CN114318042A - Carbon nano tube reinforced cast ZL105 alloy material and preparation method thereof - Google Patents
Carbon nano tube reinforced cast ZL105 alloy material and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a carbon nanotube reinforced cast ZL105 alloy material and a preparation method thereof, wherein ZL105 raw materials are mixed and heated to 820-840 ℃ until being melted to obtain a ZL105 alloy molten mass; then cooling to 570-590 ℃, and adding a carbon nano tube to obtain a carbon nano tube ZL105 alloy molten mass; heating the carbon nano tube ZL105 alloy melt to 760 ℃ to ensure that the molten alloy is completely in a liquid state, deslagging, standing, casting and cooling to obtain the carbon nano tube ZL105 alloy material; and then carrying out heat treatment on the carbon nano tube ZL105 alloy material to obtain a finished product. The method adopts specific raw material proportion and adjusts the processing technology, further improves the uniform dispersion degree and the interface bonding property of the carbon nano tube in the metal matrix at the later stage, has simple whole preparation method and short flow, and obtains the carbon nano tube reinforced cast ZL105 alloy material with good interface bonding and better mechanical property.
Description
Technical Field
The invention relates to the technical field of reinforced aluminum alloy, in particular to a carbon nano tube reinforced cast ZL105 alloy material and a preparation method thereof.
Background
The aluminum alloy material is widely used for various forming parts such as casting, forging and the like due to the characteristics of low density, good specific strength and the like. Carbon nanotubes have been widely used as reinforcements of aluminum matrix composites, and CNTs-Al composites having better properties than aluminum matrix materials can be prepared by in-situ synthesis, friction stir, and other methods. For example, the yield strength of the composite material is improved by preparing the carbon nanotube reinforced 2024 Al-based composite material by a powder metallurgy method, and the tensile strength of the material is improved and the elastic modulus is greatly improved by preparing the CNTs-Al composite material by a sandwich technology. However, these forming methods have certain limitations, and cannot be adapted to parts with complex shapes or cavities. The stirring melting casting method has the advantages of mature method, convenient operation and the like, can prepare various parts with complex cavities which meet the requirements of industrial production, but has the problems of poor interface wettability, poor dispersibility and the like of the carbon nano tube and the aluminum-based alloy, and easily has the problems of non-uniform dispersion of the carbon nano tube and poor interface bonding of the carbon nano tube and a metal matrix by adopting the melting casting method. Therefore, the wettability and the dispersibility of the carbon nanotubes in the matrix need to be changed to increase the bonding area and the bonding force of the composite material interface, so as to improve the performance of the composite material.
Disclosure of Invention
In view of the above, the present invention aims to provide a carbon nanotube reinforced cast ZL105 alloy material with good interface bonding between a carbon nanotube and a metal matrix and excellent mechanical properties, and a preparation method thereof.
According to one aspect of the present invention, there is provided a method for preparing a carbon nanotube reinforced cast ZL105 alloy material, comprising the steps of:
s1, preparing ZL105 alloy melt: mixing solid raw materials of aluminum, copper, magnesium and silicon, heating to 820-840 ℃ until the solid raw materials are molten, stirring and refining for 20-25 min to obtain ZL105 alloy molten mass;
s2, preparing a carbon nano tube ZL105 alloy molten body: cooling the ZL105 alloy molten mass to 570-590 ℃, adding carbon nanotubes into the ZL105 alloy molten mass, and stirring and refining for 5-8 min to obtain the carbon nanotube ZL105 alloy molten mass;
s3, heating and smelting: heating the carbon nano tube ZL105 alloy molten mass to 760 ℃ to ensure that the molten alloy is completely in a liquid state, adding a deslagging agent to remove slag, and standing for 20 min;
s4, casting molding: pouring the carbon nano tube ZL105 alloy molten body after deslagging into a mould, and cooling to obtain a carbon nano tube ZL105 alloy material;
s5, heat treatment: and (4) performing heat treatment on the carbon nanotube ZL105 alloy material obtained in the step S4 to obtain a final carbon nanotube reinforced cast ZL105 alloy material.
Further, the heat treatment in step S5 includes the steps of:
s51, carrying out solid solution treatment on the carbon nano tube ZL105 alloy material, wherein the temperature of the solid solution treatment is 520-530 ℃, and the time is 4 hours;
s52, carrying out hot water quenching treatment on the carbon nano tube ZL105 alloy material subjected to the solution treatment, wherein the temperature of the hot water quenching treatment is 80 ℃, and the time is 2 hours;
s53, carrying out artificial aging treatment on the carbon nano tube ZL105 alloy material subjected to hot water quenching treatment, wherein the temperature of the artificial aging treatment is 180 ℃, and the time is 4 hours.
As a preferable mode, the raw materials in the step S1 are in the following weight percentage: 1.0 to 1.5 wt% of copper, 5.0 to 5.5 wt% of silicon, 0.5 to 0.6 wt% of magnesium, and the balance of aluminum.
As a preferable mode, the raw materials in the step S1 are in the following weight percentage: 1.3 wt% of copper, 5.2 wt% of silicon, 0.6 wt% of magnesium and the balance of aluminum.
Preferably, the amount of the carbon nanotubes added in the step S2 is 0.5 to 1.5 wt% of the total mass of the ZL105 alloy melt.
Preferably, the amount of the carbon nanotubes added in the step S2 is 0.75 to 1.25 wt% of the total mass of the ZL105 alloy melt.
In a preferable mode, the diameter of the carbon nanotube in step S2 is 30-80 nm, and the length is less than 10 um.
In a preferable mode, the diameter of the carbon nanotube in step S2 is 5-15 nm, and the length is 10-30 um.
Further, nitrogen gas was introduced to exclude air during the agitation refining at steps S1 and S2.
According to another aspect of the present invention, there is provided a carbon nanotube-reinforced cast ZL105 alloy material, which is prepared by the above method for preparing a carbon nanotube-reinforced cast ZL105 alloy material.
The invention has the beneficial effects that: the invention uses ZL105 aluminum alloy as a carrier, and adopts a stirring casting method to prepare the carbon nano tube reinforced aluminum matrix composite material in a molten state. Firstly, raw materials of components of ZL105 aluminum alloy are subjected to high-temperature smelting, then are cooled to a certain temperature, are added with carbon nano tubes and are stirred and smelted, and then are subjected to heating smelting. The invention can further improve the uniform dispersion degree of the carbon nano tube in the metal matrix and the interface bonding property of the carbon nano tube and the ZL105 alloy matrix in the later period by adopting a specific raw material proportion adjusting and processing process. The whole preparation method is simple, the flow is short, the carbon nano tube can be uniformly dispersed in the ZL105 alloy matrix, and the carbon nano tube reinforced cast ZL105 alloy material with good interface combination of the carbon nano tube and the ZL105 alloy matrix and better mechanical property is obtained.
Drawings
Fig. 1 is a process flow diagram of a method for preparing a carbon nanotube reinforced cast ZL105 alloy material according to an embodiment of the present invention;
FIG. 2 is a graph showing the change in tensile strength of samples No. 0 to No. 10;
FIG. 3 is a graph showing the change in elongation of samples No. 0 to No. 10;
FIG. 4 is a graph showing the hardness change curves of samples No. 0 to No. 10;
FIG. 5 is a metallographic structure morphology chart of a tensile strength change curve chart of samples No. 0, 4, 5, 9 and 10;
FIG. 6 is a fracture morphology diagram of samples No. 0, 4, 5, 9 and 10;
FIG. 7 is a partial magnified view of the fracture morphology of sample 9;
FIG. 8 is a scanning electron micrograph and an EDS of sample 9 cut thin;
FIG. 9 is a transmission electron microscope at point E of sample 9.
Detailed Description
Example 1
Fig. 1 schematically shows a process flow of a method for preparing a carbon nanotube reinforced cast ZL105 alloy material according to an embodiment of the present invention.
Referring to fig. 1, a method for preparing a carbon nanotube reinforced cast ZL105 alloy material includes the following steps:
s1, preparing ZL105 alloy melt: mixing solid raw materials of aluminum, copper, magnesium and silicon, heating to 820-840 ℃, introducing nitrogen to isolate air after all the components are melted, and stirring and refining for 20-25 min to obtain a ZL105 alloy molten mass;
wherein the solid raw materials comprise the following components in percentage by weight: 1.0 to 1.5 wt% of copper, 5.0 to 5.5 wt% of silicon, 0.5 to 0.6 wt% of magnesium, and the balance of aluminum.
S2, preparing a carbon nano tube ZL105 alloy molten body: cooling the ZL105 alloy molten mass to 570-590 ℃, adding carbon nano tubes into the ZL105 alloy molten mass, introducing nitrogen to isolate air, and continuously stirring and refining for 5-8 min to obtain the carbon nano tube ZL105 alloy molten mass; the addition amount of the carbon nano tube is 0.5-1.5 wt% of the total mass of the ZL105 alloy melt, and preferably 0.75-1.25 wt% of the total mass of the ZL105 alloy melt.
S3, heating and smelting: heating the carbon nano tube ZL105 alloy molten mass to 760 ℃ to ensure that the molten alloy is completely in a liquid state, adding a deslagging agent to remove slag, and standing for 20 min;
s4, casting molding: pouring the carbon nano tube ZL105 alloy molten body after deslagging into a mould, and cooling to obtain a carbon nano tube ZL105 alloy material;
s5, heat treatment: and (4) performing heat treatment on the carbon nanotube ZL105 alloy material obtained in the step S4 to obtain a final carbon nanotube reinforced cast ZL105 alloy material. The heat treatment specifically comprises the following steps:
s51, carrying out solid solution treatment on the carbon nano tube ZL105 alloy material, wherein the temperature of the solid solution treatment is 520-530 ℃, and the time is 4 hours;
s52, carrying out hot water quenching treatment on the carbon nano tube ZL105 alloy material subjected to the solution treatment, wherein the temperature of the hot water quenching treatment is 80 ℃, and the time is 2 hours;
s53, carrying out artificial aging treatment on the carbon nano tube ZL105 alloy material subjected to hot water quenching treatment, wherein the temperature of the artificial aging treatment is 180 ℃, and the time is 4 hours.
Example 2
The preparation method of the carbon nanotube reinforced cast ZL105 alloy material comprises the following steps:
s1, preparing ZL105 alloy melt: putting solid raw materials of aluminum, copper, magnesium and silicon into a graphite crucible, closing a furnace cover, adjusting the temperature to 830 ℃, heating and smelting, introducing nitrogen to isolate air after all the components are molten, and stirring and refining for 20min to obtain ZL105 alloy molten mass;
the raw materials comprise the following components in percentage by weight: 1.3 wt% of copper, 5.2 wt% of silicon, 0.6 wt% of magnesium and the balance of aluminum.
S2, cooling the ZL105 alloy molten mass to 580 ℃, adding carbon nano tubes into the ZL105 alloy molten mass, introducing nitrogen to isolate air, and continuously stirring and refining for 5min to obtain the carbon nano tube ZL105 alloy molten mass.
S3, heating the carbon nano tube ZL105 alloy molten mass to 760 ℃ to enable the molten alloy to be completely in a liquid state, adding a deslagging agent to remove slag, and standing for 20 min;
s4, pouring the carbon nano tube ZL105 alloy molten mass after deslagging into a mold preheated to 200-300 ℃, and cooling the mold by air for one minute to obtain a test bar mold of the carbon nano tube ZL105 alloy material; and intercepting the experiment sample which is required by the experiment and accords with the national standard GB/T228.1-2010.
And S5, carrying out heat treatment on the carbon nanotube ZL105 alloy material obtained in the step S4 to obtain a final carbon nanotube reinforced cast ZL105 alloy material. The heat treatment specifically comprises the following steps:
s51, carrying out solution treatment on the carbon nano tube ZL105 alloy material, wherein the temperature of the solution treatment is 525 ℃ and the time is 4 hours;
s52, carrying out hot water quenching treatment on the carbon nano tube ZL105 alloy material subjected to the solution treatment, wherein the temperature of the hot water quenching treatment is 80 ℃, and the time is 2 hours;
s53, carrying out artificial aging treatment on the carbon nano tube ZL105 alloy material subjected to hot water quenching treatment, wherein the temperature of the artificial aging treatment is 180 ℃, and the time is 4 hours.
Carbon nanotubes with different length-diameter ratios and different content length-diameter ratios are prepared by the following steps: CNTs1, the pipe diameter is 5-15 nm, and the length is 10-30 um; CNTs2, the tube diameter is 30-80 nm, and the length is less than 10 um; the test specimens were prepared according to the above preparation method. Numbering the carbon nanotube samples added with different length-diameter ratios and contents, wherein No. 0 is a sample without the addition of the carbon nanotubes, No. 1-5 are samples added with CNTs1 carbon nanotube materials with large length-diameter ratio, and 6-10 are samples added with CNTs2 carbon nanotube materials with small length-diameter ratio. The specific scheme is shown in the following table 1.
TABLE 1 list of test sample numbers and component contents
And (3) detecting the characteristics of the No. 0-10 sample, such as tensile strength, elongation, hardness, metallographic structure morphology and the like, wherein the detection equipment method and the detection result are as follows:
and (3) detecting the tensile strength: the tensile strength, the stretching speed and the loading test force of the material are tested by using a WAW-300 type microcomputer servo control hydraulic universal testing machine, wherein the tensile strength and the stretching speed are 2mm/min and the loading test force is 10 KN. The data obtained by the detection are plotted into a tensile strength change curve chart, as shown in fig. 2. As can be seen from the figure, compared with a matrix ZL105 aluminum alloy without the carbon nanotubes, the strength of the CNTs-Al composite material added with the carbon nanotubes is greatly improved. With the increase of the content of the added carbon nanotubes, the tensile strength of the two groups of materials tends to increase firstly and then decrease, and the maximum value is obtained when the adding amount is 1.25%, and the tensile strength is respectively increased by 5.81% and 10.53% relative to the base material. Both groups of materials play a role in enhancing the strength of the composite material, and compared with CNTs1 reinforcement, the CNTs2 reinforcement can better play a role in enhancing the strength of the composite material.
And (3) detecting the elongation: measuring the elongation of the material using an electronic extensometer (YYU-5/25); the detected elongation data was plotted as an elongation change curve, as shown in fig. 3. As can be seen from the figure, the addition of CNTs can cause a decrease in the elongation of the composite material, which is greater than that of the matrix material only when CNTs2 is added at a mass fraction of 1.5%. As the addition amount of the CNTs is increased, the change curve of the elongation rate approximately presents a U shape. When the addition amount is 1%, the elongation of the composite material added with the CNTs1 reaches the minimum value of 2.69%, and the elongation of the composite material is reduced by 14.06% relative to that of the matrix material; the composite material with added CNTs2 achieved a minimum elongation of 2.88% at the addition level of 0.5%, a reduction of 7.98% in the elongation relative to the matrix material, and the elongation of the material differed only by 0.03% at the addition levels of 0.5% and 1%. For two different reinforcements, the elongation of both materials increases when the addition level exceeds 1%. Throughout the set of experiments, the elongation of composites with added CNTs2 was consistently greater than the elongation of composites with added CNTs 1.
And (3) hardness detection: testing the hardness of the material by using an HBRV-187.5 type electric Brookfield hardness tester, testing the force 612.9N, and maintaining the pressure for 32S; the detected data were plotted as a hardness change curve, as shown in fig. 4. As can be seen from the figure, the hardness of the composite material added with CNTs1 reaches the maximum value (77.26HB) when the addition amount is 1%, while the hardness of the composite material added with CNTs2 reaches the maximum value (75.99HB) when the addition amount is 1.25%, and the hardness of the composite material and the hardness of the matrix ZL105 aluminum alloy material are respectively increased by 12.79% and 10.93%. When the addition amount of the reinforcement is only 1.25%, the added CNTs2 has higher hardness than the CNTs1 composite material.
From the three performance results of the composite material with different length-diameter ratios, the change trends of the mechanical properties of the composite material and the composite material are basically the same, the difference between the elongation and the hardness is not obvious, and the strength has obvious difference. The addition of CNTs can improve the strength and hardness of the matrix material ZL105, but can reduce the elongation of the material. The strength and the elongation of the CNTs2 composite material are better than those of the CNTs1 composite material, but the CNTs2 has hardness performance which is not as good as that of the CNTs1, and the effect difference between the CNTs and the CNTs is not obvious.
And (3) metallographic structure morphology detection: and 3 MPD-2 metallographic polishing machines with different abrasive paper granularities are used for polishing the samples one by one on the abrasive paper with the granularity from coarse to fine. Then polishing with diamond grinding paste, and using prepared aluminum alloy corrosive liquid (phi)<HF:HCl:HNO3:H2O>1:1.5:2.5:95) etching the sample for 5min, and observing the surface metallographic structure morphology of the etched sample by using a 4XC-MS metallographic microscope, as shown in FIG. 5. FIG. 5(a) shows the metallographic structure of sample 0, in which dendrites are slightly coarse, and a small number of small black spots and small black lamellar strengthening phase precipitates are precipitated along a part of the grain boundaries and are irregularly distributed in the metallographic structure. Fig. 5(b) is the metallographic structure morphology of the sample 4, and shows that the grains in the metallographic structure at the content are scattered and spread along the central aggregation point, and the grains are tightly connected together, but as the grains grow, the grain boundary slightly far from the central point is not obvious, the interface energy is weakened, and the connection between the grains is not tight. Fig. 5(c) shows the metallographic structure of sample 5, in which most of the strengthening phases are uniformly precipitated along grain boundaries and the structure distribution is relatively uniform, but there is a condition that part of the strengthening phases are not precipitated, resulting in grain boundary deletion. Meanwhile, obvious segregation phenomenon occurs, and a black strip-shaped substance is gathered on a crystal boundary. Fig. 5(d) shows the metallographic structure of the sample 9, in which only the intermediate local strengthening phase precipitates much, the total precipitation is not sufficiently uniform, the grain boundaries formed are intermittent, and only individual portions are connected well, but the connection between the grains is incomplete as a whole. The segregation tends to be increased until the content is 1.5%, and the strengthening phase is precipitated and aggregated along the grain boundary to form a distinct thick and long black stripe, thereby causing coarse grain aggregation and uneven and non-tight interface contact, as shown in fig. 5 (e).
Observing the fracture morphology of the material by using a JEM-2100F scanning electron microscope, as shown in FIG. 6, and testing the distribution condition of each element by using EDS; the JSM-7001F type transmission electron microscope is used for observing the internal structure of the composite material and carrying out spectral inspection to obtain the content of each element component. The samples of the present invention were analyzed for enhancement mechanism.
The reinforcement mechanism of the present invention is as follows:
1. deformation strengthening: the material can generate stretching deformation when being stretched by external force, and the internal structure of the material generates a main strengthening effect when being stretched and deformed. The fracture pattern of the sample 9 is partially enlarged to find that the fracture form is different from the typical brittle fracture, as shown in fig. 7, the fracture appearance has a boss at the bottom, is flat, but has a certain crack phenomenon, the side surface is smooth and flat for one circle, and the whole dimple is in a 'half eggshell' structure. This occurs because the addition of the carbon nanotubes creates numerous microscopic interfaces with preferential nucleation sites in the melt, and the carbon nanotubes themselves have good thermal conductivity, and the supercooling degree of the region where the carbon nanotubes exist increases, thereby preferentially forming microcracks in this region. When subjected to an external force, microcracks occur in localized areas where the carbon nanotubes are present. After further stretching, the micro-cracks gradually polymerize and grow up, and visible micro-holes grow. When the load is continued to the maximum strength of the composite, the composite breaks along the middle of the micro-cavity, and a tearing edge is formed at the splitting position of the micro-cavity, and the micro-cavity can be regarded as an eggshell. The fracture boss surface and the peripheral sunken structure overcome the problem of stress concentration of brittle fracture, so that the reduction degree of the elongation of the material is relieved. Therefore, the composite material is different from the traditional brittle material, does not sacrifice the excessive elongation rate to improve the strength and the hardness, and is a brittle material with a small amount of toughness.
2. Dispersion strengthening and load transfer
FIG. 8 is a scanning electron micrograph and an EDS chart of sample 9 for thinning the cut piece. The thinned sample surface had curved damage structures with different shapes, and the damage positions were uniformly dispersed, as shown in fig. 8 a. FIG. 8b is an EDS photograph of the site showing that the C elements are more uniformly dispersed in the matrix Al and are all distributed at the site of breakage. Thus, the C element is the main element causing the structure and performance of the composite material to be enhanced. The part C in fig. 8a is enlarged partially, and the structure is found to be in a "C" shape, and such a hook-shaped structure can increase the stability of the internal bonding of the material and play a role in transferring load in the material, thereby improving the mechanical properties of the material. It was found by its EDS (fig. 8d) that this structure is composed mainly of C elements, so C elements may promote the generation of irregular structures to increase load transfer between the interior of the composite. Meanwhile, by observing the enlarged partial view 8e of the area D in fig. 8C, it is found that the elements C are closely arranged in the form of spherical fine particles to form a sheet-like structure, which plays a role in filling and reinforcing the composite material.
3. Interface strengthening and dislocation strengthening
In sample 9, the elemental composition content was measured by selecting a portion of a block structure, which was embedded in the matrix and smoothly contacted with the interface of other tissue and had a good interface bonding condition, as shown in fig. 9, point E. The contents of the main key elements are shown in table 2. From the elemental contents of Table 2, it is seen that the ZL105 aluminum alloy has the highest levels of Al and Si, and that the Al-Si phase also forms the primary phase of the ZL105 aluminum alloy, providing a primary Al-Si interface to the composite interface. Table 2 shows that there are many C and O elements, and the O element is that when the metal is melted at high temperature during the preparation of the base alloy material, oxygen in the air is absorbed into the alloy solution. At the later stage, the carbon nano tube can absorb O into the base material when the carbon nano tube is added2Desorb into the composite material, and both constitute the C-O phase. CO 22Molecular bonds between elements are easily broken at high temperature, resulting in CO2Decomposed to generate gasification reaction, which generates adsorptive ketonic group C.O and vinyl ketonic group C.CO on the carbon surface, and the structure is expressed in>C ═ O and>c ═ O, forming stable carbon bonds. The group with adsorbability plays a key role in connecting the internal interface of the composite material, so that the mechanical property of the composite material is improved.
Table 2 key element content of point E
| Element(s) | Wt.％ | At.％ |
| Al | 33.70 | 23.60 |
| Cu | 1.10 | 0.30 |
| Si | 14.30 | 9.60 |
| Mg | 1.10 | 0.80 |
| C | 26.00 | 40.90 |
| O | 18.90 | 22.30 |
4. Solid solution strengthening
During heat treatment, a temperature difference is formed between the metal material and the heat treatment furnace, so that the supersaturated solid solution is separated out and precipitated to a grain boundary, and a solid solution strengthening effect is generated. Because the carbon nano tube is high temperature resistant and good in thermal stability, the carbon nano tube can not be slightly melted along with other metals during heat treatment, and the carbon nano tube is taken as a solid solution to be separated out. Since the heat treatment process generates a precipitation kinetics, the strengthening phase is precipitated along the grain boundaries, but there is a partial segregation phenomenon. The carbon nanotubes exist on the grain boundary, and induce more precipitates to be aggregated at the grain boundary by virtue of the characteristic of high energy of the carbon nanotubes, and a limit exists in the aggregation degree. When the aggregation reaches this limit, the precipitated phase becomes coarse, and the degree of binding with the matrix is reduced to cause the phase to fall off. In addition, the position of precipitation and aggregation depends on the degree of dispersion of the carbon nanotubes, and the timing of exfoliation depends on the degree of aggregation and the magnitude of the external force applied to the material. A small amount of precipitates can strengthen the material as a strengthening phase, but an amount exceeding a certain level will have the opposite effect.
In conclusion, the invention adds the carbon nano tubes into the cast aluminum alloy ZL105 to change the mechanical properties of the cast aluminum alloy ZL105 and obtain excellent tensile strength and hardness. The microstructure of the cast aluminum alloy ZL105 is influenced by the content and the length-diameter ratio of the carbon nanotubes, and the carbon nanotubes with smaller length-diameter ratio can better improve the microstructure of the material. The mechanical property of the carbon nano tube reinforced ZL105 aluminum alloy composite material is improved through the comprehensive coupling effect of various reinforcement modes.
What has been described above are merely some embodiments of the present invention. It will be apparent to those skilled in the art that various changes and modifications can be made without departing from the inventive concept herein, and it is intended to cover all such modifications and variations as fall within the scope of the invention.
Claims (10)
1. The preparation method of the carbon nanotube reinforced cast ZL105 alloy material is characterized by comprising the following steps of:
s1, preparing ZL105 alloy melt: mixing solid raw materials of aluminum, copper, magnesium and silicon, heating to 820-840 ℃ until the solid raw materials are molten, stirring and refining for 20-25 min to obtain ZL105 alloy molten mass;
s2, preparing a carbon nano tube ZL105 alloy molten body: cooling the ZL105 alloy molten mass to 570-590 ℃, adding carbon nanotubes into the ZL105 alloy molten mass, and stirring and refining for 5-8 min to obtain the carbon nanotube ZL105 alloy molten mass;
s3, heating and smelting: heating the carbon nano tube ZL105 alloy molten mass to 760 ℃ to ensure that the molten alloy is completely in a liquid state, adding a deslagging agent to remove slag, and standing for 20 min;
s4, casting molding: pouring the carbon nano tube ZL105 alloy molten body after deslagging into a mould, and cooling to obtain a carbon nano tube ZL105 alloy material;
s5, heat treatment: and (4) performing heat treatment on the carbon nanotube ZL105 alloy material obtained in the step S4 to obtain a final carbon nanotube reinforced cast ZL105 alloy material.
2. The production method according to claim 1, wherein the heat treatment in step S5 includes the steps of:
s51, carrying out solid solution treatment on the carbon nano tube ZL105 alloy material, wherein the temperature of the solid solution treatment is 520-530 ℃, and the time is 4 hours;
s52, carrying out hot water quenching treatment on the carbon nano tube ZL105 alloy material subjected to the solution treatment, wherein the temperature of the hot water quenching treatment is 80 ℃, and the time is 2 hours;
s53, carrying out artificial aging treatment on the carbon nano tube ZL105 alloy material subjected to hot water quenching treatment, wherein the temperature of the artificial aging treatment is 180 ℃, and the time is 4 hours.
3. The preparation method according to claim 1, wherein the raw materials in the step S1 are prepared from the following raw materials in percentage by weight: 1.0 to 1.5 wt% of copper, 5.0 to 5.5 wt% of silicon, 0.5 to 0.6 wt% of magnesium, and the balance of aluminum.
4. The preparation method according to claim 1, wherein the raw materials in the step S1 are prepared from the following raw materials in percentage by weight: 1.3 wt% of copper, 5.2 wt% of silicon, 0.6 wt% of magnesium and the balance of aluminum.
5. The method according to claim 1, wherein the amount of the carbon nanotubes added in step S2 is 0.5 to 1.5 wt% based on the total mass of the ZL105 alloy melt.
6. The method according to claim 5, wherein the amount of the carbon nanotubes added in step S2 is 0.75 to 1.25 wt% based on the total mass of the ZL105 alloy melt.
7. The method according to claim 1, wherein the carbon nanotubes in step S2 have a tube diameter of 30-80 nm and a length of less than 10 μm.
8. The method according to claim 1, wherein the carbon nanotubes in step S2 have a tube diameter of 5 to 15nm and a length of 10 to 30 μm.
9. The method of claim 1, wherein nitrogen is introduced to exclude air during the agitation refining of steps S1 and S2.
10. The carbon nanotube-reinforced cast ZL105 alloy material is characterized by being prepared by the preparation method according to any one of claims 1 to 9.
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