an aluminum ingot into an aluminum melt I;
s1b, adding Al-Si intermediate alloy, mg, al-La, al-Zr intermediate alloy, cu, mn, cr and Al-Ti intermediate alloy, and alloying the aluminum melt to obtain an aluminum melt II;
s1c, adding a refining agent into the aluminum melt II according to the amount of 2kg/t, refining, wherein the refining temperature is 730 ℃, the refining time is 40min, introducing high-purity argon into the aluminum melt through a furnace bottom air brick during refining, controlling the pressure of the argon to be 0.05-0.1 MPa and the flow to be 10L/min, stirring and exhausting, and then removing slag to obtain an aluminum melt III; the chemical composition of the system is analyzed in the refining process, and the alloy composition is controlled within the range described in example 1.
S1d: and adding Al-Ti-B wires into the aluminum melt III in an online manner according to the quantity of 0.005% of the weight increment of Ti to carry out grain refinement, thus obtaining the aluminum melt IV.
S1e: and (3) purifying the aluminum melt IV sequentially through a box type degassing device and a double-stage filtering system (80-mesh foamed ceramic filter plate + RD tubular filter).
S1f: and performing semi-continuous water cooling casting on the purified aluminum melt IV at 680 ℃ within 10min to obtain an aluminum alloy ingot.
S2, heating the ingot A in a homogenizing heat treatment furnace to 420 ℃, preserving heat for 3h, heating to 560 ℃, preserving heat for 2h, then heating to 565 ℃, preserving heat for 8h, and then rapidly cooling to room temperature by using water mist to obtain an ingot B through aluminum treatment.
S3, heating the aluminum alloy ingot B to 500 ℃ for extrusion forming to obtain an extruded aluminum alloy C;
s4, heating the aluminum alloy C to 175 ℃, and preserving heat for 8 hours to obtain the aluminum alloy.
The obtained aluminum alloy extruded section C is shown in fig. 1.
Example 3
The embodiment is an aluminum alloy, and the specific content is as follows:
according to the weight percentage, cu0.30%, fe0.18%, mn0.35%, si0.88%, mg0.82%, zr0.02%, cr0.13%, la0.03%, ti0.04% and the balance of Al are prepared, wherein 0.03% of Ti is provided by an Al-Ti intermediate alloy, and the rest 0.01% of Ti adopts an on-line Al-Ti-B wire rod.
Aluminum ingot: an aluminum ingot with the grade of Al99.7 is adopted, the mass percent of Al in the aluminum ingot is more than 99.70 percent, and the aluminum ingot meets the standard GB/T1196-2008 aluminum ingot for remelting;
magnesium ingot: adopting a magnesium ingot with the mark of Mg9990, wherein the mass percent of Mg in the magnesium ingot is more than 99.9 percent, and the magnesium ingot meets the standard GB/T3499-2003 primary magnesium ingot;
alloying additive (aluminum silicon): adopting AlSi12 intermediate alloy, the quality of which accords with YS/T282-2000 standard;
aluminum copper: adopting AlCu40 intermediate alloy, the quality of which meets YS/T282-2000 standard;
aluminum lanthanum: adopting AlLa intermediate alloy with the content of 10 percent;
aluminum zirconium: adopting an AlZr intermediate alloy with the content of 4 percent;
example 4
The embodiment prepares the aluminum alloy, and the specific process is as follows:
s1a, filling Al in the raw materials in the embodiment 3 into a smelting furnace (a regenerative energy-saving furnace), controlling the temperature in the furnace at 780-800 ℃, and completely melting an aluminum ingot into an aluminum melt I;
s1b, adding Al-Si intermediate alloy, mg, al-La, al-Zr intermediate alloy, cu, mn, cr and Al-Ti intermediate alloy, and alloying the aluminum melt to obtain an aluminum melt II;
s1c, adding a refining agent into the aluminum melt II according to the amount of 2kg/t, refining, wherein the refining temperature is 730 ℃, the refining time is 40min, introducing high-purity argon into the aluminum melt through a furnace bottom air brick during refining, controlling the pressure of the argon to be 0.05-0.1 MPa and the flow to be 10L/min, stirring and exhausting, and then removing slag to obtain an aluminum melt III; the chemical composition analysis is carried out on the system in the refining process, and the alloy composition is controlled within the range of embodiment 3;
s1d: adding Al-Ti-B wires into the aluminum melt III in an online manner according to the quantity of 0.01 percent of the weight increment of Ti to carry out grain refinement, thus obtaining an aluminum melt IV;
s1e: purifying the aluminum melt IV sequentially through a box type degassing device and a two-stage filtering system (80-mesh foamed ceramic filter plate + RD tubular filter);
s1f: carrying out semi-continuous water cooling casting on the purified aluminum melt IV at 680 ℃ within 10min to obtain an ingot A;
s2, heating the ingot A in a homogenizing heat treatment furnace to 420 ℃, preserving heat for 3 hours, heating to 560 ℃, and preserving heat for 2 hours; then heating to 565 ℃ and preserving heat for 8h, and then rapidly cooling to room temperature by using water mist to obtain cast ingot B after aluminum treatment;
s3, heating the aluminum alloy ingot B to 500 ℃ for extrusion forming to obtain an extruded aluminum alloy C;
s4, heating the aluminum alloy C to 175 ℃, and preserving heat for 8 hours to obtain the aluminum alloy.
Comparative example 1
The comparative example is an aluminum alloy, and the specific contents are as follows:
preparing 0.45% of Cu0.45%, 0.20% of Fe, 0.28% of Mn0.80%, 0.68% of Mg0.68%, 0.03% of Zr0%, 0.10% of Cr0.06%, 0.02% of Ti0.02% and the balance of Al according to weight percentage, wherein 0.01% of Ti is provided by an Al-Ti intermediate alloy, and the rest 0.01% of Ti adopts an online Al-Ti-B wire rod;
aluminum ingot: an aluminum ingot with the grade of Al99.7 is adopted, the mass percent of Al in the aluminum ingot is more than 99.70 percent, and the aluminum ingot conforms to the standard GB/T1196-2008 aluminum ingot for remelting;
magnesium ingot: adopting a magnesium ingot with the mark of Mg9990, wherein the mass percent of Mg in the magnesium ingot is more than 99.9 percent, and the magnesium ingot meets the standard GB/T3499-2003 primary magnesium ingot;
alloying addition (aluminum silicon): adopting AlSi12 intermediate alloy, the quality of which accords with YS/T282-2000 standard;
aluminum copper: adopting AlCu40 intermediate alloy, the quality of which meets YS/T282-2000 standard;
aluminum lanthanum: adopting AlLa intermediate alloy with the content of 10 percent;
aluminum zirconium: an AlZr master alloy with a content of 4% was used.
Comparative example 2
The aluminum alloy is prepared by the comparative example, and the specific process is as follows:
s1a, filling Al in the raw material of the comparative example 1 into a smelting furnace (a heat accumulating type energy-saving furnace), and controlling the temperature in the furnace to be 780-800 ℃ to completely melt an aluminum ingot into an aluminum melt I;
s1b, adding Al-Si intermediate alloy, mg, al-La, al-Zr intermediate alloy, cu, mn, cr and Al-Ti intermediate alloy, and alloying the aluminum melt to obtain an aluminum melt II;
s1c, adding a refining agent into the aluminum melt II according to the amount of 2kg/t, refining, wherein the refining temperature is 730 ℃, the refining time is 40min, introducing high-purity argon into the aluminum melt through a furnace bottom air brick during refining, controlling the pressure of the argon to be 0.05-0.1 MPa and the flow to be 10L/min, stirring and exhausting, and then removing slag to obtain an aluminum melt III; the chemical composition analysis is carried out on the system in the refining process, and the alloy composition is controlled within the range of embodiment 3;
s1d: adding Al-Ti-B wires into the aluminum melt III in an online manner according to the quantity of 0.01 percent of the weight increment of Ti to carry out grain refinement, thus obtaining an aluminum melt IV;
s1e: purifying the aluminum melt IV sequentially through a box-type degassing device and a two-stage filtering system (a 80-mesh foamed ceramic filter plate and an RD tubular filter);
s1f: carrying out semi-continuous water cooling casting on the purified aluminum melt IV at 680 ℃ within 10min to obtain an ingot A;
s2, heating the ingot A in a homogenizing heat treatment furnace to 420 ℃, preserving heat for 3h, heating to 560 ℃, preserving heat for 2h, heating to 565 ℃, preserving heat for 8h, and rapidly cooling to room temperature by using water mist to obtain an ingot B after aluminum treatment;
s3, heating the aluminum alloy ingot B to 500 ℃ for extrusion forming to obtain an extruded aluminum alloy C;
s4, heating the aluminum alloy C to 175 ℃, and preserving heat for 8 hours to obtain the aluminum alloy.
