CN115141959B - High-wear-resistance high-strength and high-toughness aluminum-silicon alloy and preparation method thereof - Google Patents

High-wear-resistance high-strength and high-toughness aluminum-silicon alloy and preparation method thereof Download PDF

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CN115141959B
CN115141959B CN202110853874.1A CN202110853874A CN115141959B CN 115141959 B CN115141959 B CN 115141959B CN 202110853874 A CN202110853874 A CN 202110853874A CN 115141959 B CN115141959 B CN 115141959B
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aluminum
melt
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silicon alloy
rare earth
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CN115141959A (en
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王万林
曾杰
彭健飞
甘培原
黄道远
刘玉泉
谢佳昊
韦德仕
何俞松
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Central South University
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    • 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
    • C22C21/04—Modified aluminium-silicon alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
    • 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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • 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
    • C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising

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Abstract

The invention provides an aluminum-silicon alloy with high wear resistance and high strength and toughness and a preparation method thereof, wherein the aluminum-silicon alloy comprises the following components in percentage by mass: 15-20% of Si, 4.0-5.5% of Cu, 0.5-1.5% of Mg, 0.6-2.0% of Fe, 0.3-1.0% of Mn and 0.3-1.5% of rare earth elements, wherein the rare earth elements are selected from Ce and/or La, and the balance is aluminum and unavoidable impurities. The preparation method comprises the steps of placing a melt obtained by smelting raw materials on a permanent magnet stirring device, and carrying out permanent magnet stirring treatment on the melt until the melt is completely solidified, thus obtaining the aluminum-silicon alloy. According to the invention, the proportion of elements in the alloy is regulated, a rare earth metamorphic coupling unique magnetic field stirring technology is adopted, the solidification structure of the alloy is regulated, and the problem that precipitated phases (silicon phase and iron phase) in the aluminum-silicon alloy are coarse is solved, so that the aluminum-silicon alloy with high wear resistance and high strength and toughness is obtained. The method provided by the invention has the advantages of simple process, convenient operation, safety, reliability, low cost and wide application prospect.

Description

High-wear-resistance high-strength and high-toughness aluminum-silicon alloy and preparation method thereof
Technical Field
The invention relates to an aluminum-silicon alloy with high wear resistance and high strength and toughness and a preparation method thereof, belonging to the technical field of aluminum alloy preparation.
Background
Since the twenty-first century, the number of motor vehicles in China has increased significantly, and the transportation industry has become the second most energy consumption department next to the industrial department, and is also the main contribution department of greenhouse gas emission and air pollutants. Research shows that 60% of the fuel consumption of the automobile is derived from dead weight, and the reduction of the dead weight of the automobile is an important way for reducing energy consumption and pollution emission.
The aluminum alloy is used as a typical light metal material, is widely applied to the automobile industry, achieves the purpose of aluminum strip steel, and greatly reduces the dead weight of the automobile. However, the application of aluminum alloys is currently limited to stationary parts such as car bodies, cylinder blocks, cylinder heads, etc. For moving parts, the requirements on mechanical properties are high, such as high strength, high wear resistance, excellent plasticity, fracture toughness and the like, and the materials commonly used at present are steel materials.
The aluminum-silicon alloy has the characteristics of light weight, good electric conduction and thermal conductivity, low thermal expansion coefficient of Si, high hardness and high wear resistance of an Al matrix, and is expected to meet the requirements, so that the aluminum strip steel is realized. The prior Chinese patent CN109338180A is a high-strength and high-toughness cast aluminum-silicon alloy, and a preparation method and application thereof, wherein the fine solidification structure is obtained by optimizing the content of Si and Mg elements and adding modifier such as Sr, ti, re and the like, and the plasticity and toughness of the alloy are improved by carrying out solution treatment and aging treatment twice. The method has the silicon content of 7-8%, the Mg content of 0.4-05%, and the fine solidification structure obtained by modification and heat treatment has higher strength, the process is more complex, and the lower content of Si and Mg can limit the strength and the wear resistance of the alloy. There is a Chinese patent CN108893662B, a high wear-resistant regenerated aluminum alloy, a preparation method and application thereof, and the wear resistance of the alloy is greatly improved by utilizing the iron element existing in the regenerated aluminum and assisting with a composite modification technology. However, the inclusion of too high iron undoubtedly increases the difficulty of morphology control of the iron-rich phases in the aluminum-silicon alloy, while the coarse, needle-like iron-rich phases can greatly destroy the mechanical properties of the alloy.
Disclosure of Invention
Aiming at the problems existing in the prior art, the invention aims to provide an aluminum-silicon alloy with high wear resistance and high strength and toughness and a preparation method thereof. According to the invention, by adding a certain proportion of Cu, mg, mn, fe and other alloy elements into the high-silicon-content aluminum alloy and assisting in rare earth modification and permanent magnet stirring technology, the solidification structure of the alloy is effectively controlled.
The invention relates to an aluminum-silicon alloy with high wear resistance and high strength and toughness, which comprises the following components in percentage by mass: 15-20% of Si, 4.0-5.5% of Cu, 0.5-1.5% of Mg, 0.6-2.0% of Fe, 0.3-1.0% of Mn and 0.3-1.5% of rare earth elements, wherein the rare earth elements are selected from Ce and/or La, and the balance is aluminum and unavoidable impurities.
In a preferred embodiment, the impurity content is less than 0.2%.
The aluminum-silicon alloy adopts high silicon content, the alloy silicon content is more than 15%, a high-hardness silicon phase is formed as a reinforcing phase, the wear resistance of the material can be obviously improved, and meanwhile, alloy elements are added: cu, mg, mn, fe Cu and Mg are dissolved in an aluminum matrix to improve the strength of the matrix, and an aluminum copper phase, an aluminum copper magnesium silicon phase and an iron-rich phase are formed on the one hand and uniformly distributed in the matrix to realize precipitation phase strengthening, a small amount of rare earth elements are introduced, and a heterogeneous nucleation phase such as Al is introduced 3 La、Al 4 Ce, etc.
In a preferred embodiment, the aluminum-silicon alloy has a mass ratio of Mn to Fe of 0.4 to 0.8.
The inventors found that the mass ratio of Mn to Fe is controlled to be 0.4 to 0.8, and that the toughness of the final material can be optimized because Mn is an effective neutralizing element of Fe and has a good deterioration effect on the coarse beta-Fe phase. However, if the mass ratio of Mn/Fe is too low, the deterioration effect of Mn is weak, a beta-Fe phase is easy to form, and the matrix is easy to tear to reduce the toughness of the alloy in a coarse needle shape or a space sheet shape. If the mass ratio of Mn/Fe is too high, the Fe phase is well controlled, but the surplus Mn element is easy to segregate, so that a brittle Mn-Al compound is formed, and the alloy plasticity is seriously reduced.
In a preferred embodiment, the mass ratio of Cu to Mg in the aluminum-silicon alloy is 6 to 10.
The inventor discovers that the mass ratio of Cu to Mg is controlled to be 6-10, the strengthening effect on a matrix is optimal finally, and the Cu and Mg elements are all aluminum-silicon alloy weightsThe required alloying elements can be dissolved into the aluminum alloy matrix to form a second phase, so as to strengthen the matrix. Cu element is dissolved into the alloy matrix, so that the solid solubility of Mg element is reduced, and more Mg is generated 2 Si, improves the mechanical property of the alloy. If the Cu/Mg mass ratio is too low, mg element becomes more solid-dissolved into the matrix, and it is difficult to form a large amount of Mg 2 Si, while too high a content of Mg element forms Al 6 CuMg 4 The strengthening effect of the phase is weaker than that of Al 2 Cu，Al 2 A CuMg phase; if the Cu/Mg mass ratio is too high, the main strengthening phase is Al 2 Cu, the high content of Cu can reduce the corrosiveness of the alloy, and the low content of Mg has no obvious strengthening effect.
The invention relates to a preparation method of an aluminum-silicon alloy with high wear resistance and high strength and toughness, which comprises the following steps: and (3) preparing an aluminum source, a silicon source, a magnesium source, a copper source, a manganese source and an iron source according to a designed proportion, uniformly mixing to obtain a mixture, smelting to obtain a melt A, then cooling, adding a rare earth source, preserving heat to obtain a melt B, placing the melt B on a permanent magnet stirring device, and carrying out permanent magnet stirring treatment on the melt B until the melt B is completely solidified, thus obtaining the aluminum-silicon alloy.
In a preferred scheme, the aluminum source is selected from at least one of pure aluminum blocks, regenerated aluminum and aluminum alloy blocks, and the aluminum alloy blocks are alloy blocks formed by at least one of aluminum and Si, cu, mg, fe, mn. Such as high-iron aluminum silicon alloy, secondary aluminum, aluminum copper alloy, aluminum magnesium alloy block and the like.
Preferably, the silicon source is selected from at least one of pure silicon blocks and silicon alloy blocks, and the silicon alloy blocks are alloy blocks composed of at least one of silicon and Al, cu, mg, fe, mn. Such as high-iron aluminum silicon alloy, silicon iron alloy, etc.
Preferably, the copper source is selected from at least one of electrolytic copper and copper alloy ingots, and the copper alloy block is an alloy block formed by at least one of copper and Si, mg, al, fe, mn. Such as aluminum copper alloy
In a preferred scheme, the magnesium source is selected from at least one of pure magnesium ingot and magnesium alloy ingot, and the magnesium alloy block is an alloy block composed of at least one of magnesium and Si, cu, al, fe, mn.
In a preferred scheme, the manganese source is selected from at least one of pure manganese blocks and manganese alloy blocks, and the manganese alloy blocks are alloy blocks composed of at least one of manganese and Si, cu, al, fe, mg.
In a preferred scheme, the iron source is selected from at least one of pure iron blocks and iron alloy blocks, and the iron alloy blocks are alloy blocks composed of at least one of iron and Si, cu, al, mn, mg. Such as high-iron aluminum silicon alloy, silicon iron alloy, etc.
Preferably, the smelting temperature is 900-950 ℃.
Further preferably, the smelting process is as follows: heating to 900-950 ℃, and preserving heat for 15-25 min after the mixture is completely melted to obtain a melt A.
Preferably, the rare earth source is at least one of pure lanthanum, pure cerium, aluminum-lanthanum alloy, aluminum-cerium alloy and lanthanum-cerium alloy.
In a preferred scheme, the temperature is reduced to 750-800 ℃, a rare earth source is added, and the temperature is kept for 10-20 min to obtain a melt B.
In the actual operation process, small blocks of aluminum source, silicon source, magnesium source, copper source, manganese source and iron source are adopted, and are evenly mixed and then are placed in Al 2 O 3 Smelting in a vacuum furnace in a crucible to obtain a melt A, cooling, adding a rare earth source, preserving heat to obtain a melt B, and taking out Al containing the melt B in the vacuum furnace 2 O 3 The crucible is arranged in the permanent magnet stirring device, and alternating permanent magnet stirring treatment is applied to the melt.
In a preferred scheme, the permanent magnet stirring treatment process comprises the following steps: firstly, the melt B rotates forward for 1-2 min and then rotates reversely for 1-2 min, so that the melt B reciprocates; in the rotating process, the melt B is made to perform lifting motion every 1-2 min.
In the permanent magnet stirring process of the scheme, the movement mode of the magnetic field at the melt is continuously regulated by adopting the means of direction changing and position changing, so that lorentz forces in different directions and sizes are excited, heat transfer and mass transfer of the melt can be effectively realized, aggregation growth of precipitated phases in the melt is avoided, the solidification structure of the alloy is further refined, and the wear resistance and toughness of the alloy are enhanced. The permanent magnet stirring process in the scheme realizes multi-level multi-element control of the magnetic field through the change of the rotating speed of the magnet and the position change treatment of the melt, and has obvious stirring effect and simple control means. Compared with the traditional single magnetic field movement mode, the melt moves along with the magnetic field in a single direction, such as horizontal rotation movement, the up-and-down homogenization of the melt is realized by means of turbulence formed by high rotation speed, the effect is limited, the same speed and the same direction movement are kept for a long time, and the precipitated phase in the melt is in a relatively static state along with the melt or weakened in relative movement, so that the stirring effect is weakened. Of course, even if the steering rotation is adopted, if the rotation time in the same direction is too short, the high-speed rotation time of the melt is reduced in consideration of the mechanical acceleration time and the deceleration time, so that the stirring effect is weakened, and the service life of the equipment is influenced by frequent steering.
In the present invention, the forward rotation and the reverse rotation are only opposite directions, and the forward rotation and the reverse rotation only represent direction changes. But is not specifically limited in direction.
In a preferred scheme, the magnetic induction intensity is 500-3000 Gs, preferably 1500-3000 Gs, in the process of the permanent magnet stirring treatment.
In a preferred scheme, the rotating speed of the magnet is 80-300 rpm, preferably 150-250 rpm, in the process of the permanent magnet stirring treatment.
Principle and advantages
The aluminum-silicon alloy provided by the invention has high wear resistance and high strength and toughness, and is characterized in that: 1. the alloy silicon content is more than 15%, and the high-hardness silicon phase is used as a reinforcing phase, so that the wear resistance of the material can be remarkably improved. 2: and adding Cu, mg, mn, fe and other alloy elements, controlling the proportion of the alloy elements, on one hand, cu and Mg can be dissolved in an aluminum matrix to improve the strength of the matrix, and on the other hand, an aluminum copper phase, an aluminum copper magnesium silicon phase and an iron-rich phase are formed and uniformly distributed in the matrix to realize precipitation phase strengthening. 3: adopts rare earth modification treatment, on one hand introduces heterogeneous nuclear phase such as Al 3 La、Al 4 On one hand, the refined aluminum matrix such as Ce can be enriched near a silicon phase and an iron-rich phase, and the precipitated phases such as silicon are refined by changing the modification of the structure supercooling, the precipitated phase growth mode and the like. 4: by a unique permanent-magnet stirring treatment, through a constantly changing magnetic fieldThe non-single moving magnetic field excites the Lorentz force in each direction in the melt, effectively avoids the 'relative static' state caused by the inertial movement of the melt, and greatly improves the heat transfer and mass transfer in the melt; in addition, the lorentz force in each direction limits the single-direction growth of the precipitated phase, effectively avoids the aggregation of the alloy precipitated phase, further refines the solidification structure of the alloy and strengthens the wear resistance and toughness of the alloy.
Compared with the prior art, the invention has the beneficial effects that: the element proportion in the aluminum-silicon alloy is reasonably regulated and controlled, rare earth modification treatment is adopted, and a unique permanent magnet stirring process is combined, so that the refining of the precipitated phase of the high-silicon aluminum-silicon alloy is effectively realized, and the wear resistance and the toughness of the alloy are greatly improved.
Detailed Description
Example 1:
small aluminum blocks, silicon blocks, magnesium ingots, electrolytic copper, manganese blocks, pure iron and other intermediate alloys (18 percent of Si,4.5 percent of Cu,0.8 percent of Mg,0.8 percent of Fe,0.4 percent of Mn) which are weighed according to the component ratio are alternately arranged in Al 2 O 3 The crucible is vertically placed in a tube furnace. Starting the tube furnace, heating to 900 ℃, and preserving heat for 20min after the tube furnace is completely melted; regulating the temperature of the tube furnace to 800 ℃, adding 0.6% of rare earth Ce into the alloy melt, and preserving the heat for 15min. Taking out the crucible, placing the crucible in a permanent magnet stirring device, and applying alternating permanent magnet stirring treatment to the melt, wherein the crucible rotates forwards for 1min and then rotates reversely for 1min so as to reciprocate; in the rotating process, lifting movement is carried out through the telescopic rod every 1min, and the stirring speed of the magnet is 200rpm. And taking out the cast ingot after the melt is solidified. The test shows that the microhardness of the matrix reaches 138.6Hv, the friction coefficient is 0.4625, the tensile strength is 275MPa, and the elongation is 12%.
Example 2:
small aluminum blocks, silicon blocks, magnesium ingots, electrolytic copper, manganese blocks, pure iron and other intermediate alloys ((18% Si,4.5% Cu,0.8% Mg,0.8% Fe,0.4% Mn)) are weighed according to the component ratio and alternately placed in Al 2 O 3 The crucible is vertically placed in a tube furnace. Starting the tube furnace, heating to 900 ℃, and preserving heat for 20min after the tube furnace is completely melted; regulating the temperature of the tube furnace to 800 ℃, adding 0.6% of rare earth Ce into the alloy melt, and preserving the heat for 15min. Taking out the crucible and placing the crucible inThe permanent magnet stirring device applies alternating permanent magnet stirring treatment to the melt, and the melt is rotated forward for 1min and then rotated reversely for 1min so as to reciprocate; in the rotation process, lifting movement is carried out through the telescopic rod every 1min, and the stirring speed of the magnet is 120rpm. And taking out the cast ingot after the melt is solidified. The test shows that the microhardness of the matrix reaches 115.3Hv, the friction coefficient is 0.4862, the tensile strength is 245MPa, and the elongation is 12%.
Example 3:
small aluminum blocks, silicon blocks, magnesium ingots, electrolytic copper, manganese blocks, pure iron and other intermediate alloys (16 percent of Si,4.8 percent of Cu,1 percent of Mg,0.6 percent of Fe and 0.3 percent of Mn) which are weighed according to the component ratio are alternately arranged in Al 2 O 3 The crucible is vertically placed in a tube furnace. Starting the tube furnace, heating to 900 ℃, and preserving heat for 20min after the tube furnace is completely melted; regulating the temperature of the tube furnace to 800 ℃, adding 0.6% of rare earth Ce into the alloy melt, and preserving the heat for 15min. Taking out the crucible, placing the crucible in a permanent magnet stirring device, and applying alternating permanent magnet stirring treatment to the melt, wherein the crucible rotates forwards for 1min and then rotates reversely for 1min so as to reciprocate; in the rotating process, lifting movement is carried out through the telescopic rod every 2min, and the stirring speed of the magnet is 200rpm. And taking out the cast ingot after the melt is solidified. The test shows that the microhardness of the matrix reaches 123.9Hv, the friction coefficient is 0.4826, the tensile strength is 255MPa, and the elongation is 10%.
Example 4:
small aluminum blocks, silicon blocks, magnesium ingots, electrolytic copper, manganese blocks, pure iron and other intermediate alloys (18 percent of Si,4.5 percent of Cu,0.8 percent of Mg,0.8 percent of Fe,0.4 percent of Mn) which are weighed according to the component ratio are alternately arranged in Al 2 O 3 The crucible is vertically placed in a tube furnace. Starting the tube furnace, heating to 900 ℃, and preserving heat for 20min after the tube furnace is completely melted; regulating the temperature of the tube furnace to 800 ℃, adding 0.3% of rare earth Ce into the alloy melt, and preserving the heat for 15min. Taking out the crucible, placing the crucible in a permanent magnet stirring device, and applying alternating permanent magnet stirring treatment to the melt, wherein the crucible rotates forwards for 1min and then rotates reversely for 1min so as to reciprocate; in the rotating process, lifting movement is carried out through the telescopic rod every 1min, and the stirring speed of the magnet is 200rpm. And taking out the cast ingot after the melt is solidified. The test shows that the microhardness of the matrix reaches 127.4Hv, the friction coefficient is 0.4695,the tensile strength was 260MPa and the elongation was 10%.
Example 5:
small aluminum blocks, silicon blocks, magnesium ingots, electrolytic copper, manganese blocks, pure iron and other intermediate alloys (18 percent of Si,4.5 percent of Cu,0.8 percent of Mg,0.8 percent of Fe,0.4 percent of Mn) which are weighed according to the component ratio are alternately arranged in Al 2 O 3 The crucible is vertically placed in a tube furnace. Starting the tube furnace, heating to 900 ℃, and preserving heat for 20min after the tube furnace is completely melted; regulating the temperature of the tube furnace to 800 ℃, adding 1.5% of rare earth Ce into the alloy melt, and preserving the heat for 15min. Taking out the crucible, placing the crucible in a permanent magnet stirring device, and applying alternating permanent magnet stirring treatment to the melt, wherein the crucible rotates forwards for 1min and then rotates reversely for 1min so as to reciprocate; in the rotating process, lifting movement is carried out through the telescopic rod every 1min, and the stirring speed of the magnet is 200rpm. And taking out the cast ingot after the melt is solidified. The test shows that the microhardness of the matrix reaches 125.8Hv, the friction coefficient is 0.4685, the tensile strength is 245MPa, and the elongation is 9%.
Example 6:
small aluminum blocks, silicon blocks, magnesium ingots, electrolytic copper, manganese blocks, pure iron and other intermediate alloys (18 percent of Si,4.5 percent of Cu,0.8 percent of Mg,0.8 percent of Fe,0.4 percent of Mn) which are weighed according to the component ratio are alternately arranged in Al 2 O 3 The crucible is vertically placed in a tube furnace. Starting the tube furnace, heating to 900 ℃, and preserving heat for 20min after the tube furnace is completely melted; regulating the temperature of the tube furnace to 800 ℃, adding 0.3% rare earth La into the alloy melt, and preserving the heat for 15min. Taking out the crucible, placing the crucible in a permanent magnet stirring device, and applying alternating permanent magnet stirring treatment to the melt, wherein the crucible rotates forwards for 1min and then rotates reversely for 1min so as to reciprocate; in the rotating process, lifting movement is carried out through the telescopic rod every 1min, and the stirring speed of the magnet is 200rpm. And taking out the cast ingot after the melt is solidified. The test shows that the microhardness of the matrix reaches 135.9Hv, the friction coefficient is 0.4605, the tensile strength is 270MPa, and the elongation is 12%.
Comparative example 1:
other experimental conditions were exactly the same as in example 1, except that the iron content was increased to 2% and the manganese content was still 0.4%. The test shows that the microhardness of the matrix reaches 142.7Hv, the friction coefficient is 0.4831, the tensile strength is 175MPa, and the elongation is 7%.
As can be seen from the comparison of the data of comparative example 1 and example 1, the iron element content is too high, the Mn/Fe ratio is too low, the rare earth deterioration and the refinement of the iron-containing phase by the permanent magnet stirring technology are weak, coarse iron-containing phases are generated, the tensile property of the alloy is deteriorated while the matrix hardness is strengthened, and the comprehensive performance is weakened.
Comparative example 2:
other experimental conditions were exactly the same as in example 1, except that no rare earth element was added and no permanent magnet stirring was applied. The test shows that the microhardness of the matrix reaches 87.5Hv, the friction coefficient is 0.5481, the tensile strength is 155MPa, and the elongation is 6%.
Comparative example 3:
other experimental conditions were exactly the same as in example 1, except that no rare earth element was added. The test shows that the microhardness of the matrix reaches 101.4Hv, the friction coefficient is 0.5028, the tensile strength is 205MPa, and the elongation is 8%.
Comparative example 4:
other experimental conditions were exactly the same as in example 1, except that the rare earth was 0.1% ce. The test shows that the microhardness of the matrix reaches 103.6Hv, the friction coefficient is 0.5108, the tensile strength is 205MPa, and the elongation is 8%. As can be seen from comparative example 4, when the rare earth content is low, the rare earth deterioration effect is weak, and the alloy strengthening effect is correspondingly weak.
Comparative example 5:
other experimental conditions were exactly the same as in example 6, except that the rare earth was 3.0% ce. The test shows that the microhardness of the matrix reaches 102.2Hv, the friction coefficient is 0.5084, the tensile strength is 185MPa, and the elongation is 6%. As can be seen from comparative example 5, when the rare earth content is high, the rare earth aggregates with each other and reacts with the alloy element to generate brittle or long-strip intermetallic compounds, which correspondingly lower the alloy performance to some extent.
