CN102676889B - High-performance eutectic aluminum silicon alloy piston material of vehicle engine - Google Patents
High-performance eutectic aluminum silicon alloy piston material of vehicle engine Download PDFInfo
- Publication number
- CN102676889B CN102676889B CN201210154297.8A CN201210154297A CN102676889B CN 102676889 B CN102676889 B CN 102676889B CN 201210154297 A CN201210154297 A CN 201210154297A CN 102676889 B CN102676889 B CN 102676889B
- Authority
- CN
- China
- Prior art keywords
- remelting
- alloy
- aluminium
- temperature
- melt
- 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
Links
Images
Landscapes
- Pistons, Piston Rings, And Cylinders (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention provides a high-performance eutectic aluminum silicon alloy piston material of a vehicle engine. On the basis of ZL109 alloy, the novel eutectic alloy material with high strength and low thermal expansion coefficient can be prepared by adjusting the alloy composition and adding trace elements such as V, Zr and P. The eutectic aluminum silicon alloy has the characteristics of being excellent in high-temperature property, high in hardness, low in thermal expansion coefficient, good in wear resistance and the like, thus being better in accordance with the requirements of the high-performance vehicle engine.
Description
Technical field
The invention belongs to nonferrous materials technology of preparing and rotten treatment process field, be specifically related to a kind of high-performance vehicular engine cocrystallized Al-Si alloy piston material.
Background technology
Piston is the heart of engine, bears mechanical load and the thermal load of alternation, is one of worst key components and parts of working conditions in engine.Work under the situation of High Temperature High Pressure high speed, determining the working efficiency of engine, therefore require piston alloy to there is volume stability and higher hot strength preferably.Improving constantly of motor performance makes the working load of piston significantly increase, thereby piston performance especially high-temperature behavior is had higher requirement, and piston material stands in the breach.
The conventional alloys trades mark such as ZL109 that current domestic industry still generally adopts can not adapt to more high loading newly developed and the especially requirement of high-performance piston of automotive engine of performance piston, occur the situation of broken end or burner port cracking on the type often had especially in recent years.
The present invention is on the basis of ZL 109 alloy, by adjusting alloying constituent, add trace element, strictly controlling modification process, prepares a kind of high strength, and the novel eutectic alloy material of low thermal coefficient of expansion, meet the requirement of high-performance piston of automotive engine.
Summary of the invention
The problem to be solved in the present invention is to provide material of a kind of cocrystallized Al-Si alloy piston and preparation method thereof, especially is suitable in the piston of vehicular engine.
For solving the problems of the technologies described above, the technical solution used in the present invention is:
A kind of cocrystallized Al-Si alloy piston material, by percentage to the quality, contain Si:11～13%, Cu:3.8～4.5%, Ni:2.5～4.5%, Mg:0.5～1.0%, V:0.05～0.08%, Zr:0.05～0.08%, P:0.006～0.014%, surplus is Al and inevitable impurity.
Preferably, described cocrystallized Al-Si alloy piston material, by percentage to the quality, contain: Si:12.2～12.6%, Cu:3.8～4.5%, Ni:2.7～3.0%, Mg:0.6～0.9%, V:0.05～0.07%, Zr:0.05～0.07%, P:0.006～0.014%, surplus is Al and inevitable impurity.
Further, described cocrystallized Al-Si alloy piston material, can also contain following alloying element by mass percentage, Zn≤0.5%, Mn≤0.15%, Ti≤0.05%, Sn≤0.02%, Fe≤0.5%.
