CN115537613B - New energy automobile motor shell aluminum alloy and forming method thereof - Google Patents
New energy automobile motor shell aluminum alloy and forming method thereof Download PDFInfo
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- CN115537613B CN115537613B CN202211295606.3A CN202211295606A CN115537613B CN 115537613 B CN115537613 B CN 115537613B CN 202211295606 A CN202211295606 A CN 202211295606A CN 115537613 B CN115537613 B CN 115537613B
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 58
- 238000000034 method Methods 0.000 title claims abstract description 25
- 239000000956 alloy Substances 0.000 claims abstract description 68
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 63
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 238000007670 refining Methods 0.000 claims description 24
- 238000003723 Smelting Methods 0.000 claims description 19
- 238000010438 heat treatment Methods 0.000 claims description 19
- 238000004512 die casting Methods 0.000 claims description 16
- 239000002994 raw material Substances 0.000 claims description 16
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 claims description 14
- 239000007787 solid Substances 0.000 claims description 9
- 230000032683 aging Effects 0.000 claims description 8
- 239000007789 gas Substances 0.000 claims description 8
- 230000008569 process Effects 0.000 claims description 8
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 239000003795 chemical substances by application Substances 0.000 claims description 6
- 230000001681 protective effect Effects 0.000 claims description 6
- 229910016952 AlZr Inorganic materials 0.000 claims description 4
- 239000000155 melt Substances 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 229910017143 AlSr Inorganic materials 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 238000001035 drying Methods 0.000 claims description 3
- 238000005242 forging Methods 0.000 claims description 3
- 239000007788 liquid Substances 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 claims description 3
- 239000002184 metal Substances 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 239000002002 slurry Substances 0.000 claims description 3
- 238000007872 degassing Methods 0.000 claims description 2
- 238000003756 stirring Methods 0.000 claims description 2
- 238000002360 preparation method Methods 0.000 claims 1
- 229910052710 silicon Inorganic materials 0.000 abstract description 12
- 229910052802 copper Inorganic materials 0.000 abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052725 zinc Inorganic materials 0.000 abstract description 3
- 229910052726 zirconium Inorganic materials 0.000 abstract description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 8
- 210000001787 dendrite Anatomy 0.000 description 8
- 239000010703 silicon Substances 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 230000005496 eutectics Effects 0.000 description 6
- 238000005728 strengthening Methods 0.000 description 6
- 238000001816 cooling Methods 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 230000018109 developmental process Effects 0.000 description 4
- 231100000572 poisoning Toxicity 0.000 description 4
- 230000000607 poisoning effect Effects 0.000 description 4
- 230000004048 modification Effects 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 229910018125 Al-Si Inorganic materials 0.000 description 2
- 229910018520 Al—Si Inorganic materials 0.000 description 2
- 230000001427 coherent effect Effects 0.000 description 2
- 230000009977 dual effect Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910052712 strontium Inorganic materials 0.000 description 2
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 229910018594 Si-Cu Inorganic materials 0.000 description 1
- 229910008465 Si—Cu Inorganic materials 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000001360 synchronised effect Effects 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Classifications
-
- 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
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- 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
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- 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
Abstract
The invention relates to a new energy automobile motor shell aluminum alloy and a forming method, wherein the aluminum alloy comprises the following components in percentage by mass: 0.5 to 1.5 percent of Cu, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg, 0.5 to 0.7 percent of Fe, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of S, 0.1 to 0.35 percent of Zr, 0.03 to 0.15 percent of RE (La+Ce), and the balance of Al and impurities, wherein the total content of the impurities is not more than 0.25 percent. The invention has the advantages that: the invention endows the alloy with excellent mechanical properties, further improves the strength and toughness and heat conducting property of the alloy, reduces the cost of the alloy and improves the market competitiveness of the tough member.
Description
Technical Field
The invention belongs to the field of aluminum alloy materials, and particularly relates to a new energy automobile motor shell aluminum alloy and a forming method thereof.
