[go: up one dir, main page]

CN112981195A - High-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof - Google Patents

High-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof Download PDF

Info

Publication number
CN112981195A
CN112981195A CN202110193788.2A CN202110193788A CN112981195A CN 112981195 A CN112981195 A CN 112981195A CN 202110193788 A CN202110193788 A CN 202110193788A CN 112981195 A CN112981195 A CN 112981195A
Authority
CN
China
Prior art keywords
alloy
magnesium
silicon
calcium
aluminum
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CN202110193788.2A
Other languages
Chinese (zh)
Other versions
CN112981195B (en
Inventor
边丽萍
郑毅
薛峰平
梁伟
赵兴国
田丰
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Taiyuan University of Technology
Original Assignee
Taiyuan University of Technology
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Taiyuan University of Technology filed Critical Taiyuan University of Technology
Priority to CN202110193788.2A priority Critical patent/CN112981195B/en
Publication of CN112981195A publication Critical patent/CN112981195A/en
Application granted granted Critical
Publication of CN112981195B publication Critical patent/CN112981195B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • 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
    • 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
    • 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
    • C22F1/047—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 magnesium as the next major constituent
    • 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Conductive Materials (AREA)

Abstract

本发明公开了一种高强度铝镁硅钙导电铝合金及制备方法。高强度铝镁硅钙导电铝合金中各元素质量百分比为Mg 0.59～0.9％，Si0.5～0.9％，Ca 0.253～0.386％，余量为Al，杂质含量≤0.1％；本发明以Al块(纯度为99.8％以上)、Al‑12Si中间合金、Mg‑10Al‑27Ca共晶型中间合金为原料，采用普通重力铸造方法熔炼制备铸态Al‑Mg‑Si‑Ca合金；经固溶、水淬及预时效处理后，通过控制压下量进行冷轧、热轧两道次轧制，最后进行时效处理，制成高强度铝镁硅钙导电铝合金。以此方法制备的高强度铝镁硅钙导电铝合金在较高电导率下，实现了力学性能的大幅度提升，扩大了其在输电领域的应用。

Figure 202110193788

The invention discloses a high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and a preparation method. The mass percentage of each element in the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy is Mg 0.59-0.9%, Si 0.5-0.9%, Ca 0.253-0.386%, the balance is Al, and the impurity content is less than or equal to 0.1%; (purity is more than 99.8%), Al-12Si master alloy, Mg-10Al-27Ca eutectic type master alloy as raw materials, using ordinary gravity casting method to prepare as-cast Al-Mg-Si-Ca alloy; After quenching and pre-aging treatment, two passes of cold rolling and hot rolling are carried out by controlling the reduction amount, and finally the aging treatment is carried out to produce a high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy. The high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy prepared by this method achieves a substantial improvement in mechanical properties under higher electrical conductivity, and expands its application in the field of power transmission.

Figure 202110193788

Description

High-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof
Technical Field
The invention relates to the technical field of processing and preparation of conductive aluminum alloy, in particular to a high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and a preparation method thereof.
Background
With the continuous development of economy in China, the demand of various industries on power utilization is increased year by year, and a wire material with the characteristics of light weight, high conductivity and high strength is urgently needed. The 6xxx aluminum-magnesium-silicon alloy is often used as an overhead power transmission conductor because of high conductivity, high specific strength, good corrosion resistance and long service life. At present, the aluminum-magnesium-silicon alloy wire is industrially prepared by adopting the traditional process, which comprises solution treatment, water quenching after solution treatment, cold drawing and artificial aging. The aluminum-magnesium-silicon alloy prepared by the method has the tensile strength of 255-325 MPa and the electric conductivity of 52.5-57.5% IACS (International annealed copper standard). Therefore, the aluminum-magnesium-silicon alloy wire used in the industry at present has the problems that the conductivity is slightly high, but the strength is low, and the two contradictory with each other, so that the application of the aluminum-magnesium-silicon alloy wire in the field of long-distance power transmission is greatly limited. How to obtain an aluminum alloy wire with high strength and high conductivity becomes a technical problem which needs to be solved urgently in the current electric power energy industry.
The existing method for improving the strength of the aluminum-magnesium-silicon alloy mainly comprises the following steps: (1) alloying, such as adding elements such as Ca, Mn, Sc, etc., but in general, the electrical conductivity of the alloy is inevitably lost while the strength is improved by alloying; (2) machining deformation, such as equal channel angular extrusion, rolling deformation and the like, wherein if the grains of the deformed aluminum alloy matrix are refined and the solute atom content is reduced due to the precipitation of a second phase, the strength and the conductivity can be simultaneously improved due to the machining deformation; (3) and heat treatment, such as solution treatment and aging treatment, improves the microstructure of the alloy and enhances the strength and the electric conductivity of the alloy.
By retrieval, the CN201810208279.0 patent introduces a 'preparation method of high-strength high-conductivity aluminum-magnesium-silicon-calcium alloy', the conductivity of the alloy prepared by vacuum melting and equal channel angular pressing methods reaches 57.2 percent IACS, and the tensile strength is 370 MPa. The CN201811445500.0 patent introduces a 'preparation method of a high-strength high-conductivity aluminum alloy wire', the conductivity of the prepared aluminum alloy wire is 55.5% -58.5% IACS, the elongation is 2.0-4.0%, and the tensile strength is 310-350 MPa. The CN201711465441.9 patent introduces a heat-resistant aluminum alloy wire with high strength and high conductivity and a preparation method thereof, the conductivity of the prepared heat-resistant aluminum wire reaches 62 percent IACS, but the tensile strength is 322MPa at most. Therefore, in order to make the aluminum-magnesium-silicon alloy more widely and effectively applied in the field of power transmission, the strength of the aluminum-magnesium-silicon alloy is urgently required to be greatly improved under the condition of high conductivity.
Disclosure of Invention
The invention aims to prepare a high-strength conductive aluminum alloy, and provides a high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and a preparation method thereof.
In order to achieve the purpose, the invention provides the following technical scheme:
one of the technical schemes of the invention is as follows: the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy comprises, by mass, 0.59-0.9% of Mg, 0.5-0.9% of Si, 0.253-0.386% of Ca and the balance of Al, wherein the impurity content is less than or equal to 0.1%.
Preferably, the raw materials of the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy comprise an Al block, an Al-12Si intermediate alloy and an Mg-10Al-27Ca eutectic intermediate alloy.
More preferably, the purity of the Al block is 99.8% or more.
Preferably, the preparation method of the Mg-10Al-27Ca eutectic intermediate alloy comprises the following steps:
preparing Al block (purity over 99.8%) and Mg-30Ca intermediate alloy according to element proportion; under the protection of inert gas, firstly, keeping the temperature of an Al block at 700-720 ℃ for 20min, after the Al block is melted, removing floating slag, then adding Mg-30Ca intermediate alloy, scattering a covering agent (RJ-2 flux) on the surface of a melt, keeping the temperature at 720-740 ℃ for 20min, removing slag after the heat preservation is finished, adding the RJ-2 flux for refining, finally keeping the temperature at 690-700 ℃ for 20min to prepare a melt, and pouring the obtained melt to prepare the Mg-10Al-27Ca intermediate alloy.
Mg-10Al-27Ca is a eutectic intermediate alloy, fine and uniformly dispersed intermetallic compounds exist in the matrix structure of the eutectic intermediate alloy, and when the eutectic intermediate alloy is added into aluminum alloy as a raw material, fine and uniformly dispersed (Mg, Al) can be formed in the solidification structure of the as-cast aluminum alloy according to the tissue genetic principle2A Ca particle reinforcing phase. And high density and small (Mg, Al)2The Ca particle reinforcing phase can promote Mg in aluminum matrix2The Si particle reinforced phase is greatly separated out, so that the solid solubility of Mg atoms in an aluminum matrix is obviously reduced, and the strength and the conductivity of the aluminum-magnesium-silicon-calcium alloy are improved.
The addition of Si in the form of Al-12Si intermediate alloy can obviously reduce the melting point of Si, so that the raw materials are easier to melt, and the oxidation in the melting process can be reduced.
The second technical scheme of the invention is as follows: the preparation method of the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy is characterized in that an Al block, an Al-12Si intermediate alloy and an Mg-10Al-27Ca eutectic intermediate alloy are used as raw materials to prepare an as-cast alloy, and the as-cast alloy is rolled twice to prepare the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy.
Preferably, the cast alloy is subjected to solution treatment before rolling, water quenching and pre-aging treatment after solution treatment, and aging treatment after two times of rolling. The solid solution treatment can ensure that the alloy elements are fully solid-dissolved and the as-cast alloy components are uniform; the pre-aging treatment can precipitate a certain amount of nano precipitated phase in advance.
More preferably, the temperature of the solution treatment is 500-560 ℃, and the time is 3-5 h; the temperature of the pre-aging treatment is 150-180 ℃, and the time is 1-2 h; the temperature of the aging treatment is 130-150 ℃, and the time is 18-30 h.
Preferably, the two-pass rolling is specifically a first-pass cold rolling and a second-pass hot rolling. After the first cold rolling, high-density dislocation is generated in the alloy matrix, and the precipitated phase and the dislocation have interaction (the precipitated phase pins the dislocation), so that the rapid formation of a large-angle grain boundary in the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy matrix crystal grains is promoted, the grain refinement is accelerated, the formation of cellular elongated crystal grains is inhibited, the texture is reduced, and the strength and the plastic toughness of the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy are improved.
Preferably, the first rolling reduction of the two-pass rolling is 46%, the second rolling reduction is 37.8%, and the total reduction of the two-pass rolling is 66.6%. The high strength and toughness of the aluminum-magnesium-silicon-calcium alloy can be realized only by carrying out two times of conventional rolling, wherein the total deformation is far less than the ECAP strong plastic deformation (the strain of ECAP per pass is about 100%). The process is simple to operate, the equipment is conventional, and the industrial production is easy to realize.
More preferably, after the solid solution and pre-aging alloy plate is rolled at room temperature for the first time, the solid solution and pre-aging alloy plate is placed into a vacuum tube furnace heated to 250-350 ℃ under the protection of argon, is taken out after heat preservation is carried out for 5-10 min, and is immediately rolled for the second time. The short-time heating can partially eliminate dislocation, promote recovery and reduce residual stress, and is favorable for the second pass rolling; the second pass rolling can continuously promote the precipitation of a high-density second phase and refine aluminum matrix grains.
Preferably, the method of preparing the as-cast alloy comprises: preparing Al blocks, Al-12Si intermediate alloy and Mg-10Al-27Ca eutectic intermediate alloy according to element proportion; under the protection of inert gas, firstly, preserving heat of an Al block and an Al-12Si intermediate alloy for 30-40 min at the temperature of 740-760 ℃, after the raw materials are melted, removing floating slag, then adding an Mg-10Al-27Ca eutectic intermediate alloy, scattering a covering agent on the surface of a melt, continuously preserving heat for 20-30 min at the temperature of 720-740 ℃, removing slag after heat preservation, adding a refining agent for refining, finally preserving heat for 20-30 min at the temperature of 700-720 ℃ to prepare a melt, and pouring the obtained melt to prepare the as-cast alloy.
The invention has the following beneficial technical effects:
the invention adopts the Mg-10Al-27Ca eutectic crystal which is added and designed to be prepared in 6201 alloyThe intermediate alloy combines solid solution, pre-aging treatment, rolling deformation and subsequent aging treatment to refine the crystal grains of the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy matrix, the average crystal grain size is less than or equal to 0.2 mu m, and fine Mg is uniformly dispersed and distributed in the matrix2Si、(Mg,Al)2The Ca second phase, so that the strength of the prepared high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy is greatly improved under the condition of higher conductivity.
The high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy prepared by the invention has yield strength of 348MPa, tensile strength of 523MPa, elongation of 5.4% and conductivity of 46.77% IACS.
The preparation method of the high-strength conductive aluminum alloy provided by the invention has the advantages of simple process, conventional equipment, easiness in industrial production, low cost of the used alloy system and excellent comprehensive performance.
Drawings
FIG. 1 is a graph of as-cast OM of Mg-10Al-27Ca master alloy used in examples and comparative examples 2 to 3.
FIG. 2 is an as-cast OM diagram of the Mg-30Ca master alloy used in comparative example 1.
Fig. 3 is an OM diagram of the high strength al-mg-si-ca conductive aluminum alloy prepared in example 1.
FIG. 4 is a TEM structural image of the high-strength Al-Mg-Si-Ca conductive aluminum alloy prepared in example 1.
FIG. 5 is a tensile stress-strain curve of the high strength Al-Mg-Si-Ca conductive aluminum alloy of example 1.
Detailed Description
Reference will now be made in detail to various exemplary embodiments of the present invention, examples of which are illustrated in the accompanying drawings, and this detailed description should not be taken to be limiting of the invention, but is rather a more detailed description of certain aspects, features and embodiments of the invention. It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.
Further, for numerical ranges in this disclosure, it is understood that each intervening value, between the upper and lower limit of that range, is also specifically disclosed. Every smaller range between any stated value or intervening value in a stated range and any other stated or intervening value in a stated range is encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention.
As used herein, the terms "comprising," "including," "having," "containing," and the like are open-ended terms that mean including, but not limited to.
The preparation method of the Mg-10Al-27Ca eutectic intermediate alloy used in the embodiment and the comparative example of the invention comprises the following steps: preparing Al block (purity over 99.8%) and Mg-30Ca intermediate alloy according to element proportion; under the protection of inert gas, firstly, keeping the temperature of an Al block at 700-720 ℃ for 20min, after the Al block is melted, removing floating slag, then adding Mg-30Ca intermediate alloy, scattering a covering agent (RJ-2 flux) on the surface of a melt, keeping the temperature at 720-740 ℃ for 20min, removing slag after the heat preservation is finished, adding the RJ-2 flux for refining, finally keeping the temperature at 690-700 ℃ for 20min to prepare a melt, and pouring the obtained melt to prepare the Mg-10Al-27Ca intermediate alloy.
Example 1
The high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy comprises, by mass, 0.59% of Mg, 0.54% of Si, 0.253% of Ca and the balance of Al, wherein the content of impurities is less than or equal to 0.1%, and the preparation method comprises the following steps:
(1) melting as-cast alloys
The preparation of the alloy is completed in a crucible resistance furnace by adopting a common gravity casting method under the protection of argon gas:
472.82g of weighed and ground Al blocks (the purity is more than 99.8 percent), 22.5g of Al-12Si intermediate alloy, 4.68g of Mg-10Al-27Ca eutectic intermediate alloy, and the weighed covering agent and refining agent are put into a drying oven for drying.
Secondly, brushing materials: and (3) putting the graphite crucible into a resistance furnace for heating, starting brushing when the temperature reaches 400 ℃, and uniformly and firmly attaching the prepared coating to the inner wall of the crucible for at least three times.
Feeding: and after finishing brushing, adding the dried Al block and the Al-12Si intermediate alloy into the crucible, introducing argon for protection, keeping the temperature for 30min after the furnace temperature is raised to 760 ℃, and waiting for the raw materials to be molten.
Slagging off and feeding: after the raw materials are completely melted, the power supply is closed, the furnace door is opened, the tool is used for removing the scum on the surface, then the Mg-10Al-27Ca eutectic intermediate alloy wrapped by the aluminum foil is added, then the dried covering agent is scattered on the surface of the melt, the furnace door is closed, the power supply is opened, and the temperature is kept for 20min after the temperature is increased to 740 ℃.
And fifthly, refining: after heat preservation, the power supply is turned off, slag is removed, and then the dried refining agent is poured into the melt and fully stirred. After stirring, the furnace door is closed, the power supply is turned on, the temperature is raised to 720 ℃, and then the temperature is kept for 20 min.
Pouring: and after opening the furnace and removing slag, taking out the smelting crucible, and pouring until the steel mould pouring gate is fully poured.
(2) Wire-electrode cutting casting
And (2) taking the casting obtained in the step (1) out of the die, and cutting the casting into rectangular blocks with the size of 50mm multiplied by 20mm multiplied by 4mm by a linear cutting machine.
(3) Solid solution and pre-aging treatment
Solution treatment: coating Vaseline on the surface of the rectangular block, wrapping the rectangular block with aluminum foil, burying the rectangular block in an iron box filled with graphite powder, placing the rectangular block in a box type resistance furnace, and carrying out solution treatment for 5 hours at 550 ℃; after the solution treatment, the steel is immediately quenched by cold water at 20 ℃ for less than or equal to 10 s.
Pre-aging treatment: and putting the quenched rectangular block into a box-type resistance furnace at the temperature of 180 ℃ again for heat preservation for 2h, taking out the rectangular block, and cooling the rectangular block to room temperature in the air.
(4) Rolling of
A two-roll flat rolling mill is adopted, the roll gap is debugged by using waste materials before the experiment, and the roll gap is debugged to the expected thickness.
Before rolling, the rectangular blocks treated in the step (3) are ground by 240-mesh sand paper to remove surface defects.
Primary rolling: and rotating the switch to rotate the roller for rolling. After one-pass rolling, the rectangular block is rolled into a thin plate, the thickness of the thin plate is rolled from 3.65mm to 1.96mm, and the rolling reduction reaches 46%.
And (3) rolling for two times: before two-pass rolling, the sheet after one-pass rolling is placed into a 300 ℃ tubular heating furnace for heat preservation for 5min (argon protection), the roll gap thickness is adjusted, after 5min, the sheet is rapidly taken out of the furnace and immediately rolled, the thickness of the sheet is rolled from 1.96mm to 1.22mm, and the reduction is 37.8%. The total pressure reduction in the two passes was 66.6%.
(5) Aging treatment
And (4) wrapping the thin plate obtained in the step (4) with aluminum foil, and placing the thin plate into a tubular heating furnace for aging treatment at the temperature of 130 ℃ for 24 hours. After the aging treatment, the specimens were allowed to cool to room temperature in air.
Example 2
The high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy comprises, by mass, 0.59% of Mg, 0.50% of Si, 0.253% of Ca and the balance of Al, wherein the content of impurities is less than or equal to 0.1%, and the preparation method comprises the following steps:
(1) melting as-cast alloys
The preparation of the alloy is completed in a crucible resistance furnace by adopting a common gravity casting method under the protection of argon gas:
474.49g of weighed and ground Al blocks (the purity is more than 99.8 percent), 20.83g of Al-12Si intermediate alloy, 4.68g of Mg-10Al-27Ca eutectic intermediate alloy, and the weighed covering agent and refining agent are put into a drying oven for drying.
Secondly, brushing materials: and (3) putting the graphite crucible into a resistance furnace for heating, starting brushing when the temperature reaches 400 ℃, and uniformly and firmly attaching the prepared coating to the inner wall of the crucible for at least three times.
Feeding: and after finishing brushing, adding the dried Al block and the Al-12Si intermediate alloy into the crucible, introducing argon for protection, keeping the temperature for 40min after the furnace temperature is increased to 750 ℃, and waiting for the raw materials to be molten.
Slagging off and feeding: after the raw materials are completely melted, the power supply is closed, the furnace door is opened, the floating slag on the surface is removed by a tool, then Mg-10Al-27Ca eutectic intermediate alloy wrapped by aluminum foil is added, then the dried covering agent is scattered on the surface of the melt, the furnace door is closed, the power supply is opened, and the temperature is kept for 30min after the temperature is raised to 730 ℃.
And fifthly, refining: after heat preservation, the power supply is turned off, slag is removed, and then the dried refining agent is poured into the melt and fully stirred. After stirring, the furnace door is closed, the power supply is turned on, the temperature is raised to 710 ℃, and then the temperature is kept for 20 min.
Pouring: and after opening the furnace and removing slag, taking out the smelting crucible, and pouring until the steel mould pouring gate is fully poured.
(2) Wire-electrode cutting casting
And (2) taking the casting obtained in the step (1) out of the die, and cutting the casting into rectangular blocks with the size of 50mm multiplied by 20mm multiplied by 4mm by a linear cutting machine.
(3) Solid solution and pre-aging treatment
Solution treatment: coating Vaseline on the surface of the rectangular block, wrapping the rectangular block with aluminum foil, burying the rectangular block in an iron box filled with graphite powder, placing the rectangular block in a box type resistance furnace, and carrying out solution treatment for 3 hours at 560 ℃; after solid solution, quenching the steel plate by cold water at 20 ℃ for less than or equal to 10 s.
Pre-aging treatment: and putting the quenched rectangular block into a box-type resistance furnace at the temperature of 150 ℃ for heat preservation for 2h, taking out the rectangular block, and cooling the rectangular block to room temperature in the air.
(4) Rolling of
A two-roll flat rolling mill is adopted, the roll gap is debugged by using waste materials before the experiment, and the roll gap is debugged to the expected thickness.
Before rolling, the rectangular blocks treated in the step (3) are ground by 240-mesh sand paper to remove surface defects.
Primary rolling: and rotating the switch to rotate the roller for rolling. After one-pass rolling, the rectangular block is rolled into a thin plate, the thickness of the thin plate is rolled from 3.65mm to 1.96mm, and the rolling reduction reaches 46%.
And (3) rolling for two times: before two-pass rolling, the sheet after one-pass rolling is placed into a tube heating furnace at 250 ℃ for heat preservation for 10min (argon protection), the roll gap thickness is adjusted, after 10min, the sheet is rapidly taken out of the furnace and immediately rolled, the thickness of the sheet is rolled from 1.96mm to 1.22mm, and the reduction is 37.8%. The total pressure reduction in the two passes was 66.6%.
(5) Aging treatment
And (4) wrapping the thin plate obtained in the step (4) with aluminum foil, and placing the thin plate into a tubular heating furnace for aging treatment at the temperature of 150 ℃ for 18 hours. After the aging treatment, the specimens were allowed to cool to room temperature in air.
Example 3
The high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy comprises, by mass, 0.59% of Mg, 0.9% of Si, 0.253% of Ca and the balance of Al, wherein the content of impurities is less than or equal to 0.1%, and the preparation method comprises the following steps:
(1) melting as-cast alloys
The preparation of the alloy is completed in a crucible resistance furnace by adopting a common gravity casting method under the protection of argon gas:
457.82g of weighed and ground Al blocks (the purity is more than 99.8 percent), 37.5g of Al-12Si intermediate alloy, 4.68g of Mg-10Al-27Ca eutectic intermediate alloy, and the weighed covering agent and refining agent are put into a drying oven for drying.
Secondly, brushing materials: and (3) putting the graphite crucible into a resistance furnace for heating, starting brushing when the temperature reaches 400 ℃, and uniformly and firmly attaching the prepared coating to the inner wall of the crucible for at least three times.
Feeding: and after finishing brushing, adding the dried Al block and the Al-12Si intermediate alloy into the crucible, introducing argon for protection, keeping the temperature for 35min after the furnace temperature is raised to 760 ℃, and waiting for the raw materials to be molten.
Slagging off and feeding: after the raw materials are completely melted, closing the power supply, opening the furnace door, removing floating slag on the surface by a tool, adding Mg-10Al-27Ca eutectic intermediate alloy wrapped by aluminum foil, then scattering the dried covering agent on the surface of the melt, closing the furnace door, opening the power supply, and preserving heat for 30min after the temperature is raised to 720 ℃.
And fifthly, refining: after heat preservation, the power supply is turned off, slag is removed, and then the dried refining agent is poured into the melt and fully stirred. After stirring, the furnace door is closed, the power supply is turned on, the temperature is raised to 700 ℃, and then the temperature is kept for 30 min.
Pouring: and after opening the furnace and removing slag, taking out the smelting crucible, and pouring until the steel mould pouring gate is fully poured.
(2) Wire-electrode cutting casting
And (2) taking the casting obtained in the step (1) out of the die, and cutting the casting into rectangular blocks with the size of 50mm multiplied by 20mm multiplied by 4mm by a linear cutting machine.
(3) Solid solution and pre-aging treatment
Solution treatment: coating Vaseline on the surface of the rectangular block, wrapping the rectangular block with aluminum foil, burying the rectangular block in an iron box filled with graphite powder, placing the rectangular block in a box type resistance furnace, and carrying out solution treatment for 5 hours at 500 ℃; after solid solution, quenching the steel plate by cold water at 20 ℃ for less than or equal to 10 s.
Pre-aging treatment: and putting the quenched rectangular block into a box-type resistance furnace at the temperature of 180 ℃ again for heat preservation for 1h, taking out the rectangular block, and cooling the rectangular block to room temperature in the air.
(4) Rolling of
A two-roll flat rolling mill is adopted, the roll gap is debugged by using waste materials before the experiment, and the roll gap is debugged to the expected thickness.
Before rolling, the rectangular blocks treated in the step (3) are ground by 240-mesh sand paper to remove surface defects.
Primary rolling: and rotating the switch to rotate the roller for rolling. After one-pass rolling, the rectangular block is rolled into a thin plate, the thickness of the thin plate is rolled from 3.65mm to 1.96mm, and the rolling reduction reaches 46%.
And (3) rolling for two times: before two-pass rolling, the sheet after one-pass rolling is placed into a 350 ℃ tubular heating furnace for heat preservation for 5min (argon protection), the roll gap thickness is adjusted, after 5min, the sheet is rapidly taken out of the furnace and immediately rolled, the thickness of the sheet is rolled from 1.96mm to 1.22mm, and the reduction is 37.8%. The total pressure reduction in the two passes was 66.6%.
(5) Aging treatment
And (4) wrapping the thin plate obtained in the step (4) with aluminum foil, and placing the thin plate into a tubular heating furnace for aging treatment at the temperature of 130 ℃ for 30 hours. After the aging treatment, the specimens were allowed to cool to room temperature in air.
Comparative example 1
Compared with the example 1, the difference is that Mg-10Al-27Ca eutectic type master alloy is not used, and the added raw materials are 473.29g of Al block, 22.5g of Al-12Si master alloy and 4.21g of Mg-30Ca master alloy. The step of adding the Mg-30Ca master alloy is the same as the step of adding the Mg-10Al-27Ca eutectic type master alloy, and other steps and parameters are the same as those in the embodiment 1.
Comparative example 2
Compared with the embodiment 1, the difference is that the first cold rolling reduction is 35.2%; the hot rolling reduction of the second pass is 31.0 percent, and the total reduction of the two passes is 55.3 percent; the other steps and parameters were the same as those in example 1.
Comparative example 3
Compared with the embodiment 1, the difference is that the first cold rolling reduction is 49.2%; the second hot rolling reduction is 49.5 percent, and the total reduction of the two times of rolling is 74.3 percent; the other steps and parameters were the same as those in example 1.
FIG. 1 is a graph of as-cast OM of Mg-10Al-27Ca master alloy used in examples and comparative examples 2 to 3. As can be seen from FIG. 1, Mg-10Al-27Ca is a eutectic master alloy, except for primary (Mg, Al)2Eutectic Mg in the matrix outside the Ca phase2The Ca phase is much finer.
FIG. 2 is an as-cast OM diagram of the Mg-30Ca master alloy used in comparative example 1. From FIG. 2, Mg in the matrix can be seen2Ca is relatively coarse.
Fig. 3 is an OM diagram of the high strength al-mg-si-ca conductive aluminum alloy prepared in example 1. As can be seen from FIG. 3, Mg is uniformly dispersed and distributed in the rolled and aged high-strength Al-Mg-Si-Ca conductive aluminum alloy matrix2Si granular phase, (Mg, Al)2A particulate phase of Ca.
FIG. 4 is a TEM structural image of the high-strength Al-Mg-Si-Ca conductive aluminum alloy prepared in example 1. As can be seen from FIG. 4, the average grain size in the rolled and aged high-strength Al-Mg-Si-Ca conductive Al-Mg-Al alloy matrix is less than or equal to 0.2 μm, and a large number of dislocations exist in the matrix.
FIG. 5 is a tensile stress-strain curve of the high strength Al-Mg-Si-Ca conductive aluminum alloy of example 1. The figure shows that the yield strength reaches 348MPa, the tensile strength reaches 523MPa, and the elongation reaches 5.4%.
At room temperature, a Sigma 2008B handheld eddy current conductivity meter is adopted, five positions of the sample are selected for measurement, the average value of the conductivity is taken, and finally the conductivity of the aluminum-magnesium-calcium-silicon alloy prepared in example 1, comparative example 2 and comparative example 3 is 46.77% IACS, 52.4% IACS, 47.80% IACS and 47.45% IACS respectively.
The mechanical properties and conductivity of the aluminum alloys prepared in example 1 and comparative examples 1 to 3 were measured, and the results are shown in table 1.
TABLE 1 mechanical and conductivity properties of aluminum alloys
Performance of Yield strength/MPa Tensile strength/MPa Elongation/percent conductivity/IACS
Example 1 348 523 5.4 46.77
Comparative example 1 133 248 5.8 52.40
Comparative example 2 155 331 4.3 47.80
Comparative example 3 283 353 5.7 47.45
As can be seen from table 1, the strength of the al-mg-si-ca alloy prepared in comparative example 1 is lower than that of example 1 because: according to the principle of tissue inheritance, the cast solidification structure of example 1 has fine uniformly dispersed (Mg, Al)2Ca particulate phase which promotes Mg in the aluminum matrix2Since a large amount of Si reinforcing phase was precipitated, the strength was higher and the electrical conductivity was lower in example 1 at the same reduction.
The strength of the al-mg-si-ca alloy prepared in comparative example 2 is lower than that of example 1 because: example 1 because of the larger rolling reduction, the deformed matrix has finer grain size and more fine Mg2The Si particle phase is dispersed in the aluminum matrix, making it stronger.
The strength of the al-mg-si-ca alloy prepared in comparative example 3 is lower than that of example 1 because: in comparative example 3, the alloy undergoes dynamic recovery and recrystallization during rolling at a large reduction, so that compared with example 1, the size of matrix grains is increased, the dislocation density is reduced, precipitated phases are increased, the number is reduced, and the strength is reduced.
The above-described embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements of the technical solutions of the present invention can be made by those skilled in the art without departing from the spirit of the present invention, and the technical solutions of the present invention are within the scope of the present invention defined by the claims.

Claims (10)

1.一种高强度铝镁硅钙导电铝合金，其特征在于，所述高强度铝镁硅钙导电铝合金中各元素质量百分比为Mg 0.59～0.9％，Si 0.5～0.9％，Ca 0.253～0.386％，余量为Al，杂质含量≤0.1％。1. a high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy, characterized in that, in the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy, the mass percentages of each element are Mg 0.59～0.9%, Si 0.5～0.9%, Ca 0.253～ 0.386%, the balance is Al, and the impurity content is less than or equal to 0.1%. 2.根据权利要求1所述的高强度铝镁硅钙导电铝合金，其特征在于，所述高强度铝镁硅钙导电铝合金的原料包括Al块、Al-12Si中间合金、Mg-10Al-27Ca共晶型中间合金。2. The high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 1, wherein the raw materials of the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy comprise Al block, Al-12Si master alloy, Mg-10Al- 27Ca eutectic master alloy. 3.根据权利要求2所述的高强度铝镁硅钙导电铝合金，其特征在于，所述Mg-10Al-27Ca共晶型中间合金的制备方法为：按元素比例配制Al块、Mg-30Ca中间合金；在惰性气体的保护下，先将Al块在700～720℃的温度下保温20min，待Al块熔化后，扒去浮渣，然后加入Mg-30Ca中间合金，并将覆盖剂撒到熔体表面，继续在720～740℃的温度下保温20min，保温结束后扒渣，添加RJ-2熔剂进行精炼，最后在690～700℃保温20min制得熔体，所得熔体浇注，制得Mg-10Al-27Ca中间合金。3. high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 2, is characterized in that, the preparation method of described Mg-10Al-27Ca eutectic master alloy is: prepare Al block, Mg-30Ca by element ratio Master alloy; under the protection of inert gas, the Al block is first kept at a temperature of 700 ~ 720 ℃ for 20 minutes. After the Al block is melted, the scum is removed, then the Mg-30Ca master alloy is added, and the covering agent is sprinkled on the The surface of the melt is kept at a temperature of 720 to 740°C for 20 minutes. After the heat preservation is completed, the slag is removed, and RJ-2 flux is added for refining. Finally, the melt is kept at a temperature of 690 to 700°C for 20 minutes to obtain a melt. Mg-10Al-27Ca master alloy. 4.一种根据权利要求2-3任一项所述高强度铝镁硅钙导电铝合金的制备方法，其特征在于，以Al块、Al-12Si中间合金、Mg-10Al-27Ca共晶型中间合金为原料制备铸态合金，铸态合金经过两道次轧制，制得所述高强度铝镁硅钙导电铝合金。4. according to the preparation method of the described high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to any one of claims 2-3, it is characterized in that, with Al block, Al-12Si master alloy, Mg-10Al-27Ca eutectic type The intermediate alloy is used as the raw material to prepare the as-cast alloy, and the as-cast alloy is rolled twice to obtain the high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy. 5.根据权利要求4所述的高强度铝镁硅钙导电铝合金的制备方法，其特征在于，铸态合金轧制前进行固溶处理，固溶后水淬和预时效处理，两道次轧制后进行时效处理。5. The preparation method of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 4, characterized in that, solution treatment is carried out before as-cast alloy rolling, water quenching and pre-aging treatment after solutionization, two passes Aging treatment is carried out after rolling. 6.根据权利要求5所述的高强度铝镁硅钙导电铝合金的制备方法，其特征在于，所述固溶处理的温度为500～560℃，时间为3～5h；所述预时效处理的温度为150～180℃，时间为1～2h；所述时效处理的温度为130～150℃，时间为18～30h。6 . The preparation method of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 5 , wherein the temperature of the solution treatment is 500-560° C. and the time is 3-5h; the pre-aging treatment is performed for 3-5 hours. 7 . The temperature of the aging treatment is 150-180°C, and the time is 1-2h; the temperature of the aging treatment is 130-150°C, and the time is 18-30h. 7.根据权利要求4所述的高强度铝镁硅钙导电铝合金的制备方法，其特征在于，所述两道次轧制具体为第一道次冷轧和第二道次热轧。7 . The method for preparing a high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 4 , wherein the two-pass rolling is specifically a first-pass cold rolling and a second-pass hot rolling. 8 . 8.根据权利要求4所述的高强度铝镁硅钙导电铝合金的制备方法，其特征在于，所述两道次轧制的第一道次轧制压下量为46％，第二道次轧制压下量为37.8％。8. The preparation method of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 4, wherein the rolling reduction of the first pass of the two passes is 46%, and the second pass rolling reduction is 46%. The secondary rolling reduction was 37.8%. 9.根据权利要求4所述的高强度铝镁硅钙导电铝合金的制备方法，其特征在于，所述铸态合金经第一道次室温轧制后，在通氩气保护的情况下，放入已加热至250～350℃的真空管式炉中，保温5～10min后取出，立即进行第二道次轧制。9. The preparation method of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 4, wherein, after the as-cast alloy is rolled at room temperature for the first time, under the protection of argon gas, Put it into a vacuum tube furnace that has been heated to 250-350°C, keep it warm for 5-10 minutes, take it out, and immediately carry out the second pass rolling. 10.根据权利要求4所述的高强度铝镁硅钙导电铝合金的制备方法，其特征在于，制备铸态合金的方法包括：按元素比例配制Al块、Al-12Si中间合金、Mg-10Al-27Ca共晶型中间合金；在惰性气体保护下，先将Al块和Al-12Si中间合金在740～760℃的温度下保温30～40min，待原料熔化后，扒去浮渣，然后加入Mg-10Al-27Ca共晶型中间合金，并将覆盖剂撒到熔体表面，继续在720～740℃的温度下保温20～30min，保温结束后扒渣，添加精炼剂进行精炼，最后在700～720℃的温度下保温20～30min制得熔体，所得熔体浇注，制得铸态合金。10. The preparation method of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy according to claim 4, wherein the method for preparing the as-cast alloy comprises: preparing Al block, Al-12Si master alloy, Mg-10Al according to the element ratio -27Ca eutectic master alloy; under the protection of inert gas, the Al block and the Al-12Si master alloy are first kept at a temperature of 740 to 760 ° C for 30 to 40 minutes. After the raw materials are melted, the scum is removed, and then Mg is added. -10Al-27Ca eutectic master alloy, sprinkle the covering agent on the surface of the melt, continue to keep it at a temperature of 720 ~ 740 ℃ for 20 ~ 30 minutes, remove the slag after the insulation, add a refining agent for refining, and finally at 700 ~ The melt is obtained by holding the temperature at 720° C. for 20-30 minutes, and the obtained melt is poured to obtain the as-cast alloy.
CN202110193788.2A 2021-02-20 2021-02-20 A kind of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof Active CN112981195B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202110193788.2A CN112981195B (en) 2021-02-20 2021-02-20 A kind of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202110193788.2A CN112981195B (en) 2021-02-20 2021-02-20 A kind of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof

Publications (2)

Publication Number Publication Date
CN112981195A true CN112981195A (en) 2021-06-18
CN112981195B CN112981195B (en) 2021-12-21

Family

ID=76393919

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202110193788.2A Active CN112981195B (en) 2021-02-20 2021-02-20 A kind of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof

Country Status (1)

Country Link
CN (1) CN112981195B (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114015915A (en) * 2021-10-25 2022-02-08 宁波吉胜铸业有限公司 Wear-resisting pump cover
CN115198213A (en) * 2022-08-10 2022-10-18 华南理工大学 A composite deformation heat treatment method for regulating the electrical conductivity and mechanical properties of aluminum alloys
CN115725879A (en) * 2022-12-02 2023-03-03 广东远光电缆实业有限公司 High-conductivity aluminum alloy conductor and preparation method thereof

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000192180A (en) * 1998-12-22 2000-07-11 Nippon Light Metal Co Ltd Die-cast scroll excellent in fatigue strength and method of manufacturing the same
FR2827306A1 (en) * 2001-07-10 2003-01-17 Pechiney Aluminium Ductile aluminum alloy, used for casting under pressure of structural and security components for motor vehicles, comprises alloying additions of silicon, element for reducing adherence on mold, and element for eutectic modification
CN1639373A (en) * 2002-03-01 2005-07-13 昭和电工株式会社 Process for producing Al-Mg-Si alloy plate, Al-Mg-Si alloy plate and Al-Mg-Si alloy material
CN106480384A (en) * 2016-11-08 2017-03-08 广西科技大学 A kind of milling method of ultrahigh-strength aluminum alloy sheet material
CN106637008A (en) * 2016-11-08 2017-05-10 广西科技大学 Rolling method for high-strength aluminum alloy plate
CN108456796A (en) * 2018-03-13 2018-08-28 太原理工大学 A kind of preparation method of high-strength and high-conductivity magnalium calcium-silicon
CN110172621A (en) * 2019-06-24 2019-08-27 辽宁瑞鸥新材料科技有限公司 A kind of high-strength highly-conductive Al-Mg-Si system alloy and preparation method thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000192180A (en) * 1998-12-22 2000-07-11 Nippon Light Metal Co Ltd Die-cast scroll excellent in fatigue strength and method of manufacturing the same
FR2827306A1 (en) * 2001-07-10 2003-01-17 Pechiney Aluminium Ductile aluminum alloy, used for casting under pressure of structural and security components for motor vehicles, comprises alloying additions of silicon, element for reducing adherence on mold, and element for eutectic modification
CN1639373A (en) * 2002-03-01 2005-07-13 昭和电工株式会社 Process for producing Al-Mg-Si alloy plate, Al-Mg-Si alloy plate and Al-Mg-Si alloy material
CN106480384A (en) * 2016-11-08 2017-03-08 广西科技大学 A kind of milling method of ultrahigh-strength aluminum alloy sheet material
CN106637008A (en) * 2016-11-08 2017-05-10 广西科技大学 Rolling method for high-strength aluminum alloy plate
CN108456796A (en) * 2018-03-13 2018-08-28 太原理工大学 A kind of preparation method of high-strength and high-conductivity magnalium calcium-silicon
CN110172621A (en) * 2019-06-24 2019-08-27 辽宁瑞鸥新材料科技有限公司 A kind of high-strength highly-conductive Al-Mg-Si system alloy and preparation method thereof

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114015915A (en) * 2021-10-25 2022-02-08 宁波吉胜铸业有限公司 Wear-resisting pump cover
CN115198213A (en) * 2022-08-10 2022-10-18 华南理工大学 A composite deformation heat treatment method for regulating the electrical conductivity and mechanical properties of aluminum alloys
CN115198213B (en) * 2022-08-10 2022-12-13 华南理工大学 Composite thermomechanical treatment method for regulating and controlling conductivity and mechanical property of aluminum alloy
CN115725879A (en) * 2022-12-02 2023-03-03 广东远光电缆实业有限公司 High-conductivity aluminum alloy conductor and preparation method thereof
CN115725879B (en) * 2022-12-02 2023-08-25 广东远光电缆实业有限公司 High-conductivity aluminum alloy wire and preparation method thereof

Also Published As

Publication number Publication date
CN112981195B (en) 2021-12-21

Similar Documents

Publication Publication Date Title
CN112981195B (en) A kind of high-strength aluminum-magnesium-silicon-calcium conductive aluminum alloy and preparation method thereof
CN105821253B (en) The lightweight high conductivity and heat heat resistance aluminum conductor and its preparation technology of a kind of plus iron
CN112522645B (en) Preparation method of high-strength high-toughness homogeneous fine-grain CrCoNi intermediate-entropy alloy thin plate
CN106939386B (en) A kind of body of a motor car Al-Mg-Si-Cu alloy and preparation method thereof of high intensity quick-hardening
CN111057978B (en) Preparation method of ultrafine-grained high-toughness heat-resistant aluminum alloy wire
JP7262129B2 (en) HORIZONTAL CONTINUOUS CASTING METHOD FOR HIGH STRENGTH AND HIGH CONDUCTIVITY COPPER ALLOYS AND THEIR APPLICATIONS
CN108531790A (en) A kind of 6 line aluminium alloy band of high intensity high heat conductance and preparation method thereof
CN105441759A (en) Sc-containing high-strength Al-Cu-Mg-Mn-Zr alloy and preparation method thereof
CN113308620B (en) Copper-chromium-zirconium alloy and preparation method thereof
CN112011699A (en) Preparation process of high-strength and high-toughness aluminum alloy with specific rare earth content
CN112921208A (en) Preparation method of Al-Mg-Si series aluminum alloy plate with high forming performance
CN110863120A (en) A kind of copper alloy for lead frame and preparation method thereof
CN101086044A (en) High-strength high elasticity Cu-Ti alloy and its preparing process
CN110373568A (en) A kind of preparation method of cold deformation strengthening Cu-Cr-Zr-Mg alloy
CN115747581A (en) Aluminum-magnesium-silicon alloy plate with high strength and high conductivity and preparation method thereof
CN115125406A (en) A kind of copper-chromium alloy and preparation method thereof
CN113278831B (en) Method for preparing regenerated ADC12 aluminum alloy from scrap aluminum
CN113969362A (en) A kind of continuous gradient aluminum alloy deformation material and preparation method thereof
CN113674890A (en) A kind of high-conductivity heat-resistant aluminum alloy monofilament and preparation method thereof
CN104372220A (en) Superplastic magnesium lithium alloy material with high strain rate and preparation method thereof
CN115323203B (en) Cu and Sn composite microalloying material of Al-Mg-Si alloy for high-strength automobile body and preparation process and application thereof
CN115747564B (en) Copper-nickel-silicon-phosphorus alloy and preparation method thereof
CN107805733B (en) A kind of multi-component high-conductivity beryllium bronze alloy and its preparation method
CN112593114B (en) A kind of preparation method of high performance Cu-Cr-Zr-Mg-Si alloy strip
CN112746209B (en) Preparation method of high-plasticity thermal deformation rare earth magnesium alloy

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant