CN108971456A - The system and method that transition metal during stablizing primary solidification in cast aluminium alloy gold precipitates - Google Patents
The system and method that transition metal during stablizing primary solidification in cast aluminium alloy gold precipitates Download PDFInfo
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- CN108971456A CN108971456A CN201810474172.0A CN201810474172A CN108971456A CN 108971456 A CN108971456 A CN 108971456A CN 201810474172 A CN201810474172 A CN 201810474172A CN 108971456 A CN108971456 A CN 108971456A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
- B22D21/04—Casting aluminium or magnesium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
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Abstract
System for cast aluminium alloy gold includes the first chamber for accommodating the first melt for being in the first temperature, for accommodating the second chamber for being in the second melt of the second temperature lower than the first temperature, it is connected to first chamber and second chamber and is used to receive the first melt from first chamber and the second melt from second chamber and the mixing chamber being mixed simultaneously, and be connected to and be used to receive the mold of blend melt with mixing chamber.
Description
Technical field
The present invention relates to a kind of system and method for the transition metal precipitating during stable primary solidification in cast aluminium alloy gold.
Background technique
Context of the invention is totally presented in the introduction.The inventor referred at present is in the range described in this introduction
It works and otherwise can not neither express as the various aspects of the description of the prior art when submitting and also do not imply that ground
It is recognized as the prior art of the invention.
Because of good castability, corrosion resistance, machining property and high strength-weight ratio, so ceralumin is in vapour
It is had a wide range of applications in the structure member of vehicle, aerospace and common engineering industry.About castability, have compared with low silicon content
Alloy composite be considered inherently generating poor casting due to wider freezing range and reduced latent heat.It is lower
Silicon alloy is difficult to cast, they have the less mobility for filling mold and lower to supply the latent of solidification shrinkage
Heat.In addition, lower silicon alloy is prone to hot tear crack defect in process of setting, the casting of part solidification is because of cooling
When casting shrink and tear itself, this, which can leave, may cause leakage, reduced mechanical performance and reduced fatigue life
Crack.Due to these manufacturing issues, so transition metal is added into metal composites can aggravate castability and fatigue behaviour.
Alternatively, have the alloy composite compared with high silicon content to be increasingly difficult to be machined, and due to it is rougher just
Grade silicon particle and have lower ductility and fracture toughness.In general, the casting character of aluminium alloy depends on several factors,
Including technique or heat treatment after composition of alloy, casting and curing condition and casting.
It is attempting to expand or improve purposes of the aluminium alloy in the other application that can obtain benefit provided by aluminium alloy
When, existing aluminium alloy casting composition and technique fail in high temperature application.The aluminium of silicon with about 7 to 10 weight percent
Alloy is believed to be helpful in casting technique.Silicon expands in process of setting, which compensates alloy during solidification always shrink it is some,
Make alloy that there are more energy, increases the mobility of melt to improve the filling of mold, and casting is not usually than including silicon
Those of casting preferably solidify.However, the presence of silicon can poison or reduce the energy that alloy forms high-temperature-phase in aluminium alloy melt
Power.It reduce the abilities that these alloys are used for the application of some high temperature.The reduction of high-temperature-phase reduces casting in high temperature application
Durability.
Summary of the invention
In an illustrative aspect, the system for cast aluminium alloy gold includes being in the first of the first temperature for accommodating
The first chamber of melt, for accommodating the second chamber for being in the second melt of the second temperature lower than the first temperature, with first
Chamber is connected to second chamber to be used for while receiving the first melt from first chamber and the second melt from second chamber
And the mixing chamber being mixed, and the mold of blend melt is connected to and is used to receive with mixing chamber.
In another illustrative aspect, the first melt includes aluminium and at least one peritectoid transition metal element.
In another illustrative aspect, the first melt includes zirconium, scandium, cobalt, chromium, niobium, tantalum, titanium, vanadium, tungsten, molybdenum, hafnium and boron
One of.
In another illustrative aspect, the second melt has the combination of the silicon than the first melt comprising greater percentage
Object.
In another illustrative aspect, the second melt has the combination of the copper than the first melt comprising greater percentage
Object.
In another illustrative aspect, the second melt has the combination of the magnesium than the first melt comprising greater percentage
Object.
In another illustrative aspect, the first temperature is higher than the liquidus temperature of aluminum precipitation in the first melt, the second temperature
Liquidus temperature of the degree lower than aluminum precipitation in the first melt and the liquidus temperature higher than blend melt.
In another illustrative aspect, aluminum precipitation includes aluminium-vanadium precipitating, aluminum-zirconium precipitating, aluminium-titanium precipitates, aluminium-scandium sinks
It forms sediment, aluminium-cobalt precipitating, aluminium-chromium precipitating, aluminium-niobium precipitates and aluminium-tantalum precipitates and aluminium-tungsten precipitating, aluminium-molybdenum precipitating, aluminium-hafnium precipitating
At least one of with aluminium-boron precipitating.
In this way, improved high temperature, wearability and/or other performances of cast aluminium alloy gold are provided.In addition, primary
The formation of precipitating improve alloy from grain refining capability, to reduce or eliminate, to add external source by grain refiner brilliant
The needs of grain refiner material (for example, such as titanium diboride or titanium aluminide particle).Even if mutually being tied with this Grain refiner material
It closes, outer source additive, which can also be used alone, in crystal grain refinement than previously further improves.This provides improved castability and subtracts
Few casting flaw.
According to the specific embodiment being provided below, other application field of the invention be will become obvious.It should manage
Solution, specific embodiment and specific example are intended merely for the purpose of explanation, the range being not intended to limit the invention.
Features described above and advantage and other feature and advantage of the invention is from including claim and exemplary implementation
It is in the specific embodiment of example and apparent in conjunction with attached drawing.
Detailed description of the invention
The present invention will be more fully understood according to specific embodiment and attached drawing, in which:
Fig. 1 is the schematic diagram of exemplary casting system according to the present invention；
Fig. 2 is the phasor of aluminum-zirconium；
Fig. 3 is aluminium-titanium phasor；
Fig. 4 is aluminium-silicon phasor；
Fig. 5 A is the phasor of the aluminum-zirconium alloy with a small amount of silicon as impurity；And
Fig. 5 B be with for castability about 10 silicon, and for bardenability about 1.5% copper and
The phasor of the aluminum-zirconium alloy of 0.4% magnesium.
Specific embodiment
Fig. 1 is the schematic diagram of exemplary casting system 100 according to the present invention.Casting system 100 includes first chamber 102
With second chamber 104.First chamber 102 accommodates the first melt for being in the first temperature, and second chamber 104 is accommodated in the second temperature
Second melt of degree.First temperature is higher than second temperature.System 100 further include in first chamber 102 and second chamber 104
The mixing chamber 106 of each connection.Mixing chamber 106 is further connected to mold 108.
In an illustrative methods, the first melt and the second melt can be introduced into mixing chamber 106 simultaneously, thus
During mixing heat will the fast exchange between first and second melt, this is from causing stable aluminium in component in the first melt
The fast nucleation of the dispersoid of compound precipitating.In this way, it is rapid to carry out liquid for the mixing of the second melt of low temperature and the first melt
It is cold, wherein forming the precipitating of high-temperature stable in blend melt.Then blend melt comprising high temperature precipitations is flowed from mixing chamber
Enter in mold, the solidification of melt is mixed in the mold.Make high temperature precipitations in from mixing chamber fast transition to mold
The aggregation of (or " dispersoid ") minimizes.In addition, the low diffusion of obtained transition metal atoms minimizes in a mold
Dispersoid is transformed into more complicated intermetallic phase and during any subsequent heat treatment or makes during blend melt solidifies
Inhibit dissolution in the temperature course undergone with period casting.This leads to the casting for the high-temperature behavior for having stable.
In one exemplary embodiment, the first melt includes one of aluminium and peritectoid transition metal element, and
Be maintained at a temperature of liquidus temperature higher than the first melt in first chamber 102, and the second melt include aluminium alloy simultaneously
And lower than the first melt liquidus temperature and be higher than blend melt liquidus temperature at a temperature of be maintained at second chamber
In 104.
It is the silicon of known poisonous substance that second melt, which can also include to high temperature precipitations formation reaction, but can be in the second melt
It is interior to provide silicon to improve the castability of blend melt during casting.In this way, containing higher silicon components is prepared respectively
Two melts.Second melt can also contain age-hardening element, for example, such as copper and magnesium.
In this way, can adjust the composition of two kinds of precursor melts, temperature and volume with optimize aluminide volume fraction and
Dispersion is to provide optimum performance.The second melt of low melting point eutectic is maintained at temperature more lower than the first melt, causes first
Temperature of the melt in mix stages reduces rapidly, this just be introduced into mold and it is subsequent will solidify leading clouding close it is molten
The nucleation of body high temperature precipitate dispersions body.Therefore, The inventive process provides two kinds of mutually exclusive Hirschfeld-Klinger reactions, in institute
It obtains and the primary transition metal aluminide of height crystal grain refinement is provided in casting.
Table 1
Table 1 shows one group of illustrative bath component and temperature, mixes and leads before introducing die cavity just
Cause that there is the subject alloy for improving characteristic.First melt be maintained at a temperature of 1000 degrees Celsius in first chamber 102 and
Second melt is maintained at a temperature of 600 degrees Celsius in second chamber 104.First melt contains transition metal element, for example,
Such as zirconium and vanadium, usually with pass through peritectic reaction during the second melt mixed in mixing chamber 106 and solidify.Because of peritectoid
The property of reaction, so may only form very small amount of dispersoid during solidification, and because of the high temperatures of the phase formed
Matter, so then disperse phase cannot be formed using solid-state heat treatment process.In contrast, the second melt contains than the first melt
The concentration of much higher silicon, copper and magnesium.As described above, those elements improve the castability of blend melt and provide precipitating by force
The benefit of change.
Although Fig. 1 shows the mixing chamber 106 outside mold 108, mixing chamber 106 can be located at other
Position, for example, the casting chamber such as, but not limited in mold.In general, blend melt should introduced casting cavity by mixing
It is carried out before room, so that melt is uniform in mold, to provide consistent quality and characteristic in entire casting.Casting quality is special
The inconsistent or difference of property is one of problems solved by the invention.
Referring now to Fig. 2, when the first melt of high temperature in mixing chamber 106 with the second melt mixed of lower temperature
When, the first melt is quenched from complete liquid to the two-phase liquid of phase Figure 200 and disperse body region.The first melt of high temperature is initially from phase
A point in figure starts.Point A corresponds to the melt of complete liquid.When the first melt and the second melt mixed, temperature is reduced, from
And the first melt is caused to be quenched, as being converted to shown in B point in phase Figure 200 from A point.Once temperature, which passes through, just puts lower section at " A "
Curve, some solid ZrAl3 will initially form.This Liquid-liquid quenching leads to the precipitating immediately of high-temperature-phase ZrAl3,
As shown in the line at " C ".Maximize the quantity of dispersoid by the high drive generated by temperature change, to make dispersoid
Size minimize.Then before being introduced into mold and start disperse before solidification through the mixing that occurs in mixing chamber 106
Body is evenly distributed in entire blend melt.
The subsequent solidification immediately of casting occurs rapidly, this eliminate dispersoid any apparent growth or its to more complicated
Intermetallic phase transformation.In this way, resulting disperse phase provides the primary of the crystal grain refinement for facilitating casting
The fabulous core of solidified aluminum.
Fig. 3 provides the phasor that another exemplary high temperature melt of high-temperature-phase can be formed in similar peritectic reaction
300.In traditional casting alloy, because the solubility of hydrogen increases with temperature, pouring temperature must be minimized.Compared with
High hydrogen content will increase the porosity of gained solidification casting.Only for centesimal titanium is put into aluminium alloy, melt
Temperature just must be over about 900 degrees Celsius, as shown in the phasor of Fig. 3.On the contrary, conventional alloys are being more than Celsius no more than about 720
It is cast at a temperature of degree.Therefore, other than those of described in the text, the invention allows to provide many other high-temperature-phases,
And impossible phase before being not limited to.
The melt of higher temperature be maintained at just on melt liquidus curve at a temperature of.The composition of melt can be wrapped substantially
Include aluminium and other any amount of peritectoid transition metal elements, for example, such as, but not limited to zirconium, scandium, cobalt, chromium, niobium, tantalum, titanium,
Vanadium, tungsten, molybdenum etc..The total amount of all elements may be limited to gained liquidus temperature in alloy.In the exemplary embodiment, melt
About 1,000 degrees Celsius of temperature be may remain in hereinafter, can still be heated to 1,200 degrees Celsius or more in a short time
Height, for example, if can then be undergone using the on-demand manufacture melt of fusing system immediately, fusing system can only be melted often immediately on demand
Quantity of material needed for a casting.In such a system, 1000 degrees Celsius of temperature may be exceeded only in the temperature short time.
The melt of lower temperature may remain at a temperature of the liquidus temperature of the melt or more.It can control the melt
Composition so that liquidus temperature minimum form with the nearly Eutectic Silicon in Al-Si Cast Alloys for providing about 10-12% silicon, wherein blend melt is with about
The silicon of 6-10% silicon forms.Alloying element in the melt of lower temperature may further include the element for improving hardenability, than
It such as, such as copper and magnesium, but also may include other elements, for example, such as silver, zinc, manganese.In one exemplary embodiment,
The melt of lower temperature may include the copper of about 0.5-5.5%, the magnesium of about 0.1-0.6%, the zinc of about 0.1-3.0% and/or about
The hybrid alloys composition of the manganese of 0.1-0.6%.
Blend melt leads to the temperature of the liquidus temperature of blend melt composition or more.In view of high-temperature fusant and low temperature
The rule of the composition of melt, mixture can determine composition, temperature and volume.After blending, can be cast immediately with
Minimize the coalescence of high temperature dispersoid.It is more complicated that the low diffusion of transition metal atoms is transformed into process of setting high temperature dispersoid
Intermetallic phase, and inhibit dissolution in heat treatment temperature and at use temperature, to generate stable height during the casting service life
Warm nature energy.
Fig. 5 A shows the phasor 500 of the aluminum-zirconium alloy with a small amount of silicon as impurity.Fig. 5 B shows to have and be used for
About 10 silicon of castability, and the aluminum-zirconium alloy of about 1.5% copper and 0.4% magnesium for bardenability
Phasor 502.Compare two phasors 500 and 502 and illustrate silicon, the addition of copper and magnesium can prevent from forming high temperature at room temperature
ZrAl3.The present invention avoids this problem by following: controlling the dynamics that disperse phase is formed by quenching high-temperature fusant alloy
It being mutually distributed to prevent to balance, this is illustrated by phasor 500, to form dispersoids in two kinds of alloy mixing periods, then casting mixing
Melt forms needed for Castability and subsequent heat treatment the remaining phase for generating precipitation-hardening to solidify blend melt.?
The high temperature precipitations formed during two kinds of melt mixeds do not dissolve during subsequent solidification, because of the zirconium in these temperature ranges
The diffusion rate of (and other transition metal) is very low.This explains disperse phase cannot be formed by conventional method, for example, for example
Pass through heat treatment.
Fig. 4 shows aluminium-silicon phasor 400.Traditional casting alloy usually contains about 6% to 10% silicon.Therefore, liquid
Liquidus temperature is about 620-640 degrees Celsius, allows to be poured under about 720 degrees Celsius (that is, 100 degrees Celsius of overheats).At one
Illustrative aspect, the melt of lower temperature contain the silicon than these conventional alloys higher amounts, it means that melt has about 600 to take the photograph
The even lower liquidus curve of family name's degree.By the lower temperature, high silicon melt and high-temperature-phase melt mixed will increase high silicon melt
Temperature, while the silicon amount in blend melt is reduced, this makes the liquidus temperature of blend melt be higher by initial high silicon melt.This will be mixed
The temperature for closing melt maintains the required overheat being higher by under about 100 degrees Celsius, and required overheat is higher by the liquidus curve of blend melt
Temperature.In this way, the relatively low hold temperature of low temperature high silicon melt reduces hydrogen content, and leads to the stomata in final casting
Rate is lower.
The composition of adjustable two kinds of precursor melts, temperature and volume are to optimize aluminide volume fractiion and dispersion to obtain
Obtain the required performance in casting.
The following table 2 shows the exemplary range of preferably a set of melt:
Table 2
The following table 3 shows a preferred embodiment of melt:
Table 3
Table 4 shows another preferred embodiment of melt:
Table 4
Table 5 shows one group of specific exemplary fusion condition:
Table 5
The blend melt composition that table 6 to 8 shows other exemplary melt composition and obtains:
| Initial melt 1 | Initial melt 2 | Subject alloy | |
| Weight | 20 | 80 | 100.00 |
| Si | 0.1 | 12 | 9.62 |
| Fe | 0.1 | 0.5 | 0.42 |
| Cu | 0.1 | 3.5 | 2.82 |
| Mg | 0.1 | 0.5 | 0.42 |
| Ti | 0.3 | 0.1 | 0.14 |
| Mn | 0.3 | 0.1 | 0.14 |
| Zn | 0.1 | 0.5 | 0.42 |
| V | 0.5 | 0.01 | 0.108 |
| Zr | 0.5 | 0.01 | 0.108 |
| Temperature | 1200 | 620 | 736 |
Table 6
Table 7
Table 8
In another exemplary embodiment again, primary silicon can be refined to improve the wear-resisting property of such as gained casting.It is existing
Fig. 4 is being returned to, the melt of higher temperature may include the aluminium alloy of high silicon content.At about 900 degrees celsius, there is about 25% silicon
Alloy be completely melt, as shown in the point " A " in phasor 400.The melt of lower temperature includes eutectic or hypoeutectic composition, such as
Shown in point " B " in phasor 400.Combined alloy (or blend melt) is indicated by point " C ", because of the power of a large amount of just grade silicon crystals
Core is studied, so being formed in traditional hypereutectic alloy or than the alloy in the range of previous higher silicon.The casting of combined alloy " C "
The fine structure of silicon crystal is maintained, so that the Main Patterns of subsequent solidification are eutectic freezings, and primary crystal growth
It is some.This is provides possibility using chemical modifier in the melt of lower temperature, so that cured eutectic structure is kept
It is modified, realize the microstructure for showing primary silicon and modified Eutectic Silicon in Al-Si Cast Alloys unavailable so far.
In one exemplary embodiment, the present invention can produce the component for internal combustion engine, for example, such as aluminium alloy vapour
Cylinder cap has improved high-temperature behavior compared with previously achievable.In this way, cylinder cover is able to bear higher temperature
Degree, which improve the efficiency of combustion process, this can provide the vehicle of improved fuel economy and/or improved combination internal combustion engine
Performance, the internal combustion engine has the aluminium cylinder cover of feature that is combined with and can obtain by using the present invention.
The specification is substantially merely illustrative, is in no way intended to limit the present invention, application or purposes.Of the invention
Introduction can be implemented in a variety of manners extensively.Therefore, although the present invention includes particular instance, true scope of the invention is not
It should so be restricted, because other modifications will be apparent after specification and following claims in research attached drawing.
Claims (9)
1. a kind of system for cast aluminium alloy gold comprising:
For accommodating the first chamber for being in the first melt of the first temperature；
For accommodating the second chamber for being in the second melt of the second temperature lower than first temperature；
It is connected to the first chamber and the second chamber molten for receiving described first from the first chamber simultaneously
Body and second melt from the second chamber and the mixing chamber being mixed；And
The mold of the blend melt is connected to and is used to receive with the mixing chamber.
2. system according to claim 1, wherein first melt includes aluminium and at least one peritectoid transition metal member
Element.
3. system according to claim 1, wherein first melt include zirconium, scandium, cobalt, chromium, niobium, tantalum, titanium, vanadium, tungsten,
One of molybdenum, hafnium and boron.
4. system according to claim 1, wherein second melt, which has, includes percentage higher than first melt
The composition of the silicon of ratio.
5. system according to claim 1, wherein second melt, which has, includes percentage higher than first melt
The composition of the copper of ratio.
6. system according to claim 1, wherein second melt, which has, includes percentage higher than first melt
The composition of the magnesium of ratio.
7. system according to claim 1, wherein first temperature is higher than the liquid phase of aluminum precipitation in first melt
Line temperature, and the second temperature is lower than the liquidus temperature of aluminum precipitation in first melt and is higher than the blend melt
Liquidus temperature.
8. system according to claim 1, wherein first temperature is higher than the liquid phase of aluminum precipitation in first melt
Line temperature, and the second temperature is lower than the liquidus temperature of aluminum precipitation in first melt and is lower than the blend melt
Liquidus temperature.
9. system according to claim 7, wherein the aluminum precipitation includes aluminium-vanadium precipitating, aluminum-zirconium precipitates, aluminium-titanium sinks
Shallow lake, aluminium-scandium precipitating, aluminium-cobalt precipitating, aluminium-chromium precipitating, aluminium-niobium precipitates and aluminium-tantalum precipitates and aluminium-tungsten precipitating, aluminium-molybdenum are heavy
At least one of shallow lake, aluminium-hafnium precipitating and aluminium-boron precipitating.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US15/609155 | 2017-05-31 | ||
| US15/609,155 US20180347011A1 (en) | 2017-05-31 | 2017-05-31 | System and method to stabilize transition metal precipitates in cast aluminum alloys during primary solidification |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN108971456A true CN108971456A (en) | 2018-12-11 |
Family
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810474172.0A Pending CN108971456A (en) | 2017-05-31 | 2018-05-17 | The system and method that transition metal during stablizing primary solidification in cast aluminium alloy gold precipitates |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US20180347011A1 (en) |
| CN (1) | CN108971456A (en) |
| DE (1) | DE102018113000A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111809083A (en) * | 2019-04-12 | 2020-10-23 | 通用汽车环球科技运作有限责任公司 | Aluminum alloy composition for simplifying semi-solid casting process and semi-solid casting method |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101018630A (en) * | 2004-07-26 | 2007-08-15 | 爱尔兰都柏林国立大学-都柏林大学 | A method for producing a functionally gradient component |
| US20080311418A1 (en) * | 2007-06-18 | 2008-12-18 | Husky Injection Molding Systems Ltd. | Metal-Molding System and Process for Making Foamed Alloy |
| US20100297467A1 (en) * | 2009-05-21 | 2010-11-25 | Sawtell Ralph R | Method of producing ingot with variable composition using planar solidification |
| CN106191562A (en) * | 2016-08-17 | 2016-12-07 | 椤惧缓 | The material of a kind of Cast aluminium alloy gold and preparation method |
| CN106191561A (en) * | 2016-08-17 | 2016-12-07 | 椤惧缓 | A kind of aluminium alloy and preparation method thereof |
-
2017
- 2017-05-31 US US15/609,155 patent/US20180347011A1/en not_active Abandoned
-
2018
- 2018-05-17 CN CN201810474172.0A patent/CN108971456A/en active Pending
- 2018-05-30 DE DE102018113000.7A patent/DE102018113000A1/en not_active Withdrawn
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101018630A (en) * | 2004-07-26 | 2007-08-15 | 爱尔兰都柏林国立大学-都柏林大学 | A method for producing a functionally gradient component |
| US20080311418A1 (en) * | 2007-06-18 | 2008-12-18 | Husky Injection Molding Systems Ltd. | Metal-Molding System and Process for Making Foamed Alloy |
| US20100297467A1 (en) * | 2009-05-21 | 2010-11-25 | Sawtell Ralph R | Method of producing ingot with variable composition using planar solidification |
| CN106191562A (en) * | 2016-08-17 | 2016-12-07 | 椤惧缓 | The material of a kind of Cast aluminium alloy gold and preparation method |
| CN106191561A (en) * | 2016-08-17 | 2016-12-07 | 椤惧缓 | A kind of aluminium alloy and preparation method thereof |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111809083A (en) * | 2019-04-12 | 2020-10-23 | 通用汽车环球科技运作有限责任公司 | Aluminum alloy composition for simplifying semi-solid casting process and semi-solid casting method |
Also Published As
| Publication number | Publication date |
|---|---|
| US20180347011A1 (en) | 2018-12-06 |
| DE102018113000A1 (en) | 2018-12-06 |
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