CN116656986A - Preparation method of high-performance aluminum-based composite material forging - Google Patents

Preparation method of high-performance aluminum-based composite material forging Download PDF

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Publication number
CN116656986A
CN116656986A CN202310661046.7A CN202310661046A CN116656986A CN 116656986 A CN116656986 A CN 116656986A CN 202310661046 A CN202310661046 A CN 202310661046A CN 116656986 A CN116656986 A CN 116656986A
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forging
powder
aluminum
sintering
composite material
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Inventor
张友健
乔竹辉
汤华国
宋琳
姬朋飞
张绪圭
于源
李彤阳
王鲁杰
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Yantai Advanced Materials And Green Manufacturing Shandong Laboratory
Yantai Huihua Metal Technology Co ltd
Yantai Zhongke Advanced Materials And Green Chemical Industry Technology Research Institute
Lanzhou Institute of Chemical Physics LICP of CAS
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Yantai Advanced Materials And Green Manufacturing Shandong Laboratory
Yantai Huihua Metal Technology Co ltd
Yantai Zhongke Advanced Materials And Green Chemical Industry Technology Research Institute
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Priority to CN202310661046.7A priority Critical patent/CN116656986A/en
Publication of CN116656986A publication Critical patent/CN116656986A/en
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    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B22F3/04—Compacting only by applying fluid pressure, e.g. by cold isostatic pressing [CIP]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0005—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with at least one oxide and at least one of carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C22C32/0063—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides based on SiC
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
    • B22F2003/175—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging by hot forging, below sintering temperature
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Fluid Mechanics (AREA)
  • Powder Metallurgy (AREA)

Abstract

The application provides a preparation method of a high-performance aluminum-based composite material forging, which comprises the following steps: performing high-energy ball milling on aluminum powder and ceramic powder to obtain mixed powder; isostatic compaction is carried out on the mixed powder to obtain a preform; and preheating the preform, and forging and sintering to obtain the high-performance aluminum-based composite material forging. According to the application, the rapid sintering of the superfine aluminum-based composite material powder under pressure and the deformation, flow and mold filling processes of metal fluid are completed by a sintering forging technology, so that the powder sintering and the sintering body forging deformation are synchronously realized, and finally the aluminum-based composite material forging piece with high compactness, high mechanical property and stable high-temperature structure is obtained.

Description

Preparation method of high-performance aluminum-based composite material forging
Technical Field
The application belongs to the technical field of aluminum-based composite materials, and particularly relates to a preparation method of a high-performance aluminum-based composite material forging.
Background
With the high-speed development of transportation industry, the lightweight replacement of aluminum-based materials to steel in key parts can obviously improve equipment performance, save energy and cost, and particularly the use of aluminum alloy and aluminum-based composite materials on chassis parts, hubs, pistons, brake discs and other parts in the lightweight process of passenger cars and trucks has a greatly growing trend. The ceramic particle reinforced aluminum matrix composite material has excellent performances of high strength, low density, good thermal conductivity, wear resistance, high temperature resistance and the like, and has wide application prospect in the field of lightweight structural parts of vehicles.
The conventional casting method for preparing the particle reinforced aluminum matrix composite material is difficult to solve the problems of poor dispersibility of ceramic particles in a matrix, low content of reinforcing bodies and the like, and the conventional powder metallurgy method is difficult to obtain a product with larger size, complex structure and uniform performance. Therefore, how to obtain aluminum-based composite materials with better performance is a hot spot for research in the field.
Disclosure of Invention
In view of the above, the application aims to provide a preparation method of a high-performance aluminum-based composite material forging, which has simple process and good performance of the prepared aluminum-based composite material forging.
The application provides a preparation method of a high-performance aluminum-based composite material forging, which comprises the following steps:
performing high-energy ball milling on aluminum powder and ceramic powder to obtain mixed powder;
isostatic compaction is carried out on the mixed powder to obtain a preform;
and preheating the preform, and forging and sintering to obtain the high-strength aluminum-based composite material forging.
In an embodiment of the present application, the composition of the ceramic powder may be selected from SiC, tiC and Al 2 O 3 One or more of SiC, tiC and Al 2 O 3 The method comprises the steps of carrying out a first treatment on the surface of the SiC, tiC and Al 2 O 3 The mass ratio of (2) may be selected from 1 (0.8-1.2): 0.8-1.2, such as 1:1:1.
In embodiments of the present application, the mass content of the ceramic powder in the mixed powder may be selected from 15 to 45%, such as 20%, 25%, 30%, 35%, 40%; the mass content of the aluminum powder in the mixed powder may be selected from 55 to 85%, such as 60%, 65%, 70%, 75%, 80%.
In an embodiment of the present application, the components of the mixed powder may be:
0 to 45wt% of SiC;
0 to 45wt% of TiC;
0 to 45wt% of Al 2 O 3 ；
The balance being Al.
In embodiments of the present application, the mass content of SiC may be selected from 1%, 5%, 10%, 15%, 20%, 25%, 30%, 35%, 40%; the mass content of TiC may be selected from 1%, 5%, 10%, 15%, 20%, 25%, 30%, 35%, 40%; al (Al) 2 O 3 The mass content of (C) can be selected from 1%, 5%, 10%, 15%,20％、25％、30％、35％、40％。
In embodiments of the present application, the high energy ball milling may be selected from the group consisting of twin stage ball milling, and the method of high energy ball milling may include:
performing primary ball milling on aluminum powder to obtain superfine aluminum powder;
and mixing the superfine aluminum powder and the ceramic powder, and performing secondary ball milling to obtain mixed powder.
In embodiments of the application, the ball to material ratio during primary ball milling may be selected from (10-14): 1, such as 11:1, 12:1, 13:1; the primary ball milling time can be selected from 30-50 h, such as 35h, 40h and 45h; during the first-stage ball milling process, an anti-forging agent can be added, and the anti-forging agent can comprise: ethanol and acetone; the volume ratio of ethanol to acetone can be selected from (16-20): 1-5, such as (17-19): 2-4, 18:3; the ratio of aluminum powder to ethanol may be selected from 1000g: (16-20) mL, such as 1000g:17mL,1000g:18mL,1000g:19mL.
In embodiments of the application, the ball to material ratio during the secondary ball milling process may be selected from (8-12): 1, such as 9:1, 10:1, 11:1; the secondary ball milling time can be selected from 1 to 5 hours, such as 2 hours, 3 hours and 4 hours; during the secondary ball milling process, an anti-forging agent can be added, wherein the anti-forging agent can be selected from ethanol; the ratio of the mixed powder to the ethanol can be selected from (1200-1800) g: (1-5) mL, such as (1300-1700) g: (2-4) mL, (1400-1600) g:3mL.
In the embodiment of the application, the amplitude of the steel balls in the high-energy ball milling (such as primary ball milling and secondary ball milling) process can be selected from 4-6 mm, such as 5mm; the oscillation frequency can be selected from 1450-1490 cpm, such as 1460cpm, 1470cpm and 1480cpm; a forging inhibitor comprising ethanol and/or acetone may be added during the high energy ball milling process.
In an embodiment of the present application, the average grain size of the aluminum powder in the mixed powder may be selected from 170 to 420nm, such as 200nm, 250nm, 300nm, 350nm, 400nm; the average particle size of the ceramic powder in the mixed powder may be selected from 10 to 100. Mu.m, such as 20. Mu.m, 30. Mu.m, 40. Mu.m, 50. Mu.m, 60. Mu.m, 70. Mu.m, 80. Mu.m, 90. Mu.m.
In embodiments of the application, isostatic compaction may be selected from cold isostatic compaction, and the isostatic compaction pressure may be selected from 220-320 MPa, such as 240MPa, 270MPa, 300MPa; the isostatic pressing time can be selected from 2-4 min, such as 2.5min, 3min, and 3.5min; the density of the preform may be selected from 75 to 85%, such as 78%, 80%, 82%.
In embodiments of the present application, the temperature of the preheating may be selected from 580 to 640 ℃, such as 590 ℃, 600 ℃, 610 ℃, 620 ℃, 630 ℃; the preheating time may be selected from 3 to 7 minutes, such as 4 minutes, 5 minutes, 6 minutes.
In embodiments of the application, the calcination sintering may be performed in a forging die; the forging die temperature during the forging sintering process may be selected from 340 to 380 ℃, such as 350 ℃, 360 ℃, 370 ℃.
In an embodiment of the present application, a method of forging sintering may include:
first stage pressurization is carried out and then second stage pressurization is carried out.
In the embodiment of the present application, the temperature in the forging sintering process may be consistent with the temperature of the forging die described in the above technical scheme, and will not be described herein again; the first stage of pressurization is primary forging, and the second stage of pressurization is final forging.
In embodiments of the application, the speed of the one stage of pressurization may be selected from 0.5 to 0.6mm/s, such as 0.55mm/s; the pressure of the first stage of pressurization can be selected from 100-200T, such as 120T, 140T, 150T, 160T and 180T; the forging ratio of the first stage of pressurization may be selected from (1.8 to 2.2): 1, such as 2:1.
In embodiments of the application, the first stage pressurization results in a forging height of 45-56% of the preform height, such as 48%, 50%, 52%, 54%.
In embodiments of the application, the speed of the two stage pressurization may be selected from 10 to 12mm/s, such as 11mm/s; the pressure of the second stage pressurization can be selected from 400-750T, such as 450T, 500T, 550T, 600T, 650T and 700T; the forging ratio of the two stage pressurization may be selected from (1.1 to 1.5): 1, such as 1.2:1,1.3:1,1.4:1.
in the embodiment of the application, the forging sintering is a process technology combining powder metallurgy and precise die forging, and the forging product with uniform internal structure, high dimensional accuracy and excellent mechanical property can be obtained by taking metal and composite material powder thereof as raw materials. The forging sintering process has the advantages of powder metallurgy and forging, can prepare the forge piece with the density close to the theoretical density, overcomes the defect of low density of common powder metallurgy parts, leads the mechanical property of the powder forge piece to exceed the level of the common forge piece, and can simultaneously keep the advantages of less common powder metallurgy and no cutting process.
Because the powder metallurgy process of the aluminum-based composite material can generate serious oxidation phenomenon, the composite material becomes brittle, and the research on obtaining the forging piece by continuing forging on the basis of the powder metallurgy aluminum-based composite material is relatively less; meanwhile, the powder forging process of the "sintered body+forging" involves many process steps and is complicated in process flow, as shown in fig. 1. Therefore, the application further optimizes and simplifies the process flow based on the powder forging process, improves the material performance, and has important significance and effect on the great application and industrialization of the aluminum-based composite material.
The method adopts a powder forging process to prepare the high-performance aluminum-based composite material forging, and firstly prepares superfine aluminum-based composite material powder with clean surface and high activity; and then the powder forging technology is adopted to realize the rapid sintering and forging deformation of the superfine aluminum-based composite material powder, as shown in figure 2. The application adopts the high-energy ball milling technology, prepares the superfine aluminum-based composite material powder with clean surface and high activity by regulating and controlling the ball milling process and the process control agent, and can temporarily protect the activity and cleanliness generated on the surface of the superfine aluminum-based composite material powder due to the effect of the process control agent, thereby solving the technical problems of preparing, storing and transporting the superfine high-activity aluminum-based composite material powder in an air environment and providing basic conditions for the next step of rapid sintering and forging deformation. According to the application, the rapid sintering of the superfine aluminum-based composite material under the powder pressure and the deformation, flow and mold filling processes of metal fluid are completed through the forging sintering technology, the powder sintering and the sintering body forging deformation are synchronously realized, and finally the aluminum-based composite material forging with high compactness and high mechanical property is obtained, and the conventional powder forging product can be subjected to subsequent forging only through long-time sintering in advance. In addition, the matrix of the aluminum-based composite material prepared by the method is nanocrystalline pure aluminum, phase change can not occur under the working condition of high Wen Fuyi, the strength of the matrix is ensured, the performance degradation caused by the phase change is avoided, and the specific good high-temperature resistance is realized.
Drawings
FIG. 1 is a process flow diagram of powder forging in the prior art;
FIG. 2 is a flow chart of a sinter forging process in an embodiment of the application;
FIG. 3 is an SEM image of a fracture after a tensile test of a forging product prepared in example 1 of the present application.
Detailed Description
The following description of the technical solutions in the embodiments of the present application will be clear and complete, and it is obvious that the described embodiments are only some embodiments of the present application, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the application without making any inventive effort, are intended to be within the scope of the application.
Example 1
1000g of aluminum powder is put into a ball milling tank for primary ball milling, and the ball-to-material ratio is 12:1, adding 18ml of ethanol and 3ml of acetone as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 40 hours to obtain high-activity aluminum powder; mixing the obtained high-activity aluminum powder with 400g of SiC ceramic powder, performing secondary ball milling, wherein the ball-material ratio is 10:1, adding 3ml of ethanol as a forging inhibitor, the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and performing mechanical milling for 3 hours to obtain high-activity composite material powder; the average grain size of the aluminum powder in the composite material powder is 350 nanometers, and the average grain size of the ceramic powder is 55 microns;
performing cold isostatic pressing on the high-activity composite powder, wherein the pressure is 270MPa, and the dwell time is 3 minutes, so as to obtain a preform;
preheating the preform in a high-temperature furnace at 610 ℃ for 5 minutes;
taking out the blank body, putting the blank body into a forging die at 360 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the primary pressurization speed is 0.55mm/s; the pressure is 150 tons and the forging ratio is 2:1, a step of; when the height of the forging piece obtained by the first-stage pressurization reaches 50% of the height of the preform, performing the second-stage pressurization with the speed of 11mm/s; the pressure is 600 tons; forging ratio of 1.2:1, obtaining a forging product.
The product prepared in the embodiment 1 of the application is subjected to sampling and polishing, performance test is carried out, and a tensile test is carried out according to GB/T228.1-2010 section 1 of tensile test of metal materials: the room temperature test method tests, and the hardness test is tested according to GB231-84 metal Brinell hardness test method; the properties of the forgings obtained by detection are shown in Table 1.
By carrying out microstructure analysis on the forging prepared in the embodiment 1, fig. 3 is an SEM image of a fracture after a tensile test of an aluminum-based composite material forging, it can be seen that the composite material is compact in structure, the reinforcement is uniformly wrapped by a matrix structure and uniformly distributed in the matrix, after a sample fails and breaks, the reinforcement breaks and the composite interface bonds well, and the reinforcement has a good load transmission reinforcement effect.
Example 2
1000g of aluminum powder is put into a ball milling tank for primary ball milling, and the ball-to-material ratio is 10:1, adding 16ml of ethanol and 1ml of acetone as a forging inhibitor, wherein the amplitude of a steel ball is 4mm, the vibration frequency is 1450cpm, and mechanically pulverizing for 30 hours to obtain high-activity aluminum powder; mixing the obtained high-activity aluminum powder with 800g TiC ceramic powder, performing secondary ball milling, wherein the ball-material ratio is 8:1, adding 1ml of ethanol as a forging inhibitor, the amplitude of a steel ball is 4mm, the vibration frequency is 1450cpm, and performing mechanical milling for 1 hour to obtain high-activity composite material powder; the average grain size of aluminum powder in the composite powder is 420 nanometers, and the granularity of the ceramic powder is 100 mu m;
performing cold isostatic pressing on the high-activity composite powder, wherein the pressure is 220MPa, and the dwell time is 2 minutes, so as to obtain a preform;
preheating the preform in a high-temperature furnace at 580 ℃ for 3 minutes;
taking out the blank body, putting the blank body into a forging die at 340 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the speed of primary pressurization is 0.5mm/s; the pressure was 100 tons and the forging ratio was 1.8:1, a step of; when the first section is pressurized to 56% of the height of the forging piece, performing second section pressurization, wherein the speed of the second section pressurization is 10mm/s; the pressure was 400 tons and the forging ratio was 1.1:1, a step of; obtaining a forging product.
The forging product prepared in example 2 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Example 3
1000g of aluminum powder is put into a ball milling tank for primary ball milling, and the ball-to-material ratio is 14:1, adding 20ml of ethanol and 5ml of acetone as a forging inhibitor, wherein the amplitude of a steel ball is 6mm, the vibration frequency is 1490cpm, and mechanically pulverizing for 50 hours to obtain high-activity aluminum powder; mixing the high-activity aluminum powder obtained above with 200g of Al 2 O 3 Mixing ceramic powder, performing secondary ball milling, wherein the ball-material ratio is 12:1, and pulverizing for 5 hours to obtain high-activity composite material powder; the average grain size of the aluminum powder in the composite powder is 170 nanometers, and the average grain size of the ceramic powder is 10 mu m;
cold isostatic pressing the high-activity powder to obtain a preform, wherein the pressure is 320MPa and the dwell time is 4 minutes;
preheating the preform in a high-temperature furnace at 640 ℃ for 7 minutes;
taking out the blank body, putting the blank body into a forging die at 380 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the pressurization speed of the primary pressurization is 0.6mm/s; the pressure is 200 tons; forging ratio of 2.2:1, a step of; when the height of the forging reaches 45% of the height of the preform, carrying out second-stage pressurization, wherein the pressurization speed of the second-stage pressurization is 12mm/s, the pressure is 750 tons, and the forging ratio is 1.5:1, a step of; obtaining a forging product.
The forging product prepared in example 3 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Example 4
Putting 1000g of aluminum powder into a ball milling tank for primary ball milling, wherein the ball-material ratio is 13:1, adding 19ml of ethanol and 4ml of acetone as anti-forging agents, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 45 hours to obtain the aluminum powderHigh-activity aluminum powder; mixing the high-activity aluminum powder obtained above with 300g of Al 2 O 3 Mixing ceramic powder, and performing secondary ball milling, wherein the ball-to-material ratio is 11:1, adding 4ml of ethanol as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 4 hours to obtain high-activity composite material powder; the average grain size of aluminum powder in the composite powder is 300 nanometers, and the average grain size of a ceramic phase is 45 mu m;
cold isostatic pressing the high-activity powder to obtain a preform, wherein the pressure is 300MPa and the dwell time is 3.5 minutes;
preheating the preform in a high-temperature furnace at 620 ℃ for 6 minutes;
taking out the blank body, putting the blank body into a forging die at 370 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the speed of the primary pressurization is 0.55mm/s; the pressure is 180 tons; forging ratio is 2:1, a step of; when the first section is pressurized to the height of the forging piece to be 50% of the height of the preform, performing second section pressurization, wherein the speed of the second section pressurization is 11mm/s; the pressure was 700 tons and the forging ratio was 1.3:1, a step of; obtaining a forging product.
The forging product prepared in example 4 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Example 5
1000g of aluminum powder is put into a ball milling tank for primary ball milling, and the ball-to-material ratio is 11:1, adding 17ml of ethanol and 2ml of acetone as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 38 hours to obtain high-activity aluminum powder; mixing the high-activity aluminum powder obtained above with 300g SiC and 200g Al 2 O 3 Mixing ceramic powder, performing secondary ball milling, adding 2ml of ethanol as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, the ball-to-material ratio is 9:1, and mechanically pulverizing for 2 hours to obtain high-activity composite material powder; the average grain size of aluminum powder in the composite powder is 400 nanometers, and the granularity of ceramic powder is 65 mu m;
carrying out cold isostatic pressing on the high-activity powder, wherein the pressure is 240MPa, and the pressure maintaining time is 4 minutes, so as to obtain a preform;
preheating the preform in a high-temperature furnace at 600 ℃ for 4 minutes;
taking out the blank body, putting the blank body into a forging die at 350 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the speed of the primary pressurization is 0.55mm/s; the pressure is 120 tons; forging ratio is 2:1, a step of; when the first section is pressurized to the height of the forging piece to be 50% of the height of the preform, performing second section pressurization, wherein the speed of the second section pressurization is 11mm/s; the pressure was 500 tons and the forging ratio was 1.2:1, a step of; obtaining a forging product.
The forging product prepared in example 5 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Example 6
1000g of aluminum powder and 400g of SiC ceramic powder are put into a ball milling tank for ball milling, and the ball-to-material ratio is 12:1, adding 20ml of ethanol and 3ml of acetone as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 43 hours to obtain high-activity composite material body powder.
Performing cold isostatic pressing on the high-activity powder, wherein the pressure is 270MPa, and the pressure maintaining time is 3 minutes, so as to obtain a preform;
preheating the preform in a high-temperature furnace at 610 ℃ for 5 minutes;
taking out the blank body, putting the blank body into a forging die at 360 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the speed of primary pressurization is 0.55mm/s; the pressure is 150 tons; forging ratio is 2:1, a step of; when the first section is pressurized to the height of the forging piece to be 50% of the height of the preform, performing second section pressurization, wherein the speed of the second section pressurization is 11mm/s; the pressure is 600 tons; forging ratio of 1.2:1, obtaining a forging product.
The forging product prepared in example 6 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Example 7
Putting 1000g of aluminum powder into a ball milling tank for primary ball milling, wherein the ball-material ratio is 13:1, adding 19ml of ethanol and 4ml of acetone as anti-forging agents, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 45 hours to obtain high-activity aluminum powder; the above-mentioned materials are obtainedHigh-activity aluminum powder obtained and 200g Al 2 O 3 Mixing ceramic powder, and performing secondary ball milling, wherein the ball-to-material ratio is 11:1, adding 4ml of ethanol as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 5 hours to obtain high-activity composite material powder.
Cold isostatic pressing the high-activity powder to obtain a preform, wherein the pressure is 300MPa and the dwell time is 3.5 minutes;
preheating the preform in a high-temperature furnace at 620 ℃ for 6 minutes;
taking out the blank body, putting the blank body into a forging die at 370 ℃, carrying out powder forging sintering on the preform, and carrying out only one section of pressurization with the pressurization speed of 11mm/s; the pressure is 700 tons; forging ratio of 1.3:1, a step of; obtaining a forging product.
The forging product prepared in example 7 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Example 8
1000g of aluminum powder is put into a ball milling tank for primary ball milling, and the ball-to-material ratio is 11:1, adding 10ml of ethanol and 2ml of acetone as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, and mechanically pulverizing for 35 hours to obtain high-activity aluminum powder; mixing the high-activity aluminum powder obtained above with 200g SiC and 200g Al 2 O 3 Mixing ceramic powder, performing secondary ball milling, adding 1ml of ethanol as a forging inhibitor, wherein the amplitude of a steel ball is 5mm, the vibration frequency is 1470cpm, the ball-to-material ratio is 9:1, and mechanically pulverizing for 2 hours to obtain high-activity composite material powder;
performing cold isostatic pressing on the high-activity powder, wherein the pressure is 250MPa, and the pressure maintaining time is 4 minutes, so as to obtain a preform;
preheating the preform in a high-temperature furnace at 600 ℃ for 3 minutes;
taking out the blank body, putting the blank body into a forging die at 350 ℃, carrying out powder forging sintering on the preform, and sequentially carrying out primary pressurization and secondary pressurization, wherein the speed of the primary pressurization is 0.55mm/s; the pressure is 120 tons; forging ratio is 2:1, a step of; when the first section is pressurized to the height of the forging piece to be 50% of the height of the preform, performing second section pressurization, wherein the speed of the second section pressurization is 11mm/s; the pressure was 500 tons and the forging ratio was 1.2:1, a step of; obtaining a forging product.
The forging product prepared in example 8 was subjected to performance test according to the method of example 1, and the test results are shown in table 1.
Table 1 results of performance testing of forging products prepared in examples
As can be seen from Table 1, in examples 1 to 5, the aluminum-based composite forgings with high compactness, high mechanical properties and stable high-temperature structure were finally obtained by controlling the ball milling parameters, the addition amount of the process control agent and the forging sintering parameters. In the embodiment 6, no two-stage ball milling is adopted, in the embodiment 7, no two-stage pressurization is adopted for forging and sintering, the addition amount of the control agent in the embodiment 8 is improper, and aluminum powder is subjected to cold welding and forging in the high-energy ball milling process, so that the aluminum matrix grains in the composite forging are coarse; the properties of the products prepared in examples 6 to 8 were made lower.
The application adopts a one-step process of forging sintering under pressure to replace the multi-step process in the existing powder forging process, as shown in fig. 1 and 2; compared with the prior art, the application utilizes the high-energy dry ball milling process, repeatedly cold welding and breaking are carried out among the component powders under the collision action of the high-energy grinding ball medium, so as to obtain fine and uniform composite powder of aluminum matrix and ceramic particles, and the gaseous molecules of the added process control agent are wrapped on the surface of superfine and high-activity powder in the process, thereby playing roles of blocking oxygen and protecting surface activity; pressurizing and forming the powder by using isostatic pressure to obtain a uniform blank body with the density of about 80%; preheating the blank, releasing the gas coated on the surface of the particles, and re-exposing the superfine and high-activity surface; and finally, powder particles with high-activity surfaces in the blank are rapidly sintered through rapid sintering and forging processes under pressure, so that effective bonding among the particles is realized, and finally, a forging with a specific shape is formed through metal fluid deformation, flow and mold filling processes, and the microstructure of the prepared aluminum-based composite forging is fine and uniform, so that the strength and hardness of the forging are improved.
The preparation method provided by the application can realize rapid sintering and forging deformation under pressure, high mechanical properties of the forging can be realized without a separate powder metallurgy sintering process, a separate forging process, a subsequent solid solution, aging and other heat treatment processes, and the whole preparation process can be carried out in an air atmosphere; meanwhile, the method has the advantages of simple process, convenient operation, few steps and the like, and is suitable for the industrial production of large-scale aluminum alloy forgings. The application realizes the synchronous completion of the powder metallurgy sintering and forging of the aluminum-based composite material under pressure by a simple technology, and obtains the aluminum-based composite material forging product with superfine structure and high mechanical property. The preparation of the micro-nano aluminum-based composite material powder is realized by a high-energy ball milling technology; the high-density aluminum-based composite material forging is obtained by in-situ activated sintering and forging technology, so that the strength of the forging is greatly improved. The key point of the application is that the preparation method of the aluminum-based composite material forging is that the rapid sintering and fluid deformation, flow and mold filling processes of the superfine aluminum-based composite material powder under pressure are completed by the powder forging sintering technology, the powder sintering and sintering forging deformation are synchronously realized, and finally the aluminum-based composite material forging with high compactness and high mechanical property, such as SiC particle reinforced aluminum-based composite material with superfine structure, is obtained.
While the application has been described and illustrated with reference to specific embodiments thereof, the description and illustration is not intended to limit the application. It will be apparent to those skilled in the art that various changes may be made in this particular situation, material, composition of matter, substance, method or process without departing from the true spirit and scope of the application as defined by the following claims, so as to adapt the objective, spirit and scope of the application. All such modifications are intended to be within the scope of this appended claims. Although the methods disclosed herein have been described with reference to particular operations being performed in a particular order, it should be understood that these operations may be combined, sub-divided, or reordered to form an equivalent method without departing from the teachings of the present disclosure. Thus, unless specifically indicated herein, the order and grouping of operations is not a limitation of the present application.

Claims (10)

1. A preparation method of a high-performance aluminum-based composite material forging comprises the following steps:
performing high-energy ball milling on aluminum powder and ceramic powder to obtain mixed powder;
isostatic compaction is carried out on the mixed powder to obtain a preform;
and preheating the preform, and forging and sintering to obtain the high-performance aluminum-based composite material forging.
2. The preparation method according to claim 1, wherein the mass content of the aluminum powder in the mixed powder is selected from 55-85%; the mass content of the ceramic powder in the mixed powder is selected from 15-45%.
3. The method according to claim 1, wherein the ceramic powder is selected from the group consisting of SiC, tiC and Al 2 O 3 One or more of them.
4. The method according to claim 1, wherein the mixed powder comprises the following components:
0 to 45wt% of SiC;
0 to 45wt% of TiC;
0 to 45wt% of Al 2 O 3 ；
The balance being Al.
5. The method of claim 1, wherein the high energy ball milling process comprises:
performing primary ball milling on aluminum powder to obtain superfine aluminum powder;
mixing the superfine aluminum powder and the ceramic powder, and performing secondary ball milling to obtain mixed powder;
the primary ball milling time is selected from 30-50 hours;
the secondary ball milling time is selected from 1 to 5 hours.
6. The method according to claim 5, wherein the average grain size of the aluminum powder in the mixed powder is selected from 170 to 420nm;
the average particle size of the ceramic powder in the mixed powder is selected from 10-100 microns.
7. The method of claim 1, wherein the isostatic pressing pressure is selected from 220-320 MPa; the isostatic compaction time is selected from 2-4 min.
8. The method of claim 1, wherein the pre-heating temperature is selected from 580-640 ℃; the preheating time is selected from 3-7 minutes.
9. The method of claim 1, wherein the forging sintering is performed in a forging die, and wherein the temperature of the forging die during the forging sintering is selected from 340 to 380 ℃.
10. The method according to claim 1, wherein the forging sintering process is performed with first stage pressurization and then with second stage pressurization;
the speed of the first section of pressurization is selected from 0.5-0.6 mm/s;
the speed of the two-stage pressurization is selected from 10-12 mm/s.
CN202310661046.7A 2023-06-02 2023-06-02 Preparation method of high-performance aluminum-based composite material forging Pending CN116656986A (en)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117161381A (en) * 2023-11-02 2023-12-05 国网山东省电力公司烟台供电公司 Near-net forming preparation method of aluminum-based composite ball head and bowl hardware fitting

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117161381A (en) * 2023-11-02 2023-12-05 国网山东省电力公司烟台供电公司 Near-net forming preparation method of aluminum-based composite ball head and bowl hardware fitting
CN117161381B (en) * 2023-11-02 2024-01-16 国网山东省电力公司烟台供电公司 Near-net forming preparation method of aluminum-based composite ball head and bowl hardware fitting

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