CN101058855A - Microstructure thinning process for hypereutectic aluminum alloy - Google Patents
Microstructure thinning process for hypereutectic aluminum alloy Download PDFInfo
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- CN101058855A CN101058855A CN 200710099824 CN200710099824A CN101058855A CN 101058855 A CN101058855 A CN 101058855A CN 200710099824 CN200710099824 CN 200710099824 CN 200710099824 A CN200710099824 A CN 200710099824A CN 101058855 A CN101058855 A CN 101058855A
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Abstract
The invention discloses a hypereutectic Si-Al alloy microscopic structure finely-disintegrated technique method relating to a metallic material, which comprises the following steps: (1) adding the Ti crystal particle finely-disintegrated solvent of the fondant mass 0. 1% and mixing until completely melting; (2) adding P alterant to the solution, mixing uniformly, finely disintegrating the primary Si crystalline and ingot casting; (3) annealing the ingot casting at 500-520 DEG C, or annealing the ingot casting at 500-535 DEG C after hot extruding the ingot casting at 480 DEG C. The invention gets the structure finer and more uniform, which is a good strength for extension and a steady size.
Description
Technical field
A kind of microstructure thinning process of transcocrystallized Al-Si alloy relates to a kind of processing method of microstructure thinning of metallic substance.
Technical background
Silicone content in the hypereutectic type aluminum silicon alloy is compared with cocrystallized Al-Si alloy generally up to 16%～26%, has the silicon of solid solution in the alloy, and this silicon is present in the matrix with the primary silicon form, can improve the wear resistance and the resistance toheat of material greatly.Simultaneously, along with silicone content increases, density, the linear expansivity of alloy reduce, so this alloy is the ideal piston material.
Yet because the transcocrystallized Al-Si alloy as-cast structure is by thick strip or needle-like Eutectic Silicon in Al-Si Cast Alloys phase and thick polygonal shape and the starlike primary silicon phase composite of five lobes, this tissue makes the mechanical property and the machinability severe exacerbation of material, if handle without refinement is rotten, this alloy can not be in the industrial application that obtains reality.
At present, domestic transcocrystallized Al-Si alloy microstructure thinning technology commonly used is handled as-cast structure for adopting compound modifier to go bad, the compound modifier that adopts comprises: phosphorus-RE multiple modification, sulphur-RE multiple modification, phosphorus-sulphur-RE multiple modification etc.Composite inoculating is refined cast structure to a certain extent, but the tissue of gained does not generally reach the technical requirements of forging stock with material.
Summary of the invention
The objective of the invention is deficiency, a kind of microstructure thinning process that can satisfy forging stock with transcocrystallized Al-Si alloy is provided at above-mentioned prior art existence.
The objective of the invention is to be achieved through the following technical solutions.
A kind of microstructure thinning process of transcocrystallized Al-Si alloy is characterized in that the mass percentage content of silicon in the aluminum silicon alloy that this technology relates to is 16%-20%; The process for refining step comprises:
(1) in the fused transcocrystallized Al-Si alloy, adds the titaniferous grain-refining agent, be stirred to fusing fully;
(2) in liquation, add Phosphorus alterant then and stir refinement primary silicon, ingot casting;
(3) ingot casting of step 2 is heat-treated at 500-520 ℃, or the ingot casting of step 2 is heat-treated 480 ℃ of hot extrusions and then at 500-535 ℃.
The microstructure thinning process of a kind of transcocrystallized Al-Si alloy of the present invention is characterized in that the titaniferous grain-refining agent that adds to the fused transcocrystallized Al-Si alloy is aluminium titanium boron or aluminium titanium carbon master alloy; Add-on is a melt quality 0.1%;
The microstructure thinning process of a kind of transcocrystallized Al-Si alloy of the present invention is characterized in that Phosphorus alterant is the mixture of red phosphorus, aluminium powder and/or flux potassium fluotitanate.
The microstructure thinning process of a kind of transcocrystallized Al-Si alloy of the present invention is characterized in that Phosphorus alterant is the master alloy that contains the aluminium phosphide nucleus in advance.
The microstructure thinning process of a kind of transcocrystallized Al-Si alloy of the present invention, it is characterized in that the processing condition that phosphorus modification adopts are: the P add-on is the 0.03%-0.2% of melt quality; Deterroration is 720 ℃-830 ℃; Deteriorating time is 20-30 minute; Pouring temperature is 730 ℃-830 ℃.Best modification process condition is: best P add-on is 0.05% of a melt quality; Best deterroration is 800 ℃; Deteriorating time is 20-30 minute; Best pouring temperature is 800 ℃.
The microstructure thinning process of transcocrystallized Al-Si alloy of the present invention; adopt phosphorus modification primary silicon linkage heat to handle and hot extrusion refining eutectic silicon; organizing of gained is more tiny and even; the primary silicon average grain size is about 13 μ m; the whole granulations of Eutectic Silicon in Al-Si Cast Alloys, the gained tissue has higher tensile strength, hardness and dimensional stability.Extruding+T6 ((500 ℃, 3h) shrend, the tensile strength that (200 ℃, 6h) timeliness) handle the back material reaches 414.7MPa, and hardness (HV) is 156 (HB is 148), and unit elongation is 0.5%.
Description of drawings
The A390 alloy that Fig. 1 adopts method of the present invention through 800 ℃ rotten 30 minutes, 800 ℃ of cast, ingot casting is through 480 ℃ of hot extrusion deformations and 520 ℃, the metallographic structure photo after the 3h thermal treatment;
The A390 alloy that Fig. 2 adopts method of the present invention through 800 ℃ rotten 30 minutes, 800 ℃ of cast, ingot casting is through 535 ℃, the metallographic structure photo after the 3h thermal treatment;
The A390 alloy that Fig. 3 adopts method of the present invention through 800 ℃ rotten 30 minutes, 800 ℃ of cast, ingot casting is through 480 ℃ of hot extrusion deformations and 500, the metallographic structure photo after the 3h thermal treatment.
Embodiment
A kind of microstructure thinning process of transcocrystallized Al-Si alloy, the mass percentage content of silicon is 16%-20% in the aluminum silicon alloy that this technology relates to.The microstructure thinning technology of related transcocrystallized Al-Si alloy may further comprise the steps: (1) according to chemical composition prepares transcocrystallized Al-Si alloy.(2) the titaniferous grain-refining agent of adding 0.1% melt quality (melt is 0.1 with the mass percent of amounting to titanium) in the fused transcocrystallized Al-Si alloy is stirred to fusing fully, and titaniferous grain-refining agent can be aluminium titanium boron or aluminium titanium carbon master alloy.
(3) in liquation, add Phosphorus alterant refinement primary silicon then, stir, wait for being cast in the metal pattern after 20-30 minute.Phosphorus alterant can be the mixture of red phosphorus and flux (main component is a potassium fluotitanate), also can be the master alloy that contains the aluminium phosphide nucleus in advance.The processing condition that phosphorus modification adopts are: the P add-on is the 0.03-0.2% of melt quality; Deterroration is 720 ℃-830 ℃; Deteriorating time is 20-30 minute; Pouring temperature is 730 ℃-830 ℃.Best modification process condition is: best P add-on is 0.05% of a melt quality; Best deterroration is 800 ℃; Deteriorating time is 20-30 minute; Best pouring temperature is 800 ℃.(4) ingot casting of step 3 is heat-treated at 500-535 ℃, or the ingot casting of step 2 is heat-treated (5) 480 ℃ of hot extrusions and then at 500-535 ℃.
Provide preferred example of the present invention below.
Embodiment 1
(1) adopt aluminium ingot, one-level silicon metal, primary magnesium ingot, electrolytic copper Si:16-18% by mass percentage, Cu:4-5, Mg:0.45-0.65%, surplus is Al, preparation A390 alloy.(2) take by weighing the Al-Ti-B intermediate alloy that titanium content is a molten aluminium quality 0.1%, add in the A390 alloy of fusing, be stirred to fusing fully.(3) then behind the melt heating to 800 ℃, in liquation, add the mixing briquetting that red phosphorus content is red phosphorus, aluminium powder and the flux (being mainly potassium fluotitanate) of melt quality 0.05% (mass percent of mixing red phosphorus, aluminium powder and flux in the briquetting is 20: 25: 55), stir, wait for after 20-30 minute, be cast in the metal pattern, pouring temperature is 800 ℃.(4) ingot casting to step 3 produces in the VMK-250-S heat treatment furnace in Germany, 535 ℃ of thermal treatments 3 hours, and shrend cooling then, the gained microstructure as shown in Figure 2, the mechanical property of gained tissue is: tensile strength 245MPa, and hardness (HV) is 142, unit elongation is 0.3%.
Embodiment 2
(1) by scheme 1 method preparation A390 alloy.(2) adding titanium content in melt is the Al-Ti-B intermediate alloy of molten aluminium quality 0.1%, is stirred to fusing fully.(3) adding phosphorus content then in 800 ℃ of melts is the master alloy that contains the aluminium phosphide nucleus in advance of melt quality 0.05%, be stirred to fusing after, wait for 20 minutes, be molded in the metal pattern 800 ℃ of temperature.(3) to ingot casting at 480 ℃, extrusion ratio is 3: 1, carries out crimp under the condition of extrusion speed＜1 meter per second.(5) the excellent base after the extruding produces in the VMK-250-S heat treatment furnace in Germany, 500 ℃ of thermal treatments 3 hours, and shrend cooling then, the gained microstructure is as shown in Figure 3.Extruding+T6 ((500 ℃, 3h) shrend, the tensile strength that (200 ℃, 6h) timeliness) handle back gained tissue is 414.7MPa, and hardness (HV) is 156 (HB is 148), and unit elongation is 0.5%.
Embodiment 3
(1) by scheme 1 method preparation A390 alloy, adding titaniferous grain-refining agent.(2) then behind the melt heating to 720 ℃, adding red phosphorus content in liquation is the red phosphorus of melt quality 0.2% and the mixing briquetting of flux (being mainly potassium fluotitanate) (mass percent of red phosphorus and flux is 40: 60 in the briquetting), stir, wait for after 30 minutes, be cast in the metal pattern, pouring temperature is 730 ℃.(3) ingot casting to step 2 produces in the VMK-250-S heat treatment furnace in Germany, in 535 ℃ of thermal treatments shrend cooling after 3 hours.
Embodiment 4
(1) by scheme 1 method preparation A390 alloy, adding titaniferous grain-refining agent.(2) then behind the melt heating to 830 ℃, in liquation, add the mixing briquetting that red phosphorus content is red phosphorus, aluminium powder and the flux (being mainly potassium fluotitanate) of melt quality 0.03% (mass percent of mixing red phosphorus, aluminium powder and flux in the briquetting is 20: 25: 55), stir, wait for after 30 minutes, be cast in the metal pattern, pouring temperature is 830 ℃.(4) ingot casting to step 2 produces in the VMK-250-S heat treatment furnace in Germany, in 500 ℃ of thermal treatments shrend cooling after 3 hours.
Claims (6)
1. the microstructure thinning process of a transcocrystallized Al-Si alloy is characterized in that the mass percentage content of silicon in the aluminum silicon alloy that this technology relates to is 16%-20%; The process for refining step comprises:
(1) in the fused transcocrystallized Al-Si alloy, adds the titaniferous grain-refining agent, be stirred to fusing fully;
(2) in liquation, add Phosphorus alterant then and stir refinement primary silicon, ingot casting;
(3) ingot casting of step 2 is heat-treated at 500-520 ℃, or the ingot casting of step 2 is heat-treated 480 ℃ of hot extrusions and then at 500-535 ℃.
2. the microstructure thinning process of a kind of transcocrystallized Al-Si alloy according to claim 1 is characterized in that the titaniferous grain-refining agent that adds to the fused transcocrystallized Al-Si alloy is aluminium titanium boron or aluminium titanium carbon master alloy; Add-on is a melt quality 0.1%;
3. the microstructure thinning process of a kind of transcocrystallized Al-Si alloy according to claim 1 is characterized in that Phosphorus alterant is the mixture of red phosphorus, aluminium powder and/or flux potassium fluotitanate.
4. the microstructure thinning process of a kind of transcocrystallized Al-Si alloy according to claim 1 is characterized in that Phosphorus alterant is the master alloy that contains the aluminium phosphide nucleus in advance.
5. the microstructure thinning process of a kind of transcocrystallized Al-Si alloy according to claim 1, it is characterized in that the processing condition that phosphorus modification adopts are: the P add-on is the 0.03%-0.2% of melt quality; Deterroration is 720 ℃-830 ℃; Deteriorating time is 20-30 minute; Pouring temperature is 730 ℃-830 ℃.
6. the microstructure thinning process of a kind of transcocrystallized Al-Si alloy according to claim 1, it is characterized in that the modification process condition is: the P add-on is 0.05% of a melt quality; Deterroration is 800 ℃; Deteriorating time is 20-30 minute; Pouring temperature is 800 ℃.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101852195A (en) * | 2009-04-01 | 2010-10-06 | 苏州中成汽车空调压缩机有限公司 | Swash plate compressor with variable displacements |
| CN102787248A (en) * | 2012-08-02 | 2012-11-21 | 中原工学院 | Method for refining primary silicon of hypereutectic Al-Si alloy |
| CN106319297A (en) * | 2016-08-16 | 2017-01-11 | 江苏中色锐毕利实业有限公司 | High-strength eutectic aluminum-silicon alloy and preparation method thereof |
| CN107236875A (en) * | 2017-06-23 | 2017-10-10 | 常州大学 | A kind of phosphorus titanium dual metamorphism method of cocrystallized Al-Si alloy |
| CN108251668A (en) * | 2018-04-17 | 2018-07-06 | 青岛科技大学 | A kind of new application of silica |
| CN108277373A (en) * | 2018-02-07 | 2018-07-13 | 兰州理工大学 | A kind of Al-Ti-C-La alloys and preparation method thereof |
| CN108330308A (en) * | 2018-02-07 | 2018-07-27 | 兰州理工大学 | A kind of Al-Ti-C-La composite crystal grain fining agents, alloy and preparation method thereof |
| CN109778019A (en) * | 2019-03-01 | 2019-05-21 | 昆明理工大学 | A kind of hypereutectic aluminum-silicon alloy composite modifier and preparation method thereof |
-
2007
- 2007-05-31 CN CN 200710099824 patent/CN101058855A/en active Pending
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101852195A (en) * | 2009-04-01 | 2010-10-06 | 苏州中成汽车空调压缩机有限公司 | Swash plate compressor with variable displacements |
| CN102787248A (en) * | 2012-08-02 | 2012-11-21 | 中原工学院 | Method for refining primary silicon of hypereutectic Al-Si alloy |
| CN102787248B (en) * | 2012-08-02 | 2014-06-04 | 中原工学院 | Method for refining primary silicon of hypereutectic Al-Si alloy |
| CN106319297A (en) * | 2016-08-16 | 2017-01-11 | 江苏中色锐毕利实业有限公司 | High-strength eutectic aluminum-silicon alloy and preparation method thereof |
| CN106319297B (en) * | 2016-08-16 | 2018-11-27 | 江苏中色锐毕利实业有限公司 | A kind of high intensity cocrystallized Al-Si alloy and preparation method thereof |
| CN107236875A (en) * | 2017-06-23 | 2017-10-10 | 常州大学 | A kind of phosphorus titanium dual metamorphism method of cocrystallized Al-Si alloy |
| CN108277373A (en) * | 2018-02-07 | 2018-07-13 | 兰州理工大学 | A kind of Al-Ti-C-La alloys and preparation method thereof |
| CN108330308A (en) * | 2018-02-07 | 2018-07-27 | 兰州理工大学 | A kind of Al-Ti-C-La composite crystal grain fining agents, alloy and preparation method thereof |
| CN108251668A (en) * | 2018-04-17 | 2018-07-06 | 青岛科技大学 | A kind of new application of silica |
| CN109778019A (en) * | 2019-03-01 | 2019-05-21 | 昆明理工大学 | A kind of hypereutectic aluminum-silicon alloy composite modifier and preparation method thereof |
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