CN109518027A - A kind of preparation method and application of fine grain Mg-Al-Ti-C intermediate alloy - Google Patents
A kind of preparation method and application of fine grain Mg-Al-Ti-C intermediate alloy Download PDFInfo
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- CN109518027A CN109518027A CN201811464048.2A CN201811464048A CN109518027A CN 109518027 A CN109518027 A CN 109518027A CN 201811464048 A CN201811464048 A CN 201811464048A CN 109518027 A CN109518027 A CN 109518027A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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Abstract
The present invention is a kind of preparation method and applications of fine grain Mg-Al-Ti-C intermediate alloy.This method is changed on the basis of cast magnesium alloy, coarse-grain Mg-Al-Ti-C intermediate alloy is prepared by two-step method (cardinal principle is to prepare the Mg-Al-Ti-C intermediate alloy containing TiC by additional mode), and fine grain Mg-Al-Ti-C intermediate alloy is obtained using copper mold spray to cast method processing coarse-grain Mg-Al-Ti-C intermediate alloy, Metamorphism treatment is carried out to magnesium alloy with it.The present invention reduces coarse-grain intermediate alloys to the tendency for enhancing particle agglomeration in magnesium alloy Metamorphism treatment, is conducive to the raising of magnesium alloy bond strength；The second phase enhancing particle TiC of intermediate alloy is uniformly distributed, and improves the hardness of magnesium alloy.
Description
Technical field
The present invention relates to metal material cast magnesium alloy technical field, among specifically a kind of fine grain Mg-Al-Ti-C
The preparation method and application of alloy.
Background technique
It is current density metal material that is minimum, and widely applying by the cast magnesium alloy of representative of AZ91D.It extensive
Using for energy-saving and emission-reduction, slows down greenhouse effects and be of great significance.Moreover, the development potentiality of magnesium alloy and application are excellent in recent years
Gesture causes the great attention that magnesium alloy is studied by many countries, government, enterprise and research institution, has put into a large amount of manpowers, object
Power, financial resources, and achieve significant achievement.The application range of magnesium alloy is also more and more extensive, and range is related to auto industry, leads at present
The fields such as electronics industry and aerospace industry of news.It will be appreciated, however, that the application of magnesium alloy is limited only to non-structural part at present.Its
In a major reason be that the mechanical property and corrosion resistance of magnesium alloy are poor.Therefore, by magnesium alloy handled come
Enhance its mechanical property and corrosion resistance is imperative.Fine degenerate is carried out to magnesium alloy by additional intermediate alloy, to mention
Its high mechanical property is particularly important.In addition, on outer plus enhancing particle basis, by additional intermediate alloy, and benefit
With the second phase of intermediate alloy, the mechanical property of Lai Zengqiang magnesium alloy is also a kind of effective method.But it mostly uses at present
Coarse-grain intermediate alloy carries out Metamorphism treatment to magnesium alloy, and this method has been difficult to improve its performance again, while using among coarse-grain
The second phase enhancing magnesium alloy mechanical property of alloy be easy to cause the reunion of enhancing particle, closes to using fine grain intermediate alloy to magnesium
The report of golden Metamorphism treatment is seldom.
Currently, having both at home and abroad about the main method for preparing intermediate alloy: water quenching gets rid of band method, copper mold spray to cast method, atomization
Rapid solidification method.
1) water quenching:
Water quenching is that a kind of history is more long, and operates fairly simple rapid solidification method.Its technical process are as follows:
Master alloy is put into quartz ampoule, quartz ampoule is vacuumized and is passed through high-purity argon gas and is protected, sealed silica envelope；Using high frequency
Induction heating apparatus heated quarty tube after master alloy all fusing, intermediate alloy is put into water and is carried out to melt master alloy
Water quenching chilling, to obtain the alloy of structure refinement.
Using this process, in order to further increase cooling velocity, quartz ampoule can be replaced with metal tube.Improve heating
Rate, it is relatively early that quartz ampoule is put into water and stirred, the probability of master alloy and quartzy tube reaction can be mitigated.
2) band method is got rid of:
Get rid of the technological principle with method preparation are as follows: virgin alloy is added in quartz ampoule, vacuumizes；Using induction coil to stone
English pipe carries out high-frequency induction heating and melts virgin alloy, and high-purity argon gas is passed through into quartz ampoule, utilizes the pressure of high-purity argon gas
Molten metal is sprayed out of quartzy bottom of the tube is provided with aperture；The molten metal of ejection encounter high-speed rotating copper roller formed it is band-like
Rapidly solidified alloy.This method can change cooling velocity by adjusting the revolving speed of copper roller, the disadvantage is that bulk can not be prepared
Rapidly solidified alloy.Nanocrystalline Al -5Ti-B alloy has been prepared using band method is got rid of in the ocean Zhengzhou University Guo Jin, and to aluminium alloy
Metamorphism treatment is carried out, good effect is achieved.
3) copper mold spray to cast method:
Copper mold spray to cast method prepares the technological principle of rapidly solidified alloy are as follows: by small blocky virgin alloy be placed in bottom be provided with it is small
It in the quartz ampoule in hole, vacuumizes, leads to argon gas protection；Using high-frequency induction plus fusing intermediate alloy, it is completely melt to intermediate alloy
Afterwards, poor using two-way pressure in quartz ampoule, molten metal is sprayed into the copper mold of underface and be quickly cooled down, to obtain quickly solidification
Alloy.
Since the thermal conductivity of copper mold is high, the size of sample is small, so the alloy structure obtained is relatively fine.This method is cold
But it is lower than in rate and gets rid of band method, but this method can prepares the block rapidly solidified alloy of smaller size.
4) it is atomized rapid solidification method:
Atomization is dispersed into alloy melt using high velocity fluid strikes power, centrifugal force and mechanical hitting power collective effect
The tiny misty molten drop of size, while molten drop and fluid or substrate being allowed to contact quick solidification, to obtain the alloy structure of refinement.
This method has the advantages that at low cost, high production efficiency, is suitable for large-scale production, but it also has cooling effect is unstable to lack
Point.
It is more to the research of atomization both at home and abroad.External Ruthardt, Klaus Bauckhage think using static hair
The direct atomized alloy of thin wave, and the molten metal partial size after the atomization of this method is small, evaporation-condensation rate is very fast.Domestic Zhang Shuguang adopts
Spherical fine grain Sn-Pb alloy is prepared with ultrasonic atomizatio method.
Summary of the invention
The purpose of the present invention is provide a kind of fine grain Mg-Al- for deficiency present in current cast magnesium alloy technology
The preparation method and application of Ti-C intermediate alloy.This method is changed on the basis of cast magnesium alloy, and two-step method is passed through
(cardinal principle is that the Mg-Al-Ti-C intermediate alloy containing TiC is prepared by additional mode) prepares in coarse-grain Mg-Al-Ti-C
Between alloy, and using copper mold spray to cast method processing coarse-grain Mg-Al-Ti-C intermediate alloy obtain fine grain Mg-Al-Ti-C intermediate alloy,
Metamorphism treatment is carried out to magnesium alloy with it.The present invention reduces coarse-grain intermediate alloys to enhancing cluster of grains in magnesium alloy Metamorphism treatment
Poly- tendency is conducive to the raising of magnesium alloy bond strength；The second phase enhancing particle TiC of intermediate alloy is uniformly distributed, and is improved
The hardness of magnesium alloy.
The technical solution of the present invention is as follows:
A kind of preparation method of fine grain Mg-Al-Ti-C intermediate alloy, comprising the following steps:
Prepare Al powder, TiC powder and pure magnesium ingot, wherein the quality percentage composition of each component according to the component of the alloy
Are as follows: C 0.68%~1.2%, Ti 2.72%~4.8%, Al 3.42%~5.6%, remaining is Mg, and molar ratio Ti:C=
1:1；
Step 1: preparing prefabricated section
Al powder and TiC powder are mixed, mixed-powder is subjected to 3.5~4.5h of ball-milling treatment with ball mill；Then, it is being cold-pressed
12~16MPa of pressure under, the complete powder of ball milling is pressed into prefabricated section；
Step 2: preparing coarse-grain Mg-Al-Ti-C intermediate alloy
Prefabricated section and pure magnesium ingot are put together, high-purity argon gas protection is passed through, is heated to 820 using vacuum induction melting furnace
~860 DEG C, 1~1.5h is kept the temperature, coarse-grain Mg-Al-Ti-C intermediate alloy is made in furnace cooling；The purity of the high-purity argon gas
It is 99.999%；
Step 3: preparation fine grain Mg-Al-Ti-C intermediate alloy
Coarse-grain intermediate alloy is cut into bulk, is placed in the quartz ampoule of bottom end aperture；Copper mold spray to cast furnace body is taken out
Vacuum makes its vacuum degree not less than 1.2 × 10-3Pa, and be filled with high-purity argon gas and protected；High frequency sense is carried out using induction coil
Fusing coarse-grain intermediate alloy should be heated, high-purity argon gas is then passed to, molten metal is sprayed among copper mold, obtains closing among fine grain
Gold；
Wherein, heating temperature is 750~760 DEG C, and the air pressure for blowing molten metal is 7.5 × 104~8.5 × 104pa；
The range of prefabricated block size is 18~22mm × 13 Φ~17mm in the first step；
The block-like size of coarse-grain intermediate alloy in the third step is in 1~1.2mm.
The application of the fine grain Mg-Al-Ti-C intermediate alloy, for rotten modified magnesium alloy:
The following steps are included: magnesium alloy ingot is put into resistance furnace under protective atmosphere, heating is heated to 740~780
DEG C, it is ingot melting after slagging-off, add fine grain Mg-Al-Ti-C intermediate alloy, be cooled to 700~730 DEG C, stir lower heat preservation 8~
After slagging-off, molten metal is cast by 12min, obtains rotten magnesium alloy；
Wherein, it is 2~15wt% that the quality of the fine grain Mg-Al-Ti-C intermediate alloy of addition, which accounts for rotten quality of magnesium alloy,.
The magnesium alloy is AZ91D or AZ91HP.
The purity of high-purity Al powder, high-purity Ti C powder and high-purity argon gas is 99.999%, and the purity of pure Mg ingot is
99.95%.
The vacuum induction melting furnace is ZG-0-01 type vacuum induction melting furnace, and well formula crucible electrical resistance furnace is SG2-5-
12 well formula crucible electrical resistance furnaces.
The protective atmosphere is that percent by volume is 3%SF6+ 97%CO2Mixed gas.
Substantive distinguishing features of the invention are as follows:
The present invention is by two-step method+copper mold spray to cast legal system detailed information crystalline substance Mg-Al-Ti-C intermediate alloy (at present mostly using thick
Brilliant intermediate alloy carries out Metamorphism treatment to magnesium alloy), and to magnesium alloy Metamorphism treatment, this mechanical property for enhancing magnesium alloy
It is very favorable.The present invention first passes through copper mold spray to cast method processing coarse-grain Mg-Al-Ti-C intermediate alloy, efficiently solves increasing
The problem of strong particle serious agglomeration, so that TiC even dispersion is distributed, this is to pass for TiC being uniformly distributed in the magnesium alloy
Important；The magnesium alloy for passing through fine grain Mg-Al-Ti-C intermediate alloy Metamorphism treatment again, realizes TiC even particle distribution, solves
Coarse-grain Mg-Al-Ti-C intermediate alloy of having determined handles the problem of magnesium alloy and magnesium alloy grain boundaries a large amount of segregation TiC particles, has
Conducive to the tensile strength for improving magnesium alloy.TiC is enhancing particle, therefore the addition of TiC can increase substantially the hard of magnesium alloy
Degree.
The invention has the benefit that
The present invention designs the detailed crystalline substance Mg-Al-Ti-C intermediate alloy of two-step method+copper mold spray to cast legal system, and Metamorphism treatment magnesium closes
Gold makes magnesium alloy have excellent mechanical property；Compared with traditional cast magnesium alloy, the present invention first uses two-step method+copper
The detailed crystalline substance Mg-Al-Ti-C intermediate alloy of mould spray to cast legal system, then Metamorphism treatment magnesium alloy, not only bond strength enhances, but also hardness
It improves.Compared with traditional cast magnesium alloy, advantage is embodied in: the enhancing particle agglomeration phenomenon of magnesium alloy is obviously improved；
Bond strength is improved, and is 1.1~1.3 times of traditional cast magnesium alloy；Hardness is the 1.2~1.6 of traditional cast magnesium alloy
Times.
Detailed description of the invention
Present invention will be further explained below with reference to the attached drawings and examples.
Fig. 1 is the SEM photograph of the coarse-grain Mg-Al-Ti-C intermediate alloy in embodiment 1.
Fig. 2 is the SEM photograph of the fine grain Mg-Al-Ti-C intermediate alloy in embodiment 1.
Fig. 3 is the metallographic microscope that the modification AZ91D of fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt% is added in embodiment 1
Piece.
Fig. 4 is the SEM photograph that the modification AZ91D of fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt% is added in embodiment 1
Piece.
Fig. 5 is that the EDS of A point in Fig. 4 analyzes map.
Fig. 6 is the TiC particle that the modification AZ91D of fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt% is added in embodiment 1
SEM pattern and EMPA line scanning；Wherein, Fig. 6 a is the modification that the fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt% is added
The TiC particle SEM photograph of AZ91D；Fig. 6 b is the analysis result of Mg element in the scanning of EMPA line；Fig. 6 c is Al in the scanning of EMPA line
The analysis result of element；Fig. 6 d is the analysis result of Ti element in the scanning of EMPA line；Fig. 6 e is point of C element in the scanning of EMPA line
Analyse result；Fig. 6 f is the analysis result of O element in the scanning of EMPA line.
Fig. 7 is that the tension of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of addition 5.2wt% in embodiment 1 is strong
The comparison diagram of degree and AZ91D.
Fig. 8 is that the Vickers of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of addition 5.2wt% in embodiment 1 is hard
The comparison diagram of degree and AZ91D.
Fig. 9 is the metallographic of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of the addition 2.7wt% in embodiment 2
Picture.
Figure 10 is that the tension of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of addition 2.7wt% in embodiment 2 is strong
The comparison diagram of degree and AZ91D.
Figure 11 is that the Vickers of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of addition 2.7wt% in embodiment 2 is hard
The comparison diagram of degree and AZ91D.
Figure 12 is the gold of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of the addition 12.5wt% in embodiment 3
Phase picture.
Figure 13 is the tension that the modification AZ91D of fine grain Mg-Al-Ti-C intermediate alloy of 12.5wt% is added in embodiment 3
The comparison diagram of intensity and AZ91D.
Figure 14 is the Vickers that the modification AZ91D of fine grain Mg-Al-Ti-C intermediate alloy of 12.5wt% is added in embodiment 3
The comparison diagram of hardness and AZ91D.
Specific embodiment
Embodiment 1
The present embodiment 1 prepares fine grain Mg-Al-Ti-C intermediate alloy, with the fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt%
Metamorphism treatment AZ91D, main component are as shown in table 1.
1 AZ91D magnesium alloy chemical ingredient of table
Step 1: preparing prefabricated section
Al powder and TiC powder are mixed according to mass ratio 1:1, wherein Al powder and TiC powder purity are 99.999%, by mixed powder
End carries out ball-milling treatment with ball mill, and Ball-milling Time is 4 hours.Then, utilize cold stamping die by ball milling under the pressure of 15MPa
Complete powder is pressed into prefabricated section, and prefabricated block size is Φ 20mm × 15mm.The molar ratio Ti:C=1:1 of the TiC powder；
Step 2: preparing coarse-grain Mg-Al-Ti-C intermediate alloy
Prefabricated section and pure magnesium ingot 1:9 in mass ratio are put together, wherein the purity of pure magnesium ingot is 99.95%, is passed through height
Straight argon gas shielded, wherein the purity of high-purity argon gas is 99.999%, using ZG-0-01 type vacuum induction melting furnace (its main skill
Art parameter is as shown in table 2) 850 DEG C are heated to, 1 hour is kept the temperature, coarse-grain Mg-Al-Ti-C intermediate alloy is made in furnace cooling.
The important technological parameters of table 2ZG-0-01 type vacuum induction melting furnace
Step 3: preparation fine grain Mg-Al-Ti-C intermediate alloy
Coarse-grain intermediate alloy is cut into the bulk having a size of 1.2mm with wire cutting machine, bottom end is placed in and is provided with diameter 1.5mm
In the quartz ampoule of aperture；Copper mold spray to cast furnace body is vacuumized, makes its vacuum degree not less than 1.2 × 10-3Pa, and be filled with high-purity
Argon gas is protected；High-frequency induction heating is carried out using induction coil and melts coarse-grain intermediate alloy, then passes to 8 × 104Pa's
High-purity argon gas, molten metal are injected among copper mold under its pressure, obtain fine grain intermediate alloy (its chemical component such as 3 institute of table
Show).
3 Mg-Al-Ti-C master alloy chemistries of table
Step 4: Metamorphism treatment magnesium alloy
The fine grain Mg-Al-Ti-C intermediate alloy that mass fraction is 5.2wt% goes bad AZ91D using SG2-5-12 type well formula
Crucible electrical resistance furnace (its important technological parameters is as shown in table 4) carries out melting, the specific steps are as follows:
(1) to crucible, bamboo strainer (slagging-off use), tracheae three-way connection, metal tracheae and i.e. by the ingot casting and fine grain of melting
Mg-Al-Ti-C intermediate alloy carries out drying and processing with 50 DEG C of drying box, and the time is for 24 hours；Well formula resistance furnace is carried out in advance pre-
Heat, temperature are 150 DEG C, and the time is the drying of burner hearth when guaranteeing melting in second day for 24 hours；Metal pattern is before melting with box
Resistance furnace keeps the temperature it, and 300 DEG C of temperature, until being taken out before melting casting.
(2) protective atmosphere of melting is 3%SF6+ 97%CO2Mixed gas.Gas access equipment, nothing are checked before melting
The crucible equipped with ingot casting is placed in resistance furnace burner hearth after accidentally, covers tightly bell, protective gas is passed through, stops ventilation after 5min；It is logical
Electricity, heating are heated to 760 DEG C (the logical primary protection gas of every 5min in the process, time 1min), and intermediate alloy is added in slagging-off,
720 DEG C of heat preservation 10min are cooled to, removes the gred, prepares to come out of the stove.
(3) protection air-flow is directed at molten metal, crucible is taken out with crucible tongs, is cast in metal mold, casting is cold
But after, the casting rod having a size of 22 × 130mm of Φ is taken out in die sinking.
The important technological parameters of 4 SG2-5-12 type well formula crucible electrical resistance furnace of table
Exist in the microscopic structure for the Mg-Al-Ti-C intermediate alloy that two-step method obtains as seen in Figure 1 apparent
TiC tissue, illustrates that this method can prepare the Mg-Al-Ti-C intermediate alloy of bulk.But TiC is organized to exist and is unevenly distributed
The problem of with reuniting, this is because TiC particle is smaller, surface free energy is bigger, it is caused to be easy to reunite.Comparison diagram 2 can
With discovery, copper mold spray to cast method efficiently solves the problems, such as that enhancing particle agglomeration is serious, so that TiC even dispersion is distributed, this is right
In final TiC being uniformly distributed in AZ91D be vital.
As seen from Figure 3, TiC even particle distribution.
It can be seen that the ratio between Ti element and the atomicity of C element connect in the particle for becoming scattered about AZ91D matrix by Fig. 4 and Fig. 5
It is bordering on 1:1, it is thus determined that it is TiC, distribution in the base is more uniform.In the process of setting of molten metal, TiC and Al
Element is ostracised onto crystal boundary, and TiC and β-Mg are caused17Al12It is distributed in grain boundaries together, and the two is at a distance of relatively close.It is distributed in crystalline substance
TiC in boundary can inhibit growing up for crystal grain to a certain extent, this is advantageous for improving the intensity of AZ91D.
Along scan line, for Mg element by being restored to previous level after a bust again, Al is first from top to bottom as seen from Figure 6
It is known as a bust, Ti element and C element are once uprushed, and tri- kinds of elements of O, Ti, C are respectively once uprushed and position weighs substantially
It closes.This is proved, is followed successively by β-Mg from top to bottom along scan line17Al12Phase, TiC particle, magnesium matrix.
The tensile strength that can be seen that AZ91D alloy by Fig. 7 and Fig. 8 is 157.1MPa, and the fine grain Mg- of 5.2wt% is added
The tensile strength of the modification AZ91D of Al-Ti-C intermediate alloy is 188.2MPa, and the Vickers hardness of AZ91D is 65.9HV, is added
The Vickers hardness of the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt% is 108.7HV.To find out its cause, AZ91D
The increase of tensile strength and hardness all relies on the reduction of matrix grain size and is added to the second phase particles of AZ91D matrix
(TiC) dispersion-strengthened action.
Embodiment 2
The present embodiment 2 prepares fine grain Mg-Al-Ti-C intermediate alloy, with the fine grain Mg-Al-Ti-C intermediate alloy of 2.7wt%
Metamorphism treatment AZ91D.
Other steps are in the same manner as in Example 1.Obtained AZ91D is close to embodiment 1.
As seen from Figure 9, TiC even particle distribution is observed similar with 1 Fig. 3 of embodiment.
It is added the modification AZ91D's of the fine grain Mg-Al-Ti-C intermediate alloy of 2.7wt% it can be seen from Figure 10 and Figure 11
Tensile strength is 169.5MPa, and the Vickers hardness that the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of 2.7wt% is added is
81.2HV.It is identical as embodiment 1 Fig. 7 and Fig. 8 the reason of this trend occur, repeats no more herein.
Embodiment 3
The present embodiment 3 prepares fine grain Mg-Al-Ti-C intermediate alloy, with conjunction among the fine grain Mg-Al-Ti-C of 12.5wt%
Golden Metamorphism treatment AZ91D.
Other steps are in the same manner as in Example 1.Obtained AZ91D is close to embodiment 1.
As seen from Figure 12, when the mass fraction of fine grain Mg-Al-Ti-C intermediate alloy increases to 12.5wt%, TiC
There is obvious agglomeration.Simultaneously as TiC particle is for β-Mg17Al12Growth can not play inhibiting effect, because
This β-Mg17Al12Finally grow into the netted of connection.
The modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of 12.5wt% is added it can be seen from Figure 13 and Figure 14
Tensile strength be 183.9MPa, the Vickers that the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of 12.5wt% is added is hard
Degree is 96.5HV, and tensile strength and hardness are all declined compared with Fig. 7 and Fig. 8 in embodiment 1.The reason is that with TiC body
The increase of fraction, the viscosity of melt can also be increase accordingly, and casting fluidity can be deteriorated, and the casting flaw of casting rod is caused also to increase
Add, bond strength and hardness is caused to decline.
Embodiment 4
The present embodiment 4 prepares fine grain Mg-Al-Ti-C intermediate alloy, with the fine grain Mg-Al-Ti-C intermediate alloy of 5.2wt%
Metamorphism treatment AZ91HP, main component are as shown in table 5.
Other steps are in the same manner as in Example 1.Obtained AZ91HP is close to embodiment 1.
5 AZ91HP magnesium alloy chemical ingredient of table
Above-described embodiment explanation, the present invention prepare fine grain Mg-Al-Ti-C intermediate alloy, and in fine grain Mg-Al-Ti-C
Between alloy modification handle magnesium alloy.Wherein, in embodiment 1 proportion be C 1wt%, Ti4wt%, Al5wt%, Mg90wt%,
When the modification AZ91D of the fine grain Mg-Al-Ti-C intermediate alloy of 5.7wt% is added, the tensile strength of modified AZ91D is
The Vickers hardness of 188.2MPa, modified AZ91D are 108.7HV, and effect is best.
Unaccomplished matter of the present invention is well-known technique.
Claims (8)
1. a kind of preparation method of fine grain Mg-Al-Ti-C intermediate alloy, it is characterized in that method includes the following steps:
Prepare Al powder, TiC powder and pure magnesium ingot, the wherein quality percentage composition of each component are as follows: C according to the component of the alloy
0.68%~1.2%, Ti 2.72%~4.8%, Al 3.42%~5.6%, remaining is Mg, and molar ratio Ti:C=1:1；
Step 1: preparing prefabricated section
Al powder and TiC powder are mixed, mixed-powder is subjected to 3.5~4.5h of ball-milling treatment with ball mill；Then, in the pressure of cold pressing
Under 12~16MPa of power, the complete powder of ball milling is pressed into prefabricated section；
Step 2: preparing coarse-grain Mg-Al-Ti-C intermediate alloy
Prefabricated section and pure magnesium ingot are put together, high-purity argon gas protection is passed through, 820 are heated to using vacuum induction melting furnace~
860 DEG C, 1~1.5h is kept the temperature, coarse-grain Mg-Al-Ti-C intermediate alloy is made in furnace cooling；
Step 3: preparation fine grain Mg-Al-Ti-C intermediate alloy
Coarse-grain intermediate alloy is cut into bulk, is placed in the quartz ampoule of bottom end aperture；Copper mold spray to cast furnace body is vacuumized,
Make its vacuum degree not less than 1.2 × 10-3Pa, and be filled with high-purity argon gas and protected；High-frequency induction is carried out using induction coil to add
It is hot-melted coarse-grain intermediate alloy, then passes to high-purity argon gas, molten metal is sprayed among copper mold, fine grain intermediate alloy is obtained；
Wherein, heating temperature is 750~760 DEG C, and the air pressure for blowing molten metal is 7.5 × 104~8.5 × 104pa。
2. the preparation method of fine grain Mg-Al-Ti-C intermediate alloy as described in claim 1, it is characterized in that the first step
In prefabricated block size range be 18~22mm × 13 Φ~17mm.
3. the preparation method of fine grain Mg-Al-Ti-C intermediate alloy as described in claim 1, it is characterized in that the third step
The rapid block-like size of coarse-grain intermediate alloy is in 1~1.2mm.
4. the preparation method of fine grain Mg-Al-Ti-C intermediate alloy as described in claim 1, it is characterized in that the second step
The purity of high-purity argon gas described in rapid is 99.999%.
5. the application of fine grain Mg-Al-Ti-C intermediate alloy as described in claim 1 is closed it is characterized in that being used to prepare rotten magnesium
Gold.
6. the application of fine grain Mg-Al-Ti-C intermediate alloy as claimed in claim 5, it is characterized in that the following steps are included: protection
Under atmosphere, magnesium alloy ingot is put into resistance furnace, heating is heated to 740~780 DEG C, removes the gred after ingot melting, adds thin
Brilliant Mg-Al-Ti-C intermediate alloy is cooled to 700~730 DEG C, stirs 8~12min of lower heat preservation, after slagging-off, molten metal is cast,
Obtain rotten magnesium alloy；
Wherein, it is 2~15wt% that the quality of the fine grain Mg-Al-Ti-C intermediate alloy of addition, which accounts for rotten quality of magnesium alloy,.
7. the application of fine grain Mg-Al-Ti-C intermediate alloy as claimed in claim 5, it is characterized in that the magnesium alloy is
AZ91D or AZ91HP.
8. the application of fine grain Mg-Al-Ti-C intermediate alloy as claimed in claim 5, it is characterized in that the protective atmosphere is
Percent by volume is 3%SF6And 97%CO2Mixed gas.
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Cited By (5)
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| CN111155009A (en) * | 2020-01-16 | 2020-05-15 | 深圳市新星轻合金材料股份有限公司 | Preparation method of magnesium-aluminum-titanium-chromium alloy |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110331304A (en) * | 2019-07-02 | 2019-10-15 | 南昌大学 | A method of preparing aluminium cerium intermediate alloy |
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| CN111155010A (en) * | 2020-01-16 | 2020-05-15 | 深圳市新星轻合金材料股份有限公司 | Preparation method of magnesium-aluminum-titanium alloy |
| CN111235415A (en) * | 2020-01-16 | 2020-06-05 | 深圳市新星轻合金材料股份有限公司 | Preparation method of magnesium-aluminum-titanium-vanadium alloy |
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