CN108300884B - A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy - Google Patents

A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy Download PDF

Info

Publication number
CN108300884B
CN108300884B CN201810037556.6A CN201810037556A CN108300884B CN 108300884 B CN108300884 B CN 108300884B CN 201810037556 A CN201810037556 A CN 201810037556A CN 108300884 B CN108300884 B CN 108300884B
Authority
CN
China
Prior art keywords
alloy
melt
hypoeutectic
rotten
phase
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.)
Active
Application number
CN201810037556.6A
Other languages
Chinese (zh)
Other versions
CN108300884A (en
Inventor
武晓峰
伍复发
赵荣达
张广安
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Qingdao Liudian Bearing Technology Co.,Ltd.
Original Assignee
Liaoning University of Technology
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Liaoning University of Technology filed Critical Liaoning University of Technology
Priority to CN201810037556.6A priority Critical patent/CN108300884B/en
Publication of CN108300884A publication Critical patent/CN108300884A/en
Application granted granted Critical
Publication of CN108300884B publication Critical patent/CN108300884B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making non-ferrous alloys
    • C22C1/02Making non-ferrous alloys by melting
    • C22C1/03Making non-ferrous alloys by melting using master alloys
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making non-ferrous alloys
    • C22C1/02Making non-ferrous alloys by melting
    • C22C1/026Alloys based on aluminium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making non-ferrous alloys
    • C22C1/06Making non-ferrous alloys with the use of special agents for refining or deoxidising
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/06Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08Alloys based on aluminium with magnesium as the next major constituent with silicon

Abstract

A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy, with Bi and Zr to Mg2Si content is that the hypoeutectic Al-Mg2Si alloy of 4 ~ 12.5wt.% carries out rotten and micronization processes, after processing, makes the Bi content 0.1 ~ 0.6% in melt, Zr content is 0.05 ~ 0.2%.Eutectic Mg2Si after Bi Metamorphism treatment in alloy is changed into tiny threadiness by coarse Chinese character shape, primary α-Al after Zr micronization processes in alloy is changed into equiax crystal by column crystal, mechanical property is largely increased, and 34% and 239% is respectively increased in the wax-anti dispersant of alloy after refining, being rotten.Gone bad to the hypoeutectic Al-Mg2Si alloy of different content Mg2Si, organize significantly to be refined after micronization processes.Meanwhile rotten and Zr the thinning effect of Bi is not influenced by cooling velocity, is not only suitable for metal mold, is also applied for sand mold.And Bi alterant and Zr fining agent also have many advantages, such as that excellent long-term effect, treatment process are simple and pollution-free.

Description

A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy
Technical field
The invention belongs to aluminium alloy castings and melting technique field, in particular to a kind of hypoeutectic Al-Mg2The change of Si alloy Matter and thinning method.
Background technique
In traditional Al-Si-Mg alloy, Mg2Si is to be heat-treated disperse educt by solid gas coupling as the second phase Reinforced Al-matrix body.In recent years, Mg is directly precipitated from molten aluminum2Si phase and the Al-Mg formed2Si alloy, this is in hypereutectic composition Also referred to as in-situ authigenic Mg2The composite material of Si/Al, the extensive concern by domestic and foreign scholars.This material and traditional Al-Si-Mg alloy is compared, amount containing Mg and Mg2Si phase volume fraction is higher, has higher specific stiffness, specific strength and wearability Equal excellent performances, the Novel lightweight material as fields such as space flight and aviation and automobiles have wider application prospect.However, The Mg being precipitated under as cast condition2Si compares coarse, nascent Mg2Si is in dendritic crystalline coarse, with holes, and eutectic Mg2Si is then in coarse Chinese character shape, netted, rodlike and sheet, seriously isolate Al matrix, stress are caused to be concentrated, and form formation of crack, deteriorate the power of alloy Learn performance.In addition, for the Al-Mg of hypoeutectic ingredient2Si alloy is organized by primary α-Al and Mg2Si+ α-Al eutectic phase group At wherein pattern of the primary α-Al under as cast condition is that coarse branch is crystalline, is macroscopically column crystal, leads to alloy mechanical property With the decline of the casting characters such as feeding, crack resistance.
In recent years, people using various processes for example mechanical alloying, hot extrusion, rolling, heat treatment, quickly solidification and Metamorphism treatment etc. controls Mg2The size and pattern of Si phase.In these methods, Metamorphism treatment has easy to operate, at low cost, change The advantages that matter significant effect, is increased by the way that P, La, Nd, Y, Sr, Na, Ni, Zr and B iso-metamorphism agent element are added into alloy melt Add Mg2The nucleation rate of Si phase or the growth pattern for changing crystal, and then can effectively refine Mg2Si phase improves the mechanics of alloy Performance.
Up to now, people are to hypereutectic Al-Mg2Si alloy, that is, in-situ authigenic Mg2The Metamorphism treatment of Si/Al composite material Etc. processes have conducted extensive research, and to hypoeutectic Al-Mg2The research of Si alloy is rarely reported.With hypereutectic Al-Mg2Si Alloy is compared, hypoeutectic Al-Mg2The plasticity and toughness of Si alloy are more preferable, have more excellent comprehensive mechanical property, it is contemplated that have Wider application.On condition that coarse Chinese character shape, netted and sheet eutectic Mg2Si phase is effectively refined.Together When refine primary α-Al dendrite, so that alloy mechanical property and casting character is further improved.
At present for hypoeutectic Al-Mg2The research of Si alloy is rarely reported.The Li et al. people of University Of Tianjin is to hypoeutectic Al- 10Mg2Si alloy carries out 520 DEG C × 6h solid solution and the ageing treatment of 200 DEG C subsequent × 6h, being total in alloy after discovery processing Brilliant Mg2The rodlike of Si Xiang Youchang is changed into short threadiness and spherical, and tensile strength is increased to 234.6 MPa by 186 MPa, See Journal of Alloys and Compounds, 2016,663 (5): 15-19.Their research is also shown that hypoeutectic Al-10Mg2Corrosion resistance of the Si alloy in 3.5 wt.% NaCl solutions is also improved, and sees Materials Characterization, 2016, 122(12):142-147.Lee of material science research institute, South Korea et al. pairs AlMg5Si2Mn diecasting alloys do cold-rolling treatment before Homogenization Treatments, make coarse eutectic Mg interconnected2Si phase is crushed At tiny fragment, so that the mechanical property of alloy be made to be effectively improved, Materials Science and is seen Engineering A, 2017, 685(8):244-252.Although these methods being capable of refining eutectic Mg2Si improves alloy force Learn, the performances such as corrosion-resistant, but there are processes more, complex process and it is at high cost the disadvantages of.Therefore, there is an urgent need to research and develop both It is easy and economical, it is suitable for hypoeutectic Al-Mg2Alterant, fining agent and the rotten, thinning method of Si alloy.
Up to now there is not yet there is refinement hypoeutectic Al-Mg2The report of Si alloy primary α-Al dendrite.For casting Al-Si alloy mainly refines primary α-Al dendrite by adding fining agent into alloy melt.Currently used fining agent has The intermediate alloys such as Al-Ti, Al-B, Al-Ti-B, Al-Ti-C, Al-Zr and KBF4、K2TiF6, TiC and K2ZrF6Etc. single or multiple Close salt.The Ti class fining agent such as Al-Ti, Al -5Ti -1B and Al-Ti-C is suitable for the aluminium silicon of fine aluminium and silicon content less than 1.5% Alloy is not obvious the hypoeutectic cast aluminium-silicon alloy thinning effect of silicon content >=5%, this is because (Ti1-x Six )Al3 The generation of compound reduces the Al as raw core agent3Ti and TiB2Amount.Studies have shown that the B class such as Al-3B, Al -3Ti -3B is thin Agent has preferable thinning effect to the hypoeutectic cast aluminium-silicon alloy of silicon content > 4%, but B is easily reacted with alterant element Sr, Generate SrB6, consume Sr and B.For Al-Mg2Si alloy, due to wherein contain higher Mg amount, Refining Elements be easier to Mg and Alterant element etc. forms non-raw nuclear compound, weakens rotten and thinning effect or causes the generation of casting flaw.Iranian Teheran Fakhraei of university et al. discovery, excessive B or Zr is added in Al-20Mg alloy can generate stomata, lead to alloy tensile Materials & Design, 2014,56 (4): 557-564 are shown in the reduction of performance.
Summary of the invention
It is of the existing technology the purpose of the present invention is overcoming the problems, such as, provide that a kind of rotten, thinning effect is good, fade resistance Good, strong applicability, metal mold, sand mold be all suitable for, the hypoeutectic Al-Mg of simple production process2The rotten and refinement side of Si alloy Method.
The technical solution of the invention is as follows:
(1) %Mg of 4-12.5wt. containing mass percent is pressed2Hypoeutectic Al-the Mg of Si phase2Si alloying ingredient, wherein Mg adds Dosage are as follows: the scaling loss amount of calculation amount+10 ~ 30%;
(2) it after pure Al, the aluminium silicon intermediate alloy prepared step (1) is cleaned and dried, is put into the graphite crucible of resistance furnace, It is heated in resistance furnace, until completely melted, at 720 DEG C, by aluminium foil package, 300 DEG C of the preheating of pure Mg block of 300 DEG C of preheating Graphite bell jar indentation melt in, until fusing, stand 5min;
(3) carbon trichloride that will account for melt quality 0.05 ~ 0.2% is obtained with graphite bell jar indentation step (2) for preheating 300 DEG C To melt in, carry out refining degasification, at a temperature of 670 DEG C ~ 780 DEG C stir 1 ~ 5 min, remove the dross of bath surface, obtain Melt after to refining;
(4) Bi particle is added under conditions of temperature is 670 DEG C ~ 730 DEG C to the melt that step (3) obtains, stands 1 ~ 3 Min obtains the melt that Bi content is 0.1-0.6wt. % mass percent;
(5) Al-10Zr intermediate alloy is added under conditions of temperature is 720 DEG C ~ 800 DEG C to the melt that step (4) obtains Or compound containing Zr, 5 ~ 15min is stood, after its fusing, 2 ~ 5 min of stirring melt is uniformly distributed Zr, obtains Zr content and is The melt of 0.05-0.2wt. % mass percent;
(6) refining treatment is carried out to the melt that step (5) obtains by step (3), will be melted at being 700 DEG C ~ 780 DEG C in temperature Body is poured into casting mold, becomes casting or slab.
Bi described in step (4) is added with form of pure metal.
Zr described in step (5) is added with intermediate alloy or compound form.
Casting mold described in step (6) is the metal mold and other casting molds of 250 DEG C of sand mold or preheating.
The advantages of technical solution of the present invention, is mainly reflected in:
1, using Bi pure metal particles as alterant, can effectively go bad hypoeutectic Al-Mg2Mg in Si alloy2Si phase, In hypoeutectic Al-Mg2After adding suitable Bi in Si alloy, eutectic Mg is changed significantly2The pattern and size of Si, Mg2Si phase Tiny graininess, threadiness are changed by coarse Chinese character shape, netted and sheet, and primary α-Al phase volume fraction increases, There is apparent stigma of degeneracy and effect, solubility of the Bi in Al is extremely low, when the melt of hypoeutectic and eutectic composition reaches altogether When brilliant reflecting point, is easily adsorbing and assembling the eutectic Mg being formerly precipitated2The growth interface forward position of Si phase, in eutectic growth constantly Block eutectic Mg2The original twin step of Si, and a large amount of new re-entrant angle twins are constantly inspired, make eutectic Mg2Si Branching Ratio does not go bad Want much more frequent, moreover, twin density significantly increases so that eutectic Mg2Si growth characteristics are changed by original anisotropy For isotropism, then, eutectic Mg2The mode of Si limited and thick sheet development from rotten preceding branch is sharp to become a large amount of frequent branches Fibrous growth, final eutectic Mg2The pattern and size of Si have the change of matter;In addition, Bi is in liquid-solid boundary forward position Enrichment causes constitutional supercooling, is greatly lowered the balance crystallization temperature of liquid at the forward position of interface, thus reduces liquid phase Practical degree of supercooling, reduces the speed of growth of eutectic structure, to reach refining eutectic Mg2The purpose of Si.
2, using Al-Zr intermediate alloy or compound containing Zr to hypoeutectic Al-Mg2Primary α-Al Phase in Si alloy has Significant refining effect, in hypoeutectic Al-Mg2After adding suitable Zr in Si alloy, Primary α-Al Phase is changed significantly Pattern and size make it be changed into tiny equiax crystal by coarse columnar dendrite, and Zr is raw in conjunction with the Al in alloy melt At ZrAl3Phase.ZrAl3Mutually close with the lattice constant of Primary α-Al Phase, mismatch between the two is only 0.925%, according to different Matter forming core is theoretical, and mismatch is smaller, and the interatomic binding force of the two is stronger, easier in its substrate forming core, therefore, ZrAl3It can Using the heterogeneous forming core core as primary α-Al, to refine Primary α-Al Phase.
3, to different content Mg2Hypoeutectic Al-the Mg of Si2Si alloy all has excellent rotten, thinning effect, expands The application range of such alloy.
4, Bi alterant and Zr fining agent all have long-term effect, go bad, thinning effect, insensitive to cooling velocity, are applicable in In the various casting production process such as metal mold, sand mold, die casting, since Bi is in eutectic Mg2The absorption in Si phase growth interface forward position is simultaneously Coherent condition influenced by cooling velocity it is smaller, therefore Bi be added melt in, be either cast in metal mold, or in sand mold In, eutectic Mg2Si can be refined effectively, i.e. Bi is in hypoeutectic Al-Mg2To eutectic Mg in Si alloy2The rotten effect of Si phase Fruit is influenced smaller by cooling velocity;In addition, since bismuth with oxygen is not susceptible to chemically react, therefore in melt long-term heat preservation, casting In the process, it is unlikely to be burnt, it is ensured that melt mesometamorphism eutectic Mg2The residual quantity of the minimum Bi of Si, so that the modification effect of Bi has There is long-term effect.
5, Bi alterant and Zr fining agent also have many advantages, such as easily operated, low in cost and safety and environmental protection.
Detailed description of the invention
Fig. 1 is that 100 times of bottom dies do not refine, go bad %Mg containing 10wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy Micro-organization chart;
Fig. 2 is that 500 times of bottom dies do not refine, go bad %Mg containing 10wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy Micro-organization chart;
Fig. 3 is 100 times of bottom die 0.13%Zr refinements, the rotten %Mg containing 10wt. of 0.41%Bi2The hypoeutectic Al-of Si phase Mg2Si microstructure of the alloy micro-organization chart;
Fig. 4 is 500 times of bottom die 0.13%Zr refinements, the rotten %Mg containing 10wt. of 0.41%Bi2The hypoeutectic Al-of Si phase Mg2Si microstructure of the alloy micro-organization chart;
Fig. 5 is that 100 times of bottom dies do not refine, go bad %Mg containing 4wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy is aobvious Micro-assembly robot figure;
Fig. 6 is that 500 times of bottom dies do not refine, go bad %Mg containing 4wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy is aobvious Micro-assembly robot figure;
Fig. 7 is 100 times of bottom die 0.09%Zr refinements, the rotten %Mg containing 4wt. of 0.1%Bi2The hypoeutectic Al-of Si phase Mg2Si microstructure of the alloy micro-organization chart;
Fig. 8 is 500 times of bottom die 0.09%Zr refinements, the rotten %Mg containing 4wt. of 0.1%Bi2The hypoeutectic Al-of Si phase Mg2Si microstructure of the alloy micro-organization chart;
Fig. 9 is that 100 times of bottom dies do not refine, go bad %Mg containing 12.5wt.2Hypoeutectic Al-the Mg of Si phase2Si alloy gold Phase micro-organization chart;
Figure 10 is that 500 times of bottom dies do not refine, go bad %Mg containing 12.5wt.2Hypoeutectic Al-the Mg of Si phase2Si alloy gold Phase micro-organization chart;
Figure 11 is 100 times of bottom die 0.2%Zr refinements, the rotten %Mg containing 12.5wt. of 0.36%Bi2The hypoeutectic of Si phase Al-Mg2Si microstructure of the alloy micro-organization chart;
Figure 12 is 500 times of bottom die 0.2%Zr refinements, the rotten %Mg containing 12.5wt. of 0.36%Bi2The hypoeutectic of Si phase Al-Mg2Si microstructure of the alloy micro-organization chart;
Figure 13 is that 100 times of lower sand molds do not refine, go bad %Mg containing 10wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy is aobvious Micro-assembly robot figure;
Figure 14 is that 500 times of lower sand molds do not refine, go bad %Mg containing 10wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy is aobvious Micro-assembly robot figure;
Figure 15 is 100 times of lower sand mold 0.17Zr refinements, the rotten %Mg containing 10wt. of 0.6%Bi2Hypoeutectic Al-the Mg of Si phase2Si Microstructure of the alloy micro-organization chart;
Figure 16 is 500 times of lower sand mold 0.17Zr refinements, the rotten %Mg containing 10wt. of 0.6%Bi2Hypoeutectic Al-the Mg of Si phase2Si Microstructure of the alloy micro-organization chart;
Figure 17 is the not rotten %Mg containing 13.5wt. of 500 times of bottom dies2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy is aobvious Micro-assembly robot figure;
Figure 18 is the rotten %Mg containing 13.5wt. of 500 times of bottom die 0.44%Bi2Hypoeutectic Al-the Mg of Si phase2Si alloy gold Phase micro-organization chart;
Figure 19 is the rotten %Mg containing 10wt. of 500 times of bottom die 0.06%Bi2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy Micro-organization chart;
Figure 20 is the rotten %Mg containing 10wt. of 500 times of bottom die 0.87%Bi2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy Micro-organization chart;
Figure 21 is that 100 times of bottom die 0.02%Zr refine %Mg containing 10wt.2Hypoeutectic Al-the Mg of Si phase2Si microstructure of the alloy Micro-organization chart;
Figure 22 is 500 times of bottom die 0.64%Zr refinements, the rotten %Mg containing 10wt. of 0.47% Bi2The hypoeutectic of Si phase Al-Mg2Si microstructure of the alloy micro-organization chart;
Figure 23 is the load-deformation curve of alloy.
Specific embodiment
The present invention is for hypoeutectic Al-Mg2Si alloy is applicable in, including be added various alloy elements, it is additional and The case where interior raw reinforced phase, following implementation of the present invention be intended merely to it is detailed for example, but the invention is not limited to Following implementation, various modifications and replacement under all core of the invention technical conditions, all belongs to the scope of the present invention it It is interior.
Below to hypoeutectic Al-Mg of the present invention2Si alloying component, alterant, fining agent and melting and founder Skill condition is illustrated:
Alloying component: Al-Mg of the present invention2Mg in Si alloy2The ingredient of Si is limited to 4 ~ 12.5wt. %, Al-Mg2Si is The eutectic alloy that eutectic point is 13.9%, eutectic Mg in alloy2Si phase is hardening constituent, quantity, pattern, size and distribution pair Its Effect on Mechanical Properties is very big, works as Mg2When Si < 4wt. %, Mg2Si phasor is low, and alloy strength is too low;Work as Mg2Si=13.9wt. %(eutectic composition) and 12.5wt. % < Mg2The nearly eutectic composition of Si < 13.9wt. %() when, our experiments demonstrated that, although Bi The a small amount of block-like nascent Mg occurred under as cast condition can be eliminated2Si phase, but to eutectic Mg2The modification effect of Si phase is unobvious, sees figure 17, Figure 18;Mg2Si is within the scope of 4 ~ 12.5wt. %, with Mg2The increase of Si amount, alloy strength, hardness increase, plasticity, toughness Reduce;In practical application, Mg can be reasonably selected according to the requirement of workpiece mechanical property2The quantity of Si phase, so that it is determined that final Alloying component.
Alterant: Bi alterant is to Al-Mg2Mg in Si alloy2The modification effect of Si phase depends primarily on the content of Bi, melts There is best modification effect, as Bi content < 0.1% in melt, Mg when Bi content is 0.1 ~ 0.6% in body2Although Si phase Chinese character Shape disappears, and threadiness occurs, but there are still numerous strips, sheet, show rotten deficiency, see Figure 19;As Bi in melt When content > 0.6%, Mg2Si phase is most of still to be not fibrous, but part strip, sheet occurs, showed denaturalization phenomenon, and saw Figure 20.
Fining agent: Zr fining agent is to Al-Mg2The thinning effect of Primary α-Al Phase depends primarily on containing for Zr in Si alloy Amount, i.e., as the heterogeneous forming core core ZrAl of primary α-Al3Production quantity number, melt Zr content be 0.05 ~ 0.2% when have There is best thinning effect, as Zr content < 0.05% in melt, the ZrAl that is formed in melt3Very little, Primary α-Al Phase forming core position It sets less, α-Al is still dendrite, shows the deficiency of refinement, sees Figure 21;As Zr content > 0.2% in melt, not but not increase Strong thinning effect, excessive Zr easily form ZrBi two-spot compound or Al-Zr-Bi ternary compound with alterant Bi instead, disappear The Bi atom in melt is consumed, rotten deficiency is caused, although forming some fibre shape Mg2Si phase, but most of is still strip, piece Shape is shown in Figure 22.
Smelting technology: Al-Mg2Si series alloy amount containing Mg is higher, and the present invention is smelting technology under atmosphere, protects without gas Shield or melting under vacuum, but answer the scaling loss of strict control Mg, measure are as follows: 300 DEG C of preheating Mg blocks, and being wrapped up with aluminium foil, with pre- In the graphite bell jar indentation melt of 300 DEG C of heat, until fusing, is added Bi later, after stirring slightly, i.e. closed among addition Al-Zr Gold, it is therefore an objective to avoid MAG block under high temperature from directly contacting with the oxygen in air, shorten the fusing of magnesium and the soaking time of melt, make The scaling loss amount of magnesium is controlled 10 ~ 30%, i.e. fusible in addition molten aluminum because the fusing point of pure Bi is low, without standing, but in Al-10Zr Between alloy relative melting points it is high, standing is needed after addition 5 ~ 15 minutes, and after its fusing, 2 ~ 5 min of stirring melt divides Zr uniformly Cloth.
Embodiment 1:
1, hypoeutectic Al-Mg is prepared using Al-15Si intermediate alloy, pure Al and pure Mg2Si alloy, wherein Mg and Si are pressed 10.wt %Mg2The ratio of Si is added, the additive amount of Mg are as follows: the scaling loss amount of calculation amount+10%, surplus are pure Al;
2, it after pure Al, the aluminium silicon intermediate alloy prepared step 1 is cleaned and dried, is put into the graphite crucible of resistance furnace, Pure Al and Al-15Si intermediate alloy is heated in resistance furnace, until completely melted, at 720 DEG C, by aluminium foil package, preheating 300 DEG C pure Mg block with preheat 300 DEG C graphite bell jar indentation melt in, until fusing, stand 5min;
3, the melt for obtaining the graphite bell jar indentation step 2 that the carbon trichloride for accounting for melt quality 0.1% preheats 300 DEG C In, refining degasification is carried out, stirs 3min at a temperature of 740 DEG C, removes the dross of bath surface, the melt after being refined;
4, pure metal Bi particle is added at a temperature of 710 DEG C into melt to the melt that step 3 obtains, stands 2 min, obtains It is the melt of 0.41wt. % mass percent to Bi content;
5, Al-10Zr intermediate alloy is added under conditions of temperature is 750 DEG C to the melt that step 4 obtains, stood 10min, after its fusing, 3 min of stirring melt is uniformly distributed Zr, and obtaining Zr content is 0.13wt. % mass percent Melt;
6, the melt for obtaining the graphite bell jar indentation step 5 that the carbon trichloride for accounting for melt quality 0.05% preheats 300 DEG C In, refining degasification is carried out, is stirred at a temperature of 740 DEG C, after refining, skimming, the gold of 250 DEG C of preheating is poured at a temperature of 740 DEG C In genotype, become casting.
Specific modification effect is shown in Fig. 1, Fig. 2, Fig. 3 and Fig. 4, and the Primary α-Al Phase being not added in Bi, Zr alloy is coarse Dendrite is shown in Fig. 1, Mg2Si phase is coarse Chinese character, lath-shaped, sees Fig. 2;Add Primary α-Al Phase after Bi, Zr in alloy by Coarse branch is crystalline to be changed into tiny equiaxed dendrite shape, sees Fig. 3, Mg2Si phase becomes threadiness and minimal amount of tiny item Shape is shown in Fig. 4;The wax-anti dispersant of alloy is respectively 214.37MPa and 2.01% before refining, being rotten, after refining, being rotten 279.44MPa and 7.02% is respectively increased, sees Figure 23.
Embodiment 2:
1, hypoeutectic Al-Mg is prepared using Al-15Si intermediate alloy, pure Al and pure Mg2Si alloy, wherein Mg and Si are pressed 4.wt %Mg2The ratio of Si is added, the additive amount of Mg are as follows: the scaling loss amount of calculation amount+20%, surplus are pure Al;
2, it after pure Al, the aluminium silicon intermediate alloy prepared step 1 is cleaned and dried, is put into the graphite crucible of resistance furnace, Pure Al and Al-15Si intermediate alloy is heated in resistance furnace, until completely melted, at 720 DEG C, by aluminium foil package, preheating 300 DEG C pure Mg block with preheat 300 DEG C graphite bell jar indentation melt in, until fusing, stand 5min;
3, the melt for obtaining the graphite bell jar indentation step 2 that the carbon trichloride for accounting for melt quality 0.05% preheats 300 DEG C In, refining degasification is carried out, stirs 1min at a temperature of 780 DEG C, removes the dross of bath surface, the melt after being refined;
4, pure metal Bi particle is added at a temperature of 730 DEG C into melt to the melt that step 3 obtains, stands 3 min, obtains It is the melt of 0. 1wt. % mass percent to Bi content;
5, Al-10Zr intermediate alloy is added under conditions of temperature is 800 DEG C to the melt that step 4 obtains, stands 5min, After its fusing, 2 min of stirring melt is uniformly distributed Zr, obtains the melt that Zr content is 0.09wt. % mass percent;
6, the melt for obtaining the graphite bell jar indentation step 5 that the carbon trichloride for accounting for melt quality 0.2% preheats 300 DEG C In, refining degasification is carried out, is stirred at a temperature of 780 DEG C, after refining, skimming, the gold of 250 DEG C of preheating is poured at a temperature of 780 DEG C In genotype, become casting.
Specific modification effect is shown in Fig. 5, Fig. 6, Fig. 7 and Fig. 8, and the Primary α-Al Phase being not added in Bi, Zr alloy is coarse Dendrite is shown in Fig. 5, Mg2Si phase is coarse Chinese character, lath-shaped, sees Fig. 6;Add Primary α-Al Phase after Bi, Zr in alloy by Coarse branch is crystalline to be changed into tiny equiaxed dendrite shape, sees Fig. 7, Mg2Si phase becomes threadiness and minimal amount of tiny item Shape is shown in Fig. 8;The wax-anti dispersant of alloy is respectively 214.37MPa and 2.01% before refining, being rotten, after refining, being rotten 255.67MPa and 9.25% is respectively increased, sees Figure 23.
Embodiment 3:
1, hypoeutectic Al-Mg is prepared using Al-15Si intermediate alloy, pure Al and pure Mg2Si alloy, wherein Mg and Si are pressed 12.5wt %Mg2The ratio of Si is added, the additive amount of Mg are as follows: the scaling loss amount of calculation amount+30%, surplus are pure Al;
2, it after pure Al, the aluminium silicon intermediate alloy prepared step 1 is cleaned and dried, is put into the graphite crucible of resistance furnace, Pure Al and Al-15Si intermediate alloy is heated in resistance furnace, until completely melted, at 720 DEG C, by aluminium foil package, preheating 300 DEG C pure Mg block with preheat 300 DEG C graphite bell jar indentation melt in, until fusing, stand 5min;
3, the melt for obtaining the graphite bell jar indentation step 2 that the carbon trichloride for accounting for melt quality 0.2% preheats 300 DEG C In, refining degasification is carried out, stirs 5min at a temperature of 670 DEG C, removes the dross of bath surface, the melt after being refined;
4, pure metal Bi particle is added at a temperature of 730 DEG C into melt to the melt that step 3 obtains, stands 1 min, obtains It is the melt of 0.36wt. % mass percent to Bi content;
5, compound containing Zr is added under conditions of temperature is 720 DEG C to the melt that step 4 obtains, 15min is stood, to it After fusing, 5 min of stirring melt is uniformly distributed Zr, obtains the melt that Zr content is 0.2wt. % mass percent;
6, the melt for obtaining the graphite bell jar indentation step 5 that the carbon trichloride for accounting for melt quality 0.1% preheats 300 DEG C In, refining degasification is carried out, is stirred at a temperature of 700 DEG C, after refining, skimming, the gold of 250 DEG C of preheating is poured at a temperature of 700 DEG C In genotype, become casting.
Specific modification effect is shown in Fig. 9, Figure 10, Figure 11 and Figure 12, and the Primary α-Al Phase being not added in Bi, Zr alloy is coarse Dendrite, see Fig. 9, Mg2Si phase is coarse Chinese character, lath-shaped, sees Figure 10;Primary α-Al after addition Bi, Zr in alloy Mutually it is changed into tiny equiaxed dendrite shape by coarse branch is crystalline, sees Figure 11, Mg2Si phase becomes fibrous and minimal amount of thin Small strip, is shown in Figure 12;The wax-anti dispersant of alloy is respectively 221.61MPa and 1.82% before refining, being rotten, and refinement becomes 287.76MPa and 6.81% are respectively increased after matter, sees Figure 23.
Embodiment 4:
1, hypoeutectic Al-Mg is prepared using Al-15Si intermediate alloy, pure Al and pure Mg2Si alloy, wherein Mg and Si are pressed 10.wt %Mg2The ratio of Si is added, the additive amount of Mg are as follows: the scaling loss amount of calculation amount+15%, surplus are pure Al;
2, it after pure Al, the aluminium silicon intermediate alloy prepared step 1 is cleaned and dried, is put into the graphite crucible of resistance furnace, Pure Al and Al-15Si intermediate alloy is heated in resistance furnace, until completely melted, at 720 DEG C, by aluminium foil package, preheating 300 DEG C pure Mg block with preheat 300 DEG C graphite bell jar indentation melt in, until fusing, stand 5min;
3, the melt for obtaining the graphite bell jar indentation step 2 that the carbon trichloride for accounting for melt quality 0.2% preheats 300 DEG C In, refining degasification is carried out, stirs 4min at a temperature of 750 DEG C, removes the dross of bath surface, the melt after being refined;
4, pure metal Bi particle is added at a temperature of 710 DEG C into melt to the melt that step 3 obtains, stands 3 min, obtains It is the melt of 0.6wt. % mass percent to Bi content;
5, compound containing Zr is added under conditions of temperature is 760 DEG C to the melt that step 4 obtains, 12min is stood, to it After fusing, 4 min of stirring melt is uniformly distributed Zr, obtains the melt that Zr content is 0.05wt. % mass percent;
6, the melt for obtaining the graphite bell jar indentation step 5 that the carbon trichloride for accounting for melt quality 0.05% preheats 300 DEG C In, refining degasification is carried out, is stirred at a temperature of 730 DEG C, after refining, skimming, is poured into sand mold at a temperature of 730 DEG C.
Specific modification effect is shown in Figure 13, Figure 14, Figure 15 and Figure 16, compared with metal mold, under the conditions of sand mold, be not added with Bi, Primary α-Al Phase in Zr alloy is dendrite, and more coarse, sees Figure 13, Mg2Si phase is coarse lath-shaped, sees Figure 14; Primary α-Al Phase after addition Bi, Zr in alloy is changed into tiny equiaxed dendrite shape, sees Figure 15, Mg2Si phase becomes tiny Strip is shown in Figure 16;The wax-anti dispersant of alloy is respectively 175.96MPa and 1.23% before refining, being rotten, and refinement is gone bad After 244.69MPa and 3.83% is respectively increased, see Figure 23.

Claims (3)

1. a kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy, which is characterized in that it the following steps are included:
(1) %Mg of 4-12.5wt. containing mass percent is pressed2Hypoeutectic Al-the Mg of Si phase2Si alloying ingredient, the wherein additive amount of Mg Are as follows: the scaling loss amount of calculation amount+10 ~ 30%;
(2) it after pure Al, the aluminium silicon intermediate alloy prepared step (1) is cleaned and dried, is put into the graphite crucible of resistance furnace, in electricity It is heated in resistance furnace, until completely melted, at 720 DEG C, by aluminium foil package, the pure Mg block stone for preheating 300 DEG C of 300 DEG C of preheating In black bell jar indentation melt, until fusing, stands 5min;
(3) carbon trichloride for accounting for melt quality 0.05 ~ 0.2% is obtained with 300 DEG C of preheating of graphite bell jar indentation step (2) In melt, refining degasification is carried out, 1 ~ 5 min is stirred at a temperature of 670 DEG C ~ 780 DEG C, the dross of bath surface is removed, obtains essence Melt after refining;
(4) Bi particle is added under conditions of temperature is 670 DEG C ~ 730 DEG C to the melt that step (3) obtains, stands 1 ~ 3 min, Obtain the melt that Bi content is 0.1-0.6wt. % mass percent;
(5) Al-10Zr intermediate alloy is added under conditions of temperature is 720 DEG C ~ 800 DEG C to the melt that step (4) obtains or contained Zr compound stands 5 ~ 15min, and after its fusing, 2 ~ 5 min of stirring melt is uniformly distributed Zr, obtains Zr content and is The melt of 0.05-0.2wt. % mass percent;
(6) refining treatment is carried out to the melt that step (5) obtains by step (3), pours melt at being 700 DEG C ~ 780 DEG C in temperature It infuses in casting mold, becomes casting or slab.
2. hypoeutectic Al-Mg according to claim 12The rotten and thinning method of Si alloy, which is characterized in that step (4) The Bi is added with form of pure metal.
3. hypoeutectic Al-Mg according to claim 12The rotten and thinning method of Si alloy, which is characterized in that step (6) The casting mold is the metal mold and other casting molds of 250 DEG C of sand mold or preheating.
CN201810037556.6A 2018-01-16 2018-01-16 A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy Active CN108300884B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201810037556.6A CN108300884B (en) 2018-01-16 2018-01-16 A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201810037556.6A CN108300884B (en) 2018-01-16 2018-01-16 A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy

Publications (2)

Publication Number Publication Date
CN108300884A CN108300884A (en) 2018-07-20
CN108300884B true CN108300884B (en) 2019-10-08

Family

ID=62869153

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201810037556.6A Active CN108300884B (en) 2018-01-16 2018-01-16 A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy

Country Status (1)

Country Link
CN (1) CN108300884B (en)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109112368A (en) * 2018-09-20 2019-01-01 辽宁工业大学 One kind casting hypoeutectic Al-Mg containing Sc2Si alloy and its production method
CN111060554B (en) * 2019-12-10 2021-05-14 南昌航空大学 Rapid analysis method for determining content of supercooled hypoeutectic alloy phase
CN111187950B (en) * 2020-02-06 2021-09-21 广东宏锦新材料科技有限公司 6-series aluminum alloy, preparation method thereof and mobile terminal
CN111411246A (en) * 2020-04-27 2020-07-14 吉林化工学院 Ultrasonic treatment and Bi composite refined hypoeutectic Al-Mg2Method for forming Si alloy structure
CN113755726B (en) * 2021-08-30 2022-05-31 上海交通大学 High-modulus high-toughness aluminum-based composite material and preparation method thereof

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000017365A (en) * 1998-06-29 2000-01-18 Kobe Steel Ltd Al-Mg-Si SERIES ALUMINUM ALLOY SHEET FOR FORMING
CN104498787A (en) * 2014-12-24 2015-04-08 辽宁工业大学 Preparation method of in-situ synthesized Mg2Si particle enhanced aluminum matrix composite
CN105401012A (en) * 2015-09-21 2016-03-16 辽宁工业大学 Preparation method for novel pelletized hypereutectic Al-Si alloy
JP2017179445A (en) * 2016-03-30 2017-10-05 昭和電工株式会社 Al-Mg-Si-BASED ALLOY SHEET

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000017365A (en) * 1998-06-29 2000-01-18 Kobe Steel Ltd Al-Mg-Si SERIES ALUMINUM ALLOY SHEET FOR FORMING
CN104498787A (en) * 2014-12-24 2015-04-08 辽宁工业大学 Preparation method of in-situ synthesized Mg2Si particle enhanced aluminum matrix composite
CN105401012A (en) * 2015-09-21 2016-03-16 辽宁工业大学 Preparation method for novel pelletized hypereutectic Al-Si alloy
JP2017179445A (en) * 2016-03-30 2017-10-05 昭和電工株式会社 Al-Mg-Si-BASED ALLOY SHEET

Also Published As

Publication number Publication date
CN108300884A (en) 2018-07-20

Similar Documents

Publication Publication Date Title
CN108300884B (en) A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy
CN108866404B (en) Preparation method of large-size high-strength high-toughness 7000 series aluminum alloy round ingot
CN113061787A (en) High-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy and preparation method thereof
CN103911530B (en) A kind of automatic catch variator high performance aluminium materials and preparation method thereof
CN110643862A (en) Aluminum alloy for new energy automobile battery shell and pressure casting preparation method thereof
CN110714156B (en) Light high-strength corrosion-resistant high-entropy alloy and preparation method thereof
CN109972003A (en) High-elongation heat-resisting aluminium alloy and preparation method thereof suitable for gravitational casting
CN113737070A (en) High-yield-strength cast aluminum alloy and preparation method thereof
CN113174516B (en) Scandium-containing high-strength high-toughness aluminum-silicon alloy and preparation process thereof
CN114351017B (en) Casting method and application of high-toughness high-heat-conductivity aluminum alloy ingot
CN108330362A (en) A kind of the high-strength temperature-resistant casting Al-Cu alloy and preparation process of low porosity
CN106148787A (en) Magnesium lithium alloy being suitable to sand casting and preparation method thereof
CN102021428B (en) Sc-RE aluminium alloy material with high strength and heat resistance and preparation method thereof
CN112301259A (en) High-strength die-casting aluminum alloy, and preparation method and application thereof
CN104928549A (en) High-strength and high-elasticity-modulus casting Mg-RE alloy and preparation method thereof
CN101235454A (en) Quasi-crystal enhancement Mg-Zn-Er heat-resistant magnesium alloy and preparation method thereof
CN109266886B (en) Method for refining intermetallic compound phase of manganese-iron-containing aluminum alloy
CN111636017A (en) Semisolid forming aluminum alloy and preparation method thereof
CN115558825B (en) High-heat-conductivity high-strength and high-toughness die-casting aluminum alloy and preparation method thereof
CN100410407C (en) Mg-Al-Si-Mn-Ca alloy and method for preparing same
CN114717453B (en) High-toughness cast aluminum-silicon alloy and preparation method thereof
CN114752831B (en) High-strength corrosion-resistant aluminum alloy and preparation method and application thereof
CN110983119A (en) High-strength high-thermal-conductivity die-casting aluminum alloy material and preparation method thereof
CN115961186A (en) Die-casting aluminum alloy material and preparation method and application thereof
CN109161767A (en) A kind of creep-resistant property magnesium alloy of the phase containing W and preparation method thereof

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant
TR01 Transfer of patent right

Effective date of registration: 20210602

Address after: 121000 Room 201, building 46-15, Huanghai street, Songshan New District, Jinzhou City, Liaoning Province

Patentee after: Jinzhou Jinke High-tech Development Co.,Ltd.

Address before: 121001, 169 street, Guta District, Liaoning, Jinzhou

Patentee before: LIAONING University OF TECHNOLOGY

TR01 Transfer of patent right
CP02 Change in the address of a patent holder

Address after: 121000 room 205, 56 Songshan street, Songshan New District, Jinzhou City, Liaoning Province

Patentee after: Jinzhou Jinke High-tech Development Co.,Ltd.

Address before: 121000 Room 201, building 46-15, Huanghai street, Songshan New District, Jinzhou City, Liaoning Province

Patentee before: Jinzhou Jinke High-tech Development Co.,Ltd.

CP02 Change in the address of a patent holder
TR01 Transfer of patent right

Effective date of registration: 20230608

Address after: Room 1206, Floor 12, Tus Cluster Innovation Building, No. 118, Rongtong Road, Huangdao District, Qingdao, Shandong 266000

Patentee after: Qingdao Liudian Bearing Technology Co.,Ltd.

Address before: 121000 room 205, 56 Songshan street, Songshan New District, Jinzhou City, Liaoning Province

Patentee before: Jinzhou Jinke High-tech Development Co.,Ltd.

TR01 Transfer of patent right