CN107385284A - A kind of high ferro transcocrystallized Al-Si alloy and preparation method thereof - Google Patents
A kind of high ferro transcocrystallized Al-Si alloy and preparation method thereof Download PDFInfo
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- CN107385284A CN107385284A CN201710524821.9A CN201710524821A CN107385284A CN 107385284 A CN107385284 A CN 107385284A CN 201710524821 A CN201710524821 A CN 201710524821A CN 107385284 A CN107385284 A CN 107385284A
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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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
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Abstract
The invention discloses a kind of high ferro transcocrystallized Al-Si alloy and preparation method thereof, is related to alusil alloy Material Field, weight percentage, and high ferro transcocrystallized Al-Si alloy includes following component：Silicon 15%, iron 3%, manganese 1.8%, copper 0 3%, magnesium 0 0.5%, phosphorus 0 0.045%, surplus is aluminium, its preparation method passes through first melting intermediate alloy, by intermediate alloy, melting is together in proportion again, finally by Technology for Heating Processing, obtain the alloy that tensile strength is far above Al 15wt.%Si control sample intensity, and hardness is compared before reinforcing is gone bad and improved a lot, 87.2HB average hardness can be obtained, alloy material uniformity is also preferable, so as to obtain, mechanical property is close to be even better than the not high ferro alusil alloy of iron content or iron-holder low aluminum silicon alloy, present situation for changing the difficult recovery of the exceeded aluminium alloy of iron content plays an important roll and meaning.
Description
Technical field
The present invention relates to alusil alloy Material Field, and in particular to a kind of high ferro transcocrystallized Al-Si alloy and its preparation side
Method.
Background technology
Alusil alloy is a kind of forging using aluminium, silicon as main component and casting alloy, in existing alusil alloy, Fe-riched phase
Often treated as a kind of impurity for having harm, and in order to improve alloy property, the way of prior art generally use is logical
Cross change cooling velocity, addition nertralizer, melt overheat, addition alterant, dilution, precipitation, filtering, centrifugation removal, electromagnetism
The methods of removal, changes or removes Fe-riched phase, but such mode easily causes the exceeded aluminium alloy cost recovery of iron content
Height, recovery difficult are big.
The content of the invention
The purpose of the present invention is：In view of the shortcomings of the prior art, there is provided a kind of high ferro transcocrystallized Al-Si alloy, by Fe-riched phase
It is added to as one kind reinforcing in alusil alloy, increases considerably the iron content in alloy, harmful Fe-riched phase is changed into reinforcing
Phase, so as to improve alloy property, obtained high ferro alusil alloy mechanical property is not close to even better than iron content or iron-holder be low
Alusil alloy, this plays an important roll for the present situation of the difficult recovery of the exceeded aluminium alloy of change iron content and meaning.
In order to solve the above-mentioned technical problem, the technical solution adopted by the present invention is summarized as follows：
A kind of high ferro transcocrystallized Al-Si alloy, weight percentage, including following component：Silicon 15%, iron 3%, manganese
1.8%th, copper 0-3%, magnesium 0-0.5%, phosphorus 0.045%, surplus are aluminium.
Preferably, weight percentage, the high ferro transcocrystallized Al-Si alloy consist of the following composition：Silicon
15%th, iron 3%, manganese 1.8%, copper 3%, phosphorus 0.045%, surplus are aluminium.
Preferably, weight percentage, the high ferro transcocrystallized Al-Si alloy consist of the following composition：Silicon
15%th, iron 3%, manganese 1.8%, magnesium 0.5%, phosphorus 0.045%, surplus are aluminium.
Based on above-mentioned alloy, present invention also offers the preparation method of the high ferro transcocrystallized Al-Si alloy, including walk as follows
Suddenly：
(1) melting intermediate alloy：It is prepared using ZGJL-0.025-50-2.5 type intermediate frequency vacuum induction melting furnaces
Among aluminium silicon intermediate alloy, ferro-aluminum intermediate alloy, aluminium manganese intermediate alloy, aluminum bronze intermediate alloy, magnalium intermediate alloy and aluminium phosphorus
6 kinds of intermediate alloys of alloy, wherein the weight percentage of the aluminium in 6 kinds of intermediate alloys is respectively：70%th, 80%, 90%,
50%th, 65%, 95.5%；
(2) intermediate alloy is dried：The intermediate alloy that step (1) obtains is put into box resistance electric furnace in proportion, with 140
DEG C baking 8h；
(3) crucible is dried：Crucible is put into resistance electric furnace, is heated up to 200 DEG C, toasts 2h；
(4) casting mold is handled：First casting mold surface impurity and cleaning oil pollution are fallen, are then placed in box resistance electric furnace
In, using 200 DEG C of temperature 24h, ensure casting mold drying and surface cleaning；Casting mold takes out in time after drying,
Layer material is brushed on lower mold cavity surface, ensures that casting is smoothly stripped, after the completion of brushing, mould is placed in box resistance electricity
2~3 hours are incubated using 200 DEG C in stove, ensures dry paint layer hardening；
(5) melting：Dried intermediate alloy is put into and completed in dry crucible, voltage is tuned up, starts melting,
Smelting temperature is arranged to 820 DEG C, after raw material all melts, is incubated 15~20min, melt is seethed with excitement, and ensures that melt distribution is equal
It is even, crucible bottom is passed through using argon gas and refined, goes the removal of impurity；
(6) pour into a mould：First the surface scale in crucible is scooped out, then crucible is moved to above mould and poured into a mould,
Cooling, the demoulding obtain bulk processing product；
(7) it is heat-treated：Using T6 processing, i.e. solid solution+artificial aging, solid solubility temperature selects 525 DEG C, 4h is incubated, after taking-up
Immediately in 70~80 DEG C of quenching-in water；180 DEG C of artificial aging, cooling is to obtain high ferro transcocrystallized Al-Si alloy after being incubated 5h.
Relative to prior art, had the beneficial effect that caused by the present invention：
(1) in the present invention, using the Al-15wt.%Si control samples prepared under the same terms, its tensile strength under as cast condition
For 171.97MPa, add 3wt.%Fe and alloying component is adjusted to after Al-15wt.%Si-3wt.%Fe tension under its as cast condition
Intensity drops to 124.8MPa, and after adding the nertralizer Mn that Mn/Fe is 0.6, tensile strength is up to 130.3MPa, then divides
Not Jia Ru Cu and Mg strengthened, and gone bad using P, its tensile strength is greatly improved, and tensile strength is up under as cast condition
151.4MPa and 142MPa, it is all higher than Al-15wt.%Si-3wt.%Fe, after carrying out T6 processing, obtain maximum pulling strength
199MPa, far above Al-15wt.%Si control sample intensity, and hardness is compared before reinforcing is gone bad and improved a lot, and can be obtained
87.2HB average hardness, alloy material uniformity is also preferable, so the high ferro alusil alloy mechanical property that the present invention obtains connects
Nearly even better than not iron content or the low alusil alloy of iron-holder, solve the exceeded aluminium alloy cost recovery of existing iron content it is big,
The problem of recovery difficult is high.
(2) many documents all think that Fe-riched phase has been negative consequence in alusil alloy, it is considered that when Fe-riched phase approaches
During 0.8 wt.%, the intensity and hardness of alloy all rise, and after iron content is more than 0.8wt.%, the intensity and elongation of alloy are equal
Have substantial degradation, so prior art is all to improve alloy property from the mode for changing Fe-riched phase and removal Fe-riched phase.But this Shen
Please go to improve alloy property from the angle opposite with prior art, i.e., be added to aluminium using Fe-riched phase as one kind reinforcing
In silicon alloy, the iron content (iron content increases to 3%) in alloy is increased considerably, by adding corresponding alterant, neutralization
Agent, change the methods of cooling velocity, harmful Fe-riched phase is changed into hardening constituent, so as to improve alloy property, obtained high ferro aluminium
Silicon alloy mechanical property is close to even better than not iron content or the low alusil alloy of iron-holder.This not only overcomes the technology of industry
Prejudice, and play an important roll and meaning for changing the difficult recovery present situation of the exceeded aluminium alloy of iron content.
(3) when Mn and Fe ratios are 0.6 in the present invention, Needle like Iron Phase is reduced in alloy, and the size of Needle like Iron Phase is also corresponding
Reduce, strength of alloy has obtained significant enhancing.
Brief description of the drawings
Fig. 1 is the schematic flow sheet of the present invention.
Fig. 2 is front view, left view and the top view for the mould upstream that the present invention uses；
Fig. 3 is front view, left view and the top view for the mould bottom that the present invention uses；
Embodiment
The present invention is described in further detail with reference to the accompanying drawings and detailed description.Embodiments of the present invention bag
Include but be not limited to the following example.
Embodiment
The invention provides a kind of high ferro transcocrystallized Al-Si alloy, its alloy mechanical property can be approached and is even better than free of
Iron or the low alusil alloy of iron-holder.As shown in figure 1, the process that the present invention prepares high ferro transcocrystallized Al-Si alloy is as follows：
(1) melting intermediate alloy：Intermediate alloy is carried out using ZGJL-0.025-50-2.5 type intermediate frequencies vacuum induction melting furnace
Prepare.Pour into respectively and be divided into Al-30wt.%Si, Al-10wt.%Mn, Al-20wt.%Fe, Al-4.5wt.%P, Al-
50wt.%Cu, Al-35wt.%Mg intermediate alloy, intermediate alloy are to prevent the conjunction of high temperature using the purpose of vacuum melting furnace
Gold element is oxidized, and ensures the accurate of alloy each element addition.
(2) molten alloy：Using SG-5-12 resistance electro-smelting alloys, it is therefore an objective to make sample melting environment closer to life
Production practice, be advantageous to the popularization of experimental data, will be prepared before melting by table 1 corresponding intermediate alloy furnace charge be respectively put into it is box
In resistance electric furnace, with 140 DEG C of baking 8h, it is therefore an objective to remove the moisture in raw material, first build corundum crucible before melting and be put into resistance
In electric furnace, 200 DEG C are heated up to, toasts 2h, purpose is identical with furnace charge is dried, primarily to drying crucible；
The each group test specimen alloy composition of table 1
During melting, dried furnace charge will be prepared and be put into complete in dry crucible, voltage is tuned up, starts melting.
Smelting temperature is arranged to 820 DEG C.After raw material all melts, 15~20min is incubated, melt is seethed with excitement, ensure that melt distribution is equal
It is even, crucible bottom is passed through using argon gas and refined, goes the removal of impurity.Before cast, first surface scale is scooped out, then by earthenware
Crucible is moved to above mould and poured into a mould.
(3) pour into a mould：Need to prepare heterogeneity and tensile sample, metallographic specimen under different cooling, through analysis, if
Count the mould structure used as shown in Figure 2 and Figure 3, mould is divided into two parts up and down, and top is rising head die cavity, by left and right two halves group
Into, as shown in Fig. 2 bottom is tensile sample pickup part, left and right two halves are also classified into, as shown in figure 3, nine small cavities altogether,
Each cavity shape is in the same size, in order to which feeding needs, ensures casting quality, by the upper end side thickness of die of left and right two halves part
Reduce, make melt heat transfer in the die cavity of lower end faster, solidified prior to upper end；, need to be by die surface impurity and greasy dirt before cast
Clean out, be then placed in box resistance electric furnace, using 200 DEG C of temperature 24h, ensure mould drying and surface cleaning；
Mould is taken out in time after drying, and layer material is brushed on bottom tensile sample pickup type cavity mould surface, ensures that casting smoothly takes off
Mould.With 10%ZnO2, 4~5% waterglass, convert and coating be made in water；After the completion of brushing, mould is placed in box resistance electricity
2~3 hours are incubated using 200 DEG C in stove, ensures dry paint layer hardening；, need to be by alumina silicate before the hot top mould swabbing of top
Fiber is uniformly layered on mold interior wall surfaces after being soaked with waterglass, then is put into after being compacted with instrument in resistance electric furnace and dries baking；
It is manufacture one layer of heat preservation layer that it, which is acted on, rising head melt is ensured the feeding effect of rising head than being solidified after the die cavity melt of bottom.
(4) process and detect：
Casting is cut off from the position that rising head connects with bottom with wire cutting machine tool first, obtained9
Sample blank, wherein flawless 4 of fracture is taken by GB/T228-2010《Metal material stretching test room temperature test method》Mark
Standard, it is processed in numerically controlled lathe；Part material is non-ferrous alloy, and its toughness plasticity is good, during processing, in order to ensure outside cylinder
Surface roughness requirement, need to use high-speed steel tool, and main cutting edge is ground sharp.After sample machines, in Shenzhen new three
Think to be stretched on microcomputer controlled electronic universal tester；
The metallographic specimen that composition influences on alloy is investigated, using wire cutting machine tool, in remaining 5 blanks of every group of furnace charge
Flawless 2 of rising head cut-off part is selected, is cut to the high samples of 20 × 15mm of Φ using wire cutting in the middle, recycles line
Cutting cuts out 12 × 15mm of Φ in the middle part of sample；
Sample processing scheme of the cooling velocity change to alloy structure performance impact is investigated, and similar to the above, whole processing
Process is all using wire cutting machine tool；
180# → 240# → 320# → 400# → 600# → 800# sand paper underhand polish → water flushing → rough polishing is used respectively
(P-1 type polishing machines, polishing agent are the aluminum oxide self-control magnesia magma that granularity is W5) (P-1 types polish for → fine polishing
Machine, polishing agent are the aluminum oxide self-control magnesia magma that granularity is W2) after → cotton ball soaked in alcohol cleaning → drying in metallography microscope
Observe on mirror, can be taken a picture after no marking；
Using Olympus-tokyo type metallography microscope sem observations alloy structure crystallize situation, each phase size, shape and point
Cloth, and take a picture；S3400N types ESEM (band EDS) is recycled to analyze tissue composition；Finally utilize DX-2500 types X
X ray diffractometer x carries out XRD spectrum analysis to alloy；
(5) Technology for Heating Processing, using T6 processing, i.e. solid solution+artificial aging.The richness that the effect of solid solution is formed when being by high temperature
Iron phase, by higher temperature, make its diffusion in the base.The effect of artificial aging is diffused in matrix when being by solid solution
In Fe-riched phase homogenization.This problem solid solubility temperature selects 525 DEG C, is incubated 4h, is quenched immediately in 70~80 DEG C of water after taking-up
Fire；180 DEG C of artificial aging, it is incubated 5h.
Data and graphic analyses：
Strengthen before going bad, the tensile strength of sample is as shown in table 2：
Table 2 strengthens the tensile strength of rotten preceding sample
It can analyze to obtain with reference to table 3, the tensile strength of alloy shows first to raise what is reduced afterwards with Mn/Fe increase
Trend, maximum 130.3MPa is obtained at Mn/Fe=0.6.Its reason should be the needle-like in alloy structure after adding Mn
Fe-riched phase is largely changed into herring-bone form, and the size of small part needle-like Fe-riched phase also becomes very small, and Fe-riched phase is to alloy substrate
Tear effect reduce, make alloy tensile property raise；In addition, with the needle-like phase size in Mn/Fe increase alloy structure
Have change trend, from Mn/Fe when be not readily observed and develop into and can substantially observe, the change causes needle-like Fe-riched phase pair
The tear effect of alloy becomes big, so as to which reduction trend occurs in tensile strength.
The influence of heat treatment also may compare from table 3 and intuitively observe, the alloy tension of several compositions is strong after heat treatment
Degree has all raised, and its reason is after solution treatment, and the Fe-riched phase acute angle passivation in alloy is obvious, reduces stress collection
In, possibility caused by crackle is reduced, the extension speed of crackle is slow down, so as to improve mechanical property；It can also react
It is less obvious to tensile strength raising to go out heat treatment, in order to avoid alloy surface burns when one of its reason is solution treatment
Damage, select temperature relatively lower, the dissolving and fracture to Fe-riched phase particularly needle-like Fe-riched phase are inadequate；Another reason is
As Mn/Fe=0.6, its needle-like Fe-riched phase is very small, is heat-treated to its abstriction unobvious, and with Mn/Fe increasing
Greatly, Fe-riched phase size increases, and thermal processes act is more obvious.
Mn/Fe=0.6 sample strengthen it is rotten, strengthen it is rotten after, the tensile strength of sample is as shown in table 3：
Table 3 strengthens the tensile strength of rotten rear sample
From table 3 it is observed that the alloy property strengthened after going bad significantly improves, tensile strength is brought up to from 130.3MPa
142MPa, because the needle-like Fe-riched phase strengthened in rotten rear alloy disappears, improve strength of alloy.And again through T6
After further Overheating Treatment, it might even be possible to up to 199MPa, to find out its cause, be because the α-Al disperses in alloy in the alloy,
Its mutual continuity is more preferable, thus improves the tensile strength of alloy.
Conclusion (of pressure testing) of the present invention：
(1) during Mn/Fe ＞ 0, the Fe-riched phase skewness in Al-15wt.%Si-3wt.%Fe-xMn alloys, Fu Tie
Together with mutually overlapping mutually segregation with primary silicon；As Mn/Fe increases, the pin in Al-15wt.%Si-3wt.%Fe-xMn alloys
Shape iron phase is aobvious first to reduce the trend increased again.In Mn/Fe=0.6, Needle like Iron Phase is minimum, and size is also minimum, and alloy tension is strong
Degree is preferably also.
(2) increase of cooling velocity, have to the segregation phenomenon of Fe-riched phase in Al-15wt.%Si-3wt.%Fe-xMn alloys
Larger improvement, but when exceeding certain cooling velocity, there is segregation degree to become big trend again；As cooling velocity is certain
In the range of increase, Al-15wt.%Si-3wt.%Fe-xMn alloy rigidities are increasing, and uniformity is also become better and better.
(3) by strengthening the Al-15wt.%Si-3wt.%Fe-1.8wt.%Mn-0.5wt.%Mg- after going bad
0.045wt.%P alloys, Fe-riched phase segregation is obvious, and it shows tiny needle-like and Chinese character shape, as cooling velocity increases, pin
The aobvious change trend again that first diminishes of shape Fe-riched phase；Tensile strength lifting is little under as cast condition, but after T6 is handled, tensile strength energy
It is greatly improved, reaches 199MPa.
(4) hardness of Al-15wt.%Si-3wt.%Fe-1.8wt.%Mn-0.5wt.%Mg-0.045wt.%P alloys
Had a distinct increment before more rotten than reinforcing, when cooling velocity is smaller, maximum 87.2HB can be reached, and its uniformity is preferable.
(5) by strengthening the Al-15wt.%Si-3wt.%Fe-1.8wt.%Mn-3wt.%Cu- after going bad
0.045wt.%P alloys, Fe-riched phase segregation still have, and it shows larger needle-like and Chinese character shape, as cooling velocity increases, pin
Shape Fe-riched phase shows change trend；Tensile strength has been lifted under as cast condition, can reach 151MPa.
The present invention is selected, with when flow scheme design by rational composition, and obtained high ferro alusil alloy mechanical property connects
Nearly even better than not iron content or the low alusil alloy of iron-holder, overcome technology prejudice, solve existing iron content and surpass well
The problem of target aluminium alloy cost recovery is big, recovery difficult is high.Therefore, the present invention compared with prior art for, technological progress ten
It is clearly demarcated to show, there are prominent substantive distinguishing features and significant progress.
It is embodiments of the invention as described above.The present invention is not limited to the above-described embodiments, anyone should learn that
The structure change made under the enlightenment of the present invention, the technical schemes that are same or similar to the present invention, each fall within this
Within the protection domain of invention.
Claims (4)
1. a kind of high ferro transcocrystallized Al-Si alloy, it is characterised in that weight percentage, consist of the following composition：Silicon
15%th, iron 3%, manganese 1.8%, copper 0-3%, magnesium 0-0.5%, phosphorus 0.045%, surplus are aluminium.
2. high ferro transcocrystallized Al-Si alloy as claimed in claim 1, it is characterised in that weight percentage, by following
Composition forms：Silicon 15%, iron 3%, manganese 1.8%, copper 3%, phosphorus 0.045%, surplus are aluminium.
3. high ferro transcocrystallized Al-Si alloy as claimed in claim 1, it is characterised in that weight percentage, by following
Composition forms：Silicon 15%, iron 3%, manganese 1.8%, magnesium 0.5%, phosphorus 0.045%, surplus are aluminium.
4. the preparation method of the high ferro transcocrystallized Al-Si alloy described in any one of claims 1 to 3, it is characterised in that including such as
Lower step：
(1) melting intermediate alloy：Using ZGJL-0.025-50-2.5 type intermediate frequency vacuum induction melting furnaces carry out that aluminium silicon is prepared
Intermediate alloy, ferro-aluminum intermediate alloy, aluminium manganese intermediate alloy, aluminum bronze intermediate alloy, magnalium intermediate alloy and aluminium phosphorus intermediate alloy 6
Kind intermediate alloy, wherein the weight percentage of the aluminium in 6 kinds of intermediate alloys is respectively：70%th, 80%, 90%, 50%,
65%th, 95.5%；
(2) intermediate alloy is dried：The intermediate alloy that step (1) obtains is put into box resistance electric furnace in proportion, with 140 DEG C of bakings
Roasting 8h；
(3) crucible is dried：Crucible is put into resistance electric furnace, is heated up to 200 DEG C, toasts 2h；
(4) casting mold is handled：First casting mold surface impurity and cleaning oil pollution are fallen, are then placed in box resistance electric furnace,
Using 200 DEG C of temperature 24h, ensure casting mold drying and surface cleaning；Casting mold takes out in time after drying, under
Layer material is brushed on mold cavity surface, is ensured that casting is smoothly stripped, after the completion of brushing, mould is placed in box resistance electric furnace and adopted
2~3 hours are incubated with 200 DEG C, ensures dry paint layer hardening；
(5) melting：Dried intermediate alloy is put into and completed in dry crucible, voltage is tuned up, starts melting, melting
Temperature setting is 820 DEG C, after raw material all melts, is incubated 15~20min, melt is seethed with excitement, and ensures that melt distribution is uniform, adopts
Crucible bottom is passed through with argon gas to be refined, and goes the removal of impurity；
(6) pour into a mould：First the surface scale in crucible is scooped out, then crucible is moved to above mould and poured into a mould, cooling,
The demoulding obtains bulk processing product；
(7) it is heat-treated：Using T6 processing, i.e. solid solution+artificial aging, solid solubility temperature selects 525 DEG C, is incubated 4h, after taking-up immediately
In 70~80 DEG C of quenching-in water；180 DEG C of artificial aging, cooling is to obtain high ferro transcocrystallized Al-Si alloy after being incubated 5h.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107937767A (en) * | 2017-12-28 | 2018-04-20 | 苏州仓松金属制品有限公司 | A kind of novel high-performance aluminum alloy materials and preparation method thereof |
| CN108929976A (en) * | 2018-07-10 | 2018-12-04 | 中南大学 | Graphene enhances low cerium Al-Si-Mg alloy and its casting method |
| WO2023015578A1 (en) * | 2021-08-11 | 2023-02-16 | 江苏大学 | Al-si-cu-fe-mn alloy and preparation method therefor |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4737206A (en) * | 1983-09-07 | 1988-04-12 | Showa Aluminum Kabushiki Kaisha | Extruded aluminum alloys having improved wear resistance and process for preparing same |
| CN1651586A (en) * | 2005-03-09 | 2005-08-10 | 沈阳工业大学 | Abrasion resistant, heat resistant high silicone aluminium alloy and its shaping technology |
| CN101087895A (en) * | 2004-10-15 | 2007-12-12 | Peak材料有限责任公司 | Aluminium-based alloy and moulded part consisting of said alloy |
| CN102965551A (en) * | 2012-11-26 | 2013-03-13 | 中国铝业股份有限公司 | Hypereutectic aluminium-silicon alloy and preparation method thereof |
| CN104480357A (en) * | 2014-12-05 | 2015-04-01 | 福州大学 | High-silicon aluminum alloy cylinder sleeve and preparation method thereof |
| CN105401012A (en) * | 2015-09-21 | 2016-03-16 | 辽宁工业大学 | Preparation method for novel pelletized hypereutectic Al-Si alloy |
-
2017
- 2017-06-30 CN CN201710524821.9A patent/CN107385284B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4737206A (en) * | 1983-09-07 | 1988-04-12 | Showa Aluminum Kabushiki Kaisha | Extruded aluminum alloys having improved wear resistance and process for preparing same |
| CN101087895A (en) * | 2004-10-15 | 2007-12-12 | Peak材料有限责任公司 | Aluminium-based alloy and moulded part consisting of said alloy |
| CN1651586A (en) * | 2005-03-09 | 2005-08-10 | 沈阳工业大学 | Abrasion resistant, heat resistant high silicone aluminium alloy and its shaping technology |
| CN102965551A (en) * | 2012-11-26 | 2013-03-13 | 中国铝业股份有限公司 | Hypereutectic aluminium-silicon alloy and preparation method thereof |
| CN104480357A (en) * | 2014-12-05 | 2015-04-01 | 福州大学 | High-silicon aluminum alloy cylinder sleeve and preparation method thereof |
| CN105401012A (en) * | 2015-09-21 | 2016-03-16 | 辽宁工业大学 | Preparation method for novel pelletized hypereutectic Al-Si alloy |
Non-Patent Citations (1)
| Title |
|---|
| 任颂赞等: "《金相分析原理及技术》", 31 August 2013, 上海科学技术文献出版社 * |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107937767A (en) * | 2017-12-28 | 2018-04-20 | 苏州仓松金属制品有限公司 | A kind of novel high-performance aluminum alloy materials and preparation method thereof |
| CN107937767B (en) * | 2017-12-28 | 2019-07-26 | 苏州仓松金属制品有限公司 | A kind of novel high-performance aluminum alloy materials and preparation method thereof |
| CN108929976A (en) * | 2018-07-10 | 2018-12-04 | 中南大学 | Graphene enhances low cerium Al-Si-Mg alloy and its casting method |
| CN108929976B (en) * | 2018-07-10 | 2020-03-17 | 中南大学 | Graphene-reinforced low-cerium Al-Si-Mg alloy and casting method thereof |
| WO2023015578A1 (en) * | 2021-08-11 | 2023-02-16 | 江苏大学 | Al-si-cu-fe-mn alloy and preparation method therefor |
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