CN104532078A - AHS aluminum alloy and aluminum alloy extruded rod thereof - Google Patents
AHS aluminum alloy and aluminum alloy extruded rod thereof Download PDFInfo
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- CN104532078A CN104532078A CN201410768820.5A CN201410768820A CN104532078A CN 104532078 A CN104532078 A CN 104532078A CN 201410768820 A CN201410768820 A CN 201410768820A CN 104532078 A CN104532078 A CN 104532078A
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Abstract
The invention provides an AHS aluminum alloy and an extruded rod thereof. The AHS aluminum alloy comprises the following components in percentage by mass: 10-11.5% of Si, 2.0-3.0% of Cu, 0.35-0.45% of Mg, 0-0.5% of Fe, 0-0.3% of Zn, 0-0.1% of Mn, 0-0.01% of Ni, 0.02-0.05% of Sr, 0.01-0.04% of B and the balance of Al. The AHS aluminum alloy provided by the invention does not contain Ti, but contains B which is mainly used for refining an alpha-Al matrix and has an effect of inhibiting the growth of an alloy eutectic silicon structure. The Sr and B are adopted for compounding, refinement and modification, so that an AHS aluminum alloy casting rod with relatively small crystalline grains can be obtained, the defects of the AHS aluminum alloy can be reduced, and the product quality and the overall performance are improved. Experimental results show that the grain size of the AHS aluminum alloy provided by the invention is of 1-3 grades.
Description
Technical field
The invention belongs to technical field of metal, particularly relate to a kind of AHS aluminium alloy and aluminium alloy extruded rod thereof.
Background technology
AHS alloy is the one of Al-Si system piston alloy, and its composition is equivalent to the SAE328 alloy of domestic trade mark ZL108 and U.S.'s trade mark, and this alloy is generally used for permanent mold casting.AHS alloying constituent is close to Al-Si alloy eutectic point, and its good fluidity, resistance to air loss is high, and be inclined to without hot crackability, the also phenomenon such as pore-free and shrinkage porosite, and this alloy strength is high, thermal expansivity is little, and wear resisting property is good, and high-temperature behavior is also satisfactory.In addition, AHS alloy is different from ZL108 and SAE328 credit union, and it is a kind of wrought aluminium alloy, thus has better mechanical property and processing characteristics.Therefore, it is more suitable for than general cast Al-Si alloy and manufactures the parts such as gas engine piston and gin wheel, thus has vast potential for future development.
The extruded bars of AHS aluminium alloy is mainly used in the middle and high fast internal combustion engine forging middle or small cylinder diameter, and AHS aluminium alloy extruded rod ingot blank is adopted semicontinuous fusion casting and produced.In actual production, adopt the Φ 250mm ingot casting that the hot direct casting fabrication technique of semicontinuous founding is produced, founding controlled not at that time, often there is coarse grain, Feather-like Crystal in various degree, thick needle shaped eutectic silicon, thick block primary silicon tissue in ingot casting macro coupon, extruded product low power detects exists graniphyric defect, and the existence of this defect seriously reduces products machinery performance.
Summary of the invention
The object of the present invention is to provide a kind of AHS aluminium alloy and aluminium alloy extruded rod thereof, AHS aluminium alloy provided by the invention has less grain fineness number.
The invention provides a kind of AHS aluminium alloy, comprise the component of following massfraction:
The Si of 10.0 ~ 11.5%; The Cu of 2.0 ~ 3.0%; The Mg of 0.35 ~ 0.45%; The Fe of 0 ~ 0.5%; The Zn of 0 ~ 0.3%; The Mn of 0 ~ 0.1%; The Ni of 0 ~ 0.01%; The Sr of 0.02 ~ 0.05%; The B of 0.01 ~ 0.04%; Surplus is Al.
Preferably, the massfraction of described Si is 10.5 ~ 11.0%.
Preferably, the massfraction of described Cu is 2.2 ~ 2.8%.
Preferably, the massfraction of described Mg is 0.38 ~ 0.42%.
Preferably, the massfraction of described Si is 10.6 ~ 10.9%.
Preferably, the massfraction of described Cu is 2.6 ~ 2.7%.
Preferably, the massfraction of described Mg is 0.3 ~ 0.4%.
Preferably, the massfraction of described Fe is 0 ~ 0.3%; The massfraction of described Zn is 0 ~ 0.1%; The massfraction of described Mn is 0 ~ 0.05%; The massfraction of described Ni is 0 ~ 0.005%; The massfraction of described Sr is 0.02 ~ 0.05%.
Preferably, the grain fineness number of described AHS aluminium alloy is 1 ~ 3 grade.
The present invention also provides the aluminium alloy extruded rod of a kind of AHS, and obtained through extruding by AHS aluminium alloy cast ingot, described AHS aluminium alloy cast ingot is AHS aluminium alloy mentioned above.
