CN114892075A - Low-temperature L-shaped steel and preparation method thereof - Google Patents
Low-temperature L-shaped steel and preparation method thereof Download PDFInfo
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
- B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/001—Heat treatment of ferrous alloys containing Ni
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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Abstract
The invention discloses low-temperature L-shaped steel and a preparation method thereof, wherein the low-temperature L-shaped steel comprises the following chemical components in percentage by mass: c: 0.01-0.021%, Si: 0.65-0.80%, Mn: 0.20-0.50%, P is less than or equal to 0.01%, S is less than or equal to 0.006%, Ni: 0.35-0.60%, Zr: 0.001-0.01%, O: 0.001 to 0.01 percent of Fe and inevitable impurities, and the balance of Fe and inevitable impurities, wherein the preparation method comprises converter smelting, furnace external electric furnace refining, RH vacuum refining, continuous casting, rolling, cooling stacking after rolling and small-line energy welding, and the prepared low-temperature L-shaped steel has excellent small-line energy welding performance, the yield strength of 320-430MPa and the low-temperature impact toughness of-90 ℃ KV 2 The Vickers hardness of a heat affected zone of the small linear energy welding joint is not more than 90J, and not more than 345Hv10, so that the method can be used for building structural members such as keels, reinforcing ribs and the like of high-technology low-temperature ships such as LPG, liquid ammonia and the like, and is safe, reliable and remarkable in economic benefit.
Description
Technical Field
The invention relates to steel and a preparation method thereof, in particular to low-temperature L-shaped steel and a preparation method thereof.
Background
At present, most of the flat-bulb steels and L-shaped steels used for building keel and reinforcing rib of ships are A, B, D-grade steels and AH32, DH32, AH36, DH36 specified by classification society, generally delivered in a hot rolling state, the impact toughness at the temperature of-20 ℃ is guaranteed at the lowest, the impact toughness at lower ambient temperature cannot be guaranteed, and the hardenability of a heat-affected zone of a welding joint in a small-line energy (the welding line energy is 8-15kJ/cm) welding process is obvious due to the high carbon (C) content and the high carbon equivalent (Ceq ═ C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15) level of the common steels, so that a martensite structure is easily formed, and the welding joint is easy to crack and even break. The basic mechanical property and welding property requirements of high-technology low-temperature ships such as liquefied petroleum gas and liquid ammonia for transporting the section steel (L character lattice, flat-bulb steel and the like) are higher, the yield strength ReH is required to be controlled within the range of 315-440MPa, the low-temperature impact energy at-60 ℃ is more than or equal to 41J, the Vickers of a small-linear energy welding joint is less than or equal to 350Hv10, and the low-technology low-temperature ships cannot be built by A, B, D-grade steel grades AH32, DH32, AH36, DH36 and the like.
The Chinese patent application No. 202110457270.5 discloses a low-temperature steel bar and a production method thereof, wherein the steel bar comprises the following chemical components in percentage by mass: 0.8 to 0.9 percent of Ni, 1.6 to 1.7 percent of Mn, 0.3 to 0.4 percent of Si, 0.04 to 0.08 percent of C, 0.01 to 0.02 percent of Al, less than or equal to 0.007 percent of P, less than or equal to 0.004 percent of S, less than or equal to 0.002 percent of O, less than or equal to 0.003 percent of N, less than or equal to 0.005 percent of As, less than or equal to 0.0002 percent of H, and the balance of Fe and inevitable impurities. The steel provided by the patent technology has high Ni content and relatively high production cost, is not an economic steel grade, and the production method is only suitable for long steel bars. The Chinese patent application No. 202010765914.2 discloses an economical low-temperature steel pipe with good corrosion resistance and a manufacturing method thereof, wherein the steel pipe comprises the following components in percentage by weight: 0.09% -0.12% of C, 0.25% -0.33% of Si, 1.10% -1.29% of Mn, 0.015% -0.03% of Ti, 0.01% -0.024% of Al, less than or equal to 0.012% of P, less than or equal to 0.008% of S, and less than or equal to 0.22% of carbon equivalent CEPcm, wherein the CEPcm is (C + Si/30+ Mn/20+ Cu/20+ Ni/60+ Cr/20+ Mo/15+ V/10+5B), and the manufacturing method comprises converter smelting, external refining, square billet continuous casting, cooling to room temperature and then heating in a heating furnace, tube billet continuous rolling, reheating, continuous rolling of tubes, sizing and heat treatment. The steel grade described in the patent technology can only be used in the low temperature environment of 45 ℃ and the hydrogen sulfide corrosion environment, the production process is complex, the process parameters are difficult to control, and the steel grade is only used for manufacturing the pipe.
Disclosure of Invention
The purpose of the invention is as follows: in order to solve the technical problems in the prior art, the invention aims to provide low-temperature L-shaped steel with low production cost and simple production process, and the invention also provides a preparation method of the low-temperature L-shaped steel.
The technical scheme is as follows: the low-temperature L-shaped steel comprises the following chemical components in percentage by mass: c: 0.01-0.021%, Si: 0.65-0.80%, Mn: 0.20-0.50%, P is less than or equal to 0.01%, S is less than or equal to 0.006%, Ni: 0.35-0.60%, Zr: 0.001-0.01%, O: 0.001-0.01%, and the balance of Fe and inevitable impurities.
Further, the mass percent of the Si is 0.65-0.70%.
Further, the mass percent of Mn is 0.35-0.45%.
Further, the mass percent of the Ni is 0.40-0.50%.
Furthermore, the metallographic structure of the low-temperature L-shaped steel is an acicular ferrite structure.
The principle of the main control alloy elements is explained as follows:
c (carbon): the content of C in the steel has great influence on mechanical property and welding property, and the invention mainly considers the small linear energy welding property, so that the content of C is controlled at a lower level, the hardenability tendency of a heat affected zone in the welding process is reduced, a martensite structure is not generated, cracks are avoided, and the content of C is set to be 0.01-0.021%.
Mn (manganese): the proper amount of Mn element is added into the low-temperature L-shaped steel to stabilize the high-temperature austenite structure and reduce the austeniteThe transformation temperature of the cementite inhibits the formation of high-temperature coarsened structure, and obtains fine metallographic structure and low-temperature impact toughness of-90 ℃ KV 2 Not less than 90J; on the other hand, if the Mn content level is too high, the hardenability tendency in the small heat input welding process is increased, so that the Mn content is set in the range of 0.2 to 0.5%.
P (phosphorus), S (sulfur): the residual P, S in the invention belongs to harmful elements, reduces the impact toughness and deteriorates the welding performance, but if P, S is controlled to be too low, the production cost is greatly increased, the content of P is controlled to be less than or equal to 0.01 percent, and the content of S is preferably controlled to be less than or equal to 0.006 percent.
Si (silicon): the invention mainly adds proper amount of alloy element Si to obtain proper yield strength, Si and Fe matrix form replacement solid solution strengthening to improve the strength, but too high Si content damages low temperature impact toughness, so the Si content is controlled in the range of 0.65-0.80%.
Ni (nickel): the alloy element Ni which is dissolved in the Fe matrix can obviously stabilize the austenite structure and reduce the transformation critical temperature, and the alloy element Ni and the Mn element act together to obtain a fine metallographic structure, thereby having excellent low-temperature impact toughness. Ni is a relatively expensive alloy element, and excessive addition increases the production cost, so the Ni content in the steel is controlled within the range of 0.35-0.60%.
Zr (zirconium), O (oxygen): the invention aims to form ZrO with fine particles in the steel grade during the manufacturing process by adding proper amount of Zr and controlling proper amount of O 2 A precipitated phase in which the acicular ferrite structure is nucleated by these particles during the weld cooling process, i.e. high temperature stable ZrO 2 The precipitated phase promotes the formation of a needle-shaped structure, and avoids the formation of a polygonal and coarse ferrite structure, thereby refining the metallographic structure of a welding heat affected zone and improving the welding performance of steel.
The preparation scheme of the low-temperature L-shaped steel comprises the following steps of:
(1) smelting in a converter, namely charging molten iron, scrap steel, MnFe, SiFe and NiFe alloy materials into an alkaline converter for smelting, blowing oxygen, raising the temperature, oxidizing and removing C, and adding CaO and FeO to remove P;
(2) performing electric furnace refining outside the furnace, adding high-quality lime to remove the S content until the S content is less than or equal to 0.005%, finely adjusting the Mn content and the Ni content in the molten steel to the required range by using a metal Mn plate and a metal Ni plate, and adjusting the Si content to the required range by using a SiCa alloy material;
(3) RH vacuum refining, feeding Al wire into molten steel for deoxidation, controlling the oxygen content in the molten steel to reach a required range, feeding Zr powder wire into the molten steel, adjusting the Zr content to be in the required range, blowing Ar gas into the molten steel, stirring and homogenizing the molten steel, and treating under ultimate vacuum to remove gases such as N, H and coarse harmful impurities in the steel;
(4) continuous casting, casting temperature: 1540-1560 ℃, and the casting blank comprises the following chemical components in percentage by mass: c: 0.01-0.021%, Si: 0.65-0.80%, Mn: 0.20-0.50%, P is less than or equal to 0.01%, S is less than or equal to 0.006%, Ni: 0.35-0.60%, Zr: 0.001-0.01%, O: 0.001-0.01%, and the balance of Fe and inevitable impurities;
(5) rolling, casting blank heating temperature: 1150-1200 ℃, rolling start temperature: 1000-1040 ℃, finishing temperature: 800 ℃ and 830 ℃;
(6) cooling after rolling, and returning to red temperature: 560 ℃ and 630 ℃;
(7) stacking the rolled L-shaped steel, and eliminating rolling residual stress by using residual temperature tempering;
(8) welding with small heat input and 80% CO 2 + 20% Ar gas shield welding mode, weld line energy E: 8-15 kJ/cm.
Further, the limit vacuum treatment time in the step (3) is 8-14 minutes.
Further, the cross-sectional dimension of the rectangular billet of the casting blank in the step (4) is 300 x 350 mm.
Further, the heat preservation time after the casting blank is heated in the step (5) is 2-3 hours.
Further, the cooling mode in the step (6) is watering or water mist.
Further, the stacking time in the step (7) is 2-4 hours.
Has the advantages that: compared with the prior art, the invention has the following remarkable advantages: the invention avoids the preparation processes such as off-line heat treatment and the like by carrying out unique design on the alloy elements and the mass percentage of the steel and combining the controlled rolling and controlled cooling process, belongs to the short-flow production technology, has lower process cost,the prepared material has yield strength of 320-430MPa and low-temperature impact toughness of-90 ℃ KV 2 The liquid ammonia corrosion resistance is higher than or equal to 90J, the liquid ammonia corrosion environment is built, the stress corrosion resistance is good, the low-temperature toughness is good, and the running state of the structural part is good in the environment of 90 ℃ below zero. The Vickers hardness of a heat affected zone of the T-shaped small heat input welding joint is less than or equal to 345Hv10, the defects of welding cracks and the like are avoided, the quality of the welding joint is excellent, the welding joint can be used for building structural members such as keels, reinforcing ribs and the like of high-technology low-temperature ships such as LPG, liquid ammonia and the like, and the welding joint is safe, reliable and remarkable in economic benefit.
Detailed Description
The present invention will be further described with reference to specific examples.
According to the chemical element components, the mass percentages and the preparation method requirements of the invention, five embodiments are set, namely embodiment 1, embodiment 2, embodiment 3, embodiment 4 and embodiment 5. In order to verify the influence of the chemical components and the mass percentage content as well as the RH limit vacuum treatment time in the smelting process, the finish rolling temperature in the rolling process, the finish rolling cooling temperature and other process parameters on the performance parameters, three comparative examples, namely a comparative example 1, a comparative example 2 and a comparative example 3 are set, namely 8 batches of L-shaped steel are smelted and rolled. Wherein, the mass percentage content of the chemical components of the comparative example 1 is out of the scope of the invention, the process parameters of the preparation process are in the scope of the invention, the mass percentage content of the chemical components of the comparative example 2 is in the scope of the invention, the process parameters of the preparation process are out of the scope of the invention, and the mass percentage content of the chemical components of the comparative example 3 and the process parameters of the preparation process are out of the scope of the invention. The chemical element composition weight percentages of the five examples and the three comparative examples are shown in table 1, wherein the balance is Fe and unavoidable impurities. The process control parameters and the L-shaped steel performance conditions in the production process are shown in Table 2.
As can be seen from tables 1 and 2, the yield strengths of the low temperature L-shaped steel prepared by the chemical components and the mass percentages of the embodiments 1-5 of the invention and the process parameters controlled by the preparation process are all within the range of 320-420MPa, and the impact toughness is-90 ℃ KV 2 Are all higher than 90J. While the steel composition ranges or/and preparation processes of comparative examples 1 and 2 do notThe yield strength of the comparative L-shaped steel prepared in the range of the invention is lower than 320MPa, and the yield strength of the L-shaped steel prepared in the comparative example 3 reaches 453MPa and exceeds 420MPa, so that stress corrosion cracking is easy to occur when the L-shaped steel is used for building steel structures in corrosive environments such as liquid ammonia and the like. The L-shaped steels prepared in comparative examples 1, 2 and 3 have impact toughness at 90 ℃ below 90J and hardness in a heat affected zone of small heat input welding below 345Hv 10. The yield strength of the L-shaped steel prepared in the embodiment 1 of the invention is 377MPa, the impact toughness at 90 ℃ below zero reaches 219J, the hardness of a heat affected zone of small linear energy welding is only 303Hv10, the comprehensive mechanical property and the welding property are excellent, and the high-technology low-temperature ship for manufacturing LPG and liquid ammonia can run safely.
TABLE 1 comparison of chemical compositions (wt%) of inventive examples 1-5 and comparative examples 1-3
TABLE 2 Table of control parameters of production processes of examples 1 to 5 of the present invention and comparative examples 1 to 3 for the performance of low-temperature L-shaped steel
Claims (10)
1. The low-temperature L-shaped steel is characterized by comprising the following chemical components in percentage by mass: c: 0.01-0.021%, Si: 0.65-0.80%, Mn: 0.20-0.50%, P is less than or equal to 0.01%, S is less than or equal to 0.006%, Ni: 0.35-0.60%, Zr: 0.001-0.01%, O: 0.001-0.01%, and the balance of Fe and inevitable impurities.
2. The low-temperature L-shaped steel according to claim 1, wherein the Si is 0.65-0.70% by mass.
3. The low-temperature L-shaped steel according to claim 1, wherein the Mn is 0.35 to 0.45% by mass.
4. The low-temperature L-shaped steel according to claim 1, wherein the mass percentage of Ni is 0.40-0.50%.
5. The low-temperature L-shaped steel according to claim 1, wherein the metallographic structure of the low-temperature L-shaped steel is an acicular ferrite structure.
6. A method for producing a low-temperature L-shaped steel as defined in claim 1, comprising the steps of:
(1) smelting in a converter, namely charging molten iron, scrap steel, MnFe, SiFe and NiFe alloy materials into an alkaline converter for smelting, blowing oxygen, raising the temperature, oxidizing and removing C, and adding CaO and FeO to remove P;
(2) performing electric furnace refining outside the furnace, adding high-quality lime to remove the S content until the S content is less than or equal to 0.005%, finely adjusting the Mn content and the Ni content in the molten steel to the required range by using a metal Mn plate and a metal Ni plate, and adjusting the Si content to the required range by using a SiCa alloy material;
(3) RH vacuum refining, feeding Al wire into molten steel for deoxidation, controlling the oxygen content in the molten steel to reach a required range, feeding Zr powder wire into the molten steel, adjusting the Zr content to be in the required range, blowing Ar gas into the molten steel, stirring and homogenizing the molten steel, and treating under ultimate vacuum to remove gases such as N, H and coarse harmful impurities in the steel;
(4) continuous casting, casting temperature: 1540-1560 ℃, and the casting blank comprises the following chemical components in percentage by mass: c: 0.01-0.021%, Si: 0.65-0.80%, Mn: 0.20-0.50%, P is less than or equal to 0.01%, S is less than or equal to 0.006%, Ni: 0.35-0.60%, Zr: 0.001-0.01%, O: 0.001-0.01%, and the balance of Fe and inevitable impurities;
(5) rolling, casting blank heating temperature: 1150-1200 ℃, rolling start temperature: 1000-1040 ℃, finishing temperature: 800 ℃ and 830 ℃;
(6) cooling after rolling, and returning to red temperature: 560 ℃ and 630 ℃;
(7) stacking the rolled L-shaped steel, and eliminating rolling residual stress by using residual temperature tempering;
(8) welding with small heat input and 80% CO 2 + 20% Ar gas shield welding mode, weld line energy E: 8-15 kJ/cm.
7. The method for producing low-temperature L-shaped steel according to claim 6, wherein the minimum vacuum treatment time in the step (3) is 8 to 14 minutes.
8. The method of manufacturing low-temperature L-shaped steel according to claim 6, wherein the holding time after the billet is heated in the step (5) is 2 to 3 hours.
9. The method for producing low-temperature L-shaped steel according to claim 6, wherein the cooling means in the step (6) is watering or water mist.
10. The method for producing low-temperature L-shaped steel according to claim 6, wherein the stacking time in the step (7) is 2 to 4 hours.
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| CN116555664A (en) * | 2023-05-04 | 2023-08-08 | 南京钢铁股份有限公司 | Corrosion-resistant L-shaped steel for liquid ammonia storage tank and preparation method thereof |
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| CN112941405A (en) * | 2021-01-26 | 2021-06-11 | 南京钢铁股份有限公司 | High-toughness heat-resistant flat-bulb steel for ships and preparation method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN115786634A (en) * | 2022-12-06 | 2023-03-14 | 舞阳钢铁有限责任公司 | Method for improving welding performance of nickel-containing low-temperature steel |
| CN116555664A (en) * | 2023-05-04 | 2023-08-08 | 南京钢铁股份有限公司 | Corrosion-resistant L-shaped steel for liquid ammonia storage tank and preparation method thereof |
| CN116555664B (en) * | 2023-05-04 | 2024-03-19 | 南京钢铁股份有限公司 | Corrosion-resistant L-shaped steel for liquid ammonia storage tank and preparation method thereof |
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| CN114892075B (en) | 2023-03-21 |
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