HIGH-STRENGTH AND HIGH-TOUGHNESS NON-HEAT-TREATABLE DIE-CASTING ALUMINUM-SILICON ALLOY AND PREPARATION METHOD THEREFOR

Abstract

A high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy and a preparation method therefor are provided. The alloy includes the following components in percentage by weight: 8.0-10.0% of Si, 0.1-0.5% of Mg, 0.5-0.8% of Mn, 0.05-0.5% of Cu, 0.05-0.2% of Ti, 0.01-0.05% of Sr, 0.01-0.1% of V, 0.01-0.15% of RE, less than 0.2% of Fe, less than or equal to 0.4% of other impurities and the balance of Al. Based on modification refinement of eutectic Si by Sr, during preparation, the elements V and RE are imported to further significantly refine eutectic Si structures, so that the alloy obtains features of high strength and high toughness with a high Si content. Under a die-casting condition, the yield strength of the alloy can be 120-160 Mpa, the tensile strength thereof can be 260-320 Mpa and the ductility thereof can be 10-15%.

Claims

1. A high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, comprising the following components in percentage by weight: 8.0-10.0% of Si, 0.1-0.5% of Mg, 0.5-0.8% of Mn, 0.05-0.5% of Cu, 0.05-0.2% of Ti, 0.01-0.05% of Sr, 0.01-0.1% of V, 0.01-0.15% of RE, less than 0.2% of Fe, less than or equal to 0.4% of other impurities, and a balance of Al.

2. The high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy according to claim 1, wherein the RE comprises one or more of elements La, Ce, and Er.

3. A method for preparing the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy according to claim 1, comprising the following steps: S1: drying: pre-heating prepared raw materials of pure Al, pure Si, pure Mg, an AlMn intermediate alloy, an AlTi intermediate alloy, an AlCu intermediate alloy, an Al-RE intermediate alloy, and an AlV intermediate alloy for a drying treatment; and S2: smelting: adding the AlTi intermediate alloy, the AlCu intermediate alloy, the AlMn intermediate alloy, the AlV intermediate alloy, and the pure Si after melting the pure Al by a preliminary heating to obtain a first resulting alloy melt, and performing a cooling on the first resulting alloy melt after melting the pure Si, the AlTi intermediate alloy, the AlCu intermediate alloy, the AlMn intermediate alloy, the AlV intermediate alloy to obtain a second resulting alloy melt; pressing the pure Mg into a bottom of the second resulting alloy melt for melting to obtain a third resulting alloy melt, and performing a secondary heating on the third resulting alloy melt for a refinement of the third resulting alloy melt after completely melting the pure Mg to obtain a fourth resulting alloy melt; and then pressing the Al-RE intermediate alloy into a bottom of the fourth resulting alloy melt for melting to obtain a fifth resulting alloy melt, and leaving the fifth resulting alloy melt still after completely melting the fifth resulting alloy melt to obtain the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy.

4. The method according to claim 3, wherein a pre-heating temperature in S1 is 190-210 C.

5. The method according to claim 3, wherein a preliminary heating temperature in S2 is 750-760 C.

6. The method according to claim 3, wherein a cooling temperature in S2 is 680-700 C.

7. The method according to claim 3, wherein a secondary heating temperature in S2 is 720-730 C.

8. The method according to claim 3, wherein the refinement in S2 specifically comprises: introducing a nitrogen with a refining agent powder into the third resulting alloy melt by using a rotary blowing device for an injection refining to obtain a first refined melt, performing a deslagging treatment and a degassing treatment on the first refined melt to obtain a second refined melt, then leaving the second refined melt still for 10-15 min, and completing a slagging-off treatment on the second refined melt to obtain the fourth resulting alloy melt.

9. The method according to claim 8, wherein process parameters for the rotary blowing device are as follows: a degassing revolution is 300-350 r/min; a degassing time is 5-10 min, a pressure of a gas source during the degassing treatment is 0.350.05 MPa, and a gas flow is 0.2-0.8 sccm.

10. The method according to claim 8, wherein the refining agent powder comprises one of magnesium chloride and calcium chloride.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0028] By reading and referring to detailed description made by the following drawings to non-restrictive embodiments, other features, purposes and advantages of the present invention will become more obvious.

[0029] FIGS. 1A-1L show observation schematic diagrams of SEM structures of castings in examples and comparative examples, wherein FIG. 1A represents the observation schematic diagram of the SEM structure of the casting A1, FIG. 1B represents the observation schematic diagram of the SEM structure of the casting A2, FIG. 1C represents the observation schematic diagram of the SEM structure of the casting A3, FIG. 1D represents the observation schematic diagram of the SEM structure of the casting A4, FIG. 1E represents the observation schematic diagram of the SEM structure of the casting A5, FIG. 1F represents the observation schematic diagram of the SEM structure of the casting A6, FIG. 1G represents the observation schematic diagram of the SEM structure of the casting A7, FIG. 1H represents the observation schematic diagram of the SEM structure of the casting A8, FIG. 1I represents the observation schematic diagram of the SEM structure of the casting A9, FIG. 1J represents the observation schematic diagram of the SEM structure of the casting A10, FIG. 1K represents the observation schematic diagram of the SEM structure of the casting A11, and FIG. 1L represents the observation schematic diagram of the SEM structure of the casting A12.

DETAILED DESCRIPTION OF THE EMBODIMENTS

[0030] A high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy and a preparation method therefor provided by the present invention are further described below in combination with examples, so that those skilled in the art can easily understand advantages and features of the present invention, which is not used to limit the application scope of the present invention.

Example 1

[0031] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight: 8.0% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti, 0.15% of Cu, 0.02% of V, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0032] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0033] 1) drying: prepared raw materials: pure Al, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0034] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then the pure Mg was stirred for 5 min. Then a melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, slagging-off treatment was completed, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A1.

Example 2

[0035] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight: 8.0% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti, 0.15% of Cu, 0.05% of Er, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0036] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0037] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, and an Al-10Er intermediate alloy were pre-heated to 200 C. for drying treatment; and [0038] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then the pure Mg was stirred for 5 min. Then a melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10Er intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the Al-10Er intermediate alloy was stirred for 5 min till the Al-10Er intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A2.

Example 3

[0039] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight:8.0% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti,0.15% of Cu, 0.02% of V, 0.05% of Er, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0040] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10Er intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0041] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10Er intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the Al-10Er intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A3.

Example 4

[0042] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight:9.5% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti, 0.15% of Cu, 0.02% of V, 0.05% of Er, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0043] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0044] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10Er intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0045] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10Er intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the Al-10Er intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A4.

Example 5

[0046] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight:9.5% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti, 0.15% of Cu, 0.02% of V, 0.05% of La, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0047] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0048] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10La intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0049] 2) smelting: a furnace was heated to 720 C. to melt the pure aluminum, then the furnace was heated to 755 C. and the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then the pure Mg was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10La intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the Al-10La intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A5.

Example 6

[0050] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight:9.5% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti, 0.15% of Cu, 0.02% of V, 0.05% of Ce, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities the balance of Al.

[0051] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0052] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10Ce intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0053] 2) smelting: a furnace was heated to 720 C. to melt the pure aluminum, then the furnace was heated to 755 C. and the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then the pure Mg was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10Ce intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the Al-10Ce intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A6.

Example 7

[0054] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight: 10% of Si, 0.5% of Mg, 0.8% of Mn, 0.2% of Ti, 0.5% of Cu, 0.1% of V, 0.15% of La, 0.05% of Sr, 0.12% of Fe, 0.3% of other impurities the balance of Al.

[0055] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0056] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10La intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0057] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10La intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A7.

Example 8

[0058] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight: 8% of Si, 0.1% of Mg, 0.5% of Mn, 0.05% of Ti, 0.05% of Cu, 0.01% of V, 0.01% of La, 0.01% of Sr, 0.12% of Fe, 0.3% of other impurities the balance of Al.

[0059] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0060] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10La intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0061] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10La intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. An injections peed was 3 m/s, a casting pressure was 80 MPa, a ratio of a release agent was 1:100, and a die temperature was 230 C. The die used in a production process was a die-casting test bar die, and an obtained casting was labeled as A8.

Comparative Example 1

[0062] The comparative example of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight: 8.0% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti,0.15% of Cu, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0063] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the comparative example include the following steps: [0064] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy and an Al-50Cu intermediate alloy were pre-heated to 200 C. for drying treatment; and [0065] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then a melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, slagging-off treatment was completed, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. The die-casting process parameters and the die used for die casting were the same as those in the example 1, and the casting A9 was obtained.

Comparative Example 2

[0066] The comparative example of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight: 9.5% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti, 0.15% of Cu, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0067] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the comparative example include the following steps: [0068] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy and an Al-50Cu intermediate alloy were pre-heated to 200 C. for drying treatment; and [0069] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, slagging-off treatment was completed, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. The die-casting process parameters and the die used for die casting were the same as those in the example 1, and the casting A10 was obtained.

Comparative Example 3

[0070] The embodiment of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight:8.0% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti,0.15% of Cu, 0.15% of V, 0.05% of La, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0071] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the embodiment include the following steps: [0072] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10La intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0073] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10La intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for smelting, and then the Al-10La intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. The die-casting process parameters and the die used for die casting were the same as those in the example 1, and the casting A11 was obtained.

Comparative Example 4

[0074] The comparative example of the present invention provide a high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy, including the following components in percentage by weight:8.0% of Si, 0.25% of Mg, 0.6% of Mn, 0.15% of Ti,0.15% of Cu, 0.02% of V, 0.2% of La, 0.025% of Sr, 0.12% of Fe, 0.3% of other impurities and the balance of Al.

[0075] Preparation and die-casting processes for the high-strength and high-toughness non-heat-treatable die-casting aluminum-silicon alloy of the comparative example include the following steps: [0076] 1) drying: prepared raw materials: pure aluminum, pure Si, pure Mg, an Al-10Mn intermediate alloy, an Al-10Ti intermediate alloy, an Al-50Cu intermediate alloy, an Al-10La intermediate alloy and an Al-5V intermediate alloy were pre-heated to 200 C. for drying treatment; and [0077] 2) smelting: a furnace was heated to 755 C. to melt the pure aluminum, then the Al-10Ti, Al-50Cu, Al-10Mn, Al-5V and pure Si alloys were added into the furnace, the furnace was cooled to 690 C. after the intermediate alloys were melted, the pure Mg was pressed into a bottom area of a crucible by using a bell jar for melting, and then a melt was stirred for 5 min. Then the melt was heated to 720 C., nitrogen at a pressure of 0.4 MPa was introduced into the melt, a refining agent powder accounting for 0.4% of total weight of the melt was brought in, and nitrogen was introduced with a gas flow of 0.5 at 300 r/min for 10 min to deslag and degas. Then the melt was left still for 12 min, and slagging-off treatment was completed; after refining was completed, the Al-10La intermediate alloy was pressed into the bottom area of the crucible by using the bell jar for melting, and then the intermediate alloy was stirred for 5 min till the intermediate alloy was completely melted, and then the melt was left still for 12 min, and a blast furnace component analytical test was performed. High pressure casting was performed at 690 C. after the test passed. The die-casting process parameters and the die used for die casting were the same as those in the example 1, and the casting A12 was obtained.

[0078] Mechanical properties of the castings A1-A12 prepared in the examples 1-8 and the comparative examples 1-4 are tested, and the test results are shown in Table 1. It can be found by comparing the mechanical properties of the castings A1, A2, A3 and A9 that by independently adding the element V or the rare earth element Er, the strength and ductility of the alloy are obviously improved, the tensile strength is increased by 27 MPa to the maximum extent, and the improved amplitude of the ductility reaches 24.1%. By adding the elements V and Er simultaneously, the plasticity of the alloy is more obviously improved, and the ductility of the casting is significantly increased from 8.7% (A9) to 14.9% (A3) with an increase amplitude of 71.2%. The above rule can also be found by comparing the mechanical properties of the castings A4 and A10. By means of compound addition of the elements V and Er, the plasticity of the die-casting aluminum alloy with high Si content (9.5 wt %) is significantly improved, so that the ductility is increased from 6.5 (the casting A10) to 12.9% (the casting A4), and the characteristics of high strength and high toughness of the alloy are satisfied. It is found by comparing the mechanical properties of the castings A4, A5, A6 and A10 that by means of compound addition of V and rare earth elements Er, La and Ce, the plasticity and tensile strength of the die-casting aluminum alloy can be significantly improved. The tensile strength of the castings A4-A6 is about 281 MPa, the ductility is about 12.8%, and compared with the casting A10, the tensile strength and the ductility are respectively increased by 16.5% and 97%. Thus, it is illustrated that the three RE rare earths included in the patent have significant effects to the alloy. It can be known by comparing the mechanical properties of the castings A5, A7, A8, A11 and A12 that within a range of composition of the alloy provided by the patent, by means of compound addition of V and rare earth elements, the yield strength of the die-casting aluminum alloy can be greater than 120 MPa, the tensile strength thereof can be greater than 260 MPa and the ductility thereof can be greater than 10% (the castings A5, A7 and A8), reflecting excellent mechanical properties of the alloy within the range of composition of the alloy provided by the patent. When V in the alloy reaches 0.15 (the casting A11) or the rare earth elements reach 0.2 (the casting A12), which exceeds the range of the patent, the ductility and the tensile strength of the alloy are significantly reduced, and particularly, the ductility of the alloy is reduced to be less than 8%, so that the high-strength and high-toughness die-casting aluminum alloy material cannot be obtained. In conclusion, in the range of composition of the alloy involved in the present invention, by adding the element V and RE elements (La, Er and Ce), the die-casting AlSi alloy features high strength and high toughness in a non-heat treatment condition.

TABLE-US-00001 TABLE 1 Tensile mechanical properties of castings A1-A12 Yield Tensile strength/ strength/ Group Major components (MPa) (MPa) Ductility/% A1 Al8Si0.02V 121 265 10.5 A2 Al8Si0.05Er 125 279 10.8 A3 Al8Si0.02V0.05Er 129 281 14.9 A4 Al9.5Si0.02V0.05Er 135 283 12.9 A5 Al9.5Si0.02V0.05La 131 282 12.7 A6 Al9.5Si0.02V0.05Ce 136 281 13.0 A7 Al10Si0.1V0.15La 155 315 10.5 A8 Al8Si0.01V0.01La 123 267 13.2 A9 Al8Si 121 252 8.7 A10 Al9.5Si 136 241 6.5 A11 Al9.5Si0.15V0.05La 134 251 7.9 A12 Al9.5Si0.02V0.2La 145 265 7.5

[0079] Microstructures of the castings A1-A12 respectively prepared in the above-mentioned examples 1-8 and comparative examples 1-4 are observed. The microstructures are shown in FIGS. 1A-1L. It is found by comparing structures in A1(FIG. 1A), A2(FIG. 1B), A3(FIG. 1C) and A9(FIG. 1I) that with introduction of V and the rare earth element Er, the eutectic Si structure is obviously refined. When the alloy does not contain V and Er, the eutectic Si in the structure of the casting is of a layered structure in FIG. 1I, with a particle size of about 4 m. With introduction of the element V or Er, the eutectic Si structure is transformed from being lamellar to being granular, and the particle size is significantly decreased to 1 m, as shown in FIG. 1A and FIG. 1B. By compound addition of V and Er, the size of the eutectic Si in the structure is further decreased, and the eutectic Si is a much smaller vermiform structure, as shown in FIG. 1C. Change of structural characteristics is closely related to change of mechanical properties. It is apparent that by introducing the elements V and Er, the eutectic Si structure can be significantly refined, and its shape is changed, so that the performance of the alloy changes significantly. It can be found by comparing structures of A4 and A10 that the compound action of the elements V and Er is also effective to the alloy structure with the high Si content. When the Si content is 9.5 wt. % and elements V and Er are not added into the alloy, the eutectic Si structure in the structure is in a thick broken line shape, and the maximum size of the fold line-shaped structure can reach up to 10 m (as shown in FIG. 1J).With introduction of the elements V and Er in the alloy, the eutectic Si structure in the alloy is significantly refined to be vermiform (as shown in FIG. 1D), but there are block eutectic Si structures partially, which somewhat affects the plasticity of the alloy. Therefore, the plasticity of the alloy A3 is superior to that of the alloy A4. It is found by comparing the structures of the castings A4, A5, A6, A7, A8 and A10 that in the range of the alloy provided by the patent, by means of compound addition of the element V and the rare earth elements Er, La and Ce, the thick broken line-shaped structure in the die-casting aluminum alloy can disappear, so that the performance of the alloy is guaranteed. It can be known by comparing the structures of the castings A5, A11 and A12 that by adding excessive element V, second phases AIV can appear in the alloy structures, and by adding excessive rare earth elements, second phases AlLa can appear in the alloys. These second phases will reduce the plasticity of the alloys greatly. Generally, by introducing the compound action of the elements V and RE into the alloy provided by the patent, eutectic Si particles in the structures are finer and dispersive, and the shapes are greatly improved, so that the alloy has excellent mechanical properties due to the structural characteristic.

[0080] The above is merely embodiments of the present invention and does not hence limit the patent range of the present invention. Equivalent structures or equivalent flow conversions made by means of the description of the present invention are applied to other related technical fields directly or indirectly, which is, in a similar way, comprised in the protection scope of the patent of the present invention.