CN111961990A - Austenitic stainless steel plate with strength-elongation product more than 50Gpa and manufacturing method thereof - Google Patents
Austenitic stainless steel plate with strength-elongation product more than 50Gpa and manufacturing method thereof Download PDFInfo
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- CN111961990A CN111961990A CN202010868943.1A CN202010868943A CN111961990A CN 111961990 A CN111961990 A CN 111961990A CN 202010868943 A CN202010868943 A CN 202010868943A CN 111961990 A CN111961990 A CN 111961990A
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- 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
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- 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
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- 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
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- 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
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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
Abstract
The invention discloses a manufacturing method of a low-cost high-toughness chromium-manganese austenitic stainless steel plate with a strength-plastic product larger than 50 GPa%, and belongs to the technical field of metal processing. The chemical components of the alloy are 0.12 percent of C, 1.0 percent of Si, 6.0 to 10.0 percent of Mn, 1.5 to 3.0 percent of Ni, 16.0 to 18.0 percent of Cr, P: 0.06, S: 0.03, Cu: 1.2-2.0%, N is less than or equal to 0.30% and the balance is Fe. The preparation method comprises the following steps: raw material preparation, smelting, casting, forging, hot rolling, acid washing, cold rolling and solution treatment. The high-strength and high-toughness 200-series austenitic stainless steel has the tensile strength of 1000-1100MPa, the elongation after fracture of 46 +/-2 percent and the product of strength and elongation of 50 GPa. Through reasonable component proportion and heat treatment process, the low-cost high-strength-toughness chromium-manganese austenitic stainless steel plate with the product of strength and elongation of more than 50Gpa is obtained, so that the application scene that the demand for the product of strength and elongation is high but the cost needs to be reduced is met.
Description
Technical Field
The invention relates to the technical field of metal processing, in particular to a method for manufacturing a high-strength and high-toughness chromium-manganese austenitic stainless steel plate with a product of strength and elongation of more than 50 GPa.
Background
Conventionally, so-called austenitic-ferritic stainless steel, also called SUS329J1, which is superior in corrosion resistance to austenitic stainless steel SUS304, SUS316, has been used in marine structural steel materials such as drilling platforms, seawater suction pumps, and the like.
This duplex stainless steel has good corrosion resistance but poor mechanical properties, and generally has a tensile strength of about 588MPa and an elongation of about 18%. With the increasing demand for high-strength and high-toughness materials in production, the materials cannot meet the strength requirement of stressed structural members at present.
In practical production, a dispersion strengthening method is often used, which greatly strengthens a material by containing fine dispersed particles of an oxide or the like. When the material is attempted to be dispersion-strengthened by a mechanical alloying method, the strength is significantly increased, the creep resistance is increased, but the ductility is decreased, and the problem of the deterioration of the workability at normal temperature arises. Therefore, in order to prevent the loss of ductility, it is necessary to prevent intergranular particles as much as possible in the production process so as to increase the elongation.
Based on the problems, a new process capable of simultaneously improving the strength and the elongation of the material is developed, and the problems are well solved.
Disclosure of Invention
The invention aims to provide a low-cost high-strength high-toughness chromium-manganese austenitic stainless steel plate and a preparation method thereof.
Firstly, adding raw materials according to design components for smelting, casting and forging, and then carrying out hot rolling, hot rolling pickling annealing, cold rolling and solution treatment to obtain the austenitic stainless steel with low cost and high strength and toughness. Since the smelting, casting and forging of steel materials are the common techniques in all steel production and manufacturing processes, the invention is only explained for the components of the materials and the smelting, casting and forging processes, and the explanation and protection are focused on the following processes.
An austenitic stainless steel with a strength-elongation product of more than 50Gpa, which is characterized in that the chemical components of the austenitic stainless steel are respectively as follows by mass percent: 0.12 percent of C, 1.0 percent of Si, 6.0 to 10.0 percent of Mn, 1.5 to 3.0 percent of Ni, 16.0 to 18.0 percent of Cr, P: 0.06, S: 0.03, Cu: 1.2-2.0%, N is less than or equal to 0.30% and the balance is Fe.
The preparation method of the austenitic stainless steel plate with the strength-product of greater than 50GPa percent is characterized by comprising the following specific steps:
the method comprises the following steps: adding raw materials according to the design components for smelting, casting and forging;
step two: the austenitic stainless steel with low cost and high strength and toughness can be obtained through hot rolling, hot rolling pickling annealing, cold rolling and solution treatment.
Furthermore, in order to prevent the edge crack and the defect of the steel grade, the heating temperature needs to be controlled below 1250 ℃ in the hot rolling process, and the tapping temperature is controlled at 1200 +/-10 ℃.
Further, the temperature during the hot rolling pickling annealing process should be controlled at 1100 ℃ +/-10 ℃.
Furthermore, according to different product widths, the initial rolling thickness needs to be guaranteed to be larger than or equal to 3mm, and the thickness after hot rolling needs to be controlled to be between 2 and 5 mm.
Furthermore, the total reduction rate of the cold rolling process should be controlled to be more than or equal to 80 percent as much as possible, and the single-pass reduction rate should be controlled to be 60 to 80 percent
Further, in the process of solution treatment, the time t for rapidly heating to 900-1100 ℃ is less than or equal to 1min
Further, in the solution treatment process, in order to achieve a good solution treatment effect and prevent the precipitation of the solid solution, rapid cooling is required, and generally rapid cooling treatment is performed by water cooling, for example, rapid cooling treatment is performed by other methods, and the cooling rate of rapid cooling is required to be not lower than the cooling rate of water cooling.
Furthermore, the tensile strength of the steel plate treated by the process is 1000-1100MPa, the elongation after fracture is 46 +/-2 percent, and the product of strength and elongation is more than or equal to 50 GPa.
Because edge cracking and other phenomena are usually generated in the hot rolling process, in order to prevent the occurrence of the edge cracking, the defects and other conditions of the steel grade, the heating temperature needs to be controlled below 1250 ℃ in the hot rolling process, and the tapping temperature is controlled at 1200 +/-10 ℃. The temperature in the hot rolling acid cleaning annealing process should be controlled at 1100 +/-10 ℃.
And then, in the cold rolling process, according to different widths of required products, the initial rolling thickness is required to be more than or equal to 3mm, and the thickness after hot rolling is required to be controlled between 2 and 5 mm. The total reduction rate of the cold rolling process is controlled to be more than or equal to 80 percent as much as possible, and the single-pass reduction rate is controlled to be 60 to 80 percent.
Finally, in the process of solution treatment, the overall operation simulation is quick heating and quick cooling, namely the time t of quickly heating to 900-1100 ℃ is less than or equal to 1min, after the temperature is raised to a preset temperature interval, the temperature needs to be preserved for a certain time, the heat preservation time length is different according to the material size, and the calculation can be carried out according to the following empirical formula:
wherein:
the coefficient of (A) is generally 0.35-0.85 min/mm; k is the furnace load factor. When the workpiece is smaller (the thickness is less than or equal to 3mm), taking 1-2; when the workpiece is larger (the thickness is more than or equal to 3mm), taking 3-4; h is the effective thickness or diameter of the workpiece.
In order to achieve good solution treatment effect and prevent solid solution from separating out, rapid cooling is required, and generally rapid cooling treatment is carried out by water cooling, for example, rapid cooling treatment is carried out by other methods, and the cooling speed of rapid cooling is not lower than the cooling speed of water cooling.
The tensile strength of the steel plate treated by the process is more than or equal to 1000MPa, the elongation is more than or equal to 45 percent, and the product of strength and elongation is more than or equal to 50 GPa.
The solution treatment process in the invention needs special attention as the cooling process in the implementation process, because the faster cooling speed can not only ensure that the austenite grains are uniform and fine, but also prevent the austenite grains from precipitating carbide when passing through the 500-800 ℃ sensitization region to influence the performance. Especially, when the plate is thin, local cooling speed is difficult to achieve the strict consistency, and local stress is generated to deform the plate strip, so that the cooling speed must be ensured to be fast enough in the cooling process so as to prevent the plate strip from deforming due to overlarge difference of the cooling speed.
Compared with the prior art, the method has the advantages that through reasonable element content and heat treatment process design, compared with the traditional stainless steel such as 304 and the like, more low-cost elements Mn and N are added to replace noble metal elements Ni and Cr, so that the cost is greatly reduced, and moreover, through reasonable heat treatment process, the performance of the material is greatly improved. Solves the problem that the strength and the plasticity cannot be compatible in the prior process condition.
Drawings
FIG. 1 is a true stress-true strain curve of a tensile sample obtained after smelting, casting, forging, hot rolling, pickling and annealing, which is used in the specific example of obtaining the low-cost high-toughness chromium-manganese austenitic stainless steel plate.
FIG. 2 shows the true stress-true strain curve of a tensile sample obtained by the first embodiment of the present invention, which is obtained by performing the processes of smelting, casting, forging, hot rolling, pickling annealing, cold rolling, 900 ℃ +30s + water cooling.
FIG. 3 shows the true stress-true strain curve of a tensile sample obtained after the specific example II of the invention for obtaining the ultra-fine grained austenitic stainless steel with high strength and high toughness is subjected to smelting, casting, forging, hot rolling, pickling annealing, cold rolling, 1000 ℃ for +20s and water cooling. .
FIG. 4 shows the true stress-true strain curve of a tensile sample obtained after the third specific embodiment of the invention for obtaining the ultra-fine grained austenitic stainless steel with high strength and high toughness is subjected to smelting, casting, forging, hot rolling, pickling annealing, cold rolling, 1100 ℃ for +20s and water cooling.
Detailed Description
The invention relates to a chromium-manganese austenite stainless steel plate, which comprises the following chemical components in percentage by weight: 0.12 percent of C, 1.0 percent of Si, 6.0 to 10.0 percent of Mn, 1.5 to 3.0 percent of Ni, 16.0 to 18.0 percent of Cr, P: 0.06, S: 0.03, Cu: 1.2-2.0%, N is less than or equal to 0.30% and the balance is Fe.
Adding raw materials according to the design components, smelting, casting and forging, carrying out hot rolling, rolling to a plate with the thickness of 3mm about 7 times, limiting the temperature of a heating furnace to be below 1200 ℃ in order to prevent batch edge cracking and stripping defects of a steel plate caused by overburning, and carrying out hot rolling, annealing and pickling after discharging.
Selecting a stainless steel plate with the thickness of 3.0mm after acid washing, sampling and processing the stainless steel plate to prepare a tensile sample, and determining the tensile strength of the sample through a tensile test to be: 850MPa, yield strength: 364MPa, elongation of 33.6 percent and product of strength and elongation of 28.56 GPa. The true stress-true strain curve of the tensile specimen is shown in fig. 1.
Example one
According to the technological requirements of the invention, firstly, an austenitic stainless steel plate with the thickness of 3.0mm is cold-rolled to 0.3mm, the reduction rate is 90%, and then the treatment time of the steel plate with the thickness of 0.3mm is calculated according to an empirical formula as follows: and 6-30s, then placing the sample into an atmosphere of 900-1100 ℃ for heating, and then quickly placing the sample into water for cooling.
Further preferably, the adopted process is as follows: cold rolling +900 ℃ +30s + water cooling, the process can enable various mechanical properties of the material to be optimally matched, and the tensile strength of the material is 1074MPa, the yield strength is 530MPa, the elongation is 47.9 percent, and the product of strength and elongation is 51.4 GPa. The true stress-true strain curve of the tensile specimen is shown in fig. 2.
Example two
The same cold-rolled 0.3mm steel plate sample as in example one is used, and then the treatment time of the 0.3mm steel plate is calculated according to an empirical formula as follows: and 6-30s, then placing the sample into an atmosphere of 900-1100 ℃ for heating, and then quickly placing the sample into water for cooling.
Further preferably, the adopted process is as follows: cold rolling at +1000 ℃ +20s + water cooling, and determining by a tensile test that the tensile strength is 1090MPa, the yield strength is 626MPa, the elongation is 45.9 percent, and the product of strength and elongation is 50.0 GPa. The true stress-true strain curve of the tensile specimen is shown in fig. 3.
EXAMPLE III
The same cold-rolled 0.3mm steel plate sample as in example one is used, and then the treatment time of the 0.3mm steel plate is calculated according to an empirical formula as follows: and 6-30s, then placing the sample into an atmosphere of 900-1100 ℃ for heating, and then quickly placing the sample into water for cooling.
Further preferably, the adopted process is as follows: cold rolling at +1100 deg.C for +20s + water cooling, and determining by tensile test that the tensile strength is 1105MPa, the yield strength is 461MPa, the elongation is 46%, and the product of strength and elongation is 50.83 GPa%. The true stress-true strain curve of the tensile specimen is shown in fig. 4.
According to tensile test data and a graph, it is obvious that the strength and the elongation of the material can be effectively improved by carrying out the cold rolling and solution treatment process with large reduction on a hot rolled plate, namely the product of strength and elongation is correspondingly improved by more than 70%.
While the foregoing is directed to the preferred embodiment of the present invention, it will be understood by those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the invention as defined in the appended claims.
Claims (9)
1. An austenitic stainless steel with a strength-elongation product of more than 50Gpa, which is characterized in that the chemical components of the austenitic stainless steel are respectively as follows by mass percent: 0.12 percent of C, 1.0 percent of Si, 6.0 to 10.0 percent of Mn, 1.5 to 3.0 percent of Ni, 16.0 to 18.0 percent of Cr, P: 0.06, S: 0.03, Cu: 1.2-2.0%, N is less than or equal to 0.30% and the balance is Fe.
2. The method for preparing the austenitic stainless steel plate with the strength-product of greater than 50 GPa%, according to claim 1, is characterized by comprising the following steps:
the method comprises the following steps: adding raw materials according to the design components for smelting, casting and forging;
step two: the austenitic stainless steel with low cost and high strength and toughness can be obtained through hot rolling, hot rolling pickling annealing, cold rolling and solution treatment.
3. The method of claim 2, wherein the heating temperature is controlled to 1250 ℃ or less and the tapping temperature is controlled to 1200 ℃ ± 10 ℃ during the hot rolling process to prevent edge cracking and defects of the steel grade.
4. The method of manufacturing an austenitic stainless steel sheet according to claim 2, wherein the temperature during the hot pickling annealing is controlled to 1100 ℃ ± 10 ℃.
5. The method for manufacturing an austenitic stainless steel sheet according to claim 2, wherein the thickness at the beginning of rolling is not less than 3mm and the thickness after hot rolling is controlled to be 2-5mm according to the width of the product.
6. The method for manufacturing an austenitic stainless steel sheet according to claim 2, wherein the total reduction rate in the cold rolling process is controlled to be not less than 80% as much as possible, and the single-pass reduction rate is controlled to be 60% -80%.
7. The method for manufacturing an austenitic stainless steel sheet according to claim 2, wherein the time t for rapid heating to 900-1100 ℃ is 1min or less in the solution treatment process.
8. The method of manufacturing an austenitic stainless steel sheet according to claim 2, wherein, in the solution treatment, rapid cooling is performed to achieve good solution treatment effect and prevent precipitation of solid solution, and rapid cooling treatment is generally performed by water cooling, such as rapid cooling treatment by other means, and the rate of rapid cooling is not lower than the rate of water cooling.
9. The method for manufacturing the austenitic stainless steel plate according to claim 2, wherein the tensile strength of the steel plate after the above process treatment is 1000-1100Mpa, the elongation after fracture is 46% ± 2%, and the product of strength and elongation is greater than or equal to 50 GPa-.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5286310A (en) * | 1992-10-13 | 1994-02-15 | Allegheny Ludlum Corporation | Low nickel, copper containing chromium-nickel-manganese-copper-nitrogen austenitic stainless steel |
| CN1772942A (en) * | 2005-09-12 | 2006-05-17 | 钢铁研究总院 | Nickel-saving RE-containing austenitic stainless steel and its prepn |
| CN101724790A (en) * | 2008-10-23 | 2010-06-09 | 宝山钢铁股份有限公司 | Low-nickel austenitic stainless steel and manufacturing method thereof |
| CN102943219A (en) * | 2012-11-23 | 2013-02-27 | 四川金广技术开发有限公司 | Nickel-saving austenitic stainless steel containing manganese, nitrogen and boron and fabrication method |
| JP2014189800A (en) * | 2013-03-26 | 2014-10-06 | Nisshin Steel Co Ltd | LOW Ni AUSTENITIC STAINLESS STEEL SHEET AND MOLDED ARTICLE THEREOF |
| CN109112430A (en) * | 2017-06-26 | 2019-01-01 | 宝钢不锈钢有限公司 | A kind of low-cost high-strength low-nickel austenitic stainless steel and manufacturing method |
-
2020
- 2020-08-26 CN CN202010868943.1A patent/CN111961990A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5286310A (en) * | 1992-10-13 | 1994-02-15 | Allegheny Ludlum Corporation | Low nickel, copper containing chromium-nickel-manganese-copper-nitrogen austenitic stainless steel |
| CN1772942A (en) * | 2005-09-12 | 2006-05-17 | 钢铁研究总院 | Nickel-saving RE-containing austenitic stainless steel and its prepn |
| CN101724790A (en) * | 2008-10-23 | 2010-06-09 | 宝山钢铁股份有限公司 | Low-nickel austenitic stainless steel and manufacturing method thereof |
| CN102943219A (en) * | 2012-11-23 | 2013-02-27 | 四川金广技术开发有限公司 | Nickel-saving austenitic stainless steel containing manganese, nitrogen and boron and fabrication method |
| JP2014189800A (en) * | 2013-03-26 | 2014-10-06 | Nisshin Steel Co Ltd | LOW Ni AUSTENITIC STAINLESS STEEL SHEET AND MOLDED ARTICLE THEREOF |
| CN109112430A (en) * | 2017-06-26 | 2019-01-01 | 宝钢不锈钢有限公司 | A kind of low-cost high-strength low-nickel austenitic stainless steel and manufacturing method |
Non-Patent Citations (2)
| Title |
|---|
| 姚一帆 等: "《热处理问答》", 31 August 1981, 山西人民出版社 * |
| 高宗仁: "《简明不锈钢使用手册》", 31 January 2003, 山西科学技术出版社 * |
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