CN114086041B - High-strength high-toughness aluminum alloy and preparation method thereof - Google Patents
High-strength high-toughness aluminum alloy and preparation method thereof Download PDFInfo
- Publication number
- CN114086041B CN114086041B CN202111390921.XA CN202111390921A CN114086041B CN 114086041 B CN114086041 B CN 114086041B CN 202111390921 A CN202111390921 A CN 202111390921A CN 114086041 B CN114086041 B CN 114086041B
- Authority
- CN
- China
- Prior art keywords
- aluminum alloy
- strength
- toughness
- carrying
- sintering
- 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.)
- Active
Links
Images
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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
- B22F3/1007—Atmosphere
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/248—Thermal after-treatment
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention relates to a high-strength high-toughness aluminum alloy and a preparation method thereof, wherein the high-strength high-toughness aluminum alloy comprises the following components: si2.1-2.7 wt%, Mg 1.9-2.5 wt% and Cu 1.9-2.5 wt%, and the balance being aluminum and inevitable impurities, wherein the total amount of the inevitable impurities accounts for 0-0.8 wt% of the high-strength high-toughness aluminum alloy; the method comprises the following steps: preparing materials according to the composition of the high-strength and high-toughness aluminum alloy, preparing polygonal aluminum alloy powder by a high-pressure water atomization method, sieving by a 180-mesh and 220-mesh sieve, and taking the sieved powder for later use; pressing and molding the undersize powder, sintering for 60-480min in an inert atmosphere or a protective atmosphere, and air cooling to obtain an aluminum ingot; carrying out hot extrusion on the aluminum ingot, and then carrying out air cooling to obtain an extrusion rod; carrying out solution treatment on the extrusion rod at 560-565 ℃ for 60-180min, and then sequentially quenching and rotary forging to obtain a rotary forging piece; and carrying out two-stage aging treatment on the rotary forging piece to obtain a high-strength high-toughness aluminum alloy finished product. The aluminum alloy disclosed by the invention has good toughness and strength, and the element composition is simpler.
Description
Technical Field
The invention relates to a high-strength high-toughness aluminum alloy and a preparation method thereof, belonging to the field of alloys.
Background
The 6-series aluminum alloy has the advantages of medium strength, strong corrosion resistance, no stress corrosion cracking tendency, good welding performance, no reduction of the corrosion performance of a welding zone, good formability and technological performance and the like, and is widely applied to the industries of aerospace, rail transit, automobiles, ships, electric power engineering and the like. Since the external environment is complicated, such as large difference in stress conditions, wide temperature change range, wide humidity change range, large change in acidity and salinity in air, and the like, when exposed outdoors for a long time and exposed to wind, frost, rain and snow, the 6-series aluminum alloy is favored for its excellent corrosion resistance when selecting a material for a power grid accessory. However, the strength of the existing 6-series aluminum alloy is low, and the requirement of the application scene on the strength cannot be met. Even if the conventional means is adopted to improve the strength to the scene requirement, the elongation rate is often reduced too much. In short, the requirements of the strength and the elongation of the traditional 6-series alloy are difficult to meet certain scenes with higher requirements. In the power grid engineering, a great amount of iron-based materials are used in hardware, so that the hardware is high in strength but not corrosion-resistant. Under the background of energy conservation and emission reduction, the iron-based hardware is replaced by 6 series aluminum alloy, which is a necessary trend. According to the requirements of the iron-based hardware in service at present, the performance of 6 series aluminum alloy must be greatly improved to possibly replace the existing iron-based material. In consideration of the application background, the inventor considers from the aspects of alloy components, preparation process and the like, and finally greatly improves the performance through a large amount of long-time experiments, so that the requirement of power grid engineering on the hardware aluminum alloy is met. Corresponding achievement has already applied for the national invention patent with the application number of CN 202111055276.6. From the point of view of safety and engineering practice, it is of course desirable that the higher the properties of the material used, the greater the safety factor, the better. The pursuit of higher performance, such as higher strength, is a constant pursuit of researchers. After the research and development of 6 series aluminum alloy for many years, the performance, particularly the strength, of the 6 series aluminum alloy is close to that of a ceiling, and the breakthrough is difficult. With the technical progress, such as the progress of machinery, equipment, control and the like, more technical means choices are provided for us, so that the scheme which cannot be realized or even imagined in the past can be provided for us. Thus, the performance of the traditional material is improved and enhanced, and the possibility is provided. The aluminum alloy related in CN202111055276.6 previously reported by the applicant has good effect of grain refinement after being added with rare earth, so that the strength and the elongation of the alloy reach a good balance, and the best comprehensive performance is reached. However, since rare earth is a precious strategic resource and is expensive, it is not suitable for mass use and is not favorable for market development. Therefore, a new idea, a new method and a new means are adopted to further improve the strength of the alloy, which is very necessary and has great significance.
The strength of the existing 6 series aluminum alloy is about 300Ma generally, and is difficult to exceed 400 MPa. When the material is used as a structural material, the material is generally required to have higher strength, at least up to 400 MPa. The 6-series aluminum alloy of application No. CN202111055276.6 has a tensile strength of 420MPa or more and an elongation of 20% or more, and has achieved the above object. From the perspective of improving the safety factor of the power grid, the higher the strength is, the better the strength is, and if the strength can exceed 440MPa or higher, the application scenarios will be wider. Generally, the increase of the strength of the metal material will result in the reduction of the elongation, but as long as the elongation is not less than 13%, the requirements of the current power grid engineering can be completely met. The strength of the 6 series aluminum alloy with the tensile strength not more than 400MPa is improved to more than 440MPa, and the elongation is kept to be more than 13 percent so as to meet the engineering practice requirement of service conditions on the high strength of the 6 series aluminum alloy, and the method is a topic with great application value.
Disclosure of Invention
In view of the defects of the prior art, the invention aims to provide an aluminum alloy and a preparation method thereof, so as to obtain an aluminum alloy product with good strength performance and extensibility and simplify the element composition of the aluminum alloy.
In order to solve the technical problems, the technical scheme of the invention is as follows:
a preparation method of a high-strength high-toughness aluminum alloy comprises the following components: si 2.1-2.7 wt%, Mg1.9-2.5 wt% and Cu 1.9-2.5 wt%, and the balance being aluminum and unavoidable impurities, wherein the total amount of the unavoidable impurities is 0-0.8 wt% of the high-strength high-toughness aluminum alloy; the method comprises the following steps:
s1, preparing and smelting according to the component composition of the high-strength and high-toughness aluminum alloy, preparing polygonal aluminum alloy powder by a high-pressure water atomization method, sieving with a 180-sand 220-mesh sieve, and taking the sieved powder for later use;
wherein, when high-pressure water is atomized, the aluminum alloy melt flows down through the leakage hole of the tundish and is sprayed by high-pressure water jet; wherein the unit pressure of the high-pressure water jet is 20-23MPa, the flow rate of the high-pressure water jet is 0.8-1.2t/min, and the diameter of the leakage hole is 24-26 mm;
s2, pressing and forming the undersize powder, sintering for 60-480min in an inert atmosphere or a protective atmosphere, and air cooling to obtain an aluminum ingot;
wherein, the sintering temperature is 560-565 ℃;
s3, carrying out hot extrusion on the aluminum ingot, and then carrying out air cooling to obtain an extrusion rod;
wherein the hot extrusion temperature is controlled to be 540-545 ℃, and the hot extrusion ratio is not less than 15:1, further 20-30:1, and further 24-26: 1;
S4, carrying out solution treatment on the extrusion rod at 560-565 ℃ for 60-180min, and then sequentially quenching and swaging to obtain a rotary forging piece;
s5, carrying out double-stage aging treatment on the rotary forging piece to obtain a high-strength high-toughness aluminum alloy finished product;
wherein, when the two-stage aging treatment is carried out, the aging treatment is firstly carried out at 132-138 ℃ for 3-4h, and then the aging treatment is carried out at 157-163 ℃ for 10-11 h.
The aluminum alloy powder prepared by the invention is polygonal, is particularly suitable for pressing, and is beneficial to obtaining a high-density blank.
