CN109913675A - A kind of Al-B-P double inoculant and its preparation method and application for cocrystallized Al-Si alloy - Google Patents
A kind of Al-B-P double inoculant and its preparation method and application for cocrystallized Al-Si alloy Download PDFInfo
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- CN109913675A CN109913675A CN201910225558.2A CN201910225558A CN109913675A CN 109913675 A CN109913675 A CN 109913675A CN 201910225558 A CN201910225558 A CN 201910225558A CN 109913675 A CN109913675 A CN 109913675A
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Abstract
The invention belongs to non-ferrous alloys to process preparation field, be related to a kind of for the Al-B-P double inoculant of cocrystallized Al-Si alloy and its preparation and application.According to the 700 DEG C of isothermal section phase relations of Al-B-P ternary system, there are α-Al+AlB2A kind of Al-B-P intermediate alloy is designed in the threephase region+AlP in this area.Alloying component mass percent are as follows: 0.5%~15.0%B, 0.5%~15.0%P, surplus Al.Aluminium powder, boron powder and red phosphorus powder that granularity is 80~150 mesh are tiled on the steel plate after evenly mixing, steel plate is put into after the sealing of steel box vacuumizes, reaction in-situ is carried out in 840~930 DEG C of furnaces, prepares Al-B-P composite modifier.Al-B-P double inoculant prepared by the present invention carries out Metamorphism treatment for cocrystallized Al-Si alloy, can significantly improve the microscopic structure and mechanical property of cocrystallized Al-Si alloy.
Description
Technical field
The invention belongs to non-ferrous metals processing preparation fields, are related to a kind of dual change of the Al-B-P for cocrystallized Al-Si alloy
Matter agent and its preparation method and application.
Background technique
Cast Al-Si alloy because having many advantages, such as that density is low, thermal expansion coefficient is small, specific strength is high, is answered in cast aluminium alloy gold
With the maximum a kind of alloy of widest in area, yield, 80% or more of cast aluminium alloy gold total amount is accounted for, automobile and boat are widely used in
Its aviation field, especially cylinder body, piston.Under the conditions of routine casting, there are the following problems for alusil alloy: 1) aluminum substrate crystal grain group
It knits coarseer；2) coarse gill shape Eutectic Silicon in Al-Si Cast Alloys seriously isolates matrix；3) with the increase of silicon content, go out in alusil alloy tissue
Existing coarse, irregular blocky primary silicon, hence it is evident that drop low-alloyed toughness.Metamorphism treatment is most normal as regulation alusil alloy tissue
The means of rule, the purpose is to pass through refinement aluminium phase, silicon phase or the form for improving silicon phase, the final synthesis mechanical property for improving alloy
Energy.
The rotten member of Eutectic Silicon in Al-Si Cast Alloys is known as Na, Sr, Ca, and Ba, RE etc. can go bad eutectic Si for threadiness by gill shape.
Metamorphic mechanism is that impurity inspires twinning mechanism (IIT), which establishes on the basis of twin trench mechanism (TPRE).To aluminum substrate
It carries out rotten member and is known as Ti, B, Zr etc., compound TiAl3, AlB2, TiB2, TiC, ZrAl3There is similar crystal knot with Al
Structure and similar lattice constant can be used as the heterogeneous forming core core of Al, to refine Al crystal grain.The rotten element of primary crystal Si
Mainly P, Al and P, which react, generates AlP compound, and for Dispersed precipitate in alloy melt, crystal structure is identical as Si, belongs to face
Centered cubic lattice, and lattice constant is close, heterogeneous forming core core of the AlP as primary crystal Si, to refine primary silicon, while P
Addition can inhibit the growth of eutectic Si indirectly.
Summary of the invention
Its obdurability can be significantly improved by carrying out compound modification treatment to alusil alloy using Al-3B and Al-3P alloy, still
It needs to prepare Al-3B and Al-3P alloy respectively, and implements compound modification treatment step by step, modification process is more complicated.Of the invention
Purpose is a kind of Al-B-P composite modifier for cocrystallized Al-Si alloy Metamorphism treatment of design and development, simplifies eutectic aluminum-silicon and closes
The composite inoculating technique of gold.
The present invention is achieved in the following ways, and concrete operation step includes:
(1) by weight percent, boron: 0.5%~15.0%；Phosphorus: 0.5%~15.0%；Surplus is aluminium, weigh aluminium powder,
Boron powder and red phosphorus powder (granularity is 80~150 mesh) uniformly mix, and tile after evenly mixing on the steel plate, and tiling is with a thickness of 5 millis
Rice；
(2) steel plate be put into steel box sealing vacuumize after, it keep the temperature in 840~930 DEG C of furnaces 2~5 hours progress
Gas (P)-liquid (Al) and liquid (Al) are prepared into blocky Al-B-P composite modifier Gu reaction in-situ between-(B)；
(3) bulk Al-B-P composite modifier is taken out, is broken into 1~3 millimeter.
Preferably, the ingredient of step (1) alloy are as follows: 1.0~8.0%B, 2.5~10.0%P, aluminium are surplus.
The present invention is the ingredient that Al-B-P composite modifier is carried out according to the 700 DEG C of isothermal section phase relations of Al-B-P ternary system
Design, specific ingredient are as follows: 0.5%~15.0%B, 0.5%~15.0%P, surplus Al.The phase composition of Al-B-P alloy is
α-Al、AlB2And AlP, AlB2It is evenly distributed in α-Al matrix with AlP phase, using the Al-B-P double inoculant of invention to altogether
Rotten efficiency can be improved in the compound modification treatment of brilliant alusil alloy.
The principle of the present invention is as follows:
According to the 700 DEG C of isothermal section phase relations of Al-B-P ternary system, there are α-Al+AlB2The threephase region+AlP, in this region
Interior design Al-B-P intermediate alloy, the phase composition of alloy are α-Al, AlB2With AlP phase.When the aluminium for by granularity being 80~150 mesh
After evenly mixing, at 840~930 DEG C, liquid aluminium and gaseous state phosphorus, liquid aluminium are being mixed with solid-state boron for powder, boron powder and red phosphorus powder
Reaction in-situ occurs under configuration, aluminium element generates AlB by reaction in-situ with boron and P elements respectively2With AlP phase, these generations
It will mutually be evenly distributed in aluminum substrate.AlB2It mutually can be used as the nucleation mass point of α-Al phase, AlP phase can be used as the forming core matter of silicon phase
Point, therefore, Al-B-P alloy can play dual metamorphism to alusil alloy.
The beneficial effects of the present invention are:
The present invention prepares Al-B-P intermediate alloy, has AlB simultaneously in alloy structure2With AlP phase, and in alloy substrate
It is evenly distributed, there is significant dual metamorphism to cocrystallized Al-Si alloy, there is preferable prospects for commercial application.
Detailed description of the invention
The present invention is further described with reference to the accompanying drawings and examples.
Fig. 1 is the 700 DEG C of isothermal section phase relations of Al-B-P ternary system.
Fig. 2 is the X ray diffracting spectrum of Al-1.5B-3P intermediate alloy prepared by embodiment 1.
Fig. 3 is the microscopic structure of Al-1.5B-3P intermediate alloy prepared by embodiment 1.
Fig. 4 is the microscopic structure of Al-2.5B-2.5P intermediate alloy prepared by embodiment 2.
Fig. 5 is the microscopic structure of Al-4.0B-10P intermediate alloy prepared by embodiment 3.
Fig. 6 is the microscopic structure of Al-8.0B-8.0P intermediate alloy prepared by embodiment 4.
Fig. 7 is the microscopic structure of the rotten cocrystallized Al-Si alloy of embodiment 5Al-1.5B-3P intermediate alloy.
Specific embodiment
The present invention will be explained in more detail by embodiment, but protection scope of the present invention is not limited to these realities
Apply example.
Embodiment 1
(1) by aluminium powder, boron powder and red phosphorus powder (mass percent are as follows: boron 1.5%；Phosphorus 3.0%；Aluminium is 95.5%) uniformly mixed
It tiles after conjunction on the steel plate, mixed powder is with a thickness of 5 millimeters；
(2) steel plate be put into steel box sealing vacuumize after, it keep the temperature 2.5 hours in 850 DEG C of furnaces, progress liquid aluminium
Reaction in-situ between gaseous state phosphorus, liquid aluminium and solid-state boron is prepared into blocky Al-1.5B-3.0P composite modifier；
(3) Al-1.5B-3.0P composite modifier is taken out, is broken into 1~3 millimeter.
The X ray diffracting spectrum of Al-1.5B-3P intermediate alloy as shown in Figure 2 is it is found that the phase composition of the intermediate alloy is
α-Al、AlB2With AlP phase.Al-1.5B-3P intermediate alloy microscopic structure as shown in Figure 3 is as it can be seen that AlB2Equably divide with AlP phase
Cloth is in α-Al matrix.
Embodiment 2
(1) by aluminium powder, boron powder and red phosphorus powder (mass percent are as follows: boron 2.5%；Phosphorus 2.5%；Aluminium is 95.0%) uniformly mixed
It tiles after conjunction on the steel plate, mixed powder thickness control is at 5 millimeters；
(2) steel plate be put into steel box sealing vacuumize after, it keep the temperature 3 hours in 870 DEG C of furnaces, carry out liquid aluminium with
Reaction in-situ between gaseous state phosphorus, liquid aluminium and solid-state boron is prepared into blocky Al-2.5B-2.5P composite modifier；
(3) Al-2.5B-2.5P composite modifier is taken out, is broken into 1~3 millimeter.
Al-2.5B-2.5P intermediate alloy microscopic structure as shown in Figure 4 is as it can be seen that AlB2α-is evenly distributed in AlP phase
In Al matrix.
Embodiment 3
(1) by aluminium powder, boron powder and red phosphorus powder (mass percent are as follows: boron 4.0%；Phosphorus 10.0%；Aluminium is 86.0%) uniform
It tiles after mixing on the steel plate, mixed powder thickness control is at 5 millimeters；
(2) steel plate be put into steel box sealing vacuumize after, it is kept the temperature to 3.5 hours progress liquid aluminiums in 890 DEG C of furnaces
Reaction in-situ between gaseous state phosphorus, liquid aluminium and solid-state boron is prepared into blocky Al-4.0B-10.0P composite modifier；
(3) Al-4.0B-10.0P composite modifier is taken out, is broken into 1~3 millimeter.
Al-4.0B-10.0P intermediate alloy microscopic structure as shown in Figure 5 is as it can be seen that AlB2It is evenly distributed in AlP phase
In α-Al matrix.
Embodiment 4
(1) by aluminium powder, boron powder and red phosphorus powder (mass percent are as follows: boron 8.0%；Phosphorus 8.0%；Aluminium is 84.0%) uniformly mixed
It tiles after conjunction on the steel plate, mixed powder thickness control is at 5 millimeters；
(2) steel plate be put into steel box sealing vacuumize after, it is kept the temperature to 4 hours progress reaction in-situs in 920 DEG C of furnaces,
It is prepared into blocky Al-8.0B-8.0P composite modifier；
(3) Al-8.0B-8.0P composite modifier is taken out, is broken into 1~3 millimeter.
Al-8.0B-8.0P intermediate alloy microscopic structure as shown in Figure 6 is as it can be seen that AlB2α-is evenly distributed in AlP phase
In Al matrix.
Embodiment 5
Compound modification treatment is carried out to cocrystallized Al-Si alloy using the Al-1.5B-3.0P alterant prepared in embodiment 1:
(1) well-type electric furnace melting cocrystallized Al-Si alloy in graphite crucible is used；
(2) carbon trichloride refinery by de-gassing is added；
(3) Al-1.5B-3.0P alterant is pressed into melt rapidly, is kept the temperature after mixing evenly；
(4) by melt cast to the metal mold of preheating, the cocrystallized Al-Si alloy of dual metamorphism is made.
The microscopic structure of the rotten cocrystallized Al-Si alloy of Al-1.5B-3P intermediate alloy as shown in Figure 7 is as it can be seen that α-Al area
Score is maximum and dendrite size is minimum, and tiny primary crystal Si is uniformly distributed in matrix, and most of Eutectic Silicon in Al-Si Cast Alloys all has turned to
Graininess.Above-mentioned phenomenon shows that eutectic aluminum-silicon microstructure prepared by embodiment 5 is in preferably horizontal.
Taking the above-mentioned ideal embodiment according to the present invention as inspiration, through the above description, relevant staff is complete
Various changes and amendments can be carried out without departing from the scope of the technological thought of the present invention' entirely.The technology of this invention
Property range is not limited to the contents of the specification, it is necessary to which the technical scope thereof is determined according to the scope of the claim.
Claims (6)
1. a kind of Al-B-P double inoculant for cocrystallized Al-Si alloy, it is characterised in that: Al-B-P alloying component quality hundred
Score are as follows: 0.5%~15.0%B, 0.5%~15.0%P, surplus Al；The phase composition of the Al-B-P alloy be α-Al,
AlB2And AlP；AlB2It is evenly distributed in α-Al matrix with AlP phase.
2. being used for the Al-B-P double inoculant of cocrystallized Al-Si alloy as described in claim 1, it is characterised in that: Al-B-P is closed
The ingredient of gold are as follows: 1.0~8.0%B, 2.5~10.0%P, surplus Al.
3. a kind of preparation method for the Al-B-P double inoculant of cocrystallized Al-Si alloy as described in claim 1, special
Sign is: the Al-B-P alloy preparation method are as follows: weighs aluminium powder, boron powder and the red phosphorus powder that granularity is 80~150 mesh respectively,
It tiles after even mixing on the steel plate, steel plate is put into after the sealing of steel box vacuumizes, it keeps the temperature to 2 in 840~930 DEG C of furnaces~
5 hours carry out solution-air, it is liquid-solid between reaction in-situ, a step is prepared into blocky Al-B-P composite modifier, by blocky Al-B-
P composite modifier is crushed after taking out, and obtains Al-B-P double inoculant particle.
4. the preparation method for the Al-B-P double inoculant of cocrystallized Al-Si alloy, feature exist as claimed in claim 3
In: the flat overlay thickness of mixed-powder of aluminium powder, boron powder and red phosphorus powder composition is 5 millimeters.
5. the preparation method for the Al-B-P double inoculant of cocrystallized Al-Si alloy, feature exist as claimed in claim 3
In: it is compound by the reaction in-situ generation Al-B-P between gaseous state phosphorus and liquid aluminium, liquid aluminium and solid-state boron at 840~930 DEG C
Then alterant is broken into 1~3 mm granules.
6. a kind of application for the Al-B-P double inoculant of cocrystallized Al-Si alloy as claimed in claim 1 or 2, feature
It is, the Al-B-P alloy is used for the compound modification treatment of cocrystallized Al-Si alloy.
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| CN111044544A (en) * | 2019-12-18 | 2020-04-21 | 山东省科学院新材料研究所 | In-situ quantitative detection method for diffusion growth of multi-element intermetallic compound and application |
| CN114369742A (en) * | 2022-01-13 | 2022-04-19 | 河北工业大学 | BaB6Preparation method of/Al composite material inoculant |
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