CN115044809A - Cast aluminum-silicon alloy and preparation method thereof, and aluminum-silicon alloy for aviation or automobile castings - Google Patents
Cast aluminum-silicon alloy and preparation method thereof, and aluminum-silicon alloy for aviation or automobile castings Download PDFInfo
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Abstract
The application provides a casting aluminum-silicon alloy, a preparation method thereof and the aluminum-silicon alloy for aviation or automobile castings, which comprises the following components in percentage by mass: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg, 0.1 to 0.2 percent of Mn0.1 to 0.2 percent of Ti, 0.07 to 0.1 percent of Er, 0.01 to 0.02 percent of Sr and TiB 2 0.08 to 0.12 percent of Al, less than or equal to 0.2 percent of Fe and the balance of Al. The method optimizes the components of the aluminum-silicon alloy, adopts an aluminum ingot with the purity of 99.00-99.77 percent as a raw material, and matches a proper amount of TiB 2 The ceramic particles are matched with a heat treatment process to prepare the low-cost high-strength high-toughness aluminum-silicon alloy, the mechanical property of the low-cost high-strength high-toughness aluminum-silicon alloy is equivalent to that of the aluminum-silicon alloy produced by high-purity aluminum, but the cost of the low-cost high-strength high-toughness aluminum-silicon alloy is reduced by more than 40 percent compared with that of the aluminum-silicon alloy prepared by using a high-purity aluminum ingot, and the high-mechanical property alloy is improved due to impurity limitationThe high cost, thereby expanding the application field of the high-strength and high-toughness silicon-aluminum alloy.
Description
Technical Field
The application relates to the field of metal materials, in particular to a casting aluminum-silicon alloy, a preparation method thereof and the aluminum-silicon alloy for aviation or automobile castings.
Background
In recent years, with the development requirements in the fields of aviation and aerospace, high-strength and high-toughness cast Al-Si alloys with different components have been produced. The A357 (American military standard, Al-7Si-0.6Mg) alloy is widely applied to foreign markets as one of the high-strength and high-toughness cast Al-Si alloys produced by the corresponding transshipment. Similarly, the widely used high toughness cast Al-Si alloy is ZL114A alloy similar to the A357 alloy, which is a very heavy branch of the cast Al-Si alloy and is used more frequently in parts of airplanes and missiles which need to bear high loads. The ZL114A alloy has high strength due to the fact that the Mg content is 0.4-0.7%, but the elongation is low, and therefore plasticity and toughness of the ZL114A alloy are affected. The tensile strength of a sand casting made of the A357 alloy can reach 320MPa, the elongation is more than 5%, the performance of the sand casting is far higher than that of ZL114A alloy widely used in aerospace enterprises at present, and ZL114A alloy is facing severe test due to the characteristic of too low performance.
Meanwhile, as the weight reduction of automobiles, especially the weight reduction under springs, is more and more urgent, the ZL101A aluminum alloy shows limitations in performance, especially tensile strength and yield strength. The ZL114A can make up the performance deficiency of ZL101A aluminum alloy, however, in order to ensure the final mechanical property of ZL114A aluminum alloy, ZL114A has high requirements for the impurity content of the aluminum alloy, for example, high-purity aluminum (Al is more than or equal to 99.999%) is generally adopted for aluminum ingots, and therefore, the application of ZL114A aluminum alloy in industries such as automobiles and the like is severely limited by the increase of the cost of ZL114A aluminum alloy.
The main alloy elements in the ZL114A aluminum alloy are Si and Mg, and the main impurity is Fe. Increasing the yield strength of ZL114A aluminum alloy increases the Mg content of the alloy, and as the Mg content increases, the tensile strength and yield strength of the alloy increase, but the elongation thereof decreases dramatically. Meanwhile, Fe impurity is also an important factor influencing the strength and elongation of the alloy. Fe is harmful to the action of ZL114A aluminum alloy relative to other elements, and the higher the Fe content is, the lower the hardness and elongation of the alloy are. Especially the elongation, is seriously impaired. Therefore, even when the Fe content of the alloy is low, it can form an Fe-rich phase, and therefore, the impurities of the Fe content must be strictly controlled. In general, ZL114A adds a refiner such as Al5TiB or AlTiC during the melting process to refine the alloy cast structure, but Al114A aluminum alloy has limited refining effect and reinforcing effect.
How to solve the problem of the influence of grain refinement, obdurability matching and impurity weakening of ZL114A aluminum alloy on the performance is an important way for improving the performance and application of ZL114A aluminum alloy.
Disclosure of Invention
In order to solve the problems, the application provides a casting aluminum-silicon alloy, a preparation method thereof and an aluminum-silicon alloy for aviation or automobile castings, which solve the problem that the cost of the aluminum-silicon alloy with high mechanical property is high due to limited impurities by optimizing alloy components, and simultaneously improve the toughness of the aluminum-silicon alloy.
In a first aspect, the present application provides a cast aluminum-silicon alloy, which comprises the following components by mass percent: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg, 0.1 to 0.2 percent of Mn, 0.1 to 0.2 percent of Ti, 0.07 to 0.1 percent of Er, 0.01 to 0.02 percent of Sr and TiB 2 0.08 to 0.12 percent of Al, less than or equal to 0.2 percent of Fe and the balance of Al.
Optionally, in some embodiments of the present application, the cast aluminum-silicon alloy includes, by mass: 7.0 to 7.15 percent of Si, 0.54 to 0.60 percent of Mg, 0.14 to 0.175 percent of Mn, 0.12 to 0.18 percent of Ti, 0.08 to 0.095 percent of Er, 0.012 to 0.015 percent of Sr, and TiB 2 0.085 to 0.115 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al.
The Ti element in the aluminum alloy is added in the form of Al-Ti intermediate alloy. TiAl formation of Ti with Al 3 The phase becomes a non-spontaneous core during crystallization, and plays a role in refining a cast structure and a weld structure. TiB 2 With TiB 2 Added in the form of/Al composite material, TiB 2 Seed material of hexagonal crystal structure, TiB 2 And the mismatching degree of the plane point front of alpha-Al is less than 15 percent, and from the point of lattice matching, TiB 2 Is a latent form of alpha-AlThe nuclear substrate can be used as a heterogeneous nucleation core to effectively refine grains in the solidification process, and meanwhile, the sub-micron TiB 2 The ceramic particles are dispersed in the matrix to play a role in dispersion strengthening and improve the strength of the alloy.
In a second aspect, the present application provides a method for producing a cast aluminum-silicon alloy, comprising:
obtaining an alloy melt with the following alloy components in percentage by mass: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg, 0.1 to 0.2 percent of Mn, 0.1 to 0.2 percent of Ti, 0.07 to 0.1 percent of Er, 0.01 to 0.02 percent of Sr and TiB 2 0.08-0.12 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining an alloy ingot after casting;
and carrying out solution quenching treatment on the alloy cast ingot, then carrying out aging treatment, and cooling to obtain the aluminum-silicon alloy.
Optionally, in some embodiments of the present application, the solution quenching treatment adopts the following process parameters: the solid solution temperature is 540-545 ℃, the solid solution time is 10-16 h, and the quenching temperature is 60-80 ℃.
Optionally, in some embodiments of the present application, the aging treatment adopts the following process parameters: the aging temperature is 150-170 ℃, and the aging time is 3-8 h; and/or the cooling is air cooling.
Optionally, in some embodiments of the present application, an aluminum ingot with a purity of more than 99.00%, a Si-containing raw material, a Mn-containing raw material, and a Ti-containing raw material are added into a melting furnace to be heated and melted, all the raw materials are dissolved and then kept warm and kept stand, and then Mg and TiB are sequentially added 2 dissolving/Al composite material and Er-containing raw material, and standing to obtain intermediate melt of required components;
and removing impurities from the intermediate melt, refining, adding a Sr-containing raw material for modification while refining, and removing slag to obtain the alloy melt.
Optionally, in some embodiments of the present application, the Si-containing raw material is an Al — Si master alloy; and/or the Mn-containing raw material is Al-Mn intermediate alloy; and/or, the Ti-containing raw material is Al-Ti intermediate alloy; and/or the Er-containing raw material is Al-Er intermediate alloy; and/or the Sr-containing raw material is Al-Sr intermediate alloy.
Optionally, in some embodiments of the present application, the TiB 2 TiB of/Al composite material 2 Is 20-30% by mass, and/or the TiB 2 The particle size diameter of the/Al composite material is 100nm-1.0 mu m.
Optionally, in some embodiments of the present application, the aluminum-silicon alloy has a tensile strength of 355MPa to 377MPa, a yield strength of 300MPa to 331MPa, and an elongation of > 5%.
Correspondingly, the application also provides an aluminum-silicon alloy for aviation or automobile castings, which comprises the aluminum-silicon alloy; or the aluminum-silicon alloy prepared by the preparation method.
Alternatively, the aluminum-silicon alloy in the embodiments of the present application may be used for manufacturing aerospace castings or automobile castings.
The application has one or more of the following beneficial effects:
according to the method, the components of the aluminum-silicon alloy are optimized, the aluminum ingot with the purity of 99.00-99.77% is used as the raw material to prepare the high-strength and high-toughness aluminum-silicon alloy, the mechanical property of the high-strength and high-toughness aluminum-silicon alloy is equivalent to that of ZL114A alloy produced by high-purity aluminum, but the cost of the high-strength and high-toughness aluminum-silicon alloy is reduced by 40% compared with that of the aluminum-silicon alloy prepared by using the high-purity aluminum ingot, the problem of high cost of the high-strength and high-toughness aluminum-silicon alloy due to impurity limitation is solved, and the application field of the high-strength and high-toughness aluminum-silicon alloy is expanded.
According to the method, the components of the aluminum-silicon alloy are optimized, the Fe phase morphology influencing the mechanical property in the aluminum-silicon alloy can be improved by adding Mn element, the influence of Fe impurities on the mechanical property is weakened, and the problem that the high-mechanical-property silicon-aluminum alloy (ZL114A aluminum alloy) is limited by high production cost of impurity raw materials is solved; addition of TiB 2 The grains can be used as nucleation cores to refine the grain size of the cast structure of the aluminum-silicon alloy in the solidification process, so as to play a role of fine grain reinforcement, further be beneficial to maintaining the elongation of the material, and simultaneously be submicron-grade pure-phase TiB 2 The particles can play a role in dispersion strengthening, thereby being beneficial to improving the tensile strength and the yield strength of the material and solving the problem of the obdurability matching of the existing aluminum-silicon alloy.
According to the aluminum-silicon alloy, the components of the aluminum-silicon alloy are optimized, and the aluminum alloy is ensured to have the characteristics of high strength and toughness, high yield and the like by matching with an accurate heat treatment process, so that the tensile strength of the aluminum alloy can reach 377MPa, the yield strength can reach 331MPa, and the elongation is more than 5%. Compared with the existing ZL114A aluminum alloy, the mechanical property is improved, but the cost is reduced by nearly 40%.
Drawings
In order to more clearly illustrate the technical solutions in the embodiments of the present application, the drawings required to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the description below are only some embodiments of the present application, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without creative efforts.
FIG. 1 is an as-cast gold phase diagram of a cast aluminum-silicon alloy provided herein;
fig. 2 is an as-cast gold phase diagram of the cast aluminum-silicon alloy provided herein.
Detailed Description
The technical solutions in the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is obvious that the described embodiments are only a part of the embodiments of the present application, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present application. Furthermore, it should be understood that the detailed description and specific examples, while indicating exemplary embodiments of the invention, are given by way of illustration and explanation only, and are not intended to limit the scope of the invention. In this application, unless stated to the contrary, the use of directional terms such as "upper", "lower", "left" and "right" generally refer to the upper, lower, left and right sides of the device in actual use or operation, and specifically to the orientation of the drawing figures.
The present application provides a cast aluminum-silicon alloy, a method for producing the same, and an aluminum-silicon alloy for aviation or automobile castings, which will be described in detail below. It should be noted that the following description of the embodiments is not intended to limit the preferred order of the embodiments of the present application. In the following embodiments, the descriptions of the respective embodiments have respective emphasis, and reference may be made to related descriptions of other embodiments for parts that are not described in detail in a certain embodiment.
The related national standard ZL114A for aerospace (QJ 3185-: 6.5 to 7.5 percent of Si, 0.45 to 0.75 percent of Mg, 0.08 to 0.25 percent of Ti, 0.04 to 0.07 percent of Be, less than or equal to 0.2 percent of impurity Fe and less than or equal to 0.1 percent of Mn. Addition of Al is frequently carried out in the casting 5 TiB, AlTiC and other grain refiners refine the structure, and sodium salt or strontium is added for modification.
The application provides a cast aluminum-silicon alloy, which comprises the following components in percentage by mass: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg, 0.1 to 0.2 percent of Mn, 0.1 to 0.2 percent of Ti, 0.07 to 0.1 percent of Er, 0.01 to 0.02 percent of Sr and TiB 2 0.08 to 0.12 percent of Al, less than or equal to 0.2 percent of Fe and the balance of Al. In some embodiments, the cast aluminum-silicon alloy comprises the following components in percentage by mass: 7.0 to 7.15 percent of Si, 0.54 to 0.60 percent of Mg, 0.14 to 0.175 percent of Mn, 0.12 to 0.18 percent of Ti, 0.08 to 0.095 percent of Er, 0.012 to 0.015 percent of Sr, and TiB 2 0.085 to 0.115 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al.
In the embodiment, the aluminum ingot (A00 aluminum) with the purity of 99.00-99.77% is used as the raw material by optimizing the alloy components, so that the production cost of the aluminum-silicon alloy with high mechanical property is reduced, and the component range of main alloy elements Si and Mg is optimized. The addition of Sr element is optimized, and the modification effect of Si and the gas content of the melt are ensured. Adding Mn, Er and other trace elements and trace TiB 2 The Mn element is added to improve the Fe phase morphology affecting the mechanical property of the aluminum-silicon alloy, and the influence of the Fe impurity on the mechanical property is weakened, because the excessive Fe impurity affects the tensile property and the yield property of the aluminum alloy, and on the other hand, the cost is affected, and meanwhile, the technical bias is overcome by adding the Mn element, because the Mn element is taken as an impurity component in the existing ZL114A aluminum alloy component design rather than being added as a microalloying component, the Mn element is converted into a large power-assisted active component, so that the Fe phase morphology is improved, waste is turned into wealth, and the alloy cost is reduced; TiB 2 Is a ceramic particle which can be used as a nucleation in the solidification processThe core refines the grain size of the as-cast structure of the aluminum alloy, plays a role in fine-grained reinforcement, is favorable for maintaining the elongation of the material, and simultaneously has submicron-grade TiB 2 The particles can play a role in dispersion strengthening, so that the tensile strength and the yield strength of the material are improved, the problem of strength and toughness matching of the aluminum-silicon alloy is solved, and the elongation can be ensured to be more than 5%. In addition, by adding TiB to the alloy composition 2 And the content of the composite material is ensured to reach 0.08-0.12%, the composite material plays a role in refiner and dispersion strengthening, and the composite material is beneficial to improving the strength of the material and the elongation at the same time. In the prior art, Al is added 5 TiB、Al 5 TiC and other refiners play a refining role, and Al is added 5 B is introduced into the TiB to play a refining role, but the quantitative TiB cannot be stably formed 2 . And the Er element is added, so that the strength and the recrystallization temperature of the aluminum alloy can be further improved. In other embodiments, the optimized alloy components are matched with a heat treatment process to obtain a low-cost high-strength and high-toughness aluminum-silicon alloy material, the tensile strength, the yield strength and the elongation all reach the aerospace grade 1 standard, but the cost of the aluminum-silicon alloy material is reduced by 40 percent compared with ZL114A aluminum alloy prepared by using a high-purity aluminum ingot.
Correspondingly, the application also provides a preparation method of the cast aluminum-silicon alloy, which comprises the following steps:
s1, obtaining an alloy melt with the following alloy components in percentage by mass: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg, 0.1 to 0.2 percent of Mn, 0.1 to 0.2 percent of Ti, 0.07 to 0.1 percent of Er, 0.01 to 0.02 percent of Sr and TiB 2 0.08 to 0.12 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining alloy cast ingots after casting.
In step S1, the aluminum raw material used for melting is an aluminum ingot with a purity of greater than 99.00%, and the aluminum ingot with the purity may be industrial raw aluminum, and the purity is generally 99.00 to 99.77%. The aluminum raw material is a primary product in the aluminum electrolysis industry and is directly refined by simple gas in the electrolysis process. The purity of the high-purity aluminum is generally 99.999% -99.9999%, the aluminum raw material is a product obtained by the combined process of electrolytic refining and segregation of industrial raw aluminum, and the production and manufacturing cost of the high-purity aluminum is far higher than that of the industrial raw aluminum used in the application.
It is further noted that the alloy melt obtained in S1 and having the above composition can be obtained by conventional melting methods, such as a batch melting method or a semi-continuous melting method.
And S2, carrying out solution quenching treatment on the alloy ingot.
Specifically, an aluminum-silicon alloy cast ingot is put into a hot air circulation solid solution furnace for solid solution treatment, and is quickly put into water with set temperature for quenching after solid solution treatment.
In the solution treatment, solution treatment equipment other than the hot-air circulation solution treatment furnace may be used. In other embodiments, the solution quenching treatment employs the following process parameters: the solid solution temperature is 540-545 ℃, the solid solution time is 10-16 h, and the quenching temperature in water is 60-80 ℃. The matching of the solid solution temperature and the solid solution time is favorable for ensuring Mg 2 The re-dissolution of the solidification precipitated phases of the Si phase, the Er phase and the Si phase, and the like, and the reasonable quenching temperature can ensure that the supersaturated solid solution is fixed and not decomposed, prevent the material from cold cracking, prevent the precipitation of a strengthening phase and reduce the mechanical property after quenching aging.
In a specific example, the temperature of solid solution may be any one of 540 ℃, 541 ℃, 542 ℃, 543 ℃, 544 ℃ and 545 ℃, for example, and may be any other value within the range of solid solution temperature. The solid solution time may be any time of 10h, 11h, 12h, 13h, 14h, 15h or 16h, and may be any other value within the above solid solution time range.
And S3, aging treatment is carried out after the step S2, and the aluminum-silicon alloy is obtained after rapid cooling. In some embodiments, after the aging treatment is completed, air cooling is used to cool the aluminum-silicon alloy ingot.
Specifically, the aluminum-silicon alloy cast ingot subjected to the solution quenching treatment in the step S2 is placed into a hot air circulation aging furnace for aging treatment. In other embodiments, the aging treatment employs the following process parameters: the aging temperature is 150-170 ℃, and the aging time is 3-8 h; in one embodiment, for example, the temperature of aging may be any of 150 ℃, 155 ℃, 160 ℃, 165 ℃ or 170 ℃, although any other temperature within the above aging temperature range may be used. The aging time may be any of 3h, 4h, 5h, 6h, 7h or 8h, but any other time within the above aging time range may be employed.
In other embodiments of the present application, in order to obtain an aluminum-silicon alloy with relatively good elongation and higher tensile strength and yield strength, the aluminum-silicon alloy components designed in the above embodiments are processed by a T6 heat treatment process, and the tensile strength, yield strength and elongation of the processed material can reach above 355MPa, above 300MPa and above 5%, which are all improved compared with the ZL114A alloy after the same heat treatment. The following preferred process parameters may be specifically employed: the solid solution temperature is 545 ℃, the solid solution time is 12h, the quenching temperature is 80 ℃, the aging temperature is 160 ℃, the aging time is 6h, the tensile strength of the treated aluminum-silicon alloy reaches 376.09MPa, the yield strength reaches 331MPa, and the elongation reaches 5.4%.
It should be noted that, in the specific implementation, a person skilled in the art can match the alloy composition of the present application to the corresponding heat treatment process conditions according to actual needs to obtain the aluminum-silicon alloy material with corresponding properties.
In some embodiments of the present application, an aluminum-silicon alloy melt of a designed alloy composition is obtained using the steps comprising:
and S101, calculating and batching according to the designed components of the aluminum-silicon alloy.
S102, sequentially adding aluminum ingots with the purity of more than 99.00%, Si-containing raw materials, Mn-containing raw materials and Ti-containing raw materials into a smelting furnace, heating to 720-760 ℃ for melting, preserving heat and standing for 50-70 min after all the raw materials are dissolved, and sequentially adding Mg and TiB 2 dissolving/Al composite material and Er-containing raw material, standing for 8-15 min, performing component detection on the melt to obtain the mass content of each component of the melt, and adjusting each component of the melt to be qualified according to the detection result to obtain an intermediate melt of the required component. In a specific example, component detection may be performed using spectroscopy. In other embodiments of the present invention, the substrate may be,the Si-containing raw material is Al-Si intermediate alloy; the Mn-containing raw material is Al-Mn intermediate alloy; the Ti-containing raw material is Al-Ti intermediate alloy; the Er-containing raw material is Al-Er intermediate alloy; the intermediate alloy is used as the raw material, so that the burning loss of the raw material is avoided, and the melting of the high-melting-point alloy is facilitated. By adding TiB 2 Introduction of TiB into/Al composite material 2 ，TiB 2 Is extremely stable, so that TiB can be accurately controlled according to the addition amount in the subsequent addition process 2 Amount to match the desired amount of TiB 2 。
In step S102, the melting temperature is controlled not to exceed 760 ℃. When the melting temperature exceeds 770 ℃, serious oxidation of the aluminum alloy can be caused, hydrogen absorption and slag inclusion in the melting process are increased, coarse grains appear in the casting solidification process, and the mechanical property of the aluminum-silicon alloy is reduced. The standing time is 8-15 minutes, which is beneficial to TiB 2 More uniform dispersion in the aluminum melt and avoidance of TiB 2 Agglomeration and sedimentation phenomena occur, thereby being beneficial to improving the TiB 2 The refining and strengthening effects.
S103, adding a slag removing agent into the intermediate melt, and removing impurities.
And S104, refining after impurity removal to play a role in purifying the aluminum liquid, and adding a Sr-containing raw material to perform modification. The Sr-containing raw material is a long-acting alterant, and the modification time can last for 6-8 h, so that coarse flaky eutectic silicon is refined to form a fine structure, and the mechanical property is further improved; and the Sr-containing raw material is added during refining, so that the modification effect is improved, and the burning loss and the decline can be reduced. In a specific example, the Sr-containing raw material employs an Al — Sr intermediate alloy.
It should be noted that the refining process may employ conventional degassing rotary refining. For example, degassing refining is used, inert gases or refining agents being introduced into the intermediate melt. In a specific example, argon gas is introduced into the intermediate melt by using a rotary blowing device, the rotating speed is 300-700 r/min, and the refining time is 10-20 min.
And S105, after modification, removing floating materials on the surface of the melt, and deslagging to obtain the aluminum-silicon alloy melt.
And S106, adjusting components, degassing, refining and standing, then carrying out spectrum detection on the aluminum-silicon alloy melt sample, and adjusting the components to be qualified to obtain the melt.
In other embodiments of the present application, TiB 2 TiB of/Al composite material 2 Is 20-30% by mass, and/or TiB 2 The particle size diameter of the/Al composite material is 100nm-1.0 mu m. TiB 2 The particles are used as nucleation cores in the solidification process to effectively refine the size of the as-cast crystal grains of the aluminum alloy, play a role in fine grain strengthening, and meanwhile, the submicron TiB with the grain size diameter of 100nm-1.0 mu m 2 The particles can perform the function of dispersion strengthening, and TiB can be seen from figure 2 2 The particles are uniformly distributed in the crystal, so that the structure is effectively refined and the strength is improved. In some embodiments, TiB 2 the/Al composite material is prepared by adopting the following method:
comprises the following components, wherein the mass percentage of B is 1.0-2.5%, the molar ratio of Ti to B is 1/2, the balance is Al, and the phase composition comprises alpha-Al and TiB 2 ，TiB 2 An average particle size of 0.6 μm or less, TiB 2 The particles are dispersed relatively uniformly; the method comprises the following steps:
(1) preparing raw materials, weighing H according to requirements 3 BO 3 、TiO 2 Aluminum powder, titanium powder, aluminum ingot, wherein H 3 BO 3 ：TiO 2 : al powder: molar ratio of Ti powder ═ (3.5-5.2): (0.5-2.1):(3.5-5.7): (0.2-1.5), wherein the molar ratio of Ti to B is 1/2, and the purity of the aluminum ingot is 99.9%;
(2) will H 3 BO 3 、TiO 2 Uniformly mixing, heating at 200 ℃ for two hours, removing water, taking out every 20-40 minutes in the removing process, stirring the powder, and drying the powder uniformly without caking;
(3) heating the TiO 2 、H 3 BO 3 Mixing the powder with aluminum powder and titanium powder uniformly, placing the uniformly mixed powder in a die, and pressing the powder into a block;
(4) heating the aluminum ingot to 900-The reaction time is 5-8 min; after the reaction is completed, press C 2 C l6 Refining, stirring, standing for 5-20min, removing slag, repeating the stirring, standing and removing slag process for 1-2 times, pouring the obtained melt into a steel mould preheated to 250 ℃ at the temperature of 750-900 ℃ to obtain the large-volume-fraction Al-TiB 2 Pure phase master alloys, i.e. TiB 2 a/Al composite material.
The method adopts a melt self-propagating direct synthesis method, utilizes wide raw material sources and has low cost TiO 2 、H 3 BO 3 Develops a pure phase Al-TiB with environment-friendly and clean preparation process and high particle content 2 And (3) intermediate alloy. Solves the problems of difficult preparation, high preparation cost and TiAl existing in the traditional method 3 Residual problem, TiB in master alloy 2 The particle size is small, the distribution is uniform, the particle content is high or the volume fraction is large, the volume fraction can reach 25 percent, and generally can reach 50 percent; the obtained intermediate alloy is pure phase and only contains alpha-Al and TiB 2 。
In other embodiments, the optimized aluminum-silicon alloy components are matched with an accurate heat treatment process to obtain the aluminum-silicon alloy, and tests show that the tensile strength of the aluminum-silicon alloy is 355MPa-377MPa, the yield strength is 300MPa-331MPa, and the elongation is more than 5%. The existing related aerospace level 1 standard ZL114A is a single-cast test bar in a T6 heat treatment state, the tensile strength is more than or equal to 350MPa, the yield strength is more than or equal to 280MPA, and the elongation is more than or equal to 5%. Compared with the mechanical properties of the conventional ZL114A aluminum alloy, the aluminum-silicon alloy has improved tensile strength and yield strength. However, the prior ZL114A aluminum alloy has high requirements on the impurity content of the aluminum alloy, and 99.99 high-purity aluminum ingots are usually adopted as the aluminum ingots, so that the manufacturing cost is high.
In another embodiment of the application there is also provided an aluminium-silicon alloy for aerospace or automotive castings comprising an aluminium-silicon alloy as described above; or the aluminum-silicon alloy prepared by the preparation method. The low-cost high-strength and high-toughness aluminum-silicon alloy can be applied to the field of aerospace, and under the condition that the production cost is greatly reduced, the excellent mechanical property of the aluminum-silicon alloy is applied to industries such as automobiles and the like to make up the performance deficiency of ZL101A aluminum alloy, so that the light weight of automobiles is met, and particularly the increasingly urgent needs of weight reduction under springs are met.
The aluminum-silicon alloy in the embodiment of the application can be used for manufacturing aviation castings or automobile castings.
In order to make the details and operation of the above-mentioned embodiments of the present invention clearly understandable to those skilled in the art and to make the cast aluminum-silicon alloy and the method for manufacturing the same according to the embodiments of the present invention significantly improve the performance, the above-mentioned technical solutions are exemplified by a plurality of examples.
Example 1
The embodiment provides a preparation method of a cast aluminum-silicon alloy, which comprises the following steps:
s1, obtaining an alloy melt with the following alloy components in percentage by mass: 7.077% of Si, 0.54% of Mg, 0.15% of Mn, 0.172% of Ti, 0.08% of Er, 0.013% of Sr and 0.013% of TiB 2 0.08 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining alloy cast ingots after casting.
S2, putting the alloy ingot into a hot air circulation solid solution furnace for solid solution quenching treatment, wherein the solid solution quenching treatment adopts the following process parameters: the solid solution temperature is 542 ℃, the solid solution time is 15h, and the quenching temperature in water is 60 ℃.
S3, placing the alloy ingot subjected to the S2 solution quenching treatment into a hot air circulation aging furnace for aging treatment, wherein the aging treatment adopts the following process parameters: the aging temperature is 150 ℃, and the aging time is 4 h; and cooling to obtain the aluminum-silicon alloy.
Example 2
In this embodiment, an alloy ingot with the following alloy components is obtained by fusion casting, and the components include, by mass: 7.2 percent of Si, 0.55 percent of Mg, 0.14 percent of Mn, 0.18 percent of Ti, 0.07 percent of Er, 0.012 percent of Sr and TiB 2 0.1 percent, less than or equal to 0.2 percent of Fe and the balance of Al.
This example used the same heat treatment process as example 1.
Example 3
In this embodiment, an alloy ingot with the following alloy components is obtained by fusion casting, and the components include, by mass: 7.15 percent of Si, 0.49 percent of Mg, 0.14 percent of Mn, 0.17 percent of Ti, 0.07 percent of Er, 0.01 percent of Sr,TiB 2 0.1 percent, less than or equal to 0.2 percent of Fe and the balance of Al.
This example used the same heat treatment process as example 1.
Example 4
S1, obtaining an alloy melt with the following alloy components in percentage by mass: 7.1 percent of Si, 0.57 percent of Mg, 0.17 percent of Mn, 0.156 percent of Ti, 0.09 percent of Er, 0.012 percent of Sr and TiB 2 0.11 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining an alloy cast ingot after casting.
S2, putting the alloy ingot into a hot air circulation solid solution furnace for solid solution quenching treatment, wherein the solid solution quenching treatment adopts the following process parameters: the solid solution temperature is 540 ℃, the solid solution time is 15h, and the quenching temperature in water is 75 ℃.
S3, placing the alloy ingot subjected to the S2 solution quenching treatment into a hot air circulation aging furnace for aging treatment, wherein the aging treatment adopts the following process parameters: the aging temperature is 170 ℃, and the aging time is 5 h; and cooling to obtain the aluminum-silicon alloy.
Example 5
In this embodiment, an alloy ingot with the following alloy components is obtained by fusion casting, and the components include, by mass: 7.0 percent of Si, 0.57 percent of Mg, 0.16 percent of Mn, 0.19 percent of Ti, 0.07 percent of Er, 0.01 percent of Sr, and 0.01 percent of TiB 2 0.12 percent, less than or equal to 0.2 percent of Fe and the balance of Al.
This example uses the same heat treatment process as example 4.
Example 6
S1, obtaining an alloy melt with the following alloy components in percentage by mass: 7.15% of Si, 0.65% of Mg, 0.19% of Mn, 0.17% of Ti, 0.085% of Er, 0.015% of Sr, and TiB 2 0.118 percent, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining alloy cast ingots after casting.
This example uses the same heat treatment process as example 4.
Example 7
The embodiment provides a preparation method of a cast aluminum-silicon alloy, which comprises the following steps:
s1, obtaining an alloy melt with the following alloy components according to mass percentThe content is calculated according to the following: 7.08 percent of Si, 0.55 percent of Mg, 0.18 percent of Mn, 0.17 percent of Ti, 0.08 percent of Er, 0.02 percent of Sr, and 0.02 percent of TiB 2 0.09 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining an alloy cast ingot after casting.
S2, putting the alloy ingot into a hot air circulation solid solution furnace for solid solution quenching treatment, wherein the solid solution quenching treatment adopts the following process parameters: the solid solution temperature is 545 ℃, the solid solution time is 12h, and the quenching temperature in water is 80 ℃.
S3, placing the alloy ingot subjected to the S2 solution quenching treatment into a hot air circulation aging furnace for aging treatment, wherein the aging treatment adopts the following process parameters: the aging temperature is 160 ℃, and the aging time is 6 h; and cooling to obtain the aluminum-silicon alloy.
Example 8
S1, obtaining an alloy melt with the following alloy components in percentage by mass: 6.9 percent of Si, 0.48 percent of Mg, 0.17 percent of Mn, 0.19 percent of Ti, 0.08 percent of Er, 0.019 percent of Sr, and TiB 2 0.115 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining an alloy cast ingot after casting.
This example uses the same heat treatment process as example 7.
Example 9
S1, obtaining an alloy melt with the following alloy components in percentage by mass: 7.18 percent of Si, 0.50 percent of Mg, 0.19 percent of Mn, 0.155 percent of Ti, 0.085 percent of Er, 0.017 percent of Sr, and TiB 2 0.11 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining an alloy cast ingot after casting.
This example uses the same heat treatment process as example 7.
Comparative example
Preparing a ZL114A aluminum alloy material, comprising:
casting to obtain ZL114A aluminum alloy ingot: 6.5 percent of Si, 0.50 percent of Mg, 0.25 percent of Ti, 0.04 to 0.05 percent of Be, less than or equal to 0.2 percent of impurity Fe, less than or equal to 0.1 percent of Mn and the balance of Al. Addition of Al during casting 5 The TiB grain refiner refines the structure, and sodium salt is added for modification.
The obtained ZL114A aluminum alloy ingot is subjected to T6 heat treatment to obtain the ZL114A aluminum alloy material.
Table 1 is a table comparing the mechanical properties of the cast aluminum-silicon alloys prepared in examples 1-9 with those of the ZL114A aluminum alloy of the comparative example after heat treatment at T6:
TABLE 1
From the above, it can be seen that the cast aluminum-silicon alloys of examples 1-9 exhibit good mechanical properties, both tensile strength and yield strength higher than the ZL114A aluminum alloy grade 1 standard in QJ3185-2003, while the elongation is maintained above 5%.