The present invention also provides a kind of preparation method of described aluminium alloy, comprises the steps:
(1), by the shared mass percent Si:11 of aluminum silicon alloy interalloy element～13%, Cu:3.8～4.5%, Ni:2.5～4.5%, Mg:0.5～1.0%, V:0.05～0.08%, Zr:0.05～0.08%, P:0.006～0.014%, surplus is Al and inevitable impurity; Take respectively aluminium ingot for remelting, magnesium ingot, industrial silicon, electrolytic copper, pure nickel plate, AlV5 (aluminium vanadium master alloy), AlZr10 (aluminium zirconium hardener) and AlP3 (aluminium phosphorus master alloy) for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by 0.1～0.2% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, for remelting, the dry 2～3h of constant temperature preheating and drying stove of temperature 200-300 ℃ is put in magnesium ingot, pure nickel plate, AlV5, AlZr10, AlP3, remelting with aluminium ingot with without the sodium refining agent;
(4) dried industrial silicon, pure nickel plate, remelting in step (3) are put into to industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃;
(5) igniting 3h～4h, treat that aluminium ingot, industrial silicon and pure nickel plate for remelting in stove all melt, aluminium liquid 5～8min in rabbling roaster, then add the dried electrolytic copper of step (3), AlV5 and AlZr10 in industrial furnace, continue firing up, and set 800 ℃ of insulation 30min of melt temperature in stove.
(6) treat that in stove, all materials all melt, adjust temperature to 740～780 ℃, will be pressed into aluminium alloy melt inside 3～5min with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 4～5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 30～50min, fully stir, sampling detects alloying constituent.
(9) measure the aluminium alloy melt temperature, be sprinkled in aluminium alloy melt and fully stir without 50% of sodium refining agent step (3) is dried in 800～815 ℃ of scopes of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time sprayed into is controlled at 10～15min, carry out slag hitting, the standing 5～10min of aluminium liquid after slag hitting;
(10) come out of the stove when 800～815 ℃ of molten aluminium alloy temperature, obtain described cocrystallized Al-Si alloy piston material.
Preferably, described method comprises the steps:
(1) by the shared mass percent Si:12.5% of aluminum silicon alloy interalloy element, Cu:4.4%, Mg:0.8%, Ni:3.0%, Zr:0.065%, V:0.065%, P:0.010%, Al is surplus, takes respectively described industrial silicon, electrolytic copper, magnesium ingot, pure nickel plate, AlV5, AlZr10, aluminium ingot and AlP3 master alloy for remelting for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by step (1) 0.15% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, pure nickel plate, AlV5, AlZr10, AlP3, remelting with aluminium ingot with put into the dry 3h of constant temperature preheating and drying stove of temperature 250C without the sodium refining agent;
(4) dried industrial silicon, pure nickel plate, remelting in step (3) are put into to industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃;
(5) igniting 4h, treat that aluminium ingot, industrial silicon and pure nickel plate for remelting in stove all melt, aluminium liquid 8min in rabbling roaster, then add the dried electrolytic copper of step (3), AlV5 and AlZr10 in industrial furnace, continue firing up, and set 800 ℃ of insulation 30min of melt temperature in stove.
(6) treat that in stove, all materials all melt, adjust temperature to 760～780 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 40min, fully stir, sampling detects alloying constituent.
(9) measure the aluminium alloy melt temperature, be sprinkled in aluminium alloy melt and fully stir without 50% of sodium refining agent step (3) is dried when 810 ℃ of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time sprayed into is controlled at 10min, carry out slag hitting, the standing 5min of aluminium liquid after slag hitting;
(10) come out of the stove when 810 ℃ of molten aluminium alloy temperature, obtain described cocrystallized Al-Si alloy piston material.
Pure nickel plate in the present invention can be used AlNi20 (aluminium nickel master alloy) to substitute and realize, if that add is AlNi20, through after the taking of step (1), then in step (3), carry out drying, then in step (5) along with electrolytic copper adds together.
Realize that when substitute the pure nickel plate with AlNi20 when of the present invention, preferred, described method comprises the steps:
(1) by the shared mass percent Si:13% of aluminum silicon alloy interalloy element, Cu:4.0%, Mg:1.0%, Ni:4.0%, Zr:0.07%, V:0.07%, P:0.014%, Al is surplus, takes respectively described industrial silicon, electrolytic copper, magnesium ingot, AlNi20, AlV5, AlZr10, aluminium ingot, AlP3 master alloy for remelting for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by step (1) 0.16% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, AlV5, AlZr10, AlNi20, AlP3, remelting with aluminium ingot with put into the dry 2h of constant temperature preheating and drying stove of 250 ℃ of temperature without the sodium refining agent;
(4) dried industrial silicon, remelting in step (3) are put into to industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃;
(5) igniting 4h, treat that the remelting in stove all melts with aluminium ingot and industrial silicon, aluminium liquid 8min in rabbling roaster, then add the dried electrolytic copper of step (3), AlNi20, AlV5 and AlZr10 in industrial furnace, continue firing up, and set 800 ℃ of insulation 30min of melt temperature in stove.
(6) treat that in stove, all materials all melt, adjust temperature to 750 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 45min, fully stir, sampling detects alloying constituent.
(9) measure the aluminium alloy melt temperature, be sprinkled in aluminium alloy melt and fully stir without 50% of sodium refining agent step (3) is dried when 810 ℃ of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time sprayed into is controlled at 12min, carry out slag hitting, the standing 5min of aluminium liquid after slag hitting;
(10) come out of the stove when 805 ℃ of molten aluminium alloy temperature, obtain described cocrystallized Al-Si alloy piston material.
Preferably, above-mentioned rare gas element is argon gas.
The present invention is a kind of cocrystallized Al-Si alloy material that adds multiple strengthening element, and gordian technique is the control of modification process and the interpolation of alloying element.Alloy material adopts Al-P master alloy alterant, and deterroration is 800 ℃, and deteriorating time is 30～50min.The contriver also finds through great many of experiments, material property the best when the aluminium alloy teeming temperature is controlled at 800～815 ℃, being much better than Fig. 3, Fig. 4 from the alloy modification effect of Fig. 1, Fig. 2 can find out, when the aluminium alloy teeming temperature during lower than this temperature, primary silicon easily assemble and modification effect not good.Al, Si, Cu, Mg, Ni, V, Zr have generated multiple heat-resisting phase, play strengthening effect and refining effect, greatly improve material tensile strength at high temperature.
Advantage of the present invention and beneficial effect are:
The characteristics such as it is good that the alloy material that 1, prepared by present method has high-temperature behavior, and hardness is high, thermal expansivity is little, wear resistance is good, meet the requirement of high-performance piston of automotive engine, for the breakthrough of aluminium alloy industry on the novel material performance accumulated experience.Appropriate Ni can increase substantially the hot strength of existing high-performance piston alloy; Al, Si, Mg, Cu, Ni etc. form compound strengthening phase and high-temperature stable phase in alloy, play the effect of multiple strengthening piston alloy; But Zr and V refinement recrystallized structure, after adding the rotten processing of P, form Al-P black core, promoted the heterogeneous forming core of primary silicon, plays the effect of refinement primary silicon, and average grain size is about 12 μ m.Also can find out that from table 2 novel eutectic Al-base alloy piston material intensity of the present invention is about 350Mpa, 300 ℃ of Testing Tensile Strength at Elevated Temperatures are about 205Mpa.
Further, in alloy of the present invention, can also add Mn, it can be used as the high-temperature behavior that alloy element improves piston alloy more by a small margin.
2, the best phosphorus content of alloy of the present invention, deterroration, rotten process with refining treatment coordinate and the scope of teeming temperature in, can access a kind of good phosphorus modification technique, thereby prepare the cocrystallized Al-Si alloy of excellent property of the present invention.
The accompanying drawing explanation
The rotten tissue that Fig. 1 teeming temperature is 800 ℃ of alloys.
The rotten tissue that Fig. 2 teeming temperature is 815 ℃ of alloys.
The rotten tissue that Fig. 3 teeming temperature is 780 ℃ of alloys.
The rotten tissue that Fig. 4 teeming temperature is 730 ℃ of alloys.
The frictional wear experiment result contrast of Fig. 5 alloy of the present invention and existing ZL109.
Embodiment
Below by specific embodiment, the invention will be further described, and following examples are descriptive, is not determinate, can not limit protection scope of the present invention with this.
Embodiment 1:
(1) Si:12.3% by mass percentage, Cu:4.2%, Mg:0.8%, Ni:2.8%, Zr:0.060%, V:0.060%, P:0.010%, Al is surplus, takes aluminium ingot for remelting, magnesium ingot, industrial silicon, electrolytic copper, pure nickel plate and AlV5 (aluminium vanadium master alloy), AlZr10 ((aluminium zirconium hardener), AlP3 (aluminium phosphorus master alloy) for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by 0.15% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, pure nickel plate, AlV5, AlZr10, ALP3, remelting with aluminium ingot with put into the dry 3h of constant temperature preheating and drying stove of 250 ℃ of temperature without the sodium refining agent;
(4) dried industrial silicon, pure nickel plate, remelting in step (3) are put into to CX-GR-150 type industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃.
(5) igniting 4h, treat that aluminium ingot, industrial silicon and pure nickel plate for remelting in stove all melt, aluminium alloy melt 8min in rabbling roaster then carefully adds electrolytic copper, AlV5 and the AlZr10 in step (3) in industrial furnace energetically, continues firing up to 850 ℃.
(6) treat that in stove, all materials all melt, adjust temperature to 765 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 45min, fully stir, sampling detects alloying constituent;
(9) measure the aluminium alloy melt temperature, 815 ℃ of without 50% of sodium refining agent, being sprinkled in aluminium alloy melt and fully stirring complete drying in step (3) of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element argon gas of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time that argon gas sprays into is 10min, carry out slag hitting, standing 5min after slag hitting;
(10) when 815 ℃ of molten aluminium alloy temperature, come out of the stove.
(11) the alloy material carries out T6 thermal treatment.
By check, aluminum alloy heat treated state tensile strength prepared by this experimental technique is 333Mpa, 300 ℃ of Testing Tensile Strength at Elevated Temperature 198Mpa, 350 ℃ of Testing Tensile Strength at Elevated Temperature 157Mpa, thermal expansivity 15.8 * 10
-6/ ℃.
Described is the conventional refining agent prepared for aluminium alloy in the industry without the sodium refining agent, the HGJB-2 refining agent that as above marine rainbow light metal flux factory produces for example.
Embodiment 2
(1) by the shared mass percent Si:12.5% of aluminum silicon alloy interalloy element, Cu:4.4%, Mg:0.8%, Ni:3.0%, Zr:0.065%, V:0.065%, P:0.010%, Al is surplus, takes respectively described industrial silicon, electrolytic copper, magnesium ingot, pure nickel plate, AlV5, AlZr10, aluminium ingot and AlP3 master alloy for remelting for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by step (1) 0.15% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, pure nickel plate, AlV5, AlZr10, AlP3, remelting with aluminium ingot with put into the dry 3h of constant temperature preheating and drying stove of 250 ℃ of temperature without the sodium refining agent;
(4) dried industrial silicon, pure nickel plate, remelting in step (3) are put into to industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃;
(5) igniting 4h, treat that aluminium ingot, industrial silicon and pure nickel plate for remelting in stove all melt, aluminium liquid 8min in rabbling roaster, then add the dried electrolytic copper of step (3), AlV5 and AlZr10 in industrial furnace, continue firing up, and set 800 ℃ of insulation 30min of melt temperature in stove.
(6) treat that in stove, all materials all melt, adjust temperature to 760～780 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 40min, fully stir, sampling detects alloying constituent.
(9) measure the aluminium alloy melt temperature, be sprinkled in aluminium alloy melt and fully stir without 50% of sodium refining agent step (3) is dried when 810 ℃ of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time sprayed into is controlled at 10min, carry out slag hitting, the standing 5min of aluminium liquid after slag hitting;
(10) when 810 ℃ of molten aluminium alloy temperature, come out of the stove.
(11) the alloy material carries out T6 thermal treatment.
By check, aluminum alloy heat treated state tensile strength prepared by this experimental technique is more 330Mpa, and 300 ℃ of Testing Tensile Strength at Elevated Temperatures are about 200Mpa, and 350 ℃ of Testing Tensile Strength at Elevated Temperatures are about 161Mpa, and thermal expansivity is about 16.0 * 10
-6/ ℃.
(1) Si:12.5% by mass percentage, Cu:4.0%, Mg:0.9%, Ni:3.0%, Zr:0.07%, V:0.07%, P:0.014%, Al is surplus, takes aluminium ingot for remelting, magnesium ingot, industrial silicon, electrolytic copper, AlNi20 (aluminium nickel master alloy), AlV5 (aluminium vanadium master alloy), AlZr10 ((aluminium zirconium hardener), AlP3 (aluminium phosphorus master alloy) for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by 0.16% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, AlNi20, AlV5, AlZr10, AlP3, remelting with aluminium ingot with put into the dry 2h of constant temperature preheating and drying stove of 250 ℃ of temperature without the sodium refining agent;
(4) dried industrial silicon, remelting in step (3) are put into to CX-GR-150 type industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃.
(5) igniting 4h, treat that the remelting in stove all melts with aluminium ingot and industrial silicon, aluminium alloy melt 5min in rabbling roaster energetically, then carefully add electrolytic copper, AlNi20, AlV5 and the AlZr10 in step (3) in industrial furnace, continue firing up, and set 800 ℃ of insulation 30min of melt temperature in stove.
(6) treat that in stove, all materials all melt, adjust temperature to 760 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 50min, fully stir, sampling detects alloying constituent;
(9) measure the aluminium alloy melt temperature, 813 ℃ of without 50% of sodium refining agent, being sprinkled in aluminium alloy melt and fully stirring complete drying in step (3) of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element argon gas of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time that argon gas sprays into is 11min, then carry out slag hitting, the standing 8min of aluminium liquid after slag hitting;
(10) when 810 ℃ of molten aluminium alloy temperature, come out of the stove.
(11) the alloy material carries out T6 thermal treatment.
By check, aluminum alloy heat treated state tensile strength prepared by this experimental technique is 342Mpa, 300 ℃ of Testing Tensile Strength at Elevated Temperature 201Mpa, 350 ℃ of Testing Tensile Strength at Elevated Temperature 159Mpa, thermal expansivity 16.3 * 10-6/ ℃.
Embodiment 4
(1) by the shared mass percent Si:13% of aluminum silicon alloy interalloy element, Cu:4.0%, Mg:1.0%, Ni:4.0%, Zr:0.07%, V:0.07%, P:0.014%, Al is surplus, takes respectively described industrial silicon, electrolytic copper, magnesium ingot, AlNi20, AlV5, AlZr10, aluminium ingot, AlP3 master alloy for remelting for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by step (1) 0.16% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, AlV5, AlZr10, AlNi20, AlP3, remelting with aluminium ingot with put into the dry 2h of constant temperature preheating and drying stove of 250 ℃ of temperature without the sodium refining agent;
(4) dried industrial silicon and remelting in step (3) are put into to industrial furnace with aluminium ingot, setting the industrial furnace furnace body temperature is 850 ℃;
(5) igniting 4h, treat that the remelting in stove all melts with aluminium ingot and industrial silicon, aluminium liquid 8min in rabbling roaster, then add the dried electrolytic copper of step (3), AlV5, AlNi20 and AlZr10 in industrial furnace, continue firing up, and set 800 ℃ of insulation 30min of melt temperature in stove.
(6) treat that in stove, all materials all melt, adjust temperature to 750 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 45min, fully stir, sampling detects alloying constituent.
(9) measure the aluminium alloy melt temperature, be sprinkled in aluminium alloy melt and fully stir without 50% of sodium refining agent step (3) is dried when 810 ℃ of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time sprayed into is controlled at 12min, carry out slag hitting, the standing 5min of aluminium liquid after slag hitting;
(10) when 805 ℃ of molten aluminium alloy temperature, come out of the stove.。
(11) the alloy material carries out T6 thermal treatment.
By check, aluminum alloy heat treated state tensile strength prepared by this experimental technique is 345Mpa, 300 ℃ of Testing Tensile Strength at Elevated Temperature 203Mpa, 350 ℃ of Testing Tensile Strength at Elevated Temperature 160Mpa, thermal expansivity 17 * 10
-6/ ℃.
Below with alloy material of the present invention and existing ZL 109 alloy, contrasted, the frictional wear experiment result contrasts as shown in Figure 5.As can be seen from Figure 5, the frictional coefficient of alloy of the present invention is far below ZL 109 alloy, and wear resisting property is better, more meets the requirement of high-performance piston of automotive engine.
In addition, the present invention also provides mechanics performance comparison (referring to table 1 and table 2) under the contrast of alloy material of the present invention and existing ZL 109 alloy elemental composition, two kinds of Aluminum Alloy Room Temperature and high temperature.As can be seen from Table 2, after its as cast condition tensile strength of alloy of the present invention, thermal treatment, room temperature tensile strength, 300 ℃ of Testing Tensile Strength at Elevated Temperatures, 350 ℃ of Testing Tensile Strength at Elevated Temperatures obviously are better than ZL 109 alloy, thermal expansivity is starkly lower than ZL 109 alloy, illustrate that alloy of the present invention is a kind of high strength, the novel eutectic alloy material of low thermal coefficient of expansion, compare ZL 109 alloy, more meet the requirement of high-performance piston of automotive engine.
Table 1
Table 2
Above embodiments of the invention are had been described in detail, but described content is only preferred embodiment of the present invention, can not be considered to for limiting practical range of the present invention.All equalization variations of doing according to the present patent application scope and improvement etc., within all should still belonging to patent covering scope of the present invention.
Claims (1)
1. the preparation method of a cocrystallized Al-Si alloy piston material, comprise the steps:
(1) by the shared mass percent Si:12.5% of aluminum silicon alloy interalloy element, Cu:4.4%, Mg:0.8%, Ni:3.0%, Zr:0.065%, V:0.065%, P:0.010%, Al is surplus, takes respectively industrial silicon, electrolytic copper, magnesium ingot, pure nickel plate, AlV5, AlZr10, aluminium ingot and AlP3 master alloy for remelting for remelting; Wherein industrial silicon is broken 1 good～5cm
3fritter;
(2) by step (1) 0.15% of the quality that always feeds intake, take without the sodium refining agent;
(3) by the industrial silicon in step (1), step (2), electrolytic copper, magnesium ingot for remelting, pure nickel plate, AlV5, AlZr10, AlP3, remelting with aluminium ingot with put into the dry 3h of constant temperature preheating and drying stove of 250 ℃ of temperature without the sodium refining agent;
(4) dried industrial silicon, pure nickel plate, remelting in step (3) are put into to industrial furnace with aluminium ingot, setting the industrial furnace furnace temperature is 850 ℃;
(5) igniting 4h, treat that aluminium ingot, industrial silicon and pure nickel plate for remelting in stove all melt, aluminium liquid melt 8min in rabbling roaster, then add the dried electrolytic copper of step (3), AlV5 and AlZr10 in industrial furnace, continue firing up, and in the setting stove, melt temperature is 800 ℃ of insulation 30min;
(6) treat that in stove, all materials all melt, adjust temperature to 760～780 ℃, will be pressed into the inner 5min of aluminium alloy melt with magnesium ingot through the remelting of step (3) drying treatment with bell jar and all melt with magnesium ingot to remelting, stir rapidly 5min;
(7) the aluminium alloy melt temperature is adjusted to 830 ℃, add the processing of going bad of AlP3 master alloy;
(8) after rotten 40min, fully stir, sampling detects alloying constituent;
(9) measure the aluminium alloy melt temperature, 810 ℃ of without 50% of sodium refining agent, being sprinkled in aluminium alloy melt and fully stirring complete drying in step (3) of aluminium alloy melt temperature, put into automatic powder blower by remaining 50% without the sodium refining agent, the rare gas element of take will spray into uniformly in aluminium alloy melt and carry out refining without the sodium refining agent as carrier, the time that rare gas element sprays into is controlled at 10min, carry out slag hitting, standing 5min after slag hitting;
(10) come out of the stove when 810 ℃ of molten aluminium alloy temperature, obtain described cocrystallized Al-Si alloy piston material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210154297.8A CN102676889B (en) | 2012-05-17 | 2012-05-17 | High-performance eutectic aluminum silicon alloy piston material of vehicle engine |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201210154297.8A CN102676889B (en) | 2012-05-17 | 2012-05-17 | High-performance eutectic aluminum silicon alloy piston material of vehicle engine |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102676889A CN102676889A (en) | 2012-09-19 |
| CN102676889B true CN102676889B (en) | 2014-01-08 |
Family
ID=46809432
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201210154297.8A Active CN102676889B (en) | 2012-05-17 | 2012-05-17 | High-performance eutectic aluminum silicon alloy piston material of vehicle engine |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102676889B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103469021B (en) * | 2013-08-12 | 2016-02-10 | 安徽盛达前亮铝业有限公司 | A kind of Engine piston aluminum alloy and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102177266A (en) * | 2008-09-05 | 2011-09-07 | Ks科尔本施密特有限公司 | Method for manufacturing a piston of an internal combustion engine, comprising an improved aluminum silicon alloy |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2878534B1 (en) * | 2004-11-26 | 2007-10-19 | Ks Kolbenschmidt Gmbh | ALUMINUM ALLOY FOR HIGH HARD MECHANICAL RESISTANCE PIECE |
-
2012
- 2012-05-17 CN CN201210154297.8A patent/CN102676889B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102177266A (en) * | 2008-09-05 | 2011-09-07 | Ks科尔本施密特有限公司 | Method for manufacturing a piston of an internal combustion engine, comprising an improved aluminum silicon alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102676889A (en) | 2012-09-19 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102660701A (en) | Preparation method of cocrystallized Al-Si alloy piston material | |
| CN101560620B (en) | High strength heat-resisting hypereutectic aluminium-silicon alloy and preparation method thereof | |
| CN103602865B (en) | Copper-containing heat-resistant magnesium-tin alloy and preparation method thereof | |
| CN104561688A (en) | Heat-resistant cast aluminum alloy and gravity casting method thereof | |
| CN102560206B (en) | Rare-earth aluminum alloy piston material and preparation method thereof | |
| CN104561689A (en) | Heat-resistant cast aluminum alloy and extrusion casting method thereof | |
| CN104630577A (en) | Heat-resistant cast aluminum alloy and pressure casting method thereof | |
| CN105441705B (en) | A kind of preparation method of high-strength and high-ductility aluminium alloy | |
| CN103540812A (en) | Aluminum alloy material for engine cylinder cover and preparation method thereof | |
| CN114015914A (en) | High-strength high-thermal-conductivity die-casting aluminum alloy material and preparation method thereof | |
| CN102304651A (en) | Casting aluminum-silicon alloy and strengthening method thereof | |
| CN102162054B (en) | High-toughness magnesium alloy and preparation method thereof | |
| CN102644012B (en) | Preparation method of cocrystallized Al-Si alloy piston material | |
| CN102676889B (en) | High-performance eutectic aluminum silicon alloy piston material of vehicle engine | |
| CN103540878B (en) | A kind of CeO2The processing method of the Al-Si-Zn line aluminium alloy strengthened | |
| CN102660702A (en) | Eutectic aluminum-silicon alloy piston material | |
| CN109266886B (en) | Method for refining intermetallic compound phase of manganese-iron-containing aluminum alloy | |
| CN100410407C (en) | Mg-Al-Si-Mn-Ca alloy and method for preparing same | |
| CN103305737B (en) | Grain refinement type cast magnesium alloy and preparation method thereof | |
| CN102676888A (en) | Eutectic aluminum silicon alloy piston material of vehicle engine | |
| CN108220731A (en) | A kind of multicomponent heat-resistant magnesium alloy and preparation method thereof | |
| CN110951983B (en) | Method for refining 2618 aluminum alloy as-cast grain structure | |
| CN1168840C (en) | Multicomponent heat-resistant magnesium alloy for car and its founding process | |
| CN102660703A (en) | Method for preparing high-performance eutectic aluminum-silicon alloy piston material for vehicle engine | |
| CN112626379A (en) | High-strength light aluminum-boron alloy plate material and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20200526 Address after: 300457 No. 58 Tai Thai Road, West Development Zone, Tianjin Binhai New Area Development Zone Patentee after: Tianjin xinlizhong alloy Group Co., Ltd Address before: 300457 economic and technological development of Binhai New Area, Tianjin, No. 58 Tai Chi Road, West End Patentee before: Tianjin Lizhong Alloy Group Co.,Ltd. |
|
| TR01 | Transfer of patent right |