CN112899585A - Plasticized and reinforced economical duplex stainless steel and preparation method thereof - Google Patents
Plasticized and reinforced economical duplex stainless steel and preparation method thereof Download PDFInfo
- Publication number
- CN112899585A CN112899585A CN202110064791.4A CN202110064791A CN112899585A CN 112899585 A CN112899585 A CN 112899585A CN 202110064791 A CN202110064791 A CN 202110064791A CN 112899585 A CN112899585 A CN 112899585A
- Authority
- CN
- China
- Prior art keywords
- stainless steel
- duplex stainless
- economical
- reinforced
- treatment
- 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.)
- Granted
Links
Images
Classifications
-
- 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
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
-
- 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
-
- 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
-
- 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
- C21D2211/005—Ferrite
Abstract
The invention provides plasticized and reinforced economical duplex stainless steel and a preparation method thereof, belonging to the field of steel material manufacturing. The preparation method comprises the following steps: rapidly heating the saving type duplex stainless steel to 1300-1400 ℃, preserving heat, and slowly cooling to room temperature; then carrying out asynchronous rolling treatment on the economical duplex stainless steel at room temperature; and heating the saving type duplex stainless steel subjected to asynchronous rolling treatment to 1050-1150 ℃ under atmospheric conditions, preserving heat for 2-5min, and cooling to room temperature. The method adopts the pre-solid solution heat treatment, the asynchronous cold deformation and the solid solution treatment, improves the strip-shaped structure of the duplex stainless steel, can improve the tensile strength of the economical duplex stainless steel to be close to 1000Mpa, increases the elongation rate by nearly one time and reaches 60 percent, and improves the product of strength and elongation by more than one time and reaches 60 Gpa.
Description
Technical Field
The invention relates to the field of steel material manufacturing, in particular to plasticized and reinforced economical duplex stainless steel and a preparation method thereof.
Background
Duplex stainless steel is defined as stainless steel having a two-phase structure of ferrite and austenite, whereas the saving type duplex stainless steel allows the duplex stainless steel to exhibit metastable austenite constituent phases while reducing the Ni content of rare and expensive metals. And the metastable austenite can realize the TRIP effect through martensite phase transformation in the deformation process, improve the plastic deformation capacity of the material, obtain the combination of high plasticity and high strength, and has wide application in the aspects of marine vehicles, heat exchangers, chemical storage tanks and the like.
With the demand for weight reduction of steel materials in many modern applications, including the automotive industry, the demand for steel materials with combination of ultra-high strength and plasticity is more and more urgent, and the improvement of strength not only enables the materials to meet higher bearing requirements, but also enables the high plasticity to improve the forming capability of the materials and reduce the weight of the materials.
Grain refinement is the most direct and effective means for improving the strength of the material, the stability of metastable austenite of the saving duplex stainless steel is improved to a certain extent while grain refinement of the saving duplex stainless steel is carried out, and the plasticizing effect caused by the Trip effect is inhibited, so that the strength of the saving duplex stainless steel is improved, but the plasticity of the saving duplex stainless steel is inhibited due to the Trip effect, and the plasticizing effect of the saving duplex stainless steel is weakened to a certain extent. Therefore, how to utilize the fine crystal strengthening effect to the maximum extent and ensure that the material has good plasticizing effect has important significance for saving the forming performance of the stainless steel.
Disclosure of Invention
The invention aims to provide plasticized and reinforced economical duplex stainless steel and a preparation method thereof, and the preparation method can regulate and control the strip-shaped structure of the duplex stainless steel to have bimodal austenite distributed in a ferrite matrix, and can improve the tensile strength of the duplex stainless steel to be close to 1000Mpa, the elongation to be 60 percent and the product of strength and elongation to be 60 Gpa.
In order to achieve the above purpose of the present invention, the following technical solutions are adopted:
a method of making a plasticized enhanced economized duplex stainless steel comprising:
heating the economical duplex stainless steel to 1300-1400 ℃ at a heating speed of 20-100 ℃/s under a vacuum condition, preserving heat for 10-20 min, and slowly cooling to room temperature at a cooling speed of 5-15 ℃/s;
then, carrying out asynchronous rolling treatment on the economical duplex stainless steel at room temperature, wherein the deformation of the asynchronous rolling treatment is 70-90%;
and heating the economical duplex stainless steel subjected to asynchronous rolling treatment to 1050-1150 ℃ under atmospheric conditions, preserving heat for 2-5min, and cooling to room temperature.
Further, in a preferred embodiment of the present invention, in the step of asynchronous rolling, the roll diameter ratio of the two rolls of asynchronous rolling is 0.6 to 0.75.
Further, in a preferred embodiment of the present invention, in the asynchronous rolling step, the rolling speed is 2-3 m/min.
Further, in the preferred embodiment of the present invention, the saving-type duplex stainless steel is selected from a hot-forged 19Cr saving-type duplex stainless steel bar stock.
Further, in a preferred embodiment of the present invention, the alloy composition of the hot-forged 19 Cr-saving duplex stainless steel bar stock comprises, by mass: cr 19.00-19.60 wt.%, Ni 0.2-2.0 wt.%, Mn 2.9-4.9 wt.%, N0.2-0.3 wt.%, C0.03-0.06 wt.%, Si 0.2-0.8 wt.%.
Further, in a preferred embodiment of the present invention, after the duplex stainless steel after the asynchronous rolling treatment is subjected to a heat-holding treatment, it is cooled to room temperature by oil cooling or water cooling at a cooling rate of 50-100 ℃/s.
A plasticized and reinforced economical duplex stainless steel, which is prepared by the above preparation method.
Further, in a preferred embodiment of the present invention, the economical duplex stainless steel has a tensile strength of 940-1000 Mpa, an elongation of 55-65%, and a product of strength and elongation of 55-65 Gpa.
The invention has the following effects:
1. according to the preparation method provided by the invention, the saving type duplex stainless steel is heated to 1300-1400 ℃ at a heating speed of 20-100 ℃/s and is kept warm for 10-20 min, and the ferrite single-phase region of the duplex stainless steel is subjected to solid solution treatment to obtain a ferrite single-phase structure. The heating speed of 20-100 ℃/s is favorable for obtaining ferrite single-phase structure. And then slowly cooling to room temperature at a cooling speed of 5-15 ℃/s so as to be convenient for a small amount of austenite phase to be uniformly precipitated in the ferrite matrix and ensure that the two-phase structure is uniform and is not distributed in a strip shape. On the other hand, if a cooling rate is high, such as water cooling, the ferrite single-phase structure at high temperature is retained.
2. In the process of asynchronously rolling the duplex stainless steel, the rolling speed of the upper roller and the lower roller is controlled, so that the obtained structure is more uniform, and the thinning effect is better. And because the duplex stainless steel at the moment is mainly a ferrite single-phase structure, the rolling deformation can reach 70-90%, so that the deformation energy storage and dislocation density of a ferrite matrix are increased, the austenite particles can be uniformly nucleated in a high dislocation density area in the ferrite matrix in the subsequent solution treatment process, and the high dislocation density provides a high enough nucleation driving force and enough nucleation positions for the nucleation of the austenite.
3. The asynchronously rolled duplex stainless steel is subjected to solution treatment for a short time of 2-5min within the range of 1050-1150 ℃, so that the uniform nucleation and precipitation of an austenite grain phase in a ferrite matrix are ensured, and the smaller grain size is also ensured. In the process, if the heat preservation time is too long (10-30 min), the two-phase structure is excessively coarsened, and the plasticizing effect of the material is influenced.
In conclusion, in the preparation method of the plasticized and reinforced saving type duplex stainless steel, the strip-shaped structure of the duplex stainless steel is improved by adopting the pre-solid solution heat treatment, the asynchronous cold deformation and the solid solution treatment, the tensile strength of the saving type duplex stainless steel can be improved to be close to 1000Mpa, the elongation is increased by nearly one time and is as high as 60 percent, and the product of strength and elongation is increased by more than one time and is as high as 60 Gpa.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings needed to be used in the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings without inventive exercise.
FIG. 1 is a cold deformation-heat treatment process flow of the present invention;
FIG. 2 is an initial microstructure of an economical duplex stainless steel used in example 1 of the present invention;
FIG. 3 is a microstructure of an economical duplex stainless steel after treatment in step 1 of example 1 of the present invention;
FIG. 4 is a microstructure of an economical duplex stainless steel after treatment in step 3 of example 1 of the present invention;
FIG. 5 is an initial microstructure of an economical duplex stainless steel used in example 2 of the present invention;
FIG. 6 is a microstructure of an economical duplex stainless steel after treatment in step 1 of example 2 of the present invention;
fig. 7 is a microstructure of the saving type duplex stainless steel after the treatment of step 3 of example 2 of the present invention.
Fig. 8 is a microstructure of the saving type duplex stainless steel after the treatment of step 3 of example 3 of the present invention.
FIG. 9 is a microstructure of an economical duplex stainless steel after comparative example 1, step 1 treatment according to the present invention;
FIG. 10 is a microstructure of an economical duplex stainless steel after comparative example 1, step 3 treatment according to the present invention;
FIG. 11 is a microstructure of an economical duplex stainless steel after comparative example 2 of the present invention, step 1;
FIG. 12 is a microstructure of an economical duplex stainless steel after treatment of comparative example 2, step 3, according to the present invention;
FIG. 13 is a comparison of mechanical curves of examples and comparative examples.
Detailed Description
Embodiments of the present invention will be described in detail below with reference to examples, but it will be understood by those skilled in the art that the following examples are only illustrative of the present invention and should not be construed as limiting the scope of the present invention. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
In order to make the aforementioned objects, features and advantages of the present invention comprehensible, embodiments accompanied with figures are described in further detail below.
Example 1
This example provides a plasticized and reinforced economical duplex stainless steel, which is prepared by the following steps, and the process flow is shown in fig. 1:
step 1: the hot-forging saving duplex stainless steel plate is selected, and the contents (wt.%) of main alloy elements of Cr, Ni, Mn, N, C and Si are 19.00, 0.20, 3.91, 0.31, 0.03 and 0.21. Placing the hot-forging state conservation-oriented duplex stainless steel plate on gleeble, heating to 1300 ℃ at a heating speed of 20 ℃/s under a vacuum condition, preserving heat for 15min, and then slowly cooling to room temperature at a cooling speed of 10 ℃/s under an air condition. The process is primary solution treatment; a gleeble3800 thermophysical simulation testing machine was used.
Step 2: and (3) carrying out asynchronous rolling treatment with the deformation of 80% on the saving type duplex stainless steel plate subjected to the primary solution treatment at room temperature, wherein the roll diameter ratio of two asynchronous rolling rolls is 0.75, and the rolling speed is 3 m/min.
And step 3: and (3) placing the economical duplex stainless steel subjected to deformation treatment in a resistance furnace, heating to 1050 ℃ and preserving heat for 3min, and then performing oil quenching treatment to room temperature, wherein the process is secondary solution treatment.
The initial microstructure of the saving type duplex stainless steel used in this example is shown in fig. 2, the initial microstructure of the saving type duplex stainless steel is an austenite ferrite duplex structure distributed in a strip shape, and the average grain size of ferrite and austenite is about 28 um; the microstructure of the test steel after the first-order solution heat treatment is shown in figure 3, and a small amount of austenite is uniformly precipitated in the phase boundary and the phase of ferrite in the process of slow cooling after solution treatment at 1300 ℃. FIG. 4 is a view showing a bimodal structure after the secondary solution treatment in example 1 of the present invention, in which fine austenite grains are uniformly precipitated on a ferrite matrix and a structure in which residual austenite is coarse after the primary solution treatment.
After the cold deformation-heat treatment process is carried out on the steel in the embodiment 1 of the invention, the engineering stress-strain curve is shown in fig. 13, compared with the initial elongation of 37% and the tensile strength of 822Mpa in the embodiment 1, the elongation of the embodiment 1 is improved to 60%, the elongation is improved by nearly one time, the tensile strength is improved to 961Mpa, and the fracture form is changed from brittle fracture to plastic fracture.
Example 2
This example provides a plasticized and reinforced economical duplex stainless steel, which is prepared by the steps of:
step 1: the hot-forging state saving type duplex stainless steel plate is selected, and the contents (wt.%) of main alloy elements of Cr, Ni, Mn, N, C and Si are 19.23, 1.05, 2.94, 0.21, 0.0578 and 0.781. Placing the hot-forging state conservation-oriented duplex stainless steel plate on gleeble, heating to 1300 ℃ under a vacuum condition, preserving heat for 15min, and then cooling to room temperature at a cooling speed of 10 ℃/s under an air condition, wherein the process is primary solution treatment; a gleeble3800 thermophysical simulation testing machine was used.
Step 2: and (3) carrying out asynchronous rolling treatment with the deformation of 80% on the saving type duplex stainless steel plate subjected to the primary solution treatment at room temperature, wherein the roll diameter ratio of two asynchronous rolling rolls is 0.75, and the rolling speed is 3 m/min.
And (3) placing the economical duplex stainless steel subjected to deformation treatment in a resistance furnace, heating to 1050 ℃ and preserving heat for 3min, and then performing oil quenching treatment to room temperature, wherein the process is secondary solution treatment.
The initial microstructure of the saving type duplex stainless steel used in this example is shown in fig. 5, the initial microstructure of the saving type duplex stainless steel is an austenite ferrite duplex structure distributed in a strip shape, and the average grain size of ferrite and austenite is about 30 um; the microstructure of the test steel after the first-order solution heat treatment is shown in figure 3, and a small amount of austenite is uniformly precipitated in the phase boundary and the phase of ferrite in the process of slow cooling after solution treatment at 1300 ℃. FIG. 6 is a view showing a bimodal microstructure after the secondary solution treatment in example 2 of the present invention, in which fine austenite grains are uniformly precipitated on a ferrite matrix and a coarse structure of retained austenite after the primary solution treatment is present. After the cold deformation-heat treatment process is performed on the steel in example 2 of the invention, the engineering stress-strain curve is shown in fig. 13, and compared with the initial 34% elongation and the tensile strength of 817Mpa in example 2, the elongation of example 2 is increased by about one time by 63% elongation, the tensile strength is increased by 951Mpa, and the fracture mode is changed from brittle fracture to ductile fracture.
Example 3
This example provides a plasticized and reinforced economical duplex stainless steel, which is prepared by the steps of:
step 1: the hot-forging saving duplex stainless steel plate is selected, and the contents (wt.%) of main alloy elements of Cr, Ni, Mn, N, C and Si are 19.00, 0.20, 3.91, 0.31, 0.03 and 0.21. Placing the hot-forging state conservation-oriented duplex stainless steel plate on gleeble, heating to 1300 ℃ at a heating speed of 20 ℃/s, preserving heat for 15min, and then cooling to room temperature at a cooling speed of 10 ℃/s under the air condition, wherein the process is primary solution treatment; a gleeble3800 thermophysical simulation testing machine was used.
Step 2: and (3) carrying out asynchronous rolling treatment with the deformation of 80% on the saving type duplex stainless steel plate subjected to the primary solution treatment at room temperature, wherein the roll diameter ratio of two asynchronous rolling rolls is 0.75, and the rolling speed is 3 m/min.
And step 3: and (3) placing the economical duplex stainless steel subjected to deformation treatment in a resistance furnace, heating to 1150 ℃, preserving the heat for 3min, and then performing water crushing treatment to room temperature, wherein the process is secondary solution treatment.
The initial microstructure of the saving type duplex stainless steel used in this example is shown in fig. 2, the initial microstructure of the saving type duplex stainless steel is an austenite ferrite duplex structure distributed in a strip shape, and the average grain size of ferrite and austenite is about 28 um; the microstructure of the test steel after the first-order solution heat treatment is shown in figure 3, and a small amount of austenite is uniformly precipitated in the phase boundary and the phase of ferrite in the process of slow cooling after solution treatment at 1300 ℃. FIG. 8 is a view showing a bimodal microstructure after the secondary solution treatment in example 3 of the present invention, in which fine austenite grains are uniformly precipitated on a ferrite matrix and a coarse structure of retained austenite after the primary solution treatment is present. After the cold deformation-heat treatment process is performed on the steel in example 13 of the invention, the engineering stress-strain curve is shown in fig. 13, compared with the initial elongation of 37% and the tensile strength of 822Mpa in example 1, the elongation of example 3 is improved to 59%, the elongation is improved by nearly one time, the tensile strength is improved to 942Mpa, and the fracture form is changed from brittle fracture to ductile fracture.
To further illustrate the effects of the present invention, the following comparative examples are provided:
comparative example 1
The comparative example provides a method for preparing a saving-type duplex stainless steel, comprising the following steps:
step 1: the hot-forging saving duplex stainless steel plate is selected, and the contents (wt.%) of main alloy elements of Cr, Ni, Mn, N, C and Si are 19.00, 0.20, 3.91, 0.31, 0.03 and 0.21. Placing the hot-forging state conservation-oriented duplex stainless steel plate on a gleeble, heating to 1300 ℃ at a heating speed of 20 ℃/s, preserving heat for 15min, then rapidly cooling to room temperature at a cooling speed of 100 ℃/s under the condition of water crushing, and reserving a ferrite single-phase structure, wherein the process is primary solution treatment; a gleeble3800 thermophysical simulation testing machine was used.
Step 2: and (3) carrying out asynchronous rolling treatment with the deformation of 80% on the saving type duplex stainless steel plate subjected to the primary solution treatment at room temperature, wherein the roll diameter ratio of two asynchronous rolling rolls is 0.75, and the rolling speed is 3 m/min.
And step 3: and (3) placing the economical duplex stainless steel subjected to deformation treatment in a resistance furnace, heating to 1050 ℃ and preserving heat for 3min, and then performing oil quenching treatment to room temperature, wherein the process is secondary solution treatment.
The initial microstructure of the saving type duplex stainless steel used in this example is shown in fig. 2, the initial microstructure of the saving type duplex stainless steel is an austenite ferrite duplex structure distributed in a strip shape, and the average grain size of ferrite and austenite is about 28 um; the microstructure of the test steel after the first-order solution heat treatment is shown in FIG. 9, and shows a ferrite single-phase structure after rapid cooling after solution at 1300 ℃ without austenite precipitation. FIG. 10 is a view showing a fine structure after the secondary solution treatment of comparative example 1 of the present invention, in which austenite is uniformly precipitated in a ferrite single-phase structure after the cold rolling after the secondary solution treatment to obtain a uniformly-fine structure. The refined metastable austenite structure improves the strength of the test steel, but also inhibits the Trip effect (transformation induced plasticity) of the test steel, weakens the plasticizing effect of the test steel, and the bimodal structure distribution not only has the high strength of a fine grain structure, but also has the good Trip plasticizing effect. The mechanical curve of comparative example 1 is shown in FIG. 13, and the tensile strength is increased from 822MPa to 928MPa in comparison with the initial state of example 1, and the elongation is not greatly increased.
It is thus demonstrated that the method of comparative example 1, during the first stage solution treatment of step 1, employs a relatively fast cooling rate to cause the austenite phase to precipitate in less time than the single-phase ferrite. Therefore, by adopting a slow cooling mode with the cooling rate of 5-15 ℃/s, a small amount of austenite can be uniformly precipitated in a ferrite phase, so that a foundation is provided for the subsequent preparation of a bimodal structure, and the cooling mode is important for improving the performance of the duplex stainless steel.
Comparative example 2
The comparative example provides a method for preparing a saving-type duplex stainless steel, comprising the following steps:
step 1: the hot-forging saving duplex stainless steel plate is selected, and the contents (wt.%) of main alloy elements of Cr, Ni, Mn, N, C and Si are 19.00, 0.20, 3.91, 0.31, 0.03 and 0.21. Placing the hot-forged saving type duplex stainless steel plate in a resistance furnace, heating to 1100 ℃ under the air condition, preserving the heat for 30min, and then rapidly cooling to room temperature under the water crushing condition, wherein the process is primary solution treatment;
step 2: and (3) carrying out asynchronous rolling treatment with the deformation amount of 60% on the saving type duplex stainless steel plate subjected to the primary solution treatment at room temperature, wherein the roll diameter ratio of two asynchronous rolling rolls is 0.75, and the rolling speed is 3 m/min.
And step 3: and (3) placing the economical duplex stainless steel subjected to deformation treatment in a resistance furnace, heating to 1050 ℃ and preserving heat for 3min, and then performing water quenching treatment to room temperature, wherein the process is secondary solution treatment.
The initial microstructure of the saving type duplex stainless steel used in this example is shown in fig. 2, the initial microstructure of the saving type duplex stainless steel is an austenite ferrite duplex structure distributed in a strip shape, and the average grain size of ferrite and austenite is about 28 um; the microstructure of the test steel after the first-order solution heat treatment is shown in fig. 11, and the structure obtained after the solution treatment is still in a remarkable strip shape and is distributed with remarkable directionality. FIG. 12 is a diagram showing the two-phase structure of comparative example 2 of the present invention after the second-stage solution treatment, in which the austenite phase size of the structure obtained by the process is substantially unchanged as shown in FIG. 12, and the austenite grain size is reduced to 8um from 28um in the initial state of solid solution after the above-mentioned process treatment. The mechanical curve of comparative example 2 is shown in FIG. 13, and the tensile strength is increased from 822MPa to 889MPa compared with the initial state of example 1, and the elongation is not greatly increased.
It is thus demonstrated that the method of comparative example 2, in which the grain size of austenite is refined but the phase size is not substantially changed, is used. In the first-stage solution treatment process in the step 1, the austenite phase is difficult to precipitate in the ferrite single-phase structure by adopting a fast cooling speed after heating at 1100 ℃ under atmospheric conditions and preserving heat. Therefore, by adopting the process of rapid heating condition +1300 ℃ and slow cooling, the uniformly distributed bimodal structure can be obtained. The strength of the test steel can be improved, the plasticity of the test steel can be improved, and good performance can be obtained.
The above-mentioned embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements made to the technical solution of the present invention by those skilled in the art without departing from the spirit of the present invention shall fall within the protection scope defined by the claims of the present invention.
Claims (8)
1. A method for preparing plasticized and reinforced economical duplex stainless steel, which is characterized by comprising the following steps:
heating the economical duplex stainless steel to 1300-1400 ℃ at a heating speed of 20-100 ℃/s under a vacuum condition, preserving heat for 10-20 min, and slowly cooling to room temperature at a cooling speed of 5-15 ℃/s;
then, carrying out asynchronous rolling treatment on the economical duplex stainless steel at room temperature, wherein the deformation of the asynchronous rolling treatment is 70-90%;
and heating the economical duplex stainless steel subjected to asynchronous rolling treatment to 1050-1150 ℃ under atmospheric conditions, preserving heat for 2-5min, and cooling to room temperature.
2. The method of manufacturing plasticized reinforced economical duplex stainless steel according to claim 1, wherein in the step of asynchronous rolling treatment, the roll diameter ratio of two rolls of asynchronous rolling is 0.6 to 0.75.
3. The method of manufacturing plasticized reinforced economical duplex stainless steel according to claim 1, wherein in the step of asynchronous rolling treatment, the rolling speed is 2 to 3 m/min.
4. A method of making plasticized reinforced economized duplex stainless steel according to claim 1, wherein said economized duplex stainless steel is selected from hot forged 19Cr economized duplex stainless steel bar stock.
5. A method of producing plasticized reinforced economized duplex stainless steel according to claim 4, wherein said hot forged 19Cr economized duplex stainless steel bar stock has an alloy composition comprising, in mass percent: cr 19.00-19.60 wt.%, Ni 0.2-2.0 wt.%, Mn 2.9-4.9 wt.%, N0.2-0.3 wt.%, C0.03-0.06 wt.%, Si 0.2-0.8 wt.%.
6. The method of manufacturing plasticized reinforced economical duplex stainless steel according to claim 1, wherein the duplex stainless steel after the asynchronous rolling process is subjected to a heat-keeping treatment and then cooled to room temperature by oil-cooling or water-cooling at a cooling rate of 50-100 ℃/s.
7. A plasticized and reinforced economical duplex stainless steel, which is produced by the production method according to any one of claims 1 to 6.
8. The plasticized reinforced economical duplex stainless steel according to claim 7, wherein the economical duplex stainless steel has a tensile strength of 940-1000 Mpa, an elongation of 55-65% and a product of strength and elongation of 55-65 Gpa.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110064791.4A CN112899585B (en) | 2021-01-18 | 2021-01-18 | Plasticized and reinforced economical duplex stainless steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110064791.4A CN112899585B (en) | 2021-01-18 | 2021-01-18 | Plasticized and reinforced economical duplex stainless steel and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112899585A true CN112899585A (en) | 2021-06-04 |
| CN112899585B CN112899585B (en) | 2022-03-22 |
Family
ID=76115980
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110064791.4A Active CN112899585B (en) | 2021-01-18 | 2021-01-18 | Plasticized and reinforced economical duplex stainless steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112899585B (en) |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006233292A (en) * | 2005-02-25 | 2006-09-07 | Toshiba Corp | Corrosion resistant steel and producing method therefor |
| JP2010229459A (en) * | 2009-03-26 | 2010-10-14 | Nippon Steel & Sumikin Stainless Steel Corp | Alloy-saving duplex stainless steel material having preferable corrosion resistance and method of manufacturing the same |
| JP2011168838A (en) * | 2010-02-18 | 2011-09-01 | Nippon Steel & Sumikin Stainless Steel Corp | Duplex stainless steel material for vacuum vessel and method for manufacturing the same |
| CN103526130A (en) * | 2013-10-23 | 2014-01-22 | 北京科技大学 | Processing method for direct cold rolling of two-phase stainless steel as-cast state billet steel after solid solution treatment |
| CN105177255A (en) * | 2015-10-15 | 2015-12-23 | 东北大学 | Heat treatment technological method for ferrite-austenite duplex stainless steel |
| CN110475895A (en) * | 2017-03-30 | 2019-11-19 | 日铁不锈钢株式会社 | Two phase stainless steel and its manufacturing method |
-
2021
- 2021-01-18 CN CN202110064791.4A patent/CN112899585B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006233292A (en) * | 2005-02-25 | 2006-09-07 | Toshiba Corp | Corrosion resistant steel and producing method therefor |
| JP2010229459A (en) * | 2009-03-26 | 2010-10-14 | Nippon Steel & Sumikin Stainless Steel Corp | Alloy-saving duplex stainless steel material having preferable corrosion resistance and method of manufacturing the same |
| JP2011168838A (en) * | 2010-02-18 | 2011-09-01 | Nippon Steel & Sumikin Stainless Steel Corp | Duplex stainless steel material for vacuum vessel and method for manufacturing the same |
| CN103526130A (en) * | 2013-10-23 | 2014-01-22 | 北京科技大学 | Processing method for direct cold rolling of two-phase stainless steel as-cast state billet steel after solid solution treatment |
| CN105177255A (en) * | 2015-10-15 | 2015-12-23 | 东北大学 | Heat treatment technological method for ferrite-austenite duplex stainless steel |
| CN110475895A (en) * | 2017-03-30 | 2019-11-19 | 日铁不锈钢株式会社 | Two phase stainless steel and its manufacturing method |
Non-Patent Citations (2)
| Title |
|---|
| 轧制机械及连轧自动化国家重点实验室: "《液压张力温轧机的研制与应用》", 31 December 2016, 冶金工业出版社 * |
| 陈雷 等: "固溶温度对节约型双相不锈钢TRIP/TWIP行为的影响", 《钢铁》 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112899585B (en) | 2022-03-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110066964B (en) | Ultrahigh-strength medium manganese steel and warm rolling preparation method thereof | |
| CN107177786B (en) | A kind of design and its manufacturing method of the high manganese cut deal of LNG storage tank | |
| CN110273095B (en) | Preparation method of medium-entropy alloy with tensile strength of 1.5GPa | |
| US20230357882A1 (en) | Gpa-grade bainite steel having ultra-high yield ratio and manufacturing method for gpa-grade bainite steel | |
| CN112410681A (en) | High-strength-ductility medium manganese steel and preparation method thereof | |
| CN111321351B (en) | High-strength high-plasticity two-stage warm-rolling medium manganese steel and preparation method thereof | |
| CN107127212A (en) | The method of manganese cold-rolled steel sheet in super rapid heating technique productions high strength and ductility | |
| WO2017215478A1 (en) | High strength and high toughness stainless steel and processing method thereof | |
| CN108315655A (en) | A kind of high-yield strength LNG storage tank high manganese cut deal and preparation method thereof | |
| CN113106352B (en) | Nano-enhanced hydrogen embrittlement-resistant medium manganese steel and preparation method thereof | |
| CN114807524B (en) | High-strength and high-toughness medium manganese steel based on partial austenitization and preparation method thereof | |
| CN101684539A (en) | Thick-specification high-tenacity X70 acicular ferrite pipe line steel and manufacturing method thereof | |
| CN106435380A (en) | Microalloyed high-aluminum high-ductility steel plate and manufacturing method thereof | |
| CN115141984A (en) | High-entropy austenitic stainless steel and preparation method thereof | |
| CN110616301B (en) | Production method for improving precipitation strengthening effect of Ti microalloyed hot-rolled high-strength steel on line | |
| CN112899585B (en) | Plasticized and reinforced economical duplex stainless steel and preparation method thereof | |
| CN115522126B (en) | Medium manganese steel with good wear resistance and production method thereof | |
| CN115323252B (en) | Ultrahigh-strength high-plasticity medium manganese steel and preparation method thereof | |
| CN114480811B (en) | High-strength-plastic product medium manganese steel with gradient structure and preparation method thereof | |
| CN114480808A (en) | Manganese steel in composite gradient structure and preparation method thereof | |
| CN101429620B (en) | Phosphor intensified twin crystal inducement plastic steel material and its production technique | |
| CN115852283B (en) | High-strength plastic nickel-based alloy plate with double-peak structure and preparation method thereof | |
| CN107475622B (en) | Steel plate and its manufacturing method with good thermal processability energy | |
| CN115572879B (en) | Nickel-free high-entropy alloy with high strength and toughness and low temperature and preparation method thereof | |
| CN117127099B (en) | 1300MPa ultra-high strength plastic cold-rolled Mn-TRIP steel and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |