CN115537613A - 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
- Publication number
- CN115537613A CN115537613A CN202211295606.3A CN202211295606A CN115537613A CN 115537613 A CN115537613 A CN 115537613A CN 202211295606 A CN202211295606 A CN 202211295606A CN 115537613 A CN115537613 A CN 115537613A
- Authority
- CN
- China
- Prior art keywords
- percent
- aluminum alloy
- alloy
- new energy
- energy automobile
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 60
- 238000000034 method Methods 0.000 title claims abstract description 25
- 239000000956 alloy Substances 0.000 claims abstract description 66
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 61
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 13
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 4
- 238000007670 refining Methods 0.000 claims description 24
- 238000010438 heat treatment Methods 0.000 claims description 21
- 238000003723 Smelting Methods 0.000 claims description 16
- 238000004512 die casting Methods 0.000 claims description 15
- 239000002994 raw material Substances 0.000 claims description 15
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 claims description 14
- 230000032683 aging Effects 0.000 claims description 8
- 239000007789 gas Substances 0.000 claims description 8
- 230000008569 process Effects 0.000 claims description 8
- 230000001681 protective effect Effects 0.000 claims description 8
- 230000008018 melting Effects 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 7
- 239000007787 solid Substances 0.000 claims description 7
- 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
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 238000004321 preservation Methods 0.000 claims description 5
- 238000003756 stirring Methods 0.000 claims description 5
- 238000005242 forging Methods 0.000 claims description 4
- 239000007788 liquid Substances 0.000 claims description 4
- 239000000155 melt Substances 0.000 claims description 4
- 229910017143 AlSr Inorganic materials 0.000 claims description 3
- 229910016952 AlZr Inorganic materials 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 238000007872 degassing Methods 0.000 claims description 3
- 238000001035 drying 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
- 238000005266 casting Methods 0.000 description 9
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 8
- 239000013078 crystal Substances 0.000 description 8
- 210000001787 dendrite Anatomy 0.000 description 8
- 239000010703 silicon Substances 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
- 230000005496 eutectics Effects 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 230000007547 defect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 231100000572 poisoning Toxicity 0.000 description 4
- 230000000607 poisoning effect Effects 0.000 description 4
- 230000018109 developmental process Effects 0.000 description 3
- 239000000203 mixture Substances 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
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000001125 extrusion Methods 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
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000006104 solid solution Substances 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
- 229910018594 Si-Cu Inorganic materials 0.000 description 1
- 229910008465 Si—Cu Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 239000006185 dispersion Substances 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
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 235000015112 vegetable and seed oil Nutrition 0.000 description 1
- 239000008158 vegetable oil Substances 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Images
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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Extrusion Of Metal (AREA)
Abstract
The invention relates to a new energy automobile motor shell aluminum alloy and a forming method thereof, wherein the aluminum alloy comprises the following components in percentage by mass: 0.5 to 1.5 percent of Cu0.5 percent, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg0.5, 0.5 to 0.7 percent of Fe0.1 percent, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of Sr0.1 to 0.35 percent of Zr0.03 percent, 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 property, further improves the strength, 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 requirements on the performance of materials for automobiles and aerospace are more severe. In addition, due to social pressure of energy conservation, emission reduction, environmental pollution and the like, light weight is required as a development strategy. Therefore, in the automobile and aerospace industries, higher strength is required for part design, and high elongation and excellent impact toughness are required for deformation in order to achieve the weight reduction. The first-generation die-casting aluminum alloy material of the existing automobile motor shell is ADC12 and A380, wherein the tensile strength is 280-310MPa, the yield strength is 130-180MPa, the toughness is poor (the elongation after fracture is less than 3.5%), the heat conduction performance is only 90W/m.k, the mechanical property and the heat conduction performance of the new energy automobile motor shell can not be met far, a brand-new material needs to be developed urgently, the final mechanical property is that the tensile strength is more than or equal to 300MPa under artificial aging strengthening, the yield strength is more than or equal to 150MPa, the elongation after fracture is more than or equal to 5%, the heat conduction performance 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 new energy automobile motor shell aluminum alloy has been greatly advanced in recent years, further breakthrough is still needed in the aspects of cost reduction (the proportion ratio selection of recycled aluminum instead of electrolytic aluminum), high strength and high toughness, mutual contradiction between high heat conductivity and forming capability improvement and the like, so that high-strength and high-heat conductivity automobile parts represented by new energy automobile motor shells are developed.
