CN107385284B - A kind of preparation method of high-speed rail transcocrystallized Al-Si alloy - Google Patents
A kind of preparation method of high-speed rail transcocrystallized Al-Si alloy Download PDFInfo
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- CN107385284B CN107385284B CN201710524821.9A CN201710524821A CN107385284B CN 107385284 B CN107385284 B CN 107385284B CN 201710524821 A CN201710524821 A CN 201710524821A CN 107385284 B CN107385284 B CN 107385284B
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- C22C1/02—Making non-ferrous alloys by melting
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/02—Making non-ferrous alloys by melting
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- 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
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Abstract
The invention discloses a kind of high-speed rail transcocrystallized Al-Si alloys and preparation method thereof, it is related to alusil alloy Material Field, weight percentage, high-speed rail 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, preparation method passes through first melting intermediate alloy, by intermediate alloy, melting is together in proportion again, finally by heat treatment process, obtain the alloy that tensile strength is much higher than Al-15wt.%Si control sample intensity, and hardness is compared before reinforcing is gone bad and is improved a lot, it can obtain the average hardness of 87.2HB, alloy material uniformity is also preferable, to obtain, mechanical property is close to be even better than the not high-speed rail alusil alloy of iron content or iron-content low aluminum silicon alloy, contain for changing iron The status for measuring exceeded aluminium alloy difficulty recycling plays a significant role and meaning.
Description
Technical field
The present invention relates to alusil alloy Material Fields, and in particular to a kind of preparation method of high-speed rail transcocrystallized Al-Si alloy.
Background technique
Alusil alloy is a kind of with aluminium, silicon forging as main component and casting alloy, in existing alusil alloy, Fe-riched phase
Often treated as a kind of harmful impurity, and in order to improve alloy property, the way that the prior art generallys use is logical
Cross change cooling velocity, addition neutralizer, melt overheat, alterant is added, dilution, precipitating, filtering, centrifugation removal, electromagnetism goes
Except the methods of change or removal Fe-riched phase, but the aluminium alloy cost recovery that such mode is easy to cause iron content exceeded it is high,
Recovery difficult is big.
Summary of the invention
The purpose of the present invention is: in view of the deficiencies of the prior art, a kind of high-speed rail transcocrystallized Al-Si alloy is provided, by Fe-riched phase
It is added in alusil alloy as a kind of reinforcing, increases considerably the iron content in alloy, harmful Fe-riched phase is changed into reinforcing
Phase, so as to improve alloy property, obtained high-speed rail alusil alloy mechanical property is not close to even better than iron content or iron-content be low
The status of alusil alloy, this aluminium alloy difficulty recycling exceeded for change iron content plays a significant role 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-speed rail transcocrystallized Al-Si alloy, weight percentage, including following component: silicon 15%, iron 3%, manganese
1.8%, copper 0-3%, magnesium 0-0.5%, phosphorus 0.045%, surplus are aluminium.
Preferably, weight percentage, the high-speed rail transcocrystallized Al-Si alloy consist of the following compositions: silicon
15%, iron 3%, manganese 1.8%, copper 3%, phosphorus 0.045%, surplus are aluminium.
Preferably, weight percentage, the high-speed rail transcocrystallized Al-Si alloy consist of the following compositions: silicon
15%, iron 3%, manganese 1.8%, magnesium 0.5%, phosphorus 0.045%, surplus are aluminium.
Based on above-mentioned alloy, the present invention also provides the preparation methods of the high-speed rail transcocrystallized Al-Si alloy, including walk as follows
It is rapid:
(1) it melting intermediate alloy: is prepared using ZGJL-0.025-50-2.5 type intermediate frequency vacuum induction melting furnace
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 as follows: 70%, 80%, 90%,
50%, 65%, 95.5%；
(2) dry intermediate alloy: the intermediate alloy that step (1) obtains is put into proportion in box resistance electric furnace, with 140
DEG C baking 8h；
(3) dry crucible: crucible is put into resistance electric furnace, is heated up to 200 DEG C, toasts 2h；
(4) casting mold is handled: first being fallen casting mold surface impurity and cleaning oil pollution, is then placed in box resistance electric furnace
In, for 24 hours using 200 DEG C of temperatures, guarantee casting mold drying and surface cleaning；It is taken out in time after casting mold is dry,
Layer material is brushed in lower mold mold cavity surface, guarantees that casting smoothly demoulds, after the completion of brushing, mold is placed in box resistance electric furnace
It is middle to keep the temperature 2~3 hours using 200 DEG C, guarantee dry paint layer hardening；
(5) melting: the intermediate alloy after drying being put into and is completed in dry crucible, voltage is tuned up, and starts melting,
Smelting temperature is set as 820 DEG C, after raw material all melts, keeps the temperature 15~20min, melt is made to boil, and guarantees that melt distribution is equal
It is even, crucible bottom is passed through using argon gas and is refined, impurity is removed；
(6) it is poured: first scooping out the surface scale in crucible, then crucible is moved to above mold and is poured,
Cooling, demoulding obtains bulk processing product；
(7) it is heat-treated: being handled using T6, i.e. solid solution+artificial aging, solid solubility temperature selects 525 DEG C, 4h is kept the temperature, after taking-up
Immediately in 70~80 DEG C of quenching-in water；180 DEG C of artificial aging, cooling obtains high-speed rail transcocrystallized Al-Si alloy after keeping the temperature 5h.
Compared with the existing technology, it is had the beneficial effect that caused by the present invention:
(1) in the present invention, using the Al-15wt.%Si control sample prepared under the same terms, its tensile strength under as cast condition
For 171.97MPa, 3wt.%Fe is added, alloying component is adjusted to after Al-15wt.%Si-3wt.%Fe to tension is strong under its as cast condition
Degree falls to 124.8MPa, and after the neutralizer Mn that Mn/Fe is 0.6 is added, tensile strength is up to 130.3MPa, then adds respectively
Enter Cu and Mg is strengthened, and is rotten using P, tensile strength is greatly improved, and tensile strength is up under as cast condition
151.4MPa and 142MPa all obtains maximum pulling strength after carrying out T6 processing than Al-15wt.%Si-3wt.%Fe high
199MPa is much higher than Al-15wt.%Si control sample intensity, and hardness is compared before reinforcing is gone bad and improved a lot, and can be obtained
The average hardness of 87.2HB, alloy material uniformity is also preferable, so the high-speed rail alusil alloy mechanical property that the present invention obtains connects
Nearly even better than not iron content or the low alusil alloy of iron-content, solve the exceeded aluminium alloy cost recovery of existing iron content it is big,
The high problem of recovery difficult.
(2) many documents all think that Fe-riched phase has been negative consequence in alusil alloy, it is considered that when Fe-riched phase is close
When 0.8wt.%, the intensity and hardness of alloy all rise, and after iron content is more than 0.8wt.%, the intensity and elongation of alloy have
Very big reduction, so the prior art is all to improve alloy property from the mode for changing Fe-riched phase and removal Fe-riched phase.But the application
It goes to improve alloy property from the angle opposite with the prior art, i.e., Fe-riched phase is added to aluminium silicon as a kind of reinforcing and closed
Jin Zhong increases considerably the iron content (iron content increases to 3%) in alloy, by the way that corresponding alterant, neutralizer, change is added
Harmful Fe-riched phase is changed into hardening constituent by the methods of cooling velocity, so as to improve alloy property, obtained high-speed rail alusil alloy power
Performance is learned close to even better than not iron content or the low alusil alloy of iron-content.This not only overcomes the technology prejudice of industry, but also
The aluminium alloy difficulty recycling status exceeded for change iron content plays a significant role and meaning.
(3) when Mn and Fe ratio 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.
Detailed description of the invention
Fig. 1 is flow diagram of the invention.
Fig. 2 is main view, left view and the top view for the mould upstream that the present invention uses；
Fig. 3 is main view, left view and the top view for the mold lower part that the present invention uses；
Specific embodiment
Invention is further described in detail with reference to the accompanying drawings and detailed description.Embodiments of the present invention packet
It includes but is not limited to the following example.
Embodiment
The present invention provides a kind of high-speed rail transcocrystallized Al-Si alloy, alloy mechanical property, which can be close to, to be even better than free of
Iron or the low alusil alloy of iron-content.As shown in Figure 1, the process that the present invention prepares high-speed rail 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 frequency vacuum induction melting furnace
Preparation.It pours into respectively and is divided into Al-30wt.%Si, Al-10wt.%Mn, Al-20wt.%Fe, Al-4.5wt.%P, Al-
The intermediate alloy of 50wt.%Cu, Al-35wt.%Mg, intermediate alloy are the alloys for preventing high temperature using the purpose of vacuum melting furnace
Element is oxidized, and guarantees the accurate of alloy each element additional amount.
(2) molten alloy: SG-5-12 resistance electro-smelting alloy is used, it is therefore an objective to make sample melting environment closer to life
Practice is produced, is conducive to the popularization of experimental data, corresponding intermediate alloy furnace charge will be prepared before melting by table 1 and be respectively put into box electricity
It hinders in electric furnace, with 140 DEG C of baking 8h, it is therefore an objective to remove the moisture in raw material, first corundum crucible is built before melting and is put into resistance electricity
In furnace, 200 DEG C are heated up to, toasts 2h, purpose is identical with dry furnace charge, primarily to dry crucible；
1 each group test specimen alloy composition of table
When melting, the furnace charge after drying will be prepared and be put into complete to tune up voltage in dry crucible, melting is started.
Smelting temperature is set as 820 DEG C.After raw material all melts, 15~20min is kept the temperature, melt is made to boil, guarantees that melt distribution is equal
It is even, crucible bottom is passed through using argon gas and is refined, impurity is removed.Before casting, first surface scale is scooped out, then by crucible
It is moved to above mold and is poured.
(3) it is poured: needing to prepare tensile sample, the metallographic specimen under heterogeneity and different cooling, through analyzing, if
The mould structure for counting use is as shown in Figure 2 and Figure 3, and mold is divide into upper part and lower part, and top is to emit shape of the mouth as one speaks chamber, by left and right two halves group
At, as shown in Fig. 2, lower part 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, for feeding needs, guarantees casting quality, the upper end side thickness of die of left and right two halves part is subtracted
It is small, it transmits the melt heat in the type chamber of lower end faster, is solidified prior to upper end；It, need to be clear by die surface impurity and greasy dirt before casting
Reason is fallen, and is then placed in box resistance electric furnace, for 24 hours using 200 DEG C of temperatures, guarantees mold drying and surface cleaning；Mould
It is taken out in time after tool is dry, brushes layer material on lower part tensile sample pickup type cavity mould surface, guarantee that casting smoothly demoulds.With
10%ZnO2, 4~5% waterglass, convert and coating be made in water；After the completion of brushing, mold is placed in box resistance electric furnace and is adopted
2~3 hours are kept the temperature with 200 DEG C, guarantees dry paint layer hardening；It, need to be by aluminium silicate fiber Wesy before the hot top mould swabbing of top
Waterglass is uniformly layered on mold interior wall surfaces after soaking, then dry baking is put into resistance electric furnace after being compacted with tool；It is acted on
It is manufacture one layer of heat preservation layer, makes riser melt than solidifying after the type chamber melt of lower part, guarantee the feeding effect of riser.
(4) it processes and detects:
Casting is cut off with wire cutting machine tool from the position that riser is connected with lower part first, is obtained9
Sample blank, take wherein flawless 4 of fracture marked by GB/T228-2010 " metal material stretching test room temperature test method "
Standard is processed in numerically controlled lathe；Part material is non-ferrous alloy, and toughness plasticity is good, when processing, in order to guarantee external cylindrical surface
Roughness requirements need to use high-speed steel tool, and main cutting edge are ground sharp.Sample after processing is completed, is newly thought carefully in Shenzhen
It is stretched on microcomputer controlled electronic universal tester；
The metallographic specimen that ingredient influences alloy is investigated, using wire cutting machine tool, in remaining 5 blanks of every group of furnace charge
Selection riser cut-off part flawless 2 is cut to Φ 20 × 15mm high sample using wire cutting in the middle, and line is recycled to cut
12 × 15mm of Φ in the middle part of a sample is cut to cut out；
It investigates cooling velocity and changes the sample processing scheme influenced on alloy structure performance and similar to the above, entire processing
Process all uses 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 machine, polishing agent are the aluminium oxide self-control magnesia magma that granularity is W5) → fine polishing (P-1 type polishing machine,
Polishing agent is the aluminium oxide self-control magnesia magma that granularity is W2) after → cotton ball soaked in alcohol cleaning → drying on metallographic microscope
It observes, can take a picture after no marking；
Using Olympus-tokyo type metallography microscope sem observation alloy structure crystallize situation, each phase size, shape and point
Cloth, and take a picture；S3400N type scanning electron microscope (band EDS) is recycled to analyze tissue composition；Finally utilize DX-2500 type X
X ray diffractometer x carries out XRD diagram spectrum analysis to alloy；
(5) heat treatment process is handled using T6, i.e. solid solution+artificial aging.The richness that the effect of solid solution is formed when being by high temperature
Iron phase makes its diffusion in the base by higher temperature.The effect of artificial aging will be spread in the base when will be dissolved
Fe-riched phase homogenization.This project solid solubility temperature selects 525 DEG C, 4h is kept the temperature, immediately in 70~80 DEG C of quenching-in water after taking-up；
180 DEG C of artificial aging, keep the temperature 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 in conjunction with table 2, with the increase of Mn/Fe, show first to increase reduces afterwards for the tensile strength of alloy
Trend obtains maximum value 130.3MPa at Mn/Fe=0.6.Its reason should be the needle-shaped richness in alloy structure after Mn is added
Iron phase is largely changed into herring-bone form, and the size of the needle-shaped Fe-riched phase of small part also becomes very small, and Fe-riched phase is to alloy substrate
Tearing effect reduces, and increases alloy tensile property；In addition, as the needle-shaped phase size in the increase alloy structure of Mn/Fe has
Change trend is not readily observed development when from Mn/Fe can obviously to observe, which causes needle-shaped Fe-riched phase to alloy
Tearing effect become larger, so that there is decreasing trend in tensile strength.
The influence of heat treatment also may compare from table 2 and intuitively observe, the alloy tension of several ingredients is strong after heat treatment
Degree is all increased, the reason is that the Fe-riched phase acute angle passivation in alloy is obvious after solution treatment, reduces stress collection
In, a possibility that crackle generates is reduced, the extension speed of crackle is slowed down, to improve mechanical property；It can also react
Be heat-treated out tensile strength is improved it is less obvious, reason first is that in order to avoid alloy surface is burnt when solution treatment
Damage selects temperature relatively lower, and the dissolution and fracture for be especially needle-shaped Fe-riched phase to Fe-riched phase are not enough；Another reason is to work as
Its needle-shaped Fe-riched phase is very small when Mn/Fe=0.6, be heat-treated it is unobvious to its abstriction, and with the increase of Mn/Fe,
Fe-riched phase size increases, and thermal processes act is more obvious.
The sample of Mn/Fe=0.6 strengthen and is gone bad, is strengthened after going bad, 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 increased to from 130.3MPa
142MPa improves strength of alloy this is because the needle-shaped Fe-riched phase strengthened in rotten rear alloy disappears.And again through T6 into
After one step Overheating Treatment, it might even be possible to up to 199MPa, to find out its cause, be because alloy in α-Al disperse in the alloy,
Mutual continuity is more preferable, thus improves the tensile strength of alloy.
Conclusion (of pressure testing) of the present invention:
(1) when Mn/Fe > 0, the Fe-riched phase in Al-15wt.%Si-3wt.%Fe-xMn alloy is unevenly distributed, Fu Tie
Together with mutually overlapping mutually segregation with primary silicon；Needle as Mn/Fe increases, in Al-15wt.%Si-3wt.%Fe-xMn alloy
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, strength of alloy
It is preferably also.
(2) increase of cooling velocity has the segregation phenomenon of Fe-riched phase in Al-15wt.%Si-3wt.%Fe-xMn alloy
Larger improvement, but when being more than certain cooling velocity, and have the tendency that segregation degree becomes larger；As cooling velocity is in certain model
Interior increase is enclosed, Al-15wt.%Si-3wt.%Fe-xMn alloy rigidity is 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 alloy, Fe-riched phase segregation is obvious, shows tiny needle-shaped and Chinese character shape, needle-shaped as cooling velocity increases
The aobvious change trend again that first becomes smaller of Fe-riched phase；Tensile strength is promoted less under as cast condition, but after T6 is handled, tensile strength can be obtained
It increases substantially, reaches 199MPa.
(4) hardness of Al-15wt.%Si-3wt.%Fe-1.8wt.%Mn-0.5wt.%Mg-0.045wt.%P alloy
It has a distinct increment before more rotten than reinforcing, when cooling velocity is smaller, maximum value 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 alloy, Fe-riched phase segregation still have, and show larger needle-shaped and Chinese character shape, needle-shaped as cooling velocity increases
Fe-riched phase shows change trend；Tensile strength is promoted under as cast condition, can reach 151MPa.
The present invention is selected by reasonable ingredient, with when process design, obtained high-speed rail alusil alloy mechanical property connect
Nearly even better than not iron content or the low alusil alloy of iron-content, overcome technology prejudice well, it is super to solve existing iron content
The problem that 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 aobvious, there is substantive distinguishing features outstanding and significant progress.
It is as described above the embodiment of the present invention.The present invention is not limited to the above-described embodiments, anyone should learn that
The structure change made under the inspiration of the present invention, the technical schemes that are same or similar to the present invention each fall within this
Within the protection scope of invention.
Claims (1)
1. a kind of preparation method of high-speed rail transcocrystallized Al-Si alloy, which is characterized in that the high-speed rail transcocrystallized Al-Si alloy is pressed
Weight consists of the following compositions: silicon 15%, iron 3%, manganese 1.8%, magnesium 0.5%, phosphorus 0.045%, surplus are aluminium；It is described
Preparation method include the following steps:
(1) it melting intermediate alloy: using ZGJL-0.025-50-2.5 type intermediate frequency vacuum induction melting furnace carries out that aluminium silicon is prepared
5 kinds of intermediate alloy, ferro-aluminum intermediate alloy, aluminium manganese intermediate alloy, magnalium intermediate alloy and aluminium phosphorus intermediate alloy intermediate alloys,
In the weight percentage of aluminium in 5 kinds of intermediate alloys be respectively as follows: 70%, 80%, 90%, 65%, 95.5%；
(2) dry intermediate alloy: the intermediate alloy that step (1) obtains is put into proportion in box resistance electric furnace, is dried with 140 DEG C
Roasting 8h；
(3) dry crucible: 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,
For 24 hours using 200 DEG C of temperatures, guarantee casting mold drying and surface cleaning；It is taken out in time after casting mold is dry, under
Layer material is brushed on mold cavity surface, is guaranteed that casting smoothly demoulds, after the completion of brushing, mold is placed in box resistance electric furnace and is adopted
2 ~ 3 hours are kept the temperature with 200 DEG C, guarantees dry paint layer hardening；
(5) melting: the intermediate alloy after drying being put into and is completed in dry crucible, voltage is tuned up, and starts melting, melting
Temperature setting is 820 DEG C, after raw material all melts, keeps the temperature 15 ~ 20min, melt is made to boil, and guarantees that melt distribution is uniform, adopts
Crucible bottom is passed through with argon gas to be refined, and impurity is removed；
(6) it is poured: first scooping out the surface scale in crucible, then crucible is moved to above mold and is poured, cooling,
Demoulding obtains bulk processing product；
(7) it is heat-treated: being handled using T6, i.e. solid solution+artificial aging, solid solubility temperature selects 525 DEG C, keeps the temperature 4h, after taking-up immediately
In 70 ~ 80 DEG C of quenching-in water；180 DEG C of artificial aging, cooling obtains high-speed rail transcocrystallized Al-Si alloy after keeping the temperature 5h.
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| 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 |
| CN108929976B (en) * | 2018-07-10 | 2020-03-17 | 中南大学 | Graphene-reinforced low-cerium Al-Si-Mg alloy and casting method thereof |
| CN113737063A (en) * | 2021-08-11 | 2021-12-03 | 江苏大学 | Al-Si-Cu-Fe-Mn alloy and preparation method thereof |
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| 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 |
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| CN105401012A (en) * | 2015-09-21 | 2016-03-16 | 辽宁工业大学 | Preparation method for novel pelletized hypereutectic Al-Si alloy |
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|---|---|---|---|---|
| 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 |
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Inventor after: Li Linxin Inventor after: Chen Xianjun Inventor after: Xu Liping Inventor before: Li Linxin Inventor before: Chen Xianjun |