The invention provides a kind of AHS aluminium alloy, comprise the component of following massfraction: the Si of 10 ~ 11.5%; The Cu of 2.0 ~ 3.0%; The Mg of 0.35 ~ 0.45%; The Fe of 0 ~ 0.5%; The Zn of 0 ~ 0.3%; The Mn of 0 ~ 0.1%; The Ni of 0 ~ 0.01%; The Sr of 0.02 ~ 00.05%; The B of 0.01 ~ 0.04%; Surplus is Al.AHS aluminium alloy provided by the invention not containing Ti element, but with the addition of B element, the main refinement α of B element-Al matrix, and growing up of alloy Eutectic Silicon in Al-Si Cast Alloys tissue has restraining effect simultaneously.Adopt Sr and B composite refining to go bad, the AHS aluminium alloy cast rod that crystal grain is less can be obtained, reduce the defect of AHS aluminium alloy, improve the quality of products and overall performance.Test-results shows, AHS aluminium alloy grain fineness number provided by the invention is 1 ~ 3 grade.
Accompanying drawing explanation
In order to be illustrated more clearly in the embodiment of the present invention or technical scheme of the prior art, be briefly described to the accompanying drawing used required in embodiment or description of the prior art below, apparently, accompanying drawing in the following describes is only embodiments of the invention, for those of ordinary skill in the art, under the prerequisite not paying creative work, other accompanying drawing can also be obtained according to the accompanying drawing provided.
Fig. 1 is the low power detection figure of the AHS aluminium alloy cast ingot that the embodiment of the present invention 1 obtains;
Fig. 2 is the AHS aluminium alloy cast ingot that obtains of the embodiment of the present invention 1 500 × under high power detect figure;
Fig. 3 is the low power detection figure of the aluminium alloy extruded rod of AHS that the embodiment of the present invention 1 obtains;
Fig. 4 is the aluminium alloy extruded rod of AHS that the embodiment of the present invention 1 obtains 500 × under high power detect figure;
Fig. 5 is the low power detection figure of the AHS aluminium alloy cast ingot that the embodiment of the present invention 2 obtains;
Fig. 6 is the AHS aluminium alloy cast ingot that obtains of the embodiment of the present invention 2 500 × under high power detect figure;
Fig. 7 is the low power detection figure of the aluminium alloy extruded rod of AHS that the embodiment of the present invention 2 obtains;
Fig. 8 is the aluminium alloy extruded rod of AHS that the embodiment of the present invention 2 obtains 500 × under high power detect figure;
Fig. 9 is the low power detection figure of the AHS aluminium alloy cast ingot that the embodiment of the present invention 3 obtains;
Figure 10 is the AHS aluminium alloy cast ingot that obtains of the embodiment of the present invention 3 500 × under high power detect figure;
Figure 11 is the low power detection figure of the aluminium alloy extruded rod of AHS that the embodiment of the present invention 3 obtains;
Figure 12 is the aluminium alloy extruded rod of AHS that the embodiment of the present invention 3 obtains 500 × under high power detect figure.
Embodiment
The invention provides a kind of AHS aluminium alloy, comprise the component of following massfraction: the Si of 10 ~ 11.5%; The Cu of 2.0 ~ 3.0%; The Mg of 0.35 ~ 0.45%; The Fe of 0 ~ 0.5%; The Zn of 0 ~ 0.3%; The Mn of 0 ~ 0.1%; The Ni of 0 ~ 0.01%; The Sr of 0.02 ~ 0.05%; The B of 0.01 ~ 0.04%; Surplus is Al.
AHS aluminium alloy provided by the invention has less grain fineness number.
In the present invention, the massfraction of described Si is preferably 10 ~ 11.5%, is more preferably 10.5 ~ 11%, most preferably is 10.8%; Silicon is the principal element in alloy, the rising of the solubility with temperature of silicon in sosoloid and increasing, and be 0.05% when room temperature, be 1.65% 577 DEG C time.The silicon exceeding solubleness exists with β phase, only can dissolve the aluminium of minute quantity, can be regarded as pure silicon in β phase.Product reaction is altogether there is and generates eutectic (alpha+beta) in aluminum silicon alloy 577 DEG C time.Along with the increase of silicone content, the silicon in tissue constantly increases mutually, improves the tensile strength of alloy.Eutectic silicon is before non-Metamorphism treatment, and general all slabbings distribution, seriously isolates matrix, due to the result of stress concentration, unit elongation is significantly reduced in the alloy; When silicone content is more than 13 ~ 14%, unit elongation only has 1%, and tensile strength also only has about 100MPa, loses use value.After rotten or refinement, tensile strength can bring up to 160 ~ 190MPa, and unit elongation can reach 6 ~ 12%, solve the excellent castability of Al-Si class alloy and inferior mechanical property this to contradiction, this kind of alloy is obtained and promotes the use of.Silicone content is except the mechanical property of alloy has an impact, and the mobility of alloy, resistance to air loss, thermal expansivity and specific resistance and density all can produce certain impact.
In the present invention, the massfraction of described Cu is preferably 2.0 ~ 3.0%, is more preferably 2.5%; The effect of main alloy element Cu and Mg forms CuAl
2.And Mg
2si strengthening phase, makes alloy significantly strengthen.When copper content in alloy increases, the intensity of alloy significantly increases, elongation declines, and hot strength constantly rises.This mainly because the increase of copper content, makes the Mg in alloy
2si phase gradually reduces and becomes Q phase and CuAl
2phase.Q phase, CuAl
2phase and Mg
2si phase is all the strengthening phase of alloy, but the thermotolerance of Q phase is best, and its solubleness in αsolidsolution is little, with the distributions of disperse in crystal boundary, αsolidsolution at high temperature can be stoped to be out of shape, put forward heavy alloyed resistance toheat.CuAl
2the thermotolerance of phase is taken second place, Mg
2the thermotolerance of Si phase is the poorest, thus suitably can increase the content of copper to put forward heavy alloyed hot strength for the AHS alloy being used as piston material.
In the present invention, the massfraction of described Mg is preferably 0.2 ~ 0.5%, is more preferably 0.3 ~ 0.4%, most preferably is 0.35%; When Mg content in alloy increases, the intensity of alloy sharply rises and plasticity plunges.Plunging of plasticity is main less relevant with the solubleness of magnesium in αsolidsolution.Under equilibrium conditions, 500 ~ 530 DEG C time, the solubleness of magnesium in αsolidsolution is 0.5 ~ 0.6%, and under the non-equilibrium condition of actual production, its solubleness is lower, only has 0.3 ~ 0.4%.Therefore for keeping certain plasticity, often the Mg content in AHS alloy is controlled about 0.5%.
In the present invention, the massfraction of described Mn is preferably 0 ~ 0.1%, is more preferably 0 ~ 0.05%; Mn is a kind of element of the deleterious effect being used for eliminating iron.It forms A1 in Al-Si alloy
10mn
2si and Al
6mn phase.Iron can the β phase wherein making to be harmful to that is dissolved in partly reduce, and improves hot strength simultaneously.And when forming eutectic containing Mn phase and αsolidsolution, in close-packed arrays, be the bone shape that bar strip is short and small, its hazardness is less.When iron level is higher, the add-on of Mn is generally 1/2 of iron level.In addition, Mn itself is also often used to put forward heavy alloyed resistance toheat.
In the present invention, the massfraction of described B is preferably 0.02 ~ 0.04%, is more preferably 0.035%; The massfraction of described Fe is preferably 0 ~ 0.5%, is more preferably 0 ~ 0.3%; The massfraction of described Zn is preferably 0 ~ 0.3%, is more preferably 0 ~ 0.1%; The massfraction of described Ni is preferably 0 ~ 0.01%, is more preferably 0 ~ 0.005%; The massfraction of described Sr is preferably 0.02 ~ 0.05%, is more preferably 0.025 ~ 0.03%; The massfraction of described Al and the massfraction sum of other components are 100%.
In the present invention, described AHS aluminium alloy preferably prepares according to following steps:
A) by Al-Si master alloy, pure Cu plate and 99.7%Al ingot, in melting process furnace, carry out melting, obtain aluminium alloy melt;
B) alterant is joined described steps A) in the melt that obtains, carry out modifying-refining process, obtain the alloy melt of refinement; Described alterant comprises Sr class alterant and/or boron class alterant;
C) by described step B) alloy melt of refinement that obtains casts, and obtains AHS aluminium alloy.
By Al-Si master alloy, pure Cu plate and 99.7%Al ingot, in melting process furnace, carry out melting, obtain aluminium alloy melt.After melt melts completely, add Mg ingot when molten aluminium temperature is 720 ~ 740 DEG C.
In the present invention, the massfraction of described Si element is preferably 10 ~ 11.5%, is more preferably 10.5 ~ 11%, most preferably is 10.8%; The present invention preferably adopts Al-Si master alloy, and in the present invention, in described Al-Si alloy, the massfraction of Si is preferably 20%.
In the present invention, the massfraction of described Cu is preferably 2.0 ~ 3.0%, is more preferably 2.5%; The preferred pure Cu plate of the present invention, in described pure Cu plate, the content of Cu preferably >=99.99%.
In the present invention, the massfraction of described Mg is preferably 0.2 ~ 0.5%, is more preferably 0.3 ~ 0.4%, most preferably is 0.35%; The present invention preferably adopts pure Mg ingot to carry out described melting, and in described pure Mg ingot, the massfraction of Mg preferably >=99.95%.
In the present invention, the massfraction of described B is preferably 0.02 ~ 0.04%, is more preferably 0.035%; The present invention preferably adopts Al-B master alloy to carry out described melting, and in described Al-B master alloy, the massfraction of B (boron) is preferably 3%.
In the present invention, the massfraction of described Al and the massfraction sum of other components are 100%, and the present invention preferably adopts pure Al ingot to carry out described melting, and in described pure Al ingot, the massfraction of Al preferably >=99.7%.
In the present invention, the temperature of described melting is preferably 730 ~ 770 DEG C, is more preferably 740 ~ 760 DEG C; The time of described melting is preferably 3 ~ 7 hours; The present invention preferably carries out described melting in smelting furnace, should first prepurging or prepurging before by above-mentioned raw materials shove charge, and when filling with substance Al-Si master alloy is added in lower floor in furnace charge, and Cu plate is placed at the middle and upper levels.Then start melting, when furnace charge major partization at ordinary times, with rake, the convex peak exposing liquid level is bulldozed, and in good time rake stirs metal as far as possible, with accelerate fusing.Treat that furnace charge melts completely, when melt temperature rises to 730 ~ 740 DEG C, thoroughly stir more than 10min, if scum silica frost is many before stirring, ground flux can be sprinkled in stove.Dross on surface of fusant is scratched clean after stirring.Melt temperature 740 ~ 750 DEG C adds Mg source.Mg ingot will be pressed into melt, forbids to expose liquid level.Must carry out twice stirring after Mg ingot melts completely, twice mixing chamber interval is no less than 15min.
After completing described melting, the present invention preferably samples in stokehold the melt obtained, to analyze bath composition, then carry out corresponding composition adjustment according to the content requirement of above-mentioned each composition, the method for described adjustment is method well known to those skilled in the art.
After stokehold composition is qualified, described alterant is preferably first carried out thermal pretreatment by the present invention, then joining in described melting thing, carries out fine degenerate process, and in the present invention, the thermal pretreatment of described alterant is method well known to those skilled in the art.
After completing the thermal pretreatment of described alterant, the alterant of preheating adds in described molten aluminium by the present invention, carry out thinning processing, obtain the molten aluminium of modifying-refining, in the present invention, described alterant preferably includes Sr class alterant and/or boron class alterant, the preferred Al-Sr master alloy of described Sr class alterant, in described Al-Sr master alloy, the massfraction of Sr is preferably 10%.In the present invention, described boron class alterant preferably includes Al-B master alloy, and in described Al-B master alloy, the massfraction of B is preferably 3%; Boron in described boron class alterant is consistent with the consumption in B source in technique scheme, does not repeat them here.
In the present invention, the temperature of described Metamorphism treatment is preferably 720 ~ 740 DEG C, is more preferably 725 ~ 730 DEG C; The time of described Metamorphism treatment is preferably 10 ~ 25 minutes; After adding alterant, described alterant will be pressed into melt, forbids to swim on liquid level.After described alterant melts completely, Melt Stirring is even.It is noted that prohibit the use any flux and insulating covering agent after adding Sr class alterant.
The present invention preferably 740 ~ 750 DEG C time the refining of Ar gas is carried out to melt, two refining pipe double doors refining simultaneously 20min, scratch clean dross on surface of fusant after refining, leave standstill after skimming.
After completing described Metamorphism treatment, the molten aluminium that described Metamorphism treatment obtains modifying-refining is cast by the present invention, obtains AHS aluminium alloy.In the present invention, the speed of described casting is preferably 90 ~ 100mm/min, is more preferably 95 ~ 98mm/min; The temperature of described casting is preferably 710 ~ 730 DEG C, is more preferably 720 ~ 730 DEG C; Hydraulic pressure in described castingprocesses is preferably 0.04 ~ 0.08MPa, is more preferably 0.05 ~ 0.07MPa.
In the present invention, the AHS aluminium alloy that described casting obtains is preferably the AHS alloy casting rod that specification is Φ 250mm.
After completing described casting, the present invention preferably extrudes casting the AHS aluminium alloy cast ingot obtained, and obtain the aluminium alloy extruded rod of AHS, in the present invention, the temperature of described extruding is preferably 430 ~ 440 DEG C; The temperature of the container that described extruding is used is preferably 400 ~ 450 DEG C; The speed of described extruding preferably≤2mm/min, extrusion ratio is preferably 25.
The present invention have detected the grain fineness number of the AHS aluminium alloy that the present invention obtains according to the Al and Alalloy fabricated product microstructure method of inspection, and result shows, the grain fineness number of the AHS aluminium alloy obtained according to casting technique of the present invention is 1 ~ 3 grade.
The present invention has carried out low power detection according to the Al and Alalloy fabricated product microstructure method of inspection to the AHS aluminium alloy obtained, and result shows, the AHS aluminium alloy that the present invention obtains does not have feather crystal grain defect and primary silicon defect, and grain fineness number is 1 ~ 3 grade.
The present invention has carried out high power detection according to the Al and Alalloy fabricated product microstructure method of inspection to the AHS aluminium alloy obtained, and result shows, of the present invention to the Eutectic Silicon in Al-Si Cast Alloys of AHS aluminium alloy be organized as tiny staple fibre shape, thinning effect is better.
The invention provides a kind of AHS aluminium alloy, comprise the component of following massfraction: the Si of 10 ~ 11.5%; The Cu of 2.0 ~ 3.0%; The Mg of 0.35 ~ 0.45%; The Fe of 0 ~ 0.5%; The Zn of 0 ~ 0.3%; The Mn of 0 ~ 0.1%; The Ni of 0 ~ 0.01%; The Sr of 0.02 ~ 0.05%; The B of 0.01 ~ 0.04%; Surplus is Al.AHS aluminium alloy provided by the invention not containing Ti element, but with the addition of B element, the main refinement α of B element-Al matrix, and growing up of alloy Eutectic Silicon in Al-Si Cast Alloys tissue has restraining effect simultaneously.Adopt Sr and B composite refining to go bad, the AHS aluminium alloy cast rod that crystal grain is less can be obtained, reduce the defect of AHS aluminium alloy, improve the quality of products and overall performance.Test-results shows, AHS aluminium alloy grain fineness number provided by the invention is 1 ~ 3 grade.
In order to further illustrate the present invention, below in conjunction with embodiment, a kind of AHS aluminium alloy provided by the invention and aluminium alloy extruded rod thereof being described in detail, but can not limiting the scope of the present invention being understood as.
Embodiment 1
By the Al-Si master alloy prepared, pure Cu plate and pure Al ingot add smelting furnace, carry out melting, answer prepurging or prepurging before shove charge.When filling with substance Al-Si master alloy is added in lower floor in furnace charge, and Cu plate is placed at the middle and upper levels.Smelting temperature is 740 ± 10 DEG C.
Furnace charge major partization at ordinary times, be bulldozed at the convex peak exposing liquid level, and in good time rake is stirred metal with rake as far as possible, to accelerate fusing.Treat that furnace charge melts completely, when melt temperature rises to 730-740 DEG C, thoroughly stir more than 10min, if scum silica frost is many before stirring, ground flux can be sprinkled in stove.Dross on surface of fusant is scratched clean after stirring.Melt temperature 720 ~ 740 DEG C adds and prepares Mg ingot.Mg ingot will be pressed into melt, forbids to expose liquid level.Must carry out twice stirring after Mg ingot melts completely, twice mixing chamber interval is no less than 15min.Get stokehold sample after uniform composition, quantity is a mushroom sample and a cake sample, and probe temperature is 730 DEG C.
Add Al-Sr, Al-3B master alloy after stokehold composition is qualified and carry out fine degenerate process, must through thermal pretreatment before Al-Sr, Al-3B master alloy adds.
Al-10Sr add-on: 4.5kg/t pressed by virgin material, body waste material presses 2kg/t.Al-3B add-on: add by 0.035%B.Add temperature: 730 ± 10 DEG C.
Al-Sr (bar), Al-3B master alloy will be pressed into melt, forbid to swim on liquid level.After Al-Sr, Al-3B master alloy melts completely, Melt Stirring is even.
Any flux and insulating covering agent is prohibitted the use after adding Sr.
Carry out the refining of Ar gas to melt when 750 DEG C, two refining pipe double door refining simultaneously 20min, scratch clean dross on surface of fusant after refining.Leave standstill after skimming, carry out casting preparation work simultaneously, and cast as early as possible.
The speed of casting is 90mm/min, and hydraulic pressure is 0.04MPa, and casting temp is 710 DEG C, obtains the AHS aluminium alloy cast rod that specification is Φ 250mm.
Extrude after having cast, be AHS alloy casting rod railway carriage, the sawing of Φ 250mm by specification be after Φ 240 × 760mm, extrude by production common process, container temperature is 400 DEG C, extrusion temperature is 430 DEG C, extrusion speed≤2mm/min, extrusion ratio is 25, and extruded bars specification is Φ 34mm.Alloying constituent comprises: the Si of 10.94%, the Fe of 0.3%, the Cu of 2.66%, the Mn of 0.04%, the Mg of 0.5%, the Ni of 0.01%, the Zn of 0.02%, the Sr of the 0.03% and Al of surplus.
The present invention have detected the grain fineness number of the AHS aluminium alloy cast ingot that the present embodiment obtains according to technique scheme, and result is as shown in table 1, and table 1 is the detected result of the AHS aluminium alloy cast ingot that the embodiment of the present invention 1 ~ 3 obtains.
The present invention have detected the mechanical property of the aluminium alloy extruded rod of AHS that the present embodiment obtains according to technique scheme, and result is as shown in table 2, and table 2 is the mechanical performance data of the aluminium alloy extruded version of AHS that the embodiment of the present invention 1 ~ 3 obtains.
The present invention has carried out low power detection according to technique scheme to the AHS aluminium alloy cast ingot that the present embodiment obtains, and as shown in Figure 1, Fig. 1 is the low power detection figure of the AHS aluminium alloy cast ingot that the embodiment of the present invention 1 obtains.
The present invention has carried out high power detection according to technique scheme to the AHS aluminium alloy cast ingot that the present embodiment obtains, as shown in Figure 2, Fig. 2 is the AHS aluminium alloy cast ingot that obtains of the embodiment of the present invention 1 500 × under high power detect figure.
The present invention has carried out low power detection according to technique scheme to the aluminium alloy extruded rod of AHS that the present embodiment obtains, and as shown in Figure 3, Fig. 3 is the low power detection figure of the aluminium alloy extruded rod of AHS that the embodiment of the present invention 1 obtains.
The present invention has carried out high power detection according to technique scheme to the aluminium alloy extruded rod of AHS that the present embodiment obtains, as shown in Figure 4, Fig. 4 is the aluminium alloy extruded rod of AHS that the embodiment of the present invention 1 obtains 500 × under high power detect figure.
Embodiment 2
By the Al-Si master alloy prepared, pure Cu plate and pure Al ingot add smelting furnace, carry out melting, answer prepurging or prepurging before shove charge.When filling with substance Al-Si master alloy is added in lower floor in furnace charge, and Cu plate is placed at the middle and upper levels.Smelting temperature is 740 ± 10 DEG C.
Furnace charge major partization at ordinary times, be bulldozed at the convex peak exposing liquid level, and in good time rake is stirred metal with rake as far as possible, to accelerate fusing.Treat that furnace charge melts completely, when melt temperature rises to 730 DEG C, thoroughly stir more than 10min, if scum silica frost is many before stirring, ground flux can be sprinkled in stove.Dross on surface of fusant is scratched clean after stirring.Melt temperature 730 ± 10 DEG C adds the Mg ingot prepared.Mg ingot will be pressed into melt, forbids to expose liquid level.Must carry out twice stirring after Mg ingot melts completely, twice mixing chamber interval is no less than 15min.Get stokehold sample after uniform composition, quantity is a mushroom sample and a cake sample, and probe temperature is 730-750 DEG C.
Add Al-Sr, Al-3B master alloy after stokehold composition is qualified and carry out fine degenerate process, must through thermal pretreatment before Al-Sr, Al-3B master alloy adds.
Al-Sr add-on: 4.5kg/t pressed by virgin material, body waste material presses 2kg/t.Al-3B add-on: add by 0.04%B.Add temperature: 730 ± 10 DEG C.
Al-Sr (bar), Al-3B master alloy will be pressed into melt, forbid to swim on liquid level.After Al-Sr, Al-3B master alloy melts completely, Melt Stirring is even.
Any flux and insulating covering agent is prohibitted the use after adding Sr.
Carry out the refining of Ar gas to melt when 740 ~ 750 DEG C, two refining pipe double door refining simultaneously 20min, scratch clean dross on surface of fusant after refining.Leave standstill after skimming, carry out casting preparation work simultaneously, and cast as early as possible.
The speed of casting is 95mm/min, and hydraulic pressure is 0.05MPa, and casting temp is 710 DEG C, obtains the AHS aluminium alloy cast ingot that specification is Φ 250mm.
Extrude after having cast, be AHS alloy casting rod railway carriage, the sawing of Φ 250mm by specification be after Φ 240 × 760mm, extrude by large common process of producing, container temperature is 450 DEG C, extrusion temperature is 440 DEG C, extrusion speed≤2mm/min, extrusion ratio is 25, and extruded bars specification is Φ 34mm.
The present invention have detected the grain fineness number of the AHS aluminium alloy cast ingot that the present embodiment obtains according to technique scheme, and result is as shown in table 1, and table 1 is the detected result of the AHS aluminium alloy cast ingot that the embodiment of the present invention 1 ~ 3 obtains.
The present invention have detected the mechanical property of the aluminium alloy extruded rod of AHS that the present embodiment obtains according to technique scheme, and result is as shown in table 2, and table 2 is the mechanical performance data of the aluminium alloy extruded version of AHS that the embodiment of the present invention 1 ~ 3 obtains.
The present invention has carried out low power detection according to technique scheme to the AHS aluminium alloy cast ingot that the present embodiment obtains, and as shown in Figure 5, Fig. 5 is the low power detection figure of the AHS aluminium alloy cast ingot that the embodiment of the present invention 2 obtains.
The present invention has carried out high power detection according to technique scheme to the AHS aluminium alloy cast ingot that the present embodiment obtains, as shown in Figure 6, Fig. 6 is the AHS aluminium alloy cast ingot that obtains of the embodiment of the present invention 2 500 × under high power detect figure.
The present invention has carried out low power detection according to technique scheme to the aluminium alloy extruded rod of AHS that the present embodiment obtains, and as shown in Figure 7, Fig. 7 is the low power detection figure of the aluminium alloy extruded rod of AHS that the embodiment of the present invention 2 obtains.
The present invention has carried out high power detection according to technique scheme to the aluminium alloy extruded rod of AHS that the present embodiment obtains, as shown in Figure 8, Fig. 8 is the aluminium alloy extruded rod of AHS that the embodiment of the present invention 2 obtains 500 × under high power detect figure.
Embodiment 3
By the Al-Si master alloy prepared, pure Cu plate and pure Al ingot add smelting furnace, carry out melting, answer prepurging or prepurging before shove charge.When filling with substance Al-Si master alloy is added in lower floor in furnace charge, and Cu plate is placed at the middle and upper levels.Smelting temperature is 740 ± 10 DEG C.
Furnace charge major partization at ordinary times, be bulldozed at the convex peak exposing liquid level, and in good time rake is stirred metal with rake as far as possible, to accelerate fusing.Treat that furnace charge melts completely, when melt temperature rises to 730-740 DEG C, thoroughly stir more than 10min, if scum silica frost is many before stirring, ground flux can be sprinkled in stove.Dross on surface of fusant is scratched clean after stirring.Melt temperature 720 ± 5 DEG C adds the Mg ingot prepared.Mg ingot will be pressed into melt, forbids to expose liquid level.Must carry out twice stirring after Mg ingot melts completely, twice mixing chamber interval is no less than 15min.Get stokehold sample after uniform composition, quantity is a mushroom sample and a cake sample, and probe temperature is 730 ± 10 DEG C.
Add Al-Sr, Al-3B master alloy after stokehold composition is qualified and carry out fine degenerate process, must through thermal pretreatment before Al-Sr, Al-3B master alloy adds.
Al-Sr add-on: 4.5kg/t pressed by virgin material, body waste material presses 2kg/t.Al-3B add-on: add by 0.035%B.Add temperature: 720 ± 5 DEG C.
Al-Sr (bar), Al-3B master alloy will be pressed into melt, forbid to swim on liquid level.After Al-Sr, Al-3B master alloy melts completely, Melt Stirring is even.
Any flux and insulating covering agent is prohibitted the use after adding Sr.
Carry out the refining of Ar gas to melt when 750 DEG C, two refining pipe double door refining simultaneously 20min, scratch clean dross on surface of fusant after refining.Leave standstill after skimming, carry out casting preparation work simultaneously, and cast as early as possible.
The speed of casting is 98mm/min, and hydraulic pressure is 0.0.06MPa, and casting temp is 720 ± 10 DEG C, obtains the AHS aluminium alloy cast rod that specification is Φ 250mm.
Extrude after having cast, be AHS alloy casting rod railway carriage, the sawing of Φ 250mm by specification be after Φ 240 × 760mm, extrude by large common process of producing, container temperature is 420 DEG C, extrusion temperature is 440 DEG C, extrusion speed≤2mm/min, extrusion ratio is 25, and extruded bars specification is Φ 34mm.
The present invention have detected the grain fineness number of the AHS aluminium alloy cast ingot that the present embodiment obtains according to technique scheme, and result is as shown in table 1, and table 1 is the detected result of the AHS aluminium alloy cast ingot that the embodiment of the present invention 1 ~ 3 obtains.
The present invention have detected the mechanical property of the aluminium alloy extruded rod of AHS that the present embodiment obtains according to technique scheme, and result is as shown in table 2, and table 2 is the mechanical performance data of the aluminium alloy extruded version of AHS that the embodiment of the present invention 1 ~ 3 obtains.
The present invention has carried out low power detection according to technique scheme to the AHS aluminium alloy cast ingot that the present embodiment obtains, and as shown in Figure 9, Fig. 9 is the low power detection figure of the AHS aluminium alloy cast ingot that the embodiment of the present invention 3 obtains.
The present invention has carried out high power detection according to technique scheme to the AHS aluminium alloy cast ingot that the present embodiment obtains, as shown in Figure 10, Figure 10 is the AHS aluminium alloy cast ingot that obtains of the embodiment of the present invention 3 500 × under high power detect figure.
The present invention has carried out low power detection according to technique scheme to the aluminium alloy extruded rod of AHS that the present embodiment obtains, and as shown in figure 11, Figure 11 is the low power detection figure of the aluminium alloy extruded rod of AHS that the embodiment of the present invention 3 obtains.
The present invention has carried out high power detection according to technique scheme to the aluminium alloy extruded rod of AHS that the present embodiment obtains, as shown in figure 12, Figure 12 is the aluminium alloy extruded rod of AHS that the embodiment of the present invention 3 obtains 500 × under high power detect figure.
As can be seen from Fig. 1, Fig. 5 and Fig. 9, AHS aluminium alloy cast ingot 1 provided by the invention) eliminate featheriness crystal grain defect; 2) primary silicon defect is eliminated; 3) the obvious refinement of crystal grain (crystal grain 1-3 level, 8 grades of degree of refining standards).
The casting technique thinning effect can found out in the present invention by Fig. 2, Fig. 6 and Figure 10 is better, and alloy Eutectic Silicon in Al-Si Cast Alloys is organized as tiny staple fibre shape, and modification effect is better.
As can be seen from Fig. 3, Fig. 7 and Figure 11, AHS provided by the invention leads total extruded rod, and it organizes fine and closely woven, and maximum grain fineness number is 2 grades (8 grades of grain fineness number standards), is conducive to the performance ensureing or improve alloy bar material.
As can be seen from Fig. 4, Fig. 8 and Figure 12, the aluminium alloy extruded rod of AHS provided by the invention is organized fine and closely woven, even, and modifying-refining effect is better.
The detected result of the AHS aluminium alloy cast ingot that table 1 embodiment of the present invention 1 ~ 3 obtains
The mechanical performance data of the aluminium alloy extruded version of the AHS that table 2 embodiment of the present invention 1 ~ 3 obtains
As can be seen from table 1 and table 2, the AHS aluminium alloy that the present invention obtains has less grain fineness number, and has good mechanical property after extrusion.
The above is only the preferred embodiment of the present invention; it should be pointed out that for those skilled in the art, under the premise without departing from the principles of the invention; can also make some improvements and modifications, these improvements and modifications also should be considered as protection scope of the present invention.
Claims (10)
1. an AHS aluminium alloy, comprises the component of following massfraction:
The Si of 10.0 ~ 11.5%; The Cu of 2.0 ~ 3.0%; The Mg of 0.35 ~ 0.45%; The Fe of 0 ~ 0.5%; The Zn of 0 ~ 0.3%; The Mn of 0 ~ 0.1%; The Ni of 0 ~ 0.01%; The Sr of 0.02 ~ 0.05%; The B of 0.01 ~ 0.04%; Surplus is Al.
2. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Si is 10.5 ~ 11.0%.
3. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Cu is 2.2 ~ 2.8%.
4. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Mg is 0.38 ~ 0.42%.
5. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Si is 10.6 ~ 10.9%.
6. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Cu is 2.6 ~ 2.7%.
7. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Mg is 0.3 ~ 0.4%.
8. AHS aluminium alloy according to claim 1, is characterized in that, the massfraction of described Fe is 0 ~ 0.3%; The massfraction of described Zn is 0 ~ 0.1%; The massfraction of described Mn is 0 ~ 0.05%; The massfraction of described Ni is 0 ~ 0.005%; The massfraction of described Sr is 0.02 ~ 0.05%.
9. the AHS aluminium alloy according to claim 1 ~ 8 any one, is characterized in that, the grain fineness number of described AHS aluminium alloy is 1 ~ 3 grade.
10. the aluminium alloy extruded rod of AHS, obtained through extruding by AHS aluminium alloy cast ingot, described AHS aluminium alloy cast ingot is the AHS aluminium alloy described in claim 1 ~ 9 any one.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104878256A (en) * | 2015-05-20 | 2015-09-02 | 柳州市百田机械有限公司 | High-compactness die-cast aluminum alloy |
| CN104894441A (en) * | 2015-05-29 | 2015-09-09 | 柳州普亚贸易有限公司 | Corrosion-resistant aluminum alloy for building template |
| CN106191569A (en) * | 2016-08-17 | 2016-12-07 | 江苏亚太安信达铝业有限公司 | A kind of wear-resisting silumin for piston of automobile and preparation method thereof |
| CN109112445A (en) * | 2017-06-22 | 2019-01-01 | 宜兴市零零七机械科技有限公司 | A kind of pulley material of high-performance sealed door |
| CN110527872A (en) * | 2019-09-03 | 2019-12-03 | 苏州大学 | A kind of hypoeutectic al-si alloy and preparation method thereof |
| CN111636017A (en) * | 2020-05-29 | 2020-09-08 | 深圳市鑫申新材料科技有限公司 | Semisolid forming aluminum alloy and preparation method thereof |
| CN111893354A (en) * | 2020-08-14 | 2020-11-06 | 江西寰球新材料科技有限公司 | Al-Si-Cu-Mg wrought aluminum alloy and preparation method thereof |
| CN115094279A (en) * | 2022-07-05 | 2022-09-23 | 西南铝业（集团）有限责任公司 | Production process of high-silicon aluminum alloy pipe |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103981386A (en) * | 2014-04-30 | 2014-08-13 | 苏州有色金属研究院有限公司 | Method for modification and refinement of hypoeutectic and eutectic Al-Si alloy |
-
2014
- 2014-12-12 CN CN201410768820.5A patent/CN104532078A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103981386A (en) * | 2014-04-30 | 2014-08-13 | 苏州有色金属研究院有限公司 | Method for modification and refinement of hypoeutectic and eutectic Al-Si alloy |
Non-Patent Citations (2)
| Title |
|---|
| RAFAEL NUNES ET AL.: "《ASM HANDBOOK VOLUME 2》", 31 December 1992 * |
| 刘丹超等: "AHS合金配料工艺研究", 《铝加工》 * |
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| CN104878256A (en) * | 2015-05-20 | 2015-09-02 | 柳州市百田机械有限公司 | High-compactness die-cast aluminum alloy |
| CN104894441A (en) * | 2015-05-29 | 2015-09-09 | 柳州普亚贸易有限公司 | Corrosion-resistant aluminum alloy for building template |
| CN106191569A (en) * | 2016-08-17 | 2016-12-07 | 江苏亚太安信达铝业有限公司 | A kind of wear-resisting silumin for piston of automobile and preparation method thereof |
| CN106191569B (en) * | 2016-08-17 | 2018-02-09 | 江苏亚太安信达铝业有限公司 | A kind of wear-resisting silumin for piston of automobile and preparation method thereof |
| CN109112445A (en) * | 2017-06-22 | 2019-01-01 | 宜兴市零零七机械科技有限公司 | A kind of pulley material of high-performance sealed door |
| CN110527872A (en) * | 2019-09-03 | 2019-12-03 | 苏州大学 | A kind of hypoeutectic al-si alloy and preparation method thereof |
| CN111636017A (en) * | 2020-05-29 | 2020-09-08 | 深圳市鑫申新材料科技有限公司 | Semisolid forming aluminum alloy and preparation method thereof |
| CN111893354A (en) * | 2020-08-14 | 2020-11-06 | 江西寰球新材料科技有限公司 | Al-Si-Cu-Mg wrought aluminum alloy and preparation method thereof |
| CN115094279A (en) * | 2022-07-05 | 2022-09-23 | 西南铝业（集团）有限责任公司 | Production process of high-silicon aluminum alloy pipe |
| CN115094279B (en) * | 2022-07-05 | 2023-12-01 | 西南铝业（集团）有限责任公司 | Production process of high-silicon aluminum alloy pipe |
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