CN102787248A - Method for refining primary silicon of hypereutectic Al-Si alloy - Google Patents
Method for refining primary silicon of hypereutectic Al-Si alloy Download PDFInfo
- Publication number
- CN102787248A CN102787248A CN2012102729483A CN201210272948A CN102787248A CN 102787248 A CN102787248 A CN 102787248A CN 2012102729483 A CN2012102729483 A CN 2012102729483A CN 201210272948 A CN201210272948 A CN 201210272948A CN 102787248 A CN102787248 A CN 102787248A
- Authority
- CN
- China
- Prior art keywords
- alloy
- transcocrystallized
- primary silicon
- silicon
- tib
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Silicon Compounds (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Continuous Casting (AREA)
Abstract
A method for refining the primary silicon of a hypereutectic Al-Si alloy adopts the TiB2 particle phase to refine the primary silicon of the hypereutectic Al-Si alloy during the casting of the hypereutectic Al-Si alloy. According to the method, the TiB2 particle phase is adopted to refine the primary silicon of the hypereutectic Al-Si alloy during the casting of the hypereutectic Al-Si alloy, and the primary silicon can be refined to a size below 50 micrometers without a higher casting temperature. With high stability in the molten alloy, the TiB2 particle can not react with other elements of the alloy, so that the refining effect is lasting, and the modifying and refining effects on the eutectic silicon in the alloy by the element of Sr or Na can not be affected; and the eutectic silicon and the primary silicon of the hypereutectic Al-Si alloy can be refined at the same time, so that the performance of the alloy is greatly improved.
Description
Technical field
The invention belongs to technical field of alloy material, relate to the alloy microscopic structure structure refinement technology that improves the transcocrystallized Al-Si alloy use properties.
Background technology
Compare with other aluminum silicon alloy material, transcocrystallized Al-Si alloy, owing to contain a large amount of element silicons, the density of alloy is little, and thermal expansivity reduces, and wear resistance improves.Under the routine casting condition, in the transcocrystallized Al-Si alloy element silicon mainly with thick primary silicon mutually with the flaky Eutectic Silicon in Al-Si Cast Alloys of pin mutually form exist, two kinds of existence forms of this of element silicon, particularly thick primary silicon has significantly reduced the mechanical property of alloy mutually.So in industrial production, need carry out thinning processing mutually, to improve alloy property to phase of the primary silicon in the transcocrystallized Al-Si alloy or Eutectic Silicon in Al-Si Cast Alloys.
Silicon phase refinement in the transcocrystallized Al-Si alloy mainly is the refinement of primary silicon phase at present, and the method for primary silicon is in the practical refinement transcocrystallized Al-Si alloy, when alloy casting, adds the little P element.The method of refining eutectic silicon is to add a spot of Sr element or Na element.
Under conventional production specifications, add the primary silicon in the P element refinement transcocrystallized Al-Si alloy, need to use higher pouring temperature, the primary silicon particle is difficult to refine to below 50 microns usually.In addition, in alloy melt, the P element can be combined into stable compound with the Sr or the Na of refining eutectic silicon, and loses the effect of refinement silicon phase.Therefore, be difficult to primary silicon and Eutectic Silicon in Al-Si Cast Alloys in the transcocrystallized Al-Si alloy of refinement simultaneously on the practical applications at present.
Adopt flash set technology, like spray deposition technique, silicon is grown up mutually in the time of can effectively suppressing transcocrystallized Al-Si alloy and solidify, and realizes primary silicon and Eutectic Silicon in Al-Si Cast Alloys in the alloy of refinement simultaneously.But use the flash set technology cost high, and be difficult to the big or complex-shaped component of manufacturing dimension.
Summary of the invention
Technical problem to be solved by this invention is under conventional production specifications, and the primary silicon in the transcocrystallized Al-Si alloy is carried out refinement mutually.
Adopt following technical scheme in order to solve the problems of the technologies described above: the method for primary silicon in a kind of refinement transcocrystallized Al-Si alloy, when the transcocrystallized Al-Si alloy founding, through TiB
2Primary silicon phase in the particle phase refinement transcocrystallized Al-Si alloy.
The microstructure of transcocrystallized Al-Si alloy does, had TiB by the primary silicon of refinement in mutually
2The particle phase.
At silicon content is in the transcocrystallized Al-Si alloy of 15 ~ 30% (massfractions), the TiB that the refinement primary silicon is mutually required
2The particle phase content is 0.5 ~ 4.5% (massfraction).
First method: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add potassium fluoborate and potassium fluotitanate, make potassium fluoborate and potassium fluotitanate in transcocrystallized Al-Si alloy, form TiB
2Particle.
Second method: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add Al-Ti master alloy and Al-B master alloy, make it form TiB
2Particle wherein contains massfraction and is that to contain massfraction in 2 ~ 20% Ti, the Al-B master alloy be 1 ~ 10% B in the Al-Ti master alloy.
The third method: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add Al-TiB
2Master alloy, Al-TiB
2Contain massfraction in the master alloy and be 4 ~ 20% TiB
2
The present invention is in the molten timing of transcocrystallized Al-Si alloy, utilizes self-generated TiB
2Primary silicon phase in the grain refine transcocrystallized Al-Si alloy does not need high pouring temperature that primary silicon is refined to below 50 microns mutually.Because TiB
2Particle stability in aluminium alloy melt is high; Not with alloy in other alloying element react; It is long-lasting to have thinning effect; Do not influence Sr element or Na element to Modification of Eutectic Silicon in Al-Si Cast Alloys refining effect in the alloy, can realize primary silicon and Eutectic Silicon in Al-Si Cast Alloys refinement simultaneously in the transcocrystallized Al-Si alloy, significantly improve alloy property.
Embodiment
Embodiment 1:The method of primary silicon in a kind of refinement transcocrystallized Al-Si alloy, the molten Al-15%Si-0.5%TiB that joins in crucible electrical resistance furnace
2(%, massfraction, below identical) transcocrystallized Al-Si alloy.
(1) fusing fine aluminium ingot in the aluminium alloy smelting stove.
(2) required 15%Si element adds in the molten aluminium with Al-40%Si master alloy form in the alloy.
(3) synthetic 0.5% self-generated TiB in melt
2, in alloy melt, add Al-10Ti master alloy and Al-4B master alloy by the metering ratio.Make it to form 0.5%TiB
2
(4) alloy casting, the conventional melting technology of pressing aluminum silicon alloy are to alloy melt degasification and refining, and insulation is 10 minutes behind the refining and modifying, pours in the metal pattern in 740 ℃.
The alloy sample metallurgical analysis shows that Eutectic Silicon in Al-Si Cast Alloys is the faller gill shape in the alloy, and hypereutectic silicon is 35 ~ 45 micron particle shapes.
Embodiment 2: the method for primary silicon in a kind of refinement transcocrystallized Al-Si alloy, the molten Al-17%Si-4.5%Cu-0.6%Mg-0.06%Sr-1.3%TiB that joins in crucible electrical resistance furnace
2Transcocrystallized Al-Si alloy.
(1) fusing fine aluminium ingot in the aluminium alloy smelting stove.
(2) required 17%Si, 4.5%Cu, 0.6%Mg, 0.06%Sr add in the molten aluminium with pure Si, pure Cu, pure Mg and Al-10%Sr master alloy form respectively in the alloy.
(3) synthetic 1.3%TiB in melt
2, in alloy melt, add Al-13%TiB
2Master alloy makes alloy melt TiB
2Content is 1.3%.
(4) alloy casting, insulation is 7 minutes after refining and modifying and the degasification, pours in the graphite mo(u)ld in 750 ℃.
The alloy sample metallurgical analysis shows, eutectic Si is a point-like or tiny fibrous in the alloy, and hypereutectic Si is 20 ~ 30 microns a particulate state.
Embodiment 3:The method of primary silicon in a kind of refinement transcocrystallized Al-Si alloy, the molten Al-30%Si-4.5%TiB that joins in induction furnace
2Transcocrystallized Al-Si alloy.
(1) fusing fine aluminium ingot in the induction furnace.
(2) required 30%Si element adds in the molten aluminium with pure Si form in the alloy.
(3) synthetic 4.5% self-generated TiB in melt
2, than in alloy melt, adding potassium fluoborate and potassium fluotitanate, make and form 4.5% TiB in the alloy by metering
2
(4) alloy casting, insulation is 5 minutes after refining and modifying and the degasification, pours in the metal pattern in 870 ℃.
The alloy sample metallurgical analysis shows that hypereutectic Si is 40 ~ 50 microns a particulate state in the alloy.
Embodiment 4: the method for primary silicon in a kind of refinement transcocrystallized Al-Si alloy is in the transcocrystallized Al-Si alloy of 15 ~ 30% (massfractions) at silicon content, the TiB that the refinement primary silicon is mutually required
2The particle phase content is 0.5 ~ 4.5% (massfraction).
First method: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add potassium fluoborate and potassium fluotitanate, make potassium fluoborate and potassium fluotitanate in transcocrystallized Al-Si alloy, form TiB
2Particle.
Second method: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add Al-Ti master alloy and Al-B master alloy, make it form TiB
2Particle wherein contains massfraction and is that to contain massfraction in 2 ~ 20% Ti, the Al-B master alloy be 1 ~ 10% B in the Al-Ti master alloy.
The third method: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add Al-TiB
2Master alloy, Al-TiB
2Contain massfraction in the master alloy and be 4 ~ 20% TiB
2
The microstructure of transcocrystallized Al-Si alloy does, had TiB by the primary silicon of refinement in mutually
2The particle phase.
Claims (6)
1. the method for primary silicon in the refinement transcocrystallized Al-Si alloy is characterized in that: when the transcocrystallized Al-Si alloy founding, through TiB
2Primary silicon phase in the particle phase refinement transcocrystallized Al-Si alloy.
2. according to the method for primary silicon in the refinement transcocrystallized Al-Si alloy of claim 1, it is characterized in that: the microstructure of transcocrystallized Al-Si alloy does, had TiB by the primary silicon of refinement in mutually
2The particle phase.
3. according to the method for primary silicon in the refinement transcocrystallized Al-Si alloy of claim 1, it is characterized in that: at silicon content is in the transcocrystallized Al-Si alloy of 15 ~ 30% (massfractions), the TiB that the refinement primary silicon is mutually required
2The particle phase content is 0.5 ~ 4.5% (massfraction).
4. according to the method for primary silicon in the refinement transcocrystallized Al-Si alloy of claim 3; It is characterized in that: when the founding transcocrystallized Al-Si alloy; In the transcocrystallized Al-Si alloy melt, add potassium fluoborate and potassium fluotitanate, make potassium fluoborate and potassium fluotitanate in transcocrystallized Al-Si alloy, form TiB
2Particle.
5. according to the method for primary silicon in the refinement transcocrystallized Al-Si alloy of claim 3, it is characterized in that: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add Al-Ti master alloy and Al-B master alloy, make it form TiB
2Particle wherein contains massfraction and is that to contain massfraction in 2 ~ 20% Ti, the Al-B master alloy be 1 ~ 10% B in the Al-Ti master alloy.
6. according to the method for primary silicon in the refinement transcocrystallized Al-Si alloy of claim 3, it is characterized in that: when the founding transcocrystallized Al-Si alloy, in the transcocrystallized Al-Si alloy melt, add Al-TiB
2Master alloy, Al-TiB
2Contain massfraction in the master alloy and be 4 ~ 20% TiB
2
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210272948.3A CN102787248B (en) | 2012-08-02 | 2012-08-02 | Method for refining primary silicon of hypereutectic Al-Si alloy |
| PCT/CN2013/076255 WO2014019400A1 (en) | 2012-08-02 | 2013-05-27 | Method for refining primary silicon of hypereutectic al-si alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210272948.3A CN102787248B (en) | 2012-08-02 | 2012-08-02 | Method for refining primary silicon of hypereutectic Al-Si alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102787248A true CN102787248A (en) | 2012-11-21 |
| CN102787248B CN102787248B (en) | 2014-06-04 |
Family
ID=47152832
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201210272948.3A Expired - Fee Related CN102787248B (en) | 2012-08-02 | 2012-08-02 | Method for refining primary silicon of hypereutectic Al-Si alloy |
Country Status (2)
| Country | Link |
|---|---|
| CN (1) | CN102787248B (en) |
| WO (1) | WO2014019400A1 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104384482A (en) * | 2014-10-29 | 2015-03-04 | 青岛科技大学 | Method for refining primary silicon in hypereutectic aluminum silicon alloy |
| CN105401012A (en) * | 2015-09-21 | 2016-03-16 | 辽宁工业大学 | Preparation method for novel pelletized hypereutectic Al-Si alloy |
| CN106884113A (en) * | 2017-03-28 | 2017-06-23 | 泉州市中知信息科技有限公司 | A kind of high-strength aluminum alloy and its casting method |
| CN108251668A (en) * | 2018-04-17 | 2018-07-06 | 青岛科技大学 | A kind of new application of silica |
| CN110273087A (en) * | 2019-06-25 | 2019-09-24 | 昆明理工大学 | Regulate and control the method for hypereutectic aluminum-silicon alloy casting overall performance |
| 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 |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5217546A (en) * | 1988-02-10 | 1993-06-08 | Comalco Aluminum Limited | Cast aluminium alloys and method |
| CN101058855A (en) * | 2007-05-31 | 2007-10-24 | 中国铝业股份有限公司 | Microstructure thinning process for hypereutectic aluminum alloy |
-
2012
- 2012-08-02 CN CN201210272948.3A patent/CN102787248B/en not_active Expired - Fee Related
-
2013
- 2013-05-27 WO PCT/CN2013/076255 patent/WO2014019400A1/en active Application Filing
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5217546A (en) * | 1988-02-10 | 1993-06-08 | Comalco Aluminum Limited | Cast aluminium alloys and method |
| CN101058855A (en) * | 2007-05-31 | 2007-10-24 | 中国铝业股份有限公司 | Microstructure thinning process for hypereutectic aluminum alloy |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104384482A (en) * | 2014-10-29 | 2015-03-04 | 青岛科技大学 | Method for refining primary silicon in hypereutectic aluminum silicon alloy |
| CN104384482B (en) * | 2014-10-29 | 2016-05-04 | 青岛科技大学 | A kind of method of primary silicon in refinement transcocrystallized Al-Si alloy |
| CN105401012A (en) * | 2015-09-21 | 2016-03-16 | 辽宁工业大学 | Preparation method for novel pelletized hypereutectic Al-Si alloy |
| CN105401012B (en) * | 2015-09-21 | 2017-06-16 | 辽宁工业大学 | A kind of preparation method for being granulated hypereutectic Al Si alloys |
| CN106884113A (en) * | 2017-03-28 | 2017-06-23 | 泉州市中知信息科技有限公司 | A kind of high-strength aluminum alloy and its casting method |
| CN106884113B (en) * | 2017-03-28 | 2018-09-25 | 泉州宝顿机械技术开发有限公司 | A kind of high-strength aluminum alloy and its casting method |
| CN108251668A (en) * | 2018-04-17 | 2018-07-06 | 青岛科技大学 | A kind of new application of silica |
| CN110273087A (en) * | 2019-06-25 | 2019-09-24 | 昆明理工大学 | Regulate and control the method for hypereutectic aluminum-silicon alloy casting overall performance |
| 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 |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2014019400A1 (en) | 2014-02-06 |
| CN102787248B (en) | 2014-06-04 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102787248B (en) | Method for refining primary silicon of hypereutectic Al-Si alloy | |
| CN102676887B (en) | Aluminum alloy for compression casting and casting of aluminum alloy | |
| CN101503773B (en) | Heat resisting low expansion silumin and preparation thereof | |
| CN103290265B (en) | Die-cast zinc alloy with high flowability and preparation method thereof | |
| CN103361524B (en) | Composite modification method for hypereutectic aluminum-silicon alloy | |
| CN102181758B (en) | Novel casting aluminium alloy and preparation method thereof | |
| WO2011098813A4 (en) | Aluminium-copper alloy for casting | |
| CN108103363A (en) | It is a kind of for refinement-alterant of hypoeutectic silumin alloy and its preparation method and application | |
| CN103305729A (en) | Method for preparing novel Al-Si-Mg-Cu-Sr alloy | |
| CN105779838B (en) | High-thermal-conductivity die-casting magnesium alloy and preparation process thereof | |
| CN107881378B (en) | Aluminum alloy composition, aluminum alloy element, communication product and preparation method of aluminum alloy element | |
| CN101838761A (en) | Aluminum alloy 7085 microalloyed with strontium and preparation method thereof | |
| CN101294247B (en) | Aluminum alloy refiner and aluminum alloy produced with the refiner | |
| CN101514409A (en) | A method for preparing in situ MgSi particle reinforced metal matrix composite | |
| CN113969366A (en) | High-strength and high-toughness cast aluminum alloy and preparation method thereof | |
| CN102758108B (en) | Al-Si-Mg-Sm rare earth cast aluminum alloy and preparation method thereof | |
| KR20130058998A (en) | Aluminum alloy for continuous casting and method for producing the same | |
| CN104152731A (en) | Process for melting cast aluminum alloy | |
| CN101838759A (en) | 4032 alloy alterant and use method thereof | |
| CN103305730A (en) | Novel Al-Si-Mg-Cu-Sr cast alloy | |
| Górny et al. | Effect of Titanium and Boron on the Stability of Grain Refinement of Al-Cu Alloy | |
| CN103451487A (en) | Magnesium-containing Al-30Si aluminum alloy and preparation technique thereof | |
| CN102140601B (en) | Al-Si-Cu-Mg-xEr rare-earth die-casting aluminum alloy | |
| CN100557054C (en) | Contain creep resistance Dow metal of Si and C and preparation method thereof | |
| CN102146541B (en) | Al-Si-Cu-Mg-xLa rare earth die casting aluminum alloy |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20140604 Termination date: 20170802 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |