CN103820683A - Multi-component refining and modifying processing method of the Fe phase in high-Fe silicon aluminum alloy - Google Patents
Multi-component refining and modifying processing method of the Fe phase in high-Fe silicon aluminum alloy Download PDFInfo
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- CN103820683A CN103820683A CN201410073152.4A CN201410073152A CN103820683A CN 103820683 A CN103820683 A CN 103820683A CN 201410073152 A CN201410073152 A CN 201410073152A CN 103820683 A CN103820683 A CN 103820683A
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Abstract
The invention discloses a multi-component refining and modifying processing method of the Fe phase in a high-Fe silicon aluminum alloy. The method comprises steps of: (1) melting the high-Fe silicon aluminum alloy at 700-740 DEG C to obtain an aluminum alloy solution, with the weight percent of the Fe in the high-Fe silicon aluminum alloy being 0.8-2.0%; (2) pre-heating a multi-component refining and modifying agent at 150-250 DEG C, with the multi-component refining and modifying agent comprising Al-Ti-C, Mn and RE; and (3) adding the multi-component refining and modifying agent into the aluminum alloy solution, stirring fully until the reaction is finished, adding C2Cl6 to perform refining and to remove gas, allowing the mixture to stand for 10-15 min, deslagging, casting and forming. According to the method, refining processing and modifying processing of the Fe phase in the high-Fe silicon aluminum alloy are integrated, thus simplifying the melt processing technology. The method is simple. The refining and modifying agent is convenient to prepare and free of pollution and the adding amount is easy to control.
Description
Technical field
The present invention relates to Al-Si is the metamorphism treatment method of Fe phase in cast aluminium alloy, particularly the polynary composite refining metamorphism treatment method of Fe phase in a kind of high Fe aluminum silicon alloy.
Background technology
Cast aluminium alloy, as a kind of traditional metal alloy compositions, is widely used in the every field such as automobile, machinery, space flight.Aluminum silicon alloy is the cast aluminium alloy of consumption maximum, accounts for whole aluminium casting 85%-90%.If ADC12 is exactly Japanese a kind of cast Al-Si alloy trade mark, be equivalent to the alloy for die casting YL113 of domestic widespread use, belong to Al-Si-Cu and be associated gold.Wherein in ADC12 alloy, require Fe%<0.9%, YL113 requires Fe%<1.3%.But ADC12 alloy is used waste aluminum melting substantially, its Fe, Si content are far above limit standard.In industrial production, be generally to add primary aluminum dilution to reduce Fe content, its cost is high and polluted primary aluminum, therefore needs to launch the applied research of high Fe cast aluminium alloy.One of its method is exactly to be gone bad and changed the existence form of harmful iron phase by refinement.In the aluminum silicon alloy of high Fe, mainly generate ternary phase α iron phase and β iron phase.Wherein endanger mutually significantly with the β iron of thick sheet, the α iron that is Chinese character shape is less with respect to the impact harm of performance, therefore carry out refinement and the rotten growth pattern that changes iron phase of processing by adding appropriate trace alloying element, in refinement Fe phase, promote the generation of α iron phase, suppress the formation of β iron phase, thereby improve the performance of the high Fe aluminum silicon alloy of casting.
So-called grain refinement technology, be that anisotropy is little after thinning microstructure, processing time variation is even, and makes to be easily gathered in impurity, slag inclusion and the low melting point eutectic tissue distribution of crystal boundary more even, therefore have the more ingot casting of small grains tissue, its mechanical property and processing characteristics are all better.Common method has that the cooling intensity, reinforcement metal liquid of increase flows, additional flux method etc.So-called Modification Treatment Technique, is to add a small amount of material in sensing molten metal, promotes a kind of method of the raw core of molten metal or change crystal growing process.Traditional rotten processing, as additional flux method, Melt Overheating Treatment, raising speed of cooling etc., can change the iron phase in cast aluminium alloy in various degree.Composite refining modifying technology of the present invention, is the rotten and thinning effect that utilizes several different elements, by mutual coupling, changes Needle like Iron Phase in alloy, obtains the tissue of comparatively disperse, improves performance.The advantages such as comparatively speaking, additional flux method can play refinement and metamorphism to crystal grain simultaneously, and has simple to operate, technique and be easy to control, with low cost.