Further, the high-strength high-toughness aluminum alloy comprises the following components: 2.3 to 2.5 weight percent of Si, 2.2 to 2.5 weight percent of Mg, 1.9 to 2.5 weight percent of Cu, and the balance of aluminum and inevitable impurities.
Optionally, in S1, the smelting temperature is 700-800 ℃.
Further, in S2, the pressure of 200-230MPa is adopted for press molding.
Further, in S2, sintering was performed in an argon atmosphere.
Further, in S2, the sintering temperature was 563-564 ℃.
Further, in S2, the sintering time is 300-450min, and further 400-440 min.
Further, in S2, sintering by using a mesh belt furnace; the mesh belt furnace is provided with a sintering section and a cooling section, and a fan is arranged in the cooling section. Thus, the sintered alloy can be air-cooled by the fan, and the quenching effect is achieved.
Further, in S3, the hot extrusion temperature is 543-544 ℃.
Alternatively, in S3, the air-cooling process is performed by a fan.
Further, in S4, solution treatment was performed at 562-564 ℃.
Further, in S4, swaging 2-4 times; after each swaging, the diameter of the extruded rod is reduced by 3-5%. This contributes to an optimum cost performance.
Furthermore, in S5, when the two-stage aging treatment is performed, the aging treatment is performed at 134-136 ℃ for 3.2-3.8h, and then the aging treatment is performed at 159-161 ℃ for 10.2-10.8 h.
Further, the aluminum ingot is a bar with the diameter of 200-600 mm.
Further, the diameter of the extrusion rod is less than or equal to 120mm, and preferably 100 mm and 115 mm.
The high-strength high-toughness aluminum alloy is prepared by the preparation method.
Generally, the 6-series aluminum alloy is mainly composed of magnesium and silicon, and Mg2The aluminum alloy in which the Si phase is a strengthening phase is typically a heat-treatment-strengthenable aluminum alloy. Generally, increasing the magnesium and silicon contents can increase the volume fraction of the strengthening phase, i.e. increase the number of strengthening phases, and has a positive significance for improving the strength of the 6-series aluminum alloy. In engineering practice, 6 series aluminum alloy with higher magnesium and silicon contents is usually selected under the service condition that the strength is required to be higher. The applicant's prior study CN202111055276.6 was based on this consideration and intentionally increased the contents of si, mg and cu elements. However, the increase of the content of magnesium and silicon does not keep a linear relationship with the increase of the strength, i.e. the increase of the content and the increase of the strength have marginal weakening phenomena, which is proved by detailed data in CN 202111055276.6. The applicant has found that the main reasons for the above phenomena are: the higher the contents of magnesium and silicon, especially the further addition of other strengthening elements such as copper, etc., the more serious the segregation of the as-cast structure becomes, which weakens the strengthening effect of the alloying elements on the alloy, i.e. the linear increase thereof cannot be maintained. Of strengthening element content On the one hand, the grains of the as-cast structure are coarse and contain element segregation, and on the other hand, the heat treatment precipitation strengthening phase is obviously coarsened, which further obviously reduces the elongation of the alloy. To fully develop Mg2The strengthening effect of the Si phase or other reinforcing phases can reach a more ideal degree and the elongation can be maintained to the maximum degree only by distributing the reinforcing phases in the alloy in the form of fine dispersed particles. This segregation in the microstructure is formed by the slow cooling rate during the cooling process, and is a type of micro-segregation. In order to solve the homogenization problem of the micro segregation structure, firstly, a proper cooling rate is adopted in the casting process, so that the micro segregation structure does not appear or has slight influence on the performance of the alloy even if the micro segregation structure appears, and secondly, the homogenization annealing is used for eliminating the segregation after the casting is finished. Under the existing casting production conditions, it is difficult to obtain a structure free from segregation. The homogenization annealing is a measure for post-repair, and although it has a great effect on eliminating segregation, when the degree and range of segregation are both great, its effect has a certain limitation, and the effect is not ideal. Therefore, the segregation problem of the alloy is fundamentally solved, and the cooling process of the alloy still needs to be started. The basic knowledge of the material science is combined, so that the alloy is cooled and solidified in a balanced solidification mode under the infinitely slow cooling condition, the structure of the alloy is a balanced solidification structure, and segregation cannot occur. However, infinitely slow cooling rates are too difficult to handle and are not possible for production, and their production cost is too high to justify any market, and on the other hand, low solidification cooling rates can lead to coarse grains, which also worsen the properties of the alloy. Therefore, a new approach must be taken to achieve a close approach of the coagulated tissue to the balanced coagulated tissue. The higher the cooling rate of the melt, the more segregation of the as-cast structure occurs, which is a result of cooling rates within certain limits, and generally at cooling rates that are not so high, and are not applicable to all cooling rates. When the cooling rate is extremely large, the degree of unevenness of the as-cast structure thereof is rather decreased as the cooling rate is increased. The philosophy can be unified in the natural science and the social science just so that the object is absolutely contrary. For example, in industrial practice, the cooling can be increased by reducing the diameter of the ingot But the speed and the segregation degree can not be improved, but the alloy micro segregation can be reduced. However, this method has a limited improvement in cooling rate, and is only suitable for producing small-diameter products with a diameter of 20mm or less, but not for large-diameter products with a diameter of 200mm or more, which often contradicts the requirements of subsequent processes on product diameter.
Therefore, in order to improve the product performance, the invention adopts the extrusion rod as a raw material, and uses less cast raw material rods so as to reduce the grain size of the product as much as possible. Therefore, the raw material rod is generally a continuous casting large ingot with the diameter of 200-600mm, and then extruded into the rod. Since the as-extruded structure is a worked structure, the grain size thereof is much smaller than that of the as-cast structure. The larger the diameter of the cast rod, the lower the cooling rate, the larger the size of the crystal grains, and the more serious segregation of the alloying elements, which are problems. The higher the content of the alloy element is, the greater the significance of improving the cooling rate of the alloy is. The content of magnesium, silicon and copper elements of the aluminum alloy is higher than that of corresponding elements of the aluminum alloy of CN202111055276.6, the segregation is more serious, and the requirement on the cooling rate is higher. The aluminum alloy is prepared by a powder metallurgy method, the aluminum alloy powder is prepared firstly after the materials are prepared, and the process of preparing powder by high-pressure water atomization is equivalent to the process of directly carrying out liquid quenching on the high-temperature melt of the aluminum alloy, namely, the high-temperature liquid aluminum alloy is directly cooled to room temperature in a very short time under the action of high-pressure water, and magnesium, silicon and other alloy elements are frozen and kept to the room temperature in the process of solidification without time for segregation. When the water is atomized to prepare powder, the melt is crushed into tiny powder particles by the water under the action of high pressure at a very fast speed and a very large flow rate, and the solidification process is completed, so that crystal grains in the powder particles are smaller. In this way, the high cooling rate, small size of the grains, makes it impossible for the distribution of magnesium, silicon and other alloying elements to deviate greatly and their distribution to be very uniform. When the cooling rate problem is resolved, the strengthening elements can only be added further. Only under the condition of water atomization, a large amount of alloy elements can not be segregated in the alloy, the strengthening effect is good, and the adverse effect of elongation is minimized. The invention can improve the components on the basis of the aluminum alloy of CN 202111055276.6. Of course, the strength effect of the alloy is further increased, and a series of measures are also needed to be matched to ensure that the elements are uniformly distributed, dispersed and fine so as to obtain the optimal comprehensive performance. In the invention, high sintering temperature, high hot extrusion temperature and high solid solution temperature are adopted, and all the technical measures aim to ensure the sufficient solid solution of strengthening elements of silicon, magnesium and copper, realize the supersaturation of the strengthening elements and prepare for the precipitation of fine and dispersed strengthening phases during aging; on the other hand, the elongation of the alloy is reduced to avoid the occurrence of coarse second phases as much as possible. Likewise, after incubation at high temperature for sufficient redissolution, a high cooling rate is used: forced air cooling after sintering and hot extrusion and water cooling after quenching are carried out, and the aims of avoiding premature precipitation of a second phase and avoiding more precipitation and subsequent growth and coarsening to reduce the elongation of the alloy are achieved. And the measures are mutually matched, for example, in the subsequent aging process, a proper aging system is adopted, so that the precipitated phase can be maximally ensured to be finely, dispersedly and uniformly distributed in the matrix metal, and the effect of strengthening the aluminum alloy is exerted to the utmost extent.
Because of great change of alloy components, the double-stage aging process adopted by CN202111055276.6 is not an optimal process although still available, and must be further optimized: the temperature of 132-138 ℃ is kept for 3-4h, and the temperature of 157-163 ℃ is kept for 10-11 h. If the CN202111055276.6 two-stage aging process is adopted, during the aging at the low temperature stage, the size of part of crystal grains does not reach the critical size, but obviously begins to grow, and the uneven growth is more likely to occur in the subsequent high temperature aging stage; the overall grain structure size has large grain difference, so that the performance is unstable, and the short plate effect is easy to occur, which is not allowed in engineering. CN202111055276.6 adopts cold drawing after the aluminum alloy is quenched, and the invention adopts rotary swaging. Cold drawing has the advantage of high efficiency, but is in a tensile stress state, easily generates micro-cracks, and reduces the elongation of the metal. And the rotary swaging is in a three-dimensional compressive stress state, so that microcracks are not easy to generate, and the method is favorable for maintaining the elongation of the alloy. The processing mode with more reasonable stress state is also very beneficial to the aluminum alloy of the invention to obtain good elongation. When the temperature is maintained for 3-4h at the low temperature of 132-138 ℃, the number of formed G.P. zones is large, the critical size of the nucleation of the reinforced phase particles is achieved, and the particles are distributed in a dispersing way in tissues, namely, the effective nucleation number of the reinforced phase particles is increased, so that the strength effect is maximized and the elongation is minimized. When the aging is carried out at the temperature of 157 plus 163 ℃ for 10-11h, the strengthening phase is evenly and dispersedly precipitated, and the best comprehensive performance can be obtained.
The invention fully utilizes the liquid quenching effect of high-pressure water atomization powder preparation on the 6-series novel aluminum alloy to realize complete homogenization of the distribution of magnesium, silicon and other elements, and is assisted with three-high treatment, namely high sintering temperature, high extrusion temperature and high solid solution temperature, in the subsequent flow, thereby ensuring that Mg2The strengthening phases such as Si and the like are fine and dispersed and precipitated and are uniformly distributed in the base metal, so that the strengthening effect of the 6-series novel aluminum alloy is maximized, the strength of the 6-series novel aluminum alloy is improved by 70-100 MPa compared with that of the traditional 6-series aluminum alloy, and the strength of the 6-series novel aluminum alloy is improved by about 20MPa compared with that of CN 202111055276.6. In addition, the invention does not need to control the iron content deliberately, because the iron silicon needle phase can be generated in the casting solidification process without worrying about, the mechanical property of the alloy is deteriorated, and the needle iron silicon phase can not be generated in the high-pressure water atomization pulverization and the subsequent process.
The aluminum alloy does not contain rare earth elements, the element composition is simpler, the strength and the extensibility of the obtained aluminum alloy can meet the use requirements of power grid engineering, and the method is more improved compared with CN 202111055276.6.
Drawings
FIG. 1 is an SEM image of a polygonal aluminum alloy powder.
Detailed Description
The present invention will be described in detail with reference to examples. It should be noted that the embodiments and features of the embodiments of the present invention may be combined with each other without conflict.