Comparative example 3
The comparative example is an aluminum alloy, and the specific contents are as follows:
according to the weight percentage, preparing Cu0.20%, fe0.20%, mn0.45%, si0.80%, mg0.68%, zr0.03%, cr0.19%, la0.06%, ti0.02%, and the balance Al, wherein 0.01% of Ti is provided by an Al-Ti intermediate alloy, and the rest 0.01% of Ti adopts an on-line Al-Ti-B wire rod.
Aluminum ingot: an aluminum ingot with the grade of Al99.7 is adopted, the mass percent of Al in the aluminum ingot is more than 99.70 percent, and the aluminum ingot meets the standard GB/T1196-2008 aluminum ingot for remelting;
magnesium ingot: adopting a magnesium ingot with the mark of Mg9990, wherein the mass percent of Mg in the magnesium ingot is more than 99.9 percent, and the magnesium ingot meets the standard GB/T3499-2003 primary magnesium ingot;
alloying addition (aluminum silicon): adopting AlSi12 intermediate alloy, the quality of which accords with YS/T282-2000 standard;
aluminum copper: adopting AlCu40 intermediate alloy, the quality of which accords with YS/T282-2000 standard;
aluminum lanthanum: adopting AlLa intermediate alloy with the content of 10 percent;
aluminum zirconium: adopting an AlZr intermediate alloy with the content of 4 percent;
comparative example 4
The aluminum alloy is prepared by the comparative example, and the specific process is as follows:
s1a, filling Al in the raw material of the comparative example 3 into a smelting furnace (a heat accumulating type energy-saving furnace), and controlling the temperature in the furnace to be 780-800 ℃ to completely melt an aluminum ingot into an aluminum melt I;
s1b, adding Al-Si intermediate alloy, mg, al-La, al-Zr intermediate alloy, cu, mn, cr and Al-Ti intermediate alloy, and alloying the aluminum melt to obtain an aluminum melt II;
s1c, adding a refining agent into the aluminum melt II according to the amount of 2kg/t, refining, wherein the refining temperature is 730 ℃, the refining time is 40min, introducing high-purity argon into the aluminum melt through a furnace bottom air brick during refining, controlling the pressure of the argon to be 0.05-0.1 MPa and the flow to be 10L/min, stirring and exhausting, and then removing slag to obtain an aluminum melt III; the chemical composition analysis is carried out on the system in the refining process, and the alloy composition is controlled within the range of embodiment 3;
s1d: adding Al-Ti-B wires into the aluminum melt III in an online manner according to the amount of 0.01% of the weight increment of Ti to carry out grain refinement to obtain an aluminum melt IV;
s1e: purifying the aluminum melt IV sequentially through a box type degassing device and a two-stage filtering system (80-mesh foamed ceramic filter plate + RD tubular filter);
s1f: and carrying out semi-continuous water cooling casting on the purified aluminum melt IV within 10min at 680 ℃ to obtain an ingot A.
S2, heating the ingot A in a homogenizing heat treatment furnace to 420 ℃, preserving heat for 3h, heating to 560 ℃, preserving heat for 2h, then heating to 565 ℃, preserving heat for 8h, and then rapidly cooling to room temperature by using water mist to obtain an ingot B through aluminum treatment.
S3, heating the aluminum alloy ingot B to 500 ℃ for extrusion forming to obtain an extruded aluminum alloy C;
s4, heating the aluminum alloy C to 175 ℃, and preserving heat for 8 hours to obtain the aluminum alloy.