Summary of the invention
In order to overcome the above-mentioned shortcoming and deficiency of prior art, the object of the present invention is to provide the polynary composite refining metamorphism treatment method of Fe phase in a kind of high Fe aluminum silicon alloy, the refinement of Fe phase in high Fe aluminum silicon alloy and rotten processing are integrated, simplify melt treatment, its method is simple, polynary composite refining alterant is easy to prepare, and add-on is easy to control, pollution-free separating out.
Object of the present invention is achieved through the following technical solutions:
A polynary composite refining metamorphism treatment method for Fe phase in high Fe aluminum silicon alloy, comprises the following steps:
(1) 700～740 ℃ of high Fe aluminum silicon alloy of fusing, obtains aluminium alloy solution; In described high Fe aluminum silicon alloy, the mass percent of Fe is 0.8%～2.0%;
(2) polynary composite refining alterant is carried out to preheating at 150～250 ℃, described polynary composite refining alterant comprises Al-Ti-C, Mn and RE;
(3) polynary composite refining alterant is added to aluminium alloy solution, be stirred well to complete reaction, add C
2cl
6carry out refining degasification, leave standstill 10～15 minutes, the cast molding of skimming.
The consumption of described Al-Ti-C is:
If the mass percent of Fe is t in high Fe aluminum silicon alloy, Al-Ti-C is 0.2t～2.0t with respect to the mass percent of high Fe aluminum silicon alloy.
The consumption of described Mn is:
If the mass percent of Fe is t in high Fe aluminum silicon alloy, Mn is 0.2t～1.0t with respect to the mass percent of high Fe aluminum silicon alloy.
The consumption of described Re is:
If the mass percent of Fe is t in high Fe aluminum silicon alloy, RE is 0.01t～0.1t with respect to the mass percent of high Fe aluminum silicon alloy.
Described polynary composite refining alterant is made up of Al-5Ti-0.2C master alloy, Al-75%Mn additive, Al-10Re master alloy.
Described stirring, is specially:
Speed with 200～500r/min stirs.
The principle of polynary composite refining metamorphism treatment method of the present invention is as follows:
The refinement metamorphic mechanism of Al-Ti-C: because of titanium and reactive aluminum generation TiAl
3, at 665 ℃ of TiAl
3carry out Peritectic Reaction with liquid and generate α-Al, now α-Al is with TiAl
3as nuclei growth.TiAl
3play non-homogeneous nucleation, it has interface coherency mutually with refinement.TiAl
3for quadratic crystal, lattice constant a=b=0.0545nm, c=0.861, aluminium is face-centered cubic crystal, lattice constant a=0.405nm.When (001) TiAl3//(001)
altime, as long as the lattice of Al rotates 45 °, i.e. [100] TiAl
3// [110]
al, both have interface coherence corresponding relation, interatomic distance is: Al(a=0.573nm), TiAl
3(a=b=0.545nm), δ=4.9%; When (001) TiAl3//(001)
al, [100] TiAl
3// [110]
altime, b to δ value the same, and c to δ=0.17%.TiAl
3fusing point high (1337 ℃), can carry out again Peritectic Reaction with liquid and generate α-Al.Therefore TiAl
3it is extremely effectively heterogeneous nucleation of α-Al.May there is following reaction:
L+TiAl
3→α(Al)
After adding with master alloy, Al-Ti-C forms TiC.It is generally acknowledged, after adding C, experience following Peritectic Reaction:
L+TiC or (Al, Ti) C+TiAl
3→ α (Al)
Because TiC or (Al, Ti) C compare TiAl as the heterogeneous nucleation of α (Al)
3more effective.Just the pig iron has microcosmic smooth interface mutually, is the leading phase of crystallization, and the speed of growth is mutually faster than α-Al, and it is faller gill shape that the anisotropy of its growth causes it to produce irregular form.By rotten, the preferential growth direction of primary phase is restricted, has suppressed the trend that Fu Tiexiang grows in original forming core substrate, thereby eliminated the heredity of faller gill shape, make primary phase grow up to Chinese character shape, square shape.
The metamorphic mechanism of Mn is after Mn adds, to have expanded α iron phase region, changes mutually to α iron thereby be conducive to Needle like Iron Phase.In aluminum silicon alloy, the A1 generating in fusion process
2o
3microscopic particles is as crystallization nuclei, and FuMn district atom easily depends on forming core growth on it and raw A1
6mn phase; The enrichment of regional area Mn and Fe atom impels (FeMn) A1
6separate out growth.
RE element is adsorbed on around FuFe district, hinders Fe atomic migration, increases the concentration gradient of Fe in the liquid phase of forward position, interface, has caused constitutional supercooling.On interface, the rare earth of enrichment is adsorbed on the surface of Fu Tiexiang, hinders it and grows up.These effects have caused eutectic α (Al) mutually and eutectic Al
3the divorced eutectic growth of Fe phase.And generate rich iron phase forming core core by being combined with Al, affect the diffusion process of solute atoms and the growth pattern of impurity phase, replace rich Fe and be grouped into unit and usually reduce the nucleation rate that the approach such as Fe/Mn improve rich Fe phase and impel Fe phase multidimensional to grow in middle part mutually.
Compared with prior art, the present invention has the following advantages and beneficial effect:
(1) the present invention will be integrated to the thinning processing of Fe phase and rotten processing, simplify Fe phase melt treatment in cast aluminium alloy, reduced cost, and proved through great many of experiments and production, there is extraordinary refinement modification effect, improved the performance of aluminum silicon alloy.
(2) polynary composite refining metamorphism treatment method technique of the present invention is simple, and polynary composite refining alterant composition is easy to control, and is easy to realize industrialized mass production.
(3) polynary composite refining alterant of the present invention in use, all discharge, and belongs to Environmentally-sound technology by contamination-free.
(4) the present invention has better refinement modification effect mutually to the cast Al-Si alloy Fe of high Fe, and the refinement modification effect that is 0.8%～2.0% for the mass percent of Fe in cast aluminium alloy is especially especially remarkable.As the ADC12 alloy for being most widely used, and without the rotten ADC12 alloy phase ratio of processing of polynary composite refining, after composite refining is rotten, Needle like Iron Phase diminishes and shortens, and harmful β changes the less α phase of harm mutually in a large number.
Accompanying drawing explanation
Fig. 1 is the XRD analysis result without the rotten Al-11Si-2Cu-1Fe alloy of polynary composite refining of embodiment 1;
Fig. 2 is the XRD analysis result of the Al-11Si-2Cu-1Fe alloy after the polynary composite refining of embodiment 1 goes bad;
Fig. 3 is the metallographic structure figure without the rotten Al-11Si-2Cu-1Fe alloy of polynary composite refining of embodiment 1;
Fig. 4 is the metallographic structure figure of the Al-11Si-2Cu-1Fe alloy after the polynary composite refining of embodiment 1 goes bad;
Fig. 5 is the metallographic structure figure of the Al-11Si-2Cu-1Fe alloy after the polynary composite refining of embodiment 2 goes bad;
Fig. 6 is the metallographic structure figure without the rotten Al-12Si-0.5Cu-1Fe alloy of polynary composite refining of embodiment 3;
Fig. 7 is the metallographic structure figure of the Al-12Si-0.5Cu-1Fe alloy after the polynary composite refining of embodiment 3 goes bad;
Fig. 8 is the metallographic structure figure without the rotten Al-11Si-2Cu-2Fe alloy of polynary composite refining of embodiment 4;
Fig. 9 is the metallographic structure figure of the Al-12Si-0.5Cu-1Fe alloy after the polynary composite refining of embodiment 4 goes bad;
Figure 10 is the metallographic structure figure without the rotten Al-7Si-1.5Fe alloy of polynary composite refining of embodiment 5; ;
Figure 11 is the metallographic structure figure of the Al-7Si-1.5Fe alloy after the polynary composite refining of embodiment 5 goes bad;
Figure 12 is the metallographic structure figure without the rotten Al-11Si-1.5Fe alloy of polynary composite refining of embodiment 6;
Figure 13 is the metallographic structure figure of the Al-7Si-1.5Fe alloy after the polynary composite refining of embodiment 6 goes bad;
Figure 14 is the metallographic structure figure through the independent interpolation Al-Ti-C of comparative example 1 Al-11Si-2Cu-1Fe alloy after treatment;
Figure 15 is the metallographic structure figure through the independent interpolation Mn of comparative example 2 Al-11Si-2Cu-1Fe alloy after treatment;
Figure 16 is the metallographic structure figure through the independent interpolation RE of comparative example 3 Al-11Si-2Cu-1Fe alloy after treatment;
Figure 17 is the metallographic structure figure of compound Al-Ti-C, the Mn Al-11Si-2Cu-1Fe alloy after treatment of comparative example 4.
Embodiment
Below in conjunction with embodiment, the present invention is described in further detail, but embodiments of the present invention are not limited to this.
Embodiment 1Al-11Si-2Cu-1Fe alloy composite refining is rotten to be processed
First determine the alloying constituent of the high Fe aluminum silicon alloy of the present embodiment by ICP spectroscopic analysis, concrete composition is in 1# in table 1, and in this alloy, the mass percent of Fe is 1.05%, belongs to the ADC12 cast Al-Si alloy of high ferro.Get original sample, XRD data as shown in Figure 1; Metallographic structure as shown in Figure 3.The present embodiment adds the Al-Ti-C of 0.6 times, the Mn of 1.0 times, 0.08 times of RE of the mass percent of Fe.
In the high Fe aluminum silicon alloy of the present embodiment, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 720 ℃ alloy becomes molten.
(2) take the mass percent of iron in melt as standard, in the present embodiment, the mass percent of Fe is 1.05%A (g).By cut mechanically legal system for the block Al-5Ti-0.2C of 0.6 × 1.05%A (g) and the block Al-10RE master alloy of 0.08 × 10 × 1.05%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 1.0 × 4/3 × 1.05%A (g), all stand-by 200 ℃ of preheatings.
(3) at 760 ℃ by the block Al-5Ti-0.2C of 200 ℃ of preheatings, Al-10RE master alloy and Powdered Al-75%Mn additive, above melt, add, with the speed hand mixing of 400r/min, it is reacted completely, leave standstill after 2min; Add C
2cl
6refining degasification, leaves standstill 13min, the cast molding of skimming.Cutting sampling.
Fig. 2 is the XRD diffracting spectrum through the rotten aluminum silicon alloy after treatment of polynary composite refining of the present embodiment, as seen from the figure, and Al
5feSi and Al
9feSi has formed TiFeSi, Fe through polynary composite inoculating
2mnSi, LaFe
9si phase, illustrates that Al-Ti-C, Mn, RE have participated in treating processes.Fig. 4 is that as seen from the figure, rectangular β needle-like almost disappears through the metallographic of the rotten aluminum silicon alloy after treatment of polynary composite refining of this enforcement, and grain refining disperse is obvious.From table 2 test data, through the sample (treatment samples 1) of the present embodiment processing, the length of needle-like Fe phase, width, length-to-diameter ratio all diminish to some extent compared with original sample (original sample 1).
Embodiment 2Al-11Si-2Cu-1Fe alloy composite refining is rotten to be processed
First determine the alloying constituent of high ferro aluminum silicon alloy by ICP spectroscopic analysis, concrete composition is in 1# in table 1, and in this alloy, the mass percent of Fe is 1.05%, belongs to the ADC12 cast Al-Si alloy of high ferro.As shown in Figure 3, the present embodiment adds the Al-Ti-C of 2 times, the Mn of 0.2 times, 0.01 times of RE of the mass percent that mass percent is Fe to original sample metallographic.
In the high Fe aluminum silicon alloy of the present embodiment, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 700 ℃ alloy becomes molten.
(2) take the mass percent of iron in melt as standard, in this example, the mass percent of Fe is 1.05%A (g).By cut mechanically legal system for the block Al-5Ti-0.2C of 2.0 × 1.05%A (g) and the block Al-10RE master alloy of 0.01 × 10 × 1.05%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 0.2 × 4/3 × 1.05%A (g), all stand-by 200 ℃ of preheatings.
(3) at 740 ℃ by 150 ℃ of preheated block Al-5Ti-0.2C, Al-10RE master alloy and Powdered Al-75%Mn additive, above melt, add, with the speed hand mixing of 200r/min, it is reacted completely, leave standstill after 1min; Add C
2cl
6degasification, leaves standstill 10min, the cast molding of skimming.Sampling mill metallographic, after polynary composite refining is rotten, metallograph as shown in Figure 5.As seen from the figure, rectangular β needle-like almost disappears, the obvious refinement disperse of crystal grain, and tissue distribution is even.Compared with Fig. 2, degree of refinement is better, and the addition that increases Al-Ti-C is described, to microstructure refinement metamorphism is more obvious, even dispersion is more abundant.From table 2 test data, through the sample (treatment samples 2) of the present embodiment processing, the length of needle-like Fe phase, width, length-to-diameter ratio all diminish to some extent compared with original sample (original sample 1).