Examples 1 to 13
A preparation method of a high-strength high-toughness aluminum alloy comprises the following components: si 2.1-2.7 wt%, Mg1.9-2.5 wt% and Cu 1.9-2.5 wt% (see Table 1 for the specific component formula of each example), and the balance of aluminum and inevitable impurities, wherein the total amount of the inevitable impurities is less than 0.8 wt%; the method comprises the following steps:
s1, preparing materials according to the composition of the high-strength and high-toughness aluminum alloy, heating to 750 ℃ to melt the materials to obtain an aluminum alloy melt, preparing polygonal aluminum alloy powder by a high-pressure water atomization method, sieving the polygonal aluminum alloy powder by a 180-mesh and 220-mesh sieve, and taking the sieved powder for later use;
wherein, when high-pressure water is atomized, the aluminum alloy melt flows down through the eye of the tundish and is sprayed by high-pressure water jet; wherein the unit pressure of the high-pressure water jet is 22MPa, the flow rate of the high-pressure water jet is 1t/min, and the diameter of the leak hole is 25 mm;
s2, mould pressing the undersize powder into ingots with the diameter of 500mm by adopting the unit pressure of 210MPa, sintering for 420min in the argon atmosphere, and air cooling to obtain aluminum ingots with the diameter of 500 mm;
wherein, the sintering temperature is 560-;
s3, carrying out hot extrusion on the aluminum ingot, and then carrying out air cooling to obtain an extrusion rod with the diameter of 100 mm;
Wherein the hot extrusion temperature is controlled to be 540-;
s4, carrying out solution treatment on the extrusion rod for 120min under the conditions of 560-565 ℃ (the specific values of each embodiment are shown in table 1), and then sequentially quenching (the quenching medium is water) and carrying out rotary swaging to obtain a rotary forging piece;
wherein, rotary swaging is carried out for 3 times; after each rotary swaging, the diameter of the extrusion rod is reduced by 4%;
s5, performing two-stage aging treatment on the rotary forging piece to obtain a high-strength high-toughness aluminum alloy finished product;
when the two-stage aging treatment is carried out, the aging treatment is firstly carried out for 3.5h at 132-.
S2, sintering by using a mesh belt furnace; the mesh belt furnace is provided with a sintering section and a cooling section, and a fan is arranged in the cooling section.
The performance test results of the finished aluminum alloy products obtained in the examples are shown in table 1. Wherein, the percentage of the elongation, namely the ratio of the total deformation delta L of the gauge length section after the tensile fracture of the related sample to the original gauge length L is as follows: δ ═ Δ L/lx 100%.
Comparative examples 1 to 21
Example 1 was repeated separately, with the only differences presented in table 1.
The performance test results of the aluminum alloy finished products obtained in each comparative example are shown in table 1. Wherein, the percentage of the elongation, namely the ratio of the total deformation delta L of the gauge length section after the tensile fracture of the related sample to the original gauge length L is as follows: δ ═ Δ L/L × 100%.
TABLE 1 table of composition distribution ratio and performance test results of aluminum alloy in each example and comparative example
Upper label1)Represents: the swaging in S4 was changed to cold drawing with the same deformation amount as in example 3.
All mechanical property data in table 1 are the average of the measurements obtained for 12 samples. The foregoing examples are set forth to illustrate the present invention more clearly and are not to be construed as limiting the scope of the invention, which is defined in the appended claims to which the invention pertains, as modified in all equivalent forms, by those skilled in the art after reading the present invention.
Claims (10)
1. The preparation method of the high-strength high-toughness aluminum alloy is characterized in that the high-strength high-toughness aluminum alloy comprises the following components: 2.1-2.7wt% of Si, 1.9-2.5wt% of Mg and 1.9-2.5wt% of Cu, and the balance of aluminum and inevitable impurities, wherein the total amount of the inevitable impurities is less than 0.8 wt%; the method comprises the following steps:
s1, preparing and smelting according to the component composition of the high-strength and high-toughness aluminum alloy, preparing polygonal aluminum alloy powder by a high-pressure water atomization method, sieving with a 180-fold 220-mesh sieve, and taking the sieved powder for later use;
Wherein, when high-pressure water is atomized, the aluminum alloy melt flows down through the leakage hole of the tundish and is sprayed by high-pressure water jet; wherein the unit pressure of the high-pressure water jet is 20-23MPa, the flow rate of the high-pressure water jet is 0.8-1.2t/min, and the diameter of the leakage hole is 24-26 mm;
s2, pressing and forming the undersize powder, sintering for 60-480min in a protective atmosphere, and air cooling to obtain an aluminum ingot;
wherein the sintering temperature is 560-565 ℃;
s3, carrying out hot extrusion on the aluminum ingot, and then carrying out air cooling to obtain an extrusion rod;
wherein the hot extrusion temperature is controlled to be 540-545 ℃, and the hot extrusion ratio is not less than 15: 1;
s4, carrying out solution treatment on the extrusion rod at 560-565 ℃ for 60-180min, and then sequentially quenching and swaging to obtain a rotary forging piece;
s5, carrying out double-stage aging treatment on the rotary forging piece to obtain a high-strength high-toughness aluminum alloy finished product;
wherein, when the two-stage aging treatment is carried out, the aging treatment is firstly carried out at 132-138 ℃ for 3-4h, and then the aging treatment is carried out at 157-163 ℃ for 10-11 h.
