CN111304538A - Low-cost hot-rolled ultrahigh-strength steel and manufacturing method thereof - Google Patents
Low-cost hot-rolled ultrahigh-strength steel and manufacturing method thereof Download PDFInfo
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- CN111304538A CN111304538A CN202010242140.5A CN202010242140A CN111304538A CN 111304538 A CN111304538 A CN 111304538A CN 202010242140 A CN202010242140 A CN 202010242140A CN 111304538 A CN111304538 A CN 111304538A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
Abstract
The invention discloses a low-cost hot-rolled ultrahigh-strength steel and a manufacturing method thereof, wherein the steel comprises the following chemical components in percentage by weight: c: 0.08-0.11, Si is less than or equal to 0.05, Mn: 1.95-2.30, P: less than or equal to 0.020 and S: less than or equal to 0.006, Ti: 0.14 to 0.20 percent of the total weight of the alloy, 0.0041 to 0.0060 percent of B, less than or equal to 0.20 percent of Ti + B, and the balance of iron and inevitable impurities. The specific production process flow sequentially comprises the following steps: blast furnace molten iron and molten iron desulphurization, converter smelting, argon blowing, LF external refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing. The thickness of the low-cost hot-rolled ultrahigh-strength steel prepared by the method is 10-16 mm. The yield strength of the steel is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation percentage A is50≥20％，AKVNot less than 150J (-20 deg.C), high strength, high toughness, high welding performance and low cost.
Description
Technical Field
The invention relates to hot-rolled ultrahigh-strength steel with the thickness of 10-16 mm, belongs to the field of low-alloy ultrahigh-strength steel manufacturing, and is mainly used for manufacturing large-tonnage crane chassis and engineering components such as bottom beams of heavy truck dumper trucks and the like.
Background
With the progress of metallurgy and manufacturing technology, the yield strength of 55-ton and 70-ton crane chassis is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation A is higher than or equal to 10-16 mm50The hot-rolled ultrahigh-strength steel is more than or equal to 14 percent, the rigidity of the chassis of the crane is ensured, the self weight of the chassis is reduced, and the purpose of lightening the chassis is achieved. The design of the prior patent is no exception, the strength is improved by adding two or more of a large number of noble alloy elements Nb, Cr, Ni and Mo, so that the production cost is high, and the design idea greatly improves the cost and also influences the popularization and the use of thick hot-rolled ultrahigh-strength steel. Therefore, a low-cost hot-rolled ultrahigh-strength steel is required to make up for the above disadvantages.
Disclosure of Invention
Based on the defects of the prior art, the technical problem to be solved by the invention is to provide the low-cost hot-rolled ultrahigh-strength steel and the manufacturing method thereof, the high-Ti component design is adopted, the oxide metallurgy technology and the ultra-fast cooling technology are combined, the comprehensive matching of the obdurability, the formability and the weldability is realized on the basis of low cost, and a brand new thought is provided for the preparation of the low-cost high-performance large-tonnage crane chassis.
In order to solve the technical problems, the invention provides low-cost hot-rolled ultrahigh-strength steel, which comprises the following chemical components in percentage by weight: c: 0.08-0.11, Si is less than or equal to 0.05, Mn: 1.95-2.30, P: less than or equal to 0.020 and S: less than or equal to 0.006, Ti: 0.14 to 0.20 percent of the total weight of the alloy, 0.0041 to 0.0060 percent of B, less than or equal to 0.20 percent of Ti + B, and the balance of iron and inevitable impurities.
Preferably, the low-cost hot-rolled ultrahigh-strength steel further comprises part or all of the following technical characteristics:
as an improvement of the above technical solution, preferably, the steel comprises the following chemical components in percentage by weight (%): c: 0.085-0.10, Si 0.02-0.05, Mn: 1.95-2.20, P: less than or equal to 0.017, S: less than or equal to 0.003, Ti: 0.15 to 0.19, 0.0045 to 0.0050 of B, less than or equal to 0.19 of Ti + B, and the balance of Fe and inevitable impurities.
As an improvement of the above technical solution, preferably, the steel comprises the following chemical components in percentage by weight (%): c: 0.090-0.10, Si 0.02-0.05, Mn: 2.00-2.15, P: less than or equal to 0.015, S: less than or equal to 0.002, Ti: 0.16 to 0.19, 0.0045 to 0.0048 of B, less than or equal to 0.19 of Ti + B, and the balance of Fe and inevitable impurities.