Embodiment 3Al-12Si-0.5Cu-1Fe alloy composite refining is rotten to be processed
First determine the alloying constituent of high ferro aluminum silicon alloy by ICP spectroscopic analysis, concrete composition is in 2# in table 1, and in this alloy, the mass percent of Fe is 0.95%, belongs to the ADC12 cast Al-Si alloy of high ferro.As shown in Figure 6, with Fig. 1 comparison, along with silicone content rises, copper content reduces in metallographic structure, and minute hand shape iron tails off mutually.The present embodiment adds the Al-Ti-C of 1.0 times, the Mn of 2.0 times, 0.1 times of RE of the mass percent that mass percent is Fe.
In the high Fe aluminum silicon alloy of the present embodiment, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 300 ℃, sprinkle insulating covering agent, treat that when temperature rises to 740 ℃ alloy becomes molten.
(2) take the mass percent of iron in melt as standard, in this example, the mass percent of Fe is 0.95%A (g).By cut mechanically legal system for the block Al-5Ti-0.2C of 1.0 × 0.95%A (g) and the block Al-10RE master alloy of 0.1 × 10 × 0.95%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 2.0 × 4/3 × 0.95%A (g), all stand-by 200 ℃ of preheatings.
(3) at 780 ℃ by 250 ℃ of preheated block Al-5Ti-0.2C, Al-10RE master alloy and Powdered Al-75%Mn additive, above melt, add, with the speed hand mixing of 500r/min, it is reacted completely, leave standstill after 3min; Add C
2cl
6degasification, leaves standstill 15min, the cast molding of skimming.Sampling mill metallographic, after polynary composite refining is rotten, metallograph as shown in Figure 7.As seen from the figure, rectangular β needle-like occurs rotten, plays certain dispersion.From table 2 test data, through the sample (treatment samples 3) of the present embodiment processing, the length of needle-like Fe phase, width, length-to-diameter ratio all diminish to some extent compared with original sample (original sample 2).
Embodiment 4Al-11Si-2Cu-2Fe alloy composite refining is rotten to be processed
First determine the alloying constituent of high ferro aluminum silicon alloy by ICP spectroscopic analysis, concrete composition is in 3# in table 1, and in this alloy, the mass percent of Fe is 1.93%, belongs to the ADC12 cast Al-Si alloy of high ferro, and Fig. 8 is its original metallograph.With the ADC12 alloy phase ratio that Fig. 1 iron-holder is 1.05%Fe, iron level increase causes thick Needle like Iron Phase showed increased in metallographic view, and Needle like Iron Phase becomes longer.Al-Ti-C, the Mn of 0.6 times, 0.05 times of RE that the mass percent that is Fe that the present embodiment adds mass percent is 0.2 times.
In the high Fe aluminum silicon alloy of the present embodiment, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 740 ℃ alloy becomes molten.
(2) take the mass percent of iron in melt as standard, in this example, the mass percent of Fe is 1.93%A (g).By cut mechanically legal system for the block Al-5Ti-0.2C of 0.2 × 1.93%A (g) and the block Al-10RE master alloy of 0.05 × 10 × 1.93%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 0.6 × 4/3 × 1.93%A (g), all stand-by 200 ℃ of preheatings.
(3) at 760 ℃ by 200 ℃ of preheated block Al-5Ti-0.2C, Al-10RE master alloy and Powdered Al-75%Mn additive, above melt, add, hand mixing reacts completely it, leaves standstill after 3min; Add C
2cl
6degasification, leaves standstill 15min, the cast molding of skimming.Sampling mill metallographic, after the rotten processing of polynary composite refining, metallograph as shown in Figure 9.
As seen from the figure, elongated Needle like Iron Phase obviously shortens, and organizes disperse to distribute, and the iron of minute hand shape disappears mutually.From table 2 test data, through the sample (treatment samples 4) of the present embodiment processing, the length of needle-like Fe phase, width, length-to-diameter ratio all diminish to some extent compared with original sample (original sample 3).
Embodiment 5Al-7Si-1.5Fe hypoeutectic al-si alloy composite refining is rotten to be processed
First determine the alloying constituent of high ferro aluminum silicon alloy by ICP spectroscopic analysis, concrete composition is in 4# in table 1, in this alloy, the mass percent of Fe is 1.51%, belong to the Hypoeutectic Cast Al-Si Alloys of high ferro, Figure 10 is its original metallograph, and in picture, hypoeutectic aluminium silicon tissue has been cut in the appearance of a large amount of needle-like Fe phases.Al-Ti-C, the Mn of 1.0 times, 0.02 times of RE that the mass percent that is Fe that the present embodiment adds mass percent is 0.2 times.
In the high Fe aluminum silicon alloy of the present embodiment, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 720 ℃ alloy becomes molten.
(2) take the mass percent of iron Fe in melt as standard, in this example, the mass percent of Fe is 1.51%A (g).By cut mechanically legal system for the block Al-5Ti-0.2C of 0.2 × 1.51%A (g) and the block Al-10RE master alloy of 0.02 × 10 × 1.51%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 1.0 × 4/3 × 1.51%A (g), all stand-by 200 ℃ of preheatings.
(3) at 740 ℃ by 200 ℃ of preheated block Al-5Ti-0.2C, Al-10RE master alloy and Powdered Al-75%Mn additive, above melt, add, hand mixing reacts completely it, leaves standstill after 1min; Add C
2cl
6degasification, leaves standstill 10min, the cast molding of skimming.Sampling mill metallographic, after polynary composite refining is rotten, metallograph as shown in figure 11.As seen from the figure, the iron of minute hand shape has been phase-changed into petal-shaped, Chinese character shape, and modification effect is quite obvious.From table 2 test data, through the sample (treatment samples 5) of the present embodiment processing, the length of needle-like Fe phase, width, length-to-diameter ratio all diminish to some extent compared with original sample.
Embodiment 6Al-11Si-1.5Fe cocrystallized Al-Si alloy composite refining is rotten to be processed
First determine the alloying constituent of high ferro aluminum silicon alloy by ICP spectroscopic analysis, concrete composition is in 5# in table 1, in this alloy, the mass percent of Fe is 1.48%, belong to the casting cocrystallized Al-Si alloy of high ferro, Figure 12 is its original metallograph, and in picture, eutectic aluminum-silicon tissue has been cut in the appearance of a large amount of needle-like Fe phases.The present embodiment example is added Al-Ti-C, the Mn of 1.0 times, 0.05 times of RE of 0.6 times of mass percent that mass percent is Fe.
In the high Fe aluminum silicon alloy of the present embodiment, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 720 ℃ alloy becomes molten.
(2), take iron level in melt as standard, in this example, the mass percent of Fe is 1.48%A (g).By cut mechanically legal system for the block Al-5Ti-0.2C of 0.6 × 1.48%A (g) and the block Al-10RE master alloy of 0.05 × 10 × 1.48%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 1.0 × 4/3 × 1.48%A (g), all stand-by 200 ℃ of preheatings.
(3) at 720 ℃ by 200 ℃ of preheated block Al-5Ti-0.2C, Al-10RE master alloy and Powdered Al-75%Mn additive, above melt, add, hand mixing reacts completely it, leaves standstill after 3min; Add C
2cl
6degasification, leaves standstill 15min, the cast molding of skimming.Sampling mill metallographic, after polynary composite refining is rotten, metallograph as shown in figure 13.As seen from the figure, the iron of minute hand shape has been phase-changed into petal-shaped, and refinement modification effect is quite obvious.From table 2 test data, through the sample (treatment samples 6) of the present embodiment processing, the length of needle-like Fe phase, width, length-to-diameter ratio all diminish to some extent compared with original sample (original sample 5).
Comparative example 1 is added separately Al-Ti-C and is processed Al-11Si-2Cu-1Fe alloy
This comparative example adopts the method for adding separately Al-Ti-C.First determine the concrete composition of aluminium alloy by ICP spectroscopic data, concrete composition is in 1# in table 1, and the mass percent of this alloy Fe is 1.05%, belongs to high ferro ADC12 cast Al-Si alloy.This comparative example is added separately the Al-5Ti-0.2C master alloy that mass percent is 0.6 times of the mass percent of Fe, analyzes its impact on Fe phase in cast aluminium alloy.
In high Fe aluminum silicon alloy, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 720 ℃ aluminium alloy becomes molten.
(2) take the mass percent of Fe in melt as standard, in this example, the mass percent of Fe is 1.05%A (g).Block Al-5Ti-0.2C master alloy by cut mechanically legal system for 0.6 × 1.05%A (g), 200 ℃ of preheatings are stand-by.
(3) at 760 ℃, 200 ℃ of preheated block Al-5Ti-0.2C master alloys are added above melt, hand mixing reacts completely it, leaves standstill 2min; Add C
2cl
6degasification, leaves standstill 13min, the cast molding of skimming.Sampling mill metallographic, metallograph as shown in figure 14.
With Fig. 1 comparison, Figure 14 original structure is compared, and rectangular acicular beta iron obviously shortens and tails off mutually, and the Si of little needle-like also has certain refinement mutually, but rectangular acicular structure is still occupied sizable ratio.Fe phase crystal grain test data (contrast sample 1) as shown in table 2.
Comparative example 2 is added separately Mn and is processed Al-11Si-2Cu-1Fe alloy
This comparative example adopts the method for adding separately Mn.First determine the concrete composition of aluminium alloy by ICP spectroscopic data, concrete composition is in 1# in table 1, and the mass percent of this alloy Fe is 1.05%, belongs to high ferro ADC12 cast Al-Si alloy.This comparative example is added separately the Mn that mass percent is 1 times of the mass percent of Fe, analyzes its impact on Fe phase in cast aluminium alloy.
In high Fe aluminum silicon alloy, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 720 ℃ alloy becomes molten.
(2) take the mass percent of iron in melt as standard, in this example, the mass percent of Fe is 1.05%A (g).Al-75%Mn is Powdered, can prepare by mechanical crushing method the Al-75%Mn additive of 1.0 × 4/3 × 1.05%A (g), and 200 ℃ of preheatings are stand-by.
(3) at 760 ℃, 200 ℃ of preheated Al-75%Mn additives are added above melt, hand mixing reacts completely it, leaves standstill after 2min; Add C
2cl
6degasification, leaves standstill 13min, the cast molding of skimming.Sampling mill metallographic, metallograph as shown in figure 15.
With Fig. 1 comparison, β needle-like rectangular in Figure 15 almost disappears, and has occurred more dendroid, Chinese character shape α iron phase, but organizes comparatively thickly, and the Si of little needle-like does not almost change mutually.Fe phase crystal grain test data (contrast sample 2) as shown in table 2.
Comparative example 3 is added separately RE and is processed Al-11Si-2Cu-1Fe alloy
This comparative example adopts the method for adding separately RE.First determine the concrete composition of aluminium alloy by ICP spectroscopic data, concrete composition is in 1# in table 1, and the mass percent of this alloy Fe is 1.05%, belongs to high ferro ADC12 cast Al-Si alloy.This comparative example is added separately the RE that quality is 0.05 times of the mass percent of Fe, analyzes its impact on Fe phase in cast aluminium alloy.
In high Fe aluminum silicon alloy, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 350～400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 700～740 ℃ alloy becomes molten.
(2) take the mass percent of iron iron in melt as standard, in this example, the mass percent of Fe is 1.05%A (g).Al-10RE is solid block, can cut by mechanical process the Al-10RE master alloy of preparation 0.05 × 10 × 1.05%A (g), and 200 ℃ of preheatings are stand-by.
(3) add above melt at 760 ℃ of Al-10RE master alloys by 200 ℃ of preheated bulks, hand mixing reacts completely it, leaves standstill after 2min; Add C
2cl
6degasification, leaves standstill 13min, the cast molding of skimming.Sampling mill metallographic, metallograph as shown in figure 16.
With Fig. 1 comparison, in Figure 16, rectangular β needle-like reduces and length shortens mutually in a large number, and in alloy, has occurred that a small amount of square shape and petal-like α iron phase, the Si of little needle-like have certain refinement to occur mutually.Fe phase crystal grain test data (contrast sample 3) as shown in table 2.
The compound interpolation Al-Ti-C of comparative example 4, Mn process Al-11Si-2Cu-1Fe alloy
This comparative example adopts the method for compound interpolation Al-Ti-C and Mn.First determine the concrete composition of aluminium alloy by ICP spectroscopic data, concrete composition is in table 1, and the mass percent of this alloy Fe is 1.05%, belongs to the ADC12 cast Al-Si alloy of high ferro.0.6 times of Al-Ti-C of mass percent and 1.0 times of Mn that this comparative example is added Fe, analyze its impact on Fe phase in cast aluminium alloy.
In high Fe aluminum silicon alloy, the polynary composite refining metamorphism treatment method of Fe phase is specific as follows:
(1) taking 1# alloy mass is A(g).Adopt well formula resistance furnace, corundum crucible molten alloy.Alloy is put into corundum crucible, while being preheated to 400 ℃, sprinkle insulating covering agent, treat that when temperature rises to 720 ℃ alloy becomes molten.
(2) take the mass percent of iron in melt as standard, in this example, the mass percent of Fe is 1.05%A (g).Block Al-5Ti-0.2C master alloy by cut mechanically legal system for 0.6 × 1.05%A (g), can prepare by mechanical crushing method the Al-75%Mn additive of 1.0 × 4/3 × 1.05%A (g), all stand-by 200 ℃ of preheatings.
(3) at 760 ℃ by 200 ℃ of preheated block Al-5Ti-0.2C master alloys and Powdered Al-75%Mn additive, above melt, add, hand mixing reacts completely it, leaves standstill after 2min; Add C
2cl
6degasification, leaves standstill 13min, the cast molding of skimming, and metallograph is as shown in figure 17.
With Fig. 1 comparison, the long acicular structure in Figure 17 occurs obviously rotten, forms petal-shaped, Chinese character shape tissue, and certain refinement has occurred fine acicular Si mutually.Fe phase crystal grain test data (contrast sample 4) as shown in table 2.
The ICP spectroscopic data of the each high Fe aluminum silicon alloy of table 1
The Fe phase constitution contrast table of the each sample of table 2
Above-described embodiment is preferably embodiment of the present invention; but embodiments of the present invention are not limited by the examples; other any do not deviate from change, the modification done under spirit of the present invention and principle, substitutes, combination, simplify; all should be equivalent substitute mode, within being included in protection scope of the present invention.
Claims (6)
1. a polynary composite refining metamorphism treatment method for Fe phase in high Fe aluminum silicon alloy, is characterized in that, comprises the following steps:
(1) 700～740 ℃ of high Fe aluminum silicon alloy of fusing, obtains aluminium alloy solution; In described high Fe aluminum silicon alloy, the mass percent of Fe is 0.8%～2.0%;
(2) polynary composite refining alterant is carried out to preheating at 150～250 ℃, described polynary composite refining alterant comprises Al-Ti-C, Mn and RE;
(3) polynary composite refining alterant is added to aluminium alloy solution, be stirred well to complete reaction, add C
2cl
6carry out refining degasification, leave standstill 10～15 minutes, the cast molding of skimming.
2. the polynary composite refining metamorphism treatment method of Fe phase in high Fe aluminum silicon alloy according to claim 1, the consumption of described Al-Ti-C is:
If the mass percent of Fe is t in high Fe aluminum silicon alloy, Al-Ti-C is 0.2t～2.0t with respect to the mass percent of high Fe aluminum silicon alloy.
3. the polynary composite refining metamorphism treatment method of Fe phase in high Fe aluminum silicon alloy according to claim 1, the consumption of described Mn is:
If the mass percent of Fe is t in high Fe aluminum silicon alloy, Mn is 0.2t～1.0t with respect to the mass percent of high Fe aluminum silicon alloy.
4. the polynary composite refining metamorphism treatment method of Fe phase in high Fe aluminum silicon alloy according to claim 1, the consumption of described Re is:
If the mass percent of Fe is t in high Fe aluminum silicon alloy, RE is 0.01t～0.1t with respect to the mass percent of high Fe aluminum silicon alloy.
5. the polynary composite refining metamorphism treatment method of Fe phase in high Fe aluminum silicon alloy according to claim 1, described polynary composite refining alterant is made up of Al-5Ti-0.2C master alloy, Al-75%Mn additive, Al-10Re master alloy.
6. the polynary composite refining metamorphism treatment method of Fe phase in high Fe aluminum silicon alloy according to claim 1, described stirring, is specially:
Speed with 200～500r/min stirs.
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| CN109207773A (en) * | 2018-10-24 | 2019-01-15 | 广西大学 | A kind of composite fluxing agent and a kind of method for refining rich ferroaluminium using composite fluxing agent |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109207773A (en) * | 2018-10-24 | 2019-01-15 | 广西大学 | A kind of composite fluxing agent and a kind of method for refining rich ferroaluminium using composite fluxing agent |
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| CN113215453A (en) * | 2021-04-09 | 2021-08-06 | 华南理工大学 | Annealing softening resistant high-heat-conductivity corrosion-resistant cast aluminum alloy and preparation method thereof |
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