CN116065047B - Method for refining primary silicon in Al-18Si alloy and reducing area fraction of primary silicon by utilizing antimony alloying and phosphorus modification - Google Patents
Method for refining primary silicon in Al-18Si alloy and reducing area fraction of primary silicon by utilizing antimony alloying and phosphorus modification Download PDFInfo
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- 229910052710 silicon Inorganic materials 0.000 title claims abstract description 92
- 239000010703 silicon Substances 0.000 title claims abstract description 92
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 87
- 239000000956 alloy Substances 0.000 title claims abstract description 87
- 229910052787 antimony Inorganic materials 0.000 title claims abstract description 24
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 title claims abstract description 20
- 230000004048 modification Effects 0.000 title claims abstract description 19
- 238000012986 modification Methods 0.000 title claims abstract description 19
- 238000007670 refining Methods 0.000 title claims abstract description 18
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 title claims abstract description 14
- 238000005275 alloying Methods 0.000 title claims abstract description 14
- 238000000034 method Methods 0.000 title claims abstract description 14
- 229910052698 phosphorus Inorganic materials 0.000 title claims abstract description 14
- 239000011574 phosphorus Substances 0.000 title claims abstract description 14
- 229910000676 Si alloy Inorganic materials 0.000 claims abstract description 51
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 claims abstract description 51
- 229910052751 metal Inorganic materials 0.000 claims abstract description 15
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- URRHWTYOQNLUKY-UHFFFAOYSA-N [AlH3].[P] Chemical compound [AlH3].[P] URRHWTYOQNLUKY-UHFFFAOYSA-N 0.000 abstract description 3
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- 229910021652 non-ferrous alloy Inorganic materials 0.000 abstract description 2
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- FAWGZAFXDJGWBB-UHFFFAOYSA-N antimony(3+) Chemical compound [Sb+3] FAWGZAFXDJGWBB-UHFFFAOYSA-N 0.000 abstract 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 75
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- VHHHONWQHHHLTI-UHFFFAOYSA-N hexachloroethane Chemical compound ClC(Cl)(Cl)C(Cl)(Cl)Cl VHHHONWQHHHLTI-UHFFFAOYSA-N 0.000 description 4
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Abstract
The invention belongs to the technical field of nonferrous alloy processing and forming, and discloses a method for refining primary silicon in Al-18Si alloy and reducing the area fraction of the primary silicon by utilizing antimony alloying and phosphorus modification, which melts Al-18Si hypereutectic aluminum-silicon alloy, after the alloy is completely melted, adding pure antimony into the alloy liquid, preserving heat, then adding Al-3P intermediate alloy for modification treatment, and pouring the alloy liquid into a room-temperature metal mold for molding after preserving heat. The antimony element can increase the supercooling degree of the Al-18Si alloy melt and reduce the area fraction of primary silicon; the AlP phase in the aluminum-phosphorus intermediate alloy can be used as a nucleation point of primary silicon to refine the primary silicon. When the two are cooperated, the increase of the supercooling degree of the Al-18Si alloy can reduce the nucleation critical dimension of the primary silicon, so that more AlP particles become nucleation cores of the primary silicon, and meanwhile, the growth of the primary silicon is inhibited, the primary silicon in the alloy is thinned, and the area fraction of the primary silicon is smaller.
Description
Technical Field
The invention belongs to the technical field of nonferrous alloy processing and forming, and particularly relates to a method for refining primary silicon in an Al-18Si alloy and reducing the area fraction of the primary silicon by utilizing the combined action of antimony alloying and a phosphorus modifier.
Background
The piston of the automobile engine works under the environment of high temperature, high pressure and high strength alternating load, so that the material of the piston needs to have the characteristics of high temperature strength, wear resistance, low thermal expansion coefficient and the like. The hypereutectic aluminum-silicon alloy meets the conditions and has excellent casting performance, and particularly, the linear expansion coefficient is reduced and the wear resistance is increased along with the increase of the silicon content. However, the increase of the silicon content also increases the content of primary silicon, and the primary silicon in the cast hypereutectic aluminum-silicon alloy can severely fracture the alloy matrix, reduce the toughness of the alloy, lead to matrix cracking and severely limit the application of the hypereutectic aluminum-silicon alloy. The mechanical properties of the cast aluminum alloy cannot be improved by plastic deformation, so that a method for improving the morphology of primary silicon in the structure of the cast hypereutectic aluminum-silicon alloy is always sought, and the method is convenient to explore in modification treatment, trace element alloying, spray deposition and the like, and promotes the development and application of the hypereutectic aluminum-silicon alloy.
Although there are many studies on refining primary silicon in hypereutectic aluminum-silicon alloys, the refining effect is limited. The hypereutectic aluminum-silicon alloy is modified by phosphorus element commonly used in industry, and the size of primary silicon in a tissue after phosphorus modification is greatly reduced, but the distribution is not uniform enough, the area occupation ratio of the primary silicon is increased, and the improvement of the mechanical property of the alloy is limited. The research shows that the modification treatment of boron can effectively refine the silicon phase, but the effect of refining and improving the morphology of the silicon phase has a great relationship with the addition amount. If a method for inhibiting the precipitation of primary silicon in the hypereutectic aluminum-silicon alloy (reducing the area fraction of the primary silicon) and refining the primary silicon and improving the morphology of the primary silicon can be found, the toughness of the aluminum-silicon alloy can be further increased, and the more ideal mechanical property can be obtained, so that the application field of the hypereutectic aluminum-silicon alloy is enlarged.
Disclosure of Invention
The purpose of the present invention is to promote refining of primary silicon in an Al-18Si alloy while reducing the area fraction of primary silicon and improving the morphology thereof.
In order to solve the technical problems, the invention provides a method for refining primary silicon in Al-18Si alloy and reducing the area fraction of the primary silicon by utilizing antimony alloying and phosphorus modification, which comprises the following steps:
Putting Al-18Si hypereutectic aluminum-silicon alloy into a crucible, melting at 850 ℃, adding pure antimony into the alloy liquid after the alloy is completely melted, preserving heat for 25-30 minutes, then adding Al-3P intermediate alloy for modification treatment, preserving heat for 5 minutes, and then pouring the alloy liquid into a room-temperature metal mold for molding.
Wherein the addition amount of the antimony is 0.15-0.75 wt.% of the mass of the Al-18Si hypereutectic aluminum-silicon alloy; further preferred is an antimony addition of 0.3wt.%.
Wherein the addition amount of the Al-3P intermediate alloy is 0.2wt.% to 0.6wt.% of the mass of the Al-18Si hypereutectic aluminum-silicon alloy; further preferred is an amount of 0.4wt.%.
The invention has the beneficial effects that:
The invention adopts antimony to carry out alloying on the Al-18Si alloy and adopts aluminum phosphorus intermediate alloy to carry out modification treatment on the Al-18Si alloy. The AlP phase in the aluminum-phosphorus intermediate alloy can be used as a nucleation point of primary silicon, refine the primary silicon and improve the morphology of the primary silicon. When the Al-P intermediate alloy and the antimony act cooperatively, the increase of the supercooling degree of the Al-18Si alloy can reduce the nucleation critical dimension of the primary silicon, so that more AlP particles become nucleation cores of the primary silicon, and meanwhile, the growth of the primary silicon is inhibited, the primary silicon in the alloy is thinned, and the area fraction of the primary silicon is smaller. The average size of primary silicon of the Al-18Si alloy prepared by the invention is thinned from 44.6 mu m which is not alloyed and not degenerated to 19.5 mu m, and the area ratio of the primary silicon is reduced from 10.1% to 8.4%.
Different from other refined primary silicon modes, the method is convenient to operate, low in cost, environment-friendly and pollution-free, and has important reference values in the aspects of preparing hypereutectic aluminum-silicon alloy of fine primary silicon and expanding the application field of hypereutectic aluminum-silicon alloy.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are needed in the description of the embodiments will be briefly described below, it being obvious that the drawings in the following description are only some embodiments of the present invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a photograph of a microstructure of a sample of the Al-18Si alloy of comparative example 1 at a cross section;
FIG. 2 is a photograph of a microstructure of a sample of Al-18Si-xSb alloy at a cross-section;
FIG. 3 is a photograph of a microstructure of a sample of the Al-18Si-0.2% Al-3P alloy of comparative example 3 at a cross section;
FIG. 4 is a photograph of a microstructure of a sample of the Al-18Si-0.4% Al-3P alloy of comparative example 4 at a cross section;
FIG. 5 is a photograph of a microstructure of a sample of the Al-18Si-0.6% Al-3P alloy of comparative example 5 at a cross section;
FIG. 6 is a photograph of a microstructure of a sample of the Al-18Si-0.3Sb-0.2% Al-3P alloy of example 1 at a cross section;
FIG. 7 is a photograph of a microstructure of example 2 at a cross section of an Al-18Si-0.3Sb-0.4% Al-3P alloy sample;
FIG. 8 is a photograph of a microstructure of example 3 at a cross section of an Al-18Si-0.3Sb-0.6% Al-3P alloy specimen.
Detailed Description
In order that the above-recited objects, features and advantages of the present invention will become more apparent, a more particular description of the invention will be rendered by reference to specific embodiments thereof.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, but the present invention may be practiced in other ways other than those described herein, and persons skilled in the art will readily appreciate that the present invention is not limited to the specific embodiments disclosed below.
Further, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic can be included in at least one implementation of the invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
Comparative example 1:
after the Al-18Si hypereutectic aluminum-silicon alloy is smelted and kept at 850 ℃ for 30 minutes, the alloy is poured into a metal casting mold at room temperature, and the specific operation steps are as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
after the alloy is completely melted, scraping surface scum, refining by using hexachloroethane, and preserving heat for 30 minutes, wherein a graphite rod is used for fully stirring the melt in the heat preservation process, so that uneven components are prevented;
After the heat preservation is finished, pouring the Al-18Si hypereutectic aluminum-silicon alloy melt into a room temperature metal mold with the inner cavity size phi of 12x120 mm;
The sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 1. As can be seen from FIG. 1, coarse primary silicon exists in the tissue, about 97 primary silicon particles, the morphology is mainly flaky, regular polygonal and long strip-shaped, and a small amount of primary silicon particles are in complex shapes; a large amount of alpha-Al phase is generated. The average size of the primary silicon was 44.6 μm and the primary silicon area ratio was 10.1%.
Comparative example 2:
0.3wt.% of Sb is added into the Al-18Si hypereutectic aluminum-silicon alloy, and after the alloy is smelted and insulated for 30 minutes at 850 ℃, the alloy is poured into a metal mold at room temperature, and the specific operation is as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
after the alloy is completely melted, 0.3wt.% of Sb is added for micro-alloying treatment, and after full fusion, the alloy is kept at 850 ℃ for 30 minutes;
After the heat preservation is finished, pouring the antimonated Al-18Si hypereutectic aluminum-silicon alloy into a room temperature metal mold with the inner cavity size of phi 12x120 mm;
the sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 2. Compared with fig. 1, the particle number of primary silicon is reduced to 57 particles, and the morphology is mostly regular polygons, and the morphology is improved compared with the original tissue because of a few complicated morphologies. The average size of primary silicon in the alloy increases from 44.6 mu m to 50.6 mu m, but the area ratio of primary silicon is reduced from 10.1% to 8.0%; fine but dense alpha-Al phase transitions; the eutectic structure is reduced.
FIG. 2 is a photograph of a microstructure of a sample of Al-18Si-xSb alloy at a cross-section; (a) x=0; (b) x=0.15; (c) x=0.3; (d) x=0.45; (e) x=0.6; (f) x=0.75.
TABLE 1 quantitative analysis of primary silicon in solidification structure of Al-18Si-xSb alloy
The addition amount of the Sb element is 0.15wt.% as a gradient, and the addition amount of the Sb element is 0.15wt.% to 0.75wt.% so as to carry out modification treatment on the Al-18Si hypereutectic aluminum-silicon alloy. The results of Table 1 were obtained. The area ratio and the average size of the primary silicon show a tendency to decrease first and then increase with the increase of the content of the Sb element, and it can be seen from the solidification structure diagram that when the Sb content is too high (0.6 wt.%, 0.75 wt.%) the primary silicon morphology thereof is changed into a complicated radial shape. When the content of the Sb element is 0.3wt.%, both are minimum, and the addition amount of the Sb element is selected to be 0.3wt.% of the total mass of the Al-18Si alloy.
Comparative example 3:
0.2wt.% of Al-3P is added into the Al-18Si hypereutectic aluminum-silicon alloy, and after the alloy is smelted and insulated for 30 minutes at 850 ℃, the alloy is poured into a metal mold at room temperature, and the specific operation is as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
after the alloy is completely melted, scraping surface scum, refining by using hexachloroethane, and preserving heat for 25 minutes; after the heat preservation is finished, 0.2wt.% of Al-3P is added, and after the complete fusion, the heat preservation is carried out for 5 minutes;
after the heat preservation is finished, pouring the Al-18Si hypereutectic aluminum-silicon alloy after phosphorus modification into a room temperature metal mold with the inner cavity size phi of 12x120 mm;
the sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 3. As can be seen from FIG. 3, in the solidification structure of the alloy after 0.2% Al-3P deterioration, the average size of primary silicon is not greatly reduced, the average size is 40.1 μm, the number of particles is increased to 119 particles, and the overall ratio is increased to 12.2%; the shape is mainly composed of a large number of thin strips and polygons, and a small number of petal shapes are formed; the quantity of the alpha-Al phase is reduced and becomes short rod-shaped; the eutectic structure increases and becomes fine fiber-like.
Comparative example 4:
0.4wt.% of Al-3P is added into the Al-18Si hypereutectic aluminum-silicon alloy, and after the alloy is smelted and insulated for 30 minutes at 850 ℃, the alloy is poured into a metal mold at room temperature, and the specific operation is as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
after the alloy is completely melted, scraping surface scum, refining by using hexachloroethane, and preserving heat for 25 minutes; after the heat preservation is finished, 0.4wt.% of Al-3P is added, and after the complete fusion, the heat preservation is carried out for 5 minutes;
after the heat preservation is finished, pouring the Al-18Si hypereutectic aluminum-silicon alloy after phosphorus modification into a room temperature metal mold with the inner cavity size phi of 12x120 mm;
the sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 4. Compared with fig. 1, 2 and 3, the primary silicon is thinned and increased to 230 grains, the average size is 29.2 mu m, the area ratio is 11.6%, and the morphology is mainly regular polygons; the alpha-Al phase is concentrated near the primary silicon to be separated out and is in the shape of short rod particles; the eutectic structure is fine.
Comparative example 5:
0.6wt.% of Al-3P is added into the Al-18Si hypereutectic aluminum-silicon alloy, and after the alloy is smelted and insulated for 30 minutes at 850 ℃, the alloy is poured into a metal mold at room temperature, and the specific operation is as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
After the alloy is completely melted, scraping surface scum, refining by using hexachloroethane, and preserving heat for 25 minutes; after the heat preservation is finished, 0.6wt.% of Al-3P is added, and after the complete fusion, the heat preservation is carried out for 5 minutes;
after the heat preservation is finished, pouring the Al-18Si hypereutectic aluminum-silicon alloy after phosphorus modification into a room temperature metal mold with the inner cavity size phi of 12x120 mm;
The sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 5.
The deterioration effect of adding 0.6% Al-3P was inferior to that of 0.4% Al-3P as compared with FIG. 3, but the deterioration effect was still better as compared with FIG. 1, FIG. 2 and FIG. 3. The primary silicon starts to grow larger, 142 primary silicon particles exist, the average size is 32.2 mu m, and the area ratio is 10.8%; the alpha-Al phase changes into a short pole branch crystal shape; the eutectic structure is fine.
Example 1:
The Al-18Si hypereutectic aluminum-silicon alloy is treated by adding trace element antimony and modifier phosphorus alloy, and is poured into a room temperature metal casting mould after being insulated for 30 minutes at 850 ℃, and the specific operation steps are as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
After the alloy is completely melted, 0.3wt.% of Sb is added for micro-alloying treatment, and after full fusion, the alloy is kept at 850 ℃ for 25 minutes; after the heat preservation is finished, 0.2wt.% of Al-3P is added, and after full fusion, the heat preservation is carried out for 5 minutes;
After the heat preservation is finished, pouring the antimonated Al-18Si hypereutectic aluminum-silicon alloy into a room temperature metal mold with the inner cavity size of phi 12x120 mm;
The sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 6. Compared with FIG. 3, the particle number of the primary silicon in FIG. 6 added with 0.3 percent of Sb is increased to 126 particles, the particle number of the primary silicon is not greatly increased and the size is not greatly reduced compared with the single phosphorus adding alloy, the average size is 36.9 mu m, the area occupied ratio is greatly reduced and is 7.7 percent; the primary silicon form is mainly in a regular plate shape, has no complex form, but has particles with extremely small size; the alpha-Al phase is separated out around the primary silicon phase and is in a short rod branch crystal shape; the eutectic structure is fine.
Example 2:
treating the Al-18Si hypereutectic aluminum-silicon alloy by adding trace element antimony and modifier phosphorus alloy, and pouring the Al-18Si hypereutectic aluminum-silicon alloy into a room temperature metal casting mold after heat preservation for 30 minutes at 850 ℃, wherein the specific operation steps are as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
after the alloy is completely melted, 0.3wt.% of Sb is added for micro-alloying treatment, and after full fusion, the alloy is kept at 850 ℃ for 25 minutes; after the heat preservation is finished, 0.4wt.% of Al-3P is added, and after the mixture is fully fused, the heat preservation is carried out for 5 minutes;
After the heat preservation is finished, pouring the antimonated Al-18Si hypereutectic aluminum-silicon alloy into a room temperature metal mold with the inner cavity size of phi 12x120 mm;
The sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 7.
When the Al-3P alloy is not added in the comparative example 2, the Sb element eliminates the non-spontaneous nucleation substrate in the hypereutectic aluminum-silicon alloy, and the phenomenon of 'reduced nucleation number and increased average size' occurs; in the embodiment 2, after Al-3P alloy is added, a large amount of AlP is generated in the melt, and the AlP is the core of heterogeneous nucleation, so that the supercooling degree is increased, the critical size of nucleation is reduced, more particles conform to the nucleation condition, obvious silicon-poor phenomenon appears around the particles, the growth of primary silicon is inhibited, the synergistic effect between Sb and Al-3P is achieved, and the morphology, the quantity and the ratio of the primary silicon are improved after the Sb element is added.
Compared with fig. 4, fig. 7, to which 0.3% sb was added, the primary silicon was finer and more uniform, the average size was 19.5 μm, the particle count was increased to 370 particles, and the area ratio was reduced to 8.4%; the morphology of the primary silicon is regular polygons, and part of the primary silicon is five-pointed star-shaped; the alpha-Al phase is distributed near the primary silicon, so that the quantity is increased; the eutectic structure is finer.
Al-3P is used for generating AlP when being modified, and AlP becomes a nucleation substrate of primary silicon in the solidification process, so that the primary silicon is refined; the primary crystal silicon has uniform morphology, regular polyhedron, smooth edges and corners, increased number, small size, average size of about 30 μm and uneven distribution. After Sb is added, the supercooling degree of Al-18Si is increased due to the Sb element, so that the critical size of nucleation particles is reduced, more particles meet the nucleation conditions, the number of primary silicon is increased, the silicon concentration in a surrounding matrix is reduced, the growth of primary silicon is limited, and the size is smaller; the reduction in silicon concentration promotes the growth of the alpha-Al phase, and thus the alpha-Al phase increases.
The primary silicon phase with fine edges and smooth corners greatly improves the performance of the hypereutectic aluminum-silicon alloy, and has important value in the aspect of increasing the application prospect.
Example 3:
treating the Al-18Si hypereutectic aluminum-silicon alloy by adding trace element antimony and modifier phosphorus alloy, and pouring the Al-18Si hypereutectic aluminum-silicon alloy into a room temperature metal casting mold after heat preservation for 30 minutes at 850 ℃, wherein the specific operation steps are as follows:
Smelting Al-18Si hypereutectic aluminum-silicon alloy in a well-type resistance furnace by adopting a graphite crucible, wherein the smelting temperature is 850 ℃;
After the alloy is completely melted, 0.3wt.% of Sb is added for micro-alloying treatment, and after full fusion, the alloy is kept at 850 ℃ for 25 minutes; after the heat preservation is finished, 0.6wt.% of Al-3P is added, and after the mixture is fully fused, the heat preservation is carried out for 5 minutes;
After the heat preservation is finished, pouring the antimonated Al-18Si hypereutectic aluminum-silicon alloy into a room temperature metal mold with the inner cavity size of phi 12x120 mm;
The sample was taken at a distance of 10mm from the bottom, a metallographic phase was prepared, and the microstructure of the alloy was observed using a metallographic microscope, and a photograph of the metallographic phase was shown in FIG. 8. Compared with Al-18Si (FIG. 5) added with 0.6% Al-3P only, in the microstructure of Al-18Si added with 0.6% Al-3P and 0.3% Sb, the primary silicon is finer and has more particles, 293 particles, an average size of 26.8 μm and an area ratio of 8.9%; the shape is basically a regular polygonal plate shape, and no complex shape exists; the distribution is more uniform; alpha-Al is increased to a certain extent; the eutectic structure is fine.
As can be seen from the above illustration, the addition of Sb and Al-3P can inhibit primary silicon growth in hypereutectic aluminum-silicon alloys. The best effect is obtained when the Al-3P addition reaches 0.4% under the condition that the Sb addition is 0.3%, the average size of primary silicon is thinned from 44.553 mu m before deterioration to 19.519 mu m, and the area occupation ratio is increased although the primary silicon size is reduced when only Al-3P is deteriorated; when Al-3P is less than 0.4%, the average size variation amplitude is small and the morphology becomes more complicated although the area fraction of primary silicon is reduced; and when the content is more than 0.4%, the effect is reduced as the average size of the primary silicon and the area fraction of the primary silicon are both larger than 0.4% of the deterioration result of Al-3P.
The invention adopts trace antimony and trace phosphorus alloy to carry out compound modification treatment on the Al-18Si alloy, adds trace phosphorus alloy to increase nucleation points in the Al-18Si alloy to promote heterogeneous nucleation, and adds trace element Sb to increase supercooling degree of the Al-18Si alloy, reduce critical dimension of nucleation, and enable mass nucleation during solidification, thereby reducing silicon concentration in a matrix and inhibiting growth of primary silicon, and further refining primary silicon phase.
It should be noted that the above embodiments are only for illustrating the technical solution of the present invention and not for limiting the same, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that the technical solution of the present invention may be modified or substituted without departing from the spirit and scope of the technical solution of the present invention, which is intended to be covered in the scope of the claims of the present invention.
Claims (3)
1. A method for refining primary silicon in Al-18Si alloy and reducing the area fraction of the primary silicon by utilizing antimony alloying and phosphorus modification is characterized in that: melting Al-18Si hypereutectic aluminum-silicon alloy, adding pure antimony into the alloy liquid after the alloy is completely melted, preserving heat, adding Al-3P intermediate alloy for modification treatment, preserving heat, and pouring the alloy liquid into a room-temperature metal mold for molding; the addition amount of the Al-3P intermediate alloy is 0.2wt.% to 0.6 wt wt.% of the Al-18Si hypereutectic aluminum-silicon alloy; the addition amount of the antimony is 0.3wt.% of the total mass of the Al-18Si hypereutectic aluminum-silicon alloy.
2. The method for refining primary silicon and reducing the area fraction of primary silicon in an Al-18Si alloy by using antimony alloying and phosphorus modification according to claim 1, wherein: the addition amount of the Al-3P intermediate alloy is 0.4 wt percent of the mass of the Al-18Si hypereutectic aluminum-silicon alloy.
3. The method for refining primary silicon and reducing the area fraction of primary silicon in an Al-18Si alloy by using antimony alloying and phosphorus modification according to claim 1, wherein: the melting temperature of the Al-18Si hypereutectic aluminum-silicon alloy is 850 ℃.
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| CN101503773A (en) * | 2009-03-11 | 2009-08-12 | 华中科技大学 | Heat resisting low expansion silumin and preparation thereof |
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