Comparative example 5
The comparative example is an aluminum alloy, and the specific contents are as follows:
according to the weight percentage, cu0.25%, fe0.20%, mn0.27%, si0.80%, mg0.68%, zr0.03%, cr0.10%, la less than 0.001%, ti0.02% and the balance of Al are prepared, wherein 0.01% of Ti is provided by an Al-Ti intermediate alloy, and the rest 0.01% of Ti adopts an on-line Al-Ti-B wire rod.
Aluminum ingot: an aluminum ingot with the grade of Al99.7 is adopted, the mass percent of Al in the aluminum ingot is more than 99.70 percent, and the aluminum ingot meets the standard GB/T1196-2008 aluminum ingot for remelting;
magnesium ingot: adopting a magnesium ingot with the mark of Mg9990, wherein the mass percent of Mg in the magnesium ingot is more than 99.9 percent, and the magnesium ingot meets the standard GB/T3499-2003 primary magnesium ingot;
alloying additive (aluminum silicon): adopting AlSi12 intermediate alloy, the quality of which accords with YS/T282-2000 standard;
aluminum copper: adopting AlCu40 intermediate alloy, the quality of which meets YS/T282-2000 standard;
aluminum lanthanum: adopting AlLa intermediate alloy with the content of 10 percent;
aluminum zirconium: adopting an AlZr intermediate alloy with the content of 4 percent;
comparative example 6
The aluminum alloy is prepared by the comparative example, and the specific process is as follows:
s1a: al in the raw material of the comparative example 5 is filled into a smelting furnace (a heat accumulating type energy-saving furnace), the temperature in the furnace is controlled to be 780-800 ℃, and an aluminum ingot is completely melted into an aluminum melt I;
s1b: then adding Al-Si intermediate alloy, mg, al-La, al-Zr intermediate alloy, cu, mn, cr and Al-Ti intermediate alloy, and alloying the aluminum melt to obtain an aluminum melt II;
s1c: adding a refining agent into the aluminum melt II according to the amount of 2kg/t, refining at the temperature of 730 ℃ for 40min, introducing high-purity argon into the aluminum melt through a furnace bottom air brick during refining, controlling the pressure of the argon to be 0.05-0.1 MPa and the flow to be 10L/min, stirring and exhausting, and then removing slag to obtain an aluminum melt III; the chemical composition analysis is carried out on the system in the refining process, and the alloy composition is controlled within the range of embodiment 3;
s1d: adding Al-Ti-B wires into the aluminum melt III in an online manner according to the quantity of 0.01 percent of the weight increment of Ti to carry out grain refinement, thus obtaining an aluminum melt IV;
s1e: purifying the aluminum melt IV sequentially through a box type degassing device and a two-stage filtering system (80-mesh foamed ceramic filter plate + RD tubular filter);
s1f: and carrying out semi-continuous water cooling casting on the purified aluminum melt IV within 10min at 680 ℃ to obtain an ingot A.
S2, heating the ingot A in a homogenizing heat treatment furnace to 420 ℃, preserving heat for 3h, heating to 560 ℃, and preserving heat for 2h; then heating to 565 ℃ and preserving heat for 8h, and then rapidly cooling to room temperature by using water mist to obtain cast ingot B after aluminum treatment;
s3, heating the aluminum alloy ingot B to 500 ℃ for extrusion forming to obtain an extruded aluminum alloy C;
s4, heating the aluminum alloy C to 175 ℃, and preserving heat for 8 hours to obtain the aluminum alloy.
Test examples
The results of the performance tests of examples 2 and 4 and comparative examples 2 and 4 and 6 are shown in Table 1
TABLE 1 aluminum alloy Properties
And (4) testing standard:
extrusion property: the multi-cavity hollow thin-wall profiled bar can be extruded, and the solid solution effect can be achieved by adopting on-line strong wind, water mist and water cooling quenching. The cross section of the drawing can be extruded, and the correlation performance requirements can be met. The extrusion speed is 2 mm/s-8 mm/s.
Tensile property: in the T6 state, the tensile strength Rm is more than or equal to 320Mpa, the yield strength Rp0.2 is more than or equal to 300Mpa, and the elongation delta after fracture is more than or equal to 10 percent. Thermal stability: the test is carried out according to the test method GB/T228.1-2010, and a 50mm gauge length extensometer is adopted. The stretching speed is 5mm/min, and the yield strength Rp0.2 is more than or equal to 290MPa after the temperature is maintained for 100 hours at 150 ℃.
Stress corrosion resistance: the stress corrosion index Issrt is less than or equal to 5 percent by testing according to a GBT 15790.7-2017 testing method.
Stripping corrosion resistance: testing according to a GBT 22639-2008 testing method to reach PA level.
From the test results in table 1, it can be seen that in comparative example 2, excessive Cu affects the corrosion resistance of the aluminum alloy, and also increases the welding hot crack tendency, as well as the press quenching sensitivity and the press deformation resistance, and seriously affects the press property and the welding property.
As can be seen from the test results in Table 1, excessive Mn and Cr in comparative example 4 can cause serious segregation in the crystal, which affects the extrusion performance of the material, greatly improves the extrusion quenching sensitivity, and the conventional water mist cooling cannot meet the cooling requirement.
As shown in the test results in Table 1, in comparative example 6, the La content is low, and the La phase can effectively refine the crystal grains of the cast rod in the casting stage and improve the hot crack resistance tendency, so that the welding performance of comparative example 6 is obviously reduced.
The embodiments of the present invention have been described in detail with reference to the accompanying drawings, but the present invention is not limited to the above embodiments, and various changes can be made within the knowledge of those skilled in the art without departing from the gist of the present invention. Furthermore, the embodiments of the present invention and the features of the embodiments may be combined with each other without conflict.
Claims (9)
1. The aluminum alloy is characterized by comprising the following components in percentage by weight: 0.05 to 0.30 percent of Cu, 0.25 to 0.35 percent of Mn, 0.10 to 0.13 percent of Cr, 0.02 to 0.08 percent of La, 0.02 to 0.08 percent of Zr, 0.78 to 0.88 percent of Si, 0.62 to 0.82 percent of Mg, 0.010 to 0.04 percent of Ti, and the balance of Al and impurities,
the preparation method of the aluminum alloy comprises the following steps:
s1: melting and casting an aluminum ingot and the preparation raw materials containing Cu, mn, cr, la, zr, si, mg and Ti to obtain an aluminum alloy ingot;
s2: carrying out three-stage homogenization treatment on the aluminum alloy ingot obtained in the step S1;
s3: extruding the aluminum alloy ingot obtained in the step S2;
s4, artificially aging the cast ingot obtained in the step S3 to obtain the cast ingot;
the three-stage homogenization treatment process of the step S2 comprises primary homogenization treatment, secondary homogenization treatment and tertiary homogenization treatment;
in the step S2, the time of the first-stage homogenization treatment is 2-4 h;
the temperature of the first-stage homogenization treatment is 400-450 ℃;
the temperature of the second-stage homogenization treatment is 550-560 ℃;
the time of the second-stage homogenization treatment is 2-3 h;
the temperature of the third-stage homogenization treatment is 560-570 ℃;
the time of the three-stage homogenization treatment is 6-8 h.
2. The aluminum alloy of claim 1, wherein the sum of the weight percentages of La and Zr is not greater than 0.12% in weight percent.
3. The aluminum alloy of claim 1, wherein the sum of the weight percentages of Mn, cr, la, and Zr is not greater than 0.48%, in weight percent.
4. The aluminum alloy of claim 1, wherein the weight ratio of Mn to Cr is 2.2 to 3.
5. The aluminum alloy of claim 1, wherein the impurities comprise: fe.
6. The aluminum alloy according to claim 1, wherein the aluminum alloy has a tensile strength of 300 to 400MPa.
7. The aluminum alloy according to claim 1, wherein the melting temperature in step S1 is 750-800 ℃.
8. The aluminum alloy according to claim 1, wherein in step S1, the melting and the casting are performed under an inert gas system,
the inert gas comprises argon.
9. Use of the aluminum alloy according to any one of claims 1 to 8 in automotive profiles.
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