CN103695675B - Change the method for Fe phase morphology in Al-Mg-Si system alloy - Google Patents
Change the method for Fe phase morphology in Al-Mg-Si system alloy Download PDFInfo
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- CN103695675B CN103695675B CN201310739432.XA CN201310739432A CN103695675B CN 103695675 B CN103695675 B CN 103695675B CN 201310739432 A CN201310739432 A CN 201310739432A CN 103695675 B CN103695675 B CN 103695675B
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 24
- 239000000956 alloy Substances 0.000 title claims abstract description 24
- 229910018464 Al—Mg—Si Inorganic materials 0.000 title claims abstract description 21
- 238000000034 method Methods 0.000 title claims abstract description 15
- 239000000843 powder Substances 0.000 claims description 10
- 238000005266 casting Methods 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 238000003756 stirring Methods 0.000 claims description 7
- 238000007872 degassing Methods 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 238000002791 soaking Methods 0.000 claims description 5
- 229910052725 zinc Inorganic materials 0.000 claims description 5
- 238000010907 mechanical stirring Methods 0.000 claims description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 3
- 239000011248 coating agent Substances 0.000 claims description 3
- 238000000576 coating method Methods 0.000 claims description 3
- 229910001873 dinitrogen Inorganic materials 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 239000007787 solid Substances 0.000 claims description 3
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 9
- 239000000463 material Substances 0.000 abstract description 6
- 239000011159 matrix material Substances 0.000 abstract description 4
- 238000005275 alloying Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 abstract description 3
- 229910000765 intermetallic Inorganic materials 0.000 abstract description 3
- 229910001092 metal group alloy Inorganic materials 0.000 abstract description 2
- 230000000877 morphologic effect Effects 0.000 abstract description 2
- 238000002360 preparation method Methods 0.000 abstract description 2
- 239000010949 copper Substances 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 1
- 229910018619 Si-Fe Inorganic materials 0.000 description 1
- 229910008289 Si—Fe Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
- 239000004927 clay Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000000254 damaging effect Effects 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 238000003113 dilution method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001914 filtration Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 210000001519 tissue Anatomy 0.000 description 1
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Abstract
The present invention relates to a kind of method changing Fe phase morphology in Al-Mg-Si system alloy, specifically for the morphological control method of harmful element Fe phase in aluminium alloy, belong to technical field of metallic alloy preparation.The present invention eliminates Fe phase endanger by adding alloying element Ti in melt, and it has a extensive future; Ti element, except changing Fe phase morphology, can also react with matrix Al and generate intermetallic compound Al
3ti, effectively can increase the mechanical property of material, crystal grain thinning.And can not detrimentally affect be produced.
Description
Technical field
The present invention relates to a kind of method changing Fe phase morphology in Al-Mg-Si system alloy, specifically for the morphological control method of harmful element Fe phase in aluminium alloy, belong to technical field of metallic alloy preparation.
Background technology
Aluminium alloy has many good physicalies, as density is little, specific tenacity is high, good percentage elongation, the features such as plasticity-is good, but in aluminium alloy, be inevitably accompanied with the Fe element of certain content, because the solubleness of Fe element in aluminium alloy is very low, therefore in the tissue in the end solidified, must form Al-Si-Fe phase, it is main with α-Al in aluminum alloy organization
8siFe
2exist mutually, pattern is tip-like.Time this makes aluminum substrate stressed, easily produce stress concentration at needle point place, become formation of crack, material property is declined.Simultaneously in aluminum substrate deformation process due to α-Al
8siFe
2not only crisp but also hard mutually, make its needle point isolate matrix, impel crack propagation, thus accelerate material failure.And generally in the industrial production, the method for deironing has two kinds: one makes Fe content reduce by dilution process, but the bad control of dilution, and also the harm of Fe phase can not be eliminated.Another kind adopts the method for filtering, and effectively can reduce the harm of Fe phase, but cost is too high, is unfavorable for scale operation.Therefore eliminate by adding alloying element Ti in melt the method that Fe phase endangers), its prospect is boundless.Ti element, except changing Fe phase morphology, can also react with matrix Al and generate intermetallic compound Al
3ti, effectively can increase the mechanical property of material, crystal grain thinning.And can not detrimentally affect be produced.
Summary of the invention
The object of the invention is to overcome above-mentioned weak point, convenient, to effectively reduce Fe phase in Al-Mg-Si system alloy damaging effect, improve mechanical property and the resistance to corrosion of material.
According to technical scheme provided by the invention, change the method for Fe phase morphology in Al-Mg-Si system alloy, step is: melted at 780-800 DEG C by Al-Mg-Si system alloy, adds pure Ti powder, pure Ti powder: Fe mass ratio is 1 ~ 2:1; Stir with the speed of 400-500r/min and be incubated, holding temperature is 750-800 DEG C, and soaking time is 10-20min, namely can be used for casting.
In described Al-Mg-Si system alloy, the mass percent of each composition is: Si; 6.5%-7.5%, Mg:0.25%-0.45%, Fe<2%, Mn<0.05%, Zn<0.05%, Cu<0.1%, surplus is Al.
Alr mode is mechanical stirring, blade and agitator arm surface-coated ZnO coating, prevents from introducing more Fe phase, and is baked to melt temperature before the use, prevent melt temperature rapid drawdown.
After Al-Mg-Si system alloy melting, adopt ZnCl
2solid or pure nitrogen gas carry out degasification to melt.
Alr mode is mechanical stirring, blade and agitator arm surface-coated ZnO coating, prevents from introducing more Fe phase, and is baked to melt temperature before the use.Prevent melt temperature rapid drawdown.
Melt degasification can use ZnCl
2solid, also can use pure nitrogen gas, for removing the melt air-breathing that H element in melt and Yin Gaowen and stirring cause.
Alloy prepared by application the present invention, its Fe phase is by tip-like β-Al
5feSi is changed to Chinese character shape (or bone shape) α-Al
8siFe
2, effectively reduce the harm of Fe phase, and this invention using method is simple, the Ti added is beneficial element concerning aluminium alloy, can not produce harm.
Beneficial effect of the present invention: the present invention eliminates Fe phase endanger by adding alloying element Ti in melt, and it has a extensive future; Ti element, except changing Fe phase morphology, can also react with matrix Al and generate intermetallic compound Al
3ti, effectively can increase the mechanical property of material, crystal grain thinning.And can not detrimentally affect be produced.
Accompanying drawing explanation
The alloy casting state metallographic microstructure figure of Fig. 1 comparative example 1.
The alloy casting state metallographic microstructure figure of Fig. 2 embodiment 1.
Embodiment
Embodiment 1
Al-Mg-Si system alloy is melted at 800 DEG C, adds pure Ti powder, pure Ti powder: Fe mass ratio is 1:1; Stir with the speed of 400r/min and be incubated, holding temperature is 750 DEG C, and soaking time is 20min, namely can be used for casting.
Use ZnCl afterwards
2degasification refining are skimmed, and then pour into copper mold, the demoulding after cooling.The as cast condition metallographic microstructure figure of gained aluminium alloy is shown in accompanying drawing 2.
In described Al-Mg-Si system alloy, the mass percent of each composition is: Si; 7.5%, Mg:0.45%, Fe<2%, Mn<0.05%, Zn<0.05%, Cu<0.1%, surplus is Al.
Embodiment 2
Al-Mg-Si system alloy is melted at 780 DEG C, adds pure Ti powder, pure Ti powder: Fe mass ratio is 2:1; Stir with the speed of 400r/min and be incubated, holding temperature is 800 DEG C, and soaking time is 10min, namely can be used for casting.
In described Al-Mg-Si system alloy, the mass percent of each composition is: Si; 6.5%, Mg:0.25%, Fe<2%, Mn<0.05%, Zn<0.05%, Cu<0.1%, surplus is Al.
Embodiment 3
Al-Mg-Si system alloy is melted at 790 DEG C, adds pure Ti powder, pure Ti powder: Fe mass ratio is 1.5:1; Stir with the speed of 450r/min and be incubated, holding temperature is 780 DEG C, and soaking time is 10-20min, namely can be used for casting.
In described Al-Mg-Si system alloy, the mass percent of each composition is: Si; 7%, Mg:0.35%, Fe<2%, Mn<0.05%, Zn<0.05%, Cu<0.1%, surplus is Al.
Comparative example 1
Al-Mg-Si alloy is put into graphite-clay crucible, melting in resistance furnace, smelting temperature is 800 DEG C, stirs, and be incubated 10min after fusing with mechanical stirring oar at 760 DEG C.Use ZnCl afterwards
2degasification refining are skimmed, and then pour into copper mold, the demoulding after cooling.The as cast condition metallographic microstructure figure of gained aluminium alloy is shown in accompanying drawing 1.
By comparative example 1(Fig. 1) and embodiment 1(Fig. 2).Can find that adding Ti element can effectively change Fe phase morphology.
Claims (3)
1. change the method for Fe phase morphology in Al-Mg-Si system alloy, it is characterized in that step is: melted at 780-800 DEG C by Al-Mg-Si system alloy, add pure Ti powder, pure Ti powder: Fe mass ratio is 1 ~ 2:1; Stir with the speed of 400-500r/min and be incubated, holding temperature is 750-800 DEG C, and soaking time is 10-20min, namely can be used for casting;
After Al-Mg-Si system alloy melting, adopt ZnCl
2solid or pure nitrogen gas carry out degasification to melt.
2. change the method for Fe phase morphology in Al-Mg-Si system alloy as claimed in claim 1, it is characterized in that: in described Al-Mg-Si system alloy, the mass percent of each composition is: Si; 6.5%-7.5%, Mg:0.25%-0.45%, Fe<2%, Mn<0.05%, Zn<0.05%, Cu<0.1%, surplus is Al.
3. change the method for Fe phase morphology in Al-Mg-Si system alloy as claimed in claim 1, it is characterized in that: alr mode is mechanical stirring that blade and agitator arm surface-coated ZnO coating prevent from introducing more Fe phase, and be baked to melt temperature before the use, prevent melt temperature rapid drawdown.
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| Application Number | Priority Date | Filing Date | Title |
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| CN201310739432.XA CN103695675B (en) | 2013-12-27 | 2013-12-27 | Change the method for Fe phase morphology in Al-Mg-Si system alloy |
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|---|---|---|---|
| CN201310739432.XA CN103695675B (en) | 2013-12-27 | 2013-12-27 | Change the method for Fe phase morphology in Al-Mg-Si system alloy |
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| Publication Number | Publication Date |
|---|---|
| CN103695675A CN103695675A (en) | 2014-04-02 |
| CN103695675B true CN103695675B (en) | 2015-10-21 |
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|---|---|---|---|
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101713041A (en) * | 2009-09-04 | 2010-05-26 | 广东华昌铝厂有限公司 | Novel Al-Mg-Si alloy |
| CN102758108A (en) * | 2012-06-19 | 2012-10-31 | 南昌大学 | Al-Si-Mg-Sm rare earth cast aluminum alloy and preparation method thereof |
-
2013
- 2013-12-27 CN CN201310739432.XA patent/CN103695675B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101713041A (en) * | 2009-09-04 | 2010-05-26 | 广东华昌铝厂有限公司 | Novel Al-Mg-Si alloy |
| CN102758108A (en) * | 2012-06-19 | 2012-10-31 | 南昌大学 | Al-Si-Mg-Sm rare earth cast aluminum alloy and preparation method thereof |
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| CN103695675A (en) | 2014-04-02 |
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Effective date of registration: 20190329 Address after: 414413 South of Zhensheng South Road, Recycling Economy Industrial Park, Miluo City, Yueyang City, Hunan Province Patentee after: Hunan Zhonglian Zhiyuan Wheel Co. Address before: 214106 Houqiao Middle East Village, Xishan District, Wuxi City, Jiangsu Province Patentee before: Jiangsu Zhonglian Aluminium Industry Co., Ltd. |
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