CN115418563A - 5Ni ultralow-temperature L-shaped steel, production method and induction heat treatment device - Google Patents
5Ni ultralow-temperature L-shaped steel, production method and induction heat treatment device Download PDFInfo
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- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 7
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- 238000005496 tempering Methods 0.000 claims description 23
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- 238000010791 quenching Methods 0.000 claims description 19
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- 238000009749 continuous casting Methods 0.000 claims description 12
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- 229910000859 α-Fe Inorganic materials 0.000 description 1
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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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/06—Surface hardening
- C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
- C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
- C21D1/667—Quenching devices for spray quenching
-
- 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
-
- 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
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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
- C22C38/18—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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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
- C21D2211/008—Martensite
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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
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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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
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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Abstract
The invention discloses 5Ni ultralow temperature L-shaped steel, a production method and an induction heat treatment device, wherein the 5Ni ultralow temperature L-shaped steel comprises the following chemical element components in percentage by weight: 0.015 to 0.055 percent of C, 0.25 to 0.55 percent of Si, 0.25 to 0.50 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.008 percent of S, cr:0.05 to 0.20%, ni:4.80 to 5.20 percent of Ti, 0.020 to 0.035 percent of Ti, mo:0.02 to 0.08 percent, and the balance of Fe and inevitable impurities. The 5Ni ultralow temperature L-shaped steel provided by the invention has relatively simple chemical components and is easy to control the smelting process. The production method of the 5Ni ultralow temperature L-shaped steel adopts a medium-frequency induction heat treatment method, has compact heat treatment process, high production efficiency and easy control of production process, and the produced 5Ni ultralow temperature L-shaped steel has excellent and stable comprehensive mechanical properties, flat appearance plate shape, excellent appearance quality, high yield and good welding performance, can be directly used for building structural members such as reinforcing ribs of ship-borne LPG storage tanks, obviously improves the ship building efficiency, shortens the construction period and has huge economic benefit.
Description
Technical Field
The invention belongs to the field of low-temperature steel manufacturing, and particularly relates to 5Ni ultralow-temperature L-shaped steel and a production method thereof.
Background
With the increasing demand of clean energy, the order quantity of a shipborne Liquefied Petroleum Gas (LPG) storage tank is increased year by year, the steel for building the LPG storage tank mostly adopts 5Ni ultralow-temperature steel, at present, all medium and large steel enterprises can produce 5Ni plates, but the section steel (such as flat bulb steel, L-shaped steel and the like) for building reinforcing ribs of the storage tank is not commercially supplied due to large manufacturing difficulty, and the method of cutting the plates into flat steel or cutting and welding the plates into T-shaped sections is mostly adopted for structural members such as the reinforcing ribs of the storage tank, so that the process has long construction period, low utilization rate of the steel and high welding cost. If the reinforcing rib of the storage tank is directly constructed by the sectional material, the construction efficiency can be greatly improved, the cost is reduced, and the construction period is shortened.
The international invention patent (application number PCT/CN 2021/070624) discloses a method for manufacturing a marine 5Ni steel plate with low remanence and excellent surface quality, which comprises the following chemical components in percentage by weight: 0.07 to 0.10%, si:0.05 to 0.20%, mn:0.60 to 0.80%, ni: 4.90-5.25%, P is less than or equal to 0.0070%, S is less than or equal to 0.0020%, alt: 0.010-0.035%, V:0.010 to 0.015%, nb:0.010 to 0.020%, ca:0.0005 to 0.0030 percent, less than or equal to 0.0012 percent of O, less than or equal to 0.0040 percent of N, less than or equal to 0.00010 percent of H, and the balance of Fe and inevitable impurities. In the production method, casting blanks are peeled, hot rolled at high temperature, water cooling is not performed after rolling, then quenching and tempering are performed for two times, the first quenching temperature is increased, the segregation with high Ni content is improved, and the steel is hoisted by a vacuum chuck, so that good 5Ni steel with high toughness is obtained, and the product has excellent surface quality and low remanence. The technical scheme needs two times of quenching and tempering heat treatment, and has the advantages of more complex working procedures, lower production efficiency and higher cost.
Disclosure of Invention
In order to fill the blank of the existing 5Ni section steel for constructing the ship-borne LPG storage tank, shorten the construction period of the ship-borne LPG storage tank and reduce the construction cost, the application provides the 5Ni ultralow temperature L section steel with excellent welding performance and the production method thereof, and the microstructure structure of the manufactured 5Ni ultralow temperature L section steel is a full tempered martensite, has excellent comprehensive mechanical property and welding performance, and can be directly used for constructing the LPG storage tank.
In order to realize the purpose, the invention adopts the technical scheme that: the 5Ni ultralow-temperature L-shaped steel is characterized by comprising the following chemical element components in percentage by weight: 0.015-0.055% of C, 0.25-0.55% of Si, 0.25-0.50% of Mn, less than or equal to 0.015% of P, less than or equal to 0.008% of S, cr:0.05 to 0.20%, ni: 4.80-5.20%, ti 0.020-0.035%, mo: 0.02-0.08%, and the balance of Fe and inevitable impurities.
Further, the weight percentage of C is preferably 0.04 to 0.055%.
Further, the weight percentage of the Ni is preferably 4.90 to 5.15%.
Further, the weight percentage of Ti is preferably 0.025 to 0.030%.
Further, the weight percentage of Cr is preferably 0.06 to 0.12%.
Further, the weight percentage of Mo is preferably 0.02 to 0.06%.
The principle of the main control of the alloy elements is explained as follows:
c (carbon): the alloy element C added into the steel strongly improves the strength and obviously reduces the impact toughness, and the application emphasizes that the impact energy of the V-shaped notch is more than or equal to 100J at the temperature of minus 150 ℃, so that the content of C is set to be 0.015-0.055%, the yield strength is more than or equal to 410MPa after induction quenching and tempering treatment, the requirement that the impact energy of the V-shaped notch is more than or equal to 100J at the temperature of minus 150 ℃ is difficult to achieve if the content of C is higher than 0.055%, and the requirement that the yield strength is more than or equal to 410MPa if the content of C is lower than 0.015%.
Mn (manganese): the 5Ni ultralow temperature L-shaped steel is delivered in a quenching and tempering state, and is combined with the added alloy element Cr to improve the hardenability of the steel, obtain a full-martensite structure, and obtain the full-tempered martensite structure with excellent performance after tempering treatment. Therefore, the Mn content is set to 0.25 to 0.50%. If it is more than 0.50%, mnS is easily produced with the residual S in the steel, and the metal matrix is cleaved to lower the low-temperature impact toughness, whereas if it is less than 0.25%, it is difficult to reduce the hardenability of the steel and to have a full martensitic structure.
P (phosphorus) S (sulfur): the residual P, S obviously deteriorates the low-temperature toughness of the alloy, belongs to harmful elements, the lower the content is, the better the content is, but if the content is too low, the production cost is greatly increased, so that the P, S is preferably controlled to be less than or equal to 0.015 percent in P and less than or equal to 0.008 percent in S.
Si (silicon): the addition of a proper amount of alloy element Si in the steel can improve the tempering stability because the Si can not form carbide and has the function of inhibiting the diffusion of C atoms and the like, and on the other hand, the Si in the steel can improve the yield strength of the steel and reduce the low-temperature impact toughness, so the Si content is controlled to be in the range of 0.25-0.55 percent, the low-temperature toughness is obviously reduced when the Si content is higher than 0.55 percent, and the Si content is preferably more than or equal to 0.25 percent in order to ensure the yield strength.
Cr (chromium): the method adds a proper amount of alloy elements Cr and Mn for combined action, improves the hardenability of the steel, obtains a full martensite structure after induction quenching, thereby obtaining the required strength performance, but reduces the low-temperature impact toughness of the steel, so the Cr content in the steel is controlled within the range of 0.05-0.20 percent. The content of more than 0.20% remarkably deteriorates the low-temperature toughness, and the content of less than 0.05% causes the steel to have insufficient hardenability, and it is difficult to obtain a full martensite structure in the induction quenching process.
Ti (titanium) is added into the steel, and the aim is to improve the welding performance, on one hand, the added Ti reduces the recrystallization temperature Tnr of the steel, and inhibits austenite from recrystallizing and coarsening in the high-temperature welding process to obtain a fine original austenite structure; on the other hand, the second phases of high-temperature stable fine dispersion distribution Ti2O3, ti3O5 and the like formed by Ti added into the steel and residual oxygen atoms (O) in the manufacturing process provide nucleation cores for acicular ferrite in the welding and cooling process, promote the formation of acicular tissues, integrally refine the microstructure of a welding heat affected zone and improve the mechanical property of a welding joint, so that the application has good welding adaptability, but the excessive Ti content reduces the low-temperature toughness of the steel, and the Ti content in the steel is set to be in a range of 0.020-0.035% by comprehensive consideration.
Ni (nickel): the nominal Ni content in the 5Ni low-temperature steel is required to be 5.0%, and on one hand, ni atoms and Fe atoms form replacement mutual solubility, so that the friction force of a lattice structure is reduced, dislocation is easy to move, the buffering capacity under the action of external load is increased, and the low-temperature toughness of the steel is improved macroscopically; on the other hand, the solid-dissolved Ni can obviously stabilize austenite structure, and a martensite structure is easily obtained in the induction quenching process, so that good toughness matching is obtained, and the content range of Ni is controlled according to the central line required by the standard: 4.80 to 5.20 percent.
Mo (molybdenum): the steel grade is in an induction quenching and tempering delivery state, so that the steel grade is required to have certain tempering stability, the alloy element Mo added into the steel can inhibit atomic diffusion, moC precipitated phase particles generated by reaction with C atoms are fine, the matrix is strengthened, and the obvious strength reduction caused by tempering is avoided. Mo is an expensive alloy element, and excessive addition causes a significant increase in production cost. Therefore, the adding amount of the Mo alloy element is controlled within the range of 0.02 to 0.08 percent.
The application also provides a production method of the 5Ni ultralow temperature L-shaped steel, which is characterized by comprising the following steps:
1) Smelting in a converter:
charging molten iron, scrap steel and alloy materials into a top-bottom combined blown converter for smelting, blowing oxygen, raising the temperature, oxidizing and removing C, and adding CaO and FeO to remove P;
refining in an LF electric furnace outside the furnace, and adding lime to remove S;
RH vacuum refining, fine adjusting the components to a control range, treating for more than or equal to 15 minutes under ultimate vacuum, and removing N, H, O gas and large-particle harmful impurities in steel;
continuous casting, namely lifting the molten steel to a continuous casting platform when the temperature of the molten steel is 1540-1565 ℃, wherein the section size of a continuous casting rectangular billet is 260 multiplied by 350mm;
2) Rolling:
polishing the continuous casting blank, namely polishing the large-surface iron oxide scale of the casting blank 4 cleanly, wherein the polishing depth is 0.8-1.2mm;
coating an anti-oxidation coating on the large surface of the polished casting blank 4;
the heating temperature of the casting blank is 1240-1280 ℃, and the heat preservation time is more than or equal to 300 minutes;
the initial rolling temperature is more than or equal to 1000 ℃, and the final rolling temperature is 830-930 ℃;
3) Cooling after rolling:
air cooling to room temperature after rolling;
4) And (3) heat treatment:
induction quenching: conveying 5Ni ultralow-temperature L-shaped steel on a roller way and simultaneously carrying out continuous heat treatment, wherein the continuous heat treatment comprises preheating to 750-850 ℃, first heating to 860-980 ℃, and rapidly cooling to room temperature to obtain an all-martensite structure;
induction tempering: and (3) carrying out tempering treatment on the 5Ni ultralow-temperature L-shaped steel cooled to room temperature by induction quenching after the second heating to 550-680 ℃ to obtain a fully tempered martensite structure.
Because the L-shaped steel belongs to long materials, the L-shaped steel is easy to be seriously deformed by the heating mode heat treatment (such as quenching and the like) of the conventional box furnace, and if the L-shaped steel is distorted and deformed, the L-shaped steel is difficult to be corrected into waste products. The application further provides an induction heat treatment device, which is applied to the production method of the 5Ni ultralow-temperature L-shaped steel and is characterized by comprising a roller way, and a preheating inductor, a first heating inductor, a water spraying device and a second heating inductor which are sequentially arranged along the conveying direction of the roller way; the roller way is used for conveying the 5Ni ultralow temperature L-shaped steel, the preheating inductor is used for preheating the 5Ni ultralow temperature L-shaped steel to 750-850 ℃, the first heating inductor is used for heating the preheated 5Ni ultralow temperature L-shaped steel to 860-980 ℃, the water spraying device is used for rapidly cooling the heated 5Ni ultralow temperature L-shaped steel to room temperature to obtain a full martensite structure, and the second heating inductor is used for reheating the cooled 5Ni ultralow temperature L-shaped steel to 550-680 ℃ for tempering treatment to obtain a full tempered martensite structure.
Has the beneficial effects that:
the 5Ni ultralow temperature L-shaped steel provided by the application has relatively simple chemical components and is easy to control in the smelting process. The production method of the 5Ni ultralow temperature L-shaped steel adopts a medium-frequency induction heat treatment method, the heat treatment process is compact, the production efficiency is high, the production process is easy to control, the produced 5Ni ultralow temperature steel has good quality, the yield strength is more than or equal to 410Mpa, the impact energy of a V-shaped notch at minus 150 ℃ is more than or equal to 100J, and the surface unevenness is less than or equal to 3mm/1m. The plate shape is flat, the yield is high, the welding performance is good, the plate can be directly used for building structural members such as reinforcing ribs of a ship-borne LPG storage tank, the ship building efficiency is obviously improved, the construction period is shortened, and the economic benefit is huge.
Drawings
The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.
Fig. 1 is a schematic structural view of an induction heat treatment apparatus according to the present application.
FIG. 2 is a microstructure diagram of 5Ni ultralow temperature L-shaped steel after induction quenching and tempering.
Detailed Description
The present invention will be described in further detail with reference to the following examples, it being understood that the specific examples described herein are for the purpose of illustration and description only and are not intended to limit the invention to the examples described below.
The invention provides 5Ni ultralow temperature L-shaped steel which comprises the following chemical element components in percentage by weight: 0.015-0.055% of C, 0.25-0.55% of Si, 0.25-0.50% of Mn, less than or equal to 0.015% of P, less than or equal to 0.008% of S, cr:0.05 to 0.20%, ni: 4.80-5.20%, ti 0.020-0.035%, mo: 0.02-0.08%, and the balance of Fe and inevitable impurities.
Preferably, the 5Ni ultralow temperature L-shaped steel comprises the following chemical element components in percentage by weight: 0.04 to 0.055 percent of C, 0.25 to 0.55 percent of Si, 0.25 to 0.50 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.008 percent of S, cr:0.06 to 0.12%, ni:4.90 to 5.15 percent, ti of 0.025 to 0.030 percent, mo:0.02 to 0.06 percent, and the balance of Fe and inevitable impurities.
The invention provides a production method of the 5Ni ultralow temperature L-shaped steel, which comprises the following steps:
1) Smelting in a converter
Molten iron, scrap steel, mnFe, siFe, tiFe, crFe, niFe, moFe and other alloy materials are loaded into a top-bottom combined blown converter for smelting, oxygen blowing, temperature rising, oxidation and C removal are carried out, and CaO and FeO are added for removing P which is less than or equal to 0.015 percent.
And (3) refining in an LF electric furnace outside the furnace, and adding high-quality lime to remove the S content until the S content is less than or equal to 0.008%.
RH vacuum refining, fine adjusting the components to a control range, and treating for more than or equal to 15 minutes under ultimate vacuum to remove harmful impurities such as N, H, O and other gases and large particles in the steel.
Continuous casting temperature: and hoisting the molten steel to a continuous casting platform at the temperature of 1540-1565 ℃. The cross section of the continuous casting rectangular billet is 260 multiplied by 350mm.
2) Rolling of
And (3) grinding of the continuous casting billet: grinding the large-surface oxidized iron sheet of the casting blank 4 cleanly, wherein the grinding depth is as follows: 0.8-1.2mm.
And coating an anti-oxidation coating on the large surface of the polished casting blank 4.
Heating temperature of casting blank: 1240-1280 ℃, and the heat preservation time is more than or equal to 300 minutes.
The initial rolling temperature: not less than 1000 ℃, and the finishing rolling temperature: 830-930 deg.C.
3) Cooling after rolling
And air-cooling to room temperature after rolling.
4) Thermal treatment
Induction quenching and tempering were performed using an induction heat treatment apparatus as shown in fig. 1. The device comprises a roller way 6, and a preheating inductor 2, a first heating inductor 3, a water spraying device 4 and a second heating inductor 5 which are sequentially arranged along the conveying direction of the roller way 6. The roller bed 6 is used for conveying 5Ni ultralow temperature L-shaped steel, the preheating inductor 2 is used for preheating the 5Ni ultralow temperature L-shaped steel to 750-850 ℃, the first heating inductor 3 is used for heating the preheated 5Ni ultralow temperature L-shaped steel to 860-980 ℃, the water spraying device 4 is used for rapidly cooling the heated 5Ni ultralow temperature L-shaped steel to room temperature to obtain a full martensite structure, and the second heating inductor 5 is used for reheating the cooled 5Ni ultralow temperature L-shaped steel to 550-680 ℃ for tempering treatment to obtain a full tempering martensite structure. The preheating inductor 2, the first heating inductor 3 and the second heating inductor 5 all adopt the existing intermediate frequency induction heat treatment equipment, and the invention does not relate to the improvement and innovation of the equipment.
As shown in FIG. 1, the heat treatment process of the 5Ni ultralow temperature L-shaped steel comprises the following steps:
induction quenching: the 5Ni ultralow temperature L-shaped steel 1 is placed on a roller way 6 to run along the running direction of the roller way (the direction of an arrow in the figure) and is continuously heat-treated, the 5Ni ultralow temperature L-shaped steel 1 is preheated to 750-850 ℃ by a preheating inductor 2, then the 5Ni ultralow temperature L-shaped steel 1 is heated to 860-980 ℃ by a heating inductor 3, and the 5Ni ultralow temperature L-shaped steel is rapidly cooled to the room temperature by a water spraying device 4 to obtain an all-martensite structure.
Induction tempering: the distance between the heating inductor 5 and the water spraying device 4 is 10 meters, and the 5Ni ultralow temperature L-shaped steel is heated to 550-680 ℃ for tempering treatment when passing through the intermediate frequency heating inductor 5, so that a fully tempered martensite structure is obtained, and the microstructure structure chart is shown in figure 2.
The invention provides examples 1 to 5 according to the mass percentages of the chemical element components and the production process. In order to verify the influence of the chemical components and the mass percentage content as well as the process parameters such as the induction quenching preheating temperature, the induction quenching heating temperature, the induction tempering heating temperature and the like on the performance parameters, the invention simultaneously provides three comparative examples, namely comparative example 1, comparative example 2 and comparative example 3, and 8 batches of 5Ni ultralow temperature L-shaped steel are prepared. Wherein, the chemical components of comparative example 1 are not in the range of the present invention by mass, the process parameters of the preparation process are in the range of the present invention, the chemical components of comparative example 2 are in the range of the present invention by mass, the process parameters of the preparation process are not in the range of the present invention, and the chemical components of comparative example 3 and the process parameters of the preparation process are not in the range of the present invention by mass. The weight percentages of the main chemical element components of the five examples and the three comparative examples are shown in table 1, wherein the balance is Fe and inevitable impurities. The main process control parameters and the L-shaped steel performance conditions in the production process are shown in Table 2.
TABLE 1 comparison of chemical compositions (wt%) of inventive and comparative examples
TABLE 2 Table of control parameters of production process of examples of the present invention and comparative examples on L-shaped steel Performance
As can be seen from tables 1 and 2, the L-shaped steel produced by the chemical components and the mass percentages of the examples 1 to 5 of the invention and the process parameters controlled by the production process has yield strength higher than 410MPa, impact toughness higher than 100J at-150 ℃, shape unevenness lower than 3mm/1m and smooth surface. While the impact energy at-150 ℃ of the L-shaped steel prepared in comparative example 1 reaches 141J, the yield strength and the shape unevenness thereof do not satisfy the requirements. The L-shaped steels produced in comparative examples 2 and 3 had yield strengths higher than 410MPa, but had impact strengths of-150 ℃ and profile irregularities not satisfying the requirements. The L-shaped steel prepared in the embodiment 1 of the invention has the yield strength of 434MPa, the impact energy of 209J at-150 ℃, the shape unevenness of 1.1mm/1m and excellent surface quality, and is the best embodiment.
Claims (9)
1. The 5Ni ultralow-temperature L-shaped steel is characterized by comprising the following chemical element components in percentage by weight: 0.015 to 0.055 percent of C, 0.25 to 0.55 percent of Si, 0.25 to 0.50 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.008 percent of S, cr:0.05 to 0.20%, ni:4.80 to 5.20 percent of Ti, 0.020 to 0.035 percent of Ti, mo:0.02 to 0.08 percent, and the balance of Fe and inevitable impurities.
2. The 5Ni ultralow temperature L-shaped steel as claimed in claim 1, wherein the weight percentage of C is 0.04 to 0.055%.
3. The 5Ni ultralow temperature L-shaped steel as claimed in claim 1, wherein the weight percentage of Ni is 4.90 to 5.15%.
4. The 5Ni ultralow temperature L-shaped steel as claimed in claim 1, wherein the weight percentage of Ti is 0.025 to 0.030%.
5. The 5Ni ultralow temperature L-shaped steel as claimed in claim 1, wherein the weight percentage of Cr is 0.06 to 0.12%.
6. The 5Ni ultralow temperature L-shaped steel as claimed in claim 1, wherein the weight percentage of Mo is 0.02 to 0.06%.
7. The 5Ni ultralow temperature L-shaped steel as claimed in claim 1, wherein the microstructure of the 5Ni ultralow temperature L-shaped steel is fully tempered martensite, the yield strength is not less than 410MPa, the V-notch impact energy at-150 ℃ is not less than 100J, and the surface unevenness is not more than 3mm/1m.
8. The method for producing 5Ni ultra-low temperature L-type steel according to any one of claims 1 to 7, comprising:
1) Smelting in a converter:
charging molten iron, scrap steel and alloy materials into a top-bottom combined blowing converter for smelting, blowing oxygen, raising the temperature, oxidizing and removing C, and adding CaO and FeO for removing P;
refining in an LF electric furnace outside the furnace, and adding lime to remove S;
RH vacuum refining, fine adjusting the components to a control range, treating for more than or equal to 15 minutes under ultimate vacuum, and removing N, H, O gas and large-particle harmful impurities in steel;
continuous casting, namely lifting the molten steel to a continuous casting platform when the temperature of the molten steel is 1540-1565 ℃, wherein the section size of a continuous casting rectangular billet is 260 multiplied by 350mm;
2) Rolling:
polishing the continuous casting blank, namely completely polishing the large-surface oxidized iron sheet of the casting blank 4, wherein the polishing depth is 0.8-1.2mm;
coating an anti-oxidation coating on the large surface of the polished casting blank 4;
the heating temperature of the casting blank is 1240-1280 ℃, and the heat preservation time is more than or equal to 300 minutes;
the initial rolling temperature is more than or equal to 1000 ℃, and the final rolling temperature is 830-930 ℃;
3) Cooling after rolling:
air cooling to room temperature after rolling;
4) And (3) heat treatment:
induction quenching: conveying 5Ni ultralow-temperature L-shaped steel on a roller way and simultaneously carrying out continuous heat treatment, wherein the continuous heat treatment comprises preheating to 750-850 ℃, first heating to 860-980 ℃, and rapidly cooling to room temperature to obtain an all-martensite structure;
induction tempering: and (3) carrying out tempering treatment on the 5Ni ultralow-temperature L-shaped steel cooled to room temperature by induction quenching after the second heating to 550-680 ℃ to obtain a fully tempered martensite structure.
9. An induction heat treatment device applied to the production method of 5Ni ultralow temperature L-shaped steel as claimed in claim 8, characterized by comprising a roller way (6), and a preheating inductor (2), a first heating inductor (3), a water spraying device (4) and a second heating inductor (5) which are sequentially arranged along the conveying direction of the roller way (6); the roller way (6) is used for conveying the 5Ni ultralow temperature L-shaped steel, the preheating inductor (2) is used for preheating the 5Ni ultralow temperature L-shaped steel to 750-850 ℃, the first heating inductor (3) is used for heating the preheated 5Ni ultralow temperature L-shaped steel to 860-980 ℃, the water spraying device (4) is used for rapidly cooling the heated 5Ni ultralow temperature L-shaped steel to room temperature to obtain a full martensite structure, and the second heating inductor (5) is used for reheating the cooled 5Ni ultralow temperature L-shaped steel to 550-680 ℃ for tempering treatment to obtain a full tempering martensite structure.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN117305565A (en) * | 2023-10-09 | 2023-12-29 | 常熟市龙腾特种钢有限公司 | Flat-bulb steel with gradient performance and preparation method thereof |
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| CN117305565A (en) * | 2023-10-09 | 2023-12-29 | 常熟市龙腾特种钢有限公司 | Flat-bulb steel with gradient performance and preparation method thereof |
| CN117305565B (en) * | 2023-10-09 | 2024-04-05 | 常熟市龙腾特种钢有限公司 | Flat-bulb steel with gradient performance and preparation method thereof |
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Application publication date: 20221202 |