As an improvement of the technical scheme, the thickness of the low-cost hot-rolled ultrahigh-strength steel is 10-16 mm, the yield strength is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation percentage A is50≥20％，AKV(-20℃)≥150J。
A manufacturing method of low-cost hot-rolled ultrahigh-strength steel comprises the following specific production process flows in sequence: blast furnace molten iron and molten iron desulphurization, converter smelting, argon blowing, LF external refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing; the method comprises the following key steps of:
(1) converter steelmaking and tapping alloying, wherein when molten steel reaches an LF furnace for refining, an oxide metallurgical technology is adopted, firstly, ferromanganese or ferrosilicon is added to control the oxygen content to be less than or equal to 150ppm, then, Zr iron and Ti iron are fed, the Zr iron is added according to 0.20-0.30 kg/t molten steel, the Ti iron is added according to an internal control target value molten steel, and oxide particles of Ti and Zr are controlled to be formed; fine and dispersed oxide particles are beneficial to promoting new phase nucleation, and can effectively pin and prevent austenite grains from growing and refine the grains at high temperature;
(2) rolling: firstly, heating a steel billet to fully austenitize; rolling in two stages, wherein the rolling start temperature of the stage I is controlled to be 1120-1270 ℃, the final rolling is 1050-1180 ℃, the cumulative reduction rate is more than or equal to 70%, the deformation of the material in a non-recrystallization austenite region is increased, the dislocation in the deformed austenite is increased, and austenite grains are refined; the initial rolling temperature of the rolling in the stage II is less than or equal to 940 ℃, and the final rolling temperature is 880-920 ℃;
(3) laminar cooling: an ultra-fast cooling control mode is adopted, the cooling speed is 70-100 ℃/s, and the coiling temperature is controlled at 520-560 ℃;
(4) leveling and finishing: and (4) flattening and finishing by adopting a powerful flattening device, and cutting into fixed-length plates or rewinding for delivery according to the contract requirements.
Preferably, the method for manufacturing low-cost hot-rolled ultrahigh-strength steel according to the present invention further includes some or all of the following technical features:
as an improvement of the technical scheme, in the control step (2), the billet is heated at 1150-1280 ℃.
As an improvement of the technical scheme, the thickness of the low-cost hot-rolled ultrahigh-strength steel is 10-16 mm.
As an improvement of the technical scheme, the yield strength of the low-cost hot-rolled ultrahigh-strength steel is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation percentage A is50≥20％，AKV(-20℃)≥150J。
The main alloying element content of the invention is based on the following principle:
c: c is an inexpensive solid-solution strengthening element. According to the application range of the steel grade, the steel grade is mainly used for processing parts such as large-tonnage crane chassis and the like, and needs to be subjected to stamping deformation processing to a greater degree, so that the material is required to have good cold forming performance while meeting the strength requirement. If the content is less than 0.08 percent, the requirement of material strength cannot be met; if the content thereof is more than 0.11%, good formability of the material cannot be satisfied. Therefore, the content of C in the steel is designed to be 0.08-0.11%.
Mn: the proper amount of Mn is added into the steel, so that the strength of the steel can be improved through the solid solution strengthening of Mn, the phase transition temperature of the steel can be reduced, the crystal grains are refined, and the comprehensive performance of the steel is improved, wherein the Mn content in the steel is designed to be 1.95-2.30%.
Si: the lower Si content is beneficial to improving the surface quality of steel, and the Si content in the steel is designed to be less than or equal to 0.05 percent.
P: in order to avoid deterioration of the weldability, press formability, toughness, and secondary workability of the material, the upper limit of the content is set to 0.020%. Therefore, the content of P in the steel is designed to be less than or equal to 0.020%.
S: s is a very harmful element. S in steel often exists in the form of sulfide of manganese, which is very disadvantageous in impact toughness of steel and causes anisotropy of properties, and therefore, it is desirable to control the sulfur content in steel as low as possible. Therefore, the S content in the steel of the present invention is designed to be 0.006% or less.
Ti is a ferrite forming element of Ti closed austenite region, Ti raises A3 point and lowers A4 point in Fe-Ti binary system, when W (Ti) is more than 0.72%, the austenite region is closed, Ti and C, N elements form high temperature resistant TiN, TiC and Ti (C, N) particles, which play a role of precipitation strengthening, pin at original austenite grain boundary and prevent austenite grain growth, TiC has a role of precipitation strengthening during ultra-fast cooling, Ti can slow down C diffusion in α phase during tempering, slow down Fe, Mn and other carbides precipitation and growth, increase tempering stability, and increase strength of the obtained steel by secondary precipitation of a small amount of TiC, TiN, Ti (C, N) particles formed during welding obviously prevent heat affected zone grain growth, improve welding performance, in addition, trace Zr iron is added during refining in a furnace, Ti and Zr can form Ti and Zr oxides, forming dispersed Ti and Zr distributed particles, N, ZrN, Zr (C, Zr) and Zr (C, Zr) particles are further improved, and the comprehensive strength of Ti-Ti alloy steel is improved by considering that the steel is formed in a state that Ti-Ti alloy steel plate with high comprehensive grain size distribution and Ti-Ti alloy.
Trace B can obviously improve the hardenability of the steel, refine the austenite in-crystal structure and contribute to obtaining the bainite structure required by high strength and high toughness, the steel of the invention avoids the boron brittleness phenomenon of a steel plate with over-high B element content in the cooling process by designing the B content in the range of 0.0041-0.0060%, and experiments show that the steel plate material of the invention can obtain higher tensile strength and yield strength under the condition of lower B element content.
Compared with the prior art, the technical scheme of the invention has the following beneficial effects: the invention is different from the design idea of the existing hot-rolled ultrahigh-strength steel, does not add noble alloy elements such as Nb, Cr, Ni and Mo, adopts the high-Ti micro-B component design, refines the tissue structure of the steel and controls the formation of oxide particles of Ti and Zr through the oxide metallurgy technology, promotes new phase nucleation, ensures that the steel has high strength, high toughness and high welding performance, and meets the manufacturing requirement of a large-tonnage crane chassis. The invention has the characteristics of low cost and excellent performance.
The invention has the advantages that the strength of the steel is improved by using cheap Ti and B, the crystal grains are refined by using an oxide metallurgy technology, the obdurability, the formability and the weldability of the steel are improved, the addition of a large amount of noble alloy elements such as Nb, Cr, Ni and Mo is avoided, and the cost is saved.
The preparation method provided by the invention is used for producing the low-cost hot-rolled ultrahigh-strength steel with the thickness of 10-16 mm by using an oxide smelting technology. The yield strength of the steel is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation percentage A is50≥20％，AKVNot less than 150J (-20 deg.C), high strength, high toughness, high welding performance and low cost.
The foregoing description is only an overview of the technical solutions of the present invention, and in order to make the technical means of the present invention more clearly understood, the present invention may be implemented in accordance with the contents of the description, and in order to make the above and other objects, features, and advantages of the present invention more clearly understood, the following detailed description is given in conjunction with the preferred embodiments.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings of the embodiments will be briefly described below.
FIG. 1 is a metallographic structure diagram of a low-cost hot-rolled ultrahigh-strength steel prepared in example 3 of the present invention, and the structure types are bainite + ferrite + pearlite.
Detailed Description
Other aspects, features and advantages of the present invention will become apparent from the following detailed description, which, when taken in conjunction with the drawings, illustrate by way of example the principles of the invention.
The present invention is described in detail below:
the embodiments of the invention are produced according to the following steps:
the method comprises the following steps:
(1) converter steelmaking and tapping alloying, when molten steel reaches LF furnace refining, adopting oxide metallurgy technology, firstly adding ferromanganese or ferrosilicon to control the oxygen content to be less than or equal to 150ppm, then feeding Zr iron and Ti iron, adding Zr iron according to 0.20-0.30 kg/t molten steel, and adding Ti iron according to internal control target value molten steel.
(2) Rolling: firstly, heating a steel billet at 1150-1280 ℃ to fully austenitize. Then, rolling in two stages, wherein the rolling initial temperature of the stage I is controlled to be 1120-1270 ℃, the final rolling temperature is 1050-1180 ℃, and the cumulative reduction rate is more than or equal to 70%; the rolling initial temperature of the second stage is less than or equal to 940 ℃, and the final rolling temperature is 880-920 ℃.
(3) Laminar cooling: an ultra-fast cooling control mode is adopted, the cooling speed is 70-100 ℃/s, and the coiling temperature is controlled at 520-560 ℃.
(4) Leveling and finishing: and (4) flattening and finishing by adopting a powerful flattening device, and cutting into fixed-length plates or rewinding for delivery according to the contract requirements.
Table 1 chemical composition list of each example of the invention
Table 2 list of main process parameters of various embodiments of the present invention
TABLE 3 mechanical Property test results List of the various embodiments of the present invention
As can be seen from Table 1, the steel of the present invention greatly reduces the alloy cost by adopting the high Ti micro B component design and the oxide metallurgy technology in the component design; as shown in Table 3, the mechanical property detection results of the steel of the invention in the embodiments show that the steel of the invention has excellent mechanical properties, welding properties and forming properties under the condition of ensuring low cost, fully embodies the advantages of the steel of the invention adopting high Ti content and micro B content design and oxide metallurgy technology, and has extremely high popularization value.
The raw materials listed in the invention, the upper and lower limits and interval values of the raw materials of the invention, and the upper and lower limits and interval values of the process parameters (such as temperature, time and the like) can all realize the invention, and the examples are not listed.
While the foregoing is directed to the preferred embodiment of the present invention, other and further embodiments of the invention may be devised without departing from the basic scope thereof, and the scope thereof is determined by the claims that follow.
Claims (8)
1. A low-cost hot-rolled ultrahigh-strength steel is characterized in that: the steel comprises the following chemical components in percentage by weight (%): c: 0.08-0.11, Si is less than or equal to 0.05, Mn: 1.95-2.30, P: less than or equal to 0.020 and S: less than or equal to 0.006, Ti: 0.14 to 0.20 percent of the total weight of the alloy, 0.0041 to 0.0060 percent of B, less than or equal to 0.20 percent of Ti + B, and the balance of iron and inevitable impurities.
2. The low-cost hot-rolled ultrahigh strength steel according to claim 1, characterized in that: preferably, the steel comprises the following chemical components in percentage by weight (%): c: 0.085-0.10, Si 0.02-0.05, Mn: 1.95-2.20, P: less than or equal to 0.017, S: less than or equal to 0.003, Ti: 0.15 to 0.19, 0.0045 to 0.0050 of B, less than or equal to 0.19 of Ti + B, and the balance of Fe and inevitable impurities.
3. The low-cost hot-rolled ultrahigh strength steel according to claim 1, characterized in that: preferably, the steel comprises the following chemical components in percentage by weight (%): c: 0.090-0.10, Si 0.02-0.05, Mn: 2.00-2.15, P: less than or equal to 0.015, S: less than or equal to 0.002, Ti: 0.16 to 0.19, 0.0045 to 0.0048 of B, less than or equal to 0.19 of Ti + B, and the balance of Fe and inevitable impurities.
4. The low-cost hot-rolled ultrahigh strength steel according to claim 1, characterized in that: the thickness of the low-cost hot-rolled ultrahigh-strength steel is 10-16 mm, the yield strength is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation A50≥20％，AKV(-20℃)≥150J。
5. A manufacturing method of low-cost hot-rolled ultrahigh-strength steel is characterized by comprising the following steps: the specific production process flow sequentially comprises the following steps: blast furnace molten iron and molten iron desulphurization, converter smelting, argon blowing, LF external refining, continuous casting, hot charging and hot conveying, heating, rolling, laminar cooling, coiling, flattening and finishing; the method comprises the following key steps of:
(1) converter steelmaking and tapping alloying, when molten steel reaches LF furnace refining, adopting oxide metallurgy technology, firstly adding ferromanganese or ferrosilicon to control the oxygen content to be less than or equal to 150ppm, then feeding Zr iron and Ti iron, adding Zr iron according to 0.20-0.30 kg/t molten steel, adding Ti iron according to internal control target value molten steel, and controlling to form oxide particles of Ti and Zr
(2) Rolling: firstly, heating a steel billet; then, rolling in two stages, wherein the rolling initial temperature of the stage I is controlled to be 1120-1270 ℃, the final rolling temperature is 1050-1180 ℃, and the cumulative reduction rate is more than or equal to 70%; the initial rolling temperature of the rolling in the stage II is less than or equal to 940 ℃, and the final rolling temperature is 880-920 ℃;
(3) laminar cooling: an ultra-fast cooling control mode is adopted, the cooling speed is 70-100 ℃/s, and the coiling temperature is controlled at 520-560 ℃;
(4) leveling and finishing: and (4) flattening and finishing by adopting a powerful flattening device, and cutting into fixed-length plates or rewinding for delivery according to the contract requirements.
6. The method of manufacturing a low-cost hot-rolled ultrahigh strength steel according to claim 5, characterized by: in the control step (2), the billet is heated at 1150-1280 ℃.
7. The method of manufacturing a low-cost hot-rolled ultrahigh strength steel according to claim 5, characterized by: the thickness of the low-cost hot-rolled ultrahigh-strength steel is 10-16 mm.
8. The method of manufacturing a low-cost hot-rolled ultrahigh strength steel according to claim 5, characterized by: the yield strength of the low-cost hot-rolled ultrahigh-strength steel is more than or equal to 800MPa, the tensile strength is more than or equal to 850MPa, and the elongation percentage A is50≥20％，AKV(-20℃)≥150J。
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| JPS5329219A (en) * | 1976-08-31 | 1978-03-18 | Sumitomo Metal Ind Ltd | Production of high strength steel |
| JPS6213533A (en) * | 1985-07-09 | 1987-01-22 | Nippon Steel Corp | Manufacture of high strength steel sheet having superior bending characteristic |
| JPS6293005A (en) * | 1985-10-18 | 1987-04-28 | Kobe Steel Ltd | Production of high strength hot rolled steel sheet |
| JPH0819461B2 (en) * | 1988-12-09 | 1996-02-28 | 新日本製鐵株式会社 | High-tensile steel plate manufacturing method |
| TW201425597A (en) * | 2012-12-24 | 2014-07-01 | Nippon Steel & Sumitomo Metal Corp | Hot-rolled steel sheet and manufacturing method thereof |
| JP2018095904A (en) * | 2016-12-12 | 2018-06-21 | Ｊｆｅスチール株式会社 | Manufacturing method of hot rolled steel sheet for rectangular steel pipe with low yield ratio and manufacturing method of rectangular steel pipe with low yield ratio |
| CN110066966A (en) * | 2019-05-22 | 2019-07-30 | 武汉钢铁有限公司 | A kind of low internal stress titaniferous high-strength steel and production method |
| CN110106322A (en) * | 2019-05-22 | 2019-08-09 | 武汉钢铁有限公司 | A kind of thin gauge engineering machinery high-strength steel and board-shape control method |
| CN110284053A (en) * | 2019-04-30 | 2019-09-27 | 武汉钢铁有限公司 | A kind of high P high-strength tenacity high-weatherability hot continuous rolling steel and its manufacturing method |
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2020
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5329219A (en) * | 1976-08-31 | 1978-03-18 | Sumitomo Metal Ind Ltd | Production of high strength steel |
| JPS6213533A (en) * | 1985-07-09 | 1987-01-22 | Nippon Steel Corp | Manufacture of high strength steel sheet having superior bending characteristic |
| JPS6293005A (en) * | 1985-10-18 | 1987-04-28 | Kobe Steel Ltd | Production of high strength hot rolled steel sheet |
| JPH0819461B2 (en) * | 1988-12-09 | 1996-02-28 | 新日本製鐵株式会社 | High-tensile steel plate manufacturing method |
| TW201425597A (en) * | 2012-12-24 | 2014-07-01 | Nippon Steel & Sumitomo Metal Corp | Hot-rolled steel sheet and manufacturing method thereof |
| JP2018095904A (en) * | 2016-12-12 | 2018-06-21 | Ｊｆｅスチール株式会社 | Manufacturing method of hot rolled steel sheet for rectangular steel pipe with low yield ratio and manufacturing method of rectangular steel pipe with low yield ratio |
| CN110284053A (en) * | 2019-04-30 | 2019-09-27 | 武汉钢铁有限公司 | A kind of high P high-strength tenacity high-weatherability hot continuous rolling steel and its manufacturing method |
| CN110066966A (en) * | 2019-05-22 | 2019-07-30 | 武汉钢铁有限公司 | A kind of low internal stress titaniferous high-strength steel and production method |
| CN110106322A (en) * | 2019-05-22 | 2019-08-09 | 武汉钢铁有限公司 | A kind of thin gauge engineering machinery high-strength steel and board-shape control method |
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Application publication date: 20200619 |
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