CN113502417A - High-heat-strength aluminum-silicon alloy material and manufacturing method thereof - Google Patents
High-heat-strength aluminum-silicon alloy material and manufacturing method thereof Download PDFInfo
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- CN113502417A CN113502417A CN202110795041.4A CN202110795041A CN113502417A CN 113502417 A CN113502417 A CN 113502417A CN 202110795041 A CN202110795041 A CN 202110795041A CN 113502417 A CN113502417 A CN 113502417A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
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Abstract
The invention discloses a high-heat-strength aluminum-silicon alloy material and a manufacturing method thereof, and the technical scheme is characterized by comprising the following components in percentage by mass: si: 8.5-10%; cu: 3.0-4.5%; ni: 2.0-3.0%; mg: 1.0-2.5%; 0.05 to 0.3 percent of Zr; ti: 0.05-0.3%; er: 0.05-0.3%; pt: 0.05-0.23 percent, and the balance of Al, and the invention has the advantages of better high-temperature creep resistance, better high heat strength, refined crystal grains and more uniform metallographic structure.
Description
Technical Field
The invention relates to the field of high-strength alloy and preparation thereof, in particular to a high-heat-strength aluminum-silicon alloy material and a manufacturing method thereof.
Background
The aluminum-silicon alloy is an important industrial alloy and is widely applied to important industries such as aviation, traffic, construction, automobiles and the like. Whether aeronautical, maritime or land-based, the engine is kept off, and the piston is called the heart of the engine, which is one of the most important parts in the engine. The piston bears high-temperature and high-pressure heat load and mechanical load in an engine, the traditional aluminum-silicon alloy cannot be used in the harsh environment for a long time, and the development of the piston is seriously restricted by the insufficient high-temperature performance of the traditional aluminum-silicon alloy, so that the development of an aluminum-silicon alloy material with high heat strength is necessary.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide the high-heat-strength aluminum-silicon alloy material and the manufacturing method thereof, and the high-heat-strength aluminum-silicon alloy material has the advantages of better high-temperature creep resistance, better high heat strength, refined crystal grains and more uniform metallographic structure.
The technical purpose of the invention is realized by the following technical scheme:
a high-heat-strength aluminum-silicon alloy material comprises the following components in percentage by mass:
si: 8.5-10%; cu: 3.0-4.5%; ni: 2.0-3.0%; mg: 1.0-2.5%; 0.05 to 0.3 percent of Zr; ti: 0.05-0.3%; er: 0.05-0.3%; pt: 0.05-0.23% and the balance of Al.
Further, the composite material comprises the following components in percentage by mass: 0.08-0.16% of Zr.
Further, the composite material comprises the following components in percentage by mass: 0.08-0.15% of Er.
Further, the composite material comprises the following components in percentage by mass: 0.08 to 0.16 percent of Ti.
A manufacturing method for preparing high-heat-strength aluminum-silicon alloy material comprises the following steps:
s1: preparing each component to prepare aluminum liquid, and preparing a mold;
s2: injecting the aluminum liquid into a mold, solidifying and molding to obtain a casting;
s3: quenching the casting;
s4: and (5) tempering the casting.
Further, in step S2, the molten aluminum is first heated to 760 ℃ and smoothly filled into the cavity through the mold runner.
Further, in step S3, the casting is placed in a water tank for quenching.
Further, in step S3, the temperature of the water tank is controlled within the range of 60-80 ℃, and the water level of the water tank is controlled at the center of the casting pin hole.
Further, in step S4, the casting is placed in an oven and tempered at 230 ℃ for 15 h.
Further, in step S4, the hardness of the casting after tempering is controlled to be 105-140 HB.
In conclusion, the invention has the following beneficial effects:
1. zirconium and aluminum in the material form a ZrAl3 compound, so that the recrystallization process can be hindered, recrystallized grains can be refined, when recrystallization nucleation occurs in an aluminum matrix, AlgZr particles can play a role in blocking, grain boundaries and dislocation can be well pinned, the recrystallization behavior of the alloy is inhibited, and finally the refined grains are achieved.
Ti can form TiAlz phase in the alloy, and becomes a non-spontaneous core during crystallization, thereby obviously refining the casting structure and further improving the mechanical property of the material.
Er generates an AlgEr phase in the material, the lattice constant of the AlgEr phase is very close to AI, the melting point is 1067 ℃, so the AlgEr phase has higher thermal stability, the lattice constant of the Al3Er phase is close to Al, and the AlgEr phase can be coherent with an Al matrix and becomes a nucleation core, so the nucleation rate is improved, and the AlgEr phase can continue to grow to form a coarse primary phase Al3Er to hinder the grains from continuing to grow, so the grains can be effectively refined, and the material performance is improved.
Drawings
FIG. 1 is a schematic representation of the steps of a method of manufacturing a high heat strength aluminum-silicon alloy material;
FIG. 2 is a phase diagram of an AI-Er binary alloy;
FIG. 3 is a gold phase diagram of sample 1;
FIG. 4 is a gold phase diagram of sample 2;
FIG. 5 is a gold phase diagram of sample 3;
FIG. 6 is a gold phase diagram of sample 4;
FIG. 7 is a gold phase diagram of sample 5;
FIG. 8 is a gold phase diagram of sample 6.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the following detailed description of the present invention is provided with reference to the accompanying drawings and the detailed description. The advantages and features of the present invention will become more apparent from the following description. It is to be noted that the drawings are in a very simplified form and are all used in a non-precise scale for the purpose of facilitating and distinctly aiding in the description of the embodiments of the present invention. To make the objects, features and advantages of the present invention comprehensible, reference is made to the accompanying drawings. It should be understood that the structures, ratios, sizes, and the like shown in the drawings and described in the specification are only used for matching with the disclosure of the specification, so as to be understood and read by those skilled in the art, and are not used to limit the implementation conditions of the present invention, so that the present invention has no technical significance, and any structural modification, ratio relationship change or size adjustment should still fall within the scope of the present invention without affecting the efficacy and the achievable purpose of the present invention.
Example 1: a high-heat-strength aluminum-silicon alloy material comprises the following components in percentage by mass: si: 8.5-10%; cu: 3.0-4.5%; ni: 2.0-3.0%; mg: 1.0-2.5%; 0.05 to 0.3 percent of Zr; ti: 0.05-0.3%; er: 0.05-0.3%; pt: 0.05-0.23% and the balance of Al.
Furthermore, the addition amount of Zr in the aluminum-silicon alloy is 0.05-0.25%, and Zr and aluminum form a ZrAl3 compound, which can hinder the recrystallization process and refine recrystallized grains. Zirconium also refines the cast structure but is less effective than titanium. Since zirconium has less influence on quenching sensitivity than chromium and manganese, it is preferable to refine the recrystallized structure by replacing chromium and manganese with zirconium
Further, the composite material comprises the following components in percentage by mass: 0.08-0.16% of Zr. The Zr particles and Al have good coherent relationship, AlgZr particles are fine and densely distributed, and a-Al can be attached to the fine AlgZr for nucleation during the peritectic reaction, so that the Zr plays a role in refining grains. Meanwhile, when recrystallization nucleation occurs in the aluminum matrix, the AlgZr particles can play a role of blocking, and can well pin grain boundaries and dislocation, so that the recrystallization behavior of the alloy is inhibited, and the purpose of refining grains is finally achieved. The size of the crystal grain has a crucial influence on the mechanical property of the alloy, and the smaller the crystal grain of the alloy is, the better the mechanical property is. Secondly, the addition of Zr can improve the corrosion resistance of the alloy, when the Zr content is more than 0.12%, the recrystallization rate of the alloy is obviously reduced, and a large amount of subgrains form an uncrystallized part, thereby cutting off an expansion channel of continuous corrosion stress and improving the anti-spalling corrosion capability of the alloy. In addition, Zr can reduce the quenching sensitivity of the alloy, improve the fracture toughness of the aluminum-silicon alloy, and can cause the crystal lattice of the matrix to generate distortion while being dissolved in the aluminum matrix, thereby playing the role of solid solution strengthening. In conclusion, the addition of Zr is beneficial to improving the comprehensive performance of the aluminum-silicon alloy, and is an important trace element for strengthening the aluminum-silicon alloy.
Further, the composite material comprises the following components in percentage by mass: 0.08 to 0.16 percent of Ti. Ti can form TiAlz phase in the aluminum-silicon alloy after being added, a non-spontaneous core during crystallization is formed, the casting structure is obviously refined, and a better refining effect can be obtained if the Ti is mixed with boron for use. Only a small amount of the metal in the alloy is needed to improve the mechanical properties, but the conductivity is reduced. When peritectic reaction of Al-Ti alloy occurs, the critical content of Ti is about 0.16%.
Further, the composite material comprises the following components in percentage by mass: 0.08-0.15% of Er. As shown in FIG. 2, the Al-terminated eutectic A1-AlgEr, which is a binary Al-Er alloy phase diagram, has a eutectic temperature of 928K (625 deg.C) and a eutectic point Er of about 6%.
Furthermore, Er mainly generates an AlgEr phase in aluminum, and the compound has a lattice constant very close to AI and a melting point of 1067 ℃, thereby having high thermal stability. The Al3Er phase is cubic, has an L12 type structure and a lattice constant of 4.215A, and belongs to the same space group as Al3Sc, and the lattice constants of the two phases are very close to each other and are very similar to the structure of aluminum, so that the Er element is probably similar to Sc in aluminum and aluminum alloy.
Further, the lattice constant of the Al3Er phase is close to that of Al, and therefore, the Al3Er phase can be coordinated with the Al matrix to form a nucleation core, thereby increasing the nucleation rate, and can be continuously grown to coarse primary phase Al3Er, thereby inhibiting the continuous growth of crystal grains and effectively refining the crystal grains. Meanwhile, Er can also form a supersaturated solid solution in A1, secondary Al3Er particles are precipitated from the matrix after proper heat treatment, the particles are fine and dispersed in the matrix, and the pinning effect on subboundaries and dislocations can be effectively realized, so that the recrystallization temperature and the strength of the alloy are improved. In addition, the addition of Er can reduce the gas of the aluminum melt, purify the alloy structure, improve the microstructure of the cast aluminum alloy, and improve the cyclic deformation resistance and the fatigue life of the cast aluminum alloy.
Example 2: a method for manufacturing a high-heat-strength aluminum-silicon alloy material, as shown in fig. 1, comprising the steps of:
and S1, preparing each component to prepare aluminum liquid, and preparing a mould.
S2, heating the aluminum liquid to 760 ℃, stably filling the aluminum liquid into an inner cavity through a die pouring channel, cooling key parts of the piston by adopting a casting method of rapid cooling, accurately controlling the flow of cooling water by adopting a flowmeter and then outputting the cooling water, and controlling the temperature of the die by using a temperature sensor. The top dead head is ensured to be upward. And after the aluminum liquid is cooled, solidified and formed, opening the mold and taking out the casting.
And S3, putting the steel pipe into a water tank at the temperature of 60-80 ℃ for as-cast quenching, wherein the water level is controlled at the center of the pin hole.
S4, putting the casting subjected to quenching into an oven, tempering at 230 ℃ for 15h, and ensuring that the hardness of the tempered material is controlled at 105-140 HB.
And (3) material comprehensive performance experiment:
experimental group preparation:
sample 1: the reinforced material of example 2 was cast by rapid cooling.
Sample 2: the reinforced material is prepared by adopting a non-rapid cooling casting mode.
Sample 3: and preparing the common aluminum-silicon alloy material by adopting a non-rapid cooling casting mode.
A. And (5) detecting the metallographic structure of the material casting.
Experimental structure and analysis thereof:
sample 1: the metallographic phase is shown in fig. 3, secondary dendrites appear in the structure, and the crystal spacing is uniform.
Sample 2: metallographic phase secondary dendrites appeared in the structure as shown in fig. 4, but the grain spacing was not uniform.
Sample 3: the metallographic phase is shown in fig. 5, and the structure has no secondary dendrites.
B. And (5) detecting the final metallographic structure of the material.
Experimental structure and analysis thereof:
sample 4: the metallographic phase is as shown in FIG. 6, and the crystal structure is fine and uniform.
Sample 5: the metallographic phase is as shown in fig. 7, the crystal structure is fine and uniform, but the fineness is lower than that of sample 1, and it is proved that the structure is further refined by rapidly cooling the critical part.
Sample 6: the metallographic phase is shown in FIG. 8, and the crystal structure is coarse, which is a large difference from those of samples 4 and 5 as the comparative group.
The combination of the two metallographic phase detection structures proves that compared with the traditional aluminum-silicon alloy, the aluminum-silicon alloy disclosed by the invention has a finer and more uniform microstructure, and forms uniform secondary dendrites to further refine the structure. Meanwhile, the crystal structure is further refined by reasonably controlling the manufacturing mode.
And (3) material comprehensive performance experiment:
preparation of the experiment: randomly selecting three groups of samples from different batches of products, and marking the three groups of samples as a sample a, a sample b and a sample c.
Experimental items: the performance test was carried out at 20 deg.C, 350 deg.C, 400 deg.C.
The experimental results are as follows:
TABLE 1 comprehensive Properties of 20 deg.C alloy
TABLE 2 comprehensive Properties of 350 ℃ alloy
TABLE 3 comprehensive properties of 400 ℃ alloy
And (3) detection results: the alloy still has good comprehensive mechanical properties under high temperature conditions.
The technical features of the embodiments described above may be arbitrarily combined, and for the sake of brevity, all possible combinations of the technical features in the embodiments described above are not described, but should be considered as being within the scope of the present specification as long as there is no contradiction between the combinations of the technical features.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (10)
1. The high-heat-strength aluminum-silicon alloy material is characterized by comprising the following components in percentage by mass:
si: 8.5-10%; cu: 3.0-4.5%; ni: 2.0-3.0%; mg: 1.0-2.5%; 0.05 to 0.3 percent of Zr; ti: 0.05-0.3%; er: 0.05-0.3%; pt: 0.05-0.23% and the balance of Al.
2. A high-heat-strength aluminum-silicon alloy material as claimed in claim 1, wherein: comprises the following components in percentage by mass: 0.08-0.16% of Zr.
3. A high-heat-strength aluminum-silicon alloy material as claimed in claim 1, wherein: comprises the following components in percentage by mass: 0.08-0.15% of Er.
4. A high-heat-strength aluminum-silicon alloy material as claimed in claim 1, wherein: comprises the following components in percentage by mass: 0.08 to 0.16 percent of Ti.
5. A manufacturing method for preparing the high-heat-strength aluminum-silicon alloy material as claimed in any one of claims 1 to 4, characterized by comprising the following steps:
s1: preparing each component to prepare aluminum liquid, and preparing a mold;
s2: injecting the aluminum liquid into a mold, solidifying and molding to obtain a casting;
s3: quenching the casting;
s4: and (5) tempering the casting.
6. A method for manufacturing a high-heat-strength Al-Si alloy material according to claim 5, wherein: in step S2, the molten aluminum is first heated to 760 ℃ and smoothly filled into the cavity through the mold runner.
7. A method for manufacturing a high-heat-strength Al-Si alloy material according to claim 5, wherein: in step S3, the casting is placed in a water tank for quenching.
8. A method for manufacturing a high-thermal-strength Al-Si alloy material according to claim 7, wherein: in step S3, the water tank temperature is controlled to be 60-80 ℃, and the water level of the water tank is controlled to be at the center of the casting pin hole.
9. A method for manufacturing a high-heat-strength Al-Si alloy material according to claim 5, wherein: in step S4, the casting is placed in an oven and tempered at a temperature of 230 ℃ for 15 hours.
10. A method for manufacturing a high-thermal-strength aluminum-silicon alloy material according to claim 9, characterized in that: in step S4, the hardness of the casting after tempering is controlled to be 105-140 HB.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN116334461A (en) * | 2023-02-24 | 2023-06-27 | 安阳高晶铝材有限公司 | Aluminum alloy material for hub and preparation method thereof |
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