CN112779472B - 1GPa grade steel plate with excellent low-temperature toughness for ocean engineering and preparation method thereof - Google Patents
1GPa grade steel plate with excellent low-temperature toughness for ocean engineering and preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- 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
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- C21D8/0226—Hot rolling
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- 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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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention belongs to the field of steel material preparation, and discloses a 1GPa grade steel plate with excellent low-temperature toughness for ocean engineering and a preparation method thereof. The steel plate has the characteristics of ultrahigh strength (the yield strength is more than or equal to 1GPa), low yield ratio (less than 0.94) and excellent low-temperature toughness (the impact energy at minus 80 ℃ is more than or equal to 150J).
Description
Technical Field
The invention belongs to the field of steel material preparation, and particularly relates to a steel plate for ocean engineering, which has the characteristics of low yield ratio, excellent low-temperature impact toughness and 1 GPa-grade ultrahigh strength, and a preparation method thereof.
Background
The vast oceans contain abundant resources, and in order to develop and utilize ocean resources, human beings continuously develop and promote the technical level of ocean engineering equipment. Steel is the most important and irreplaceable material for manufacturing marine equipment. However, the marine environment is very complex, and ships and marine engineering equipment are in service in severe marine environments such as sea waves, sea tides, storms, cold running ice and the like, and the safety of the marine equipment is required to be ensured by the comprehensive properties such as high strength, low-temperature toughness, low yield ratio and the like of the steel for marine engineering. In recent years, although the application of ultra-high strength steel in the field of high-end marine equipment manufacturing is increasing, high strength brings higher yield ratio and poorer impact toughness, and the development of high-end manufacturing industry is limited. Therefore, it is important not only to increase the strength but also to decrease the yield ratio and improve the low-temperature toughness.
At present, the yield strength grade of the traditional steel for the ultrahigh-strength ocean engineering is from 550MPa to 960MPa, and a tempered martensite microstructure is formed by adopting a quenching and tempering production process. The steel for the current ultrahigh strength ocean engineering has the following defects: (1) the yield ratio of the steel plate with the tempered martensite as the characteristic structure is increased along with the yield increase is continuously close to 1, and the use safety of the material is seriously influenced; (2) the steel for ocean engineering above 890MPa level has insufficient low-temperature toughness, and cannot meet the construction of ocean engineering projects in extremely cold regions; (3) the construction of advanced marine equipment requires higher-strength steel for marine engineering, and the yield strength needs to be further improved to be above 1GPa grade. Therefore, how to simultaneously obtain the ultrahigh strength, the low yield ratio characteristic and the excellent low-temperature toughness of the grade of 1GPa is the main direction of the development of the steel for ocean engineering in the future.
The invention patent with publication number CN109161791B proposes a 690MPa grade steel for ships and ocean engineering with excellent low-temperature toughness and a manufacturing method thereof. The alloy comprises Cu less than or equal to 0.5 percent, Ti: 0.005-0.05%, Ni: 1.0-2.5%, and quenching and tempering, or normalizing, quenching and tempering, or tempering, quenching and tempering, wherein the temperature control precision is high. In addition, the yield strength of the steel plate developed by the production process is lower than 1GPa, and the low-temperature impact toughness at minus 80 ℃ is insufficient.
The invention patent with publication number CN102618793B provides a steel plate with yield strength of 960MPa grade and a manufacturing method thereof. The alloy composition contains Nb: 0.02-0.06%, Ti: 0.003-0.04%, B: 0.0006 to 0.0025 percent and adopts a controlled rolling, controlled cooling and on-line tempering process. The steel plate produced by the technology has a yield ratio of more than 0.94 and insufficient low-temperature impact toughness at-80 ℃.
The publication number CN111057965A provides a low-yield-ratio steel for ocean engineering and a preparation method thereof. The patent component is added with Cu: 1.4-1.5%, and microalloying element Nb: 0.01-0.03%, Ti: 0.008-0.018%, long production period and high production cost due to the adoption of multiple quenching and tempering heat treatment processes. In addition, the yield strength of the ultrahigh-strength steel produced by the technology is lower than 1 GPa.
Publication No. CN111542636A proposes a high-strength steel material having excellent low yield ratio characteristics and a method for producing the same. The patent component is added with microalloy element Nb: 0.01-0.05%, and adopts multi-stage cooling, and the process is complicated. In addition, the yield strength of the steel plate produced by the technology is lower than 1 GPa.
Disclosure of Invention
The invention provides a 1GPa grade steel plate for ocean engineering with low yield ratio characteristic and excellent low-temperature toughness and a preparation method thereof, wherein the steel plate has ultrahigh yield strength (more than or equal to 1GPa), low yield ratio (the yield ratio is less than 0.94) and excellent low-temperature toughness (the impact energy at minus 80 ℃ is more than or equal to 150J) by alloy optimization and rolling and multi-step heat treatment process regulation and control of the microstructure and the grain size of the steel plate.
The invention carries out a great deal of systematic experimental research on the aspects of alloy element content, steel cleanliness control, process optimization and parameter selection, microstructure control and the like, and finally determines the alloy element proportion and the preparation process which can meet the aim of the invention.
The steel plate for 1GPa grade ocean engineering with low yield ratio and excellent low-temperature toughness comprises the following chemical components in percentage by weight: 0.08-0.13%, Si: 0.20 to 0.50%, Mn: 0.70-1.50%, Ni: 6.50-8.50%, Cr: 0.40-0.60%, Mo: 0.50-0.90%, V: 0.05-0.09%, P: less than or equal to 0.003 percent, S: less than or equal to 0.002 percent, and the balance of Fe and inevitable impurities.
The preparation method of the steel plate adopts a rolling and on-line quenching process, and then carries out a multi-step heat treatment process on the steel plate, wherein the yield strength of the steel plate is more than or equal to 1GPa, the yield ratio is less than 0.94, and the impact energy at minus 80 ℃ is more than or equal to 150J. The multiphase microstructure is tempered martensite, fine metastable austenite and VC second phase.
The thickness range of the steel plate finished product is 10-50 mm.
The preparation process of the steel plate for the 1GPa grade ocean engineering comprises the following steps:
s1, preparing to carry out smelting and continuous casting according to chemical components of the steel to obtain a continuous casting billet, and carrying out LF and RH refining furnace treatment, wherein the superheat degree of the tundish molten steel is less than or equal to 20 ℃, and the whole process is protected for casting;
s2, heating the continuous casting slab to 1100-1150 ℃, and preserving heat for 2-3 h;
s3, carrying out high-temperature rolling on the continuous casting billet, wherein the rolling temperature is an austenite recrystallization temperature region of 1050-950 ℃, so that austenite grains are refined, the phase transformation nucleation rate is improved, and the purpose of refining the grains is achieved;
s4, adopting a rapid cooling system with the average cooling speed of more than 20 ℃/S for the steel plate processed in the step S3, and controlling the final cooling temperature to be below 200 ℃;
and S5, processing the steel plate by adopting a two-step heat treatment process.
In step S1, the time for the LF refining furnace treatment and the RH refining furnace treatment is respectively 20-30 min; the temperature of the superheat degree of the tundish molten steel is 10-20 ℃.
In step S1, the non-metallic inclusions of a, i.e., sulfides, B, i.e., aluminas, C, i.e., silicates, D, i.e., spherical oxides, in the fully protective cast steel satisfy: a is less than or equal to 0.5, B is less than or equal to 0.5, C is less than or equal to 0.5, and D is less than or equal to 0.5.
In step S3, the average single pass reduction is 15% or more in the rolling process in order to sufficiently recrystallize austenite and refine austenite grain size.
In step S4, the average cooling speed is 20-30 ℃/S; the final cooling temperature is 30-200 ℃. In step S5, the heat treatment process includes: the first step of critical heat treatment, wherein the critical heat treatment range is Ac 1-Ac 3, the temperature is 700-720 ℃, and the heat preservation time coefficient is as follows: 1.0-1.2 min/mm, and adopting water cooling in a cooling mode; and a second step of critical heat treatment, wherein the critical heat treatment range is Ac 1-Ac 3, the temperature is 520-560 ℃, and the heat preservation time coefficient is as follows: 2.0-2.5 min/mm, and adopting air cooling for cooling.
The mechanism of action of the alloy components in the steel according to the invention is illustrated below, wherein the% symbols represent the weight percentages:
c: is an essential element for ensuring the strength, has obvious effect on improving the strength of the steel through solid solution strengthening and precipitation strengthening, but has negative influence on the ductility and toughness of the steel, particularly the weldability through excessively high C content. From the viewpoint of economy and product performance, the C content is preferably controlled to 0.08-0.13%.
Si: is one of main elements for improving the strength, and simultaneously, the addition of Si can inhibit the formation of bainite, inhibit the precipitation and coarsening of cementite and improve the toughness, so that the content of Si is preferably 0.20-0.50%.
Mn: the Mn content is 0.70-1.50% in order to improve the toughness of the material.
P: the P is an element which brings adverse effects on low-temperature toughness and ductility, can be segregated in the central part of a slab, is aggregated in a grain boundary and the like to damage the low-temperature toughness, and is controlled to be not higher than 0.003 percent.
S: the S-containing rare earth-iron-based alloy material is an element which brings adverse effects on low-temperature toughness and ductility, can form sulfide inclusions and become a crack source, and the S content of the material is controlled to be not higher than 0.002%.
Ni: the alloy has the solid solution strengthening effect, stabilizes main alloy elements of austenite, reduces an Ar3 point, shifts a CCT curve to the right, can form a martensite structure with small size, and improves the obdurability, particularly the low-temperature toughness of steel; and because Ni can influence the transverse slip of dislocation and reduce the ductile-brittle transition temperature of steel, and the other important function is to promote the formation of metastable austenite and increase the stability of the metastable austenite, the Ni content is controlled to be 6.50-8.50%.
Mo: the element for improving hardenability expands a gamma phase region, plays an important role in controlling a phase change structure and can effectively improve the strength of the material; the phase transition temperature is reduced, the critical cooling rate of bainite transformation is reduced, the stability of the strength and toughness performance of the steel plate in the thickness direction can be effectively improved, and the Mo content is controlled to be 0.50-0.90%.
V: the grain size of the steel is effectively refined, and meanwhile, the strength is remarkably improved under the action of forming a nanoscale second phase and dislocation in the steel. A large number of experiments prove that the strength of the steel can be effectively improved by the V content of 0.05-0.09%.
In the chemical components, a large amount of martensite structures can be formed due to too high contents of C, Si, Mn and Mo, so that precipitation of bainite structures is influenced, and finally toughness performance of the steel plate is influenced; too low content will affect the insufficient strength of the steel plate. The proper combination of Ni, Cr and V improves the strength and low-temperature toughness of the steel plate.
(1) The weldability of the steel plate is ensured by low C content, the high Ni content is added to promote the formation of metastable austenite and improve the stability of the metastable austenite, and a nano-sized precipitated phase (VC) can be formed by adding a microalloy element V to improve the strength; the sulfur and phosphorus content is controlled, and the influence of impurities on low-temperature toughness is reduced. By adopting a rolling and on-line quenching method and a multi-step heat treatment process, particularly a critical zone quenching and tempering process, a metastable austenite and tempered martensite structure is finally obtained, and the yield ratio of the steel can be greatly reduced; the strength of the steel can be obviously improved through the VC precipitated phase precipitated after tempering. The high-performance steel for ocean engineering can be obtained by combining chemical components and a preparation process.
(2) The yield strength of the steel plate is more than or equal to 1GPa, the yield ratio is less than 0.94, and the impact energy at minus 80 ℃ is more than or equal to 150J.
(3) The manufacturing process of the product is easy to realize, the product performance is stable, and the yield is high.
Detailed Description
The chemical components of the steel of the embodiment of the invention are shown in Table 1, the steel smelting process of the embodiment of the invention is shown in Table 2, the steel rolling process of the embodiment of the invention is shown in Table 3, the heat treatment process is shown in Table 4, and the mechanical properties are shown in Table 5.
TABLE 1 chemical composition of steel of examples of the invention
| Examples | C | Si | Mn | P | S | Cr | Ni | Mo | V |
| 1 | 0.08 | 0.40 | 1.42 | 0.002 | 0.001 | 0.55 | 6.50 | 0.50 | 0.05 |
| 2 | 0.10 | 0.25 | 1.33 | 0.002 | 0.001 | 0.40 | 7.80 | 0.65 | 0.08 |
| 3 | 0.13 | 0.20 | 0.70 | 0.001 | 0.001 | 0.44 | 8.20 | 0.90 | 0.09 |
| 4 | 0.09 | 0.38 | 0.85 | 0.002 | 0.001 | 0.60 | 8.50 | 0.87 | 0.06 |
| 5 | 0.11 | 0.45 | 1.16 | 0.001 | 0.001 | 0.58 | 6.90 | 0.79 | 0.07 |
| 6 | 0.09 | 0.50 | 0.98 | 0.001 | 0.001 | 0.46 | 7.40 | 0.64 | 0.08 |
| 7 | 0.08 | 0.37 | 1.50 | 0.001 | 0.001 | 0.57 | 8.10 | 0.88 | 0.09 |
| 8 | 0.12 | 0.29 | 1.25 | 0.001 | 0.001 | 0.43 | 7.50 | 0.73 | 0.07 |
TABLE 2 Steel smelting Process according to the invention
Table 3 steel rolling and cooling process of examples of the invention
TABLE 4 Multi-step Heat treatment Process for Steel of examples of the present invention
TABLE 5 mechanical Properties of steels according to examples of the invention
Claims (7)
1. A preparation process of a 1GPa grade steel plate with excellent low-temperature toughness for ocean engineering is characterized in that the steel plate comprises the following chemical components in percentage by weight: 0.08-0.13%, Si: 0.20 to 0.50%, Mn: 0.70-1.50%, Ni: 6.50-8.50%, Cr: 0.40-0.60%, Mo: 0.50-0.90%, V: 0.05-0.09%, P: less than or equal to 0.003 percent, S: less than or equal to 0.002 percent, and the balance of Fe and inevitable impurities; the yield strength of the steel plate is more than or equal to 1GPa, the yield ratio is less than 0.94, and the impact energy at minus 80 ℃ is more than or equal to 150J;
the preparation process of the steel plate adopts a rolling and on-line quenching process, and then the steel plate is subjected to a two-step heat treatment process, wherein the multiphase microstructure comprises tempered martensite, fine metastable austenite and VC second phase; the method comprises the following specific steps:
s1, preparing to carry out smelting and continuous casting according to chemical components of the steel to obtain a continuous casting billet, and carrying out LF and RH refining furnace treatment, wherein the superheat degree of the tundish molten steel is less than or equal to 20 ℃, and the whole process is protected for casting;
s2, heating the continuous casting slab to 1100-1150 ℃, and preserving heat for 2-3 h;
s3, rolling the continuous casting blank at a high temperature, wherein the rolling temperature is an austenite recrystallization temperature region of 1050-950 ℃;
s4, adopting a rapid cooling system with the average cooling speed of more than 20 ℃/S for the steel plate processed in the step S3, and controlling the final cooling temperature to be below 200 ℃;
and S5, processing the steel plate by adopting a two-step heat treatment process.
2. The preparation process according to claim 1, wherein the thickness of the finished steel plate is 10-50 mm.
3. The preparation process of claim 1, wherein in step S1, the time for the LF and RH refining furnace treatment is 20 to 30min each; the temperature of the superheat degree of the tundish molten steel is 10-20 ℃.
4. The production process according to claim 1, wherein in step S1, the non-metallic inclusions of a that is sulfides, B that is alumina, C that is silicates, D that is spherical oxides in the fully protective cast steel satisfy: a is less than or equal to 0.5, B is less than or equal to 0.5, C is less than or equal to 0.5, and D is less than or equal to 0.5.
5. The process according to claim 1, wherein in step S3, the average single pass reduction during rolling is 15% or more.
6. The preparation process according to claim 1, wherein in step S4, the average cooling rate is 20 to 30 ℃/S; the final cooling temperature is 30-200 ℃.
7. The production process according to claim 1, wherein in step S5, the heat treatment process includes: the first step of critical heat treatment, wherein the critical heat treatment range is Ac 1-Ac 3, the temperature is 700-720 ℃, and the heat preservation time coefficient is as follows: 1.0-1.2 min/mm, and adopting water cooling in a cooling mode; and a second step of critical heat treatment, wherein the critical heat treatment range is Ac 1-Ac 3, the temperature is 520-560 ℃, and the heat preservation time coefficient is as follows: 2.0-2.5 min/mm, and adopting air cooling for cooling.
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| CN115074630B (en) * | 2022-07-01 | 2023-05-16 | 鞍钢股份有限公司 | FH36 grade ocean engineering steel with high ductility and manufacturing method |
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