CN112410591B - Super-long-effect double-modification method for hypereutectic aluminum-silicon alloy - Google Patents
Super-long-effect double-modification method for hypereutectic aluminum-silicon alloy Download PDFInfo
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Abstract
The invention discloses a hypereutectic aluminum-silicon alloy ultra-long-term dual-modification method, which specifically comprises the following steps: 1) preparing materials: preparing hypereutectic aluminum-silicon alloy; 2) preparing the weight of fluorine salt and the weight of carbon powder according to the total weight of the aluminum-silicon alloy, wherein the formula comprises the following components in parts by weight: the mass ratio of Si/(Ti + Zr + B + C) is more than or equal to 5 and more than or equal to 2; the molar ratio of Ti to Zr to B to C is Ti: b: C ═ 1:1:2: 2; 3) firstly, adding prepared aluminum and silicon materials into an intermediate frequency reaction furnace for melting, then adding prepared potassium fluoborate for reaction, then adding potassium fluotitanate for reaction, then adding graphene for reaction, heating aluminum water, then adding potassium fluozirconate for reaction, pouring residual liquid villiaumite after the reaction is finished, and then heating and preserving heat; 4) and pouring molten aluminum in the intermediate frequency furnace into a transfer ladle, then pouring into an ingot furnace, and casting into an aluminum alloy ingot after the molten aluminum is cooled and argon is degassed.
Description
Technical Field
The invention relates to the technical field of aluminum alloy material modification methods, in particular to a long-acting dual modification method for hypereutectic aluminum-silicon alloy.
Background
The hypereutectic aluminum-silicon alloy has the characteristics of good high-temperature mechanical property, good wear resistance, good volume stability, high temperature resistance and the like, and is widely applied to the important industrial fields of automobile engine pistons, petroleum industry and other fields requiring light weight requirements and wear resistance. Because the content of silicon element in hypereutectic aluminum silicon system exceeds the eutectic point of alloy, a great deal of needle-shaped or plate-shaped eutectic silicon structures and a great deal of block-shaped primary crystal silicon structures exist in the micro-casting structure of the alloy, if modification treatment is not carried out, the block-shaped primary crystal silicon particles in the structure are large, and the length of the eutectic silicon is large. The shapes of the coarse eutectic silicon and the primary silicon cause the reduction of the mechanical property of the material, and the material cannot be applied to the industry. In order to improve the performance of the hypereutectic aluminum-silicon alloy material, the traditional modification process is to add phosphorus-containing salts or phosphorus-containing compounds such as Al-P, Cu-P alloy and the like into molten aluminum for refining and modifying primary crystal silicon in the hypereutectic aluminum-silicon alloy; meanwhile, modifying elements such As Na, Sr, Ba, Te, Sb, S, Y, Ca, Bi, As, Ce, Nd, RE and the like are added to modify the eutectic silicon; or a phosphorus and mixed rare earth composite alterant is added to cause eutectic silicon and primary crystal silicon to be simultaneously altered, so that the hypereutectic aluminum-silicon alloy has good dual alteration effect and a large amount of best mechanical properties.
Patent CN1242082 discloses a hypereutectic aluminum-silicon alloy modifier, which is composed of Cu, Ti, La, Ce, Nd, Pr, C, B and aluminum, and the modifier is added into hypereutectic aluminum alloy, and then is blown and stirred by inert gas, so that eutectic silicon in the hypereutectic aluminum-silicon alloy can be modified, the primary silicon can be modified, and the size of the primary silicon can be maintained below 50um for a long time (8 hours). The refining and purifying effect can be maintained for 5-10 hours, and no pollution is caused.
In the paper "dual modification effect of Ce-P to hypereutectic aluminum-silicon alloy" in the 4 th period of the hot working process in 1998, the modification effect of P, Ce and the composite addition thereof to hypereutectic Al-20% Si alloy is studied, and the modification effects are comprehensively compared. The result shows that the P, Ce composite modification can refine primary crystal silicon and eutectic silicon simultaneously, and the modification effect can last for 5 hours.
The existing aluminum-silicon alloy modification technology mainly adds modification elements into the alloy As a main technical means, wherein modification primary crystal silicon mainly comprises primary crystal silicon with fine particles, which is formed in a structure after P is added into aluminum liquid, the primary crystal silicon is solidified by taking the AlP As a crystal nucleus in the solidification process, if double modification is realized, Na, Sr, Ba, Te, Sb, S, Y, Ca, Bi, As, Ce, Nd, RE and other elements are required to be added, but because the P element reacts with most elements, double modification cannot be realized, or although the P element does not react with S, Ce, Nd, Y, RE and other elements, the P element has mutual weakening effect in the common modification process, so that a large amount of modification elements are required to be added, the modification effect is general, the modification effective time is short, and the modification effect can hardly exceed 10 hours and can also be the initial modification effect; in addition, almost all modification treatment methods by adding modification elements weaken modification effect due to burning loss, segregation and the like of the modification elements after re-melting, and a certain amount of modification elements need to be added again for supplement, so that quality fluctuation and waste are caused.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provides a method for ultra-long-term dual-modification of hypereutectic aluminum-silicon alloy. Micron-scale and submicron-scale TiCb and ZrCB ceramic particles are generated in the hypereutectic aluminum-silicon alloy through in-situ reaction, and are distributed to the crystal boundary of eutectic silicon and primary crystal silicon respectively in the process of solidifying the molten aluminum, so that the growth of the eutectic silicon and the primary crystal silicon is prevented, and the dual deterioration of the eutectic silicon and the primary crystal silicon can be realized simultaneously; because the ceramic particles exist stably in the aluminum liquid, the ceramic particles can not react with any element, need no modification element and can not be decomposed, the problem of modification interference of eutectic silicon and primary crystal silicon can not occur; meanwhile, as long as the ceramics can be stored in the aluminum liquid, the problem of failure can not occur due to double deterioration, so that the deterioration of primary crystal silicon and eutectic silicon can be realized for an unlimited time, even if the aluminum ingot is remelted for many times, the double deterioration effect can still be realized, and the great optimal mechanical properties of the hypereutectic aluminum-silicon alloy can be maintained.
The technical scheme adopted by the invention for solving the technical problems is as follows:
a hypereutectic aluminum-silicon alloy ultra-long-term dual-modification method specifically comprises the following steps:
1) preparing materials: preparing hypereutectic aluminum-silicon alloy;
2) preparing the weight of fluorine salt and the weight of carbon powder according to the total weight of the aluminum-silicon alloy, wherein the formula comprises the following components in parts by weight:
the mass ratio of Si/(Ti + Zr + B + C) is more than or equal to 5 and more than or equal to 2;
the molar ratio of Ti to Zr to B to C is Ti: b: C ═ 1:1:2: 2;
3) firstly, adding prepared aluminum and silicon materials into an intermediate frequency reaction furnace for melting, then adding prepared potassium fluoborate for reaction, then adding potassium fluotitanate for reaction, then adding graphene for reaction, heating aluminum water, then adding potassium fluozirconate for reaction, pouring residual liquid fluorine salt after the reaction is finished, and then heating and preserving heat;
4) and pouring molten aluminum in the intermediate frequency furnace into a transfer ladle, then pouring into an ingot furnace, and casting into aluminum alloy ingots for later use after the temperature of the molten aluminum is reduced.
The silicon content of the hypereutectic aluminum-silicon alloy in the step 1) is more than or equal to 13% and less than or equal to 25%, and the balance is aluminum.
In the step 2), Ti is prepared according to potassium fluotitanate, B is prepared according to potassium fluoborate, Zr is prepared according to potassium fluozirconate, and C is 8000-mesh graphene material.
The melting temperature of the intermediate frequency reaction furnace in the step 3) is controlled to be 700-750 ℃, the reaction time of adding the potassium fluoborate is 10 minutes, the reaction time of adding the potassium fluotitanate is 10 minutes, and the reaction time of adding the graphene is 10 minutes; heating the molten aluminum to 900 ℃, adding potassium fluozirconate, reacting for 10 minutes, after finishing the reaction and pouring out the residual liquid villiaumite, heating to 1200-1250 ℃, and keeping the temperature for 30 minutes.
And 4) reducing the temperature of the aluminum liquid to 790 ℃, degassing the aluminum liquid by argon gas, and then casting the aluminum liquid into aluminum alloy ingots.
The invention has the beneficial effects that:
1. micron-scale and submicron-scale TiCb and ZrCB ceramic particles are generated in the hypereutectic aluminum-silicon alloy through in-situ reaction, and are distributed to the crystal boundary of eutectic silicon and primary crystal silicon respectively in the process of solidifying the molten aluminum, so that the growth of the eutectic silicon and the primary crystal silicon is prevented, and the dual deterioration of the eutectic silicon and the primary crystal silicon can be realized simultaneously; because the ceramic particles exist stably in the aluminum liquid, the ceramic particles can not react with any element, need no modification element and can not be decomposed, the problem of modification interference of eutectic silicon and primary crystal silicon can not occur; meanwhile, because the ceramics can be stored in the aluminum liquid, the problem of failure can not occur due to double deterioration, the deterioration effect on primary crystal silicon and eutectic silicon for infinite time can be realized, even if the aluminum ingot is remelted for many times, the double deterioration effect can still be realized, and the great optimal mechanical properties of the hypereutectic aluminum-silicon alloy can be maintained. .
2. After the technology of the invention is adopted, the primary silicon and the eutectic silicon in the aluminum-silicon alloy structure are both modified and refined, wherein the size of the primary silicon is less than 40 microns, and the original shape is changed from thick plate shape and sheet shape into fine particle shape; the edges of the granular primary crystal silicon are smooth and have no obvious edges and corners; the eutectic silicon has obviously reduced size and fine granular shape changed from lamellar shape or long needle shape, so that the mechanical property and the processing property of the hypereutectic aluminum-silicon alloy are obviously improved due to the microscopic shape, and the processing requirements of precision processing products such as pistons and the like can be met.
3. After the technology of the invention is adopted, even if the hypereutectic aluminum-silicon alloy is subjected to long-time heat preservation and repeated remelting without adding modification elements, the primary silicon and the eutectic silicon in the alloy structure can still be guaranteed to reach modification effects, so that the modification effects of the hypereutectic aluminum-silicon alloy can be kept at temperature under the condition of long-time use, and meanwhile, the casting process is simplified and the alloy refining quality is guaranteed because other modification elements are not added.
Drawings
FIG. 1 is a gold phase diagram in which metallographic primary silicon is coarse and eutectic silicon is long acicular before the composite material is added;
FIG. 2 is a diagram of a gold phase in which primary silicon is refined into small blocks and eutectic silicon is dotted, due to the double metamorphic effect of the added composite material;
FIG. 3 is a metallographic image of a sample taken at 500 hours of incubation;
FIG. 4 is a diagram of the gold phase after 50 times of remelting;
FIG. 5 is a metallographic image taken at 500 hours of incubation;
FIG. 6 is a diagram of the gold phase after 50 times of remelting;
FIG. 7 is a metallographic image taken after 500 hours of incubation;
FIG. 8 is a diagram of the gold phase after 50 times of remelting.
Detailed Description
In order to make those skilled in the art better understand the technical solution of the present invention, the technical solution in the embodiment of the present invention will be clearly and completely described below with reference to the drawings in the embodiment of the present invention, and it is obvious that the described embodiment is only a part of the embodiment of the present invention, and not all embodiments.
As shown in figure 1, figure 2 and figures 3-8, the invention provides a super-long-acting double-modification method for hypereutectic aluminum-silicon alloy, which specifically comprises the following steps:
1) preparing materials: preparing hypereutectic aluminum-silicon alloy, wherein the silicon content is more than or equal to 13% and less than or equal to 25% and the balance is aluminum;
2) preparing the weight of fluorine salt and the weight of carbon powder according to the total weight of the aluminum-silicon alloy, wherein the formula comprises the following components in parts by weight: the mass ratio of Si/(Ti + Zr + B + C) is more than or equal to 5 and more than or equal to 2; the molar ratio of Ti to Zr to B to C is Ti: b: C ═ 1:1:2:2, Ti is prepared according to potassium fluotitanate, B is prepared according to potassium fluoborate, Zr is prepared according to potassium fluozirconate, and C is a 8000-mesh graphene material;
3) adding the prepared aluminum and silicon materials into an intermediate frequency reaction furnace for melting, controlling the temperature to 700 ℃ and 750 ℃, then adding the prepared potassium fluoborate for reaction for 10 minutes; adding potassium fluotitanate for reaction for 10 minutes, and then adding graphene for reaction for 10 minutes; heating the aluminum water to 900 ℃, adding potassium fluozirconate, and reacting for 10 minutes; after the reaction is finished, pouring off the residual liquid villiaumite, then heating to 1200-1250 ℃, and preserving the heat for 30 minutes;
4) and pouring the molten aluminum in the intermediate frequency furnace into a transfer ladle, then pouring into an ingot furnace, and casting the molten aluminum into an aluminum alloy ingot for later use after argon degassing is performed on the molten aluminum until the temperature of the molten aluminum is reduced to 790 ℃.
After the technology of the invention is adopted, the primary silicon and the eutectic silicon in the aluminum-silicon alloy structure are both modified and refined, wherein the size of the primary silicon is less than 40 microns, and the original shape is changed from thick plate shape and sheet shape into fine particle shape; the edges of the granular primary crystal silicon are smooth and have no obvious edges and corners; the size of eutectic silicon is obviously reduced, the shape of the eutectic silicon is changed from the lamellar shape or the long needle shape shown in figure 1 into the fine granular shape shown in figure 2, the mechanical property and the processing property of the hypereutectic aluminum-silicon alloy are obviously improved due to the microcosmic shape, and the processing requirement of precision processing products such as pistons and the like can be met.
After the technology of the invention is adopted, even if the hypereutectic aluminum-silicon alloy is subjected to long-time heat preservation and repeated remelting without adding modification elements, the primary silicon and the eutectic silicon in the alloy structure can still be guaranteed to wait for modification effect, as shown in fig. 3 and 4, the modification effect of the hypereutectic aluminum-silicon alloy can be kept at temperature under the condition of long-time use, and meanwhile, the casting process is simplified without adding other modification elements, and the refining quality of the alloy is guaranteed.
Example 1
1) Preparing materials:
a, preparing hypereutectic aluminum-silicon alloy: weighing 87 kg of A00 aluminum ingot and 13 kg of industrial silicon;
b, preparing fluorine salt according to the weight of the aluminum-silicon alloy, wherein the formula principle is as follows: the molar ratio of Si/Ti + Zr + B + C is 2, and the molar ratio of Ti to Zr to B to C is 1:1:2:2, wherein 8.6 kg of potassium fluotitanate (in terms of 98% absorption) needs to be weighed; wherein 10.1 kilograms of potassium fluorozirconate (in terms of 99% absorption) needs to be weighed; potassium fluoroborate was weighed at 8.9 kg (according to 98% absorption) and graphene was weighed at 1.1 kg (according to 80% absorption);
2) in-situ reaction:
putting raw aluminum ingots and industrial silicon into an intermediate frequency furnace, starting the furnace to heat, removing floating slag on the surface after the aluminum ingots and the industrial silicon are completely melted, measuring the temperature of molten aluminum at 700 ℃, firstly adding potassium fluoborate, and reacting for 10 minutes; adding prepared potassium fluotitanate, and reacting for 10 minutes; then adding graphene, reacting for 10 minutes, heating the aluminum water to 900 ℃, adding potassium fluozirconate, and reacting for 10 minutes; after the reaction is finished, pouring out the residual liquid villiaumite, then heating to 1200 ℃, and preserving heat for 30 minutes;
3) and (3) heat preservation test:
pouring the aluminum liquid into a heat-preservation crucible, degassing by adopting argon gas when the temperature of the aluminum liquid is reduced to 790 ℃, degassing again and sampling after the aluminum liquid is preserved for 500 hours at 760 plus 790 ℃, and referring to the attached drawing 3.
4) Remelting test:
pouring the molten aluminum into a transfer ladle, adding the transfer ladle into an ingot furnace, and casting the molten aluminum into an aluminum alloy ingot for later use after online degassing of the molten aluminum when the temperature of the molten aluminum is reduced to 790 ℃. 50 kg of aluminum ingot is added into a heat-preservation crucible for remelting test, the remelting and sampling temperature is controlled at 760-790 ℃, and sampling is carried out after 50 times of remelting (degassing treatment is carried out after each remelting), as shown in figure 4.
Example 2
1) Preparing materials:
a, preparing hypereutectic aluminum-silicon alloy: weighing 80 kg of A00 aluminum ingot and 20 kg of industrial silicon;
b, preparing fluorine salt according to the weight of the aluminum-silicon alloy, wherein the formula principle is as follows: the molar ratio of Si/Ti + Zr + B + C is 3.5, and the molar ratio of Ti to B to C is 1:1:2:2, wherein 7.6 kg of potassium fluotitanate (in terms of 98% absorption) needs to be weighed; wherein 8.9 kilograms of potassium fluorozirconate (in terms of 99% absorption) needs to be weighed; potassium fluoroborate was weighed at 7.8 kg (according to 98% absorbance) and graphene was weighed at 0.93 kg (according to 80% absorbance); 2) in-situ reaction:
putting raw aluminum ingots and industrial silicon into an intermediate frequency furnace, starting the furnace to heat, removing surface scum after the aluminum ingots and the industrial silicon are completely melted, controlling the temperature of aluminum water to 720 ℃, firstly adding potassium fluoborate, and reacting for 10 minutes; adding prepared potassium fluotitanate, and reacting for 10 minutes; then adding graphene, reacting for 10 minutes, heating the aluminum water to 900 ℃, adding potassium fluozirconate, and reacting for 10 minutes; after the reaction is finished, pouring out the residual liquid villiaumite, then heating to 1230 ℃, and preserving the heat for 30 minutes;
3) and (3) heat preservation test:
pouring the aluminum liquid into a heat-preservation crucible, degassing by adopting argon gas when the temperature of the aluminum liquid is reduced to 790 ℃, degassing again and sampling after the aluminum liquid is preserved for 500 hours at 760 plus 790 ℃, and referring to the attached drawing 5.
4) Remelting test:
pouring the molten aluminum into a transfer ladle, adding the transfer ladle into an ingot furnace, and casting the molten aluminum into an aluminum alloy ingot for later use after online degassing of the molten aluminum when the temperature of the molten aluminum is reduced to 790 ℃. 50 kg of aluminum ingot is added into a heat-preservation crucible for remelting test, the remelting and sampling temperature is controlled at 760-790 ℃, and sampling is carried out after 50 times of remelting (degassing treatment is carried out after each remelting), as shown in figure 6.
Example 3
1) Preparing materials:
a, preparing hypereutectic aluminum-silicon alloy: weighing 75 kg of A00 aluminum ingot and 25 kg of industrial silicon;
b, preparing fluorine salt according to the weight of the aluminum-silicon alloy, wherein the formula principle is as follows: the molar ratio of Si/Ti + Zr + B + C is 5, and the molar ratio of Ti to Zr to B to C is 1:1:2:2, wherein 6.6 kg of potassium fluotitanate (in terms of 98% absorption) needs to be weighed; wherein 7.8 kilograms of potassium fluorozirconate (in terms of 99% absorption) needs to be weighed; potassium fluoroborate was weighed 6.9 kg (according to 98% absorbance) and graphene was weighed 0.81 kg (according to 80% absorbance);
2) in-situ reaction:
putting raw aluminum ingots and industrial silicon into an intermediate frequency furnace, starting the furnace to heat, removing surface scum after the aluminum ingots and the industrial silicon are completely melted, controlling the temperature of aluminum water to 750 ℃, firstly adding potassium fluoborate, and reacting for 10 minutes; adding prepared potassium fluotitanate, and reacting for 10 minutes; then adding graphene, reacting for 10 minutes, heating the aluminum water to 900 ℃, adding potassium fluozirconate, and reacting for 10 minutes; after the reaction is finished, pouring out the residual liquid villiaumite, then heating to 1250 ℃, and preserving heat for 30 minutes;
3) and (3) heat preservation test:
pouring the aluminum liquid into a heat-preservation crucible, degassing by adopting argon gas when the temperature of the aluminum liquid is reduced to 790 ℃, degassing again and sampling after the aluminum liquid is preserved for 500 hours at 760 plus 790 ℃, and referring to the attached figure 7.
4) Remelting test:
pouring the molten aluminum into a transfer ladle, adding the transfer ladle into an ingot furnace, and casting the molten aluminum into an aluminum alloy ingot for later use after online degassing of the molten aluminum when the temperature of the molten aluminum is reduced to 790 ℃. 50 kg of aluminum ingot is added into a heat-preservation crucible for remelting test, the remelting and sampling temperature is controlled at 760-790 ℃, and sampling is carried out after 50 times of remelting (degassing treatment is carried out after each remelting), as shown in figure 8.
In the description of the present invention, the terms "upper", "lower", "front", "rear", "left", "right", "top", "bottom", "vertical", "horizontal", and the like indicate orientations or positional relationships based on those shown in the drawings, and are only for the purpose of describing the present invention but do not require that the present invention must be constructed or operated in a specific orientation, and thus, should not be construed as limiting the present invention. The terms "connected" and "connected" in the present invention should be interpreted broadly, and may be connected or disconnected, for example; the terms may be directly connected or indirectly connected through intermediate components, and specific meanings of the terms may be understood as specific conditions by those skilled in the art.
The above description is of the preferred embodiment of the present invention, and the description of the specific embodiment is only for better understanding of the idea of the present invention. It will be appreciated by those skilled in the art that various modifications and equivalents may be made in accordance with the principles of the invention and are considered to be within the scope of the invention.
Claims (3)
1. A hypereutectic aluminum-silicon alloy ultra-long-term dual-modification method is characterized by comprising the following steps:
1) preparing materials: preparing hypereutectic aluminum-silicon alloy;
2) preparing fluorine salt weight and graphene weight according to the total weight of the aluminum-silicon alloy, wherein the formula comprises the following components in parts by weight:
the mass ratio of Si/(Ti + Zr + B + C) is more than or equal to 5 and more than or equal to 2;
the molar ratio of Ti to Zr to B to C is 1:1:2: 2;
wherein Ti is prepared according to potassium fluotitanate, B is prepared according to potassium fluoborate, Zr is prepared according to potassium fluozirconate, and C is a 8000-mesh graphene material;
3) firstly, adding prepared aluminum and silicon materials into an intermediate frequency reaction furnace for melting, then adding prepared potassium fluoborate for reaction, then adding potassium fluotitanate for reaction, then adding graphene for reaction, heating aluminum water, then adding potassium fluozirconate for reaction, pouring residual liquid fluorine salt after the reaction is finished, and then heating and preserving heat;
4) pouring molten aluminum in the intermediate frequency furnace into a transfer ladle, then pouring into an ingot furnace, and casting into an aluminum alloy ingot for later use after the temperature of the molten aluminum is reduced;
the melting temperature of the intermediate frequency reaction furnace in the step 3) is controlled to be 700-750 ℃, the reaction time of adding the potassium fluoborate is 10 minutes, the reaction time of adding the potassium fluotitanate is 10 minutes, and the reaction time of adding the graphene is 10 minutes; heating the molten aluminum to 900 ℃, adding potassium fluozirconate, reacting for 10 minutes, after finishing the reaction and pouring out the residual liquid villiaumite, heating to 1200-1250 ℃, and keeping the temperature for 30 minutes;
micron-scale and submicron-scale TiCb and ZrCB ceramic particles are generated in the hypereutectic aluminum-silicon alloy through in-situ reaction, and the ceramic particles are distributed at the crystal boundaries of eutectic silicon and primary crystal silicon respectively in the process of solidifying the molten aluminum, so that the growth of the eutectic silicon and the primary crystal silicon is prevented, and the dual deterioration of the eutectic silicon and the primary crystal silicon is realized; because the ceramic particles exist stably in the aluminum liquid, the ceramic particles can not react with any element, need no modification element, can not be decomposed, and can not cause the problem of modification interference of eutectic silicon and primary crystal silicon; meanwhile, because the ceramics can be stored in the aluminum liquid, the dual deterioration can not cause failure problem, and the deterioration effect on primary crystal silicon and eutectic silicon for an unlimited time can be realized;
the primary silicon and eutectic silicon in the aluminum-silicon alloy structure are modified and refined, wherein the size of the primary silicon is less than 40 microns, and the form is changed from original thick plate-like and sheet-like to fine particle-like; the edges of the granular primary crystal silicon are smooth and have no obvious edges and corners; the eutectic silicon has obviously reduced size, the morphology of the eutectic silicon is changed from lamellar shape or long needle shape into fine granular shape, and the mechanical property and the processing property of the hypereutectic aluminum-silicon alloy are obviously improved due to the microscopic morphology.
2. The method for ultra-long-term dual deterioration of hypereutectic aluminum-silicon alloy according to claim 1, wherein the hypereutectic aluminum-silicon alloy of step 1) has a silicon content of 13% to 25% Si, with the balance being aluminum.
3. The method for ultra-long-term dual deterioration of hypereutectic aluminum-silicon alloy according to claim 1, wherein the temperature of the molten aluminum in step 4) is reduced to 790 ℃, and the molten aluminum is degassed by argon gas and cast into aluminum alloy ingots.
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Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB792172A (en) * | 1955-11-16 | 1958-03-19 | Aluminiumwerke Nurnberg G M B | Process for refining the crystalline structure of hypereutectic aluminium-silicon alloys |
| WO1996030550A1 (en) * | 1995-03-31 | 1996-10-03 | Merck Patent Gmbh | TiB2 PARTICULATE CERAMIC REINFORCED AL-ALLOY METAL-MATRIX COMPOSITES |
| CN1632146A (en) * | 2004-12-31 | 2005-06-29 | 清华大学 | Preparation of aluminium titanium carbide intermediate alloy grain refiner in the ultrasonic field |
| CN1936044A (en) * | 2006-10-14 | 2007-03-28 | 重庆工学院 | Efficient composite modifying-refining agent for hypoeutectic cast aluminium-silicon alloy and treatment process |
| CN101591746A (en) * | 2009-03-26 | 2009-12-02 | 广州钢铁企业集团有限公司 | A kind of aluminium, aluminium alloy grain refinement and modification master alloy and preparation method thereof |
| CN101591740A (en) * | 2009-06-22 | 2009-12-02 | 济南大学 | A kind of preparation method of Al-Ti-B-C master alloy fining agent |
| CN102560200A (en) * | 2012-01-11 | 2012-07-11 | 山东大学 | Aluminum-titanium-iron-carbon-boron intermediate alloy and preparation method thereof |
| CN102787248A (en) * | 2012-08-02 | 2012-11-21 | 中原工学院 | Method for refining primary silicon of hypereutectic Al-Si alloy |
| CN105908024A (en) * | 2016-06-21 | 2016-08-31 | 上海交通大学 | High-temperature-resistant nano ceramic particle reinforced cocrystallized Al-Si alloy and casting method thereof |
| CN106756149A (en) * | 2016-12-12 | 2017-05-31 | 南京云开合金有限公司 | A kind of aluminium titanium boron carbon zirconium rare earth fining agent, its preparation method and its application |
| CN110129631A (en) * | 2019-05-24 | 2019-08-16 | 西安康博新材料科技有限公司 | A kind of internal combustion engine high-toughness heat-resistant aluminum alloy materials and preparation method thereof |
| CN111411270A (en) * | 2020-05-21 | 2020-07-14 | 滨州渤海活塞有限公司 | Method for changing morphology of ferrosilicon phase in aluminum alloy |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102206777B (en) * | 2011-06-10 | 2013-07-10 | 深圳市新星轻合金材料股份有限公司 | Method for preparing aluminum-zirconium-titanium-carbon intermediate alloy |
-
2020
- 2020-10-30 CN CN202011192622.0A patent/CN112410591B/en active Active
Patent Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB792172A (en) * | 1955-11-16 | 1958-03-19 | Aluminiumwerke Nurnberg G M B | Process for refining the crystalline structure of hypereutectic aluminium-silicon alloys |
| WO1996030550A1 (en) * | 1995-03-31 | 1996-10-03 | Merck Patent Gmbh | TiB2 PARTICULATE CERAMIC REINFORCED AL-ALLOY METAL-MATRIX COMPOSITES |
| CN1632146A (en) * | 2004-12-31 | 2005-06-29 | 清华大学 | Preparation of aluminium titanium carbide intermediate alloy grain refiner in the ultrasonic field |
| CN1936044A (en) * | 2006-10-14 | 2007-03-28 | 重庆工学院 | Efficient composite modifying-refining agent for hypoeutectic cast aluminium-silicon alloy and treatment process |
| CN101591746A (en) * | 2009-03-26 | 2009-12-02 | 广州钢铁企业集团有限公司 | A kind of aluminium, aluminium alloy grain refinement and modification master alloy and preparation method thereof |
| CN101591740A (en) * | 2009-06-22 | 2009-12-02 | 济南大学 | A kind of preparation method of Al-Ti-B-C master alloy fining agent |
| CN102560200A (en) * | 2012-01-11 | 2012-07-11 | 山东大学 | Aluminum-titanium-iron-carbon-boron intermediate alloy and preparation method thereof |
| CN102787248A (en) * | 2012-08-02 | 2012-11-21 | 中原工学院 | Method for refining primary silicon of hypereutectic Al-Si alloy |
| CN105908024A (en) * | 2016-06-21 | 2016-08-31 | 上海交通大学 | High-temperature-resistant nano ceramic particle reinforced cocrystallized Al-Si alloy and casting method thereof |
| CN106756149A (en) * | 2016-12-12 | 2017-05-31 | 南京云开合金有限公司 | A kind of aluminium titanium boron carbon zirconium rare earth fining agent, its preparation method and its application |
| CN110129631A (en) * | 2019-05-24 | 2019-08-16 | 西安康博新材料科技有限公司 | A kind of internal combustion engine high-toughness heat-resistant aluminum alloy materials and preparation method thereof |
| CN111411270A (en) * | 2020-05-21 | 2020-07-14 | 滨州渤海活塞有限公司 | Method for changing morphology of ferrosilicon phase in aluminum alloy |
Non-Patent Citations (1)
| Title |
|---|
| Zr对过共晶铝硅合金中初生硅组织的影响;陈霖等;《功能材料》;20121231;第2360-2362+2368页 * |
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