CN111411270A - Method for changing morphology of ferrosilicon phase in aluminum alloy - Google Patents
Method for changing morphology of ferrosilicon phase in aluminum alloy Download PDFInfo
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- CN111411270A CN111411270A CN202010434279.XA CN202010434279A CN111411270A CN 111411270 A CN111411270 A CN 111411270A CN 202010434279 A CN202010434279 A CN 202010434279A CN 111411270 A CN111411270 A CN 111411270A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 38
- 229910000519 Ferrosilicon Inorganic materials 0.000 title claims abstract description 28
- 238000000034 method Methods 0.000 title claims abstract description 25
- 239000000956 alloy Substances 0.000 claims abstract description 51
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 48
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 22
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 21
- 238000007670 refining Methods 0.000 claims abstract description 19
- 238000007872 degassing Methods 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims abstract description 7
- 229910018575 Al—Ti Inorganic materials 0.000 claims abstract description 4
- 229910001339 C alloy Inorganic materials 0.000 claims abstract description 4
- 229910018619 Si-Fe Inorganic materials 0.000 claims abstract description 3
- 229910008289 Si—Fe Inorganic materials 0.000 claims abstract description 3
- 239000003795 chemical substances by application Substances 0.000 claims description 25
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 12
- 238000002844 melting Methods 0.000 claims description 11
- 230000008018 melting Effects 0.000 claims description 11
- 229910052786 argon Inorganic materials 0.000 claims description 6
- 229910000521 B alloy Inorganic materials 0.000 claims description 3
- 239000007788 liquid Substances 0.000 claims description 3
- 239000000919 ceramic Substances 0.000 abstract description 13
- 239000002245 particle Substances 0.000 abstract description 13
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 abstract description 12
- 229910000676 Si alloy Inorganic materials 0.000 abstract description 11
- 238000005266 casting Methods 0.000 abstract description 8
- 230000000694 effects Effects 0.000 abstract description 6
- 238000011065 in-situ storage Methods 0.000 abstract description 6
- 239000011159 matrix material Substances 0.000 abstract description 5
- 238000001816 cooling Methods 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 28
- 239000000463 material Substances 0.000 description 15
- 229910005347 FeSi Inorganic materials 0.000 description 12
- 229910052742 iron Inorganic materials 0.000 description 9
- 229910052710 silicon Inorganic materials 0.000 description 6
- 229910001610 cryolite Inorganic materials 0.000 description 5
- XWHPIFXRKKHEKR-UHFFFAOYSA-N iron silicon Chemical compound [Si].[Fe] XWHPIFXRKKHEKR-UHFFFAOYSA-N 0.000 description 5
- 230000035553 feeding performance Effects 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- 238000007546 Brinell hardness test Methods 0.000 description 1
- -1 Cu and Ni Chemical class 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 150000002505 iron Chemical class 0.000 description 1
- 238000011031 large-scale manufacturing process Methods 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000010907 mechanical stirring Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 239000012758 reinforcing additive Substances 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- VWDWKYIASSYTQR-UHFFFAOYSA-N sodium nitrate Inorganic materials [Na+].[O-][N+]([O-])=O VWDWKYIASSYTQR-UHFFFAOYSA-N 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention discloses a method for changing the morphology of ferrosilicon phase in aluminum alloy, which comprises the steps of firstly adding aluminum ingot and Si-Fe intermediate alloy to melt, adding Al-Ti and Al-B, Al-C alloy at 750 ℃ and 950 ℃, heating to 1300 ℃ and 1500 ℃ after covering, preserving heat for 15-20min, rapidly cooling to 700 ℃ and 900 ℃, removing the covering, refining, degassing and casting to obtain the aluminum alloy, wherein the invention generates high-activity TiBC/TiC submicron ceramic in the alloy by an in-situ reaction method, and the β -Al5FeSi phase and-Al 4FeSi phase in a matrix can be modified by using the ceramic particles to be converted into a granular or fine block morphology principle, so that the obtained aluminum-silicon alloy has good casting shrinkage-supplementing performance and the alloy strength and wear resistance are improved.
Description
Technical Field
The invention relates to the field of aluminum alloy and preparation thereof, in particular to a method for changing the morphology of a silicon-iron phase in aluminum alloy (aluminum-silicon alloy).
Background
The aluminum-silicon alloy has the advantages of light weight, quick heat dissipation, good wear resistance and the like, but the strength of the aluminum-silicon alloy is not high, if the strength and the wear resistance of the material are further improved on the basis of the aluminum-silicon alloy, the content of silicon needs to be continuously increased or other elements, such as Cu, Ni, Mg, Fe and the like, need to be added into the alloy, wherein the content of the Fe element is strictly controlled below 1 percent in the using process, and β -Al is easily formed in a matrix once the content of the Fe element is overhigh5FeSi phase and-Al4The FeSi phases are in a coarse needle-shaped appearance and influence the feeding performance of alloy casting, and the phases exist in the grain boundary of alloy micro-casting, are not uniformly distributed, have a cutting effect on the matrix of the alloy and influence the strength performance of the alloy. However, these ferrosilicon phases generally have high hardness and high melting point, and if the morphology of the ferrosilicon phase can be changed and the acicular shape can be eliminated, the ferrosilicon phase is used as a reinforcing phase, so that the heat resistance and strength of the alloy can be improved, and the ferrosilicon phase has good economical efficiency for metals such as Cu and Ni, so that the cost of the material can be reduced, and thus the application range of the aluminum alloy is expanded.
Patent CN108893662A discloses a high-wear-resistance regenerated aluminum alloy and a preparation method and application thereof, wherein the content of Fe is 1.2-5%, elements such as Mn, B and RE are adopted to improve the form of an iron phase, Mn replaces Fe to form a replacement solid solution, a needle-shaped iron phase in the regenerated aluminum is eliminated, and then B and rare earth elements are used to inhibit and refine a ferrosilicon phase. Patent CN107385257A discloses a method for modifying an iron-rich phase of a regenerated aluminum alloy, which adopts W element and Fe to form a replacement solid solution, changes the growth orientation of the silicon-iron phase, reduces the harm of Fe element enrichment, and then refines the silicon-iron phase through violent stirring. In the prior art, the research on the silicon-iron phase of the aluminum alloy mainly focuses on two aspects, firstly, the influence of needle-shaped silicon iron on the alloy performance is eliminated by adding elements to neutralize Fe element, but the method can only eliminate adverse influence and cannot be used as reinforcing additive, and the method is only suitable for the aluminum alloy with the Fe content of less than 5%; and secondly, the ferrosilicon phase is refined by mechanical stirring, so that the influence of the coarse acicular ferrosilicon on the alloy performance is eliminated, but the method has more complex process and high requirement on equipment.
Disclosure of Invention
The invention generates high-activity TiBC/TiC submicron ceramics in the alloy by an in-situ reaction method, and can be used for β -Al in a matrix by using the ceramic particles5FeSi phase and-Al4The modification treatment of the FeSi phase is carried out to convert the FeSi phase into a granular or fine massive shape, and the aluminum-silicon alloy has good casting feeding performance and simultaneously improves the alloy strength and the wear resistance by adjusting the proportion of the TiBC/TiC submicron ceramic to the iron element.
The technical scheme of the invention is as follows: a method for changing the morphology of a ferrosilicon phase in an aluminum alloy is characterized in that the method controls the components in the aluminum alloy material of a product: 15-25% of Si, 5-12% of Fe, (Ti + B + C) 5-7% of Al in balance; the method specifically comprises the following steps:
(1) starting the intermediate frequency furnace, adding aluminum ingots, adding Si-Fe intermediate alloy after melting, and controlling the temperature at 750-950 ℃ after all the intermediate frequency furnace is melted;
(2) adding Al-Ti alloy, Al-B alloy and Al-C alloy according to the proportion, and then adding a covering agent on the surface of the aluminum liquid;
(3) rapidly heating to 1300 ℃ and 1500 ℃, and preserving the heat for 15-20 min;
(4) after the temperature is rapidly reduced to 700-900 ℃, the covering agent is removed;
(5) adding an aluminum alloy refining agent, introducing argon, refining and degassing for 8-15 minutes, and skimming dross;
(6) and standing, and pouring molten alloy aluminum into a preheated mold to obtain the granular or fine massive ferrosilicon phase reinforced aluminum alloy.
The covering agent can be covering agent such as cryolite: the aluminum alloy refining agent is a commercially available aluminum alloy refining agent, and preferably, the main component is NaNO3The aluminum alloy refining agent is used in an amount of 0.5-3kg/500 kg.
Preferably, in the step (2), the ratio is the ratio of Al-Ti alloy, Al-B alloy and Al-C alloy to the contents of Si and Fe, and the ratio range is as follows: 15-25% of Si, 5-12% of Fe and 5-7% of (Ti + B + C).
Preferably, in the step (2), the molar ratio of Ti, B and C is controlled to be 2:2: 1.
Preferably, in the step (3), the temperature is raised to 1300-1500 ℃, and the temperature is maintained for 15-20min, so that the in-situ reaction in the melt can be fully performed, and the high-activity TiBC/TiC submicron ceramic particles can be obtained in the microstructure.
Preferably, in the step (3), the rapid temperature rise refers to a temperature rise from 750-950 ℃ to 1300-1500 ℃ within 20 minutes.
Preferably, in the step (4), the rapid temperature reduction refers to a reduction from 1300-1500 ℃ to 700-900 ℃ within 2 minutes. The rapid cooling is to prevent the aggregation and growth of the TiBC/TiC submicron ceramic particles, and to enable the ceramic particles to be uniformly distributed in the aluminum liquid, so as to achieve the purpose of treating the ferrosilicon phase transition.
Preferably, in the step (6), the ferrosilicon phase is granular or fine massive ferrosilicon phase obtained by the above steps.
The content of Fe in the aluminum-silicon alloy is 5-12%, and a large amount of coarse acicular β -Al is formed in the microstructure of the material before modification treatment5FeSi phase and coarse flaky-Al4FeSi phase (see figure 1). Then, by utilizing the principle of in-situ reaction, the prepared material contains high-activity TiBC/TiC submicron ceramic particles (figure 2), and part of the high-activity submicron ceramic particles serve as crystal nuclei to become a ferrosilicon phase solidification core in the process of solidifying the material; part of the particles are enriched around the ferrosilicon phase to prevent the ferrosilicon phase from growing (see the attached figure 3), and based on the above principle, the proportion of the TiBC/TiC particles in the material to the iron element can be adjustedEffectively make coarse acicular β -Al in the microstructure of the aluminum-silicon alloy5FeSi phase and flaky-Al4The FeSi phase is completely converted into a granular or fine massive ferrosilicon phase with the size of about 40 mu m (see attached figure 4), so that the material has good casting feeding performance; meanwhile, as the coarse structure of the cutting matrix is eliminated, the microstructure of the material is more uniform, the tensile strength and the wear resistance of the material are obviously improved, and the material is suitable for large-scale production and application of parts.
The aluminum-silicon alloy can be used for gravity casting and pressure casting, and is suitable for producing engine wear-resistant parts such as pistons, cylinder sleeves and the like. After T6 treatment, the normal temperature tensile strength is more than 300MPa, the friction coefficient is lower than 0.1, the elongation reaches 0.8%, and the hardness is more than or equal to 190 HBW.
Drawings
FIG. 1 shows coarse acicular β -Al in the microstructure of the Al-Si alloy of the present invention before in-situ reaction5FeSi phase and coarse flaky-Al4Scanning a FeSi phase SEM picture;
FIG. 2 is an SEM scanning picture of TiBC/TiC ceramic particles generated by in-situ reaction in the present invention (the light color is TiC ceramic particles, and the dark color is TiBC particles);
FIG. 3 shows the fine block β -Al of the TiBC/TiC ceramic particles in the present invention5SEM scanning pictures distributed in the FeSi phase crystal and on the interface;
fig. 4 is a SEM scan of the particulate and fine bulk ferrosilicon phase in the aluminum silicon alloy of the present invention.
Detailed Description
Four preferred examples are given below, in which the aluminum alloy refining agent used is NaNO as the main component3The aluminum alloy refining agent is used in an amount of 0.5-3kg/500 kg.
Example 1:
(1) adding an aluminum ingot into an intermediate frequency furnace, adding 60Si-Fe intermediate alloy after melting, and controlling the temperature to be 800 ℃ after completely melting;
(2) adding Al-10Ti alloy, Al-5B alloy and Al-0.5C alloy, then adding cryolite covering agent on the surface of the molten aluminum, controlling the molar ratio of Ti, B and C to be 2:2:1, and controlling the content of (Ti + B + C) in the alloy components: 5%, Si: 15%, Fe: 5.5 percent, and the balance of Al;
(3) heating to 1300 deg.C, and maintaining the temperature for 20 min;
(4) after the temperature is rapidly reduced to 700 ℃, the covering agent is removed;
(5) adding an aluminum alloy refining agent, introducing argon, refining and degassing for 10 minutes, and skimming dross;
(6) and after standing for 5 minutes, pouring the molten alloy aluminum into a preheated mold to obtain the granular or fine massive ferrosilicon phase reinforced aluminum alloy.
The performance index of the alloy after T6 treatment is shown in the following 1.
Example 2:
(1) adding an aluminum ingot into an intermediate frequency furnace, adding 70Si-Fe intermediate alloy after melting, and controlling the temperature to be 800 ℃ after completely melting;
(2) adding Al-10Ti alloy, Al-10B alloy and Al-0.5C alloy, then adding cryolite covering agent on the surface of the molten aluminum, controlling the molar ratio of Ti, B and C to be 2:2:1, and controlling the content of (Ti + B + C) in the alloy components: 6%, Si: 18.5%, Fe: 7.4 percent, and the balance of Al;
(3) heating to 1400 deg.C, and maintaining the temperature for 18 min;
(4) after the temperature is rapidly reduced to 750 ℃, the covering agent is removed;
(5) adding an aluminum alloy refining agent, introducing argon, refining and degassing for 10 minutes, and skimming dross;
(6) and after standing for 5 minutes, pouring the molten alloy aluminum into a preheated mold to obtain the granular or fine massive ferrosilicon phase reinforced aluminum alloy.
The performance index of the alloy after T6 treatment is shown in the following 1.
Example 3:
(1) adding an aluminum ingot into an intermediate frequency furnace, adding 80Si-Fe intermediate alloy after melting, and controlling the temperature to be 850 ℃ after completely melting;
(2) adding Al-15Ti alloy, Al-5B alloy and Al-1C alloy, then adding cryolite covering agent on the surface of the molten aluminum, controlling the molar ratio of Ti, B and C to be 2:2:1, and controlling the content of (Ti + B + C) in the alloy components: 6.5%, Si: 21.8%, Fe: 9.3 percent of Al;
(3) heating to 1450 deg.C, and maintaining the temperature for 16 min;
(4) after the temperature is rapidly reduced to 800 ℃, the covering agent is removed;
(5) adding an aluminum alloy refining agent, introducing argon, refining and degassing for 12 minutes, and skimming dross;
(6) and after standing for 5 minutes, pouring the molten alloy aluminum into a preheated mold to obtain the granular or fine massive ferrosilicon phase reinforced aluminum alloy.
The performance index of the alloy after T6 treatment is shown in the following 1.
Example 4:
(1) adding an aluminum ingot into an intermediate frequency furnace, adding 80Si-Fe intermediate alloy after melting, and controlling the temperature to be 850 ℃ after completely melting;
(2) adding Al-15Ti alloy, Al-10B alloy and Al-1C alloy, then adding cryolite covering agent on the surface of the molten aluminum, controlling the molar ratio of Ti, B and C to be 2:2:1, and controlling the content of (Ti + B + C) in the alloy components: 7%, Si: 23.8%, Fe: 11.2 percent and the balance of Al;
(3) heating to 1500 ℃, and keeping the temperature for 15 min;
(4) after the temperature is rapidly reduced to 850 ℃, the covering agent is removed;
(5) adding an aluminum alloy refining agent, introducing argon, refining and degassing for 15 minutes, and skimming dross;
(6) and after standing for 5 minutes, pouring the molten alloy aluminum into a preheated mold to obtain the granular or fine massive ferrosilicon phase reinforced aluminum alloy.
The performance index of the alloy after T6 treatment is shown in the following 1.
The materials prepared in the embodiments 1-4 of the invention are compared with the existing aluminum-silicon alloy Z L109 commonly used for pistons, after the two materials are treated by T6, the two materials are tested according to the standards of GB/T228.1-2010 metal material tensile test method, GB/T231.1 metal material Brinell hardness test, GB/T12444-2006 metal material abrasion test method-test ring-test block sliding abrasion test, and the material properties are shown in Table 1, and as can be seen from Table 1, the aluminum-silicon alloy of the invention has high strength and hardness, excellent high temperature performance, improved strength and improved heat resistance.
TABLE 1 comparison of Material Property data
Claims (8)
1. A method for changing the morphology of a ferrosilicon phase in an aluminum alloy is characterized in that the method controls the components in the aluminum alloy material of a product: 15-25% of Si, 5-12% of Fe, (Ti + B + C) 5-7% of Al in balance; the method specifically comprises the following steps:
(1) starting the intermediate frequency furnace, adding aluminum ingots, adding Si-Fe intermediate alloy after melting, and controlling the temperature at 750-950 ℃ after all the intermediate frequency furnace is melted;
(2) adding Al-Ti alloy, Al-B alloy and Al-C alloy according to the proportion, and then adding a covering agent on the surface of the aluminum liquid;
(3) rapidly heating to 1300 ℃ and 1500 ℃, and preserving the heat for 15-20 min;
(4) after the temperature is rapidly reduced to 700-900 ℃, the covering agent is removed;
(5) adding an aluminum alloy refining agent, introducing argon, refining, degassing and removing scum;
(6) and standing, and pouring molten alloy aluminum into a preheated mold to obtain the granular or fine massive ferrosilicon phase reinforced aluminum alloy.
2. The method for changing the morphology of the ferrosilicon phase in the aluminum alloy as claimed in claim 1, wherein in the step (2), the molar ratio of Ti, B and C is controlled to be 2:2: 1.
3. The method as claimed in claim 1, wherein the rapid temperature increase in step (3) is from 750-950 ℃ to 1300-1500 ℃ within 20 minutes.
4. The method as claimed in claim 1, wherein the rapid temperature decrease in step (4) is from 1300-1500 ℃ to 700-900 ℃ within 2 minutes.
5. The method for changing the morphology of the ferrosilicon phase in the aluminum alloy as claimed in claim 1, wherein in the step (5), refining degassing is performed for 8 to 15 minutes.
6. An aluminum alloy produced by the method of any one of claims 1 to 5.
7. The aluminum alloy as recited in claim 6, wherein the aluminum alloy has a room temperature tensile strength of >300MPa, a coefficient of friction of less than 0.1, an elongation of 0.8% or more, and a hardness of 190HBW or more.
8. Use of the aluminum alloy of claim 6 in pistons, cylinder liners and other engine wear parts.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112410591A (en) * | 2020-10-30 | 2021-02-26 | 滨州渤海活塞有限公司 | Super-long-effect double-modification method for hypereutectic aluminum-silicon alloy |
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|---|---|---|---|---|
| JPH036344A (en) * | 1989-06-01 | 1991-01-11 | Sumitomo Light Metal Ind Ltd | Aluminum alloy having heat resistance and wear resistance |
| US20050163647A1 (en) * | 2003-05-02 | 2005-07-28 | Donahue Raymond J. | Aluminum-silicon alloy having reduced microporosity |
| US20110168451A1 (en) * | 2010-01-13 | 2011-07-14 | Baker Hughes Incorporated | Boron Aluminum Magnesium Coating for Earth-Boring Bit |
| CN107502791A (en) * | 2017-09-01 | 2017-12-22 | 宁国市润丰金属制品有限公司 | A kind of casting technique of high-strength aluminum alloy wheel hub |
| CN107955888A (en) * | 2017-06-12 | 2018-04-24 | 吉林大学 | A kind of micro-nano TiC-TiB for aluminium alloy2Grain refiner and thinning method |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH036344A (en) * | 1989-06-01 | 1991-01-11 | Sumitomo Light Metal Ind Ltd | Aluminum alloy having heat resistance and wear resistance |
| US20050163647A1 (en) * | 2003-05-02 | 2005-07-28 | Donahue Raymond J. | Aluminum-silicon alloy having reduced microporosity |
| US20110168451A1 (en) * | 2010-01-13 | 2011-07-14 | Baker Hughes Incorporated | Boron Aluminum Magnesium Coating for Earth-Boring Bit |
| CN107955888A (en) * | 2017-06-12 | 2018-04-24 | 吉林大学 | A kind of micro-nano TiC-TiB for aluminium alloy2Grain refiner and thinning method |
| CN107502791A (en) * | 2017-09-01 | 2017-12-22 | 宁国市润丰金属制品有限公司 | A kind of casting technique of high-strength aluminum alloy wheel hub |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112410591A (en) * | 2020-10-30 | 2021-02-26 | 滨州渤海活塞有限公司 | Super-long-effect double-modification method for hypereutectic aluminum-silicon alloy |
| CN112410591B (en) * | 2020-10-30 | 2022-03-04 | 滨州渤海活塞有限公司 | Super-long-effect double-modification method for hypereutectic aluminum-silicon alloy |
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Denomination of invention: A Method for Changing the Morphology of Silicon Iron Phase in Aluminum Alloy Granted publication date: 20210319 Pledgee: Binzhou branch of China CITIC Bank Co.,Ltd. Pledgor: BINZHOU BOHAI PISTON Co.,Ltd. Registration number: Y2024980014544 |