As shown in FIG. 1 and FIG. 2, the cast aluminum-silicon alloy of examples 1 to 9 has an as-cast structure, and as shown in FIG. 1, the secondary dendrite arm spacing of 20 μm to 25 μm is measured by the intercept method, and the result shows that the aluminum alloy secondary dendrite arm spacing is significantly refined and the structure is uniform after refinement. And a needle-shaped or flaky beta-Fe phase is not found in the matrix, which shows that the addition of Mn element can improve the appearance of the Fe phase in the aluminum alloy. As can be seen from FIG. 2, TiB 2 The particles are uniformly distributed in the crystal, so that the structure is effectively refined and the strength is improved.
The present application is described in detail above, and specific examples are applied herein to explain the principles and embodiments of the present application, and the descriptions of the above examples are only used to help understand the method and the core idea of the present application; meanwhile, for a person skilled in the art, according to the idea of the present application, there may be variations in the specific embodiments and the application scope, and in summary, the content of the present specification should not be construed as a limitation to the present application.
Claims (10)
1. The cast aluminum-silicon alloy is characterized by comprising the following components in percentage by mass: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg0.1 to 0.2 percent of Mn0.1 to 0.2 percent of Ti0.1 to 0.2 percent of Er0.07 to 0.1 percent of,Sr0.01％-0.02％、TiB 2 0.08 to 0.12 percent of Al, less than or equal to 0.2 percent of Fe and the balance of Al.
2. The cast aluminum-silicon alloy according to claim 1, characterized in that the composition comprises, in mass percent: si7.0% -7.15%, Mg0.54% -0.60%, Mn0.14% -0.175%, Ti0.12% -0.18%, Er0.08% -0.095%, Sr0.012% -0.015%, TiB 2 0.085 to 0.115 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al.
3. A method for preparing a cast aluminum-silicon alloy is characterized by comprising the following steps:
obtaining an alloy melt with the following alloy components in percentage by mass: 6.8 to 7.2 percent of Si, 0.45 to 0.65 percent of Mg, 0.1 to 0.2 percent of Mn, 0.1 to 0.2 percent of Ti, 0.07 to 0.1 percent of Er, 0.01 to 0.02 percent of Sr and TiB 2 0.08-0.12 percent of Fe, less than or equal to 0.2 percent of Fe and the balance of Al, and obtaining an alloy ingot after casting;
and carrying out solution quenching treatment on the alloy cast ingot, then carrying out aging treatment, and cooling to obtain the aluminum-silicon alloy.
4. The method of manufacturing cast aluminium-silicon alloy according to claim 3, characterised in that the solution quenching treatment uses the following process parameters: the solid solution temperature is 540-545 ℃, the solid solution time is 10-16 h, and the quenching temperature is 60-80 ℃.
5. The method for the preparation of cast aluminium silicon alloy according to claim 3, characterised in that the ageing treatment uses the following process parameters: the aging temperature is 150-170 ℃, and the aging time is 3-8 h; and/or the presence of a gas in the gas,
the cooling is air cooling.
6. The method of manufacturing cast aluminum-silicon alloy according to claim 3, characterized in that,
adding aluminum ingot with purity more than 99.00%, Si-containing raw material, Mn-containing raw material and Ti-containing raw material into a smelting furnace, and heatingMelting, standing after all the raw materials are dissolved, and sequentially adding Mg and TiB 2 dissolving/Al composite material and Er-containing raw material, and standing to obtain intermediate melt of required components;
and removing impurities from the intermediate melt, refining, adding a Sr-containing raw material for modification while refining, and removing slag to obtain the alloy melt.
7. The method of manufacturing cast aluminum-silicon alloy according to claim 6, characterized in that,
the Si-containing raw material is Al-Si intermediate alloy; and/or the presence of a gas in the gas,
the Mn-containing raw material is Al-Mn intermediate alloy; and/or the presence of a gas in the gas,
the Ti-containing raw material is Al-Ti intermediate alloy; and/or the presence of a gas in the atmosphere,
the Er-containing raw material is Al-Er master alloy; and/or the presence of a gas in the gas,
the Sr-containing raw material is Al-Sr intermediate alloy.
8. The method of manufacturing cast aluminum-silicon alloy according to claim 6, characterized in that,
the TiB 2 TiB of/Al composite material 2 Is 20-30% by mass, and/or,
the TiB 2 The particle size diameter of the/Al composite material is 100nm-1.0 mu m.
9. The method of manufacturing a cast aluminium-silicon alloy according to any one of claims 3 to 8, characterised in that the aluminium-silicon alloy has a tensile strength of 355MPa-377MPa, a yield strength of 300MPa-331MPa and an elongation > 5%.
10. An aluminium-silicon alloy for aerospace or automotive castings, comprising an aluminium-silicon alloy according to any one of claims 1 to 2; or an aluminium-silicon alloy produced by the production method according to any one of claims 3 to 9.
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