Background
In recent years, with the rapid development of industries such as automobiles, aerospace and the like, the performance requirements on materials for automobiles and aerospace are more severe. In addition, due to social pressure such as energy conservation and emission reduction, environmental pollution and the like, light weight is a strategic development requirement. Therefore, the parts in the industries such as automobiles and aerospace require higher strength, and the parts are required to have high elongation and excellent impact toughness during deformation, so as to achieve the aim of light weight. The first generation of die-casting aluminum alloy materials of the existing automobile motor shell are ADC12 and A380, wherein the tensile strength is 280-310MPa, the yield strength is 130-180MPa, the toughness is poor (the elongation after break is less than 3.5%), the heat conduction property is only 90W/m.k, the mechanical property and the heat conduction property of the new energy automobile motor shell can not be met far, the development of a brand new material is needed, the final mechanical property is that the tensile strength is more than or equal to 300MPa under the artificial aging strengthening, the yield strength is more than or equal to 150MPa, the elongation after break is more than or equal to 5%, the heat conduction property is more than or equal to 130W/m.k, and the occurrence of thermal fatigue failure of the motor shell is prevented.
Although the development of the aluminum alloy of the new energy motor shell has been greatly advanced in recent years, the aluminum alloy still needs to be further broken through in the aspects of cost reduction (the selection of the proportion ratio of the regenerated aluminum to the electrolytic aluminum), both the contradiction between the high strength and the high toughness and the high heat conduction and the improvement of the forming capability are met, so as to develop the high strength and the high heat conduction automobile parts which are represented by the new energy automobile motor shell.
Disclosure of Invention
In order to overcome the defects of the existing ADC12 and A380 aluminum alloy, and further improve the strength, toughness and heat conducting property of the alloy, the invention provides the novel energy automobile motor shell aluminum alloy and the forming method thereof, wherein the components of alloy elements are controlled, and AlZr, TCB, alRE and AlSrZr intermediate alloy are added to endow the alloy with excellent mechanical property.
The invention adopts the following technical scheme: the new energy automobile motor shell aluminum alloy comprises the following components in percentage by mass: 0.5 to 1.5 percent of Cu, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg, 0.5 to 0.7 percent of Fe, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of S, 0.1 to 0.35 percent of Zr, 0.03 to 0.15 percent of RE (La+Ce), and the balance of Al and impurities, wherein the total content of the impurities is not more than 0.25 percent.
The invention also provides a forming method of the new energy automobile motor shell aluminum alloy, which is characterized by comprising the following steps:
s1, smelting: preparing raw materials according to the percentages of all components in the formula of the aluminum alloy material; each raw material is added into a smelting furnace in sequence respectively, and is stirred uniformly after being heated and melted to obtain alloy melt;
s2, refining: refining the alloy melt obtained in the step S1 to finish degassing and impurity removal;
s3, forming: delivering the alloy melt processed in the step S2 into forming equipment or preparing semi-solid slurry and then forming to obtain an aluminum alloy component;
s4, heat treatment: and (3) feeding the aluminum alloy component in the step (S3) into a heat treatment furnace for T5 treatment.
In the step S1, the raw materials are dried and preheated, and then all the preheated raw materials are added into a smelting furnace in sequence, wherein the preheating and drying temperature is 100-450 ℃, the melting temperature is 700-800 ℃ and the stirring time is 2-15 minutes.
The sequence of adding the raw materials into the smelting furnace in the step S1 is as follows: adding an AlSi alloy ingot into a smelting furnace for smelting, adding pure metal or intermediate alloy containing Cu element and Mg element after the AlSi alloy ingot is completely melted, adding intermediate alloy of AlZr and TCB after the AlSi alloy ingot is completely melted, and adding intermediate alloy of AlRE and AlSr after the AlSi alloy ingot is completely melted.
The specific method for refining treatment in the step S2 comprises the following steps: and (3) introducing protective gas into the alloy melt, wherein the refining time is 10-30 minutes, and the introducing amount of the protective gas is 0.05-6L/min. The protective gas is nitrogen or argon.
The specific method of refining treatment in step S2 may further be: adding a solid refining agent into the alloy melt, wherein the content of the added solid refining agent is 0.1-0.5% of the mass of the melt, and the refining time is 10-30 minutes.
The tensile strength of the aluminum alloy component prepared in the step S3 is 300-310MPa, the yield strength is 135-150MPa, the elongation after fracture is 5.5-7%, and the heat conductivity coefficient is 125-135W/m.k.
The heat treatment process of the step S4 comprises the following steps: the artificial aging temperature is 180+/-5 ℃, the heat preservation time is 2-4 hours, and the room temperature is cooled along with a furnace; after T5 heat treatment, the tensile strength of the aluminum alloy member is 310-330MPa, the yield strength is 150-185MPa, the elongation after break is 5-7%, and the heat conductivity coefficient is 135-145W/m.k.
The forming equipment adopted in the step S3 is a die casting machine and a liquid forging machine.
Compared with the prior art, the invention has the following advantages:
(1) The TCB seed crystal alloy is added, a new mechanism of direct nucleation of the seed crystal is adopted, the refined poisoning source caused by Si element is eliminated, the dual effects of fine crystal strengthening and interfacial coherent strengthening are realized, and a plurality of defects caused by coarse alpha-Al dendrites in the eutectic AlSi alloy are fundamentally overcome.
(2) The eutectic silicon is thinned by strontium modification, zr element is added to achieve the synchronous thinning and modification, crystal grains and the eutectic silicon are obviously thinned, meanwhile, solid solution strengthening brought by combining Cu and Mg elements is realized, excellent mechanical properties are endowed to the alloy, and in addition, trace rare earth elements are added to endow the alloy with good corrosion resistance and heat conductivity.
(3) In the raw material proportion of the aluminum alloy, the addition amount of the regenerated aluminum is fifty percent, so that the cost of the alloy is reduced, and the market competitiveness of the tough member is improved.
Drawings
FIG. 1 shows the microstructure of the aluminum alloy of the present invention after T5 heat treatment after die casting.
FIG. 2 shows the microstructure of the aluminum alloy of the present invention after being subjected to T5 heat treatment and stretch-broken after die casting.
Detailed Description
The invention will be further described with reference to specific embodiments, and advantages and features of the invention will become apparent from the description. These examples are merely exemplary and do not limit the scope of the invention in any way. It will be understood by those skilled in the art that various changes and substitutions of details and forms of the technical solution of the present invention may be made without departing from the spirit and scope of the present invention, but these changes and substitutions fall within the scope of the present invention.
The invention relates to a new energy automobile motor shell aluminum alloy which comprises the following components in percentage by mass: 0.5 to 1.5 percent of Cu, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg, 0.5 to 0.7 percent of Fe, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of S, 0.1 to 0.35 percent of Zr, 0.03 to 0.15 percent of RE (La+Ce), and the balance of Al and impurities, wherein the total content of the impurities is not more than 0.25 percent.
For eutectic AlSi alloy, the mechanical property of the alloy can be improved by adding Ti, but the alpha-Al dendrite of the alloy casting is coarse, and the coarse alpha-Al dendrite brings a plurality of problems: if the cast is caused to generate shrinkage porosity, snow spots, segregation and other defects, the tissue compactness and the product consistency are poor. In addition, coarse alpha-Al dendrites also significantly reduce the toughness, particularly poor fatigue properties, of aluminum alloy castings. However, the conventional Al-Ti-B/Al-Ti-C master alloy is difficult to refine the Al-Si series alloy, and the root cause is that Si element causes refining 'poisoning'.
The invention adds TCB crystal seed alloy, provides a new mechanism for directly nucleating crystal seeds, not only avoids the coarse alpha-Al dendrites, but also solves a plurality of problems caused by the coarse alpha-Al dendrites, eliminates the 'poisoning' origin, and realizes the dual effects of fine crystal strengthening and interfacial coherent strengthening.
The novel method for forming the aluminum alloy of the motor shell of the new energy automobile comprises the following steps:
s1, smelting: preparing raw materials according to the percentage of each element in the formula of the aluminum alloy material, respectively weighing each raw material, preheating in a drying furnace heated to 100-450 ℃, respectively adding each raw material into a smelting furnace in sequence, heating to 700-800 ℃, and uniformly melting the raw materials for 2-15 minutes to obtain an aluminum alloy melt.
The addition sequence of the raw materials is as follows: adding an AlSi alloy ingot into a smelting furnace for smelting, adding pure metal or intermediate alloy containing Cu element and Mg element after the AlSi alloy ingot is completely melted, adding intermediate alloy of AlZr and TCB after the AlSi alloy ingot is completely melted, and adding intermediate alloy of AlRE and AlSr after the AlSi alloy ingot is completely melted.
S2, refining: and (3) introducing protective gas or solid refining agent into the alloy melt, wherein the refining time is 10-30 minutes, so as to degas and remove impurities from the melt.
The shielding gas is nitrogen or argon, the introducing amount is 0.05-6L/min, and the content of the added solid refining agent is 0.1-0.5% of the mass of the melt.
S3, forming: and (3) sending the refined alloy melt into forming equipment or preparing semi-solid slurry and then forming to obtain the aluminum alloy component.
The high-strength high-conductivity aluminum alloy forming process comprises die casting and liquid die forging.
The tensile strength of the aluminum alloy component is 300-310MPa, the yield strength is 135-150MPa, the elongation after breaking is 5.5-7%, and the heat conductivity coefficient is 125-135W/m.k.
S4, heat treatment: and feeding the formed aluminum alloy component into a heat treatment furnace for T5 treatment.
The heat treatment process is that the working efficiency temperature of the human body is 180+/-5 ℃, the heat preservation time is 2-4 hours, and the room temperature is cooled along with a furnace.
After T5 heat treatment, the tensile strength of the aluminum alloy member is 310-330MPa, the yield strength is 150-185MPa, the elongation after break is 5-7%, and the heat conductivity coefficient is 135-145W/m.k.
The aluminum alloy is formed by refining grains through vanadium treatment, refining eutectic silicon through strontium modification, and the addition of TCB avoids coarse alpha-Al dendrites, so that various problems caused by coarse alpha-Al dendrites are solved: if the defects of shrinkage porosity, snow spots, segregation and the like are caused in the casting, the structure compactness and the product consistency are poor, and meanwhile, the toughness, particularly the fatigue performance, of the aluminum alloy casting is obviously reduced. The traditional Al-Ti-B/Al-Ti-C intermediate alloy is difficult to refine the Al-Si series alloy, and the root cause is that Si element causes refining poisoning.
Example 1:
preparing high-strength high-toughness die-casting aluminum alloys with different silicon contents, preparing standard samples by utilizing the prepared alloys with different silicon contents according to the aluminum alloy smelting and high-vacuum die-casting process, and measuring to obtain the mechanical properties with different silicon contents, wherein the mechanical properties are shown in a graph 1:
table 1 die-cast aluminum alloy compositions with different silicon contents, mechanical properties and thermal conductivity (T5 heat treatment state, artificial aging temperature of 180±5 ℃, holding time of 2 hours, cooling to room temperature with furnace).
TABLE 1 die-cast aluminum alloys with different Si contents, mechanical properties and thermal conductivity (T5 Heat treatment State, artificial aging temperature 180+ -5deg.C, holding time 2 hours, furnace cooling Room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | Tensile strength degree/MPa | Yield strength- MPa | After breaking Elongation of Rate/% | Thermal conductivity W/m.k |
| 1 | 9 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 310 | 160 | 6.5 | 135 |
| 2 | 9.5 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 318 | 165 | 6.2 | 142 |
| 3 | 10.0 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 323 | 171 | 5.7 | 145 |
| 4 | 10.5 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 328 | 182 | 5.3 | 139 |
As can be seen from the graph 1, the tensile strength, the yield strength and the elongation after break of the test sample are gradually improved along with the increase of the silicon content, but the mechanical property of the test sample prepared from the alloy meets more than 310MPa, the yield strength reaches more than 150MPa, the elongation after break exceeds 5%, the heat conduction property exceeds 130W/m.k, and the requirements of the motor shell part of the new energy automobile on the mechanical property and the heat conduction property are met. The metallographic structure of the sample is shown in figure 1, the structure is compact, the primary aluminum matrix is fine and uniformly distributed, the eutectic Si phase is fine and uniformly distributed in the primary aluminum matrix, and the requirements of the metallographic structure of parts such as a motor shell of a new energy automobile are met. The fracture structure of the sample is shown in figure 2, and the distribution is tiny and obvious in ductile cast, and the fracture structure of the sample shows obvious plastic deformation.
Example 2
Preparing die-casting aluminum alloys with different Mg contents, preparing standard samples by utilizing the prepared alloys with different Mg contents according to the aluminum alloy smelting and high-vacuum die casting process, and measuring to obtain the mechanical properties with different Mg contents, wherein the mechanical properties are shown in a graph 2:
TABLE 2 die-cast aluminum alloys with different Mg contents, mechanical properties and thermal conductivity (artificial aging temperature 180.+ -. 2 ℃ C., holding time 2 hours, cooling with furnace at room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | Tensile strength degree/MPa | Yield strength- MPa | After breaking Elongation of Rate/% | Thermal conductivity W/m.k |
| 1 | 9.5 | 0.05 | 0.2 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 305 | 157 | 7.8 | 141 |
| 2 | 9.5 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 318 | 165 | 6.2 | 142 |
| 3 | 9.5 | 0.05 | 0.30 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 325 | 175 | 5.9 | 141 |
| 4 | 9.5 | 0.05 | 0.35 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 331 | 183 | 5.5 | 135 |
| 5 | 9.5 | 0.05 | 0.4 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Allowance of | 338 | 187 | 5.2 | 139 |
As can be seen from the graph 2, the tensile strength, the yield strength and the elongation after break of the test sample are gradually improved along with the increase of the Mg content, but the mechanical property of the test sample prepared from the alloy is more than 300MPa, the yield strength is more than 150MPa, the elongation after break is more than 5%, the heat conduction property is more than 130W/m.k, and the requirements of the light-weight part of the automobile on the mechanical property and the heat conduction property are met. Can be used for manufacturing parts requiring the motor shell of the new energy automobile and the like.
Example 3
Preparing die casting aluminum alloy with different components, preparing standard sample table 3 according to the aluminum alloy smelting and high-vacuum die casting process of the invention, wherein the die casting aluminum alloy with different components comprises mechanical properties and heat conduction properties (T5 heat treatment state artificial aging temperature is 180+/-5 ℃, heat preservation time is 2 hours, and cooling along with furnace to room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | Tensile strength degree/MPa | Yield strength of degree/MPa | Elongation after break Rate/% | Thermal conductivity W/m.k |
| 1 | 9.5 | 0.05 | 0.2 | 0.12 | 0.6 | 0.55 | 0.034 | 0.023 | Allowance of | 305 | 157 | 7.6 | 141 |
| 2 | 9.9 | 0.03 | 0.25 | 0.15 | 0.8 | 0.58 | 0.038 | 0.027 | Allowance of | 321 | 163 | 6.3 | 140 |
| 3 | 9.7 | 0.01 | 0.30 | 0.13 | 0.6 | 0.65 | 0.039 | 0.021 | Allowance of | 328 | 171 | 5.8 | 141 |
| 4 | 10.2 | 0.02 | 0.35 | 0.17 | 0.6 | 0.61 | 0.039 | 0.022 | Allowance of | 335 | 183 | 5.6 | 137 |
| 5 | 9.8 | 0.03 | 0.4 | 0.15 | 0.6 | 0.57 | 0.039 | 0.028 | Allowance of | 336 | 185 | 5.2 | 138 |
As can be seen from the graph 3, the mechanical properties of the samples prepared by the alloy of the present invention meet the technical requirements, and under the condition that Si and Mg. are relatively low, the samples have a low strength and a high elongation after breaking, but because other elements such as Cu have a high strength, a function of reducing the elongation and Fe has a function of remarkably reducing the strength and the elongation, under the conditions, the mechanical properties of the samples are the lowest, the tensile strength is 300MPa, the yield strength is 150MPa, the elongation after breaking is 5%, and the thermal conductivity exceeds 130W/m.k, so that the mechanical properties and the thermal conductivity of the alloy are ensured, and the content of Cu and Fe needs to be controlled within the required range.
Example 4
The standard die-casting test sample is prepared by adopting common Al-Si-Cu die-casting aluminum alloy ADC12 and A380 and the die-casting aluminum alloy of the invention and using the same process, and the mechanical properties are tested, and the test results are shown in a graph 4:
TABLE 4 comparison of mechanical properties of different alloys (T5 heat treatment artificial aging temperature 180+ -5deg.C, holding time 2 hours, furnace cooling room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | Tensile strength degree/MPa | Yield strength of degree/MPa | Elongation after break Rate/% | Thermal conductivity W/m.k |
| ADC12 | 10.6 | 0.25 | 0.23 | 0.01 | 1.8 | 0.89 | 0.0034 | 0.0023 | Allowance of | 283 | 157 | 2.6 | 91 |
| A380 | 8.9 | 0.23 | 0.25 | 0.02 | 3.3 | 0.88 | 0.0018 | 0.0027 | Allowance of | 311 | 163 | 3.3 | 93 |
| The aluminum of the invention Alloy | 9.7 | 0.01 | 0.30 | 0.13 | 0.6 | 0.65 | 0.039 | 0.021 | Allowance of | 328 | 171 | 5.8 | 141 |
From the graph 4, the novel alloy in the T5 cast state has good mechanical property, strong heat conduction property and better elongation after breaking than the common alloy.
It will be readily understood by those skilled in the art that the foregoing description is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art who is skilled in the art to which the present invention pertains shall be covered by the scope of the present invention.
Claims (7)
1. The novel energy automobile motor shell aluminum alloy is characterized by comprising the following components in percentage by mass: 0.5% -1.5% of Cu, 9% -10.5% of Si, less than or equal to 0.1% of Mn, 0.2% -0.45% of Mg, 0.5% -0.7% of Fe, less than or equal to 0.1% of Zn, 0.015% -0.035% of S, 0.1% -0.35% of Zr, 0.03% -0.15% of RE (La+Ce), and the balance of Al and impurities, wherein the total content of the impurities is not more than 0.25%;
the preparation method of the motor shell aluminum alloy specifically comprises the following steps:
s1, smelting: preparing raw materials according to the percentages of all components in the formula of the aluminum alloy material; each raw material is added into a smelting furnace in sequence respectively, and is stirred uniformly after being heated and melted to obtain alloy melt;
s2, refining: refining the alloy melt obtained in the step S1 to finish degassing and impurity removal;
s3, forming: delivering the alloy melt processed in the step S2 into forming equipment or preparing semi-solid slurry and then forming to obtain an aluminum alloy component;
s4, heat treatment: feeding the aluminum alloy component in the step S3 into a heat treatment furnace for T5 treatment;
the sequence of adding the raw materials into the smelting furnace in the step S1 is as follows: adding an AlSi alloy ingot into a smelting furnace for smelting, adding pure metal or intermediate alloy containing Cu element and Mg element after the AlSi alloy ingot is completely smelted, adding intermediate alloy of AlZr and TCB after the AlSi alloy ingot is completely smelted, and adding intermediate alloy of AlRE and AlSr after the AlSi alloy ingot is completely smelted;
the heat treatment process of the step S4 comprises the following steps: the artificial aging temperature is 180+/-5 ℃, the heat preservation time is 2-4 hours, and the room temperature is cooled along with a furnace; after T5 heat treatment, the tensile strength of the aluminum alloy member is 310-330MPa, the yield strength is 150-185MPa, the elongation after break is 5-7%, and the heat conductivity coefficient is 135-145W/m.k.
2. The method for forming the aluminum alloy for the motor housing of the new energy automobile according to claim 1, wherein in the step S1, the raw materials are firstly dried and preheated, and then the preheated raw materials are respectively added into a smelting furnace in sequence, wherein the preheating and drying temperature is 100-450 ℃, the melting temperature is 700-800 ℃, and the stirring time is 2-15 minutes.
3. The method for forming the aluminum alloy of the motor housing of the new energy automobile according to claim 1, wherein the specific method for refining in the step S2 is as follows: and (3) introducing protective gas into the alloy melt, wherein the refining time is 10-30 minutes, and the introducing amount of the protective gas is 0.05-6L/min.
4. The method for forming the aluminum alloy for the motor housing of the new energy automobile according to claim 3, wherein the shielding gas is nitrogen or argon.
5. The method for forming the aluminum alloy of the motor housing of the new energy automobile according to claim 1, wherein the specific method for refining in the step S2 further comprises the following steps: adding a solid refining agent into the alloy melt, wherein the content of the added solid refining agent is 0.1-0.5% of the mass of the melt, and the refining time is 10-30 minutes.
6. The method for forming the aluminum alloy for the motor housing of the new energy automobile according to claim 1, wherein the tensile strength of the aluminum alloy member prepared in the step S3 is 300-310MPa, the yield strength is 135-150MPa, the elongation after break is 5.5-7%, and the heat conductivity is 125-135W/m.k.
7. The method for forming aluminum alloy for motor housing of new energy automobile as claimed in claim 1, wherein the forming equipment adopted in the step S3 is a die casting machine and a liquid forging machine.
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