CN109457148A - A kind of Al-Mg-Mn-Cu alloy and preparation method thereof - Google Patents
A kind of Al-Mg-Mn-Cu alloy and preparation method thereof Download PDFInfo
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- CN109457148A CN109457148A CN201811592012.2A CN201811592012A CN109457148A CN 109457148 A CN109457148 A CN 109457148A CN 201811592012 A CN201811592012 A CN 201811592012A CN 109457148 A CN109457148 A CN 109457148A
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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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22F1/047—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 magnesium as the next major constituent
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Abstract
The present invention provides a kind of Al-Mg-Mn-Cu alloy, ingredients are as follows: the Mg of 2.3~3wt%；The Cu of 0.1~0.5wt%；The Ho of 0.1~0.5wt%；The Ce of 0.2~1wt%；The Ti of 0.01~0.2wt%；The Zr of 0.05~0.3wt%；The Mn of 0.1~0.3wt%；Surplus is Al；The Ho and Ce total mass content: the mass content of Ti: the mass content of Zr is (3~6): 1:2.The present invention uses suitable alloy element and rationally controls the usage ratio of alloying element, and invigoration effect can be played to alloy matrix aluminum and forming pseudoeutectic transitional face increases the mobility of alloy, to improve the comprehensive performance of alloy.The present invention also provides a kind of preparation methods of Al-Mg-Mn-Cu alloy.
Description
Technical field
The present invention relates to technical field of aluminum alloy technology more particularly to a kind of Al-Mg-Mn-Cu alloy and preparation method thereof.
Background technique
The microalloying modification of aluminium alloy is concentrated mainly in the raising to the original performance of aluminium alloy etc., such as increases aluminium
The elongation percentage or intensity of alloy, or the intensity of cond aluminium is improved, homogenization recrystallization temperature of alloy material etc. is improved,
While improving aluminium alloy comprehensive performance using microalloying, for improving the mobility of aluminium alloy, change the solidification of aluminium alloy
It is had not been reported in terms of temperature range.
Summary of the invention
In view of this, the present invention mentions the purpose of the present invention is to provide a kind of Al-Mg-Mn-Cu alloy and preparation method thereof
The Al-Mg-Mn-Cu alloy of confession has good mobility and mechanical property, good combination property.
The present invention provides a kind of Al-Mg-Mn-Cu alloy, ingredients are as follows:
The Mg of 2.3~3wt%；
The Cu of 0.1~0.5wt%；
The Ho of 0.1~0.5wt%；
The Ce of 0.2~1wt%；
The Ti of 0.01~0.2wt%；
The Zr of 0.05~0.3wt%；
The Mn of 0.1~0.3wt%；
Surplus is Al.
In the present invention, the mass content of the Ho is preferably 0.2~0.4%, and more preferably 0.3%.
In the present invention, the mass content of the Ce is preferably 0.3~0.9%, and more preferably 0.4~0.8%, more preferably
It is 0.5~0.7%, most preferably 0.6%.
In the present invention, the mass content of the Ti is preferably 0.03~0.16%, and more preferably 0.06~0.13%, more
Preferably 0.08~0.11%, most preferably 0.09~0.1%.
In the present invention, the mass content of the Zr is preferably 0.1~0.25%, and more preferably 0.15~0.2%, it is optimal
It is selected as 0.16~0.18%.
In the present invention, the mass content of the Mg is preferably 2.5~2.8%, and more preferably 2.5~2.6%, most preferably
It is 2.5%.
In the present invention, the mass content of the Mn is preferably 0.15~0.3%, and more preferably 0.2~0.3%, it is optimal
It is selected as 0.3%.
In the present invention, the mass content of the Cu is preferably 0.2~0.4%, and more preferably 0.2~0.3%, most preferably
It is 0.2%.
In the present invention, the Al-Mg-Mn-Cu alloy is preferably Al-2.5%Mg-0.3%Mn-0.2%Cu alloy.?
In the present invention, the mass content of the Ho is preferably that the mass content of 0.1~0.5%, Ce is preferably the quality of 0.2~1%, Zr
Content is preferably that the mass content of 0.05~0.3%, Ti is preferably 0.01~0.1%.
In the present invention, in order to guarantee the mechanical property of Al-Mg-Mn-Cu alloy, Ho, Ce and Ti, Zr constituent content are preferred
According to a certain percentage.In the present invention, the Ho and Ce total mass content: the mass content of Ti: the mass content of Zr is preferred
For (3~6): 1:2, more preferably (3.5~5.5): 1:2, most preferably (4~5): 1:2.
In the present invention, the Ho and Ce total mass content preferably >=0.4%；The Ti and Zr total mass content is excellent
Choosing >=0.2%.In the present invention, the mass content of the Mg is preferably 2.5wt%, at the same Ho and Ce it is total mass content it is preferred
>=0.5%, while the mass content that Ho and Ce is total: the mass content of Ti: the mass content of Zr is preferably (3~6): 1:2.
In the present invention, the ingredient of the Al-Mg-Mn-Cu alloy is preferred are as follows: the Mn of the Mg of 2.5wt%, 0.3wt%,
The Ti of the Zr of the Ce of the Ho of the Cu of 0.2wt%, 0.4wt%, 0.3wt%, 0.2wt%, 0.1wt%, surplus Al.
The present invention uses suitable alloy element, and invigoration effect can be played to alloy matrix aluminum and is formed pseudo- total
Brilliant transitional face increases the mobility of alloy, to improve the comprehensive performance of alloy.
The present invention attempt using microalloying as inducement, enable aluminum alloy in primary alloy constituent solidification precipitation sequence generation
Change, and then cause solid solubility variation at room temperature, so that its performance be made to change.It is found by the numerous studies of inventor,
Under the composite inoculating effect of Ho, Ce, Ti, Zr, make Al-Mg-Mn-Cu alloy that there is excellent casting fluidity, compactness, it is narrow
Temperature range and unique comprehensive mechanical performance.Collective effect of the present invention in more kinds of micro alloying elements of Ho, Ce, Ti, Zr
Under, be solid-solution in aluminium alloy, selectively become α phase forming core core, selectively with main alloy element Mg, Mn, Cu
The area GP of precipitate complicated composition ingredient is simultaneously gathered in α phase crystal boundary, and the area GP with α phase precipitate constitutes pseudoeutectic so that alloy
Crystallization temperature section narrows, and mobility enhancing, crystal grain becomes smaller, and forms the work that refined crystalline strengthening, dispersion-strengtherning and transitional face are strengthened
With.
The present invention provides a kind of preparation methods of Al-Mg-Mn-Cu alloy described in above-mentioned technical solution, comprising:
The source Al, the source Mg, the source Ho, the source Zr, the source Mn, the source Cu, the source Ce and the source Ti are subjected to melting, obtain aluminium alloy；
The aluminium alloy is subjected to die casting, obtains Al-Mg-Mn-Cu alloy.
In the present invention, the source Al is preferably commercial-purity aluminium.
In the present invention, the source Mg is preferably industrial magnesium ingot.
In the present invention, the source Ho is preferably Ho metal, and the purity of the Ho metal is preferably 97~99%, more preferably
It is 98%.
In the present invention, the source Zr is preferably Mg-Zr intermediate alloy, and the quality of Zr contains in the Mg-Zr intermediate alloy
Amount preferably 25~35%, more preferably 28~32%, most preferably 30%.
In the present invention, the source Mn is preferably Al-Mn intermediate alloy, and the quality of Mn contains in the Al-Mn intermediate alloy
Amount preferably 15~25%, more preferably 18~22%, most preferably 20%.
In the present invention, the source Cu is preferably Al-Cu intermediate alloy, and the quality of Cu contains in the Al-Cu intermediate alloy
Amount preferably 45~55%, more preferably 48~52%, most preferably 50%.
In the present invention, the source Ce is preferably richness Ce mischmetal.
In the present invention, the source Ti is preferably fluotitanate.
In the present invention, the dosage in the source Al, the source Mg, the source Ho, the source Zr, the source Mn, the source Cu, the source Ce and the source Ti makes to be prepared into
To Al-Mg-Mn-Cu alloy ingredient meet Al-Mg-Mn-Cu alloying component described in above-mentioned technical proposal requirement.
In the present invention, the melting carries out preferably in intermediate frequency furnace.In the present invention, the temperature of the melting is excellent
It is selected as 830~870 DEG C, more preferably 840~860 DEG C, most preferably 850 DEG C.
The present invention needs that alloy is made to have low solidification temperature range, high fluidity while with excellent mechanical performances
And the compactness of die casting tissue, fusion process preferably control technique and are adjusted, it is preferably suitable to the addition of alloying element
Sequence and additional proportion are adjusted.In the present invention, the method for the melting is preferred are as follows:
The source Al, the source Mn and the source Cu are heated to 850 DEG C, fusing is stirred after adding the covering of the source Ti, then adds the source Ho
With the source Ce, the source Zr and the source Mg are added, refines slagging-off after completing alloying.
The present invention does not have special limitation to the method for the refining slagging-off, is closed using aluminium well known to those skilled in the art
The technical solution for refining, removing the gred in golden preparation process.
In the present invention, the equipment of the die casting is preferably die casting machine, more preferably D350 Toshiba die casting machine.In the present invention
In, the temperature of the die casting is preferably 660~700 DEG C, more preferably 670~690 DEG C, most preferably 680 DEG C.In the present invention
In, the speed of the die casting is preferably 1~2m/s, more preferably 1.2~1.8m/s, more preferably 1.4~1.6m/s, most preferably
For 1.5m/s.In the present invention, the mould temperature of the die casting is preferably 260~300 DEG C, and more preferably 270~290 DEG C, most preferably
It is 280 DEG C.
The alloy that method provided by the invention is prepared has under as cast condition from quenching characteristics, natrual ageing 7 days, can be real
Existing tensile strength and yield strength improve 25~30%, and elongation percentage can be improved to 20~30%.
In the present invention, obtained die-cast product is preferably subjected to ageing treatment after the completion of the die casting.In the present invention,
The temperature of the ageing treatment is preferably 180~220 DEG C, more preferably 190~210 DEG C, most preferably 200 DEG C；The timeliness
Time be preferably 6~10 hours, more preferably 7~9 hours, most preferably 8 hours.In the present invention, the timeliness is cold
But mode is preferably air-cooled.
Micro alloying element ratio is suitable in Al-Mg-Mn-Cu alloy provided by the invention, under Die Casting Condition, removes conduct
Outside the ingredient of solidification nucleation core, the Mg that the microalloying ingredient and main component being preferentially precipitated are precipitated forms continuous bend crystal boundary
It is complicated that pseudoeutectic is mutually formed with the symbiosis of α phase, and strengthened with solution strengthening, dispersion-strengtherning and crystallite and improve mechanical performance, such as Fig. 1 institute
The microscopic structure shown.If some microalloy Ingredient Amounts in the present invention are beyond the scope of this invention, it is possible to create isolate crystalline substance
The coarse hard phase on boundary causes elongation percentage to decline, and crystallization temperature section broadens, mobility decline, to make the compactness and crystalline substance of alloy
The uniformity of grain is deteriorated, such as comparative example 1.
The present invention adds Ho, Ce, Ti, Zr with certain alloying sequence by a certain percentage in Al-Mg-Mn-Cu alloy
Element is simultaneously used cooperatively corresponding smelting technology, under the composite inoculating effect of Ho, Ce, Ti, Zr, has the aluminium alloy obtained
Excellent mobility and compactness, while there is good mechanical property.
Detailed description of the invention
In order to more clearly explain the embodiment of the invention or the technical proposal in the existing technology, to embodiment or will show below
There is attached drawing needed in technical description to be briefly described, it should be apparent that, the accompanying drawings in the following description is only this
The embodiment of invention for those of ordinary skill in the art without creative efforts, can also basis
The attached drawing of offer obtains other attached drawings.
Fig. 1 is the structural schematic diagram of beta alloy mobility device of the present invention；
Fig. 2 is the tundish structural schematic diagram of beta alloy mobility device of the present invention；
Fig. 3 is the spiral pouring gate structure schematic diagram of beta alloy mobility device of the present invention；
Fig. 4 is the microscopic structure metallograph of alloy prepared by the embodiment of the present invention 2.
Specific embodiment
Following will be combined with the drawings in the embodiments of the present invention, and technical solution in the embodiment of the present invention carries out clear, complete
Site preparation description, it is clear that described embodiments are only a part of the embodiments of the present invention, instead of all the embodiments.It is based on
Embodiment in the present invention, it is obtained by those of ordinary skill in the art without making creative efforts every other
Embodiment shall fall within the protection scope of the present invention.
The alloy that following embodiment of the present invention is prepared is according to GB/T7999-2007 " aluminium and aluminium alloy photo-electronic directly reading light
Spectrometer analysis " and " the 25th part of aluminium and aluminum alloy chemically analysis method: inductively coupled plasma body GB/T20975.25-2008
Atomic emission spectrometry ", the detection of alloying component is carried out using direct-reading spectrometer and ICP (emission spectrometer).
The tensile strength of the alloy that following embodiment of the present invention is prepared, yield strength, elongation percentage mechanical property according to
GB/T228.1-2010 " metal material stretching test part 1: room temperature test method ", is detected using universal testing machine.
The method of beta alloy mobility in following embodiment of the present invention are as follows:
Spiral flow length measuring device (cast iron quality) is put into batch-type furnace and is preheated to 200 DEG C for use；Preparation is closed
Molten metal during gold is kept the temperature at 680 DEG C, when test, is poured into the tundish of measuring device with bale-out aluminium alloy is poured, is made it
Discharge port 30mm is overflowed across, aluminium alloy is allowed to flow freely, by frozen metal spiral sample together with tundish one after aluminium alloy solidifies completely
It rises and takes out, measure helix length.The schematic diagram of the structure snd size of Spiral flow length measuring device is as shown in Figure 1, Fig. 2 is to pour
The structure snd size schematic diagram of cup, Fig. 3 are the structure snd size schematic diagram of spiral running channel, wherein adjacent two screw threads of spiral running channel
The distance between be 20mm, the dimensional units in FIG. 1 to FIG. 3 are millimeter (mm).
Raw materials used following embodiment of the present invention is commercial goods.
Embodiment 1
The melting in medium-frequency induction furnace, by industrial pure Al, Al-20%Mn intermediate alloy and Al-50%Cu intermediate alloy
850 DEG C are heated to according to the fusing of prealloy composition proportion, is stirred after fluotitanate covering is added according to prealloy composition proportion
Fusing is mixed, and Ho metal block and richness Ce mischmetal that purity is 98% is added, Mg-30%Zr intermediate alloy and work is then added
Industry Mg ingot, carries out refining slagging-off, obtains aluminium alloy.
680 DEG C of heat preservations in resistance furnace by obtained aluminium alloy, 20 × 100 are cast into using D350 Toshiba die casting machine ×
The sheet test piece of 2.5mm, die casting speed be 1.5m/s, 280 DEG C of mould temperature.
It is air-cooled after the ageing treatment that the test piece obtained after die casting is carried out 8 hours at 200 DEG C, obtain alloy components.
According to method described in above-mentioned technical proposal, the alloy components ingredient that the embodiment of the present invention 1 is prepared is tested.Through examining
It surveys, the alloy components ingredient result that the embodiment of the present invention 1 is prepared are as follows: the Mn of the Mg of 2.51wt%, 0.29wt%, 0.18wt%
Cu, the Ti of the Zr of the Ce of the Ho of 0.17wt%, 0.2wt%, 0.09wt%, 0.08wt%, surplus Al.
The alloy mechanical property and stream that the embodiment of the present invention 1 is prepared according to method described in above-mentioned technical proposal
Dynamic property is detected, and testing result is as shown in table 1, and table 1 is the performance detection of the alloy of the embodiment of the present invention and comparative example preparation
As a result.
Embodiment 2
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Ce of the Ho of the Cu of the Mn of the Mg of 2.55wt%, 0.25wt%, 0.19wt%, 0.36wt%, 0.3wt%,
The Ti of the Zr of 0.18wt%, 0.12wt%, surplus Al.
Metallographic structure detection is carried out to the alloy components that the embodiment of the present invention 2 is prepared, testing result is as shown in Figure 4.
The mechanical property for the alloy that the embodiment of the present invention 2 is prepared according to method described in above-mentioned technical proposal and
Mobility is detected, and testing result is as shown in table 1.
Comparative example 1
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Ho of the Cu of the Mn of the Mg of 2.53wt%, 0.26wt%, 0.18wt%, 0.55wt%, 0.35wt%'s
The Ti of the Zr of Ce, 0.21wt%, 0.13wt%, surplus Al.
The mechanical property for the alloy components that comparative example 1 of the present invention is prepared according to method described in above-mentioned technical proposal with
And mobility is detected, testing result is as shown in table 1.
Comparative example 2
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Ti of the Ce of the Cu of the Mn of the Mg of 2.5wt%, 0.3wt%, 0.2wt%, 0.3wt%, 0.15wt%, it is remaining
Amount is Al.
The mechanical property for the alloy components that comparative example 2 of the present invention is prepared according to method described in above-mentioned technical proposal with
And mobility is detected, testing result is as shown in table 1.
Comparative example 3
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Zr of the Ce of the Cu of the Mn of the Mg of 2.5wt%, 0.3wt%, 0.2wt%, 0.25wt%, 0.2wt%, it is remaining
Amount is Al.
The mechanical property for the alloy components that comparative example 3 of the present invention is prepared according to method described in above-mentioned technical proposal with
And mobility is detected, testing result is as shown in table 1.
Comparative example 4
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Ho of the Cu of the Mn of the Mg of 2.5wt%, 0.3wt%, 0.2wt%, 0.4wt%, surplus Al.
The mechanical property for the alloy components that comparative example 4 of the present invention is prepared according to method described in above-mentioned technical proposal with
And mobility is detected, testing result is as shown in table 1.
Comparative example 5
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Cu of the Mn of the Mg of 2.45wt%, 0.25wt%, 0.2wt%, surplus Al.
The mechanical property for the alloy components that comparative example 5 of the present invention is prepared according to method described in above-mentioned technical proposal with
And mobility is detected, testing result is as shown in table 1.
Comparative example 6
Alloy components are prepared according to method described in embodiment 1, the difference from embodiment 1 is that, the conjunction being prepared
The ingredient of golden part are as follows: the Ce of the Ho of the Cu of the Mn of the Mg of 4.5wt%, 0.25wt%, 0.18wt%, 0.35wt%, 0.32wt%,
The Ti of the Zr of 0.2wt%, 0.1wt%, surplus Al.
The mechanical property for the alloy components that comparative example 6 of the present invention is prepared according to method described in above-mentioned technical proposal with
And mobility is detected, testing result is as shown in table 1.
Comparative example 7
Outsourcing ADC12 casts Al-Si12 alloy.
According to the mechanical property and flowing of the alloy that method described in above-mentioned technical proposal provides comparative example 7 of the present invention
Property is detected, and testing result is as shown in table 1.
The alloy property testing result that 1 embodiment of the present invention of table and comparative example are prepared
As shown in Table 1, the alloy of the alloying component in the present invention and component content has preferable mobility and mechanics
The comprehensive performance of performance, individually addition a certain kind or two kinds of micro constitutents or alloying component ratio are not in the scope of the present invention
The alloy of acquisition cannot obtain active balance in mechanical property and mobility.It is best with alloy property prepared by embodiment 2, no
Only tensile strength, yield strength are high, elongation percentage is high, and mobility is also fine.
As seen from the above embodiment, the present invention provides a kind of Al-Mg-Mn-Cu alloy, ingredients are as follows: 2.3~3wt%'s
Mg；The Cu of 0.1~0.5wt%；The Ho of 0.1~0.5wt%；The Ce of 0.2~1wt%；The Ti of 0.01~0.2wt%；0.05~
The Zr of 0.3wt%；The Mn of 0.1~0.3wt%；Surplus is Al；The Ho and Ce total mass content: the mass content of Ti: Zr
Mass content be (3~6): 1:2.The present invention uses suitable alloy element and rationally controls the amount ratio of alloying element
Example, invigoration effect can be played to alloy matrix aluminum and forming pseudoeutectic transitional face increases the mobility of alloy, to mention
The comprehensive performance of high alloy.
Claims (9)
1. a kind of Al-Mg-Mn-Cu alloy, ingredient are as follows:
The Mg of 2.3~3wt%；
The Cu of 0.1~0.5wt%；
The Ho of 0.1~0.5wt%；
The Ce of 0.2~1wt%；
The Ti of 0.01~0.2wt%；
The Zr of 0.05~0.3wt%；
The Mn of 0.1~0.3wt%；
Surplus is Al；
The Ho and Ce total mass content: the mass content of Ti: the mass content of Zr is (3~6): 1:2.
2. Al-Mg-Mn-Cu alloy according to claim 1, which is characterized in that the mass content of the Mg is 2.5%.
3. Al-Mg-Mn-Cu alloy according to claim 1, which is characterized in that the mass content of the Mn is 0.3%.
4. Al-Mg-Mn-Cu alloy according to claim 1, which is characterized in that the mass content of the Cu is 0.2%.
5. Al-Mg-Mn-Cu alloy according to claim 1, which is characterized in that the Ho and Ce total mass content >=
0.4%.
6. Al-Mg-Mn-Cu alloy according to claim 1, which is characterized in that the Ti and Zr total mass content >=
0.2%.
7. a kind of preparation method of Al-Mg-Mn-Cu alloy described in claim 1, comprising:
The source Al, the source Mg, the source Ho, the source Zr, the source Mn, the source Cu, the source Ce and the source Ti are subjected to melting, obtain aluminium alloy；
The aluminium alloy is subjected to die casting, obtains Al-Mg-Mn-Cu alloy.
8. the method according to the description of claim 7 is characterized in that the temperature of the die casting be 660~700 DEG C, the die casting
Speed be 1~2m/s, the mould temperature of the die casting is 260~300 DEG C.
9. the method according to the description of claim 7 is characterized in that after the completion of the die casting further include:
The casting obtained after die casting is subjected to ageing treatment；
The temperature of the ageing treatment is 180~220 DEG C；
The time of the ageing treatment is 7~9 hours.
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| CN107502793A (en) * | 2017-08-08 | 2017-12-22 | 上海航天精密机械研究所 | A kind of high-strength high hard cast Al-Si alloy and its manufacture method |
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| WO2000011232A1 (en) * | 1998-08-21 | 2000-03-02 | Daimlerchrysler Ag | Weldable anti-corrosive aluminium-magnesium alloy containing a high amount of magnesium, especially for use in aviation |
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