2. The preparation method according to claim 1, wherein the high-strength high-toughness aluminum alloy comprises the following components: 2.3 to 2.5 weight percent of Si, 2.2 to 2.5 weight percent of Mg, 1.9 to 2.5 weight percent of Cu, and the balance of aluminum and inevitable impurities.
3. The preparation method as claimed in claim 1, wherein in S2, the pressure of 200-230MPa is adopted for compression molding.
4. The method according to claim 1, wherein the sintering is performed in an argon atmosphere in S2.
5. The method as claimed in claim 1, wherein the sintering temperature in S2 is 563-564 ℃.
6. The method according to claim 1, wherein in S2, sintering is performed using a mesh belt furnace; the mesh belt furnace is provided with a sintering section and a cooling section, and a fan is arranged in the cooling section.
7. The method as claimed in claim 1, wherein the hot extrusion temperature in S3 is 543-.
8. The method as claimed in claim 1, wherein the solution treatment is performed at 562-564 ℃ in S4.
9. The method as claimed in claim 1, wherein the dual-stage aging treatment is performed in S5, wherein the dual-stage aging treatment is performed at 134-136 ℃ for 3.2-3.8h, and then at 159-161 ℃ for 10.2-10.8 h.
10. A high-strength high-toughness aluminum alloy, which is produced by the production method as recited in any one of claims 1 to 9.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111390921.XA CN114086041B (en) | 2021-11-23 | 2021-11-23 | High-strength high-toughness aluminum alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111390921.XA CN114086041B (en) | 2021-11-23 | 2021-11-23 | High-strength high-toughness aluminum alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114086041A CN114086041A (en) | 2022-02-25 |
| CN114086041B true CN114086041B (en) | 2022-06-14 |
Family
ID=80303184
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202111390921.XA Active CN114086041B (en) | 2021-11-23 | 2021-11-23 | High-strength high-toughness aluminum alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114086041B (en) |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105234411A (en) * | 2014-07-11 | 2016-01-13 | 东睦新材料集团股份有限公司 | Preparation method for manufacturing rotor of phaser through powder metallurgy |
| CN107012346A (en) * | 2017-03-14 | 2017-08-04 | 郭和谦 | A kind of preparation method of the aluminium base of high temperature resistant low thermal coefficient of expansion/PMOS base complex layered materials |
| CN109881069A (en) * | 2019-04-09 | 2019-06-14 | 宁夏大学 | A kind of high intensity, high tenacity, the preparation method of high-wearing feature metal material |
| CN110735070A (en) * | 2019-10-24 | 2020-01-31 | 珠海格力节能环保制冷技术研究中心有限公司 | Aluminum alloy material, wear-resistant part, preparation method and scroll compressor |
| CN110923518A (en) * | 2019-12-04 | 2020-03-27 | 中车青岛四方机车车辆股份有限公司 | 6XXX series aluminum alloy and aging process thereof |
| KR20200048518A (en) * | 2018-10-30 | 2020-05-08 | 명화공업주식회사 | 400MPa GRADE HIGH-STRENGTH ALUMINUM ALLOY AND ITS MANUFACTURING METHOD |
| CN112176212A (en) * | 2020-09-25 | 2021-01-05 | 上海交通大学 | Composite material with in-situ synthesized particles and preparation method thereof |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3235916B1 (en) * | 2016-04-19 | 2018-08-15 | Rheinfelden Alloys GmbH & Co. KG | Cast alloy |
-
2021
- 2021-11-23 CN CN202111390921.XA patent/CN114086041B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105234411A (en) * | 2014-07-11 | 2016-01-13 | 东睦新材料集团股份有限公司 | Preparation method for manufacturing rotor of phaser through powder metallurgy |
| CN107012346A (en) * | 2017-03-14 | 2017-08-04 | 郭和谦 | A kind of preparation method of the aluminium base of high temperature resistant low thermal coefficient of expansion/PMOS base complex layered materials |
| KR20200048518A (en) * | 2018-10-30 | 2020-05-08 | 명화공업주식회사 | 400MPa GRADE HIGH-STRENGTH ALUMINUM ALLOY AND ITS MANUFACTURING METHOD |
| CN109881069A (en) * | 2019-04-09 | 2019-06-14 | 宁夏大学 | A kind of high intensity, high tenacity, the preparation method of high-wearing feature metal material |
| CN110735070A (en) * | 2019-10-24 | 2020-01-31 | 珠海格力节能环保制冷技术研究中心有限公司 | Aluminum alloy material, wear-resistant part, preparation method and scroll compressor |
| CN110923518A (en) * | 2019-12-04 | 2020-03-27 | 中车青岛四方机车车辆股份有限公司 | 6XXX series aluminum alloy and aging process thereof |
| CN112176212A (en) * | 2020-09-25 | 2021-01-05 | 上海交通大学 | Composite material with in-situ synthesized particles and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN114086041A (en) | 2022-02-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103667825B (en) | A kind of ultra-high-strength/tenacity anticorodal and manufacture method thereof | |
| CN108425050B (en) | High-strength high-toughness aluminum lithium alloy and preparation method thereof | |
| CN102796976B (en) | Staged homogenization heat treatment method for improving microstructure and performances of Zr-containing 7xxx aluminum alloy | |
| CN102796925B (en) | High-strength die-casting aluminum alloy for pressure casting | |
| KR102452962B1 (en) | 6 series aluminum alloy and its manufacturing method, mobile terminal | |
| CN112522645B (en) | Preparation method of high-strength high-toughness homogeneous fine-grain CrCoNi intermediate-entropy alloy thin plate | |
| CN107164669B (en) | A kind of easy processing recycling 7 is wrought aluminium alloy and preparation method thereof | |
| CN103725932A (en) | High-strength silicon, magnesium, manganese-aluminum bar and preparation method thereof | |
| CN113444940A (en) | Preparation method of high-strength high-toughness corrosion-resistant 7055 aluminum alloy medium-thickness plate | |
| CN113737068B (en) | High-strength and high-toughness corrosion-resistant 7xxx series aluminum alloy and processing method thereof | |
| CN106636806A (en) | Fine-grain medium-strength aluminum alloy as well as preparation method and application thereof | |
| CN106929720B (en) | A kind of high strength easy recrystallization wrought aluminium alloy and preparation method thereof | |
| CN109136685B (en) | A kind of aluminium alloy and its preparation method and application | |
| CN104789826A (en) | Automobile air conditioner compressor planetary plate and production method thereof | |
| CN114959377A (en) | Ultrahigh-strength and high-toughness deformable cast aluminum alloy and preparation method thereof | |
| CN111074121B (en) | Aluminum alloy and preparation method thereof | |
| CN113403508A (en) | Heat treatment process for spray-formed high-silicon wear-resistant aluminum alloy | |
| CN109988953A (en) | High-strength and high ductility Al-Cu system cast aluminium alloy gold and preparation method thereof and railway locomotive components | |
| CN114086041B (en) | High-strength high-toughness aluminum alloy and preparation method thereof | |
| CN114686735A (en) | Wrought aluminum alloy with gradient structure and preparation method thereof | |
| CN114561575A (en) | Preparation method of Er and Zr compositely added high-toughness aluminum alloy | |
| CN114480984A (en) | Ti alloyed low-density high-strength steel and preparation method thereof | |
| CN115961184B (en) | Nanoparticle reinforced aluminum alloy and preparation method thereof | |
| CN115233058B (en) | Low-cost high-performance wrought magnesium alloy and preparation method thereof | |
| CN115369294B (en) | Heat-resistant Al-Mg-Cu-Zn alloy and heat treatment process |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |