WO2022041268A1 - 一种高强Al-Cu-Mg-Mn铝合金及其制备方法 - Google Patents
一种高强Al-Cu-Mg-Mn铝合金及其制备方法 Download PDFInfo
- Publication number
- WO2022041268A1 WO2022041268A1 PCT/CN2020/112715 CN2020112715W WO2022041268A1 WO 2022041268 A1 WO2022041268 A1 WO 2022041268A1 CN 2020112715 W CN2020112715 W CN 2020112715W WO 2022041268 A1 WO2022041268 A1 WO 2022041268A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- aluminum
- mold
- deformation
- alloy
- strength
- Prior art date
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 58
- 238000002360 preparation method Methods 0.000 title claims abstract description 28
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 85
- 239000000956 alloy Substances 0.000 claims abstract description 85
- 229910052706 scandium Inorganic materials 0.000 claims abstract description 37
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 32
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 32
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 31
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 29
- 238000010438 heat treatment Methods 0.000 claims abstract description 27
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 22
- 229910052802 copper Inorganic materials 0.000 claims abstract description 17
- 230000032683 aging Effects 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 238000005242 forging Methods 0.000 claims abstract description 14
- 239000012535 impurity Substances 0.000 claims abstract description 14
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 14
- 238000012545 processing Methods 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 9
- 238000000265 homogenisation Methods 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 239000004576 sand Substances 0.000 claims abstract description 8
- 238000007872 degassing Methods 0.000 claims abstract description 7
- 229910052751 metal Inorganic materials 0.000 claims abstract description 7
- 239000002184 metal Substances 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 5
- 238000007670 refining Methods 0.000 claims abstract description 5
- 239000011572 manganese Substances 0.000 claims description 46
- 239000011777 magnesium Substances 0.000 claims description 30
- 238000001125 extrusion Methods 0.000 claims description 29
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 23
- 239000010949 copper Substances 0.000 claims description 22
- 239000000155 melt Substances 0.000 claims description 17
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 16
- WPPDFTBPZNZZRP-UHFFFAOYSA-N aluminum copper Chemical compound [Al].[Cu] WPPDFTBPZNZZRP-UHFFFAOYSA-N 0.000 claims description 16
- -1 aluminum-manganese Chemical compound 0.000 claims description 16
- 239000002994 raw material Substances 0.000 claims description 16
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 15
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 14
- ZGUQGPFMMTZGBQ-UHFFFAOYSA-N [Al].[Al].[Zr] Chemical compound [Al].[Al].[Zr] ZGUQGPFMMTZGBQ-UHFFFAOYSA-N 0.000 claims description 13
- LUKDNTKUBVKBMZ-UHFFFAOYSA-N aluminum scandium Chemical compound [Al].[Sc] LUKDNTKUBVKBMZ-UHFFFAOYSA-N 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 13
- 238000010274 multidirectional forging Methods 0.000 claims description 11
- 238000003825 pressing Methods 0.000 claims description 11
- 230000009467 reduction Effects 0.000 claims description 10
- 238000010791 quenching Methods 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- RFEISCHXNDRNLV-UHFFFAOYSA-N aluminum yttrium Chemical compound [Al].[Y] RFEISCHXNDRNLV-UHFFFAOYSA-N 0.000 claims description 8
- 238000004321 preservation Methods 0.000 claims description 8
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 7
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 claims description 7
- 230000009466 transformation Effects 0.000 claims description 7
- 238000010275 isothermal forging Methods 0.000 claims description 6
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 6
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 230000008569 process Effects 0.000 claims description 3
- 238000009825 accumulation Methods 0.000 claims description 2
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 239000007789 gas Substances 0.000 claims description 2
- 230000000171 quenching effect Effects 0.000 claims description 2
- 239000002893 slag Substances 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 claims 5
- 239000010959 steel Substances 0.000 claims 5
- 239000000498 cooling water Substances 0.000 claims 1
- 238000005266 casting Methods 0.000 abstract description 13
- 239000006104 solid solution Substances 0.000 abstract description 2
- 238000000746 purification Methods 0.000 abstract 1
- 239000000243 solution Substances 0.000 description 17
- 230000000052 comparative effect Effects 0.000 description 6
- 230000007306 turnover Effects 0.000 description 6
- 230000006872 improvement Effects 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 3
- 229910001093 Zr alloy Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000004146 energy storage Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910019015 Mg-Ag Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- XWHPIFXRKKHEKR-UHFFFAOYSA-N iron silicon Chemical compound [Si].[Fe] XWHPIFXRKKHEKR-UHFFFAOYSA-N 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000003110 molding sand Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
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
- C22C21/12—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
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- 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
- C22C21/12—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
- 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
Definitions
- the invention provides a high-strength Al-Cu-Mg-Mn aluminum alloy and a preparation method thereof, belonging to the field of aluminum alloys.
- Al-Cu-Mg-Mn aluminum alloy has the characteristics of low density, high strength, excellent plasticity, and excellent electrical and thermal conductivity. It has a wide range of applications in the industrial field, especially in the aerospace field. , The aircraft fuselage joints, frames, hubs and other supporting structural components are all made of aluminum alloys.
- Chinese patent CN103748246A discloses a heat-resistant Al-Cu-Mg-Ag alloy and a method for producing semi-finished or finished products composed of this aluminum alloy, the composition comprising: 0.3-0.7wt% silicon, not more than 0.15wt% silicon iron, 3.5-4.7wt% copper, 0.05-0.5wt% manganese, 0.3-0.9wt% magnesium, 0.02-0.15wt% titanium, 0.03-0.25wt% zirconium, 0.1-0.7wt% silver, 0.03-0.5wt% of scandium, 0.03-0.2wt% of vanadium, no more than 0.05wt% of single other elements, no more than 0.15wt% of all other elements, and the balance of aluminum.
- the prepared aluminum alloy has a tensile strength of 449 MPa and an elongation of 10.6%.
- Chinese patent CN105441759A discloses a high-strength Al-Cu-Mg-Mn-Zr alloy containing Sc and its preparation method, the alloy composition: copper is 3.7%-4.0%, magnesium is 1.4%-1.6%, scandium is 0.2% -0.3%, zirconium is 0.2%-0.3%, manganese is 0.3%-0.5%, the balance is aluminum, Sc and Zr are added, and rolling deformation is carried out, the room temperature tensile strength of the prepared aluminum alloy is 450-520MPa , the elongation is 6.5%-11.5%.
- the invention provides a high-strength Al-Cu-Mg-Mn aluminum alloy and a preparation method thereof. Sc, Zr, Y microalloying is adopted, and high-quality ingots are prepared in combination with casting process control. Pre-deformation treatment is carried out, and then isothermal extrusion or isothermal forging deformation processing is carried out to achieve substructure strengthening while avoiding the increase of deformation energy storage. %.
- the present invention provides a high-strength Al-Cu-Mg-Mn aluminum alloy and a preparation method thereof.
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, aluminum-zirconium master alloy, and aluminum-yttrium master alloy are used as raw materials; among them, the purity of high-purity aluminum is ⁇ 99.9%, industrial pure
- the purity of magnesium is greater than or equal to 99.9%
- the content of copper in the aluminum-copper master alloy is greater than or equal to 50.0%
- the content of scandium in the aluminum-scandium master alloy is greater than or equal to 1.0%
- the content of zirconium in the aluminum-zirconium master alloy is greater than or equal to 10.0%
- the content of manganese in the aluminum-manganese master alloy is greater than or equal to 10.0%.
- the content is ⁇ 20.0%, and the content of yttrium in the aluminum-yttrium master alloy is ⁇ 10.0%; the raw materials are weighed according to the proportion, put into a resistance furnace, and heated
- a steel mold of a certain size (wall thickness greater than or equal to 30mm) is designed and prepared as an inner mold, and the cooling pipe is surrounded upward from the bottom of the outer wall of the steel mold, and the cooling water is introduced into the pipe. It can be controlled, using sand mold as the outer mold, in which the thickness ratio of steel mold and sand mold is 1: (2-5), and the gating system adopts steel mold gating system; the cooling speed is controlled by controlling the temperature and flow of cooling water.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 13-15 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420-450° C. in a resistance furnace and kept for 30-60 minutes, more preferably 40-50 minutes, and even more preferably 45 minutes, and then undergo three-dimensional large deformation.
- reduction rate 1 ⁇ 3 mm/s, preferably 2mm/s; the first deformation: press down and deform in the direction of the largest dimension (Y axis), when the strain reaches 0.5 ⁇ 0.8, perform the first flip transformation: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis), perform multiple reversal deformations to obtain multi-rhombic columnar blanks.
- the second reversal transformation is performed: along the Reverse and deform multiple times in the direction of the largest angle between the X axis and the Y axis to obtain a spherical polyhedron; repeat the above steps 3-5 times; and finally reverse and deform along the X axis direction to obtain a polyrhombic columnar blank.
- step E the blank obtained in step E is kept at 420-450°C for 1-2h, preferably 1.5h, the mold is kept at 420-450°C for 25-35min, and the extrusion ratio is (10-20): 1, The extrusion speed ensures that the ingot strain rate is 0.05 ⁇ 0.2s -1 ; or isothermal forging, the billet is kept at 420-450 °C for 1-2h, the mold is kept at 420-450 °C for 25-40min, and the hydraulic press pressing speed during forging is 0.05 ⁇ 0.1 mm/s, preferably 0.05 mm/s; an isothermally deformed workpiece is obtained.
- Heat treatment firstly carry out solution treatment, heat the isothermally deformed parts to 480-520°C, keep for 1-3h, and then quench them with water; then carry out gradient aging treatment, first heat the solution treated parts to 100-130°C for heat preservation 0.5-1.5h, then the temperature is raised to 170-220°C for 5.0-10.0h, and air-cooled to obtain a product.
- step A the melt temperature after heating is 750-800°C.
- step F the homogenized ingot obtained in step E is heated to 420-450 ° C in a resistance furnace and kept for 45 minutes, and then three-dimensional large deformation multi-directional forging is performed, and the reduction rate is 2 mm/s;
- Secondary deformation Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first flipping transformation is performed: along the radial direction (X-axis), that is, perpendicular to the first compression direction (Y-axis) for several times of reversal deformation to obtain multi-rhombic cylindrical blanks, when the strain reaches 0.5, the second reversal transformation is performed: along the direction of the largest dimension of the angle between the X-axis and the Y-axis
- the spherical polyhedron is obtained by commutating and deforming multiple times to obtain a spherical polyhedron; repeating the above steps 3-5 times; and finally commutating and deforming along the
- step G the isothermal deformation processing technology is adopted in step G, the billet is kept at 420-450 °C for 1.5 hours, the mold is kept at 420-450 °C for 30 minutes, the extrusion ratio is (10-20): 1, and the extrusion speed is guaranteed.
- the ingot strain rate is 0.1s -1 ; or isothermal forging, the billet is kept at 420-450°C for 1.5h, the mold is kept at 420-450°C for 30min, and the hydraulic press is pressed down at a speed of 0.05mm/s during forging.
- Step H solution treatment, heating the isothermally deformed workpiece to 500° C., holding the temperature for 2 hours, and quenching with water.
- Step H Gradient aging treatment, firstly heating the solution treated part to 120°C for 1 hour, then heating to 200°C for 7 hours, and air cooling to obtain the part.
- the product designed and prepared by the present invention has a strength of 520-530 MPa and an elongation of 12-16%.
- the present invention adopts Sc, Y and Zr to carry out microalloying of aluminum alloy, forms a second phase dispersed in the aluminum alloy, increases the recrystallization temperature, and can also form an Al3 (ScxZr1-x) composite phase at the same time, this phase has Higher thermal stability, so the prepared aluminum alloy has higher strength and thermal stability, and improves service life and temperature.
- the preparation process of the present invention strictly controls the purity of materials, reduces the content of Fe and Si elements, avoids the formation of coarse brittle phases, and affects the plasticity of the alloy; at the same time, micro-alloying elements such as Y, Sc and Zr are used to refine the crystal grains and improve the alloy element bias. The degree of aggregation can improve the mechanical properties of the alloy.
- the present invention proposes to use three-dimensional large deformation multi-directional forging to deform the alloy ingot, so that the structure of the ingot can be homogenized, especially the coarse second phase can be fully broken and homogenized, and the overall performance of the alloy can be improved.
- the present invention adopts the synergistic effect of gradient aging, low temperature aging and high temperature aging to form a uniformly distributed multi-scale nano second phase, which effectively improves the uniformity of the structure and the mechanical properties.
- the casting mold of the aluminum alloy of the present invention adopts the metal mold as the inner mold, surrounds the water cooling pipe, and then uses the sand mold as the outer mold, which not only improves the cooling rate, refines the crystal grains, but also reduces the mold production cost, while ensuring the casting. ingot quality.
- the solidification rate of the melt is adjusted in coordination with the sand mold, and the structure of the ingot is adjusted to improve the grain size uniformity and composition uniformity of the surface and central parts of the casting, and obtain uniform structure and composition. of castings.
- the process provided by the present invention is simple to operate, and effectively avoids the fact that the sand mold is in direct contact with the molding sand due to the slow cooling rate, which causes the ingot to be prone to sand inclusion, coarse structure and other defects; the cooling rate of the metal mold is fast, but the casting surface layer
- the structure uniformity between the central part and the structure is poor, and the mold size needs to be increased in order to improve the structure uniformity, which leads to problems such as high cost of metal molds and difficult processing; , excellent performance; compared with sand mold casting, the mechanical properties of the ingot are excellent; compared with metal mold casting, the structure of the central part can be effectively controlled, and the surface layer and the central part of the prepared casting have good organizational uniformity and composition uniformity;
- the prepared aluminum alloy casting has compact structure, small grain size and uniform composition, which is beneficial to the plastic processing of the aluminum alloy.
- the strength of the aluminum alloy prepared by the invention is greater than 520 MPa, and the elongation rate is increased to 12-16%.
- Example 1 is a photo of the metallographic microstructure of the Al-Cu-Mg-Mn aluminum alloy ingot prepared in Example 1.
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, and aluminum-zirconium master alloy are used as raw materials; among them, the purity of high-purity aluminum is 99.9%, and the purity of industrial pure magnesium is 99.9% %, the copper content in the aluminum-copper master alloy is 50.0%, the scandium content in the aluminum-scandium master alloy is 2.0%, the zirconium content in the aluminum-zirconium master alloy is 40.0%, and the manganese content in the aluminum-manganese master alloy is 20.0%, The content of yttrium in the aluminum-yttrium master alloy is 10%, and the raw materials are weighed according to the proportion, put into a resistance furnace, heated and melted, and the melt temperature is 750-800 °C.
- B. Mold Design and prepare a certain size of steel mold (wall thickness equal to 30mm) according to the size of the aluminum alloy ingot to serve as the inner mold, and surround the cooling pipe from the bottom of the outer wall of the steel mold upward, and the cooling water is passed into the pipe, the water temperature is 10 °C, and the flow rate is 1 m /s, the sand mold is used as the outer mold, the thickness ratio of the steel mold sand mold is 1:2, and the gating system adopts the steel mold gating system.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 13 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420 ° C in a resistance furnace and kept for 45 minutes, and a hydraulic press is used for three-dimensional large deformation and multi-directional forging, with a reduction rate of 2 mm/s; the first deformation: in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and deformation to obtain a multi-rhombic columnar blank.
- the first deformation in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and de
- the second reversal and commutation deformation is performed: the direction of the maximum dimension of the included angle between the X axis and the Y axis is commutated for many times. Deformation to obtain a spherical polyhedron; repeat the above steps 4 times; and finally reverse and deform along the X-axis direction to obtain a multi-rhombic columnar blank.
- step E the ingot obtained in step E is kept at 430°C for 1.5h, and the mold is kept at 430°C for 30min.
- the extrusion ratio is 15:1, and the extrusion speed should ensure that the ingot strain rate is 0.1s -1 .
- Heat treatment firstly carry out solution treatment, heat the isothermal extruded parts to 500 °C, hold for 2 hours, and then quench them with water; then carry out gradient aging treatment, first heat the solution treated parts to 120 °C for 1.0 hours, and then heat up to 200°C, heat preservation for 7.0h, and air cooling to obtain a product.
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, and aluminum-zirconium master alloy are used as raw materials; among them, the purity of high-purity aluminum is 99.9%, and the purity of industrial pure magnesium is 99.9% %, the copper content in the aluminum-copper master alloy is 50.0%, the scandium content in the aluminum-scandium master alloy is 2.0%, the zirconium content in the aluminum-zirconium master alloy is 40.0%, and the manganese content in the aluminum-manganese master alloy is 20.0%, The content of yttrium in the aluminum-yttrium master alloy is 10%, and the raw materials are weighed according to the proportion, put into a resistance furnace, heated and melted, and the melt temperature is 750-800 °C.
- B. Mold Design and prepare a certain size of steel mold (wall thickness 40mm) according to the size of the aluminum alloy ingot to serve as the inner mold. From the bottom of the outer wall of the steel mold, the cooling pipe is surrounded upward, and cooling water is passed into the pipe. The water temperature is 10 °C and the flow rate is 1m/ s, using a sand mold as the outer mold, in which the steel mold sand mold thickness ratio is 1:2, and the gating system adopts a steel mold gating system.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 14 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420 ° C in a resistance furnace and kept for 45 minutes, and a hydraulic press is used for three-dimensional large deformation and multi-directional forging, with a reduction rate of 2 mm/s; the first deformation: in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and deformation to obtain a multi-rhombic columnar blank.
- the first deformation in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and de
- the second reversal and commutation deformation is performed: the direction of the maximum dimension of the included angle between the X axis and the Y axis is commutated for many times. Deformation to obtain a spherical polyhedron; repeat the above steps 4 times; and finally reverse and deform along the X-axis direction to obtain a multi-rhombic columnar blank.
- step E the ingot obtained in step E is kept at 430°C for 1.5h, and the mold is kept at 430°C for 30min.
- the extrusion ratio is 20:1, and the extrusion speed should ensure that the ingot strain rate is 0.1s -1 .
- Heat treatment firstly carry out solution treatment, heat the isothermal extruded parts to 500 °C, hold for 2 hours, and then quench them with water; then carry out gradient aging treatment, first heat the solution treated parts to 120 °C for 1.0 hours, and then heat up to 200°C, heat preservation for 7.0h, and air cooling to obtain a product.
- Al-Cu-Mg-Mn aluminum alloy without Sc and Zr the alloy composition by weight percentage: copper content 4.6%, magnesium content 0.6%, manganese content 0.8%, and the balance is pure aluminum.
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, and aluminum-zirconium master alloy are used as raw materials.
- the purity of high-purity aluminum is 99.9%
- the purity of industrial pure magnesium is 99.9%
- the content of copper in the aluminum-copper master alloy is 50.0%
- the content of manganese in the aluminum-manganese master alloy is 20.0%.
- the raw materials are weighed according to the proportion, put into a resistance furnace, heated and melted, and the melt temperature is 750-800 °C.
- B. Mold Design and prepare a certain size of steel mold (wall thickness equal to 30mm) according to the size of the aluminum alloy ingot to serve as the inner mold, and surround the cooling pipe from the bottom of the outer wall of the steel mold upward, and the cooling water is passed into the pipe, the water temperature is 10 °C, and the flow rate is 1 m /s, the sand mold is used as the outer mold, the thickness ratio of the steel mold sand mold is 1:2, and the gating system adopts the steel mold gating system.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 14 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420 ° C in a resistance furnace and kept for 45 minutes, and a hydraulic press is used for three-dimensional large deformation and multi-directional forging, with a reduction rate of 2 mm/s; the first deformation: in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and deformation to obtain a multi-rhombic columnar blank.
- the first deformation in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and de
- the second reversal and commutation deformation is performed: the direction of the maximum dimension of the included angle between the X axis and the Y axis is commutated for many times. Deformation to obtain a spherical polyhedron; repeat the above steps 4 times; and finally reverse and deform along the X-axis direction to obtain a multi-rhombic columnar blank.
- step E the ingot obtained in step E is kept at 430°C for 1.5h, and the mold is kept at 430°C for 30min.
- the extrusion ratio is 15:1, and the extrusion speed should ensure that the ingot strain rate is 0.1s -1 .
- Heat treatment firstly carry out solution treatment, heat the isothermal extruded parts to 500 °C, hold for 2 hours, and then quench them with water; then carry out gradient aging treatment, first heat the solution treated parts to 120 °C for 1.0 hours, and then heat up to 200°C, heat preservation for 7.0h, and air cooling to obtain a product.
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, and aluminum-zirconium master alloy are used as raw materials.
- the purity of high-purity aluminum is 99.9%
- the purity of industrial pure magnesium is 99.9%
- the content of copper in the aluminum-copper master alloy is 50.0%
- the content of manganese in the aluminum-manganese master alloy is 20.0%
- the content of yttrium in the aluminum-yttrium master alloy is 20.0%.
- the content is 10%
- the raw materials are weighed according to the proportion, put into a resistance furnace, heated and melted, and the melt temperature is 750-800 °C.
- a steel mould (wall thickness 35mm) of a certain size is designed and prepared as an inner mould, and the cooling pipe is surrounded upward from the bottom of the outer wall of the steel mould. s, using a sand mold as the outer mold, in which the steel mold sand mold thickness ratio is 1:2, and the gating system adopts a steel mold gating system.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 14 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420 ° C in a resistance furnace and kept for 45 minutes, and a hydraulic press is used for three-dimensional large deformation and multi-directional forging, with a reduction rate of 2 mm/s; the first deformation: in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and deformation to obtain a multi-rhombic columnar blank.
- the first deformation in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and de
- the second reversal and commutation deformation is performed: the direction of the maximum dimension of the included angle between the X axis and the Y axis is commutated for many times. Deformation to obtain a spherical polyhedron; repeat the above steps 4 times; and finally reverse and deform along the X-axis direction to obtain a multi-rhombic columnar blank.
- step E the ingot obtained in step E is kept at 430°C for 1.5h, and the mold is kept at 430°C for 30min.
- the extrusion ratio is 20:1, and the extrusion speed should ensure that the ingot strain rate is 0.1s -1 .
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, and aluminum-zirconium master alloy are used as raw materials.
- the purity of high-purity aluminum is 99.9%
- the purity of industrial pure magnesium is 99.9%
- the content of copper in the aluminum-copper master alloy is 50.0%
- the content of manganese in the aluminum-manganese master alloy is 20.0%
- the content of yttrium in the aluminum-yttrium master alloy is 20.0%.
- the content is 10%
- the raw materials are weighed according to the proportion, put into a resistance furnace, heated and melted, and the melt temperature is 750-800 °C.
- B. Mold Design and prepare a certain size of steel mold (wall thickness 30mm) according to the size of the aluminum alloy ingot to serve as the inner mold, and surround the cooling pipe from the bottom of the outer wall of the steel mold upwards. s, using a sand mold as the outer mold, in which the steel mold sand mold thickness ratio is 1:2, and the gating system adopts a steel mold gating system.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 14 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420 ° C in a resistance furnace and kept for 45 minutes, and a hydraulic press is used for three-dimensional large deformation and multi-directional forging, with a reduction rate of 2 mm/s; the first deformation: in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and deformation to obtain a multi-rhombic columnar blank.
- the first deformation in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and de
- the second reversal and commutation deformation is performed: the direction of the maximum dimension of the included angle between the X axis and the Y axis is commutated for many times. Deformation to obtain a spherical polyhedron; repeat the above steps 4 times; and finally reverse and deform along the X-axis direction to obtain a multi-rhombic columnar blank.
- step E the ingot obtained in step E is kept at 430°C for 1.5h, and the mold is kept at 430°C for 30min.
- the extrusion ratio is 15:1, and the extrusion speed should ensure that the ingot strain rate is 0.1s -1 .
- Heat treatment firstly carry out solution treatment, heat the isothermal extruded parts to 500 °C, hold for 2 hours, and then quench them with water; then carry out gradient aging treatment, first heat the solution treated parts to 120 °C for 1.0 hours, and then heat up to 200°C, heat preservation for 7.0h, and air cooling to obtain a product.
- High-purity aluminum, high-purity magnesium, aluminum-copper master alloy, aluminum-scandium master alloy, aluminum-manganese master alloy, and aluminum-zirconium master alloy are used as raw materials.
- the purity of high-purity aluminum is 99.9%
- the purity of industrial pure magnesium is 99.9%
- the content of copper in the aluminum-copper master alloy is 50.0%
- the content of scandium in the aluminum-scandium master alloy is 2.0%
- the content of zirconium in the aluminum-zirconium master alloy is 2.0%.
- the content is 40.0%
- the content of manganese in the aluminum-manganese master alloy is 20.0%.
- the raw materials are weighed according to the proportion, put into a resistance furnace, heated and melted, and the melt temperature is 750-800 °C.
- step D Homogenization heat treatment: the ingot obtained in step D is heated to 480 ⁇ 10° C., kept for 14 hours, and air-cooled to room temperature.
- step F forging pre-deformation: the homogenized ingot obtained in step E is heated to 420 ° C in a resistance furnace and kept for 45 minutes, and a hydraulic press is used for three-dimensional large deformation and multi-directional forging, with a reduction rate of 2 mm/s; the first deformation: in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and deformation to obtain a multi-rhombic columnar blank.
- the first deformation in Deformation is performed in the direction of the largest dimension (Y-axis), and when the strain reaches 0.5, the first turn-over deformation is performed: along the radial direction (X-axis), that is, perpendicular to the first pressing direction (Y-axis) ) for several times of commutation and de
- the second reversal and commutation deformation is performed: the direction of the maximum dimension of the included angle between the X axis and the Y axis is commutated for many times. Deformation to obtain a spherical polyhedron; repeat the above steps 4 times; and finally reverse and deform along the X-axis direction to obtain a multi-rhombic columnar blank.
- step E the ingot obtained in step E is kept at 430°C for 1.5h, and the mold is kept at 430°C for 30min.
- the extrusion ratio is 15:1, and the extrusion speed should ensure that the ingot strain rate is 0.1s -1 .
- Heat treatment firstly carry out solution treatment, heat the isothermal extruded parts to 500 °C, hold for 2 hours, and then quench them with water; then carry out gradient aging treatment, first heat the solution treated parts to 120 °C for 1.0 hours, and then heat up to 200°C, heat preservation for 7.0h, and air cooling to obtain a product.
