CN115478134A - Method for directly quenching rolled steel plate - Google Patents
Method for directly quenching rolled steel plate Download PDFInfo
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- CN115478134A CN115478134A CN202211185712.6A CN202211185712A CN115478134A CN 115478134 A CN115478134 A CN 115478134A CN 202211185712 A CN202211185712 A CN 202211185712A CN 115478134 A CN115478134 A CN 115478134A
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- quenching
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
-
- 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
- C21D2211/008—Martensite
Abstract
The invention particularly relates to a method for directly quenching a steel plate after rolling, which belongs to the technical field of steel preparation and comprises the following steps: obtaining the non-recrystallization temperature of the steel billet; rolling the steel billet to obtain a steel plate; relaxing the steel plate to obtain a relaxed steel plate; quenching the relaxed steel plate to obtain a quenched steel plate; wherein, in the rolling process, the temperature of the steel billet is higher than the non-recrystallization temperature of the steel billet; the austenite which is subjected to pressure processing in the recrystallization region has a grain form which is similar to that of offline quenching and comprises equiaxed grains similar to offline quenching structures and the characteristic of diversified lath orientations in the grains, and the rolling deformation of the online quenching process provides conditions for increasing the phase transformation nucleation rate in the subsequent phase transformation process, so that the formation of lath refining characteristics in the grains is promoted, and good obdurability matching can be achieved.
Description
Technical Field
The invention belongs to the technical field of steel preparation, and particularly relates to a method for directly quenching a rolled steel plate.
Background
The online quenching process is applied to various steel plants, and plays a positive role in shortening the delivery cycle of quenched and tempered steel products, reducing the manufacturing cost, reducing carbon emission and the like, but because the components of the products are designed and the process route and the like have defects, the products manufactured based on the process generally have the problems of high strength and low impact toughness.
Disclosure of Invention
The application aims to provide a method for directly quenching a steel plate after rolling so as to solve the problem that the impact toughness of the existing on-line quenched steel plate is low.
The embodiment of the invention provides a method for directly quenching a steel plate after rolling, which comprises the following steps:
obtaining the non-recrystallization temperature of the steel billet;
rolling the steel billet to obtain a steel plate;
relaxing the steel plate to obtain a relaxed steel plate;
quenching the relaxed steel plate to obtain a quenched steel plate;
wherein, in the rolling process, the temperature of the steel billet is higher than the non-recrystallization temperature of the steel billet.
Optionally, the final rolling temperature of the rolling is more than 30 ℃ higher than the non-recrystallization temperature of the billet.
Optionally, the pass average reduction rate of the rolling is more than 10%.
Optionally, the average grain size of the steel sheet is 8 μm to 50 μm.
Optionally, the non-recrystallization temperature of the steel slab is calculated according to the actual composition of the steel plate by using the non-recrystallization temperature TNR.
Optionally, the non-recrystallization temperature of the steel slab is measured according to a thermal simulation experiment.
Optionally, the relaxation time is less than or equal to 150s.
Optionally, the metallographic structure of the relaxed steel plate includes ferrite, and the proportion of the ferrite is less than or equal to 60% by volume.
Optionally, the quenching is on-line quenching.
Optionally, the metallographic structure of the relaxed steel sheet comprises dislocated austenite.
One or more technical solutions in the embodiments of the present invention at least have the following technical effects or advantages:
according to the method for directly quenching the rolled steel plate, the austenite subjected to pressure processing is completed in the recrystallization region, the grain form is similar to that of off-line quenching, the method comprises equiaxial grains similar to off-line quenching tissues and the characteristic of diversified lath orientations in the grains, and the rolling deformation of the on-line quenching process provides conditions for increasing the phase transformation nucleation rate in the subsequent phase transformation process, so that the formation of the lath refining characteristic in the grains is promoted, and good obdurability matching can be achieved.
The above description is only an overview of the technical solutions of the present invention, and the present invention can be implemented in accordance with the content of the description so as to make the technical means of the present invention more clearly understood, and the above and other objects, features, and advantages of the present invention will be more clearly understood.
Drawings
In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the drawings needed to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on the drawings without creative efforts.
FIG. 1 is a flow chart of a method provided by an embodiment of the present invention;
FIG. 2 is a schematic diagram of the structure characteristics of various quenching processes provided by the embodiments of the present invention;
FIG. 3 is a grain morphology diagram of the steel sheet provided in example 1 of the present invention.
Detailed Description
The present invention will be specifically explained below in conjunction with specific embodiments and examples, and the advantages and various effects of the present invention will be more clearly presented thereby. It will be understood by those skilled in the art that these specific embodiments and examples are for the purpose of illustrating the invention and are not to be construed as limiting the invention.
Throughout the specification, unless otherwise specifically noted, terms used herein should be understood as having meanings as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. If there is a conflict, the present specification will control.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
In order to solve the technical problems, the general idea of the embodiment of the application is as follows:
the applicant finds in the course of the invention: at present, the problems of high strength and low impact toughness of steel plate products generally exist, and one of the most important reasons for generating the problems is as follows: because the designed composition of the material is higher than the non-recrystallization temperature, and a part of deformation of the steel plate is completed in a non-recrystallization area during the press working process, austenite grains are flat after the rolling is completed, and austenite in the state forms martensite lath bundles with more consistent orientation during the subsequent quenching process, which is not beneficial to preventing the expansion of cracks, so the impact work is lower than the traditional off-line quenching numerical value.
According to an exemplary embodiment of the present invention, there is provided a method of direct quenching after rolling of a steel sheet, the method including:
s1, obtaining the non-recrystallization temperature of a steel billet;
in some embodiments, the non-recrystallization temperature of the steel slab is calculated from the actual composition of the steel sheet by the non-recrystallization temperature TNR, or the non-recrystallization temperature of the steel slab is measured according to a thermal simulation experiment.
S2, rolling the steel billet to obtain a steel plate; in the rolling process, the temperature of the steel billet is higher than the non-recrystallization temperature of the steel billet;
in some embodiments, the finish rolling temperature of rolling is greater than the non-recrystallization temperature of the steel slab by more than 30 ℃.
The set finish rolling temperature is higher than the calculated value of TNR or the measured value of TNR by more than 30 ℃, which is beneficial to the recrystallization of austenite and the equiaxial transformation after the recrystallization.
In some embodiments, the pass average reduction of rolling is 10% or more.
The pass average reduction rate of rolling is controlled to be more than 10%, which is beneficial to the refinement of original coarse austenite.
In some embodiments, the average grain size of the steel sheet is 8 μm to 50 μm.
The average grain size of the prior austenite after being rolled in a recrystallization zone is 8 to 50 mu m. The martensite with different orientations and fine substructure can be formed after the subsequent phase transformation.
S3, relaxing the steel plate to obtain a relaxed steel plate;
in some embodiments, the time to relaxation ≦ 150s.
In some embodiments, the metallographic structure of the relaxed steel sheet comprises ferrite in an amount of 60% by volume or less.
Specifically, the steel sheet after completion of rolling is relaxed for a period of 0 to 150 seconds, which contributes to the completion of equiaxial transformation of austenite. According to the mechanical property requirement of the finished product, 0-60% of ferrite (acicular ferrite) is formed before quenching.
S4, quenching the relaxation steel plate to obtain a quenched steel plate;
in some embodiments, the quenching is an in-line quenching.
In some embodiments, the metallographic structure of the relaxed steel sheet comprises dislocated austenite.
Specifically, the steel sheet is directly quenched at the main rolling line, and the partially dislocated austenite is directly quenched, thereby forming martensite lath bundles having different orientations in austenite grains.
The austenite which is subjected to pressure processing in the recrystallization region has a grain shape similar to that of offline quenching, contains equiaxed grains similar to offline quenching structures and features of diversified lath orientations inside the grains (see fig. 2), and the rolling deformation of the online quenching process provides conditions for increasing the phase transformation nucleation rate in the subsequent phase transformation process, so that the formation of lath refining features inside the grains is promoted, and good toughness matching can be achieved.
The method of direct quenching after rolling of the steel sheet of the present application will be described in detail with reference to examples, comparative examples, and experimental data.
Example 1
A method for directly quenching a steel plate after rolling comprises the following steps:
1) The thickness of the steel plate is 25mm, and the design alloy components of the steel billet are as follows: 0.11% of carbon, 0.2% of silicon, 1.5% of manganese, 0.008% of Nb and 0.015% of Ti. The TNR temperature was calculated according to the formula to be 899 ℃.
2) The steel plate is rolled to the target thickness of 25mm from the plate blank at the finishing temperature of 968 ℃, 16 passes are performed in total, and the average reduction rate is 14.3 percent. The pass reduction is shown in the table below:
| pass of rolling | Pass reduction rate/%) |
| 1 | 6.69 |
| 2 | 8.79 |
| 3 | 8.39 |
| 4 | 8.79 |
| 5 | 8.25 |
| 6 | 16.42 |
| 7 | 16.95 |
| 8 | 18.31 |
| 9 | 19.86 |
| 10 | 21.06 |
| 11 | 20.13 |
| 12 | 20.06 |
| 13 | 16.79 |
| 14 | 14.97 |
| 15 | 12.64 |
| 16 | 10.35 |
| Mean value of | 14.3％ |
3) And (3) carrying out corresponding deformation simulation by a laboratory Gloobe tester, then rapidly cooling, and detecting the obtained average austenite grain size of 28 micrometers.
4) After the steel plate is rolled in the recrystallization zone, the steel plate is slowly transported to a rapid cooling device (quenching device) of a main rolling line through a roller way to realize the relaxation of austenite, the relaxation time is 41 seconds, and the proportion of the formed acicular ferrite is 10 percent.
5) The steel sheet is directly quenched in a rapid cooling apparatus to form bundles of martensite laths of various orientations within the austenite grains.
Example 2
A method for directly quenching a steel plate after rolling comprises the following steps:
5) The steel plate with the thickness of 25mm, the design alloy components of the steel billet are as follows: 0.11% of carbon, 0.2% of silicon, 1.5% of manganese, 0.008% of Nb and 0.015% of Ti. The TNR temperature was calculated to be 899 ℃.
6) The final rolling temperature of the steel plate is 980 ℃, the steel plate is rolled to the target thickness of 25mm by the plate blank, 16 passes are performed totally, and the average reduction rate is 14.6 percent. The pass reduction is as follows:
| pass of rolling | Pass reduction/% |
| 1 | 6.8 |
| 2 | 8.9 |
| 3 | 8.4 |
| 4 | 9 |
| 5 | 8 |
| 6 | 16.5 |
| 7 | 18 |
| 8 | 18.3 |
| 9 | 20 |
| 10 | 22 |
| 11 | 19 |
| 12 | 21 |
| 13 | 18 |
| 14 | 16 |
| 15 | 13 |
| 16 | 10 |
| Mean value of | 14.6 |
7) And (3) carrying out corresponding deformation simulation by a laboratory Gloobe tester, then rapidly cooling, and detecting the obtained average austenite grain size to be 30 mu m.
8) After the completion of the rolling in the recrystallization zone, the steel sheet was slowly transported to a rapid cooling facility (quenching facility) of the main rolling line through a roller table to achieve the relaxation of austenite with a relaxation time of 44 seconds and a proportion of formed acicular ferrite of 9%.
5) The steel sheet is directly quenched in a rapid cooling apparatus to form bundles of martensite laths of different orientations within the austenite grains.
Comparative example 1
1) The steel plate with the thickness of 25mm, the design alloy components of the steel billet are as follows: 0.11% of carbon, 0.2% of silicon, 1.5% of manganese, 0.009% of Nb and 0.016% of Ti. The TNR temperature is calculated according to a formula and is 901 ℃.
2) The final rolling temperature of the steel plate is 840 ℃, the steel plate is rolled to the target thickness of 25mm through the plate blank, 17 passes are performed in total, and the average reduction rate is 9.2%. The pass reduction is as follows:
| pass of rolling | Pass reduction/% |
| 1 | 3 |
| 2 | 5 |
| 3 | 5 |
| 4 | 6 |
| 5 | 7 |
| 6 | 10 |
| 7 | 11 |
| 8 | 11 |
| 9 | 11 |
| 10 | 12 |
| 11 | 11 |
| 12 | 12 |
| 13 | 12 |
| 14 | 11 |
| 15 | 11 |
| 16 | 11 |
| 17 | 7 |
| Mean value of | 9.2％ |
3) And (3) carrying out corresponding deformation simulation by a laboratory Gloobe tester, then rapidly cooling, and detecting the obtained average austenite grain size of 51 mu m.
4) After the steel sheet was rolled in two stages, it was transported to a rapid cooling facility (quenching facility) of the main rolling line through a roller table, and the proportion of acicular ferrite formed was 25%.
5) The steel sheet is directly quenched in a rapid cooling apparatus to form similarly oriented bundles of martensite laths within the austenite grains.
Comparative example 2
The comparative example adopts an off-line quenching process, which specifically comprises the following steps:
1) The thickness of the steel plate is 25mm, and the design alloy components of the steel billet are as follows: 0.11% of carbon, 0.2% of silicon, 1.5% of manganese, 0.009% of Nb and 0.016% of Ti.
2) The steel plate is heated to 900 ℃ in a quenching heating furnace, the total heating time is 85 minutes, and the steel plate is fully austenitized.
3) After the steel plate is taken out of the heating furnace, quenching is carried out in a quenching machine, and the steel plate is cooled to room temperature.
Related experiments:
the steels obtained in examples 1-2 and comparative examples 1-2 were subjected to property tests, and the test results are shown in the following table.
From the above table, the strength and toughness of the steel plate prepared by the method provided by the embodiment of the present application are equivalent to those of off-line quenching, and the toughness performance is much higher than that of the existing steel plate prepared by on-line quenching.
One or more technical solutions in the embodiments of the present invention at least have the following technical effects or advantages:
(1) The method provided by the embodiment of the invention finishes the pressure processed austenite in the recrystallization region, the grain form is similar to that of off-line quenching, the method comprises equiaxed grains similar to off-line quenching tissues and the characteristic of diversified lath orientations in the grains, and the rolling deformation of the on-line quenching process provides conditions for the increase of the phase transformation nucleation rate in the subsequent phase transformation process, so that the formation of lath refining characteristics in the grains is promoted, and good obdurability matching can be achieved;
(2) The method provided by the embodiment of the invention has the advantages of reducing the energy consumption in the process of manufacturing the steel material, shortening the product preparation flow and the like.
Finally, it should be further noted that the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (10)
1. A method for directly quenching a steel plate after rolling is characterized by comprising the following steps:
obtaining the non-recrystallization temperature of the steel billet;
rolling the steel billet to obtain a steel plate;
relaxing the steel plate to obtain a relaxed steel plate;
quenching the relaxed steel plate to obtain a quenched steel plate;
wherein, in the rolling process, the temperature of the steel billet is higher than the non-recrystallization temperature of the steel billet.
2. The method of direct post rolling quenching of steel sheet according to claim 1 wherein the final rolling temperature of said rolling is greater than the unrecrystallized temperature of said steel slab by more than 30 ℃.
3. The method for direct quenching after rolling of steel sheet according to claim 1, wherein the pass average reduction rate of the rolling is 10% or more.
4. A method for direct post rolling quenching of a steel sheet as claimed in claim 1 wherein the steel sheet has an average grain size of 8 μm to 50 μm.
5. The method for direct quenching after rolling of steel plate according to claim 1, wherein the non-recrystallization temperature of the steel slab is calculated by non-recrystallization temperature TNR based on the actual composition of the steel plate.
6. The method of direct post rolling quenching of steel sheet according to claim 1 wherein the unrecrystallized temperature of the steel slab is measured according to a thermal simulation experiment.
7. A method for direct quenching after rolling of steel sheet according to claim 1, characterized in that the relaxation time is less than or equal to 150s.
8. A method for direct quenching after rolling of steel sheet according to claim 1, characterized in that the metallographic structure of the relaxed steel sheet comprises ferrite, the proportion of ferrite being less than or equal to 60% by volume.
9. A method of direct post rolling quenching of a steel sheet as claimed in claim 1 wherein the quenching is an in-line quenching.
10. The method of direct post-rolling quenching of a steel sheet as claimed in claim 1 wherein the metallographic structure of the relaxed steel sheet comprises dislocation austenite.
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| CN114891994A (en) * | 2022-03-29 | 2022-08-12 | 江阴兴澄特种钢铁有限公司 | Grain size control method for rolling 316H austenitic stainless steel medium plate for nuclear power |
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2022
- 2022-09-27 CN CN202211185712.6A patent/CN115478134A/en active Pending
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| Publication number | Priority date | Publication date | Assignee | Title |
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| KR20130076570A (en) * | 2011-12-28 | 2013-07-08 | 주식회사 포스코 | Ultra heavy steel plate for pressure vessel with excellent low-temperature toughness and tensile property and manufacturing method of the same |
| CN104232868A (en) * | 2014-09-04 | 2014-12-24 | 东北大学 | Optimal controlled rolling method adopting ultra-fast cooling to control Austenite structure |
| CN111566249A (en) * | 2017-12-24 | 2020-08-21 | 株式会社Posco | High-strength steel sheet and method for producing same |
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| CN112195402A (en) * | 2020-09-28 | 2021-01-08 | 首钢集团有限公司 | Precipitation-strengthened high-strength and high-toughness medium manganese steel plate and preparation method thereof |
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