CN115074582B - Preparation method of hypoeutectic Al-Ce alloy with bimodal grain structure - Google Patents
Preparation method of hypoeutectic Al-Ce alloy with bimodal grain structure Download PDFInfo
- Publication number
- CN115074582B CN115074582B CN202210697013.3A CN202210697013A CN115074582B CN 115074582 B CN115074582 B CN 115074582B CN 202210697013 A CN202210697013 A CN 202210697013A CN 115074582 B CN115074582 B CN 115074582B
- Authority
- CN
- China
- Prior art keywords
- alloy
- hypoeutectic
- grain structure
- bimodal grain
- rolling
- 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.)
- Active
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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The invention discloses a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure, belonging to the technical field of processing and preparation of aluminum alloy materials. The alloy structure has the characteristic of mixing fine crystals and coarse crystals, wherein the size distribution of the fine crystals is 2-15 mu m, and the size distribution of the coarse crystals is 20-50 mu m. The preparation method comprises the following steps: placing the as-cast hypoeutectic Al-Ce alloy billet into a furnace, carrying out hot rolling after heat preservation at 200-300 ℃, and then carrying out cold rolling; then semi-solid heat preservation treatment is carried out; and then quenching to obtain hypoeutectic Al-Ce alloy with a bimodal grain structure. The invention can obtain a bimodal grain structure with spherical coarse-fine mixture in the hypoeutectic Al-Ce alloy, thereby realizing the great improvement of the comprehensive mechanical property of the hypoeutectic Al-Ce alloy. The invention has simple process flow and low requirement on equipment, and is suitable for industrial production.
Description
Technical Field
The invention relates to a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure; belonging to the technical field of processing and preparing aluminum alloy materials.
Background
The Al-Ce alloy has excellent thermal stability and castability, is a preferable material for the next-generation heat-resistant automobile structural parts, but the poor mechanical properties make it disadvantageous in competition with other cast alloys. Eutectic structure of Al-Ce alloyFibrous Al 11 Ce 3 The phase composition, this fibrous second phase, severely compromises the mechanical properties of the alloy, and the presence of other elements has not been found to effect significant deterioration of the morphology of the fiber. Although laser additive manufacturing, powder metallurgy and other modes can prepare the Al-Ce alloy with a fine microstructure, the high preparation cost is not beneficial to large-scale industrial production. Solid solution strengthening and precipitation strengthening can also improve the strength of al—ce alloy, but cause a significant decrease in elongation. The conventional method for obtaining the Al-Ce alloy with high strength and high ductility still has great difficulty at present.
Grain refinement is an effective way to improve both alloy strength and ductility, but the refinement effect brought by the addition of refiners in conventional casting is limited, often relying on subsequent plastic deformation to achieve grain refinement. However, after plastic deformation or recrystallization annealing, the eutectic alloy can achieve grain refinement, but the streamline distribution of the eutectic structure still causes anisotropy of material properties. Although the anisotropy can be eliminated by long-term heat preservation at high temperature, coarsening of crystal grains can be caused. Although the processing modes such as equal channel extrusion and high-pressure torsion can also realize the grain refinement of the eutectic alloy, the fine grains reduce the work hardening capacity and the deformation stability of the material, and are unfavorable for devices in long-term service. The bimodal grain structure realizes that the fine grain strength is reserved, simultaneously enhances the work hardening capacity of the alloy, resists the deformation instability of fine grains, and is an ideal structure for comprehensively improving the strength and the ductility. Therefore, the hypoeutectic Al-Ce alloy which is isotropic and has a bimodal grain structure is prepared by a proper processing mode and a subsequent heat treatment, and has important industrial value.
Disclosure of Invention
Aiming at the defects of coarse structure and poor plasticity of the existing hypoeutectic Al-Ce alloy, the invention provides a preparation method of the hypoeutectic Al-Ce alloy with a bimodal grain structure, which has excellent mechanical properties. The invention can realize controllable bimodal grain structure, high production efficiency and excellent mechanical properties of the prepared alloy.
The invention provides a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure, the obtained alloy structure has the characteristic of mixing fine crystals and coarse crystals, wherein the size distribution of the fine crystals is 2-15 mu m, the size distribution of the coarse crystals is 20-50 mu m, and all grains are equiaxed spheres.
The invention provides a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure, wherein the tensile strength of the obtained alloy is 125-171MPa, and the elongation is 12.5-19%; when the components are the same, compared with an as-cast product, the tensile strength of the obtained alloy is improved by more than 20%, the elongation is improved by more than 50%, and particularly, the tensile strength of the alloy can be improved by 28% -36%, and the elongation is improved by 53% -87%.
The invention provides a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure, wherein the mass fraction of Ce in the hypoeutectic Al-Ce alloy is 3-8%, preferably 4-8%, and more preferably 5-8%. When the Ce content is lower than the range, the eutectic structure content is low, and the alloy strength is poor; when the temperature is higher than the above range, the deformation capability of the alloy is poor, the processing process is easy to crack, the rejection rate is high, the subsequent cold rolling processing is not facilitated, the solidification range of the alloy with high Ce content is small, and the subsequent determination of the semi-solid temperature is not facilitated.
The invention provides a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure, wherein the volume ratio of coarse crystals in the obtained alloy structure is 15-35%, and the balance is fine crystals.
The invention provides a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure, which comprises the following steps:
step one
Placing the as-cast hypoeutectic Al-Ce alloy billet into a holding furnace, and holding the temperature at 200-300 ℃, preferably 230-300 ℃ and then carrying out multi-pass isothermal hot rolling; obtaining a hot rolled plate;
step two
Carrying out multi-pass cold rolling on the hot rolled material obtained in the step one; obtaining a cold-rolled sheet;
step three
Semi-solid heat preservation treatment is carried out on the cold-rolled sheet obtained in the step two; then quenching; obtaining hypoeutectic Al-Ce alloy with a bimodal grain structure; the temperature of the semi-solid heat preservation treatment is 650-655 ℃, and the heat preservation time is 15-30 min.
As a preferable scheme, the hypoeutectic Al-Ce alloy with a bimodal grain structure is prepared by the method; the rolling pass of the hot rolling in the first step is not less than 5 times, and the total deformation is 50-80%. The multi-pass hot rolling improves the deformability of the Al-Ce alloy, promotes the recovery and recrystallization of the inside of a structure, and reduces the deformation resistance of cold rolling in the subsequent process.
As a preferable scheme, the hypoeutectic Al-Ce alloy with a bimodal grain structure is prepared by the method; in the second step, the rolling pass of cold rolling is not less than 5 times, and the total deformation is 40-60%. Multipass cold rolling reduces the likelihood of sheet edge cracking and stores sufficient deformation energy within the structure.
The invention relates to a preparation method of hypoeutectic Al-Ce alloy with a bimodal grain structure; the tensile strength of the obtained alloy is 125-171MPa, and the elongation is 12.5-19%; when the components are the same, the tensile strength of the alloy is improved by 28 to 36 percent and the elongation is improved by 53 to 87 percent compared with the cast product.
Principle and advantages
In the hypoeutectic Al-Ce alloy, the mass fraction of Ce is 3-8%, and when the content of Ce is lower than the range, the content of eutectic structure is low, and the alloy strength is poor; above this interval, the alloy has poor deformability, and the processing process is easy to crack, so that the rejection rate is high.
The Al-Ce alloy plate is prepared by combining multi-pass hot rolling with multi-pass cold rolling, and the primary forming of the plate is realized by hot rolling; cold rolling provides a significant amount of deformation energy storage into the tissue while achieving the final gauge sheet size, which provides sufficient driving force for subsequent strain-induced melting activation.
The cold-rolled sheet is insulated in a semi-solid temperature interval and the heat-insulating time is strictly controlled, so that eutectic tissues with a large amount of energy storage and lower melting point are melted, and part of unmelted aluminum matrix is in a regular sphere shape under the action of surface energy; in the subsequent quenching process, the melted structure is cooled to fine grains and eutectic structures form fine crystals, and unmelted matrix aluminum forms coarse crystals, so that the hypoeutectic Al-Ce alloy with the bimodal grain structure is obtained.
Drawings
FIG. 1 is an SEM micrograph of Al-4Ce prepared in example 1;
FIG. 2 is an SEM micrograph of Al-5Ce prepared in example 2;
FIG. 3 is an SEM micrograph of Al-7Ce prepared in example 3;
FIG. 4 is an SEM micrograph of Al-8Ce prepared in example 4;
FIG. 5 is an SEM micrograph of Al-5Ce prepared in comparative example 1;
FIG. 6 is an SEM micrograph of Al-8Ce prepared in comparative example 2;
FIG. 7 is a photograph of a plate of Al-5Ce prepared in comparative example 3;
FIG. 8 is an SEM micrograph of Al-8Ce of comparative example 4.
Detailed Description
Example 1
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-4Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 230 ℃ for 1 hour in a heat preservation furnace, and then is rolled for a plurality of times, wherein the rolling passes are 6 times, and the total deformation is 75 percent. And (3) carrying out cold rolling on the rough rolled plate at room temperature for multiple times, wherein the rolling passes are 7 times, and the total deformation is 60%, so that the plate with the thickness of 2mm is obtained. And (3) carrying out heat preservation treatment on the cold-rolled sheet in a heat treatment furnace for 15min at 650 ℃, quenching after heat preservation, and polishing to remove surface oxide skin to obtain the hypoeutectic Al-Ce alloy with the bimodal grain structure. The average grain size of fine crystals in the Al-4Ce alloy prepared by the process is 12.2 mu m, the size distribution of coarse crystals is 37.2 mu m, and the volume ratio of the coarse crystals is about 18%; the tensile strength and the elongation of the alloy are 125.6MPa and 18.9 percent respectively, which are improved by 35.8 percent and 53.7 percent respectively compared with 92.5MPa and 12.3 percent in the as-cast state.
Example 2
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-5Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 250 ℃ for 1 hour in a heat preservation furnace, and then is rolled for a plurality of times, wherein the rolling passes are 6 times, and the total deformation is 75 percent. And (3) carrying out cold rolling on the rough rolled plate at room temperature for multiple times, wherein the rolling passes are 8 times, and the total deformation is 60%, so that the plate with the thickness of 2mm is obtained. And (3) carrying out heat preservation treatment on the cold-rolled sheet in a heat treatment furnace for 30min at 655 ℃, quenching after heat preservation, and polishing to remove surface oxide skin to obtain the hypoeutectic Al-Ce alloy with the bimodal grain structure. The average grain size of fine crystals in the Al-5Ce alloy prepared by the process is 6.4 mu m, the size distribution of coarse crystals is 35.3 mu m, and the volume ratio of the coarse crystals is about 32%; the tensile strength and the elongation of the alloy are 132.6MPa and 16.8 percent respectively, and are improved by 28.1 percent and 57 percent respectively compared with 103.5MPa and 10.7 percent in the as-cast state.
Example 3
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-7Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 290 ℃ for 1h in a heat preservation furnace, and then is rolled for multiple times, wherein the rolling passes are 7 times, and the total deformation is 80%. And (3) carrying out cold rolling on the rough rolled plate at room temperature for a plurality of times, wherein the rolling passes are 10 times, and the total deformation is 50%, so as to obtain the plate with the thickness of 2 mm. And (3) carrying out heat preservation treatment on the cold-rolled sheet in a heat treatment furnace for 15min at 655 ℃, quenching after heat preservation, and polishing to remove surface oxide skin to obtain the hypoeutectic Al-Ce alloy with the bimodal grain structure. The average grain size of fine crystals in the Al-7Ce alloy prepared by the process is 5.7 mu m, the size distribution of coarse crystals is 36.5 mu m, and the volume ratio of the coarse crystals is about 30%; the tensile strength and the elongation of the alloy are 162.4MPa and 13.5 percent respectively, and are improved by 28.8 percent and 82.4 percent respectively compared with 126.1MPa and 7.4 percent in the as-cast state.
Example 4
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-8Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 290 ℃ for 1h in a heat preservation furnace, and then is rolled for a plurality of times, wherein the rolling passes are 9 times, and the total deformation is 80%. And (3) carrying out cold rolling on the rough rolled plate at room temperature for a plurality of times, wherein the rolling passes are 12 times, and the total deformation is 50%, so as to obtain the plate with the thickness of 2 mm. And (3) carrying out heat preservation treatment on the cold-rolled sheet in a heat treatment furnace for 15min at 655 ℃, quenching after heat preservation, and polishing to remove surface oxide skin to obtain the hypoeutectic Al-Ce alloy with the bimodal grain structure. The average grain size of fine crystals in the Al-8Ce alloy prepared by the process is 12.3 mu m, the size distribution of coarse crystals is 43.4 mu m, and the volume ratio of the coarse crystals is about 23%; the tensile strength and the elongation of the alloy are 170.8MPa and 12.7 percent respectively, and are improved by 30.5 percent and 86.8 percent respectively compared with 130.9MPa and 6.8 percent in the as-cast state.
Comparative example 1
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-5Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 230 ℃ for 1 hour in a heat preservation furnace, and then is rolled for a plurality of times, wherein the rolling passes are 6 times, and the total deformation is 75 percent. And (3) carrying out cold rolling on the rough rolled plate at room temperature for multiple times, wherein the rolling passes are 7 times, and the total deformation is 60%, so that the plate with the thickness of 2mm is obtained. And (3) carrying out heat preservation treatment on the cold-rolled sheet in a heat treatment furnace for 15min at 645 ℃, and quenching after heat preservation is finished. Compared with the example 2, the Al-5Ce alloy prepared by the process has the advantages that the eutectic structure is not melted due to the temperature of 645 ℃ at the rearmost heat preservation, and the structure is formed by a recrystallized matrix and coarsened Al 11 Ce 3 The particles are mainly. The tensile strength and elongation of the alloy are 95.2MPa and 14.3 percent respectively, and the strength is lower than that of the as-cast alloy.
Comparative example 2
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-8Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 290 ℃ for 1h in a heat preservation furnace, and then is rolled for a plurality of times, wherein the rolling passes are 9 times, and the total deformation is 80%. The rough rolling plate is subjected to room temperature for a plurality of timesAnd (3) carrying out cold rolling for 12 times, wherein the total deformation is 50%, and obtaining the plate with the thickness of 2 mm. And (3) carrying out heat preservation treatment on the cold-rolled sheet in a heat treatment furnace for 5min at 655 ℃, quenching after heat preservation, and polishing to remove surface oxide skin to obtain the hypoeutectic Al-Ce alloy with the bimodal grain structure. The Al-8Ce alloy prepared by the process has a eutectic structure which is not completely melted due to the rearmost heat preservation temperature of 655 ℃ and the heat preservation time of 5min, and the structure is composed of a recrystallized matrix and coarsened Al 11 Ce 3 The particles are mainly. The tensile strength and elongation of the alloy are 115.4MPa and 7.4 percent respectively, and the strength is lower than that of the as-cast alloy.
Comparative example 3
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-5Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. And carrying out cold rolling on the ingot blank for a plurality of times at room temperature, wherein the rolling passes are 14 times, and the total deformation is 90%, so as to obtain the plate with the thickness of 2 mm. As hot rolling and rough rolling are not carried out, the cold rolling deformation is large, and the edge crack of the plate is obvious, thus being an unqualified product.
Comparative example 4
The method comprises the steps of taking industrial pure aluminum and Al-20Ce intermediate alloy as raw materials, adopting gravity casting to prepare an Al-8Ce alloy ingot blank, and carrying out face milling cutting on the ingot blank to obtain a rough rolling ingot blank with the size of 100mm multiplied by 40mm multiplied by 20 mm. The ingot blank is kept at the temperature of 300 ℃ for 1 hour in a heat preservation furnace, and then is rolled for multiple times, wherein the rolling passes are 12 times, the total deformation is 90%, and the plate with the thickness of 2mm is obtained. And (3) carrying out heat preservation treatment on the hot rolled plate in a heat treatment furnace for 15min at 655 ℃, quenching after heat preservation, and polishing to remove surface oxide skin. Compared with the example 4, the technology has the advantages that the cold rolling is not carried out, the deformation energy stored in the structure is low, the grains after recrystallization are coarse, and the eutectic region is slowly melted, so that the structure is mainly coarse crystals. The average grain size of fine crystals in the Al-8Ce alloy prepared by the process is 7.8 mu m, the size distribution of coarse crystals is 48.4 mu m, and the volume ratio of the coarse crystals is about 86%; the tensile strength and elongation of the alloy are 120.6MPa and 6.0% respectively, and the strength and elongation are lower than those of the as-cast alloy.
Claims (5)
1. A method for preparing hypoeutectic Al-Ce alloy with bimodal grain structure, which is characterized in that: the obtained alloy structure has the characteristic of mixing fine crystals and coarse crystals, wherein the size distribution of the fine crystals is 2-15 mu m, the size distribution of the coarse crystals is 20-50 mu m, and all crystal grains are equiaxed spheres; the mass fraction of Ce in the hypoeutectic Al-Ce alloy is 3-8%; the hypoeutectic Al-Ce alloy with the bimodal grain structure is prepared by the following method:
step one
Placing the as-cast hypoeutectic Al-Ce alloy blank in a holding furnace, and carrying out multi-pass isothermal hot rolling after holding the temperature at 200-300 ℃; obtaining a hot rolled plate;
step two
Carrying out multi-pass cold rolling on the hot rolled material obtained in the step one; obtaining a cold-rolled sheet;
step three
Semi-solid heat preservation treatment is carried out on the cold-rolled sheet obtained in the step two; then quenching; obtaining hypoeutectic Al-Ce alloy with a bimodal grain structure; the temperature of the semi-solid heat preservation treatment is 650-655 ℃, and the heat preservation time is 15-30 min.
2. The method for preparing a hypoeutectic Al-Ce alloy with a bimodal grain structure according to claim 1, wherein: the tensile strength of the obtained alloy is 125-171MPa, and the elongation is 12.5-19%; when the components are the same, the tensile strength of the alloy is improved by 28% -36% and the elongation is improved by 53% -87% compared with an as-cast product.
3. The method for preparing a hypoeutectic Al-Ce alloy with a bimodal grain structure according to claim 1, wherein: the volume ratio of coarse crystals in the obtained alloy structure is 15-50%, and the balance is fine crystals.
4. The method for preparing a hypoeutectic Al-Ce alloy with a bimodal grain structure according to claim 1, wherein: and in the first step, the rolling pass of hot rolling is not less than 5 times, and the total deformation is 50-80%.
5. The method for preparing a hypoeutectic Al-Ce alloy with a bimodal grain structure according to claim 1, wherein: and in the second step, the rolling pass of cold rolling is not less than 5 times, and the total deformation is 40-60%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210697013.3A CN115074582B (en) | 2022-06-20 | 2022-06-20 | Preparation method of hypoeutectic Al-Ce alloy with bimodal grain structure |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210697013.3A CN115074582B (en) | 2022-06-20 | 2022-06-20 | Preparation method of hypoeutectic Al-Ce alloy with bimodal grain structure |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115074582A CN115074582A (en) | 2022-09-20 |
| CN115074582B true CN115074582B (en) | 2023-07-18 |
Family
ID=83253409
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210697013.3A Active CN115074582B (en) | 2022-06-20 | 2022-06-20 | Preparation method of hypoeutectic Al-Ce alloy with bimodal grain structure |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115074582B (en) |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102641890B (en) * | 2012-04-28 | 2014-04-02 | 中南大学 | Preparation method of powder metallurgy superfine crystal titanium aluminum base alloy panel |
| CN105821253B (en) * | 2016-03-25 | 2017-06-23 | 中南大学 | The lightweight high conductivity and heat heat resistance aluminum conductor and its preparation technology of a kind of plus iron |
| CN109439976B (en) * | 2019-01-09 | 2019-12-24 | 广东省材料与加工研究所 | Composite modification method for casting aluminum-silicon alloy |
| CN114369776B (en) * | 2022-01-14 | 2022-08-30 | 合肥工业大学 | Method for improving strength of (Ce + Yb) composite modified hypoeutectic Al-Si-Mg-Cu-Cr alloy |
-
2022
- 2022-06-20 CN CN202210697013.3A patent/CN115074582B/en active Active
Non-Patent Citations (3)
| Title |
|---|
| "Microstructure diversity dominated by the interplay between primary intermetallics and eutectics for Al-Ce heat-resistant alloys";Yueling Guo et al.;《Journal of Alloys and Compounds》;第第899卷卷;162914 * |
| "Microstructure selection map for rapidly solidified Al-rich Al–Ce alloys";Zhonghua Zhang et al.;《Journal of Crystal Growth》;第第260卷卷(第第3-4期期);第557-565页 * |
| "Thermal stability of aluminum–cerium binary alloys containing the Al–Al11Ce3 eutectic";Frank Czerwinski;《Materials Science and Engineering: A》;第第809卷卷;140973 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115074582A (en) | 2022-09-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108300918B (en) | Calcium-containing rare earth magnesium alloy sheet with high room temperature forming performance and preparation method thereof | |
| CN103339276B (en) | Aluminum alloy wire for use in bolts, bolt, and manufacturing method of these. | |
| CN109182857B (en) | High-strength and high-toughness deformed magnesium alloy and preparation method thereof | |
| CN104451296A (en) | Method for manufacturing 2-series aluminum alloy | |
| CN103014510A (en) | High-strength cold-extrusion die steel and processing technology thereof | |
| CN115125423B (en) | High-strength Gao Chengxing magnesium-lithium alloy and preparation method and application thereof | |
| CN105838928A (en) | High strength aluminum alloy sheet | |
| US11351585B2 (en) | Preparation method for a high-strength extruded profile of Mg—Zn—Sn—Mn alloy | |
| CN111074121B (en) | Aluminum alloy and preparation method thereof | |
| CN113462937A (en) | Impact-resistant high-toughness aluminum alloy material and preparation method thereof | |
| CN110468317B (en) | Magnesium alloy with excellent room temperature plasticity and preparation method thereof | |
| CN109234592B (en) | Low-temperature rolled high-strength-toughness wrought magnesium alloy and preparation method thereof | |
| JP7318274B2 (en) | Al-Mg-Si-based aluminum alloy cold-rolled sheet and its manufacturing method, and Al-Mg-Si-based aluminum alloy cold-rolled sheet for forming and its manufacturing method | |
| CN102965554A (en) | Hard aluminum alloy cast ingot | |
| CN112210703B (en) | High-recrystallization-resistance and high-toughness aluminum lithium alloy and preparation method thereof | |
| CN104532091A (en) | 2-series aluminum alloy | |
| US11186899B2 (en) | Magnesium-zinc-manganese-tin-yttrium alloy and method for making the same | |
| CN114277295B (en) | High-strength magnesium-lithium alloy with weak basal plane texture and preparation method thereof | |
| CN109371301B (en) | Room-temperature high-plasticity magnesium alloy and preparation method thereof | |
| CN115074582B (en) | Preparation method of hypoeutectic Al-Ce alloy with bimodal grain structure | |
| CN108193101B (en) | Er, Zr and Si microalloyed Al-Mg-Cu alloy and thermomechanical treatment process thereof | |
| CN113897567B (en) | Homogenization thermomechanical treatment method for rapidly refining and homogenizing cast aluminum-lithium alloy | |
| CN113005347B (en) | High-plasticity Mg-Al-Ca magnesium alloy and preparation method thereof | |
| CN111254324A (en) | Al-Mg-Si alloy plate and manufacturing method thereof | |
| KR101252784B1 (en) | Magnesium alloy sheet having high strength and high formability and method for manufacturing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |