CN113774240A - Method for separating hypereutectic aluminum-silicon alloy from dissimilarity during eutectic solidification - Google Patents
Method for separating hypereutectic aluminum-silicon alloy from dissimilarity during eutectic solidification Download PDFInfo
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- 230000005496 eutectics Effects 0.000 title claims abstract description 49
- 229910000676 Si alloy Inorganic materials 0.000 title claims abstract description 43
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 title claims abstract description 43
- 238000000034 method Methods 0.000 title claims abstract description 43
- 238000007711 solidification Methods 0.000 title claims abstract description 36
- 230000008023 solidification Effects 0.000 title claims abstract description 36
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 40
- 239000000956 alloy Substances 0.000 claims abstract description 40
- 238000001816 cooling Methods 0.000 claims abstract description 37
- 239000011521 glass Substances 0.000 claims abstract description 16
- 238000007872 degassing Methods 0.000 claims abstract description 10
- 239000007788 liquid Substances 0.000 claims abstract description 5
- 230000008018 melting Effects 0.000 claims description 20
- 238000002844 melting Methods 0.000 claims description 20
- 239000002994 raw material Substances 0.000 claims description 20
- 238000010438 heat treatment Methods 0.000 claims description 11
- 238000005204 segregation Methods 0.000 claims 6
- 229910001366 Hypereutectic aluminum Inorganic materials 0.000 claims 3
- 238000010521 absorption reaction Methods 0.000 claims 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract description 37
- 229910052710 silicon Inorganic materials 0.000 abstract description 37
- 239000010703 silicon Substances 0.000 abstract description 37
- 239000000155 melt Substances 0.000 abstract description 23
- 230000008569 process Effects 0.000 abstract description 14
- 238000005266 casting Methods 0.000 abstract description 11
- 238000007670 refining Methods 0.000 abstract description 8
- 230000000694 effects Effects 0.000 abstract description 6
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 239000011856 silicon-based particle Substances 0.000 abstract description 4
- 239000012535 impurity Substances 0.000 abstract description 3
- 238000010128 melt processing Methods 0.000 abstract description 3
- 238000004321 preservation Methods 0.000 abstract description 3
- 238000009827 uniform distribution Methods 0.000 abstract description 2
- 238000003723 Smelting Methods 0.000 abstract 1
- 239000008187 granular material Substances 0.000 abstract 1
- 239000000463 material Substances 0.000 description 10
- 238000005070 sampling Methods 0.000 description 10
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 7
- 230000001276 controlling effect Effects 0.000 description 7
- 239000002184 metal Substances 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 239000002245 particle Substances 0.000 description 2
- 238000007712 rapid solidification Methods 0.000 description 2
- 230000008859 change Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000010835 comparative analysis Methods 0.000 description 1
- 230000008878 coupling Effects 0.000 description 1
- 238000010168 coupling process Methods 0.000 description 1
- 238000005859 coupling reaction Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005058 metal casting Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
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- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- 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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- 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
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Abstract
The invention discloses a method for solidifying and separating hypereutectic aluminum-silicon alloy eutectic, which comprises the steps of smelting hypereutectic aluminum-silicon alloy through a resistance crucible furnace, controlling the temperature of a melt by adopting a thermocouple and a silicon controlled temperature controller, and degassing, deslagging and refining after the melt is clear. Subsequently, melt processing is carried out: and (3) powering off the resistance crucible furnace, cooling the resistance crucible furnace, electrifying when the temperature is close to the set temperature of 580-720 ℃, adjusting the power coefficient of the electric furnace, carrying out heat preservation for 10-60min, absorbing liquid by using a glass tube, and then cooling and solidifying in the air to manufacture an alloy sample. The invention has good refining effect on the primary silicon phase appearing in the hypereutectic aluminum-silicon alloy, and the primary silicon particles have small size and uniform distribution; compared with the conventional casting, the method can separate the eutectic solidification process, granulate the flaky eutectic silicon phase in the conventional casting, and provide a new process idea for improving the plasticity of the hypereutectic aluminum-silicon alloy; the invention can not introduce impurities into the melt, has low operation cost and can not cause pollution to the environment.
Description
Technical Field
The invention belongs to the technical field of metal casting, and particularly relates to a method for separating hypereutectic aluminum-silicon alloy eutectic solidification.
Background
The hypereutectic aluminum-silicon alloy has the advantages of excellent wear resistance, low thermal expansion performance, good volume stability and the like, so that the hypereutectic aluminum-silicon alloy becomes an ideal material for manufacturing key parts such as automobile internal combustion engine pistons and the like. However, the hypereutectic aluminum-silicon alloy has a significant disadvantage, and the presence of plate-shaped, five-petal star-shaped, octahedral and pyramid-shaped coarse primary silicon phases and sheet-shaped eutectic silicon formed in the cast hypereutectic aluminum-silicon alloy is easy to become a propagation channel of cracks, and becomes an important factor for limiting the improvement of the casting plasticity and toughness. The texture state seriously cracks the matrix, causes serious reduction of the plasticity of the casting, and causes limitation to the large popularization of hypereutectic aluminum-silicon alloy in the actual industrial production. In order to generalize the advantages of hypereutectic aluminum-silicon alloys themselves, it becomes important to reduce the size of primary and eutectic silicon phases, and to improve the morphology of primary and eutectic silicon and their distribution in microscopic structures.
At present, many researchers at home and abroad have conducted a lot of research on how to refine the primary silicon phase in hypereutectic aluminum-silicon alloy and change the morphology of the eutectic silicon phase. The main methods for regulating and controlling the silicon phase include semi-solid treatment, modification treatment, melt treatment, rapid solidification and the like. These methods are all capable of reducing the size of the primary silicon phase to some extent in refining the primary silicon phase, especially the rapid solidification method. However, some of the methods have high production cost and complex preparation process, and particularly the eutectic solidification process is not dissociated, so that the mechanical properties are not obviously broken through.
Disclosure of Invention
The purpose of the invention is as follows: the invention aims to provide a method for separating the eutectic solidification and dissimilation of hypereutectic aluminum-silicon alloy, which completely separates the eutectic solidification process, ensures that the size of the silicon phase particles after the dissimilation is less than 20 mu m, has round appearance and uniform distribution, and is not sharp any more.
The technical scheme is as follows: the invention relates to a method for separating eutectic solidification of hypereutectic aluminum-silicon alloy, which comprises the following steps:
(1) placing the hypereutectic aluminum-silicon alloy raw material into a resistance crucible furnace, heating to 600-650 ℃, and then preserving heat;
(2) heating the raw materials obtained in the step (1) to 750-780 ℃ for melting, and preserving heat after melting down;
(3) cooling the alloy melt obtained in the step (2) to 720-730 ℃ in a furnace, and performing degassing, deslagging and purifying treatment;
(4) continuing to preserve the heat of the alloy melt obtained in the step (3) at 720-730 ℃, then cooling, and controlling the temperature to be preserved within +/-2 ℃ of 580-720 ℃;
(5) and (4) preparing an alloy sample by a method of imbibing the alloy melt obtained in the step (4) and cooling and solidifying in air.
Further, in the step (1), the hypereutectic aluminum-silicon alloy raw material is preheated at the temperature of 250-300 ℃ for 30-35min and then placed in a resistance crucible furnace.
Further, in the step (1), the heat preservation time is 10-15 min.
Further, in the step (2), heat preservation is carried out for 30-60min after melting down.
Further, in the step (4), the alloy melt obtained in the step (3) is kept at 720-.
Further, in the step (4), the temperature is controlled within 580-.
Further, in the step (5), the liquid suction is performed through a glass tube.
Further, in the step (5), the inner diameter of the glass tube is 8-12 mm.
Further, in the step (1), the power of the resistance crucible furnace is 5-100 kW.
In the steps of the method, all materials and moulds in contact with the melt are preheated for more than 30 minutes at the preheating temperature of 250-300 ℃. Wherein all materials in contact with the melt include a strainer, a bell, a refining agent, and a mold used for casting.
Has the advantages that: compared with the prior art, the invention has the following remarkable advantages:
(1) the invention discloses a method for separating eutectic solidification and dissimilation of hypereutectic aluminum-silicon alloy, which has good effect of inhibiting the eutectic solidification coupling growth commonly occurring in hypereutectic aluminum-silicon alloy, so that the eutectic solidification process is completely dissimilated, the size of the silicon phase particles after dissimilation is less than 20 mu m, the appearance becomes round and round, the edges and corners are not clear any more, and the distribution is uniform.
(2) The invention has no flaky eutectic silicon phase, and provides an ideal process design idea for improving the plasticity of the hypereutectic aluminum-silicon alloy.
(3) In the invention, no alterant is added in the operation process, so that the serious pollution of the past method for adding the alterant to the environment is avoided, other impurities cannot be introduced into the melt, and the operation cost is low.
Drawings
FIG. 1 shows the structure of a hypereutectic Al-Si alloy obtained by taking samples of example 1, in which the melt was kept at 720 ℃ for 10 minutes and the glass tube was imbibed with liquid and then air-cooled (cooled and solidified in air);
FIG. 2 shows the structure of a hypereutectic Al-Si alloy obtained by holding the melt at 650 ℃ for 10 minutes, imbibing the glass tube and then sampling the melt by air cooling in example 2;
FIG. 3 shows the structure of a hypereutectic Al-Si alloy obtained by holding the melt at 580 ℃ for 10 minutes, imbibing the glass tube and then sampling the melt by air cooling in example 3;
FIG. 4 shows the structure of a hypereutectic Al-Si alloy obtained by direct liquid suction through a glass tube and subsequent air cooling sampling of the melt at 650 ℃ in example 4;
FIG. 5 shows the structure of a hypereutectic Al-Si alloy obtained by holding the melt at 650 ℃ for 60 minutes, imbibing the glass tube and then sampling the melt by air cooling in example 5;
FIG. 6 shows the structure of a hypereutectic Al-Si alloy obtained in a metal mold obtained by direct casting of the melt at 720 ℃ in example 6;
FIG. 7 shows the structure of a hypereutectic Al-Si alloy obtained by casting the melt of example 7 at 650 ℃ for 10 minutes in a metal mold.
Detailed Description
The technical scheme of the invention is further explained by combining the attached drawings.
By taking Al-16Si-4.2Cu-0.6Mg-0.8Fe alloy as an example (the protection scope of the invention is not limited to the alloy), the substantial connotation and the obvious effect of refining the primary silicon by the method are clarified by different examples.
Example 1
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the heat of the alloy melt obtained in the step (3) for 30 minutes at 720 ℃, and controlling the temperature within 720 +/-2 ℃ for 10 minutes by adjusting the power coefficient of an electric furnace.
(5) And (4) sucking the alloy melt obtained in the step (4) through a glass tube, and then sampling in an air cooling mode to obtain the structural state of the alloy. The solidification microstructure is shown in figure 1, the diameter value of primary silicon is 10-20 μm, the appearance is round and uniform, the eutectic solidification is completely separated, and no flaky eutectic silicon phase exists.
Example 2
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the heat of the alloy melt obtained in the step (3) for 30 minutes at 720 ℃, then cooling, and controlling the temperature to be 650 +/-2 ℃ for 10 minutes by adjusting the power coefficient of the electric furnace in the cooling process.
(5) And (4) sucking the alloy melt obtained in the step (4) through a glass tube, and then sampling in an air cooling mode to obtain the structural state of the alloy. The solidification microstructure is shown in figure 2, the diameter value of primary silicon is 10-20 μm, the appearance is round and uniform, the eutectic solidification is completely separated from dissimilation, and no flaky eutectic silicon phase exists.
Example 3
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the heat of the alloy melt obtained in the step (3) for 30 minutes at 720 ℃, then cooling, and controlling the temperature to be preserved for 10 minutes at 580 +/-2 ℃ by adjusting the power coefficient of the electric furnace in the cooling process.
(5) And (4) sucking the alloy melt obtained in the step (4) through a glass tube, and then sampling in an air cooling mode to obtain the structural state of the alloy. The solidification microstructure is shown in figure 3, the diameter value of primary silicon is 10-20 μm, the appearance is round and uniform, the eutectic solidification is completely separated, and no flaky eutectic silicon phase exists.
Example 4
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the heat of the alloy melt obtained in the step (3) for 30 minutes at 720 ℃, then cooling, and controlling the temperature to be preserved for 0 minute at 650 +/-2 ℃ by adjusting the power coefficient of the electric furnace in the cooling process.
(5) And (4) sucking the alloy melt obtained in the step (4) through a glass tube, and then sampling in an air cooling mode to obtain the structural state of the alloy. The solidification microstructure is shown in figure 4, the diameter value of primary silicon is 10-20 μm, the appearance is round and uniform, the eutectic solidification is completely separated, and no flaky eutectic silicon phase exists.
Example 5
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the heat of the alloy melt obtained in the step (3) for 30 minutes at 720 ℃, then cooling, and controlling the temperature to be 650 +/-2 ℃ for 60 minutes by adjusting the power coefficient of the electric furnace in the cooling process.
(5) And (4) sucking the alloy melt obtained in the step (4) through a glass tube, and then sampling in an air cooling mode to obtain the structural state of the alloy. The solidification microstructure is shown in figure 5, the diameter value of primary silicon is 10-20 μm, the appearance is round and uniform, the eutectic solidification is completely separated, and no flaky eutectic silicon phase exists.
Example 6
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the temperature of the alloy melt obtained in the step (3) at 720 ℃ for 30 minutes.
(5) And (4) directly pouring the alloy melt obtained in the step (4) into a metal mold, and cooling to obtain a structure state. The solidification microstructure is shown in figure 6, the diameter value of primary silicon is about 100 mu m, the appearance is sharp, the eutectic solidification is completely coupled to grow, and a plurality of coarse flaky eutectic silicon phases exist.
Example 7
(1) All materials and molds in contact with the melt need to be preheated for more than 30 minutes at the preheating temperature of 250 ℃. The hypereutectic aluminum-silicon alloy raw material is put into a resistance crucible furnace and heated to 600 ℃.
(2) Heating the raw materials obtained in the step (1) to 760 ℃ for melting, and preserving heat for 30 minutes after melting down.
(3) And (3) cooling the alloy melt obtained in the step (2) to 720 ℃ in a furnace, and carrying out degassing, deslagging and purifying treatment.
(4) And (4) preserving the temperature of the alloy melt obtained in the step (3) at 720 ℃ for 30 minutes. And then cooling, wherein the temperature is controlled within 650 +/-2 ℃ for 10 minutes by adjusting the power coefficient of the electric furnace in the cooling process.
(5) And (4) directly pouring the alloy melt obtained in the step (4) into a metal mold, and cooling to obtain a structure state. The solidification microstructure is shown in figure 7, the diameter value of primary silicon is about 100 mu m, the appearance is sharp, eutectic solidification is completely coupled to grow, and a plurality of coarse flaky eutectic silicon phases exist.
Comparative analysis of examples 1-7:
the method for solidifying and dissimilating the hypereutectic aluminum-silicon alloy eutectic can obtain better effect of refining silicon phase, eliminate common flaky eutectic silicon phase in the structure, completely dissociate the eutectic solidification, and provide an ideal process thought for improving the plasticity of the hypereutectic aluminum-silicon alloy. Examples 1 to 5 the microstructure of the alloy was obtained by direct glass tube sampling followed by air cooling after melt processing, and examples 6 and 7 were cast at a set temperature using a conventional casting and casting process, and it was found that: in the figures 1 to 5, the size of the silicon phase is obviously smaller and is within 20 mu m, the primary silicon phase becomes passivated and rounded, the whole distribution is uniform, the eutectic solidification can be completely separated from the dissimilarity, and the flaky eutectic silicon phase in the structure completely disappears. Examples 6 and 7, which employ a method of performing metal mold casting after melt processing, have found that the size of primary silicon particles is about 100 μm, the refining effect is not as good as that of fig. 1 to 5, and the primary silicon particles are not rounded and contain coarse flaky eutectic silicon phases. Therefore, in summary, the method for solidifying and dissimilating the hypereutectic aluminum-silicon alloy eutectic can achieve good refining effect, the silicon particles are small in size and uniform in distribution, the separation of flaky eutectic silicon in conventional casting can be eliminated, and an ideal process thought is provided for improving the plasticity of the hypereutectic aluminum-silicon alloy. In addition, the operation cost is low, impurities cannot be introduced in the production process, and the environment cannot be polluted.
Claims (9)
1. A method for separating the eutectic solidification of a hypereutectic aluminum-silicon alloy, comprising the steps of:
(1) placing the hypereutectic aluminum-silicon alloy raw material into a resistance crucible furnace, heating to 600-650 ℃, and then preserving heat;
(2) heating the raw materials obtained in the step (1) to 750-780 ℃ for melting, and preserving heat after melting down;
(3) cooling the alloy melt obtained in the step (2) to 720-730 ℃ in a furnace, and performing degassing, deslagging and purifying treatment;
(4) continuing to preserve the heat of the alloy melt obtained in the step (3) at 720-730 ℃, then cooling, and controlling the temperature to be preserved at 580-720 +/-2 ℃;
(5) and (4) preparing an alloy sample by a method of imbibing the alloy melt obtained in the step (4) and cooling and solidifying in air.
2. The method for separating the eutectic solidification of the hypereutectic aluminum-silicon alloy according to claim 1, wherein in the step (1), the hypereutectic aluminum-silicon alloy raw material is preheated at 300 ℃ of 250 ℃ for 30-35min and then placed in the resistance crucible furnace.
3. The method for eutectic solidification and segregation of hypereutectic aluminum silicon alloys according to claim 1, wherein in step (1), the holding time is 10-15 min.
4. The method for eutectic solidification and segregation of hypereutectic aluminum-silicon alloys according to claim 1, wherein in step (2), the temperature is maintained for 30-60min after melting down.
5. The method for eutectic solidification and segregation of hypereutectic aluminum-silicon alloys according to claim 1, wherein in step (4), the alloy melt obtained in step (3) is kept at 720-730 ℃ for 30-60 min.
6. The method for eutectic solidification and segregation of hypereutectic aluminum-silicon alloy as claimed in claim 1, wherein in the step (4), the temperature is controlled within 580-.
7. A method of eutectic solidification and segregation of hypereutectic aluminum silicon alloys according to claim 1, wherein in step (5) said liquid absorption is performed through a glass tube.
8. The method for eutectic solidification and segregation of hypereutectic aluminum silicon alloys according to claim 7, wherein in step (5), the inner diameter of the glass tube is 8-12 mm.
9. The method for dissociating the eutectic solidification of a hypereutectic aluminum-silicon alloy according to claim 1, wherein in step (1), the power of the electric resistance crucible furnace is 5-100 kW.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114643345A (en) * | 2022-02-21 | 2022-06-21 | 东南大学 | Copper pipe suction casting method for obviously refining hypereutectic aluminum-silicon alloy primary silicon particles |
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| US4969428A (en) * | 1989-04-14 | 1990-11-13 | Brunswick Corporation | Hypereutectic aluminum silicon alloy |
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| CN114643345A (en) * | 2022-02-21 | 2022-06-21 | 东南大学 | Copper pipe suction casting method for obviously refining hypereutectic aluminum-silicon alloy primary silicon particles |
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Application publication date: 20211210 |