CA3021397C - Die casting alloy - Google Patents
Die casting alloy Download PDFInfo
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- CA3021397C CA3021397C CA3021397A CA3021397A CA3021397C CA 3021397 C CA3021397 C CA 3021397C CA 3021397 A CA3021397 A CA 3021397A CA 3021397 A CA3021397 A CA 3021397A CA 3021397 C CA3021397 C CA 3021397C
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- 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
- C22C21/04—Modified aluminium-silicon alloys
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
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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
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
Abstract
The invention relates to a die casting alloy on an aluminum-silicon base with a composition consisting of: 8.5 to 11.5 wt.% of silicon; 0.1 to 0.5 wt.% of magnesium; 0.3 to 0.8 wt.% of manganese; 0.02 to 0.5 wt.% of iron; 0.005 to 0.5 wt.% of zinc; 0.02 to 0.3 wt.% of molybdenum; 0.1 to 0.5 wt.% of copper; 0.02 to 0.15 wt.% of titanium; 0.02 to 0.3 wt.% of zirconium, 5 to 250 ppm of phosphorus, 10 to 200 ppm of gallium and the remainder of aluminum and unavoidable impurities. The alloy can be produced with a recycling rate of 50 %.
Description
Die Casting Alloy The invention relates to a die-cast alloy based on aluminium and silicon, in particular for use in lightweight vehicle structural parts.
The ever higher demands for lightweight construction in the automotive industry are taken into account with the alloy of the invention. The use of a material having higher strength makes it possible for the designer to realize more thin-walled and hence more lightweight structures. A further step towards low fuel consumption in the car can be realized in this manner.
Alloys of the type AlSi 1 0Mg or AlSi7Mg belong to the cast alloys used most widely in the industry.
At this point two die-cast alloys known from the state of the art and used in automotive engineering may be mentioned which have been developed by the applicant itself.
EP 1 612 286 B1 discloses an AlSi alloy which has high extension values even in the cast state without further heat treatment. Good values for the yield strength and tensile strength can be achieved with this alloy for die-cast parts in the cast state so that the alloy is suitable particularly for manufacturing safety components in automotive engineering. For this alloy known from the state of the art, it has been shown that due to the addition of molybdenum or combined addition of molybdenum and zirconium, the required values for tensile strength and yield strength are achieved.
EP 0 687 742 B1 likewise discloses a die-cast alloy based on aluminium-silicon, which is used in particular for safety components in automotive engineering.
Different to the alloy from EP 1 612 286 BI, the die-cast pieces manufactured are subjected to a heat treatment. It has been established for this alloy that the increased strength values achieved are dependent to a great extent on the
The ever higher demands for lightweight construction in the automotive industry are taken into account with the alloy of the invention. The use of a material having higher strength makes it possible for the designer to realize more thin-walled and hence more lightweight structures. A further step towards low fuel consumption in the car can be realized in this manner.
Alloys of the type AlSi 1 0Mg or AlSi7Mg belong to the cast alloys used most widely in the industry.
At this point two die-cast alloys known from the state of the art and used in automotive engineering may be mentioned which have been developed by the applicant itself.
EP 1 612 286 B1 discloses an AlSi alloy which has high extension values even in the cast state without further heat treatment. Good values for the yield strength and tensile strength can be achieved with this alloy for die-cast parts in the cast state so that the alloy is suitable particularly for manufacturing safety components in automotive engineering. For this alloy known from the state of the art, it has been shown that due to the addition of molybdenum or combined addition of molybdenum and zirconium, the required values for tensile strength and yield strength are achieved.
EP 0 687 742 B1 likewise discloses a die-cast alloy based on aluminium-silicon, which is used in particular for safety components in automotive engineering.
Different to the alloy from EP 1 612 286 BI, the die-cast pieces manufactured are subjected to a heat treatment. It has been established for this alloy that the increased strength values achieved are dependent to a great extent on the
- 2 -magnesium content and this content is therefore to be tolerated very tightly in the manufacture.
Further AlSi alloys known from the state of the art are cited in EP 2 653 579 and in EP 2 735 621 Al. Both alloys define the iron proportion at a maximum 0.2% by weight.
Starting from the alloy described in EP 0 687 742 B1, the object consists in developing a high-strength aluminium die-cast alloy which shows improved mechanical characteristic values with regard to tensile strength, yield strength and elongation at break. Furthermore, the alloy of the invention should have good castability, no increased tendency to adhesion, no increased risk of tendency to heat cracks and no restriction with regard to mould filling capacity.
It is a further object to develop a high-strength aluminium die-cast alloy having the properties mentioned above, wherein the aluminium base of the alloy may contain a proportion of at least 50% of secondary metal (recycling material).
According to the invention, this object is achieved by a die-cast alloy, based on aluminium-silicon, consisting of:
8.5 to 11.5% by weight silicon 0.1 to 0.5% by weight magnesium 0.3 to 0.8% by weight manganese 0.02-0.5% by weight iron 0.005-0.5% by weight zinc 0.1 to 0.5% by weight copper 0.02 to 0.3% by weight molybdenum 0.02 to 0.3% by weight zirconium 0.02 to 0.25% by weight titanium
Further AlSi alloys known from the state of the art are cited in EP 2 653 579 and in EP 2 735 621 Al. Both alloys define the iron proportion at a maximum 0.2% by weight.
Starting from the alloy described in EP 0 687 742 B1, the object consists in developing a high-strength aluminium die-cast alloy which shows improved mechanical characteristic values with regard to tensile strength, yield strength and elongation at break. Furthermore, the alloy of the invention should have good castability, no increased tendency to adhesion, no increased risk of tendency to heat cracks and no restriction with regard to mould filling capacity.
It is a further object to develop a high-strength aluminium die-cast alloy having the properties mentioned above, wherein the aluminium base of the alloy may contain a proportion of at least 50% of secondary metal (recycling material).
According to the invention, this object is achieved by a die-cast alloy, based on aluminium-silicon, consisting of:
8.5 to 11.5% by weight silicon 0.1 to 0.5% by weight magnesium 0.3 to 0.8% by weight manganese 0.02-0.5% by weight iron 0.005-0.5% by weight zinc 0.1 to 0.5% by weight copper 0.02 to 0.3% by weight molybdenum 0.02 to 0.3% by weight zirconium 0.02 to 0.25% by weight titanium
3 to 50 ppm boron 10 to 200 ppm gallium optionally 30 to 300 ppm strontium or 5 to 30 ppm sodium or 1 to 30 ppm calcium for permanent modification and 5 to 250 ppm phosphorus and/or 0.02 to 0.25% by weight titanium, and 3 to 50 ppm boron for grain refinement, with the remainder being aluminium and unavoidable impurities.
In one embodiment, the alloy of the invention contains 0.15-0.5% by weight iron.
In a further embodiment, the alloy of the invention contains 0.05 to 0.20% by weight molybdenum.
In a further embodiment, the alloy of the invention contains by 0.05 to 0.20%
by weight zirconium.
In a further embodiment, the alloy of the invention contains 60 to 120 ppm gallium.
In a further embodiment, the alloy of the invention contains 0.3 to 0.5% by weight manganese.
In a further embodiment, the alloy of the invention contains 0.2 to 0.4% by weight zinc.
In a further embodiment, the alloy of the invention contains 0.15 to 0.25% by weight copper.
In a further embodiment, the alloy of the invention contains 8.5 to 10.0% by weight silicon.
In a further embodiment, the alloy of the invention contains 0.3 to 0.4% by weight magnesium.
The die-cast alloy of the invention is preferably used for die-casting crash-relevant or strength-relevant structural parts in automotive engineering.
Date Recue/Date Received 2022-06-07
In one embodiment, the alloy of the invention contains 0.15-0.5% by weight iron.
In a further embodiment, the alloy of the invention contains 0.05 to 0.20% by weight molybdenum.
In a further embodiment, the alloy of the invention contains by 0.05 to 0.20%
by weight zirconium.
In a further embodiment, the alloy of the invention contains 60 to 120 ppm gallium.
In a further embodiment, the alloy of the invention contains 0.3 to 0.5% by weight manganese.
In a further embodiment, the alloy of the invention contains 0.2 to 0.4% by weight zinc.
In a further embodiment, the alloy of the invention contains 0.15 to 0.25% by weight copper.
In a further embodiment, the alloy of the invention contains 8.5 to 10.0% by weight silicon.
In a further embodiment, the alloy of the invention contains 0.3 to 0.4% by weight magnesium.
The die-cast alloy of the invention is preferably used for die-casting crash-relevant or strength-relevant structural parts in automotive engineering.
Date Recue/Date Received 2022-06-07
- 4 -The suitable strength of an aluminium die-cast alloy is achieved, in addition to the choice of the combination of alloying elements, also by a specific heat treatment. The alloy of the invention is subjected to a T6 heat treatment comprising solution annealing, air quenching or water quenching and artificial ageing. It could thus be established that, compared to the alloy from EP 0 687 742 B I, high yield strengths of just over 200 N/mm2 may be achieved.
The alloy of the invention has fatigue strength after the T6 heat treatment, that is, there is no self-hardening.
Furthermore, it is possible to achieve yield strengths of up to 280 N/mm2 due to a T6 heat treatment when using high annealing temperatures of 530 C, in which subsequently water quenching is effected.
Furthermore, the alloy of the invention may be subjected to a T7 heat treatment.
For die-cast parts in the material state T6 or T7, improved values for tensile strength, the yield strength and the elongation at break can be achieved with the alloy composition of the invention.
Compared to the alloy from EP 0 687 742 Bl, it could be established that the choice of content of copper of 0.1 to 0.5% by weight, preferably 0.15 to 0.25% by weight, is responsible for improving the mechanical characteristic values of the alloy.
According to EP 0 687 742 B1, the introduction of copper during melting down are to be avoided, since copper has a disadvantageous influence on corrosion resistance. The composition of the alloy of the invention was selected so that the production of corrosion-promoting phases, such as for example Al2Cu, is avoided. A salt-spray alternating test (ISO 9227) and an intergranular corrosion test (ASTM G110-92) served to investigate tendency to corrosion. A comparable corrosion resistance to that of the alloy from EP 1 already used in automotive engineering, but which restricts the copper content expressly to a maximum 0.1% by weight copper, could be established. Further elements, which improve the mechanical characteristic values, in particular extension, are the choice of molybdenum content and the addition of zirconium. The addition of
The alloy of the invention has fatigue strength after the T6 heat treatment, that is, there is no self-hardening.
Furthermore, it is possible to achieve yield strengths of up to 280 N/mm2 due to a T6 heat treatment when using high annealing temperatures of 530 C, in which subsequently water quenching is effected.
Furthermore, the alloy of the invention may be subjected to a T7 heat treatment.
For die-cast parts in the material state T6 or T7, improved values for tensile strength, the yield strength and the elongation at break can be achieved with the alloy composition of the invention.
Compared to the alloy from EP 0 687 742 Bl, it could be established that the choice of content of copper of 0.1 to 0.5% by weight, preferably 0.15 to 0.25% by weight, is responsible for improving the mechanical characteristic values of the alloy.
According to EP 0 687 742 B1, the introduction of copper during melting down are to be avoided, since copper has a disadvantageous influence on corrosion resistance. The composition of the alloy of the invention was selected so that the production of corrosion-promoting phases, such as for example Al2Cu, is avoided. A salt-spray alternating test (ISO 9227) and an intergranular corrosion test (ASTM G110-92) served to investigate tendency to corrosion. A comparable corrosion resistance to that of the alloy from EP 1 already used in automotive engineering, but which restricts the copper content expressly to a maximum 0.1% by weight copper, could be established. Further elements, which improve the mechanical characteristic values, in particular extension, are the choice of molybdenum content and the addition of zirconium. The addition of
- 5 -at least 0.08% zirconium effects an increase in extension values without a drop in strength of the material. This effect is achieved by a high-melting phase. In this context the time factor plays a particular part. Size and extent of high-melting phases are always dependent on the solidification conditions. In die-casting, solidification usually starts even in the casting chamber, continues during mould filling and ends in thick-walled regions, often only after component removal. The alloy of the invention has been developed for these processes. Only in the die-casting process do the deposits have the correct size and extent to show optimum material characteristic values after a T6 heat treatment.
If molybdenum is added at the same time, these two elements work together and an increase in strength is additionally achieved. An increase of these elements above 0.2%
does not have a positive effect on the characteristic values of the material.
The addition of gallium to the alloy of the invention showed a similar effect.
With addition of gallium, in addition to zirconium and molybdenum, a finer structure could be achieved, in particular with slightly increased iron content.
The addition of Mo, Zr and Ga plays a particular part if recycling material, say .. secondary aluminium, is used for manufacturing the alloy. At an iron content of 0.2%
it is possible to minimize the damaging effect of iron on elongation at break.
A
significantly finer structure is produced in which AlMgFeSi phases are smaller and distributed more uniformly.
The slightly increased iron content is taken into account by reducing the manganese proportion, otherwise the danger of sludge formation exists in the holding furnace on the casting machine. The tendency to adhesion of the alloy drops nevertheless, since iron just like manganese thus has a positive effect and the reduction of Mn is over-compensated by the Fe content.
In addition, the production of so-called beta phases is avoided due to the MnFe proportion, that is, lamellar AlMnFeSi deposits, whereby the ductility of the material is
If molybdenum is added at the same time, these two elements work together and an increase in strength is additionally achieved. An increase of these elements above 0.2%
does not have a positive effect on the characteristic values of the material.
The addition of gallium to the alloy of the invention showed a similar effect.
With addition of gallium, in addition to zirconium and molybdenum, a finer structure could be achieved, in particular with slightly increased iron content.
The addition of Mo, Zr and Ga plays a particular part if recycling material, say .. secondary aluminium, is used for manufacturing the alloy. At an iron content of 0.2%
it is possible to minimize the damaging effect of iron on elongation at break.
A
significantly finer structure is produced in which AlMgFeSi phases are smaller and distributed more uniformly.
The slightly increased iron content is taken into account by reducing the manganese proportion, otherwise the danger of sludge formation exists in the holding furnace on the casting machine. The tendency to adhesion of the alloy drops nevertheless, since iron just like manganese thus has a positive effect and the reduction of Mn is over-compensated by the Fe content.
In addition, the production of so-called beta phases is avoided due to the MnFe proportion, that is, lamellar AlMnFeSi deposits, whereby the ductility of the material is
- 6 -decisively reduced. Such deposits are known under the microscope as so-called iron needles.
The alpha AlMnFeSi deposits are formed to be very fine in the alloy of the invention due to the addition of the elements Mo, Zr and Ga, so that their damaging effect on extension values and tendency to corrosion may be minimized.
An improvement in castability and an increase in elongation at break were achieved due to the selected, low proportion of zinc in conjunction with the other elements of the invention. Generally a zinc content of up to 0.5% by weight still shows no effect on material characteristic values. However, the castability of the alloy which is improved with respect to EP 0 687 742 B1 has an effect on the surface quality of the components and thus on the material characteristic values.
The addition of strontium or sodium leads to a fine-grained deposit of silicon, which results in the formation of a modified eutectic, and likewise has a positive influence on the strength and extension of the alloy of the invention.
Grain refinement is preferably carried out for the alloy of the invention.
Hence, preferably 1 to 30 ppm phosphorus may be added to the alloy. Alternatively or additionally, the alloy may also contain titanium and boron for grain refinement, wherein the addition of titanium and boron is effected via a master alloy with 1 to 2% by weight Ti and 1 to 2% by weight B, remainder aluminium. The aluminium master alloy preferably contains 1.3 to 1.8% by weight Ti and 1.3 to 1.8% by weight B and has a Ti/B weight ratio of about 0.8 to 1.2. The content of the master alloy in the alloy of the invention is preferably adjusted to 0.05 to 0.5% by weight.
Within the framework of the investigations it was possible to manufacture the alloy of the invention with a recycling proportion of 50-70%.
High-grade recycling material, such as for example scrap metal of wheels, extruded profiles, sheet metals and also cuttings and the use of a tried and tested tilting-drum
The alpha AlMnFeSi deposits are formed to be very fine in the alloy of the invention due to the addition of the elements Mo, Zr and Ga, so that their damaging effect on extension values and tendency to corrosion may be minimized.
An improvement in castability and an increase in elongation at break were achieved due to the selected, low proportion of zinc in conjunction with the other elements of the invention. Generally a zinc content of up to 0.5% by weight still shows no effect on material characteristic values. However, the castability of the alloy which is improved with respect to EP 0 687 742 B1 has an effect on the surface quality of the components and thus on the material characteristic values.
The addition of strontium or sodium leads to a fine-grained deposit of silicon, which results in the formation of a modified eutectic, and likewise has a positive influence on the strength and extension of the alloy of the invention.
Grain refinement is preferably carried out for the alloy of the invention.
Hence, preferably 1 to 30 ppm phosphorus may be added to the alloy. Alternatively or additionally, the alloy may also contain titanium and boron for grain refinement, wherein the addition of titanium and boron is effected via a master alloy with 1 to 2% by weight Ti and 1 to 2% by weight B, remainder aluminium. The aluminium master alloy preferably contains 1.3 to 1.8% by weight Ti and 1.3 to 1.8% by weight B and has a Ti/B weight ratio of about 0.8 to 1.2. The content of the master alloy in the alloy of the invention is preferably adjusted to 0.05 to 0.5% by weight.
Within the framework of the investigations it was possible to manufacture the alloy of the invention with a recycling proportion of 50-70%.
High-grade recycling material, such as for example scrap metal of wheels, extruded profiles, sheet metals and also cuttings and the use of a tried and tested tilting-drum
- 7 -furnace for melting the alloy, is necessary for this. The demands of crash-relevant structural components could be fulfilled up to an iron content of 0.25%, use in strength-relevant structural components was possible up to an iron content of 0.40%.
Suitability for welding could be investigated in TIG welding tests. The alloy of the invention could be riveted without cracks in spite of its high strength in die-rivet tests.
Comparative example The compositions of an exemplary alloy from EP 0 687 742 B1 (alloy 1) and two exemplary embodiments (alloys A, B) of the alloy of the invention are compared below. The details are in % by weight. Using these two alloys, the mechanical characteristic values (R,õõ R02 and A5) were measured on die-cast 3 mm plates.
In all tests, the same T6 heat treatment was used with air quenching and with water quenching. In each case the average value of about 30 tension tests is shown.
, 1 Si Fe 0.0006 0.J.355 F Mi-1 Zn I
Alloy 1 10.15 0.110 0.0006 0.658 0.355 0.0013 j r I-Alloy A 1 9.41 0.114 I 0.197 0.49 1 0.340 0296J
Alloy B 9.01 0.227 F 0.198 0.440 1 0.349 1 0.351 I
1 Ti B __ _ T- _Sr Zr Mo i I
Alloy 1 0.050 0.001 0.020 0.002 0.0 Alloy A 0.1W 0.0003 0.023 0.117 0.087 r"
,Al1oy B 0.150 0.0049 0.0175 1 0A02 1 0.108 , Ga P
:Alloy 1 0.0050 0.0009
Suitability for welding could be investigated in TIG welding tests. The alloy of the invention could be riveted without cracks in spite of its high strength in die-rivet tests.
Comparative example The compositions of an exemplary alloy from EP 0 687 742 B1 (alloy 1) and two exemplary embodiments (alloys A, B) of the alloy of the invention are compared below. The details are in % by weight. Using these two alloys, the mechanical characteristic values (R,õõ R02 and A5) were measured on die-cast 3 mm plates.
In all tests, the same T6 heat treatment was used with air quenching and with water quenching. In each case the average value of about 30 tension tests is shown.
, 1 Si Fe 0.0006 0.J.355 F Mi-1 Zn I
Alloy 1 10.15 0.110 0.0006 0.658 0.355 0.0013 j r I-Alloy A 1 9.41 0.114 I 0.197 0.49 1 0.340 0296J
Alloy B 9.01 0.227 F 0.198 0.440 1 0.349 1 0.351 I
1 Ti B __ _ T- _Sr Zr Mo i I
Alloy 1 0.050 0.001 0.020 0.002 0.0 Alloy A 0.1W 0.0003 0.023 0.117 0.087 r"
,Al1oy B 0.150 0.0049 0.0175 1 0A02 1 0.108 , Ga P
:Alloy 1 0.0050 0.0009
- 8 Ga Alloy A 0.0092 0.0020 Alloy B 0.0104 0.0034 Results achieved T6 heat treatment, quenching in air t---- Rm IN/mm21 Rpm IN/mm21 A5 MI I
Alloy 1 236 167 7.9 Alloy A 288 209 11.0 Alloy B 280 189 9.6 T6 heat treatment, quenching in water Rm 114/mm2] Rp0.2 IN/mm21 As [%1 ,./t.11oy 1 326 241 7.9 Alloy A 332 257 10.0 'Alloy B 348 264 8.2
Alloy 1 236 167 7.9 Alloy A 288 209 11.0 Alloy B 280 189 9.6 T6 heat treatment, quenching in water Rm 114/mm2] Rp0.2 IN/mm21 As [%1 ,./t.11oy 1 326 241 7.9 Alloy A 332 257 10.0 'Alloy B 348 264 8.2
Claims (11)
1. A die-cast alloy, based on aluminum-silicon, consisting of:
8.5 to 11.5% by weight silicon 0.1 to 0.5% by weight magnesium 0.3 to 0.8% by weight manganese 0.02-0.5% by weight iron 0.005-0.5% by weight zinc 0.02 to 0.3% by weight molybdenum 0.02 to 0.3% by weight zirconium 10 to 200 ppm gallium 0.15 to 0.25% by weight copper, and 3 to 50 ppm boron for grain refinement, with the remainder being aluminum and unavoidable impurities.
8.5 to 11.5% by weight silicon 0.1 to 0.5% by weight magnesium 0.3 to 0.8% by weight manganese 0.02-0.5% by weight iron 0.005-0.5% by weight zinc 0.02 to 0.3% by weight molybdenum 0.02 to 0.3% by weight zirconium 10 to 200 ppm gallium 0.15 to 0.25% by weight copper, and 3 to 50 ppm boron for grain refinement, with the remainder being aluminum and unavoidable impurities.
2. The die-cast alloy according to claim 1, characterized by 30 to 300 ppm strontium or 5 to 30 ppm sodium or 1 to 30 ppm calcium for permanent modification and at least one of 5 to 250 ppm phosphorus and 0.02 to 0.25% by weight titanium.
3. The die-cast alloy according to claim 1 or 2, characterized by 0.15-0.5%
by weight iron.
by weight iron.
4. The die-cast alloy according to any one of claims 1 to 3, characterized by 0.05 to 0.20% by weight molybdenum.
5. The die-cast alloy according to any one of claims 1 to 4, characterized by 0.05 to 0.20% by weight zirconium.
Date Recue/Date Received 2022-1 0-1 9
Date Recue/Date Received 2022-1 0-1 9
6. The die-cast alloy according to any one of claims 1 to 5, characterized by 60 to 120 ppm gallium.
7. The die-cast alloy according to any one of claims 1 to 6 , characterized by 0.3 to 0.5% by weight manganese.
8. The die-cast alloy according to any one of claims 1 to 7, characterized by 0.2 to 0.4% by weight zinc.
9. The die-cast alloy according to any one of claims 1 to 8, characterized by 8.5 to 10.0% by weight silicon.
10. The die-cast alloy according to any one of claims 1 to 9, characterized by 0.3 to 0.4% by weight magnesium.
11. Use of a die-cast alloy according to any one of claims 1 to 10, for die-casting crash-relevant or strength-relevant structural parts in automotive engineering.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP16165969.3A EP3235917B1 (en) | 2016-04-19 | 2016-04-19 | Alloy for pressure die casting |
| EP16165969.3 | 2016-04-19 | ||
| PCT/EP2016/059723 WO2017182102A1 (en) | 2016-04-19 | 2016-05-02 | Die casting alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA3021397A1 CA3021397A1 (en) | 2017-10-26 |
| CA3021397C true CA3021397C (en) | 2023-05-23 |
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ID=55794875
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA3021397A Active CA3021397C (en) | 2016-04-19 | 2016-05-02 | Die casting alloy |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US20190119791A1 (en) |
| EP (1) | EP3235917B1 (en) |
| KR (1) | KR102609410B1 (en) |
| CN (1) | CN109072353A (en) |
| CA (1) | CA3021397C (en) |
| MX (1) | MX2018012786A (en) |
| WO (1) | WO2017182102A1 (en) |
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|---|---|---|---|---|
| CN112391562B (en) * | 2019-11-26 | 2021-09-21 | 比亚迪股份有限公司 | Aluminum alloy and preparation method thereof |
| JP7282054B2 (en) * | 2020-05-19 | 2023-05-26 | 堺アルミ株式会社 | Low thermal expansion aluminum alloy rolled material and its manufacturing method |
| CN115917024A (en) * | 2020-06-01 | 2023-04-04 | 美铝美国公司 | Al-Si-Fe casting alloy |
| CN113862530B (en) * | 2020-06-30 | 2023-04-07 | 比亚迪股份有限公司 | Aluminum alloy and preparation method thereof |
| CN113862531A (en) * | 2020-06-30 | 2021-12-31 | 比亚迪股份有限公司 | Aluminum alloy and preparation method thereof |
| CN112831695A (en) * | 2020-12-30 | 2021-05-25 | 安徽鑫铂铝业股份有限公司 | Large-scale vehicle aluminum profile with high tensile strength and preparation method thereof |
| DE102021129329A1 (en) | 2021-11-11 | 2023-05-11 | Bayerische Motoren Werke Aktiengesellschaft | Process for producing an aluminum alloy and component |
| CN115161521B (en) * | 2022-07-14 | 2023-09-08 | 山西瑞格金属新材料有限公司 | Heat treatment-free die-casting aluminum-silicon-zinc alloy |
| CN115287485A (en) * | 2022-08-10 | 2022-11-04 | 帅翼驰新材料集团有限公司 | Method for manufacturing high-pressure cast aluminum alloy with performance improved after baking |
| CN115821127A (en) * | 2022-08-10 | 2023-03-21 | 帅翼驰新材料集团有限公司 | High pressure cast aluminum alloys with improved performance after baking |
| CN115181878B (en) * | 2022-09-14 | 2022-12-23 | 苏州慧金新材料科技有限公司 | Integrated die casting aluminum alloy for new energy automobile, and preparation method and application thereof |
| CN115896504B (en) * | 2022-10-27 | 2023-07-04 | 广州致远新材料科技有限公司 | Preparation method of aluminum alloy material and preparation method of barrier gate transmission structural member |
| CN115386771B (en) * | 2022-10-27 | 2023-01-06 | 广州致远新材料科技有限公司 | Aluminum alloy material and die casting method of barrier gate transmission structural member |
Family Cites Families (21)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB605282A (en) | 1945-12-01 | 1948-07-20 | Nat Smelting Co | Improvements in or relating to aluminium silicon alloys |
| US3211547A (en) | 1961-02-10 | 1965-10-12 | Aluminum Co Of America | Treatment of molten aluminum |
| GB942629A (en) | 1961-02-10 | 1963-11-27 | Aluminum Co Of America | Improvements in purification of aluminium |
| US4222830A (en) | 1978-12-26 | 1980-09-16 | Aluminum Company Of America | Production of extreme purity aluminum |
| CH689143A5 (en) | 1994-06-16 | 1998-10-30 | Rheinfelden Aluminium Gmbh | Aluminum-silicon casting alloys with high corrosion resistance, particularly for safety components. |
| FR2841164B1 (en) | 2002-06-25 | 2004-07-30 | Pechiney Aluminium | ALLOY MOLDING WITH HIGH FLUID RESISTANCE |
| SI1443122T1 (en) * | 2003-01-23 | 2009-12-31 | Rheinfelden Aluminium Gmbh | Die cast aluminium alloy |
| DE10351666B3 (en) | 2003-11-05 | 2005-01-27 | Erbslöh Aluminium Gmbh | Aluminum product for the inner and outer parts of vehicles is made from an aluminum alloy containing alloying additions of magnesium and silicon |
| DE10352932B4 (en) * | 2003-11-11 | 2007-05-24 | Eads Deutschland Gmbh | Cast aluminum alloy |
| US20050167012A1 (en) | 2004-01-09 | 2005-08-04 | Lin Jen C. | Al-Si-Mn-Mg alloy for forming automotive structural parts by casting and T5 heat treatment |
| SI1612286T1 (en) * | 2004-06-29 | 2011-10-28 | Rheinfelden Aluminium Gmbh | Aluminium alloy for pressure die casting |
| CN101855125B (en) | 2007-11-08 | 2013-11-06 | Ksm铸造集团有限公司 | Front axle carrier for motor vehicles |
| DE112008003601A5 (en) | 2007-11-08 | 2010-10-07 | Ksm Castings Gmbh | Al-cast alloys |
| DE102008046803B4 (en) | 2008-09-11 | 2011-01-27 | Audi Ag | Cast aluminum alloy and method of making a cast component |
| DE102009012073B4 (en) | 2009-03-06 | 2019-08-14 | Andreas Barth | Use of an aluminum casting alloy |
| DE102010055011A1 (en) | 2010-12-17 | 2012-06-21 | Trimet Aluminium Ag | Readily castable ductile aluminum-silicon alloy comprises silicon, magnesium, manganese, copper, titanium, iron, molybdenum, zirconium, strontium, and aluminum and unavoidable impurities, and phosphorus for suppressing primary silicon phase |
| MX353904B (en) | 2011-07-25 | 2018-02-02 | Nissan Motor | Aluminum alloy plate and method for manufacturing same. |
| DE102011112005A1 (en) | 2011-08-29 | 2013-02-28 | Audi Ag | Alloy, preferably aluminum casting alloy, useful e.g. as a sand or die casting alloy, comprises a specified range of silicon, zinc, iron, copper, magnesium, strontium, sodium, antimony and aluminum |
| EP2653579B1 (en) | 2012-04-17 | 2014-10-15 | Georg Fischer Druckguss GmbH & Co. KG | Aluminium alloy |
| SI2657360T1 (en) * | 2012-04-26 | 2014-07-31 | Audi Ag | Pressure cast alloy on an Al-Si basis, comprising secondary aluminium |
| EP2735621B1 (en) | 2012-11-21 | 2015-08-12 | Georg Fischer Druckguss GmbH & Co. KG | Aluminium die casting alloy |
-
2016
- 2016-04-19 EP EP16165969.3A patent/EP3235917B1/en active Active
- 2016-05-02 CN CN201680084625.8A patent/CN109072353A/en active Pending
- 2016-05-02 WO PCT/EP2016/059723 patent/WO2017182102A1/en active Application Filing
- 2016-05-02 KR KR1020187032871A patent/KR102609410B1/en active IP Right Grant
- 2016-05-02 US US16/094,324 patent/US20190119791A1/en not_active Abandoned
- 2016-05-02 CA CA3021397A patent/CA3021397C/en active Active
- 2016-05-02 MX MX2018012786A patent/MX2018012786A/en unknown
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| EP3235917B1 (en) | 2018-08-15 |
| WO2017182102A1 (en) | 2017-10-26 |
| KR102609410B1 (en) | 2023-12-01 |
| KR20180132140A (en) | 2018-12-11 |
| US20190119791A1 (en) | 2019-04-25 |
| CA3021397A1 (en) | 2017-10-26 |
| EP3235917A1 (en) | 2017-10-25 |
| CN109072353A (en) | 2018-12-21 |
| MX2018012786A (en) | 2019-06-17 |
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