As can be seen from the comparison of the data of comparative examples 2 to 5 and example 1, the rare earth addition significantly affects the deterioration effect of the alloy, and when the rare earth addition is too low or 0, the deterioration effect of the rare earth is not significantly insufficient; when the addition amount of rare earth is too high, coarse rare earth compounds appear in the alloy, and tear the matrix to play a role in reaction.
Comparative example 6:
other experimental conditions were exactly the same as in example 1, except that no permanent magnet stirring was applied. The test shows that the microhardness of the matrix reaches 98.3Hv, the friction coefficient is 0.5131, the tensile strength is 185MPa, and the elongation is 7%.
Comparative example 7:
other experimental conditions were exactly the same as in example 1, except that the permanent magnet stirring speed was 30rpm. The test shows that the microhardness of the matrix reaches 99.4Hv, the friction coefficient is 0.5181, the tensile strength is 190MPa, and the elongation is 6%.
As can be seen from comparative example 7, the permanent magnet stirring process parameters also have a certain influence on the performance of the cast ingot, when the permanent magnet stirring speed is smaller, the excited Lorentz force is smaller, the formed vortex is smaller, the stirring effect is correspondingly weakened, the growth restriction on the precipitated phase is weaker, and the strengthening effect is poor.
Comparative example 8:
other experimental conditions were exactly the same as in example 1, except that the speed direction was not changed during the permanent magnet stirring. The test shows that the microhardness of the matrix reaches 99.8Hv, the friction coefficient is 0.5041, the tensile strength is 215MPa, and the elongation is 8%.
Comparative example 9:
other experimental conditions were exactly the same as in example 1, except that no lifting bar was moved during the application of the permanent magnet stirring. The test shows that the microhardness of the matrix reaches 115.4Hv, the friction coefficient is 0.4931, the tensile strength is 225MPa, and the elongation is 8%.
Comparative example 10:
other experimental conditions were exactly the same as in example 1, except that in the application of permanent magnetic stirring, the lifting movement of the lifting rod was once every 4 min. The test shows that the microhardness of the matrix reaches 116.8Hv, the friction coefficient is 0.4923, the tensile strength is 225MPa, and the elongation is 8%. As can be seen from comparative example 10, when the moving frequency of the telescopic rod is low, the moving magnetic field is relatively slow, and due to the rapid movement in the horizontal direction, precipitated phases in the melt are gathered to a certain extent, so that the structure is coarsened, and the alloy performance is correspondingly reduced.
As can be seen from comparative examples 6-10 and example 1, the stirring effect is reduced at a lower magnetic field rotation speed, a lower lifting frequency and a constant magnetic field rotation speed direction in the magnetic field control process, and the alloy performance cannot be optimized well.
As can be seen from the comparison of the data in comparative examples 2-10 and example 1, the alloy can be strengthened to a certain extent by utilizing the rare earth modification and the permanent magnet stirring technology, the permanent magnet stirring technology is superior to the rare earth modification, and the combined moving magnetic field stirring technology effect is better; the permanent magnet stirring coupling rare earth modification technology can obviously improve the microhardness, tensile strength and elongation of the matrix, reduce the friction coefficient of the alloy and obviously improve the wear resistance and the toughness of the alloy.
The method is feasible by the examples and the comparison examples, and has certain practical value and industrial application potential. The above embodiments are provided for illustrating the present invention and not for limiting the present invention, and various changes and modifications may be made by one skilled in the relevant art without departing from the spirit and scope of the present invention, and thus all equivalent technical solutions should be defined by the claims.

Claims (5)

1. A preparation method of an aluminum-silicon alloy with high wear resistance and high strength and toughness is characterized by comprising the following steps: the method comprises the following steps: preparing an aluminum source, a silicon source, a magnesium source, a copper source, a manganese source and an iron source according to a design proportion, uniformly mixing to obtain a mixture, smelting to obtain a melt A, then cooling, adding a rare earth source, preserving heat to obtain a melt B, placing the melt B on a permanent magnet stirring device, and carrying out permanent magnet stirring treatment on the melt B until the melt B is completely solidified to obtain the aluminum-silicon alloy;
the process of the permanent magnet stirring treatment comprises the following steps: firstly, the melt B rotates forward for 1-2 min and then rotates reversely for 1-2 min, so that the melt B reciprocates; in the rotating process, the melt B is lifted and lowered once every 1-2 min;
in the process of the permanent magnet stirring treatment, the magnetic induction intensity is 500-3000 Gs;
in the process of the permanent magnet stirring treatment, the rotating speed of the magnet is 80-300 rpm;
the aluminum-silicon alloy comprises the following components in percentage by mass: 15 to 20 percent of Si, 4.0 to 5.5 percent of Cu, 0.5 to 1.5 percent of Mg,0.6 to 2.0 percent of Fe,0.3 to 1.0 percent of Mn and 0.3 to 1.5 percent of rare earth elements, wherein the rare earth elements are selected from Ce and/or La, and the balance is aluminum and unavoidable impurities
In the aluminum-silicon alloy, the mass ratio of Mn to Fe is 0.4-0.8.
2. The method for producing a high-wear-resistance high-toughness aluminum-silicon alloy according to claim 1, wherein: the smelting temperature is 900-950 ℃.
3. The method for producing a high-wear-resistance high-toughness aluminum-silicon alloy according to claim 1, wherein: the smelting process comprises the following steps: heating to 900-950 ℃, and preserving heat for 15-25 min after the mixture is completely melted to obtain a melt A.
4. The method for producing a high-wear-resistance high-toughness aluminum-silicon alloy according to claim 1, wherein: cooling to 750-800 ℃, adding rare earth source, and preserving heat for 10-20 min to obtain melt B.
5. The method for producing a high-wear-resistance high-toughness aluminum-silicon alloy according to claim 1, wherein: in the aluminum-silicon alloy, the mass ratio of Cu to Mg is 6-10.
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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5122208A (en) * 1991-07-22 1992-06-16 General Motors Corporation Hypo-eutectic aluminum-silicon alloy having tin and bismuth additions
US5762728A (en) * 1994-03-16 1998-06-09 Nippon Light Metal Company Ltd. Wear-resistant cast aluminum alloy process of producing the same
CN1289856A (en) * 2000-09-29 2001-04-04 江汉大学 Compression casting of Al alloy with Al-Si-Cu rare earth
CN1345983A (en) * 2000-09-27 2002-04-24 北京科技大学 Method for spraying and depositing high silicon aluminium alloy
CN104975196A (en) * 2015-06-25 2015-10-14 江西雄鹰铝业股份有限公司 Manufacturing process of regenerated high-silicon aluminum alloy ingots
CN110144501A (en) * 2019-05-15 2019-08-20 苏州仓松金属制品有限公司 A kind of long-acting rotten silumin and its modification process
CN112210696A (en) * 2020-10-09 2021-01-12 东莞理工学院 High-strength and high-wear-resistance Al-Si alloy and preparation method and application thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5122208A (en) * 1991-07-22 1992-06-16 General Motors Corporation Hypo-eutectic aluminum-silicon alloy having tin and bismuth additions
US5762728A (en) * 1994-03-16 1998-06-09 Nippon Light Metal Company Ltd. Wear-resistant cast aluminum alloy process of producing the same
CN1345983A (en) * 2000-09-27 2002-04-24 北京科技大学 Method for spraying and depositing high silicon aluminium alloy
CN1289856A (en) * 2000-09-29 2001-04-04 江汉大学 Compression casting of Al alloy with Al-Si-Cu rare earth
CN104975196A (en) * 2015-06-25 2015-10-14 江西雄鹰铝业股份有限公司 Manufacturing process of regenerated high-silicon aluminum alloy ingots
CN110144501A (en) * 2019-05-15 2019-08-20 苏州仓松金属制品有限公司 A kind of long-acting rotten silumin and its modification process
CN112210696A (en) * 2020-10-09 2021-01-12 东莞理工学院 High-strength and high-wear-resistance Al-Si alloy and preparation method and application thereof

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
铝合金熔炼中永磁搅拌的应用效果;王刚等;《轻合金加工技术》;20111231;第39卷(第6期);第25-30页 *

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