CN112962005A - Preparation method of high-strength high-thermal-conductivity aluminum alloy - Google Patents
Preparation method of high-strength high-thermal-conductivity aluminum alloy Download PDFInfo
- Publication number
- CN112962005A CN112962005A CN202110142029.3A CN202110142029A CN112962005A CN 112962005 A CN112962005 A CN 112962005A CN 202110142029 A CN202110142029 A CN 202110142029A CN 112962005 A CN112962005 A CN 112962005A
- Authority
- CN
- China
- Prior art keywords
- aluminum alloy
- preparation
- thermal
- following
- quenching
- 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.)
- Pending
Links
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
- C22C21/02—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
- 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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
-
- 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
-
- 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
- C22F1/053—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 zinc 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
- C22F1/057—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 copper as the next major constituent
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)
- Extrusion Of Metal (AREA)
Abstract
本发明公开一种高强高导热铝合金制备方法，包括以下步骤：对经过均匀化热处理和表面清洁处理的铝合金铸锭进行热挤压初成形制备坯料、固溶、淬火、中/低温终成形制得最终产品，然后对最终产品进行短时人工时效处理；其特征在于，所述热挤压初成形的挤压出口温度为500℃～580℃，所述中/低温终成形的加工温度范围为5℃～150℃，所述坯料与最终产品的横截面积之比为1.30～1.05∶1.00，所述短时人工时效处理的温度为150℃～200℃，时间为0.5～6h。本发明实现了铝合金的材料强度、延伸率与导热性能的兼顾，最终得到高性能的铝合金产品。The invention discloses a method for preparing an aluminum alloy with high strength and high thermal conductivity, which comprises the following steps: performing hot extrusion and initial forming on an aluminum alloy ingot subjected to homogenization heat treatment and surface cleaning to prepare a billet, solid solution, quenching, and medium/low temperature final forming. The final product is obtained by forming the final product, and then the final product is subjected to a short-time artificial aging treatment; it is characterized in that, the extrusion outlet temperature of the hot extrusion initial forming is 500 ℃ ~ 580 ℃, and the processing temperature of the middle/low temperature final forming The range is 5℃～150℃, the ratio of the cross-sectional area of the blank to the final product is 1.30～1.05:1.00, the temperature of the short-time artificial aging treatment is 150℃～200℃, and the time is 0.5～6h. The invention realizes the balance of the material strength, elongation and thermal conductivity of the aluminum alloy, and finally obtains a high-performance aluminum alloy product.
Description
Technical Field
The invention belongs to the field of aluminum alloy materials, and particularly relates to a preparation method of a high-strength high-heat-conductivity aluminum alloy.
Background
Because of the excellent properties of light weight, environmental protection, high specific strength and the like, the aluminum alloy is widely applied to the fields of transportation, building structures and the like. In addition, aluminum and aluminum alloys also have excellent electrical and thermal conductivity. The advantages enable the high-strength high-heat-conductivity aluminum alloy to be widely applied to parts such as power transmission lines, communication products and equipment (such as 5G base station parts, mobile phone middle plates and shells and the like), mechanical engine accessories, lighting lamps and brackets, industrial lubricating oil station heat exchangers and the like.
According to different production processes, high-strength and high-thermal conductivity aluminum alloy products can be roughly classified into die castings, graphene aluminum-based composites and deformation parts. The existing product adopts a die-casting process to a great extent, and compared with a wrought aluminum alloy production process, the die-casting process is very suitable for heat-conducting parts with complex shapes, and is short in production flow and high in efficiency. However, die cast products have high structure porosity and increase with component sizeLarge, the difficulty of filling is obviously increased; furthermore, the mechanical and thermal properties of die castings with high Si contents are far from those of wrought aluminum alloys, limited by the alloy composition and process characteristics. For example, the invention patent application with the Chinese publication number of CN111270110A refines a hypoeutectic cast aluminum alloy, removes harmful impurities such as Mn, Cr, V, Ti and the like by adding Al-B intermediate alloy, obviously improves the heat conductivity of die castings, but the heat conductivity and the elongation after fracture still do not reach 200W/m.K and 5 percent, can not meet the requirements of many occasions on material performance, and needs to seek more high-performance materials and preparation processes. Graphene aluminum-based composites have attracted considerable interest in recent years due to their extremely high thermal conductivity and adequate strength. The process also has its limitations, such as the problem of uniform mixing of graphene sheets with aluminum, brittle interphase Al4C3Reactant avoidance, mass production on a large scale, and the like. A Chinese patent application with publication number CN110983088A adopts a high-temperature sintering method to prepare a blank with the diameter of 50mm, and the blank is extruded to obtain a product with the thermal conductivity of more than 300W/m.K and the yield strength of more than 200 MPa. But the preparation process is harsh and needs to be sintered in a high-temperature and high-pressure environment; in addition, the blank size can not meet the requirements of large-size rods and profiles; furthermore, whether brittle Al is generated in a sintering environment of up to 600 ℃ or not4C3The reactants still need to be further characterized. The deformed aluminum alloy part is another high-strength and high-heat-conductivity product widely applied, the method for improving the heat conductivity of the deformed aluminum alloy part is tedious and old at present, and mainly adopts a single-stage/multi-stage overaging process, for example, as described in the invention patent applications with Chinese publication numbers of CN111560574A, CN111809088A and the like, although the method can obviously improve the heat conductivity, the strength loss can be inevitably caused, and the combination of high heat conductivity and high strength can not be realized.
Aiming at the current situation, how to find a rule between a production process, a material organization and product performance, reconcile the contradiction between the strength and the heat conductivity of the material and prepare a product with high strength and high heat conductivity comprehensive performance is a great challenge for material researchers at present.
Disclosure of Invention
The invention aims to provide a preparation method of a high-strength high-heat-conductivity aluminum alloy, which can be used for obtaining a wrought aluminum alloy material with high mechanical strength and excellent heat conductivity.
In order to achieve the purpose, the invention adopts the following technical scheme.
A preparation method of a high-strength high-thermal-conductivity aluminum alloy comprises the following steps: carrying out hot extrusion primary forming on the aluminum alloy cast ingot subjected to the homogenization heat treatment and surface cleaning treatment to prepare a blank, carrying out solid solution, quenching and medium/low temperature final forming to obtain a final product, and then carrying out short-time artificial aging treatment on the final product; the method is characterized in that the extrusion outlet temperature of the hot extrusion primary forming is 500-580 ℃, the processing temperature range of the medium/low temperature final forming is 5-150 ℃, the ratio of the cross sectional area of the blank to the cross sectional area of the final product is 1.30-1.05: 1.00, the temperature of the short-time artificial aging treatment is 150-200 ℃, and the time is 0.5-6 h.
The preparation method of the high-strength high-heat-conductivity aluminum alloy mainly aims at the subsequent process treatment of alloy smelting and casting and homogenization, does not involve component allocation and homogenization heat treatment parameter regulation and control of the alloy, and the homogenization heat treatment is reasonable conventional heat treatment.
In the invention, the aluminum alloy ingot is a 6-series aluminum alloy, and contains Si, Mg and several of Fe, Cu, Mn, Cr, Ni, Zn and Ti; the mass percentages of all elements in the aluminum alloy ingot are within the following ranges: 0.3-1.2% of Si, 0-0.3% of Fe, 0-1.0% of Cu, 0-1.0% of Mn, 0.3-1.3% of Mg, 0-0.3% of Cr, 0-0.2% of Ni, 0-1.0% of Zn, 0-0.1% of Ti, and the balance of aluminum and uncontrollable impurities.
In the present invention, the hot extrusion is used to form a blank including, but not limited to, a pipe, a bar, a plate, a wire, a profile, etc.
In the present invention, the hot extrusion is initially formed, and the extrusion outlet temperature is preferably 550 ℃.
In the present invention, the ratio of the cross-sectional area of the hot extrusion preform, the shaped billet, and the desired end product is preferably 1.15: 1.00.
In the invention, the cross-sectional areas of the hot extrusion primary formed blank and the required final product are both the cross-sectional area vertical to the hot extrusion direction.
In the invention, the hot extrusion preliminary forming and the hot extrusion outlet cooling mode include but are not limited to air natural cooling, online air cooling, online water mist cooling and the like, and preferably, the online air cooling is adopted.
In the invention, the temperature range of the solid solution is 500-580 ℃, and the time is 0.5-2 h. Preferably, the temperature of the solution treatment is 550 ℃ and the time is 1.0 h.
In the present invention, the solution treatment and the quenching treatment are performed in such a manner that the quenching transition time after the solution treatment is completed is within 30 seconds, and the cooling method includes, but is not limited to, water quenching, air quenching, oil quenching, and the like. Preferably, the quenching transfer time is within 5s, and a water quenching mode is adopted.
In the present invention, the intermediate/low temperature final forming process may be performed by processes including, but not limited to, forging, stamping, extruding, drawing, etc. according to the shape and characteristics of the final product.
In the present invention, the medium/low temperature final forming temperature is preferably 5 to 100 ℃, and more preferably 25 ℃.
In the present invention, the cooling method after the end of the medium/low temperature final forming includes, but is not limited to, air natural cooling, air cooling, water quenching, and the like, and preferably, the air natural cooling is used as the cooling method.
In the invention, the time interval between solid solution, quenching and medium/low temperature final forming is 0-48 h. Preferably, the time interval is 0-24 h, and further preferably, the time interval is 0-2 h.
In the invention, the short-time artificial aging temperature is preferably 180 ℃, and the time is preferably 4 h.
In the invention, the time interval between the medium/low temperature final forming and the short-time artificial aging is 0-48 h. Preferably, the time interval is 0-24 h, and further preferably, the time interval is 0-2 h.
In the invention, the hot extrusion primary forming, the solution quenching, the middle/low temperature final forming and the short-time artificial aging are sequentially carried out.
The invention has the beneficial effects that: the short-term and long-term aging process of single-phase structure medium/low temperature deformation collocation is creatively provided, and the technical problem of contradiction between high strength and high heat conductivity in the prior art is overcome by adopting the interpenetration and combination of a hot and cold step deformation technology and a strengthening heat treatment technology. The concrete expression is as follows: 1) the specific process advantages of the invention change the crystal structure of the aging precipitation phase, thereby greatly avoiding the damage of the relative thermal conductivity of the traditional aging precipitation; 2) the regulated and controlled deformation structure greatly improves the precipitation power of the aging strengthening phase and greatly shortens the production period. 3) The unicity of the existing material strengthening mechanism is improved, and the synergistic effect of aging strengthening, grain boundary strengthening and dislocation strengthening is realized, so that the strength of the material is ensured; 4) through scientific combination of a deformation system and a heat treatment process, the consideration of the strength and the heat conductivity of the material is realized, and finally the high-performance aluminum alloy product is obtained.
Detailed Description
The following further describes the embodiments of the present invention, so that the technical solutions and the advantages thereof of the present invention are more clear and definite. The following description of the embodiments is exemplary in nature and is in no way intended to limit the invention.
Additional aspects and advantages of the invention will be set forth in part in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention.
Example one
The 6063 alloy cast rod with the diameter of 90mm comprises the following components in percentage by mass: 0.35% of Si, 0.45% of Mg, 0.13% of Fe, 0.08% of Mn, 0.02% of Ti, 0.02% of V, 98.9% of Al, and the sum of other elements (inevitable impurities) being less than or equal to 0.1%.
A high-strength high-heat-conductivity aluminum alloy and a preparation method thereof comprise the following steps: placing a conventional 6063 aluminum alloy cast rod with the diameter of 90mm in a homogenizing heating furnace, preserving the heat for 6 hours at 570 ℃, and cooling by strong wind after discharging; peeling the surface of the cast rod; and carrying out hot extrusion on the cast ingot subjected to peeling treatment to obtain a plate blank, and carrying out extrusion at an outlet temperature of 550 ℃ and carrying out online air cooling. And (3) carrying out solid solution treatment at 550 ℃ for 1h on the hot extruded plate, and then carrying out water quenching treatment within 5 s. After quenching, stamping the plate at room temperature (25 ℃) within 2h to obtain the mobile phone shell, wherein the ratio of the cross sectional areas before and after stamping is about 1.15: 1.00. after the punching is finished, the aging treatment is carried out within 2h at 180 ℃ for 4 h. Finally obtaining the high-strength high-heat-conductivity aluminum alloy product.
Example two
In the first example, the ratio of the cross-sectional areas before and after the punching was changed to 1.30: 1.00 and the rest are unchanged, thus obtaining the high-strength high-heat-conductivity aluminum alloy.
EXAMPLE III
In the first example, the ratio of the cross-sectional areas before and after the punching was changed to 1.05: 1.00 and the rest are unchanged, thus obtaining the high-strength high-heat-conductivity aluminum alloy.
Example four
In the first embodiment, the extrusion outlet temperature is changed to 500 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
EXAMPLE five
In the first embodiment, the temperature of the extrusion outlet is changed to 580 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
EXAMPLE six
In the first embodiment, the solid solution temperature is changed to 500 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
EXAMPLE seven
In the first embodiment, the solid solution temperature is changed to 580 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example eight
In the first embodiment, the solid solution time is changed to 0.5h, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example nine
In the first embodiment, the solid solution time is changed to 2 hours, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example ten
In the first embodiment, the transfer time of solid solution and quenching is changed to 30s, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
EXAMPLE eleven
In the first embodiment, the stamping temperature is changed to 5 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example twelve
In the first embodiment, the stamping temperature is changed to 150 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
EXAMPLE thirteen
In the first embodiment, the time interval between the solid solution, the quenching and the room temperature stamping is 48 hours, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example fourteen
In the first embodiment, the aging temperature is changed to 150 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example fifteen
In the first embodiment, the aging temperature is changed to 200 ℃, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example sixteen
In the first embodiment, the aging time is changed to 0.5h, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example seventeen
In the first embodiment, the aging time is changed to 6 hours, and the rest time is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
EXAMPLE eighteen
In the first embodiment, the time interval between stamping and aging is changed to 48h, and the rest is unchanged, so that the high-strength high-heat-conductivity aluminum alloy is obtained.
Example nineteen
The 6063 alloy cast rod with the diameter of 102mm comprises the following components in percentage by mass: 0.35% of Si, 0.45% of Mg, 0.13% of Fe, 0.08% of Mn, 0.02% of Ti, 0.02% of V, 98.9% of Al, and the sum of other elements (inevitable impurities) being less than or equal to 0.1%.
A high-strength high-heat-conductivity aluminum alloy and a preparation method thereof comprise the following steps: placing a conventional 6063 aluminum alloy cast rod with phi 102mm in a homogenizing heating furnace, preserving heat for 6 hours at 570 ℃, and cooling by strong wind after discharging; peeling the surface of the cast rod; and (3) carrying out hot extrusion on the cast ingot subjected to peeling treatment to obtain a pipe blank, and carrying out on-line air cooling after the extrusion outlet temperature is 550 ℃. And (3) performing solid solution treatment on the hot extruded pipe at 550 ℃ for 1h, and performing water quenching treatment within 5 s. And (3) performing die forging on the pipe at room temperature within 2h after quenching is finished to obtain the triangular pipe lighting bracket, wherein the ratio of the cross sectional area before and after die forging is about 1.15: 1.00. after the die forging is finished, the aging treatment of 180 ℃ multiplied by 4h is carried out within 2 h. Finally obtaining the high-strength high-heat-conductivity aluminum alloy product.
Example twenty
The 6063 alloy cast rod with the diameter of 80mm comprises the following components in percentage by mass: 0.35% of Si, 0.45% of Mg, 0.13% of Fe, 0.08% of Mn, 0.02% of Ti, 0.02% of V, 98.9% of Al, and the sum of other elements (inevitable impurities) being less than or equal to 0.1%.
A high-strength high-heat-conductivity aluminum alloy and a preparation method thereof comprise the following steps: placing a conventional 6063 aluminum alloy cast rod with the diameter of 80mm in a homogenizing heating furnace, preserving the heat for 6 hours at 570 ℃, and cooling by strong wind after discharging; peeling the surface of the cast rod; and hot extruding the cast ingot subjected to peeling treatment into a wire rod with the outer diameter of 15mm, and performing on-line air cooling at an extrusion outlet temperature of 550 ℃. Carrying out water quenching treatment within 5s after solid solution is carried out for 1h at 550 ℃. After quenching, stretching to the diameter of 14mm at room temperature within 2h, wherein the ratio of the cross-sectional areas before and after stretching is about 1.15: 1.00. after the stretching is finished, the aging treatment is carried out within 2h at 180 ℃ for 4 h. Finally obtaining the high-strength high-heat-conductivity aluminum alloy transmission cable wire.
Example twenty one
The 6063 alloy cast rod with the diameter of 124mm comprises the following components in percentage by mass: 0.35% of Si, 0.45% of Mg, 0.13% of Fe, 0.08% of Mn, 0.02% of Ti, 0.02% of V, 98.9% of Al, and the sum of other elements (inevitable impurities) being less than or equal to 0.1%.
A high-strength high-heat-conductivity aluminum alloy and a preparation method thereof comprise the following steps: placing a conventional 6063 aluminum alloy cast rod with the diameter of 124mm in a homogenizing heating furnace, preserving the heat for 6 hours at 570 ℃, and cooling by strong wind after discharging; peeling the surface of the cast rod; and hot extruding the cast ingot subjected to peeling treatment into a pipe with the outer diameter of 200mm and the wall thickness of 10mm, and performing on-line air cooling at the extrusion outlet temperature of 550 ℃. Carrying out water quenching treatment within 5s after solid solution is carried out for 1h at 550 ℃. After quenching, the steel is drawn at room temperature within 2h until the outer diameter is 180mm and the wall thickness is 9.5mm, and the ratio of the cross sectional area before and after drawing is about 1.15: 1.00. after the drawing is finished, the aging treatment is carried out within 2h at 180 ℃ for 4 h. Finally obtaining the high-strength high-heat-conductivity aluminum alloy tubular shell which is used for a heat exchanger of a lubricating oil station of mechanical equipment.
Example twenty two
The aluminum alloy cast rod with the diameter of 124mm comprises the following components in percentage by mass: 1.10 percent of Si, 1.0 percent of Mg, 0.4 percent of Cu, 0.13 percent of Fe, 0.45 percent of Mn, 0.02 percent of Ti, 98.9 percent of Al, and the sum of other elements (inevitable impurities) is less than or equal to 0.1 percent.
A high-strength high-heat-conductivity aluminum alloy and a preparation method thereof comprise the following steps: placing the conventional aluminum alloy cast rod with the diameter of 124mm in a homogenizing heating furnace, preserving the heat for 8 hours at 570 ℃, and cooling by strong wind after discharging; peeling the surface of the cast rod; and hot extruding the cast ingot subjected to peeling treatment into a pipe with the outer diameter of 200mm and the wall thickness of 10mm, and performing on-line air cooling at the extrusion outlet temperature of 550 ℃. Carrying out water quenching treatment within 5s after solid solution is carried out for 1h at 550 ℃. After quenching, the steel is drawn at room temperature within 2h until the outer diameter is 180mm and the wall thickness is 9.5mm, and the ratio of the cross sectional area before and after drawing is about 1.15: 1.00. after the drawing is finished, the aging treatment is carried out within 2h and at 180 ℃ for X4 h. Finally obtaining the high-strength high-heat-conductivity aluminum alloy tubular shell which is used for a heat exchanger of a lubricating oil station of mechanical equipment.
Comparative example 1
In the first example, the ratio of the cross-sectional areas before and after the punching was changed to 1.01: 1.00 and the rest unchanged, obtaining a comparative aluminum alloy material.
Comparative example No. two
In the first example, the ratio of the cross-sectional areas before and after the punching was changed to 1.40: 1.00 and the rest unchanged, obtaining a comparative aluminum alloy material.
Comparative example No. three
In the first example, the stamping temperature was changed to-10 ℃ and the rest was unchanged, to obtain a comparative aluminum alloy material.
Comparative example No. four
In the first example, the stamping temperature was changed to 250 ℃ and the rest was unchanged, to obtain a comparative aluminum alloy material.
Comparative example five
The 6063 alloy cast rod with the diameter of 90mm comprises the following components in percentage by mass: 0.35% of Si, 0.45% of Mg, 0.13% of Fe, 0.08% of Mn, 0.02% of Ti, 0.02% of V, 98.9% of Al, and the sum of other elements (inevitable impurities) being less than or equal to 0.1%.
A high-strength high-heat-conductivity aluminum alloy and a preparation method thereof comprise the following steps: placing a conventional 6063 aluminum alloy cast rod with the diameter of 90mm in a homogenizing heating furnace, preserving the heat for 6 hours at 570 ℃, and cooling by strong wind after discharging; peeling the surface of the cast rod; adopting the conventional hot extrusion + CNC method: and carrying out hot extrusion on the cast ingot subjected to peeling treatment to obtain a plate blank, and machining the blank to obtain the mobile phone shell. And (3) carrying out solid solution treatment on the machined shell at 550 ℃ for 1h, and then carrying out water quenching treatment within 5 s. After quenching is finished, aging treatment is carried out within 2h at 180 ℃ for 8 h. Finally obtaining a comparative aluminum alloy product.
The yield strength, elongation and thermal conductivity indexes of the final formed products in the examples and the comparative examples are shown in table 1, the performance detection is a conventional detection technology, and a tensile tester and a thermal conductivity meter are adopted for mechanical performance detection and thermal conductivity detection.
TABLE 1 test data in examples and comparative examples
Note: the values in Table 1 in italics with bold red indicate poor or not-achieved performance.
As can be seen in connection with table 1: embodiments one to eighteen are examples of 6063 aluminum alloy mobile phone shells, and the product of embodiment one can simultaneously achieve high strength and high thermal conductivity on the premise of satisfying elongation percentage, and is a process product with optimal comprehensive performance; nineteen to twenty of the examples are light support, transmission cable and oil station heat exchanger wall shell that 6063 alloy obtained through medium/low temperature deformation respectively, similar to the punching press cell-phone shell product in the first example, and comprehensive properties is all relatively good. The twenty-second embodiment is other 6 series aluminum alloy materials, the heat exchanger shell elongation of the alloy with the components reaches the standard, and meanwhile, the heat exchanger shell has extremely high strength and excellent heat conductivity. The first to fifth comparative examples exceed the protection range of the invention, the performance is poor, and certain indexes do not reach the standard.
From the above description of the principles, it will be appreciated by those skilled in the art that the present invention is not limited to the specific embodiments described above, and that modifications and alterations based on the present invention using techniques known in the art are within the scope of the present invention, which is defined by the claims and their equivalents. The details not described in the detailed description are prior art or common general knowledge.
Claims (10)
1. A preparation method of a high-strength high-thermal-conductivity aluminum alloy comprises the following steps: carrying out hot extrusion primary forming on the aluminum alloy cast ingot subjected to the homogenization heat treatment and surface cleaning treatment to prepare a blank, carrying out solid solution, quenching and medium/low temperature final forming to obtain a final product, and then carrying out short-time artificial aging treatment on the final product; the method is characterized in that the extrusion outlet temperature of the hot extrusion primary forming is 500-580 ℃, the processing temperature range of the medium/low temperature final forming is 5-150 ℃, the ratio of the cross sectional area of the blank to the cross sectional area of the final product is 1.30-1.05: 1.00, the temperature of the short-time artificial aging treatment is 150-200 ℃, and the time is 0.5-6 h.
2. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the aluminum alloy cast ingot is a 6-series aluminum alloy and contains Si, Mg and a plurality of Fe, Cu, Mn, Cr, Ni, Zn and Ti; the mass percentages of all elements in the aluminum alloy ingot are within the following ranges: 0.3-1.2% of Si, 0-0.3% of Fe, 0-1.0% of Cu, 0-1.0% of Mn, 0.3-1.3% of Mg, 0-0.3% of Cr, 0-0.2% of Ni, 0-1.0% of Zn, 0-0.1% of Ti, and the balance of aluminum and uncontrollable impurities.
3. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the blank material prepared by the hot extrusion primary forming is a pipe, a bar, a plate, a wire or a section.
4. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the outlet cooling mode for preparing the blank by hot extrusion primary forming comprises one or more of air natural cooling, online air cooling, online water cooling and water mist cooling.
5. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the temperature range of the solution treatment is 500-580 ℃, and the time is 0.5-2 h.
6. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the quenching transfer time after the solution treatment is 0-30 s, and the quenching mode comprises one or more of water quenching, air quenching and oil quenching.
7. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the intermediate/low temperature final forming process is forging, stamping, extruding or drawing.
8. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the cooling mode after the medium/low temperature final forming is one or more of air natural cooling, air cooling and water quenching.
9. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the time interval between quenching and medium/low temperature final forming is 0-48 h.
10. The preparation method of the high-strength high-thermal-conductivity aluminum alloy according to claim 1, characterized by comprising the following steps: the time interval between the medium/low temperature final forming and the short-time artificial aging is 0-48 h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110142029.3A CN112962005A (en) | 2021-02-02 | 2021-02-02 | Preparation method of high-strength high-thermal-conductivity aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110142029.3A CN112962005A (en) | 2021-02-02 | 2021-02-02 | Preparation method of high-strength high-thermal-conductivity aluminum alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN112962005A true CN112962005A (en) | 2021-06-15 |
Family
ID=76271835
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110142029.3A Pending CN112962005A (en) | 2021-02-02 | 2021-02-02 | Preparation method of high-strength high-thermal-conductivity aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112962005A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114672749A (en) * | 2022-03-17 | 2022-06-28 | 中南大学 | Heat treatment method for improving conductivity of Al-Mg-Si-Cu aluminum alloy |
| CN116574946A (en) * | 2023-06-02 | 2023-08-11 | 苏州大学 | Deformed aluminum alloy material and preparation method thereof |
| CN117737517A (en) * | 2023-12-28 | 2024-03-22 | 中南大学 | High-iron-content secondary Al-Mg-Si series alloy and preparation method thereof |
| CN117845105A (en) * | 2023-12-06 | 2024-04-09 | 苏州大学 | High-strength and high-toughness cast aluminum alloy and preparation method and application thereof |
| CN119491145A (en) * | 2024-11-15 | 2025-02-21 | 天津忠旺铝业有限公司 | A 6-series aluminum alloy sheet for a new energy battery bottom plate and a preparation method thereof |
| CN121087312A (en) * | 2025-11-11 | 2025-12-09 | 东北大学 | High-strength corrosion-resistant Al-Mg-Si-Cu-Zn aluminum-based cross alloy and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101558177A (en) * | 2006-12-13 | 2009-10-14 | 住友轻金属工业株式会社 | High-strength aluminum-base alloy products and process for production thereof |
| CN102416558A (en) * | 2011-09-15 | 2012-04-18 | 天津锐新昌轻合金股份有限公司 | Method for producing extruded aluminium alloy components, in particular for cold-bending plastic forming |
| US20180282849A1 (en) * | 2015-12-23 | 2018-10-04 | Norsk Hydro Asa | Method for producing a heat treatable aluminium alloy with improved mechanical properties |
| CN109576515A (en) * | 2018-12-05 | 2019-04-05 | 辽宁忠旺集团有限公司 | A kind of production technology of high intensity aluminum alloy pattern plate |
| CN110355225A (en) * | 2019-06-26 | 2019-10-22 | 辽宁忠旺集团有限公司 | Extrusion process of high-strength aluminum alloy bending profiles for vehicles |
-
2021
- 2021-02-02 CN CN202110142029.3A patent/CN112962005A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101558177A (en) * | 2006-12-13 | 2009-10-14 | 住友轻金属工业株式会社 | High-strength aluminum-base alloy products and process for production thereof |
| CN102416558A (en) * | 2011-09-15 | 2012-04-18 | 天津锐新昌轻合金股份有限公司 | Method for producing extruded aluminium alloy components, in particular for cold-bending plastic forming |
| US20180282849A1 (en) * | 2015-12-23 | 2018-10-04 | Norsk Hydro Asa | Method for producing a heat treatable aluminium alloy with improved mechanical properties |
| CN109576515A (en) * | 2018-12-05 | 2019-04-05 | 辽宁忠旺集团有限公司 | A kind of production technology of high intensity aluminum alloy pattern plate |
| CN110355225A (en) * | 2019-06-26 | 2019-10-22 | 辽宁忠旺集团有限公司 | Extrusion process of high-strength aluminum alloy bending profiles for vehicles |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114672749A (en) * | 2022-03-17 | 2022-06-28 | 中南大学 | Heat treatment method for improving conductivity of Al-Mg-Si-Cu aluminum alloy |
| CN116574946A (en) * | 2023-06-02 | 2023-08-11 | 苏州大学 | Deformed aluminum alloy material and preparation method thereof |
| CN117845105A (en) * | 2023-12-06 | 2024-04-09 | 苏州大学 | High-strength and high-toughness cast aluminum alloy and preparation method and application thereof |
| CN117737517A (en) * | 2023-12-28 | 2024-03-22 | 中南大学 | High-iron-content secondary Al-Mg-Si series alloy and preparation method thereof |
| CN119491145A (en) * | 2024-11-15 | 2025-02-21 | 天津忠旺铝业有限公司 | A 6-series aluminum alloy sheet for a new energy battery bottom plate and a preparation method thereof |
| CN121087312A (en) * | 2025-11-11 | 2025-12-09 | 东北大学 | High-strength corrosion-resistant Al-Mg-Si-Cu-Zn aluminum-based cross alloy and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112962005A (en) | Preparation method of high-strength high-thermal-conductivity aluminum alloy | |
| CN110396629B (en) | A kind of 800MPa grade aluminum alloy extruded profile and preparation method thereof | |
| CN113737068B (en) | High-strength and high-toughness corrosion-resistant 7xxx series aluminum alloy and processing method thereof | |
| CN103103424B (en) | Method for manufacturing aviation aluminum alloy profiles by double aging | |
| CN103361523B (en) | A kind of Structural Engineering aluminium alloy extrusions and preparation method thereof | |
| CN109355537B (en) | 6-series aluminum alloy section for new energy battery tray and processing method thereof | |
| CN114277291B (en) | Al-Zn-Mg-Cu aluminum alloy extrusion material for aerospace and preparation method thereof | |
| CN110592508B (en) | Low-cost and high-performance titanium alloy short-process forging process | |
| CN109207811A (en) | A kind of preparation method and applications of aluminium alloy extrusions | |
| CN101509091A (en) | High-strength high-ductility Al-Zn-Mg-Cu-Sr alloy and production method | |
| CN103205616B (en) | Ultrahigh-strength and high-elongation Al-Zn-Mg-Cu alloy and method for manufacturing same | |
| CN109371266B (en) | Production method of high-strength corrosion-resistant weldable Al-Mg-Si series alloy extrusion material | |
| CN117070787B (en) | Aluminum alloy profile, preparation method and application thereof | |
| CN105200288A (en) | Ultra-high-strength Al alloy bar and production method thereof | |
| CN115094278A (en) | 6-series aluminum alloy material with good thermal stability and preparation method thereof | |
| CN101736183A (en) | Preparation method of superplastic aluminum alloy plates for track traffic | |
| CN108359863B (en) | A GIS pipe shell production process | |
| CN114086040A (en) | A kind of aluminum magnesium silicon scandium zirconium alloy and preparation method thereof | |
| CN104109781A (en) | Aluminum alloy, micro channel aluminum flat tube, preparation method of micro channel aluminum flat tube, heat exchanger and electric appliance | |
| CN107619973A (en) | A kind of process of aluminium alloys for automobile control arm performance boost | |
| CN108385008B (en) | Preparation device and method of medium-strength high-energy-absorbing magnesium alloy and deep cold-bendable pipe | |
| CN104451251B (en) | A kind of high ferro White brass alloy tubing and short-flow production method thereof | |
| WO2018072052A1 (en) | Deformable zinc alloy capable of being cold headed and application thereof | |
| CN121428309A (en) | A method for preparing high-strength beryllium-containing Al-Mg-Zn-Cu aluminum alloy profiles | |
| CN114107769A (en) | High-strength high-ductility aluminum alloy material and preparation method thereof |
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 | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20210615 |
|
| RJ01 | Rejection of invention patent application after publication |