CN115216701B - Low-compression-ratio lamellar tearing resistant Q960 high-strength steel and preparation method thereof - Google Patents
Low-compression-ratio lamellar tearing resistant Q960 high-strength steel and preparation method thereof Download PDFInfo
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21D2211/00—Microstructure comprising significant phases
Abstract
The application discloses low-compression-ratio lamellar tearing resistant Q960 high-strength steel, which comprises the following chemical components in percentage by weight: c:0.12 to 0.15 percent, si:0.12 to 0.50 percent, mn:1.30 to 1.60 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.010 percent, mo:0.20 to 0.40 percent, cr:0.20 to 0.60 percent, ni:0.10 to 0.30 percent, V:0.04 to 0.06 percent, nb:0.015% -0.060%, alt:0.010% -0.060%, ti:0.008 to 0.035 percent, less than or equal to 0.005 percent of B, less than or equal to 0.0070 percent of N, less than or equal to 0.0030 percent of O, less than or equal to 0.0002 percent of H, and the balance of Fe and unavoidable impurities; the method has the technical key points that the casting blank with the thickness of 150mm is adopted, the high-thickness and high-strength steel plate Q960D with the thickness of 60mm is produced, the compression ratio is 2.5, and the technical problem of producing the high-strength steel plate with the compression ratio more than 3 is overcome; only a small amount of Nb, cr, mo, ni, V alloy elements are added, and the alloy cost is lower than that of the steel plates with the same specification in the same strength level of other plants or enterprises, so that the cost is saved; the lamellar tearing resistant steel has even structure in the thickness direction and good performance through a high-temperature high-pressure process and a quenching and tempering process.
Description
Technical Field
The application belongs to the technical field of ferrous metallurgy, and particularly relates to low-compression-ratio lamellar tearing resistant Q960 high-strength steel and a preparation method thereof.
Background
With the development of large-scale heavy-duty of coal mine machinery and engineering machinery, low-strength steel plates and common-thickness steel plates cannot meet the production requirements of part of special structural members.
The extra thick plate generally refers to a steel plate with the thickness of more than or equal to 60 mm; the compression ratio, in the case of sheet material, refers to the ratio of the thickness of the blank to the thickness of the rolled steel sheet; in order to fully ensure the internal metallurgical quality and the core performance of the steel plate, the minimum compression ratio between the continuous casting blank and the finished steel plate is more than 6:1, and the uniformity of the mechanical property in the thickness direction is difficult to control and the core quality is difficult to ensure due to the thickness; in order to ensure uniformity of mechanical properties in the thickness direction, thermal refining is often adopted.
In the prior patent CN111088467A, a low-compression-bit-thickness Q690D quenched and tempered high-strength steel plate and a production method thereof are disclosed, wherein N is less than or equal to 50ppm, and CEV is less than or equal to 0.64 through a converter smelting process; the LF refining time is 35-50 min, and the total level of inclusions in steel is effectively controlled to be not more than 1.0 level; the extra-thick Q690D high-strength steel plate with the mechanical property meeting the standard requirement can be produced, but the thickness of the casting blank adopted by the method is 220-260mm, the compression ratio is 3.67-4.34, and the strength grade is only Q690D;
CN106244922a discloses a method for producing high-strength steel with large thickness Q960E, wherein the thickness of a blank is 320mm, the thickness of a finished steel plate is 70mm, the width specification is less than 2800mm, and the compression ratio is more than 4; the Chinese patent No. 106756544A discloses a production method of Q690D high-strength steel with ultra-low carbon equivalent and large thickness, wherein a 320mm blank is adopted to produce 100mmQ690D high-strength steel with the compression ratio of 3.2, and the two patents both follow the general requirement that the compression ratio of the traditional medium plate production requirement is more than 3;
CN105177424a discloses a high-strength super-thick steel plate and a production method thereof, wherein the high-strength super-thick steel plate has high alloy component content, low steel ingot rolling yield, high production cost and long production period;
CN110423946 a discloses a production method of a low-compression-ratio ultra-high-strength steel Q960E extra-thick plate, which is a production method of a low-compression-ratio ultra-high-strength steel Q960E extra-thick plate, adopts a 300mm continuous casting billet to produce a 120mm thick Q960E steel plate, breaks through the limitation of the compression ratio of the traditional plate billet to produce the ultra-high-strength steel, realizes the rolling compression ratio of 2.5 to produce the large-thickness ultra-high-strength steel, but has more alloy addition, the addition of noble alloy Ni is 1.17%, cr is 0.64%, mo is 0.53%, the cost is higher, and the lamellar tearing resistance is not involved;
in summary, the existing Q960-grade high-strength quenched and tempered steel has the problems of higher compression ratio than 3, high alloy cost, high production cost and the like.
Disclosure of Invention
Technical problem to be solved
Aiming at the defects of the prior art, the application provides low-compression-ratio lamellar tearing resistant Q960 high-strength steel and a preparation method thereof, and solves the problems in the prior art.
Technical proposal
In order to achieve the above purpose, the application is realized by the following technical scheme:
the low-compression-ratio lamellar tearing resistant Q960 high-strength steel comprises the following chemical components in percentage by weight: c:0.12-0.15%, si:0.12-0.50%, mn:1.30-1.60%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, mo:0.20-0.40%, cr:0.20-0.60%, ni:0.10-0.30%, V:0.04-0.06%, nb:0.015% -0.060%, alt:0.010% -0.060%, ti: 0.008-0.035%, B less than or equal to 0.005%, N less than or equal to 0.0070%, O less than or equal to 0.0030%, H less than or equal to 0.0002%, and Fe and unavoidable impurities as the rest.
Preferably, the composition comprises the following chemical components in percentage by weight: c:0.13-0.15%, si:0.15-0.50%, mn:1.40-1.60%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, mo:0.30-0.40%, cr:0.30-0.60%, ni:0.20-0.30%, V:0.05-0.06%, nb:0.025% -0.060%, alt:0.030% -0.060%, ti:0.020% -0.035%, B is less than or equal to 0.005%, N is less than or equal to 0.0070%, O is less than or equal to 0.0030%, H is less than or equal to 0.0002%, and the balance is Fe and unavoidable impurities.
Preferably, the composition comprises the following chemical components in percentage by weight: c:014%, si:0.30%, mn:1.50 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.010 percent, mo:0.35%, cr:0.50%, ni:0.25%, V:0.055%, nb:0.040%, alt:0.050%, ti:0.025 percent, less than or equal to 0.005 percent of B, less than or equal to 0.0070 percent of N, less than or equal to 0.0030 percent of O, less than or equal to 0.0002 percent of H, and the balance of Fe and unavoidable impurities.
Preferably, the preparation method of the high-strength steel comprises the following specific steps:
s1, reheating the pretreated steel: 1200-1240 ℃;
s2, a high-temperature and high-pressure process: the initial rolling temperature is 1000-1150 ℃, the accumulated rolling reduction is more than or equal to 60%, and the final rolling temperature is in the interval: performing water cooling treatment after rolling at 850-950 ℃;
s3, the quenching and tempering process comprises a quenching and tempering process;
(1) Quenching process, wherein the quenching heating temperature is 920+/-5 ℃, and the heating coefficient is 1.4-1.5min/mm;
(2) And tempering, wherein the tempering temperature is 400-500 ℃, the tempering coefficient is 3.0min/mm, and the steel plate is cooled to room temperature after being taken out of the furnace.
Preferably, in the step S1, the steel is initially heated at a temperature of: the heat preservation treatment is needed between the primary heating and the reheating treatment at the temperature of 1000-1200 ℃, the time point of maintaining the temperature is 1200 ℃, and the heat preservation time is 10-30 min.
Preferably, in S2, the cooling temperature is 300 ℃ to 400 ℃.
Preferably, in the step S3, the steel sheet is fed to a plurality of transfer rolls to move after being discharged from the furnace, and air-cooled to room temperature.
Preferably, in the step S3, the tempered steel plate microstructure is tempered sorbite.
In summary, the present application includes at least one of the following beneficial technical effects:
firstly, the casting blank with the thickness of 150mm is adopted to produce the high-thickness and high-strength steel plate Q960D with the thickness of 60mm, the compression ratio is 2.5, and the technical problem of producing the high-strength steel plate with the compression ratio more than 3 is overcome;
secondly, only a small amount of Nb, cr, mo, ni, V alloy elements are added, and the alloy cost is lower than that of the steel plates with the same specification and the same strength level of other plants or enterprises, so that the cost is saved;
thirdly, the application adopts the high-temperature high-pressure process and the quenching and tempering process, so that the structure in the thickness direction is uniform, and the lamellar tearing resistance of the steel is good.
Detailed Description
It will be apparent that the described embodiments are only some, but not all, embodiments of the application. All other embodiments, which can be made by those skilled in the art based on the embodiments of the application without making any inventive effort, are intended to be within the scope of the application.
A low-compression-ratio lamellar tearing resistant Q960 high-strength steel and a preparation method thereof comprise the following chemical components in percentage by weight: c:0.12 to 0.15 percent, si:0.12 to 0.50 percent, mn:1.30 to 1.60 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.010 percent, mo:0.20 to 0.40 percent, cr:0.20 to 0.60 percent, ni:0.10 to 0.30 percent, V:0.04 to 0.06 percent, nb:0.015% -0.060%, alt:0.010% -0.060%, ti:0.008 to 0.035 percent, less than or equal to 0.005 percent of B, less than or equal to 0.0070 percent of N, less than or equal to 0.0030 percent of O, less than or equal to 0.0002 percent of H, and the balance of Fe and unavoidable impurities.
A low-compression-ratio lamellar tearing resistant Q960 high-strength steel and a preparation method thereof comprise the following steps:
reheating temperature: 1200-1240 ℃;
high temperature and high pressure process: the initial rolling temperature is 1000-1150 ℃, the accumulated rolling reduction is more than or equal to 60%, and the final rolling temperature is in the interval: water cooling is carried out after rolling at 850-950 ℃ and the cooling temperature is 300-400 ℃;
the quenching and tempering process comprises a quenching process and a tempering process; quenching process, wherein the quenching heating temperature is 920+/-5 ℃, the steel plate is ensured to be fully austenitized, and the heating coefficient is 1.5min/mm; tempering process, wherein the tempering temperature is 400-500 ℃, the tempering coefficient is 3.0min/mm, the steel plate is cooled to room temperature after being taken out of the furnace, and the microstructure of the tempered steel plate is tempered sorbite.
The steel plate with 960MPa grade produced by the manufacturing method has the yield strength of more than or equal to 960MPa, the tensile strength of more than or equal to 980MPa, the elongation A of more than or equal to 14 percent, the longitudinal impact energy of more than or equal to 100J at minus 20 ℃, the Z-direction stretching reduction of area of more than or equal to 35 percent and good lamellar tearing resistance.
The arrangement of the steel plate components in the application considers the following points:
1) Carbon is effective for strengthening the steel plate, and has obvious effect on improving the hardenability of the steel, but higher carbon content can improve the carbon equivalent of the steel and reduce the weldability of the steel, so that the carbon content is controlled in a low carbon steel range, and the hardenability and strength of the steel are provided through the synergistic effect of C, mn, cr, mo and B;
2) Manganese can effectively improve the performance of steel through solid solution strengthening and phase change strengthening, but too high manganese can generate component segregation to influence the low-temperature toughness of a final product, so that the manganese content is controlled to be about 1.4 percent;
3) Molybdenum, chromium, boron and vanadium are important elements in the application, the hardenability of the steel plate can be obviously improved after the molybdenum, chromium and boron are added, the steel plate is ensured to obtain a high-strength martensitic structure, meanwhile, the composite addition of the molybdenum, chromium, boron and vanadium can effectively inhibit the softening of a welding heat affected zone structure in the welding process, and the welding part is ensured not to crack under the condition of low preheating temperature;
the rolling process adopts a high-temperature and high-pressure process, deformation and permeation reach the core part directly, so that the tissue refinement of the core part is ensured, and the lamellar tearing resistance is good.
The chemical compositions of the steel sheets of examples 1-2 of the present application are shown in Table 1.
The key rolling, cooling, heat treatment process parameters for each example are shown in table 2.
The mechanical properties of each example are shown in Table 3, which shows good toughness and plasticity.
Table 1 is:
examples 1-2 chemical composition of Steel sheet (second behavior example 1, third behavior example 2)
The low-compression-ratio lamellar tearing resistant Q960 high-strength steel and the preparation method thereof in the embodiment 1-2 are rolled, cooled and heat treated by the following processes: the reheating temperature of the slab is 1230 ℃, the heating time is 130min, the high-temperature high-pressure process is adopted, the initial rolling temperature is 1150 ℃, the accumulated rolling reduction is more than or equal to 60%, and the finishing rolling temperature interval is that: and (3) cooling the steel at 950 ℃ and 400 ℃ after rolling.
The quenching and tempering process comprises a quenching process and a tempering process, wherein the quenching and heating temperature is 920 ℃, the steel plate is ensured to be fully austenitized, and the heating coefficient is 1.4min/mm; and tempering, wherein the tempering temperature is 400 ℃, the tempering coefficient is 3.0min/mm, the steel plate is cooled to room temperature after being taken out of the furnace, and the microstructure of the tempered steel plate is tempered sorbite.
Table 2 is:
examples 1-2 production Process System (second behavioural example 1, third behavioural example 2)
The steel sheets produced according to the procedure of this example have the performance indexes shown in Table 3.
Table 3 is:
performance index of steel sheet manufactured in examples 1-2
According to the embodiment, through regulating and controlling the hardenability element, adding a small amount of Nb, cr, mo, ni, V alloy element, and utilizing a 150mm casting blank and adopting a high-temperature high-pressure process and a quenching and tempering process, the steel with the thickness of 960MPa and 60mm is produced under the process condition that the compression ratio is 2.5, and the lamellar tearing resistance is excellent.
Finally, it should be noted that: it is apparent that the above examples are only illustrative of the present application and are not limiting of the embodiments. Other variations or modifications of the above teachings will be apparent to those of ordinary skill in the art. It is not necessary here nor is it exhaustive of all embodiments. And obvious variations or modifications thereof are contemplated as falling within the scope of the present application.
Claims (6)
1. The low-compression-ratio lamellar tearing resistant Q960 high-strength steel is characterized by comprising the following chemical components in percentage by weight: c:0.12-0.15%, si:0.12-0.50%, mn:1.30-1.60%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, mo:0.20-0.40%, cr:0.20-0.60%, ni:0.10-0.30%, V:0.04-0.06%, nb:0.015% -0.060%, alt:0.010% -0.060%, ti: 0.008-0.035%, B less than or equal to 0.005%, N less than or equal to 0.0070%, O less than or equal to 0.0030%, H less than or equal to 0.0002%, and Fe and unavoidable impurities as the rest;
the preparation method of the high-strength steel comprises the following specific steps:
s1, reheating the pretreated steel: 1200-1240 ℃;
s2, a high-temperature and high-pressure process: the initial rolling temperature is 1000-1150 ℃, the accumulated rolling reduction is more than or equal to 60%, and the final rolling temperature is in the interval: performing water cooling treatment after rolling at 850-950 ℃;
s3, the quenching and tempering process comprises a quenching and tempering process:
(1) Quenching process, wherein the quenching heating temperature is 920+/-5 ℃, and the heating coefficient is 1.4-1.5min/mm;
(2) And tempering, wherein the tempering temperature is 400-500 ℃, the tempering coefficient is 3.0min/mm, and the steel plate is cooled to room temperature after being taken out of the furnace.
2. A low compression ratio lamellar tearing resistant Q960 high strength steel in accordance with claim 1, characterized in that: comprises the following chemical components in percentage by weight: c:0.13-0.15%, si:0.15-0.50%, mn:1.40-1.60%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, mo:0.30-0.40%, cr:0.30-0.60%, ni:0.20-0.30%, V:0.05-0.06%, nb:0.025% -0.060%, alt:0.030% -0.060%, ti:0.020% -0.035%, B is less than or equal to 0.005%, N is less than or equal to 0.0070%, O is less than or equal to 0.0030%, H is less than or equal to 0.0002%, and the balance is Fe and unavoidable impurities.
3. The method for preparing the low-compression-ratio lamellar tearing resistant Q960 high-strength steel according to claim 1 or 2, which is characterized in that: the method comprises the following specific steps:
s1, reheating the pretreated steel: 1200-1240 ℃;
s2, a high-temperature and high-pressure process: the initial rolling temperature is 1000-1150 ℃, the accumulated rolling reduction is more than or equal to 60%, and the final rolling temperature is in the interval: performing water cooling treatment after rolling at 850-950 ℃;
s3, the quenching and tempering process comprises a quenching and tempering process:
(1) Quenching process, wherein the quenching heating temperature is 920+/-5 ℃, and the heating coefficient is 1.4-1.5min/mm;
(2) And tempering, wherein the tempering temperature is 400-500 ℃, the tempering coefficient is 3.0min/mm, and the steel plate is cooled to room temperature after being taken out of the furnace.
4. The method for preparing the lamellar tearing resistant Q960 high-strength steel with low compression ratio according to claim 3, which is characterized in that: in S1, the steel is initially heated at the following temperature: the heat preservation treatment is needed between the primary heating and the reheating treatment at the temperature of 1000-1200 ℃, the time point of maintaining the temperature is 1200 ℃, and the heat preservation time is 10-30 min.
5. The method for preparing the lamellar tearing resistant Q960 high-strength steel with low compression ratio according to claim 3, which is characterized in that: in S2, the cooling temperature is 300 ℃ to 400 ℃.
6. The method for preparing the lamellar tearing resistant Q960 high-strength steel with low compression ratio according to claim 3, which is characterized in that: in S3, the tempered steel sheet microstructure is tempered sorbite.
Applications Claiming Priority (2)
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59100214A (en) * | 1982-11-29 | 1984-06-09 | Nippon Kokan Kk <Nkk> | Production of thick walled high tension steel |
| JP2000319726A (en) * | 1999-03-11 | 2000-11-21 | Sumitomo Metal Ind Ltd | Manufacture of high strength steel plate excellent in weldability |
| CN102392192A (en) * | 2011-11-01 | 2012-03-28 | 南京钢铁股份有限公司 | Steel plate with thickness of 80mm and low compression ratio for ocean engineering and manufacturing method thereof |
| CN108642390A (en) * | 2018-05-30 | 2018-10-12 | 武汉钢铁有限公司 | The high-strength steel plate and production method of a kind of thickness directional properties Z 35 ~ 50% |
| EP3467136A1 (en) * | 2016-08-31 | 2019-04-10 | Nanjing Iron&Steel Co., Ltd. | Large-thickness q960e ultra-high strength steel production method |
| CN110423946A (en) * | 2019-09-02 | 2019-11-08 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of low compression ratio super-high strength steel Q960E special heavy plate |
| WO2020062564A1 (en) * | 2018-09-29 | 2020-04-02 | 南京钢铁股份有限公司 | Ultrahigh-steel q960e slab and manufacturing method |
| CN112143958A (en) * | 2019-06-27 | 2020-12-29 | 宝山钢铁股份有限公司 | 1000 MPa-grade steel plate with super-thick, super-high toughness and excellent weldability and manufacturing method thereof |
| CN113832387A (en) * | 2020-06-23 | 2021-12-24 | 宝山钢铁股份有限公司 | Low-cost ultra-thick 1000 MPa-grade steel plate and manufacturing method thereof |
-
2022
- 2022-08-03 CN CN202210925769.9A patent/CN115216701B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59100214A (en) * | 1982-11-29 | 1984-06-09 | Nippon Kokan Kk <Nkk> | Production of thick walled high tension steel |
| JP2000319726A (en) * | 1999-03-11 | 2000-11-21 | Sumitomo Metal Ind Ltd | Manufacture of high strength steel plate excellent in weldability |
| CN102392192A (en) * | 2011-11-01 | 2012-03-28 | 南京钢铁股份有限公司 | Steel plate with thickness of 80mm and low compression ratio for ocean engineering and manufacturing method thereof |
| EP3467136A1 (en) * | 2016-08-31 | 2019-04-10 | Nanjing Iron&Steel Co., Ltd. | Large-thickness q960e ultra-high strength steel production method |
| CN108642390A (en) * | 2018-05-30 | 2018-10-12 | 武汉钢铁有限公司 | The high-strength steel plate and production method of a kind of thickness directional properties Z 35 ~ 50% |
| WO2020062564A1 (en) * | 2018-09-29 | 2020-04-02 | 南京钢铁股份有限公司 | Ultrahigh-steel q960e slab and manufacturing method |
| CN112143958A (en) * | 2019-06-27 | 2020-12-29 | 宝山钢铁股份有限公司 | 1000 MPa-grade steel plate with super-thick, super-high toughness and excellent weldability and manufacturing method thereof |
| CN110423946A (en) * | 2019-09-02 | 2019-11-08 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of low compression ratio super-high strength steel Q960E special heavy plate |
| CN113832387A (en) * | 2020-06-23 | 2021-12-24 | 宝山钢铁股份有限公司 | Low-cost ultra-thick 1000 MPa-grade steel plate and manufacturing method thereof |
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