CN113000842A - Method for preparing alloy semi-solid thixotropic blank by continuously extruding simple substance mixed powder - Google Patents
Method for preparing alloy semi-solid thixotropic blank by continuously extruding simple substance mixed powder Download PDFInfo
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- 239000007787 solid Substances 0.000 title claims abstract description 50
- 238000000034 method Methods 0.000 title claims abstract description 39
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 34
- 239000000956 alloy Substances 0.000 title claims abstract description 34
- 239000011812 mixed powder Substances 0.000 title claims abstract description 27
- 230000009974 thixotropic effect Effects 0.000 title claims abstract description 16
- 239000000126 substance Substances 0.000 title claims abstract description 14
- 239000000843 powder Substances 0.000 claims abstract description 53
- 229910052751 metal Inorganic materials 0.000 claims abstract description 46
- 239000002184 metal Substances 0.000 claims abstract description 46
- 238000002844 melting Methods 0.000 claims abstract description 32
- 230000008018 melting Effects 0.000 claims abstract description 32
- 239000000463 material Substances 0.000 claims abstract description 19
- 238000001125 extrusion Methods 0.000 claims abstract description 18
- 239000007791 liquid phase Substances 0.000 claims abstract description 10
- 238000003466 welding Methods 0.000 claims abstract description 8
- 239000007790 solid phase Substances 0.000 claims abstract description 5
- 238000001953 recrystallisation Methods 0.000 claims description 14
- 230000008569 process Effects 0.000 claims description 13
- 239000013078 crystal Substances 0.000 claims description 9
- 238000002156 mixing Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 6
- 230000009471 action Effects 0.000 claims description 5
- 239000011159 matrix material Substances 0.000 claims description 4
- 230000009466 transformation Effects 0.000 claims description 3
- 238000012545 processing Methods 0.000 abstract description 7
- 238000005265 energy consumption Methods 0.000 abstract description 3
- 230000004913 activation Effects 0.000 abstract description 2
- 238000004553 extrusion of metal Methods 0.000 abstract 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 11
- 229910001297 Zn alloy Inorganic materials 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 7
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 6
- 238000010586 diagram Methods 0.000 description 6
- 238000010099 solid forming Methods 0.000 description 6
- JRBRVDCKNXZZGH-UHFFFAOYSA-N alumane;copper Chemical compound [AlH3].[Cu] JRBRVDCKNXZZGH-UHFFFAOYSA-N 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 5
- 229910000838 Al alloy Inorganic materials 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- FJMNNXLGOUYVHO-UHFFFAOYSA-N aluminum zinc Chemical compound [Al].[Zn] FJMNNXLGOUYVHO-UHFFFAOYSA-N 0.000 description 4
- 229910002056 binary alloy Inorganic materials 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 239000007788 liquid Substances 0.000 description 3
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- 230000035939 shock Effects 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 238000009825 accumulation Methods 0.000 description 2
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000004455 differential thermal analysis Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
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- 238000002360 preparation method Methods 0.000 description 2
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- 239000013008 thixotropic agent Substances 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
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- 238000005495 investment casting Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000009704 powder extrusion Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
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- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000001228 spectrum Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
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Classifications
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- 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
- B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
-
- 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
-
- 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
- C22F3/00—Changing the physical structure of non-ferrous metals or alloys by special physical methods, e.g. treatment with neutrons
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention discloses a method for preparing an alloy semi-solid thixotropic billet by continuously extruding elemental mixed powder, belonging to the technical field of material processing. The method of the invention mixes two or more simple substance mixed powder evenly, conveys the mixed powder into a groove of a continuous extrusion wheel, the powder in a female die is crushed, rubbed, extruded and welded, a block material is formed after passing through the female die, the block material is intercepted according to the equal volume of a target part, the temperature is kept near the melting point of the simple substance metal with low melting point for a certain time, the low melting point powder starts to melt, the welding area of the high melting point powder is restored and recrystallized, a high melting point solid phase is formed as a framework, and a low melting point liquid phase is distributed in a semi-solid structure. The invention combines the continuous extrusion of metal powder and the activation of strain-induced melting, realizes the semi-solid alloy blank making method with short flow and batch, and can reduce the semi-solid thixotropic temperature of the alloy and reduce the energy consumption and the cost of tooling dies.
Description
Technical Field
The invention relates to a method for preparing an alloy semi-solid thixotropic billet by continuously extruding simple substance mixed powder, in particular to a method for efficiently and continuously preparing the alloy semi-solid billet and simultaneously reducing the alloy semi-solid thixotropic forming temperature, belonging to the technical field of material processing.
Background
The semi-solid forming technique, abbreviated as SSM, was initiated in the early 70 s of the 20 th century by professor m.c. flemings of the american academy of science and technology of the ma province, and received extensive attention and intensive research. Compared with the traditional casting technology, the liquid phase of the semi-solid forming technology contains a solid phase with a certain volume fraction, the latent heat of crystallization is small, and the solidification shrinkage is small. Therefore, the formed part has compact structure, high mechanical property and high dimensional precision, can realize near-net forming, has small thermal shock to the die and can prolong the service life of the die. Compared with the traditional forging, the forging method contains a certain amount of liquid phase, has small deformation resistance and low forming force, can reduce the requirements of forming on equipment and dies, and can form complex parts. Just because of the above series of advantages of semi-solid forming, research and application of semi-solid forming have attracted extensive attention and high attention of the world.
The near-net forming technology of complex components of engineering application alloys such as aluminum, copper, nickel, iron and titanium-based alloys is mainly developed around precision casting, and particularly thin-wall parts of the components are complex and expensive in processing equipment, special in mold materials, high in processing cost, strict in process parameter control and low in yield, so that the cost is high; the processing of the forging piece is difficult to form a complex structure at one time, a plurality of procedures such as driving, milling and the like are needed, the flow is long, and the cost is still high; the semi-solid thixoforming can obtain parts with complex structures at one time, the performance of the parts is close to that of forgings, but the semi-solid thixoforming temperature of the alloy is close to the liquidus line of the alloy, the deformation temperature is high, the high-temperature heat insulation difficulty is high, the thermal shock to a die is large, and the die is required to be made of special materials. Even part of the alloy has no solid-liquid interval, and semi-solid processing cannot be carried out. Therefore, the popularization and development of the semi-solid thixoforming technology of the alloy are limited no matter the high-temperature performance requirement and the operation feasibility of the tool and die materials; therefore, a method for efficiently and continuously preparing alloy semi-solid blank and reducing the thixoforming temperature of the alloy is needed, the alloy semi-solid blank preparation process is shortened, the semi-solid thixoforming process window is reduced, the material cost of tools and dies is reduced, and the service life of the dies is prolonged. At the same time, a short and easy-to-operate process flow is to be ensured.
Disclosure of Invention
In order to solve the problems existing in the background technology, the invention aims to provide an efficient and continuous alloy semi-solid blank making technology and a method capable of reducing the semi-solid thixoforming temperature of alloys (such as aluminum-zinc alloy, copper-aluminum alloy, titanium-aluminum alloy and the like), and the technical scheme of the invention is as follows:
a method for preparing alloy semi-solid thixotropic billet by continuously extruding simple substance mixed powder comprises the following steps:
(1) mixing two or more simple substance mixed powders with high melting point and low melting point uniformly in a powder mixer, conveying the mixed powders into a groove of a continuous extrusion wheel, and carrying the mixed powders into a shoe groove of an extrusion female die in the rotary motion of a roller; then under the action of friction force, the powder in the female die is crushed, rubbed, extruded and welded, and after passing through the female die, a block material (such as a rod-shaped or a rod-shaped) is formed,
(2) remelting the intercepted block material in a heating furnace for the second time, heating the material until the low-melting-point metal is melted, recrystallizing the high-melting-point metal to form high-melting-point isometric crystals serving as a framework, and distributing a semi-solid blank of a molten liquid phase among crystal grains; wherein the simple substance with high melting point and low melting point should satisfy the recrystallization temperature of the high melting point metal being less than or equal to the melting point of the low melting point metal (for example, the recrystallization temperature of the mixed powder of aluminum powder and zinc powder is about 350 ℃, the melting point of zinc is about 420 ℃, and the recrystallization temperature of the mixed powder of copper powder and aluminum powder is about 450 ℃, and the melting point of aluminum is about 660 ℃).
Preferably, in the simple substance mixed powder of the present invention: the high-melting-point metal powder is used as a base material, the low-melting-point metal powder is used as a secondary main metal, the mass percent of the high-melting-point metal powder is 80-95%, and the mass percent of the low-melting-point metal powder is 5-20%.
Preferably, the conditions of the secondary remelting of the invention are as follows: (1) reaching the melting point of the low-melting-point metal powder, and preserving the heat for 10-30 minutes to ensure that at least a liquid phase with the volume fraction of more than 5 percent exists in the semi-solid blank; (2) the high melting point metal powder welding matrix generates recrystallization transformation above the recrystallization temperature, and ensures that high temperature solid phase recrystallization is changed into isometric crystal.
Preferably, in the step (1) of the present invention, the mixing process of the metal powder in the powder mixer is more than 30 minutes, and the rotating speed of the extrusion roller is 4-7 rpm.
Preferably, the conditions of the secondary remelting of the invention are as follows: (1) the melting point of the low-melting-point metal powder is reached, and at least a liquid phase with the volume fraction of more than 5 percent is ensured to exist in the semi-solid blank; (2) the high melting point metal powder welding matrix generates recrystallization transformation above the recrystallization temperature, and ensures that high temperature solid phase recrystallization is changed into isometric crystal.
Preferably, the metal powder is mixed for at least 30 minutes in a powder mixer, so that the heterogeneous metal powder is uniformly mixed, and the rotating speed of an extrusion roller is controlled to be 4-7 rpm; the purpose of lower rotating speed is to control the mixed metal powder to undergo several processes of rotation, crushing and welding in the die cavity, so as to realize that the high-temperature metal powder is mutually welded into a block material, wherein the low-temperature melting point powder and the high-temperature powder are subjected to interface welding reaction, and the concentration of high-temperature metal atoms is distributed in a gradient manner from the interface to the interior of the low-temperature metal powder.
The continuous extrusion pass can be carried out once or for multiple times, the purpose is to accumulate the distortion energy with different energy for the forming lump materials, and because the distortion capacities of the high-temperature metal and the low-temperature metal are mismatched, the accumulated distortion energy between the high-temperature metal and the low-temperature metal is different, the recrystallization and melting temperature points of the high-temperature metal and the low-temperature metal can be adjusted and controlled by changing the deformation pass.
The mixed elemental metal powder is subjected to large plastic deformation, and metallurgical bonding is generated among powder particles; the solid solution degree of the heterogeneous particles is limited, and the powder particles are still free of elemental metal except for the metallurgically bonded interface.
The invention has the advantages and technical effects that:
(1) the invention combines the continuous powder extrusion and the strain-induced melting activation method, has flexible regulation and control of powder metallurgy components, can directly carry out powder forming and large plastic deformation, has shorter casting-cooling-heating-forging-blank procedures and lower energy consumption compared with the traditional semi-solid blank preparation process, and reduces the production cost and the production period of the alloy semi-solid blank.
(2) According to the invention, the high-melting-point metal and low-melting-point metal mixed powder is matched with continuous extrusion, the high-temperature metal is recrystallized in the remelting process by virtue of the distortion energy accumulated by large plastic deformation of the continuous extrusion, and the low-temperature metal is melted to form the liquid-phase thixotropic agent, so that the high-quality alloy semi-solid thixotropic blank is obtained, the alloy semi-solid thixotropic forming temperature is reduced, the energy consumption required in the remelting process is reduced, the thermal shock to a die in the alloy semi-solid blank forming process at high temperature is weakened, the material requirement of the die is reduced, the service life of the die is prolonged, and the feasibility of alloy semi-solid thixotropic forming is.
Drawings
FIG. 1 is a schematic process flow diagram of the process of the present invention;
FIG. 2 is a schematic diagram of the extrusion-fusion evolution of the hybrid powder of the present invention;
FIG. 3 is a schematic view showing the microstructure evolution during the remelting process of a continuously extruded alloy semi-solid billet;
FIG. 4 is a microstructure diagram of an Al-8wt% Zn alloy semi-solid billet;
FIG. 5 is a microstructure of a continuously extruded Al-8wt% Zn alloy and a differential thermal analysis spectrum thereof.
Detailed Description
The present invention is further illustrated by the following examples, but the scope of the invention is not limited to the above-described examples.
The method comprises the steps that two or more simple substance powders are uniformly mixed and are conveyed into a roller groove of a continuous extruding machine through a funnel, mixed powders enter and are accumulated in front of an extruding shoe along with the rotation of an extruding roller, and the accumulated powders are formed into rod-shaped and rod-shaped blanks through a die under the action of the friction force of the extruding roller; according to the equal-volume blanking of the target part, the blank is heated to a certain temperature and is kept warm, so that a high-temperature alloy semi-solid blank is obtained, and then the high-temperature alloy semi-solid blank is extruded or die-cast to form the target part.
Example 1
The semi-solid blank prepared by the experiment is a copper-aluminum semi-solid blank (Cu-10 wt% Al), and the used binary alloy powder is respectively aluminum powder with the purity of 99.7% (the granularity is 200 meshes) and copper powder with the purity of 99.8% (the granularity is 200 meshes)
(1) Mixing copper powder and aluminum powder in a ratio of 9: 1 was thoroughly mixed in a V-type powder mixer for 30 minutes.
(2) Preheating a die of the CONFORM continuous extruder, wherein the preheating temperature is 400 ℃, and the heat preservation time is 30 minutes.
(3) And pouring the mixed powder into an extrusion wheel groove of a CONFORM powder continuous extruder, wherein the rotating speed of the extrusion wheel is 4rpm, continuously feeding the mixed powder into a die cavity for accumulation, continuously rotating the extrusion wheel, crushing and welding the powder under the action of friction force, and forming a bar by a die opening.
(4) Cutting off the bar stock, putting the bar stock with proper volume into a crucible, putting the crucible into a resistance furnace, heating at 660 ℃, and keeping the temperature for 15 minutes.
According to a copper-aluminum phase diagram, the binary alloy under the component has no obvious solid-liquid interval, and can not be subjected to semi-solid near-net forming; the semi-solid thixotropic blank of the copper-aluminum alloy is successfully prepared by the method, compared with the conventional casting method, the possibility of semi-solid forming of the copper-aluminum alloy is realized, and the semi-solid thixotropic forming temperature is 660 ℃.
Fig. 3 is a schematic diagram of the microstructure evolution of the remelting process of the continuously extruded alloy semi-solid billet, and it can be seen from the diagram that the powder after large plastic deformation is recrystallized and transformed into equiaxial crystals, and the low-temperature metal powder is melted into a liquid phase and distributed in equiaxial crystal grain framework gaps as a thixotropic agent.
Example 2
The semi-solid blank prepared by the experiment is a titanium-aluminum semi-solid blank (Al-8 wt% Zn), and the used binary alloy powder is respectively aluminum powder with the purity of 99.5% (the granularity is 200 meshes) and zinc powder with the purity of 99.5% (the granularity is 200 meshes).
(1) Mixing aluminum powder and zinc powder in a ratio of 9.2: 0.8 mass ratio in V type powder mixer fully mixed, mixing time is 60 minutes.
(2) Preheating a die of a CONFORM powder continuous extruder, wherein the preheating temperature is 400 ℃, and the heat preservation time is 30 minutes.
(3) And pouring the mixed powder into an extrusion wheel groove of a CONFORM powder continuous extruder, wherein the rotating speed of the extrusion wheel is 7rpm, continuously feeding the mixed powder to a die cavity for accumulation, continuously rotating the extrusion wheel, crushing and welding the powder under the action of friction force, and forming a bar by a die opening.
(4) Cutting off the bar stock, putting the bar stock with proper volume into a crucible, putting the crucible into a resistance furnace, heating to 420 ℃, and keeping the temperature for 15 minutes.
According to an aluminum-zinc phase diagram, the solid-liquid interval of the binary alloy with the components is about 640-650 ℃; the aluminum-zinc alloy semi-solid blank is successfully prepared by the method, and compared with the conventional method, the aluminum-zinc alloy semi-solid forming temperature is greatly reduced and is 410-425 ℃.
FIG. 4 is a microstructure diagram of an Al-8wt% Zn alloy semi-solid billet prepared by continuously extruding elemental powders of aluminum and zinc, from which it can be seen that the powdered aluminum matrix after large plastic deformation is dense, the metallurgical bonding is sufficient, and the crushed aluminum powder and zinc powder are distributed therebetween. FIG. 5 is a differential thermal analysis curve of an Al-8wt% Zn alloy prepared by continuous extrusion, which shows that a more obvious semi-solid state region exists in a region of 410-425 ℃, and the temperature of a traditional semi-solid processing window of the alloy is reduced.
Claims (4)
1. A method for preparing alloy semi-solid thixotropic blank by continuously extruding simple substance mixed powder is characterized by comprising the following steps:
(1) mixing two or more simple substance mixed powders with high melting point and low melting point uniformly in a powder mixer, conveying the mixed powders into a groove of a continuous extrusion wheel, and carrying the mixed powders into a shoe groove of an extrusion female die in the rotary motion of a roller; then under the action of friction force, the powder in the female die is crushed, rubbed, extruded and welded, and after passing through the female die, a block material is formed,
(2) remelting the intercepted block material in a heating furnace for the second time, heating the material until the low-melting-point metal is melted, recrystallizing the high-melting-point metal to form high-melting-point isometric crystals serving as a framework, and distributing a semi-solid blank of a molten liquid phase among crystal grains; wherein, the simple substances with high melting point and low melting point should meet the requirement that the recrystallization temperature of the high melting point metal is less than or equal to the melting point of the low melting point metal.
2. The method for preparing the alloy semi-solid thixotropic billet by continuously extruding the elemental mixed powder according to claim 1, wherein the method comprises the following steps: in the simple substance mixed powder: the high-melting-point metal powder is used as a base material, the low-melting-point metal powder is used as a secondary main metal, the mass percent of the high-melting-point metal powder is 80-95%, and the mass percent of the low-melting-point metal powder is 5-20%.
3. The method for continuously extruding elemental mixed powder to prepare the alloy semi-solid thixotropic billet according to claim 1 or 2, wherein the method comprises the following steps: the conditions of secondary remelting are as follows: (1) reaching the melting point of the low-melting-point metal powder, and preserving the heat for 10-30 minutes to ensure that at least a liquid phase with the volume fraction of more than 5 percent exists in the semi-solid blank; (2) the high melting point metal powder welding matrix generates recrystallization transformation above the recrystallization temperature, and ensures that high temperature solid phase recrystallization is changed into isometric crystal.
4. The method for preparing the alloy semi-solid thixotropic billet by continuously extruding the elemental mixed powder according to claim 1, wherein the method comprises the following steps: in the step (1), the mixing process of the metal powder in the powder mixer is more than 30 minutes, and the rotating speed of the extrusion roller is 4-7 rpm.
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| CN113770357A (en) * | 2021-09-15 | 2021-12-10 | 昆明理工大学 | Device and method for rapidly preparing multi-element alloy material with continuously-changed components by microwaves |
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