Disclosure of Invention
In order to overcome the defects of the existing ADC12 and A380 aluminum alloys and further improve the strength, toughness and heat conductivity of the alloys, the invention provides the new energy automobile motor shell aluminum alloy and the forming method thereof.
The invention adopts the following technical scheme: the aluminum alloy for the motor shell of the new energy automobile comprises the following components in percentage by mass: 0.5 to 1.5 percent of Cu0.5 percent, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg0.5, 0.5 to 0.7 percent of Fe0.1 percent, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of Sr0.1 to 0.35 percent of Zr0.03 percent, 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 aluminum alloy of the motor shell of the new energy automobile, which is characterized by comprising the following steps:
s1, smelting: preparing raw materials according to the percentage of each component in the formula of the aluminum alloy material; adding the raw materials into a smelting furnace in sequence, and stirring uniformly after heating and melting to obtain an alloy melt;
s2, refining: refining the alloy melt obtained in the step S1 to complete degassing and impurity removal;
s3, forming: sending the alloy melt processed in the step S2 into a forming device or forming after preparing semisolid slurry to obtain an aluminum alloy component;
s4, heat treatment: and (5) conveying the aluminum alloy component in the S3 into a heat treatment furnace for T5 treatment.
In the step S1, the raw materials are 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.
In the step S1, the sequence of adding the raw materials into the smelting furnace is as follows: adding an AlSi alloy ingot into a smelting furnace for melting, adding pure metal or intermediate alloy containing Cu and Mg after the AlSi alloy ingot is completely melted, adding AlZr and TCB intermediate alloy after the AlSi alloy ingot is completely melted, and adding AlRE and AlSr intermediate alloy after the AlSi alloy ingot is completely melted.
The refining treatment in the step S2 comprises the following specific steps: and introducing protective gas into the alloy melt, wherein the refining time is 10-30 minutes, and the introduction amount of the protective gas is 0.05-6L/min. The protective gas is nitrogen or argon.
The refining treatment in step S2 may further include: 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 member 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 the 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 fracture is 5-7%, and the heat conductivity coefficient is 135-145W/m.k.
And the forming equipment adopted in the step S3 is a die casting machine and a liquid die forging machine.
Compared with the prior art, the invention has the following advantages:
(1) The invention adds TCB crystal seed alloy, adopts a new mechanism of direct crystal seed nucleation, eliminates the thinning poisoning origin caused by Si element, realizes the double effects of fine crystal strengthening and interface coherent strengthening, and fundamentally solves a plurality of defects caused by coarse alpha-Al dendrites in the eutectic AlSi alloy.
(2) Strontium is used for modifying and refining eutectic silicon, zr element is added to achieve the purpose of synchronously modifying and refining, crystal grains and the eutectic silicon are obviously refined, solid solution strengthening brought by Cu and Mg elements is combined, the alloy is endowed with excellent mechanical property, and in addition, trace rare earth elements are added to endow the alloy with good corrosion resistance and heat conductivity.
(3) In the aluminum alloy raw material proportion, the addition amount of the secondary aluminum is fifty percent, 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 die-casting and T5 heat treatment.
FIG. 2 shows the microstructure of the aluminum alloy after T5 heat treatment and tensile fracture after die-casting.
Detailed Description
The invention is further described below in conjunction with specific embodiments, and the advantages and features of the invention will become more apparent as the description proceeds. These examples are illustrative only and do not limit the scope of the present invention in any way. It will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention, and that such changes and substitutions are intended to be within the scope of the invention.
The new energy automobile motor shell aluminum alloy comprises the following components in percentage by mass: 0.5 to 1.5 percent of Cu0.5 percent, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg0.5, 0.5 to 0.7 percent of Fe0.1 percent, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of Sr0.1 to 0.35 percent of Zr0.03 percent, 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 alpha-Al dendrites of the alloy casting are coarse, and the coarse alpha-Al dendrites bring a plurality of problems: for example, the casting has the defects of shrinkage porosity, snow spots, segregation and the like, and the tissue compactness and the product consistency are poor. In addition, the coarse alpha-Al dendrites also obviously reduce the toughness of the aluminum alloy casting, and particularly have poor fatigue performance. However, the traditional Al-Ti-B/Al-Ti-C intermediate alloy is difficult to refine the Al-Si series alloy, and the fundamental reason is that Si element causes refining poisoning.
The invention adds TCB crystal seed alloy, provides a new mechanism of direct crystal seed nucleation, not only avoids the coarseness of alpha-Al dendrite, but also solves a plurality of problems caused by the coarseness of alpha-Al dendrite, eliminates the origin of poisoning, and realizes the double effects of fine crystal strengthening and interface coherent strengthening.
The new 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 ℃, then respectively adding each raw material into a smelting furnace in sequence, heating to 700-800 ℃, and stirring for 2-15 minutes to homogenize melt components to obtain the aluminum alloy melt.
The addition sequence of various raw materials is as follows: adding an AlSi alloy ingot into a smelting furnace for melting, adding pure metal or intermediate alloy containing Cu and Mg after the AlSi alloy ingot is completely melted, adding AlZr and TCB intermediate alloy after the AlSi alloy ingot is completely melted, and adding AlRE and AlSr intermediate alloy after the AlSi alloy ingot is completely melted.
S2, refining: and (3) introducing protective gas or a solid refining agent into the alloy melt, wherein the refining time is 10-30 minutes, so that degassing and impurity removal are carried out on the melt.
The protective gas is nitrogen or argon, the input amount is 0.05-6L/min, and the content of the added solid refining agent is 0.1-0.5% of the melt mass.
S3, forming: and (3) feeding the refined alloy melt into a forming device or forming after preparing semisolid slurry to obtain the aluminum alloy component.
The forming process of the high-strength high-conductivity aluminum alloy comprises die casting and liquid die forging.
The tensile strength of the aluminum alloy member is 300-310MPa, the yield strength is 135-150MPa, the elongation after fracture is 5.5-7%, and the thermal conductivity is 125-135W/m.k.
S4, heat treatment: the formed aluminum alloy member is sent to a heat treatment furnace for T5 treatment.
The heat treatment process is characterized in that the working efficiency temperature is 180 +/-5 ℃, the heat preservation time is 2-4 hours, and the temperature is cooled along with the furnace to room temperature.
After T5 heat treatment, the tensile strength of the aluminum alloy member is 310-330MPa, the yield strength is 150-185MPa, the elongation after fracture is 5-7%, and the heat conductivity coefficient is 135-145W/m.k.
The forming of the aluminum alloy of the invention refines crystal grains by utilizing the vanadization treatment, refines eutectic silicon by utilizing the modification of strontium, avoids the thick alpha-Al dendrite due to the addition of TCB, and solves a plurality of problems caused by the thick alpha-Al dendrite: for example, the defects of shrinkage porosity, snow spots, segregation and the like are generated on the casting, the tissue compactness and the product consistency are poor, and meanwhile, the obdurability, especially the fatigue performance, of the aluminum alloy casting is also obviously reduced. The Al-Si series alloy is difficult to refine in the traditional Al-Ti-B/Al-Ti-C intermediate alloy, the fundamental reason is that Si element causes refining poisoning, the invention combines solid solution strengthening and dispersion strengthening simultaneously to endow the alloy with excellent mechanical property, the prepared alloy has good fluidity and excellent casting property, and can be applied to forming modes such as high-pressure casting, semi-solid extrusion casting, liquid die forging (extrusion casting) and the like, and the application prospect is wide.
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 of the invention, and measuring to obtain the mechanical properties of different silicon contents, wherein the mechanical properties are shown in a chart 1:
TABLE 1 die-casting aluminum alloy compositions with different silicon contents, mechanical properties and heat conductivity (T5 heat treatment state, artificial aging temperature of 180 +/-5 ℃, heat preservation time of 2 hours, furnace cooling room temperature).
TABLE 1 composition, mechanical properties and thermal conductivity of die-cast aluminum alloys of different Si contents (T5 heat treatment state, artificial aging temperature of 180 + -5 deg.C, holding time of 2 hours, furnace cooling room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | High tensile strength degree/MPa | Yield strength- MPa | After fracture Elongation of Ratio- ％ | Heat-conducting property W- m.k |
| 1 | 9 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 310 | 160 | 6.5 | 135 |
| 2 | 9.5 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 318 | 165 | 6.2 | 142 |
| 3 | 10.0 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 323 | 171 | 5.7 | 145 |
| 4 | 10.5 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 328 | 182 | 5.3 | 139 |
From the graph 1, it can be seen that as the content of silicon increases, the tensile strength and the yield strength of the sample gradually increase, and the elongation after fracture decreases, but the mechanical property of the sample prepared from the alloy meets the requirements of the new energy automobile motor shell component on the mechanical property and the heat conductivity, wherein the yield strength of the sample is more than 310MPa, the yield strength of the sample is more than 150MPa, the elongation after fracture exceeds 5%, and the heat conductivity of the sample exceeds 130W/m.k. The metallographic structure of the sample is as shown in fig. 1, the structure is compact, the primary aluminum matrix is fine and is uniformly distributed, the eutectic Si phase is fine and is uniformly distributed in the primary aluminum matrix, and the requirements of the metallographic structure of parts such as a new energy automobile motor shell and the like are met. The fracture structure of the sample is shown in figure 2, tiny and obvious fossa is distributed, and obvious plastic deformation is presented.
Example 2
Die-casting aluminum alloys with different Mg contents were prepared, standard samples were prepared according to the aluminum alloy melting and high vacuum die-casting process of the present invention using the above prepared alloys with different Mg contents, and the mechanical properties of different Mg contents were measured as shown in Table 2:
TABLE 2 die-casting aluminum alloy compositions with different Mg contents, mechanical properties and thermal conductivity (artificial aging temperature 180 + -2 deg.C, holding time 2 hours, furnace cooling room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | High tensile strength degree/MPa | Yield strength- MPa | After fracture Elongation of Ratio- ％ | Heat-conducting property W- m.k |
| 1 | 9.5 | 0.05 | 0.2 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 305 | 157 | 7.8 | 141 |
| 2 | 9.5 | 0.05 | 0.25 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 318 | 165 | 6.2 | 142 |
| 3 | 9.5 | 0.05 | 0.30 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 325 | 175 | 5.9 | 141 |
| 4 | 9.5 | 0.05 | 0.35 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 331 | 183 | 5.5 | 135 |
| 5 | 9.5 | 0.05 | 0.4 | 0.15 | 0.6 | 0.55 | 0.039 | 0.025 | Balance of | 338 | 187 | 5.2 | 139 |
From the graph 2, it can be seen that the tensile strength and yield strength of the sample are gradually improved and the elongation after fracture is reduced with the increase of the Mg content, but the mechanical property of the sample prepared from the alloy is more than 300MPa, the yield strength is more than 150MPa, the elongation after fracture is more than 5%, the heat conductivity is more than 130W/m.k, and the requirements of lightweight automobile parts on the mechanical property and the heat conductivity are met. The method can be used for manufacturing parts such as a motor shell of a new energy automobile and the like.
Example 3
Preparing die-casting aluminum alloys with different components, preparing standard samples according to the aluminum alloy smelting and high vacuum die-casting process of the invention, wherein the components, the mechanical properties and the heat conductivity of the die-casting aluminum alloys with different component contents are shown in the table 3 (T5 heat treatment state artificial aging temperature is 180 +/-5 ℃, the heat preservation time is 2 hours, furnace cooling room temperature)
| Yuan Vegetable oil | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | Tensile strength Intensity- MPa | Yield and yield Strength- MPa | Elongation after fracture Rate/% of | Heat-conducting property 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 | Balance of | 321 | 163 | 6.3 | 140 |
| 3 | 9.7 | 0.01 | 0.30 | 0.13 | 0.6 | 0.65 | 0.039 | 0.021 | Balance of | 328 | 171 | 5.8 | 141 |
| 4 | 10.2 | 0.02 | 0.35 | 0.17 | 0.6 | 0.61 | 0.039 | 0.022 | Balance 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 fig. 3, the mechanical properties of the sample prepared by using the alloy of the present invention all satisfy the technical requirements, and in the case of relatively low Si and mg, the sample has a tendency of low strength and high elongation after fracture, but because other elements such as Cu have the effects of increasing strength and decreasing elongation and Fe has the effects of significantly decreasing strength and elongation, under such conditions, the mechanical properties of the sample are the lowest, the tensile strength is 300MPa, the yield strength is 150MPa, the elongation after fracture 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 mechanical properties were measured using conventional Al-Si-Cu series die cast aluminum alloys ADC12 and a380, and the die cast aluminum alloy of the present invention, and standard die cast specimens prepared by the same process, and the results are shown in table 4:
TABLE 4 comparison table of mechanical properties of different alloys (T5 heat treatment state artificial aging temperature is 180 + -5 deg.C, holding time is 2 hours, furnace cooling room temperature)
| Element(s) | Si | Mn | Mg | Zr | Cu | Fe | RE | Sr | Al | Tensile strength Intensity- MPa | Yield and yield Intensity- MPa | Elongation after fracture Rate/%) | Heat-conducting property W/m.k |
| ADC12 | 10.6 | 0.25 | 0.23 | 0.01 | 1.8 | 0.89 | 0.003 4 | 0.0023 | Allowance of | 283 | 157 | 2.6 | 91 |
| A380 | 8.9 | 0.23 | 0.25 | 0.02 | 3.3 | 0.88 | 0.001 8 | 0.0027 | Allowance of | 311 | 163 | 3.3 | 93 |
| The invention Aluminium alloy | 9.7 | 0.01 | 0.30 | 0.13 | 0.6 | 0.65 | 0.039 | 0.021 | Balance of | 328 | 171 | 5.8 | 141 |
As can be seen from the graph 4, the new alloy in the T5 as-cast state has good mechanical properties and thermal conductivity and elongation after fracture superior to those of the common alloy.
It is easily understood by those skilled in the art that the above 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 can substitute or change the technical solution of the present invention and the inventive concept thereof within the technical scope of the present invention.
Claims (10)
1. The aluminum alloy for the motor shell of the new energy automobile is characterized by comprising the following components in percentage by mass: 0.5 to 1.5 percent of Cu0.5 percent, 9 to 10.5 percent of Si, less than or equal to 0.1 percent of Mn, 0.2 to 0.45 percent of Mg0.5, 0.5 to 0.7 percent of Fe0.1 percent, less than or equal to 0.1 percent of Zn, 0.015 to 0.035 percent of Sr0.1 to 0.35 percent of Zr0.03 percent, 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.
2. The forming method of the aluminum alloy for the motor shell of the new energy automobile as claimed in claim 1, characterized by comprising the following steps:
s1, smelting: preparing raw materials according to the percentage of each component in the formula of the aluminum alloy material; adding the raw materials into a smelting furnace in sequence, and uniformly stirring after heating and melting to obtain an alloy melt;
s2, refining: refining the alloy melt obtained in the step S1 to complete degassing and impurity removal;
s3, forming: sending the alloy melt processed in the step S2 into a forming device or forming after preparing semisolid slurry to obtain an aluminum alloy component;
s4, heat treatment: and (5) conveying the aluminum alloy component in the S3 into a heat treatment furnace for T5 treatment.
3. The method for forming the aluminum alloy of the motor shell of the new energy automobile as claimed in claim 2, wherein in the step S1, the raw materials are 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.
4. The method for forming the aluminum alloy of the motor shell of the new energy automobile as claimed in claim 2, wherein 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 and Mg after the AlSi alloy ingot is completely smelted, adding an AlZr and TCB intermediate alloy after the AlSi alloy ingot is completely smelted, and adding an AlRE and AlSr intermediate alloy after the AlSi alloy ingot is completely smelted.
5. The forming method of the aluminum alloy for the motor shell of the new energy automobile as claimed in claim 2, wherein the refining treatment in step S2 is specifically: and introducing protective gas into the alloy melt, wherein the refining time is 10-30 minutes, and the introduction amount of the protective gas is 0.05-6L/min.
6. The forming method of the aluminum alloy for the motor shell of the new energy automobile as claimed in claim 5, wherein the protective gas is nitrogen or argon.
7. The method for forming the aluminum alloy of the motor shell of the new energy automobile according to claim 2, wherein the refining treatment in the step S2 is further specifically: 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.
8. The forming method of the aluminum alloy for the motor shell of the new energy automobile as claimed in claim 2, wherein the aluminum alloy member prepared in the step S3 has a tensile strength of 300-310MPa, a yield strength of 135-150MPa, an elongation after fracture of 5.5-7% and a thermal conductivity of 125-135W/m.k.
9. The forming method of the aluminum alloy for the motor shell of the new energy automobile according to claim 5, wherein the heat treatment process in the step S4 is as follows: the artificial aging temperature is 180 +/-5 ℃, the heat preservation time is 2-4 hours, and the room temperature is cooled along with the 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 fracture is 5-7%, and the heat conductivity coefficient is 135-145W/m.k.
10. The method for forming the aluminum alloy of the motor shell of the new energy automobile according to claim 2, wherein the forming equipment adopted in the step S3 is a die casting machine and a liquid forging machine.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211295606.3A CN115537613B (en) | 2022-10-21 | 2022-10-21 | New energy automobile motor shell aluminum alloy and forming method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211295606.3A CN115537613B (en) | 2022-10-21 | 2022-10-21 | New energy automobile motor shell aluminum alloy and forming method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115537613A true CN115537613A (en) | 2022-12-30 |
| CN115537613B CN115537613B (en) | 2023-09-15 |
Family
ID=84734828
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211295606.3A Active CN115537613B (en) | 2022-10-21 | 2022-10-21 | New energy automobile motor shell aluminum alloy and forming method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115537613B (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115852214A (en) * | 2023-02-27 | 2023-03-28 | 南通鸿劲金属铝业有限公司 | Heat-treatable reinforced high-strength and high-toughness aluminum alloy and preparation method thereof |
| CN117821813A (en) * | 2024-03-04 | 2024-04-05 | 鸿劲新材料研究(南通)有限公司 | Aluminum alloy material for auxiliary frame of automobile and preparation method |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110343916A (en) * | 2019-08-19 | 2019-10-18 | 北京科技大学 | High thermal conductivity aluminium alloy suitable for rheo-diecasting and preparation method thereof and forming technology |
| US20210207249A1 (en) * | 2018-05-30 | 2021-07-08 | Byd Company Limited | Aluminum alloy and preparation method and application thereof |
| CN114540672A (en) * | 2022-02-22 | 2022-05-27 | 南通鸿劲金属铝业有限公司 | High-strength high-thermal-conductivity AlSi aluminum alloy and preparation method thereof |
| CN114717455A (en) * | 2022-04-20 | 2022-07-08 | 北京车和家汽车科技有限公司 | Heat treatment-free high-strength and high-toughness die-casting aluminum alloy and preparation method thereof |
| CN114908275A (en) * | 2022-06-08 | 2022-08-16 | 广东省科学院新材料研究所 | Heat-treatment-free high-strength and high-toughness die-casting aluminum alloy, and preparation method and application thereof |
-
2022
- 2022-10-21 CN CN202211295606.3A patent/CN115537613B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20210207249A1 (en) * | 2018-05-30 | 2021-07-08 | Byd Company Limited | Aluminum alloy and preparation method and application thereof |
| CN110343916A (en) * | 2019-08-19 | 2019-10-18 | 北京科技大学 | High thermal conductivity aluminium alloy suitable for rheo-diecasting and preparation method thereof and forming technology |
| CN114540672A (en) * | 2022-02-22 | 2022-05-27 | 南通鸿劲金属铝业有限公司 | High-strength high-thermal-conductivity AlSi aluminum alloy and preparation method thereof |
| CN114717455A (en) * | 2022-04-20 | 2022-07-08 | 北京车和家汽车科技有限公司 | Heat treatment-free high-strength and high-toughness die-casting aluminum alloy and preparation method thereof |
| CN114908275A (en) * | 2022-06-08 | 2022-08-16 | 广东省科学院新材料研究所 | Heat-treatment-free high-strength and high-toughness die-casting aluminum alloy, and preparation method and application thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115852214A (en) * | 2023-02-27 | 2023-03-28 | 南通鸿劲金属铝业有限公司 | Heat-treatable reinforced high-strength and high-toughness aluminum alloy and preparation method thereof |
| CN117821813A (en) * | 2024-03-04 | 2024-04-05 | 鸿劲新材料研究(南通)有限公司 | Aluminum alloy material for auxiliary frame of automobile and preparation method |
| CN117821813B (en) * | 2024-03-04 | 2024-04-26 | 鸿劲新材料研究(南通)有限公司 | Aluminum alloy material for auxiliary frame of automobile and preparation method |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115537613B (en) | 2023-09-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5383916B2 (en) | High-strength multi-element heat-resistant aluminum alloy material and preparation method thereof | |
| CN115537613A (en) | New energy automobile motor shell aluminum alloy and forming method thereof | |
| CN111690849A (en) | Refining method of iron-rich phase in Al-Si series die-casting aluminum alloy and alloy | |
| CN111349821A (en) | Low-silicon low-iron high-fluidity high-thermal-conductivity die-casting aluminum alloy and preparation method thereof | |
| CN115852214B (en) | High-strength and high-toughness aluminum alloy capable of being strengthened by heat treatment and preparation method thereof | |
| CN113174516B (en) | Scandium-containing high-strength high-toughness aluminum-silicon alloy and preparation process thereof | |
| CN112941377B (en) | Er-containing cast heat-resistant Al-Si-Cu-Mg alloy | |
| CN112921209B (en) | Ultrahigh-heat-conductivity high-plasticity medium-strength aluminum alloy and preparation method thereof | |
| CN115261683B (en) | Water quenching-free high-strength and high-toughness cast Al-Si alloy and preparation method thereof | |
| CN117568671B (en) | Die-casting aluminum alloy material free of heat treatment, preparation method thereof and automobile structural member | |
| CN110079711A (en) | Heat-resisting high-pressure casting Al-Si-Ni-Cu aluminium alloy and preparation method | |
| CN112626401A (en) | 2XXX series aluminum alloy and preparation method thereof | |
| CN115961186A (en) | Die-casting aluminum alloy material and preparation method and application thereof | |
| CN112779443A (en) | Aluminum alloy and aluminum alloy structural part | |
| CN110819863B (en) | Low-rare earth high-thermal conductivity magnesium alloy and preparation method thereof | |
| CN114015914A (en) | High-strength high-thermal-conductivity die-casting aluminum alloy material and preparation method thereof | |
| CN115433857A (en) | Lightweight aluminum-silicon alloy with good plasticity and preparation process thereof | |
| CN113481395A (en) | Composite treatment method for improving thermal conductivity of cast Al-Si alloy | |
| CN116590583A (en) | High-strength and high-toughness cast aluminum alloy material and preparation method thereof | |
| WO2020052129A1 (en) | Rare-earth aluminum alloy material having high ductility and high strength and preparation method therefor | |
| CN114836656A (en) | High-strength high-heat-conductivity die-casting aluminum alloy capable of being strengthened by aging and preparation method thereof | |
| CN115029593A (en) | Composite rare earth-added heat-resistant aluminum alloy and preparation method thereof | |
| CN114686735A (en) | Wrought aluminum alloy with gradient structure and preparation method thereof | |
| CN111705248A (en) | Al-4.5Cu aluminum-copper alloy material and preparation method thereof | |
| CN117488148B (en) | Cast aluminum alloy and preparation method and application thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20231225 Address after: 226000, No. 116 Jinqiao West Road, High tech Industrial Development Zone, Nantong City, Jiangsu Province Patentee after: Hongjin New Materials Research (Nantong) Co.,Ltd. Address before: 226300 Jinqiao Road, Tongzhou Development Zone, Nantong City, Jiangsu Province Patentee before: NANTONG HONGJIN METAL ALUMINUM INDUSTRY CO.,LTD. |
|
| TR01 | Transfer of patent right |