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)
- Forging (AREA)
Abstract
Description
Claims (10)
- 一种高强Al-Cu-Mg-Mn铝合金,其特征在于,按重量百分比,包括以下成分:Cu:4.5-6.3%,Mg:0.6-1.2%,Mn:0.6-1.5%,Si: ≤0.5%,Fe:≤0.5%,Sc:0.15-0.35%,Zr:0.1-0.2%,Y:0.1-0.3%,Sc与Zr按质量比Sc:Zr=1-3:1添加,余量为铝及不可除杂质。
- 根据权利要求1所述的一种高强Al-Cu-Mg-Mn铝合金,其特征在于,按重量百分比,包括以下成分:Cu:4.5-5.2%,Mg:0.6-1.0%,Mn:0.6-1.5%,Si: ≤0.5%,Fe: ≤0.5%,Sc:0.2-0.3%,Zr:0.12-0.15%,Y:0.2-0.3%,Sc与Zr按质量比Sc:Zr=1-3:1添加,余量为铝及不可除杂质。
- 根据权力要求1-2所述的一种高强Al-Cu-Mg-Mn铝合金,其特征在于,按重量百分比,包括以下成分:Cu:5.0%,Mg:0.6%,Mn:1.0%,Si:≤0.5%,Fe: ≤0.5%,Sc:0.26%,Zr:0.13%,Sc:Zr=2:1,Y:0.3%,余量为铝及不可除杂质。
- 如权利要求1-3所述一种高强Al-Cu-Mg-Mn铝合金的制备方法,其特征在于,按以下步骤进行:A、熔炼:以高纯铝、高纯镁、铝铜中间合金、铝钪中间合金、铝锰中间合金、铝锆中间合金、铝钇中间合金为原料;其中,高纯铝纯度≥99.99%,工业纯镁的纯度≥99.95%,铝铜中间合金中铜的含量≥50.0%,铝钪中间合金中钪的含量≥1.0%,铝锆中间合金中锆的含量≥10.0%,铝锰中间合金中锰的含量≥20.0%,铝钇中间合金中钇的含量≥10.0%;按成分配比称取原料,装入电阻炉内,加热熔融;B、模具:依据铝合金铸锭尺寸设计并制备一定尺寸的钢模具;钢模具的壁厚大于等于30mm,充当内模,从钢模具外壁底部向上环绕冷却管,管内通入冷却水,冷却水温度和流量可以控制,采用砂型模具作为外模,其中钢模具与砂型模具厚度比为1:(2-5),浇注系统采用钢模具浇注系统;通过控制冷却水温度和流量控制冷却速度;C、精炼、除杂、除气:待金属熔体完全合金化之后,将除杂剂加入合金熔体中进行聚渣,并同时通入氩气,时间10-20分钟,静置、扒渣,重复上述操作2-3次,然后将铝合金熔体静置,时间大于20分钟;D、浇注:待铝合金熔体精炼、除杂、除气完毕,保持熔体温度720±5℃,浇注至B所设计制备的模具冷却凝固,得到铸锭;E、均匀化热处理:将步骤D获得的铸锭加热至480±10℃,并保温13-15h,出炉空冷至室温;F:锻造预变形:将步骤E获得的均匀化铸锭在电阻炉中加热至420-450℃并保温40~60min,然后进行三维大变形多向锻造,压下速率1~3mm/s、优选为3mm/s;第一次变形:在最大尺寸方向进行压下变形,当应变达到0.5~0.8时,进行第一次翻转换向变形:沿着径向即垂直于第一次加压方向进行换向多次变形,得到多菱形柱状坯料,当应变达到0.5~0.8时,进行第二次翻转换向变形:沿着X轴向和Y轴向之间夹角最大尺寸方向进行换向多次变形,得到球状多面体;重复上述步骤3-5次;最后沿X轴方向换向变形,得到多菱形柱状坯料;G、等温变形加工:将步骤E获得的坯料在420-450℃保温1~2h、优选为1.5h,模具在420-450℃保温25-35min,挤压比为(10-20):1,挤压速度确保铸锭应变速率为0.05~0.2s -1;或等温锻造,坯料在420-450℃保温1-2h,模具在420-450℃保温25-40min,锻造时液压机下压速度为0.05~0.1mm/s、优选为0.05 mm/s;得到等温变形加工件;H、热处理:先进行固溶处理,将等温变形加工件加热至480-520℃,保温1-3h,出炉水淬;然后进行梯度时效处理,首先将固溶处理件加热至100-130℃保温0.5-1.5h,随后升温至170-220℃保温5.0-10.0h,空冷,得到制件。
- 根据权利要求4所述的一种高强Al-Cu-Mg-Mn铝合金及其制备方法,其特征在于,步骤A:加热后熔体温度为750-800℃。
- 根据权利要求4所述的一种高强Al-Cu-Mg-Mn铝合金及其制备方法,其特征在于,步骤F:将步骤E获得的均匀化铸锭在电阻炉中加热至420-450℃并保温45min,然后进行三维大变形多向锻造,压下速率2mm/s;第一次变形:在最大尺寸方向进行压下变形,当应变达到0.5时,进行第一次翻转换向变形:沿着径向即垂直于第一次加压方向进行换向多次变形,得到多菱形柱状坯料,当应变达到0.5时,进行第二次翻转换向变形:沿着X轴向和Y轴向之间夹角最大尺寸方向进行换向多次变形,得到球状多面体;重复上述步骤3-5次;最后沿X轴方向换向变形,得到多菱形柱状坯料。
- 根据权利要求4所述的一种高强Al-Cu-Mg-Mn铝合金及其制备方法,其特征在于;步骤G:采用等温变形工艺,坯料在420-450℃保温1.5h,模具在420-450℃保温30min,挤压比为(10-20):1,挤压速度需确保铸锭应变速率为0.1s -1;或等温锻造,坯料在420-450℃保温1.5h,模具在420-450℃保温30min,锻造时液压机下压速度0.05mm/s。
- 根据权利要求4所述的一种高强Al-Cu-Mg-Mn铝合金及其制备方法,其特征在于步骤H:固溶处理,将等温变形加工件加热至500℃,保温2h,出炉水淬。
- 根据权利要求4所述的一种高强Al-Cu-Mg-Mn铝合金及其制备方法,其特征在于,步骤H:梯度时效处理,首先将固溶处理件加热至120℃保温1h,随后升温至200℃保温7h,空冷,得到制件。
- 根据权利要求5~9任意一项所述的一种高强Al-Cu-Mg-Mn铝合金及其制备方法,其特征在于:所得产品的强度为520~530MPa、延伸率为12%~16%。
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US18/023,733 US20240035123A1 (en) | 2020-08-30 | 2020-08-31 | High-strength al-cu-mg-mn aluminum alloy and preparation method therefor |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN202010891335.2 | 2020-08-30 | ||
CN202010891335.2A CN111996426B (zh) | 2020-08-30 | 2020-08-30 | 一种高强Al-Cu-Mg-Mn铝合金及其制备方法 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2022041268A1 true WO2022041268A1 (zh) | 2022-03-03 |
Family
ID=73465665
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/CN2020/112715 WO2022041268A1 (zh) | 2020-08-30 | 2020-08-31 | 一种高强Al-Cu-Mg-Mn铝合金及其制备方法 |
Country Status (3)
Country | Link |
---|---|
US (1) | US20240035123A1 (zh) |
CN (1) | CN111996426B (zh) |
WO (1) | WO2022041268A1 (zh) |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114959378A (zh) * | 2022-06-15 | 2022-08-30 | 湖南江滨机器(集团)有限责任公司 | 一种铝硅合金和铝硅合金的铸件的制备方法 |
CN115044843A (zh) * | 2022-06-29 | 2022-09-13 | 东北大学 | 一种轧制态碳纤维增强铝合金复合材料的制备方法 |
CN115094283A (zh) * | 2022-06-22 | 2022-09-23 | 中南大学 | 高强高导铝合金电枢材料及其制造方法和应用 |
CN115747592A (zh) * | 2022-08-29 | 2023-03-07 | 山东南山铝业股份有限公司 | 一种各向同性高强度变形铝合金及其制备方法 |
CN115821091A (zh) * | 2022-12-14 | 2023-03-21 | 四川越创铝业有限公司 | 一种铝合金制备方法、铝合金浇铸装置 |
CN115874121A (zh) * | 2022-12-13 | 2023-03-31 | 山东创新金属科技有限公司 | 一种可热处理强化铝合金的时效热处理工艺 |
CN115874031A (zh) * | 2022-12-07 | 2023-03-31 | 东北轻合金有限责任公司 | 一种航空用2a12铝合金板材的加工方法 |
CN116837246A (zh) * | 2023-07-04 | 2023-10-03 | 秦皇岛峰越科技有限公司 | 原位生成铝基碳化钛复合材料的制备方法 |
CN116984844A (zh) * | 2023-09-27 | 2023-11-03 | 山东三源铝业有限公司 | 一种实用型新能源水冷板的制造方法 |
CN117165877A (zh) * | 2023-11-01 | 2023-12-05 | 湖南卓创精材科技股份有限公司 | 一种提高铝合金性能的制备方法 |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN113857401B (zh) * | 2021-09-05 | 2023-05-05 | 桂林理工大学 | 一种Al-Zn-Mg-Sc合金硬盘盒体等温挤压工艺 |
CN115652154B (zh) * | 2022-11-10 | 2023-08-22 | 中力鸿(深圳)新材料科技有限公司 | 一种高强耐热高钪Al-Cu-Mg系合金及其制造工艺 |
CN115821132A (zh) * | 2022-11-25 | 2023-03-21 | 江苏徐工工程机械研究院有限公司 | 一种铝合金及其制备方法 |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101240390A (zh) * | 2008-03-11 | 2008-08-13 | 中南大学 | 一种高强耐热耐疲劳损伤铝合金及其制备方法 |
JP2017128789A (ja) * | 2016-01-19 | 2017-07-27 | 株式会社神戸製鋼所 | 耐熱性アルミニウム合金形材及びアルミニウム合金部材 |
CN108342628A (zh) * | 2018-02-12 | 2018-07-31 | 沈阳铸造研究所有限公司 | 一种铝铜镁系高强耐热铸造铝合金及其制备方法 |
CN111020320A (zh) * | 2019-09-23 | 2020-04-17 | 山东南山铝业股份有限公司 | 一种高强度铝合金及其生产方法 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8002913B2 (en) * | 2006-07-07 | 2011-08-23 | Aleris Aluminum Koblenz Gmbh | AA7000-series aluminum alloy products and a method of manufacturing thereof |
JP6185870B2 (ja) * | 2014-03-27 | 2017-08-23 | 株式会社神戸製鋼所 | 溶接構造部材用アルミニウム合金鍛造材およびその製造方法 |
CN106541064B (zh) * | 2015-09-22 | 2018-08-21 | 首都航天机械公司 | 一种超大规格铝合金铸锭的锻造开坯工艺方法 |
CN106498248B (zh) * | 2016-11-18 | 2018-11-13 | 东北轻合金有限责任公司 | 铝合金模锻件的制造方法 |
-
2020
- 2020-08-30 CN CN202010891335.2A patent/CN111996426B/zh active Active
- 2020-08-31 WO PCT/CN2020/112715 patent/WO2022041268A1/zh active Application Filing
- 2020-08-31 US US18/023,733 patent/US20240035123A1/en active Pending
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101240390A (zh) * | 2008-03-11 | 2008-08-13 | 中南大学 | 一种高强耐热耐疲劳损伤铝合金及其制备方法 |
JP2017128789A (ja) * | 2016-01-19 | 2017-07-27 | 株式会社神戸製鋼所 | 耐熱性アルミニウム合金形材及びアルミニウム合金部材 |
CN108342628A (zh) * | 2018-02-12 | 2018-07-31 | 沈阳铸造研究所有限公司 | 一种铝铜镁系高强耐热铸造铝合金及其制备方法 |
CN111020320A (zh) * | 2019-09-23 | 2020-04-17 | 山东南山铝业股份有限公司 | 一种高强度铝合金及其生产方法 |
Non-Patent Citations (1)
Title |
---|
LIAO SIMIN: "Microstructural Evolution of Al-Cu-Mg-Mn-Sc-Zr Alloy during Homogenization", HEAT TREATMENT OF METALS, vol. 45, no. 4, 25 April 2020 (2020-04-25), JP , pages 55 - 59, XP055903184, ISSN: 0254-6051, DOI: 10.13251/j.issn.0254-6051.2020.04.011 * |
Cited By (18)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114959378A (zh) * | 2022-06-15 | 2022-08-30 | 湖南江滨机器(集团)有限责任公司 | 一种铝硅合金和铝硅合金的铸件的制备方法 |
CN114959378B (zh) * | 2022-06-15 | 2023-05-26 | 湖南江滨机器(集团)有限责任公司 | 一种铝硅合金和铝硅合金的铸件的制备方法 |
CN115094283A (zh) * | 2022-06-22 | 2022-09-23 | 中南大学 | 高强高导铝合金电枢材料及其制造方法和应用 |
CN115094283B (zh) * | 2022-06-22 | 2023-06-09 | 中南大学 | 高强高导铝合金电枢材料及其制造方法和应用 |
CN115044843A (zh) * | 2022-06-29 | 2022-09-13 | 东北大学 | 一种轧制态碳纤维增强铝合金复合材料的制备方法 |
CN115044843B (zh) * | 2022-06-29 | 2023-09-22 | 东北大学 | 一种轧制态碳纤维增强铝合金复合材料的制备方法 |
CN115747592B (zh) * | 2022-08-29 | 2024-04-16 | 山东南山铝业股份有限公司 | 一种各向同性高强度变形铝合金及其制备方法 |
CN115747592A (zh) * | 2022-08-29 | 2023-03-07 | 山东南山铝业股份有限公司 | 一种各向同性高强度变形铝合金及其制备方法 |
CN115874031A (zh) * | 2022-12-07 | 2023-03-31 | 东北轻合金有限责任公司 | 一种航空用2a12铝合金板材的加工方法 |
CN115874031B (zh) * | 2022-12-07 | 2023-08-15 | 东北轻合金有限责任公司 | 一种航空用2a12铝合金板材的加工方法 |
CN115874121A (zh) * | 2022-12-13 | 2023-03-31 | 山东创新金属科技有限公司 | 一种可热处理强化铝合金的时效热处理工艺 |
CN115821091A (zh) * | 2022-12-14 | 2023-03-21 | 四川越创铝业有限公司 | 一种铝合金制备方法、铝合金浇铸装置 |
CN115821091B (zh) * | 2022-12-14 | 2024-02-06 | 四川越创铝业有限公司 | 一种铝合金制备方法、铝合金浇铸装置 |
CN116837246B (zh) * | 2023-07-04 | 2024-01-23 | 秦皇岛峰越科技有限公司 | 原位生成铝基碳化钛复合材料的制备方法 |
CN116837246A (zh) * | 2023-07-04 | 2023-10-03 | 秦皇岛峰越科技有限公司 | 原位生成铝基碳化钛复合材料的制备方法 |
CN116984844A (zh) * | 2023-09-27 | 2023-11-03 | 山东三源铝业有限公司 | 一种实用型新能源水冷板的制造方法 |
CN117165877A (zh) * | 2023-11-01 | 2023-12-05 | 湖南卓创精材科技股份有限公司 | 一种提高铝合金性能的制备方法 |
CN117165877B (zh) * | 2023-11-01 | 2024-01-23 | 湖南卓创精材科技股份有限公司 | 一种提高铝合金性能的制备方法 |
Also Published As
Publication number | Publication date |
---|---|
CN111996426B (zh) | 2021-11-23 |
CN111996426A (zh) | 2020-11-27 |
US20240035123A1 (en) | 2024-02-01 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2022041268A1 (zh) | 一种高强Al-Cu-Mg-Mn铝合金及其制备方法 | |
CN108425050B (zh) | 一种高强高韧铝锂合金及其制备方法 | |
CN111996425B (zh) | 一种高强Al-Zn-Mg-Cu铝合金及其制备方法 | |
CN108251710B (zh) | 一种适合挤压铸造的高强韧高硅铝合金及其制备工艺 | |
CN115198149B (zh) | 免热处理压铸铝合金及其制备方法 | |
CN114645162A (zh) | 一种难变形高温合金的细晶均质盘锻件的制造方法 | |
CN106636806A (zh) | 一种细小晶粒中等强度铝合金及其制备方法与应用 | |
CN102330004A (zh) | 一种铝合金模锻件的制造方法 | |
CN113430429A (zh) | 一种多元耐热变形稀土铝合金及其制备方法 | |
CN109536803B (zh) | 一种高延展性低稀土镁合金板材及其制备方法 | |
CN114517267A (zh) | 一种抗冲击稀土铝合金及制造方法 | |
CN112981198B (zh) | 一种高强韧铝锂合金薄板的短流程制备方法 | |
CN111218597B (zh) | 一种低成本高导热超高塑性镁合金及其制备方法 | |
CN110205505B (zh) | 一种室温高塑性锌合金制备方法 | |
CN113897567B (zh) | 一种快速细化和均匀化铸态铝锂合金的均匀化形变热处理方法 | |
CN114525421B (zh) | 一种镁合金及其制备方法与应用 | |
WO2020052129A1 (zh) | 一种高延展性高强度的稀土铝合金材料及其制备方法 | |
JP3852915B2 (ja) | 輸送機器用アルミニウム合金の半溶融成型ビレットの製造方法 | |
US20230074156A1 (en) | Magnesium alloy for wheel and preparation method thereof | |
CN114480930B (zh) | 客车车身骨架用铝合金型材及其制备方法 | |
CN114686735A (zh) | 一种具有梯度结构变形铝合金及其制备方法 | |
CN113388761A (zh) | 一种电子封装用铝硅合金盖板材料及其制备方法 | |
CN113444932A (zh) | 一种高强度变形铝合金及其制备方法 | |
CN111961896A (zh) | 一种铝合金铸件的制备方法 | |
CN111809091A (zh) | 一种高性能镁稀土合金及其制备方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 20950937 Country of ref document: EP Kind code of ref document: A1 |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 20950937 Country of ref document: EP Kind code of ref document: A1 |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 20950937 Country of ref document: EP Kind code of ref document: A1 |
|
32PN | Ep: public notification in the ep bulletin as address of the adressee cannot be established |
Free format text: NOTING OF LOSS OF RIGHTS PURSUANT TO RULE 112(1) EPC (EPO FORM 1205N DATED 04/10/2023) |