CN115141960A - High-strength and high-toughness cast aluminum alloy with low Si content and preparation method thereof - Google Patents
High-strength and high-toughness cast aluminum alloy with low Si content and preparation method thereof Download PDFInfo
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Abstract
The invention provides a high-strength and high-toughness low-Si-content cast aluminum alloy and a preparation method thereof, wherein the aluminum-silicon alloy comprises the following components in percentage by mass: si: 4.5-7%, mg:0.4 to 0.7%, cu:0.2 to 0.5%, RE:0.1 to 0.4%, cr: 0.15-0.35%, fe is less than or equal to 0.15%, ti:0.01 to 0.05 percent, sr:0.001 to 0.004%, B: 0.001-0.004%, the rare earth element is selected from Ce and/or La, and the rest is aluminum and inevitable impurities. According to the preparation method, the melt obtained by smelting the raw materials is placed on a permanent magnetic stirring device, and the casting is carried out after the permanent magnetic stirring treatment is carried out on the melt, so that the cast aluminum alloy is obtained. According to the invention, the solidification structure of the alloy is regulated and controlled by adjusting the element proportion in the alloy and adopting a multi-element modification coupling unique magnetic field stirring technology, so that the problem of coarse precipitated phase in the aluminum-silicon alloy is solved, and the cast aluminum alloy with high strength and toughness Si content is obtained. The method provided by the invention has the advantages of simple process, convenience in operation, safety, reliability, low cost and wide application prospect.
Description
Technical Field
The invention relates to a high-strength and high-toughness cast aluminum alloy with low Si content and a preparation method thereof, belonging to the technical field of aluminum alloy preparation.
Background
Research shows that 60% of automobile fuel consumption is caused by dead weight, and reducing the dead weight of the automobile is an important way for reducing energy consumption and pollutant emission. Lightweight, high safety and greenness are important directions for the development of the automobile industry. With the continuous and rapid development of new energy automobile industry in China, the demands of various domestic large passenger car manufacturers on light-weight high-strength new materials are gradually increased.
The aluminum-silicon alloy has the advantages of small density, high strength, good heat conductivity, small thermal expansion coefficient and the like, can reduce weight, reduce abrasion, reduce consumption of lubricating oil and piston clearance, and meets the condition of replacing the traditional steel materials. However, at present, the application of aluminum alloys is limited to stationary parts such as vehicle bodies, cylinder blocks, cylinder heads, etc. For moving parts or important stressed structural parts, the requirements on mechanical properties such as strength, plasticity, fracture toughness and the like are high, and the materials commonly used at present are steel materials.
When the content of Si in the aluminum-silicon alloy is too high, si phase is precipitated first in the solidification process, and coarse primary Si phase is easy to appear in the alloy, so that the product performance is deteriorated. Accordingly, the aluminum-silicon alloy with high silicon content has excellent wear resistance and can be used for parts such as automobile cylinders, pistons and the like. When the content of Si in the aluminum-silicon alloy is lower than the eutectic point, si is usually precipitated as a eutectic Si phase, the alloy has small linear shrinkage rate, low hot cracking tendency and good air tightness, and can be used for producing medium and high-strength automobile parts such as automobile hubs, engine frames, steering knuckles and the like, and automobile gearbox shells, shock absorbers, shock absorber covers and the like. However, in untreated aluminum-silicon alloy, the eutectic Si phase is in a slender needle shape, which greatly harms the toughness of the alloy and is not beneficial to the production and utilization of the alloy.
In the traditional Chinese patent CN112143945A, the plasticity and the toughness of the Al-Si-Mg alloy are improved by adding the composite rare earth elements and a plurality of refiners, strengthening solid solution treatment and multistage aging treatment. The method obtains fine solidification structure and high strength through modification and multiple heat treatments, and the process is complex. In the traditional Chinese patent CN103469028A, a rare earth element praseodymium alloyed aluminum-silicon alloy and a preparation method thereof are adopted, modified aluminum-silicon alloy is treated by combining single rare earth with ultrasonic, the silicon content is controlled to be 9.0-12.0%, heat is preserved for 31-180 min before melt casting, the heat preservation time is too long, and the energy consumption is higher. In the existing Chinese patent CN108220703A, the performance of cast aluminum-silicon alloy is modified by the synergy of graphene and rare earth, but the cost of graphene is extremely high, which is not beneficial to industrial implementation.
Disclosure of Invention
Aiming at the problems in the prior art, the invention aims to provide a high-strength and high-toughness cast aluminum alloy with low Si content and a preparation method thereof. According to the invention, the low-content Si is added into the aluminum alloy, the elements of Mg, cu, cr and Fe in a certain proportion and the trace elements of Ti, sr and B are added, and the rare earth modification and permanent magnet stirring process is assisted, so that the alloy solidification structure is effectively controlled.
The invention relates to a high-strength and high-toughness cast aluminum alloy with low Si content, which comprises the following components in percentage by mass: si: 4.5-7%, mg:0.4 to 0.7%, cu:0.2 to 0.5%, RE:0.1 to 0.4%, cr: 0.15-0.35%, fe is less than or equal to 0.15%, ti:0.01 to 0.05 percent, sr:0.001 to 0.004%, B:0.001 to 0.004%, wherein the RE (rare earth element) is Ce and/or La, and the balance is aluminum and unavoidable impurities.
Preferably, the impurity content is less than 0.2%.
According to the cast aluminum alloy, the alloy elements of Mg, cu, cr and Fe are added, so that on one hand, mg, cu and Cr can be dissolved in an aluminum matrix in a solid mode to improve the strength of the matrix, on the other hand, a magnesium-silicon phase, an aluminum-copper-magnesium-silicon phase and an iron-rich phase are formed and are uniformly distributed in the matrix, and precipitated phase strengthening is realized. In addition, rare earth elements and trace amounts of Ti, sr and B elements are added to introduce heterogeneous nucleation phases such as Al 3 La、Al 4 Ce、Al 3 Ti、Ti 2 B, thinning the aluminum matrix; the aggregation of Sr and Re elements at the Si phase can limit the growth of the Si phase, refine the Si phase and improve the toughness of the alloy, and finally, the cast aluminum alloy has excellent toughness under the coordination of the elements.
In a preferable scheme, the mass ratio of Cr to Fe in the cast aluminum alloy is 1-3.
The inventors have found that controlling the mass ratio of Cr to Fe to be 1 to 3 optimizes the toughness of the final material, since Cr acts as an effective neutralizing element for Fe and has a good modifying effect on the coarse β -Fe phase. However, if the mass ratio of Cr/Fe is too low, the Mn modification effect is weak, a beta-Fe phase is easily formed and is in a thick needle shape or a space sheet shape, and the matrix is easy to tear, so that the toughness of the alloy is reduced. If the Cr/Fe mass ratio is too high, the Fe phase is well controlled, but the surplus Cr element increases the quenching sensitivity and the preparation cost of the alloy.
Preferably, in the cast aluminum alloy, the mass ratio of Ti to B is 5 to 10.
The inventor finds that the mass ratio of Ti to B is controlled to be 5-10, so that the toughness of the final material is optimal, the Ti element can effectively refine primary aluminum, and the refining effect of Ti can be enhanced by adding a proper amount of B element; if the amount of B element is too large, the Sr deterioration is deteriorated.
Preferably, the cast aluminum alloy has a mass ratio of Sr to B of 1 to 2.
The inventor finds that the Sr and B mass ratio is controlled to be 1-2, the strengthening effect on the matrix is optimal finally, and the addition of Sr can effectively refine SiThe addition of phase B enables the refinement of the matrix. However, if the Sr/B mass ratio is too low, B reacts with Sr to produce Sr 6 And B, the modification effect of Sr is reduced. If the Sr/B mass ratio is too high, the B content is small, and the synergistic effect with Ti is weakened.
In a preferred scheme, the cast aluminum alloy comprises the following components in percentage by mass: si: 6-8%, mg:0.5 to 0.7%, cu:0.3 to 0.5%, RE:0.2 to 0.3%, cr:0.15 to 0.30%, fe:0.1 to 0.15%, ti:0.02 to 0.04 percent, sr:0.003 to 0.004%, B: 0.003-0.004%, RE is Ce and/or La, and the rest is aluminum and inevitable impurities.
Preferably, RE is selected from La. When RE is selected from La, the alloy has better alloy performance.
The invention relates to a preparation method of a cast aluminum alloy with high strength and toughness Si content, which comprises the following steps: preparing an aluminum source, a silicon source, a magnesium source, a copper source, an iron source and a chromium source according to a designed proportion, uniformly mixing to obtain a mixture, introducing argon to discharge air, smelting to obtain a melt A, starting a permanent magnetic stirring device, and applying permanent magnetic stirring treatment to the melt; and then adding a rare earth source, a titanium source, a strontium source and a boron source, preserving heat to obtain a melt B, cooling, stopping applying permanent magnetic stirring treatment, stopping introducing argon, and casting to obtain the cast aluminum alloy.
In the preparation process, by controlling the feeding sequence of elements in the smelting process and applying permanent magnetic stirring in the smelting process, the alloy casting blank with uniform and refined structure is finally obtained, precipitated phases are uniformly dispersed and distributed in a matrix, and the obtained cast aluminum alloy has excellent mechanical properties.
Preferably, the aluminum source is at least one selected from pure aluminum blocks, secondary aluminum blocks and aluminum alloy blocks, and the aluminum alloy blocks are alloy blocks composed of aluminum and at least one of Si, cu, mg, fe and Cr. Such as high-iron aluminum silicon alloy, secondary aluminum, aluminum copper alloy, aluminum magnesium alloy block, etc.
Preferably, the silicon source is selected from a silicon alloy block, and the silicon alloy block is an alloy block composed of silicon and at least one of Al, cu, mg and Ti. Such as a high-iron aluminum silicon alloy.
Preferably, the copper source is selected from at least one of a pure copper block and a copper alloy block, and the copper alloy block is an alloy block composed of copper and at least one of Si, mg, al and Fe. Such as aluminum bronze, etc.
Preferably, the magnesium source is selected from at least one of pure magnesium blocks and magnesium alloy blocks, and the magnesium alloy blocks are alloy blocks composed of magnesium and at least one of Si, cu, al and Fe.
Preferably, the iron source is selected from a ferrous alloy block, and the ferrous alloy block is an alloy block composed of iron and at least one of Si, cu, al and Mg. Such as high-iron aluminum silicon alloy, silicon iron alloy, etc.
Preferably, the chromium source is selected from at least one of silicon-chromium alloy and ferrochrome.
In a preferable scheme, the smelting temperature is 800-850 ℃.
Further preferably, the smelting process comprises the following steps: and heating to 800-850 ℃, and preserving the temperature for 15-25 min after the mixture is completely melted to obtain a melt A.
Preferably, the rare earth source is selected from at least one of aluminum-lanthanum alloy, aluminum-cerium alloy and lanthanum-cerium alloy.
Preferably, the titanium source is at least one selected from the group consisting of an aluminum-titanium alloy and an aluminum-titanium-boron alloy.
Preferably, the strontium source is selected from aluminum strontium alloy.
Preferably, the boron source is at least one selected from the group consisting of aluminum boron alloy and aluminum titanium boron alloy.
In a preferable scheme, the temperature is reduced to 750-800 ℃, a rare earth source, a titanium source, a strontium source and a boron source are added, and the temperature is kept for 10-20 min to obtain a melt B.
According to the preferable scheme, after the melt B is obtained, the temperature is reduced to 680-720 ℃, the permanent magnetic stirring treatment is stopped, the argon gas is stopped being introduced, and the casting is carried out to obtain the cast aluminum alloy.
In the actual operation process, small aluminum sources, silicon sources, magnesium sources, copper sources, iron sources and chromium sources are adopted, mixed uniformly and then placed in Al 2 O 3 Smelting in a crucible in a vacuum furnace to obtain a melt A, starting a permanent magnet stirring deviceAnd (3) performing alternate permanent magnetic stirring treatment on the melt, adding a rare earth source, a titanium source, a strontium source and a boron source, preserving heat to obtain a melt B, cooling, closing permanent magnetic stirring, stopping ventilation, and casting to obtain a finished product.
Preferably, the process of the permanent magnetic stirring treatment comprises the following steps: the melt is rotated forward for 1-4 min and then reversely for 1-4 min, so as to reciprocate; in the rotating process, the melt is lifted every 1-4 min.
In the permanent magnetic stirring process, the magnetic field motion mode at the melt is continuously adjusted by adopting the means of turning and shifting, so that Lorentz forces in different directions and different sizes are excited, heat transfer and mass transfer of the melt can be effectively realized, smelting of intermediate alloy is promoted, solute elements are uniformly distributed, an alloy solidification structure is refined, and the toughness of the alloy is strengthened. The permanent magnetism stirring process in this scheme is through magnet rotational speed diversion and the processing of fuse-element position shifting, realizes the multi-level pluralism control in magnetic field, and the stirring effect is showing, and the control means is simple. 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 inside the melt is realized by means of turbulence formed by high rotating speed, the effect is limited, and the separated phase in the melt is in a relative static state or weakened in relative movement along with the melt by keeping the same speed and the same direction for a long time, so that the stirring effect is weakened. Of course, even if the turning rotation is adopted, if the time for one rotation in the same direction is too short, the time for the high-speed rotation of the melt is reduced in consideration of the mechanical acceleration time and deceleration time, so that the stirring effect is weakened, and the service life of the equipment is affected by frequent turning.
In the invention, the forward rotation and the reverse rotation are only corresponding reverse directions, and the forward rotation and the reverse rotation only represent direction changes. But there is no specific direction limitation.
Further preferably, the permanent magnetic stirring treatment process comprises the following steps: the melt is rotated forwards for 3-4 min and then reversely for 3-4 min, so as to reciprocate; and in the rotating process, the melt is subjected to lifting motion every 3-4 min. The inventor finds that the performance of the finally obtained alloy material is optimal by changing the direction in stages by adopting the preferred scheme.
Preferably, in the permanent magnetic stirring treatment process, the magnetic induction intensity is 500-3000 Gs, and preferably 1500-3000 Gs.
Preferably, in the permanent magnetic stirring treatment process, the rotating speed of the magnet is 80-300 rpm, preferably 150-250 rpm.
Principles and advantages
The cast aluminum alloy provided by the invention has high strength and toughness as follows: 1: alloy elements such as Cu, mg, cr, fe and the like are added, on one hand, the Cu, mg and Cr can be dissolved in an aluminum matrix in a solid mode to improve the strength of the matrix, on the other hand, an aluminum-copper phase, an aluminum-copper-magnesium-silicon phase and an iron-rich phase are formed and are uniformly distributed in the matrix, and precipitated phase strengthening is achieved. 2: adopts multiple elements of Re, ti, sr and B to perform synergistic modification treatment, on the one hand introduces heterogeneous nucleation phase such as Al 3 La、Al 4 Ce、Al 3 Ti、Ti 2 B and the like can enrich the aluminum matrix in the vicinity of a silicon phase and an iron-rich phase, and refine precipitated phases such as the silicon phase and the like through changing the structural supercooling, the precipitated phase growth mode and the like. 3: the unique permanent magnetic stirring treatment is adopted, and the constantly changing magnetic field instead of the single moving magnetic field excites the lorentz force in the melt, so that the 'relative rest' state caused by the inertia motion of the melt is effectively avoided, and the heat transfer and mass transfer in the melt are greatly improved; in addition, the Lorentz force effectively avoids the aggregation of alloy elements, improves the distribution of nucleation sites, further refines the solidification structure of the alloy and strengthens the obdurability of the alloy.
Compared with the prior art, the invention has the beneficial effects that: the element proportion in the aluminum alloy is reasonably regulated, multielement modification treatment is adopted, and a unique permanent magnet stirring process is combined, so that the refining of precipitated phases of the aluminum alloy is effectively realized, and the toughness of the alloy is greatly improved.
Detailed Description
Example 1:
alloy components: 6% Si,0.5% Mg,0.3% Cu,0.2% La,0.2% Cr,0.1% Fe,0.03% Ti,0.003% Sr,0.003% B, the remainder being aluminum and unavoidable impurities, the content of impurities being less than 0.2%. The alloy used has an aluminum ingot, an Al-20% Si, a magnesium ingot, an Al-10% Cu, an Al-10% La, an Al-10% Cr, an Al-5% Fe, an Al-5% Ti-1% B, an Al-10% Ti, an Al-10% Sr.
The preparation method comprises the following steps: small aluminum source, silicon source, magnesium source, copper source, iron source and chromium source which are weighed according to the component proportion are alternately placed in Al 2 O 3 The crucible is vertically placed in a tube furnace. Introducing high-purity argon for 15min, starting the tube furnace, heating to 830 ℃, and preserving heat for 20min after the high-purity argon is completely melted; starting a permanent magnetic stirring device, and applying alternate permanent magnetic stirring treatment; adding a rare earth source, a titanium source, a strontium source and a boron source into the alloy melt in proportion, and keeping the temperature for 15min; and cooling to 700 ℃, closing the permanent magnetic stirring device, stopping ventilation, taking out the melt, and casting to obtain the aluminum alloy. The alternate permanent magnetic stirring treatment comprises the following steps: rotating forwards for 3min and then rotating backwards for 3 min; in the rotating process, the magnetic stirrer performs lifting motion once every 3min through the telescopic rod, the stirring speed of the magnet is 200rpm, and the magnetic induction intensity is 1500-2500 Gs (changing along with the lifting). And taking out the cast ingot after the melt is solidified. The test result shows that the tensile strength of the obtained aluminum alloy is 271MPa, and the elongation is 11.8%.
Example 2:
alloy components: 7% Si,0.5% Mg,0.3% Cu,0.2% La,0.2% Cr,0.15% Fe,0.03% Ti,0.003% Sr,0.003% B, the remainder being aluminum and unavoidable impurities, the content of impurities being less than 0.2%. The alloy used has an aluminum ingot, an Al-20% Si, a magnesium ingot, an Al-10% Cu, an Al-10% La, an Al-10% Cr, an Al-5% Fe, an Al-5% Ti-1% B, an Al-10% Ti, an Al-10% Sr.
The preparation method comprises the following steps: small aluminum source, silicon source, magnesium source, copper source, iron source and chromium source which are weighed according to the component proportion are alternately placed in Al 2 O 3 The crucible is vertically placed in a tube furnace. After introducing high-purity argon for 15min, starting the tube furnace, heating to 830 ℃, and preserving heat for 20min after the tube furnace is completely melted; starting a permanent magnetic stirring device, and applying alternate permanent magnetic stirring treatment; adding a rare earth source, a titanium source, a strontium source and a boron source into the alloy melt in proportion, and keeping the temperature for 15min; and cooling to 700 ℃, closing the permanent magnetic stirring device, stopping ventilation, taking out the melt, and casting to obtain the aluminum alloy. The alternate permanent magnetic stirring treatment comprises the following steps: rotating forwards for 4min and then rotating backwards for 4min to reciprocate; during the rotation, every other3min, performing one-time lifting movement through a telescopic rod, wherein the stirring speed of the magnet is 150rpm, and the magnetic induction intensity is 1500-2500 Gs (changing along with lifting). And taking out the cast ingot after the melt is solidified. The tensile strength of the obtained aluminum alloy is 263MPa and the elongation is 10.5 percent through test detection.
Example 3:
alloy components: 7% Si,0.6% Mg,0.4% Cu,0.3% by weight Ce,0.25% Cr,0.1% Fe,0.03% Ti,0.004% Sr,0.004% B, the remainder being aluminum and unavoidable impurities, the content of impurities being less than 0.2%. The alloy used has an aluminum ingot, an Al-20% Si, a magnesium ingot, an Al-10% Cu, an Al-10% Ce, an Al-10% Cr, an Al-5% Fe, an Al-5% Ti-1% B, an Al-10% Ti, an Al-10% Sr.
The preparation method comprises the following steps: small aluminum source, silicon source, magnesium source, copper source, iron source and chromium source which are weighed according to the component proportion are alternately placed in Al 2 O 3 The crucible is vertically placed in a tube furnace. Introducing high-purity argon for 15min, starting the tube furnace, heating to 850 ℃, and preserving heat for 20min after the tube furnace is completely melted; starting a permanent magnetic stirring device, and applying alternate permanent magnetic stirring treatment; adding a rare earth source, a titanium source, a strontium source and a boron source into the alloy melt in proportion, and preserving heat for 10min; and cooling to 700 ℃, closing the permanent magnetic stirring device, stopping ventilation, taking out the melt, and casting to obtain the aluminum alloy. The alternative permanent magnetic stirring treatment comprises the following steps: rotating forwards for 4min and then rotating backwards for 4min to reciprocate; in the rotating process, the magnetic stirrer performs lifting motion once every 4min through the telescopic rod, the stirring speed of the magnet is 200rpm, and the magnetic induction intensity is 1500-2500 Gs (changing along with the lifting). And taking out the cast ingot after the melt is solidified. The test shows that the tensile strength of the obtained aluminum alloy is 264MPa, and the elongation is 9.8%.
Example 4:
the alloy comprises the following components: 7% Si,0.6% Mg,0.4% Cu,0.3% by weight Ce,0.2% Cr,0.1% Fe,0.02% Ti,0.004% Sr,0.004% B, the remainder being aluminum and unavoidable impurities, the content of impurities being less than 0.2%. The alloy used has an aluminum ingot, an Al-20% Si, a magnesium ingot, an Al-10% Cu, an Al-10% Ce, an Al-10% Cr, an Al-5% Fe, an Al-5% Ti-1% B, an Al-10% Ti, an Al-10% Sr.
The preparation method comprises the following steps: aluminum source of small blocks weighed according to component proportionA silicon source, a magnesium source, a copper source, an iron source and a chromium source which are alternately arranged in Al 2 O 3 The crucible is vertically placed in a tube furnace. Introducing high-purity argon for 15min, starting the tube furnace, heating to 800 ℃, and preserving heat for 20min after the high-purity argon is completely melted; starting a permanent magnetic stirring device, and applying alternate permanent magnetic stirring treatment; adding a rare earth source, a titanium source, a strontium source and a boron source into the alloy melt in proportion, and preserving heat for 10min; and cooling to 700 ℃, closing the permanent magnetic stirring device, stopping ventilation, taking out the melt, and casting to obtain the aluminum alloy. The alternate permanent magnetic stirring treatment comprises the following steps: rotating forwards for 4min and then rotating backwards for 4min to reciprocate; in the rotating process, the magnetic stirrer performs lifting motion once every 4min through the telescopic rod, the stirring speed of the magnet is 150rpm, and the magnetic induction intensity is 1500-2500 Gs (changing along with the lifting). And taking out the cast ingot after the melt is solidified. The test shows that the tensile strength of the obtained aluminum alloy is 258MPa, and the elongation is 9.5%.
Comparative example 1:
the other experimental conditions were completely the same as those in example 1, except that the content of iron was increased to 1% and that the content of chromium was unchanged. The tensile strength of the obtained aluminum alloy is 162MPa and the elongation is 5.6 percent through test detection.
As can be seen from the comparison of the data of comparative example 1 with those of example 1, the content of iron element is too high and the Cr/Fe ratio is too low, so that coarse iron-containing phase is formed, which deteriorates the tensile properties of the alloy though strengthening the hardness of the matrix.
Comparative example 2:
the other experimental conditions were completely identical to those of example 1, except that no rare earth element was added and no permanent magnetic stirring was applied. The test result shows that the tensile strength of the obtained aluminum alloy is 158MPa, and the elongation is 6.4%.
Comparative example 3:
the other experimental conditions were completely identical to those of example 1, except that no rare earth element was added. The test result shows that the tensile strength of the obtained aluminum alloy is 194MPa, and the elongation is 6.8%.
Comparative example 4:
the other experimental conditions were completely identical to those of example 1 except that the rare earth was 0.02% La. The test shows that the tensile strength of the obtained aluminum alloy is 213MPa, and the elongation is 7.3%. As can be seen from comparative example 4, when the rare earth content is low, the modification effect of rare earth is weak, complete modification is not achieved, and the alloy strengthening effect is correspondingly weak.
Comparative example 5:
the other experimental conditions were completely the same as those in example 1 except that the rare earth was 3.0% La. The test shows that the tensile strength of the obtained aluminum alloy is 217MPa, and the elongation is 7.9%. As can be seen from comparative example 5, when the rare earth content is high, the rare earth aggregates with each other, reacts with the alloy element, generates a brittle or long-strip intermetallic compound, and correspondingly reduces the alloy performance to a certain extent.
As can be seen from the comparison of the data of the comparative examples 2-5 and the data of the example 1, the modification effect of the alloy is obviously influenced by the addition amount of the rare earth, and when the addition amount of the rare earth is too low or 0, the modification effect of the rare earth is not obviously insufficient; when the addition amount of the rare earth is too high, coarse rare earth compounds appear in the alloy, and the matrix is torn to play a role in reaction.
Comparative example 6:
the other experimental conditions were identical to those of example 1, except that no permanent magnetic stirring was applied. The tensile strength of the obtained aluminum alloy is 189MPa and the elongation is 6.4 percent through test detection.
Comparative example 7:
the other experimental conditions were identical to those of example 1, except that the permanent magnet stirring speed was 30rpm. The tensile strength of the obtained aluminum alloy is 218MPa and the elongation is 7.2 percent through test detection.
As can be seen from the comparative example 7, the technological parameters of the permanent magnet stirring also have certain influence on the performance of the cast ingot, when the stirring speed of the permanent magnet is lower, the excited Lorentz force is also lower, the formed eddy current is also lower, the stirring effect is correspondingly weakened, the limitation on the growth of the precipitated phase is weaker, and the strengthening effect is less satisfactory.
Comparative example 8:
the other experimental conditions were completely the same as in example 1, except that the speed direction was not changed during the permanent magnet stirring. The test shows that the tensile strength of the obtained aluminum alloy is 209MPa, and the elongation is 8.2%.
Comparative example 9:
the other experimental conditions were identical to those of example 1, except that the lifting rod was not moved during the application of the permanent magnetic stirring. The test shows that the tensile strength of the obtained aluminum alloy is 213MPa, and the elongation is 8.6%.
Comparative example 10:
other experimental conditions were completely the same as in example 1, except that the elevating rod was moved up and down once every 6min while applying permanent magnetic stirring. The tensile strength of the obtained aluminum alloy is 221MPa and the elongation is 8.9 percent through test detection. As can be seen from the comparative example 10, when the movement frequency of the telescopic rod is lower, the relative change of the movement magnetic field is slower, and due to the rapid movement in the horizontal direction, precipitated phases in the melt are gathered to a certain extent to cause coarsening of the structure, and the alloy performance is correspondingly reduced.
It can be seen from comparative examples 6-10 and example 1 that in the magnetic field control process, the stirring effect is weakened by the lower magnetic field rotation speed, the lower lifting frequency and the direction of the constant magnetic field rotation speed, and the alloy performance cannot be optimized well.
It can be seen from the comparison of the comparative examples 2-10 with the data in the example 1 that the alloy can be strengthened to a certain extent by utilizing the independent action of the rare earth modification and the permanent magnetic stirring technology, the permanent magnetic stirring technology is superior to the rare earth modification, and the effect of the combined moving magnetic field stirring technology is better; the permanent magnetic stirring coupled rare earth modification technology can obviously improve the tensile strength and the elongation of the alloy and obviously improve the obdurability of the aluminum alloy.
The method is feasible and has certain practical value and industrial application potential as shown in the examples and the comparative examples. The above embodiments are provided only for illustrating the present invention and not for limiting the present invention, and those skilled in the art can make various changes and modifications without departing from the spirit and scope of the present invention, therefore, all equivalent technical solutions should also fall within the scope of the present invention, and should be defined by the claims.
Claims (10)
1. A high-strength and high-toughness cast aluminum alloy with low Si content is characterized in that: the cast aluminum alloy comprises the following components in percentage by mass: si: 4.5-7%, mg:0.4 to 0.7%, cu:0.2 to 0.5%, RE:0.1 to 0.4%, cr: 0.15-0.35%, fe is less than or equal to 0.15%, ti:0.01 to 0.05 percent, sr:0.001 to 0.004%, B:0.001 to 0.004%, and the balance of aluminum and inevitable impurities.
2. The high-toughness low-Si-content cast aluminum alloy according to claim 1, wherein: in the cast aluminum alloy, the mass ratio of Cr to Fe is 1-3;
in the cast aluminum alloy, the mass ratio of Ti to B is 5-10;
in the cast aluminum alloy, the mass ratio of Sr to B is 1-2.
3. A high toughness low Si content cast aluminum alloy as claimed in claim 1 or 2, wherein: the cast aluminum alloy comprises the following components in percentage by mass: si: 6-8%, mg:0.5 to 0.7%, cu:0.3 to 0.5%, RE:0.2 to 0.3%, cr:0.15 to 0.30%, fe:0.1 to 0.15%, ti:0.02 to 0.04 percent, sr:0.003 to 0.004%, B: 0.003-0.004%, RE is Ce and/or La, and the rest is aluminum and inevitable impurities.
4. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to any one of claims 1 to 3, wherein the method comprises the following steps: the method comprises the following steps: preparing an aluminum source, a silicon source, a magnesium source, a copper source, an iron source and a chromium source according to a designed proportion, uniformly mixing to obtain a mixture, introducing argon to discharge air, smelting to obtain a melt A, starting a permanent magnetic stirring device, and applying permanent magnetic stirring treatment to the melt; and then cooling, adding a rare earth source, a titanium source, a strontium source and a boron source, preserving heat to obtain a melt B, cooling, stopping applying permanent magnetic stirring treatment, stopping introducing argon, and casting to obtain the cast aluminum alloy.
5. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to claim 4, wherein the method comprises the following steps: the smelting process comprises the following steps: and heating to 800-850 ℃, and preserving the temperature for 15-25 min after the mixture is completely melted to obtain a melt A.
6. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to claim 5, wherein the method comprises the following steps: cooling to 750-800 deg.c, adding RE source, ti source, sr source and B source, and maintaining for 10-20 min to obtain melt B.
7. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to claim 5, wherein the method comprises the following steps: and after obtaining the melt B, cooling to 680-720 ℃, stopping applying permanent magnetic stirring treatment, stopping introducing argon, and casting to obtain the cast aluminum alloy.
8. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to claim 5, wherein the method comprises the following steps: the process of the permanent magnetic stirring treatment comprises the following steps: the melt is rotated forward for 1-4 min and then reversely for 1-4 min, so as to reciprocate; in the rotating process, the melt is lifted every 1-4 min.
9. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to claim 5 or 8, wherein the method comprises the following steps: and in the permanent magnetic stirring treatment process, the magnetic induction intensity is 500-3000 Gs.
10. The method for preparing the high-toughness low-Si-content cast aluminum alloy according to claim 5 or 8, wherein the method comprises the following steps: in the process of permanent magnet stirring treatment, the rotating speed of the magnet is 80-300 rpm.
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