CN114525443B - Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof - Google Patents
Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof Download PDFInfo
- Publication number
- CN114525443B CN114525443B CN202210157204.0A CN202210157204A CN114525443B CN 114525443 B CN114525443 B CN 114525443B CN 202210157204 A CN202210157204 A CN 202210157204A CN 114525443 B CN114525443 B CN 114525443B
- Authority
- CN
- China
- Prior art keywords
- medium manganese
- manganese steel
- rolling
- steel
- rolled plate
- 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
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides a Cu-Al alloyed high-strength medium manganese steel hot rolled plate and a preparation method thereof, and relates to the technical field of medium manganese steel. The medium manganese steel hot rolled plate takes steel ingots as raw materials, and is prepared into a finished product Cu-Al alloyed medium manganese steel hot rolled plate through the steps of smelting, forging, hot rolling, post-rolling heat treatment and the like. According to the invention, by introducing Cu and Al elements into the alloy, the medium manganese steel has proper austenite content and good stability, so that the medium manganese steel can generate a TRIP effect in a sufficient and coordinated manner in a deformation process, and the product has excellent mechanical properties. The tensile strength of the Cu-Al alloyed medium manganese steel hot rolled plate can reach 866-1061MPa, the elongation is 35.2% -47.1%, and the product of strength and elongation is 35-40 GPa%.
Description
Technical Field
The invention relates to the technical field of medium manganese steel, in particular to a Cu-Al alloyed high-strength medium manganese steel hot rolled plate and a preparation method thereof.
Background
The medium manganese steel (the manganese mass fraction is 3-12%) is used as the third-generation advanced automobile high-strength steel, and has very wide application prospect due to the characteristics of excellent product of strength and elongation (20-70 GPa%), light weight, low cost and the like. The austenite content in the medium manganese steel is a main factor for ensuring the occurrence of a transformation induced plasticity (TRIP) effect, and the local strength is improved by deformation induced martensite phase transformation, so that the deformation is transferred to a region without martensite phase transformation, and necking is delayed, thereby obtaining excellent mechanical properties. In addition, the stability of austenite is very important for improving the mechanical properties of medium manganese steel, if the stability of austenite is too poor, a large amount of austenite generates martensite phase transformation at the initial stage of deformation, and the residual austenite cannot ensure the occurrence of effective TRIP effect to maintain the whole plastic deformation stage, thereby causing premature fracture. Therefore, the preparation of the medium manganese steel with both austenite content and stability is the mainstream development trend of the application of the medium manganese steel industry at present.
In recent years, scholars at home and abroad generally adjust the austenite content and stability by adding microalloy elements into medium manganese steel. For example, the addition of aluminum in the medium manganese steel can greatly reduce the reduction of the density of the steel; the range of an austenite-ferrite two-phase region can be remarkably enlarged, the industrial annealing time is shortened, and the cost is saved; meanwhile, aluminum is used as a ferrite forming element, so that excessive austenite formation in the annealing process is inhibited to a certain extent, and the enrichment of manganese content in austenite is promoted, so that the stability of austenite is improved; in addition, aluminum is insoluble in cementite, so that the precipitation of the cementite is inhibited, carbon is promoted to be enriched in austenite, and the stability of the austenite is improved; finally, aluminum can promote the occurrence of recrystallization during annealing to refine the grains. Copper itself is used as an austenite stabilizing element, and the content and stability of austenite can be obviously improved by the copper dissolved in austenite. The precipitated copper-rich nanoparticles can be used as a second phase to further play a role in precipitation strengthening, and are different from the traditional precipitation strengthening particles such as niobium carbide, vanadium carbide and the like in medium manganese steel, and C atoms dissolved in austenite are consumed, so that the content and stability of the austenite are weakened. However, in the prior art, no report is made about the preparation of high-strength medium manganese steel by adjusting the austenite content and stability in medium manganese steel through Cu-Al composite addition. In summary, on the basis of research and development of common hot-rolled medium manganese steel, on the premise of not remarkably improving the production cost, the novel medium manganese steel with both austenite content and stability is prepared by compositely adding Cu-Al microalloy elements and adjusting the corresponding heat treatment process, so that the method has great practical significance.
Disclosure of Invention
In order to solve the problems, on the basis of the design concept of medium manganese steel, the invention develops a high-strength and high-toughness automobile steel plate with excellent performance by compositely adding Cu-Al alloy elements to influence the austenite reverse transformation of the medium manganese steel, reasonably controlling components and optimizing a heat treatment process, and meets the use indexes of different automobile parts, and the preparation method of the Cu-Al alloyed medium manganese steel hot rolled plate comprises the following steps:
(1) Smelting: carrying out vacuum melting and casting on the steel ingot to obtain a cannonball-shaped steel ingot;
(2) Forging: heating the steel ingot obtained in the step (1) to 1200-1250 ℃, preserving heat for 2-3h, forging the steel ingot into a plate blank with the cross section of 100mm multiplied by 30mm, and then air-cooling the plate blank to room temperature;
(3) Hot rolling: heating the plate blank obtained in the step (2) to 1200-1250 ℃, preserving heat for 2-3h, rolling at the initial rolling temperature of 1150-1250 ℃ and the final rolling temperature of more than or equal to 900 ℃, rolling to obtain a thin plate with the thickness of 4 +/-0.5 mm, and then air cooling to room temperature;
(4) And (3) post-rolling heat treatment: and (4) carrying out austenitizing quenching on the thin plate obtained in the step (3) at 900 ℃, preserving heat for 0-30min, then carrying out water cooling to room temperature, carrying out critical annealing on the hot-rolled plate after water quenching, and then carrying out water cooling to room temperature to obtain the finished product of the Cu-Al alloyed medium manganese steel hot-rolled plate.
Further, in the step (1), the mass percentages of the elements in the steel ingot are as follows: c:0.15-0.18%, mn:10.0-10.32%, al:1.9-2.1%, cu:1.8-2.2 percent, and the balance of Fe and inevitable impurities.
Further, in the step (2), the heating temperature of the steel ingot is 1200 ℃, and the heat preservation time is 2 hours.
Further, in the step (3), the heating temperature of the slab is 1200 ℃, and the heat preservation time is 2 hours.
Further, the slab rolling temperature in the step (3) is 1200 ℃, the finish rolling temperature is 1000 ℃, and further, the rolling in the step (3) is 5-7 passes.
Further, the annealing temperature in the step (4) is 600 ℃, and the heat preservation time is 30min.
The invention also provides the Cu-Al alloyed medium manganese steel hot rolled plate prepared by the method, and the Cu-Al alloyed medium manganese steel hot rolled plate can be applied to the automobile industry.
Compared with the prior art, the invention has the beneficial technical effects that:
the invention combines the microalloy element Cu-Al and the heat treatment process, so that the medium manganese steel has proper austenite content and good stability, and the medium manganese steel can generate the TRIP effect in a sufficient and coordinated manner in the deformation process, and has excellent mechanical properties. The tensile strength of the Cu-Al alloyed medium manganese steel hot rolled plate can reach 866-1061MPa, the elongation is 35.2% -47.1%, and the product of strength and elongation is 35-40GPa%, so that the mechanical property of the medium manganese steel is effectively improved on the premise of not remarkably improving the production cost, and the industrial production and application of the medium manganese steel are promoted.
Drawings
The invention is further illustrated in the following description with reference to the drawings.
FIG. 1 (a) is an engineering stress-strain curve for example 1 and comparative examples 1-1/2;
FIG. 1 (b) is an engineering stress strain curve of example 2 and comparative example 2-1/2;
FIG. 2 (a) is a graph showing austenite contents before and after stretching in example 1 and comparative examples 1-1/2;
FIG. 2 (b) is a graph showing austenite contents before and after stretching in example 2 and comparative example 2-1/2.
Detailed Description
The invention provides a high-toughness automobile steel plate with excellent performance, which meets the use indexes of different automobile parts. The preparation method of the Cu-Al alloyed medium manganese steel hot rolled plate comprises the following steps:
(1) Smelting: carrying out vacuum melting and casting on the steel ingot to obtain a shell-shaped steel ingot;
(2) Forging: heating the steel ingot obtained in the step (1) to 1200-1250 ℃, preserving heat for 2-3h, forging the steel ingot into a plate blank with the cross section of 100mm multiplied by 30mm, and then air-cooling the plate blank to room temperature;
(3) Hot rolling: heating the plate blank obtained in the step (2) to 1200-1250 ℃, preserving heat for 2-3h, rolling at the initial rolling temperature of 1150-1250 ℃ and the final rolling temperature of more than or equal to 900 ℃, rolling to obtain a thin plate with the thickness of 4 +/-0.5 mm, and then air cooling to room temperature;
(4) Heat treatment after rolling: and (4) performing austenitizing quenching on the thin plate obtained in the step (3) at 900 ℃, preserving heat for 0-30min, then performing water cooling to room temperature, performing critical annealing on the hot-rolled plate after water quenching, and then performing water cooling to room temperature to obtain the finished product of the Cu-Al alloyed medium manganese steel hot-rolled plate.
Further, in the step (1), the mass percentages of the elements in the steel ingot are as follows: c:0.15-0.18%, mn:10.0-10.32%, al:1.9-2.1%, cu:1.8-2.2 percent, and the balance of Fe and inevitable impurities.
In one embodiment, the heating temperature of the steel ingot in the step (2) is 1200 ℃, and the holding time is 2 hours.
In one embodiment, the heating temperature of the slab in the step (3) is 1200 ℃, and the holding time is 2 hours.
In one embodiment, the slab rolling temperature in the step (3) is 1200 ℃ and the final rolling temperature is 1000 DEG C
In one embodiment, the rolling in the step (3) is 5-7 passes of rolling.
In one embodiment, the annealing temperature in the step (4) is 600 ℃ and the holding time is 30min.
The Cu-Al alloyed medium manganese steel hot rolled plate can be applied to the automobile industry.
The technical solution provided by the present invention is further illustrated by the following examples.
Example 1
The steel ingot comprises the following chemical components in percentage by mass: c:0.15%, mn:10.32%, al:2.01%, cu:1.98 percent, and the balance of Fe and inevitable impurities;
smelting the steel ingot by using a vacuum induction furnace, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and forging the steel ingot into a steel billet; heating the steel billet to 1200 ℃, preserving heat for 2h, hot rolling into a sheet with the thickness of 4mm by 6 passes, carrying out final rolling at the temperature of 900 ℃, and then air cooling to room temperature; heating the hot-rolled steel plate to 600 ℃ in a heating furnace, preserving heat for 30min, and then water-quenching to room temperature to obtain a Cu-Al alloyed medium manganese steel hot-rolled plate;
processing the heat-treated steel plate into a tensile sample according to GB/T228-2002 'method for testing the tensile property of the metal material at room temperature', wherein the stress-strain curve is shown in figure 1 a; the austenite content before and after stretching is shown in figure 2 a.
Comparative examples 1 to 1
The steel ingot comprises the following chemical components in percentage by mass: c:0.18%, mn:10.25%, al:2.11%, the balance being Fe and unavoidable impurities;
smelting the steel ingot by using a vacuum induction furnace, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and forging the steel ingot into a steel billet; heating the billet to 1200 ℃, preserving heat for 2h, carrying out 6-pass hot rolling to obtain a sheet with the thickness of 4mm, carrying out final rolling at the temperature of 900 ℃, and then carrying out air cooling to room temperature; heating the hot-rolled steel plate to 600 ℃ in a heating furnace, preserving heat for 30min, and then performing water quenching to room temperature to obtain a medium manganese steel hot-rolled plate;
processing the heat-treated steel plate into a tensile sample according to GB/T228-2002 'method for testing the tensile property of the metal material at room temperature', wherein the stress-strain curve is shown in figure 1 a; the austenite content before and after stretching is shown in figure 2 a.
Comparative examples 1 to 2
The steel ingot comprises the following chemical components in percentage by mass: c:0.15%, mn:10.09%, cu:1.99%, the balance being Fe and inevitable impurities;
and smelting the steel ingot by adopting a vacuum induction furnace, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and forging the steel ingot into a steel billet. Heating the steel billet to 1200 ℃, preserving heat for 2h, hot rolling into a sheet with the thickness of 4mm by 6 passes, carrying out final rolling at the temperature of 900 ℃, and then air cooling to room temperature; heating the hot-rolled steel plate in a heating furnace to 600 ℃, preserving heat for 30min, and then quenching the steel plate to room temperature to obtain a medium manganese steel hot-rolled plate;
processing the heat-treated steel plate into a tensile sample according to GB/T228-2002 'method for testing the tensile property of the metal material at room temperature', wherein the stress-strain curve is shown in figure 1 a; the austenite content before and after stretching is shown in figure 2 a.
Comparing the engineering stress-strain curve (fig. 1 a) and the mechanical properties (table 1) under the annealing process, it is found that, compared with comparative examples 1-1 (single addition of Al) and comparative examples 1-2 (single addition of Cu), example 1 (composite addition of Cu-Al) has the optimal strength-plasticity combination, and the product of strength and elongation reaches 37.4GPa%. Wherein, the tensile strength reaches 1061MPa, the elongation is 35.2%, and it can be seen from fig. 2a that the austenite content before stretching in example 1 is 68.3%, the austenite content after breaking is 34.3%, the austenite conversion rate is 49.7%, and the austenite content and stability are both satisfied, thereby meeting the use requirement of modern automobile steel and the development requirement of future staging.
Example 2
The steel ingot comprises the following chemical components in percentage by mass: c:0.15%, mn:10.32%, al:2.01%, cu:1.98 percent, and the balance of Fe and inevitable impurities;
and smelting the steel ingot by adopting a vacuum induction furnace, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and forging the steel ingot into a steel billet. Heating the steel billet to 1200 ℃, preserving heat for 2h, hot rolling into a sheet with the thickness of 4mm by 6 passes, carrying out final rolling at the temperature of 900 ℃, and then air cooling to room temperature; reheating the hot-rolled steel plate to 900 ℃ in a heating furnace, carrying out austenitizing water quenching and heat preservation for 30min, and then carrying out water quenching to room temperature; and heating the austenitized hot-rolled plate to 600 ℃ after water quenching, preserving the heat for 30min, and then performing water quenching to room temperature to obtain a medium manganese steel hot-rolled plate and obtain the Cu-Al alloyed medium manganese steel hot-rolled plate.
Processing the heat-treated steel plate into a tensile sample according to GB/T228-2002 'method for testing tensile strength of metal materials at room temperature', and carrying out performance test, wherein the stress-strain curve is shown in figure 1 b; the austenite content before and after stretching is shown in figure 2 b.
Comparative example 2-1
The steel ingot comprises the following chemical components in percentage by mass: c:0.18%, mn:10.25%, al:2.11%, the balance being Fe and unavoidable impurities;
and smelting the steel ingot by adopting a vacuum induction furnace, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and forging the steel ingot into a steel billet. Heating the steel billet to 1200 ℃, preserving heat for 2h, hot rolling into a sheet with the thickness of 4mm by 6 passes, carrying out final rolling at the temperature of 900 ℃, and then air cooling to room temperature; and reheating the hot-rolled steel plate to 900 ℃ in a heating furnace, carrying out austenitizing water quenching and heat preservation for 30min, and then carrying out water quenching to room temperature. Heating the austenitized hot rolled plate to 600 ℃ after water quenching, preserving the heat for 30min, and then performing water quenching to room temperature to obtain a medium manganese steel hot rolled plate;
processing the heat-treated steel plate into a tensile sample according to GB/T228-2002 'method for testing the tensile property of the metal material at room temperature', wherein the stress-strain curve is shown in figure 1 b; the austenite content before and after stretching is shown in fig. 2 b.
Comparative examples 2 to 2
The steel ingot comprises the following chemical components in percentage by mass: c:0.15%, mn:10.09%, cu:1.99%, and the balance of Fe and inevitable impurities;
smelting the steel ingot by using a vacuum induction furnace, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, and forging the steel ingot into a steel billet; heating the steel billet to 1200 ℃, preserving heat for 2h, hot rolling into a sheet with the thickness of 4mm by 6 passes, carrying out final rolling at the temperature of 900 ℃, and then air cooling to room temperature; and reheating the hot-rolled steel plate to 900 ℃ in a heating furnace, carrying out austenitizing water quenching and heat preservation for 30min, and then carrying out water quenching to room temperature. And heating the austenitized hot-rolled plate to 600 ℃ after water quenching, preserving the heat for 30min, and then performing water quenching to room temperature to obtain the medium manganese steel hot-rolled plate.
Processing the heat-treated steel plate into a tensile sample according to GB/T228-2002 'method for testing the tensile property of the metal material at room temperature', wherein the stress-strain curve is shown in figure 1 b; the austenite content before and after stretching is shown in fig. 2 b.
Comparison of the engineering stress-strain curve (fig. 1 b) and the mechanical properties (table 1) under the quenching-annealing process revealed that example 2 (composite addition of Cu-Al) had an optimal strength-plasticity combination with a product of strength and plasticity of 40.8GPa, relative to comparative examples 2-1 (single addition of Al) and 2-2 (single addition of Cu). Wherein, the tensile strength reaches 866MPa, the elongation is 47.1%, and it can be seen from fig. 2b that the austenite content before stretching is 52.5%, the austenite content after breaking is 28.4%, the austenite conversion rate is 45.9% in example 2, and both the austenite content and the stability meet the use requirement of modern automobile steel and the development requirement of the future staging.
TABLE 1 results of mechanical Properties measurements
The principles and embodiments of the present invention have been described herein using specific examples, which are provided only to help understand the method and the core concept of the present invention; meanwhile, for a person skilled in the art, according to the idea of the present invention, the specific embodiments and the application range may be changed. In view of the above, the present disclosure should not be construed as limiting the invention.
Claims (6)
1. A preparation method of a Cu-Al alloyed medium manganese steel hot rolled plate is characterized by comprising the following steps:
(1) Smelting: carrying out vacuum melting and casting on the steel ingot to obtain a shell-shaped steel ingot;
(2) Forging: heating the steel ingot obtained in the step (1) to 1200-1250 ℃, preserving heat for 2-3h, forging the steel ingot into a plate blank with the cross section of 100mm multiplied by 30mm, and then air-cooling the plate blank to room temperature;
(3) Hot rolling: heating the plate blank obtained in the step (2) to 1200-1250 ℃, preserving heat for 2-3h, rolling at the initial rolling temperature of 1150-1250 ℃ and the final rolling temperature of more than or equal to 900 ℃, rolling to obtain a thin plate with the thickness of 4 +/-0.5 mm, and then air cooling to room temperature;
(4) And (3) post-rolling heat treatment: carrying out austenitizing quenching on the thin plate obtained in the step (3) at 900 ℃, preserving heat for 0-30min, then cooling with water to room temperature, carrying out critical annealing on the hot-rolled plate after water quenching, and then cooling with water to room temperature to obtain a finished product of the Cu-Al alloyed medium manganese steel hot-rolled plate;
in the step (1), the mass percentages of the elements in the steel ingot are as follows: c:0.15-0.18%, mn:10.0-10.32%, al:1.9-2.1%, cu:1.8-2.2%, and the balance of Fe and inevitable impurities;
in the step (4), the annealing temperature is 600 ℃, and the heat preservation time is 30min.
2. The method for preparing the hot rolled plate of Cu-Al alloying medium manganese steel as claimed in claim 1, wherein the ingot in the step (2) is heated at 1200 ℃ for 2h.
3. The method for preparing the hot rolled plate of Cu-Al alloying medium manganese steel as claimed in claim 1, wherein the heating temperature of the plate blank in the step (3) is 1200 ℃ and the holding time is 2h.
4. The method for preparing the hot rolled plate of Cu-Al alloying medium manganese steel as claimed in claim 1, wherein the slab rolling temperature in the step (3) is 1200 ℃ and the finishing temperature is 1000 ℃.
5. The method of preparing a hot rolled plate of Cu-Al alloyed medium manganese steel according to claim 1, characterized in that the rolling in step (3) is a 5-7 pass rolling.
6. A hot-rolled Cu-Al alloyed medium manganese steel sheet produced by the method according to any one of claims 1 to 5.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210157204.0A CN114525443B (en) | 2022-02-21 | 2022-02-21 | Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210157204.0A CN114525443B (en) | 2022-02-21 | 2022-02-21 | Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114525443A CN114525443A (en) | 2022-05-24 |
| CN114525443B true CN114525443B (en) | 2022-11-29 |
Family
ID=81625086
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210157204.0A Active CN114525443B (en) | 2022-02-21 | 2022-02-21 | Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114525443B (en) |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106498278B (en) * | 2016-09-29 | 2018-04-13 | 北京科技大学 | A kind of cut deal of high-strength high-elongation ratio low-density and preparation method thereof |
| CN106756567B (en) * | 2017-02-08 | 2018-06-15 | 北京科技大学 | A kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% |
| CN112195402B (en) * | 2020-09-28 | 2022-08-05 | 首钢集团有限公司 | Precipitation-strengthened high-strength and high-toughness medium manganese steel plate and preparation method thereof |
| CN112410681B (en) * | 2020-11-26 | 2022-07-26 | 燕山大学 | High-strength-ductility medium manganese steel and preparation method thereof |
-
2022
- 2022-02-21 CN CN202210157204.0A patent/CN114525443B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN114525443A (en) | 2022-05-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110066964B (en) | Ultrahigh-strength medium manganese steel and warm rolling preparation method thereof | |
| CN108486492B (en) | 1200 MPa-grade high-strength high-plasticity low-density steel plate and manufacturing method thereof | |
| CN113388779B (en) | 1.5 GPa-grade ultrahigh-strength high-plasticity high-hole-expansion DH steel plate and preparation method thereof | |
| CN102400036B (en) | Twin induced plastic steel with high elongation percentage and high hole expansion rate and manufacture method thereof | |
| CN113403549A (en) | 1.2 GPa-grade fatigue-resistant high-formability ultrahigh-strength automobile steel and preparation method thereof | |
| CN114457290B (en) | 1200 MPa-level precipitation strengthening vanadium-containing high-manganese austenitic steel and preparation method thereof | |
| JP2023505172A (en) | Hot-rolled H-shaped steel based on beam blank rolling forming and its preparation method | |
| CN113249641A (en) | 100-120 mm Q460D super-thick high-strength steel and preparation method thereof | |
| CN114134388B (en) | Thin-specification ultrahigh-strength steel plate with 1300 MPa-level tensile strength and manufacturing method thereof | |
| CN113846269B (en) | Cold-rolled high-weather-resistance steel plate with high strength and plasticity and preparation method thereof | |
| CN114525443B (en) | Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof | |
| JPH029647B2 (en) | ||
| CN115558851A (en) | Hot rolled steel plate for 370 MPa-level engineering structure and manufacturing method thereof | |
| CN114717478A (en) | Light high-strength steel and production method thereof | |
| KR20150039008A (en) | Precipitation hardening steel sheet having excellent yield strength and yield ratio and method for manufacturing the same | |
| CN116018421A (en) | High strength austenitic stainless steel having excellent productivity and cost reduction effect and method for producing the same | |
| CN114807551A (en) | Preparation method of austenitic stainless steel cold-deformed plate | |
| CN114182182A (en) | Hot-rolled pickled steel plate for refrigerator compressor shell and manufacturing method thereof | |
| CN111334713A (en) | Q390D steel plate and production method thereof | |
| CN111455268A (en) | High-strength and high-toughness steel plate for coal mine machinery and preparation method thereof | |
| CN109898018A (en) | A kind of cold rolling 1300MPa grades of martensite steel and its production method | |
| CN114164373B (en) | Nb microalloying duplex stainless steel and preparation method thereof | |
| CN112795837B (en) | 1300Mpa high-toughness cold-formed steel plate and production method thereof | |
| CN114934228B (en) | Hot-formed steel plate and production method thereof | |
| CN115612928B (en) | High-strength steel based on CSP process and manufacturing 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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |