CN114807785B - 390 MPa-grade corrosion-resistant steel plate and production method thereof - Google Patents
390 MPa-grade corrosion-resistant steel plate and production 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- 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
-
- 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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
-
- 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
- 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
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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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- 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
- C21D2211/009—Pearlite
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- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides a 390 MPa-grade corrosion-resistant steel plate and a production method thereof, and relates to the technical field of alloys.
Description
Technical Field
The invention relates to the technical field of alloys, in particular to a 390 MPa-level corrosion-resistant steel plate and a production method thereof.
Background
The steel structure building is a novel building system, steel plates and the like are used for replacing reinforced concrete, and the steel structure building has the following advantages: the volume weight and the strength of the steel are smaller than those of common wood, concrete and masonry, and the steel is more portable; the section of the steel structure is small, and the effective area of the building can be increased by about 8 percent compared with a reinforced concrete structure; the steel structure has good ductility and better shock resistance; steel can be repeatedly used, construction waste is reduced, and the environment is more greenAnd (5) protecting. Therefore, steel structure construction is the development direction of future construction. The steel structure building is generally in the atmosphere corrosion environment of the industry in the big city, and the corrosive gas SO in the atmosphere 2 Has 1300 times higher solubility than oxygen in water, and generates H after dissolving in water film on metal surface 2 SO 3 Or H 2 SO 4 The PH value of the metal surface can reach 3 to 3.5, and the corrosion of a steel structure can be greatly accelerated. At present, the main means of corrosion prevention of steel structure buildings is to coat an anticorrosive paint or a zinc coating on the surface of a steel structure, the anticorrosive paint is generally coated and maintained once in 3~5 years, and the anticorrosive paint is coated again once in 10 to 15 years, so that the coating process causes health hazards and environmental pollution. If the steel plate with industrial atmospheric corrosion resistance is used, the construction efficiency of the steel structure building can be obviously improved, and the life cycle cost is reduced.
However, the existing industrial atmospheric corrosion resistant steels have some defects, mainly including:
a large amount of P or N is added to improve the corrosion resistance, such as CN102534381A, CN103233167A, CN112662947A, CN112795844B, CN113293334A, CN103540871B, CN103993229B, CN107502835B, CN108286026A, CN109402508B, but the addition of a large amount of P or N is not beneficial to the low-temperature toughness or weldability of the steel.
A large amount of Cu or Ni or N is added to improve the corrosion resistance, for example, CN112813360B, CN108396231B, CN113584376A, but the addition of a large amount of Cu or Ni alloy is high in cost and is not beneficial to popularization and application of products.
Rare earth is added to improve the corrosion resistance, for example, CN102268613B, CN105734406A, CN108070796B, CN108754303A, CN111850429B, CN111575449A, CN113061805A, CN114086074A, but the rare earth yield fluctuation is large, the steel making process is complicated, and the method is not suitable for mass production.
Therefore, it is urgent to develop a steel plate for steel structure construction having excellent comprehensive performance and resistance to corrosion by industrial atmosphere.
Disclosure of Invention
The invention aims to provide a 390 MPa-grade corrosion-resistant steel plate and a production method thereof.
The invention provides a 390 MPa-level corrosion-resistant steel plate which comprises the following chemical components in percentage by mass: 0.05 to 0.10 percent of Sb, 0.07 to 0.10 percent of C, 0.4 to 0.5 percent of Si, 1.15 to 1.25 percent of Mn, 0.2 to 0.3 percent of Cr, 0.5 to 0.6 percent of Ni, 0.2 to 0.3 percent of Cu, 0.02 to 0.04 percent of Nb, 0.02 to 0.04 percent of Al, 0.015 to 0.025 percent of P and the balance of Fe and inevitable impurities, wherein the impurities comprise: s is less than or equal to 0.002%, O is less than or equal to 0.002%, and N is less than or equal to 0.004%;
the atmospheric corrosion resistance index I of the steel plate is more than or equal to 6.3, wherein the calculation formula of the atmospheric corrosion resistance index is as follows:
I=26.01(%Cu)+3.88(%Ni)+1.20(%Cr)+1.49(%Si)+17.28(%P)-7.29(%Cu)(%Ni)-9.10(%Ni)(%P)-33.39(%Cu) 2 ，
wherein, the element symbol in the bracket is the mass percent of the corresponding element, the% element symbol represents the mass percent of the corresponding element multiplied by 100;
the yield strength of the steel plate is more than or equal to 390MPa.
As a further improvement of the invention, the chemical components of the steel plate further comprise the following components in percentage by mass: 0.02 to 0.10 percent of Sn.
As a further improvement of the invention, the microstructure of the steel plate comprises ferrite and pearlite, wherein the pearlite content is less than or equal to 8%, and the ferrite comprises polygonal ferrite, quasi-polygonal ferrite and acicular ferrite.
As a further improvement of the invention, the carbon equivalent CE of the steel plate is less than or equal to 0.40, wherein the calculation formula of the carbon equivalent CE is as follows:
CE=(%C)+(%Mn)/6+(%Cr+%Mo+%V)/5+(%Ni+%Cu)/15，
wherein, the symbol of the element in parentheses is the mass percentage of the corresponding element, and the symbol of% element represents the mass percentage of the corresponding element multiplied by 100.
As a further improvement of the invention, the grades of A, B, C, D type inclusions of the steel plate under the GB/T10561 standard are respectively less than or equal to 1.5 grade, the sum of the grades of A, B, C, D type inclusions is less than or equal to 3.0 grade, and the area density of the inclusions with the size of more than 15 mu m on the cross section of the steel plate is less than or equal to 0.1 piece/mm 2 。
As a further improvement of the invention, the tensile strength of the steel plate is 510-660 MPa, the yield ratio is less than or equal to 0.80, the elongation after fracture is more than or equal to 25 percent, and the impact absorption at minus 40 ℃ is realizedEnergy KV 2 ≥150J。
As a further improvement of the invention, in a periodic immersion corrosion test, the average corrosion weight loss ratio of the steel plate is less than or equal to 1.2 g/(m) 2 H), wherein the test conditions of the periodic immersion corrosion test are:
temperature: 45. + -.2 ℃ humidity: 70. + -.5% RH, corrosion medium: (1.0. + -. 0.05). Times.10 -2 mol/L aqueous sodium bisulfite solution, cycle period: 60 +/-3 min, infiltration time: 12 ± 1.5min, duration of the experiment: for 72 hours.
As a further improvement of the invention, when the welding heat input of the steel plate is less than or equal to 100kJ/cm, the impact absorption energy KV of the post-welding heat affected zone at 40 ℃ below zero 2 ≥80J。
As a further improvement of the invention, the thickness of the steel plate is not more than 100mm.
As a further improvement of the present invention, the method for producing a steel sheet comprises the following steps performed in sequence:
pre-desulfurizing molten iron, smelting in a converter, LF refining, RH refining, continuous casting, heating, rolling control and cooling control.
As a further improvement of the invention, in the controlled rolling procedure, two-stage controlled rolling is adopted, wherein the finishing temperature is controlled at 820 +/-15 ℃.
As a further improvement of the invention, in the controlled rolling process, a multifunctional intermittent cooling system is adopted for water cooling, and the final cooling temperature of the steel plate is controlled at 580 +/-30 ℃.
Based on the same invention idea, the invention also provides a production method of the 390 MPa-level corrosion-resistant steel plate, and the steel plate comprises the following chemical components in percentage by mass: 0.05 to 0.10 percent of Sb, 0.07 to 0.10 percent of C, 0.4 to 0.5 percent of Si, 1.15 to 1.25 percent of Mn, 0.2 to 0.3 percent of Cr, 0.5 to 0.6 percent of Ni, 0.2 to 0.3 percent of Cu, 0.02 to 0.04 percent of Nb, 0.02 to 0.04 percent of Al, 0.015 to 0.025 percent of P and the balance of Fe and inevitable impurities, wherein the impurities comprise: s is less than or equal to 0.002%, O is less than or equal to 0.002%, and N is less than or equal to 0.004%;
the production method comprises the following steps: pre-desulfurizing molten iron, smelting in a converter, LF refining, RH refining, continuous casting, heating, rolling control and cooling control;
wherein the controlled rolling process specifically comprises:
two-stage controlled rolling is adopted, the two-stage controlled rolling comprises a first-stage austenite recrystallization region rolling and a second-stage austenite non-recrystallization region rolling, and the finishing rolling temperature in the second-stage austenite non-recrystallization region rolling is controlled to be 820 +/-15 ℃.
As a further improvement of the invention, the chemical components of the steel plate further comprise the following components in percentage by mass: 0.02 to 0.10 percent of Sn.
As a further improvement of the present invention, the controlled cooling process specifically includes:
and (3) performing water cooling by adopting a multifunctional intermittent cooling system, and controlling the final cooling temperature of the steel plate to be 580 +/-30 ℃.
As a further improvement of the present invention, the controlled rolling process further comprises:
and rolling the continuous casting slab obtained by the continuous casting into a steel sheet having a thickness of not more than 100mm.
The invention has the beneficial effects that: the corrosion-resistant steel disclosed by the invention adopts a low-alloy component system with low C, low Mn and low S matched with Sb + Cr + Ni + Cu + P or Sb + Cr + Ni + Cu + P + Sn corrosion-resistant elements added in a composite manner, compared with the high-P, high-N, high-Ni and high-Cu or rare earth element added alloy component system of corrosion-resistant steel in the prior art, the addition amount of alloy elements is small, and the adopted alloy system greatly reduces the raw material cost and the production difficulty of the steel plate on the premise of ensuring the corrosion resistance of the steel plate. In the production flow, the finish rolling temperature and the finish cooling temperature are controlled, so that the microstructure, the size and the quantity of inclusions of the steel plate are accurately controlled, the industrial atmospheric corrosion resistance, the low-temperature toughness and the welding performance of the steel plate are improved, and the 390 MPa-grade steel plate for the building, which has good comprehensive performance and is resistant to the industrial atmospheric corrosion, is finally obtained.
Drawings
FIG. 1 is a metallographic structure picture of a corrosion resistant steel plate of 390MPa grade provided in example 4 of the present invention at a thickness of 1/4.
FIG. 2 is a metallographic structure photograph of a corrosion-resistant steel plate of 390MPa grade according to comparative example 4 of the present invention at a thickness of 1/2.
FIG. 3 is a metallographic structure photograph of a steel sheet according to comparative example 4 of the present invention at a thickness of 1/4.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the technical solutions of the present invention will be described in detail and completely with reference to the following detailed description of the invention and the accompanying drawings. It should be apparent that the described embodiments are only some embodiments of the present application, and not all embodiments. All other embodiments obtained by a person of ordinary skill in the art based on the embodiments of the present invention without any creative effort belong to the protection scope of the present application.
Compared with the existing industrial atmospheric corrosion resistant steel, the 390 MPa-grade corrosion resistant steel has the advantages that the adopted low-C, low-Mn and low-S corrosion resistant element composite-added low-alloy component system which is matched with Sb + Cr + Ni + Cu + P or Sb + Cr + Ni + Cu + P + Sn corrosion resistant elements obviously reduces the raw material cost and the production process difficulty on the premise of ensuring the corrosion resistance, and improves the low-temperature toughness and the welding performance of the steel plate. Furthermore, on the basis of the comprehensive design of chemical components, steel plate preparation is carried out by a Thermo-mechanical Control Process (TMCP) technology, the microstructure, the size and the quantity of inclusions of the steel plate are accurately controlled by controlling the finish rolling temperature and the finish cooling temperature, and the 390 MPa-grade steel plate for the industrial atmospheric corrosion resistant building with good comprehensive performance is obtained.
The 390 MPa-grade corrosion-resistant steel plate comprises the following chemical components in percentage by mass: 0.05 to 0.10 percent of Sb, 0.07 to 0.10 percent of C, 0.4 to 0.5 percent of Si, 1.15 to 1.25 percent of Mn, 0.2 to 0.3 percent of Cr, 0.5 to 0.6 percent of Ni, 0.2 to 0.3 percent of Cu, 0.02 to 0.04 percent of Nb, 0.02 to 0.04 percent of Al, 0.015 to 0.025 percent of P and the balance of Fe and inevitable impurities, wherein the impurities comprise: less than or equal to 0.002% of S, less than or equal to 0.002% of O and less than or equal to 0.004% of N.
In some embodiments of the present invention, sn:0.02 to 0.10 percent.
The core idea of the design of the chemical components of the steel plate is that a small amount of corrosion resistance elements are added in a compounding manner, so that the corrosion resistance of the steel plate is improved, and the performance of the steel plate is comprehensively improved.
Specifically, the design principle of the chemical composition of the steel sheet is explained as follows:
sb: sb is added into steel, and after the steel is corroded for a period of time, the Sb on the surface of the steel is enriched, so that compact Sb firmly combined with a steel matrix can be formed on the surface of the steel 2 O 5 The rust layer can effectively prevent harmful ions from invading and greatly delay the further corrosion of the steel matrix. In addition, when Sb and Cu are used in combination, sb and Cu, which are uniformly distributed, can reduce the current of corrosion microcirculation in steel, thereby reducing the overall corrosion current and inhibiting corrosion at the position of the surface of the steel plate where the pH of the anode is reduced. The pitting corrosion resistance of the steel plate in an industrial atmospheric corrosion environment can be obviously improved through the comprehensive effect of Sb, but when the content of SB exceeds 0.1%, the SB is easy to segregate in a grain boundary, and the low-temperature toughness and the welding performance of the steel plate are influenced, so that in the invention, the content of Sb is controlled to be 0.05-0.10%, and the low-temperature toughness and the welding performance of the steel plate are ensured on the premise of ensuring the corrosion resistance of the steel plate.
C: c is a strengthening element, the structure of steel can be obviously influenced by the content of C, so that the strength of the steel plate is directly influenced, but when the content of C is higher, the content of pearlite can be increased, and further the low-temperature toughness and the welding performance of the steel plate are poor. Therefore, in the invention, the content of C is controlled to be 0.07 to 0.10 percent, and the whole design of other elements is combined, so that not only can the strengthening effect be ensured, but also the low-temperature toughness and the welding performance of the steel plate can be improved, and the problem of large liquid level fluctuation is solved without adopting special protective slag in the continuous casting process.
Si: si is a solid solution strengthening and deoxidizing element, and although there are different viewpoints in the current chemical industry and the industry with respect to the mechanism by which Si plays a role in the corrosion resistance of steel, it is generally considered that SiO is a three-dimensional network structure formed by adding Si 2 Can promote the formation of alpha-FeOOH and the grain refinement, and the Fe of the rust layer 3 O 4 Fe in the alloy can be replaced by Si to form more stable SiO 2 . In addition, when Sb is used in combination with Cu, siO in the rust layer 2 And the enrichment degree of Cu can be improved, so that the industrial atmospheric corrosion resistance is improved. However, when the Si content is larger, the Si content is increased by P, S, Sb. Segregation of elements such as Sn at grain boundaries reduces low-temperature toughness and weldability of the steel sheet, and adversely affects corrosion resistance. Therefore, in the invention, the Si content is controlled to be 0.4 to 0.5 percent, and the deoxidation effect is ensured, and the strength and the corrosion resistance are improved on the premise of not influencing the low-temperature toughness and weldability of the steel plate.
Mn: mn is a solid solution strengthening element that can improve the hardenability of the steel sheet, thereby improving the strength thereof, and can also be combined with a harmful element S to reduce the hot brittleness of the steel sheet. However, excessive Mn accelerates segregation of elements such as P, sb, and Sn, and further weakens the corrosion resistance of the steel sheet, and deteriorates the low-temperature toughness and weldability of the steel sheet core. Therefore, in the invention, the Mn content is controlled to be 1.15 to 1.25 percent, so that the strength of the steel plate can be ensured, and the influence of segregation on the corrosion resistance, the low-temperature toughness and the welding performance of the steel plate can be reduced.
Cr: cr can promote the loose incomplete oxidation phase in the rust layer on the steel surface to be converted into a more compact and stable phase, reduce the occurrence of pores and cracks in the rust layer and improve the corrosion resistance of the steel. Cr is gathered at the end of the rust layer close to the substrate to form a passive film, so that the anion selectivity of the rust layer is reduced, the infiltration of external anions is blocked, and the steel plate substrate is protected. When Cr and Cu act synergistically, alpha-FeOOH can be refined, and the stability of the rust layer is improved. However, when the Cr content is large, carbide is easily formed, and the corrosion resistance of the steel is lowered. Therefore, in the present invention, the corrosion resistance of the steel can be prevented from being deteriorated with time by controlling the Cr content to 0.2 to 0.3%.
Ni: the addition of the Ni element can shift the self-corrosion potential of the steel forward, increase the resistance generated by anodic dissolution reaction, promote the formation of an alpha-FeOOH phase in the rust layer, improve the stability of the rust layer, and possibly enrich the Ni element in the rust layer, so that the selectivity of anions of the rust layer is reduced, and the corrosion of a steel plate substrate is slowed down. In addition, the addition of Ni can improve the low-temperature toughness and weldability of the steel plate, but the addition of too much Ni results in higher alloy cost. Therefore, in the invention, the Ni content is controlled to be 0.5-0.6%, the corrosion resistance, low-temperature toughness and welding performance of the steel plate are ensured, and the alloy cost can be reasonably controlled.
Cu：The addition of Cu in steel has a good effect of improving the corrosion resistance of the steel, and the Cu is low in price, is widely applied to corrosion-resistant steel, and has various main action mechanisms: cu can hinder the crystallization of the rust layer and promote alpha-FeOOH and amorphous Fe 3 O 4 Forming; moreover, cu can be enriched at the weak part of the rust layer, an oxide is formed in the corrosion process, the rust layer and a steel matrix are tightly connected, cracks, gaps and the like in the rust layer are reduced, and the pitting corrosion resistance is improved; in addition, the Cu element has the function of activating the cathode, so that a steel matrix is passivated, and the corrosion rate is reduced. However, the high Cu content is not favorable for the weldability of the steel sheet. Therefore, in the invention, the Cu content is controlled to be 0.2 to 0.3 percent, so that the corrosion resistance is improved, and the welding performance is not influenced.
Nb: nb is a fine crystalline element and a strong carbide forming element, which can prevent C from being combined with Cr to influence the corrosion resistance of the steel plate, and can promote the rapid formation of alpha-FeOOH and the increase of the content. When the content of Nb is large, the low-temperature toughness of a heat affected zone of the welded joint is degraded and the corrosion resistance is adversely affected, so that the content of Nb is controlled to be 0.02 to 0.04 percent in the invention, the grain refining effect and the corrosion resistance are ensured, and the low-temperature toughness of the heat affected zone of the welded joint is not adversely affected.
Al: al is an important deoxidizing element, the content of Al is controlled within 0.02-0.04%, the beneficial effect of Al is guaranteed, the smelting difficulty is reduced, and the nozzle is prevented from being blocked in the casting process.
P: p is a typical element for improving the corrosion resistance of steel, and can play a role of an anode depolarizer and accelerate Fe 2+ The oxidation rate of the steel and the uniform dissolution of the steel can effectively help the steel surface to form a uniform alpha-FeOOH rust layer. And P can form PO 4 3- In one aspect, PO 4 3- Capable of complexing H + Improve the pH value of the interface, slow down the cathodic hydrogen evolution reduction reaction and slow down the dissolution of the rust layer, and on the other hand, PO 4 3- Can react with Fe in the anode dissolving process 2+ And Mn 2+ And the combination forms a phosphate film which is difficult to dissolve, and the phosphate film can block the anode dissolution reaction and play a role of a corrosion inhibitor. In addition, P and Cu are also preferableSo as to comprehensively play a role in improving the corrosion resistance of the steel. Meanwhile, P is also an easily segregated element, and when the content of P is too high, the low-temperature toughness and the welding performance of the core of the steel plate can be obviously reduced. Therefore, the content of P is controlled to be 0.015-0.025 percent in the invention, and the corrosion resistance is ensured, and meanwhile, the serious segregation is not generated, and the low-temperature toughness and the welding performance of the steel plate are not deteriorated.
Sn: the mechanism of action of Sn on corrosion resistance in steel is yet to be studied, and it is currently thought that Sn can form dense SnO on the surface of steel 2 And the protective rust layer plays a role in improving corrosion resistance. When the content of Sn is too high, the segregation is easy to occur in the grain boundary, and the low-temperature toughness and the welding performance are influenced, so that the content of Sn is controlled to be 0.02 to 0.10 percent in the invention, and the low-temperature toughness and the welding performance of the steel plate are ensured to be good on the premise of not reducing the corrosion resistance.
S, O and N: the content of the impurity elements is respectively controlled as follows: s is less than or equal to 0.002%, O is less than or equal to 0.002%, and N is less than or equal to 0.004%, and the design of the whole chemical composition is combined, so that the comprehensive performance of the steel plate is ensured, and the problems of high production difficulty and high production cost caused by too strict requirement on content control are avoided.
Further, the carbon equivalent CE of the steel plate is controlled to be less than or equal to 0.40 so as to ensure that the steel plate has good weldability, wherein the calculation formula of the carbon equivalent CE is as follows according to the B/T1591-2018 standard:
CE=(%C)+(%Mn)/6+(%Cr+%Mo+%V)/5+(%Ni+%Cu)/15。
the atmospheric corrosion resistance index I of the steel plate is more than or equal to 6.3, wherein the calculation formula of the atmospheric corrosion resistance index is as follows:
I=26.01(%Cu)+3.88(%Ni)+1.20(%Cr)+1.49(%Si)+17.28(%P)-7.29(%Cu)(%Ni)-9.10(%Ni)(%P)-33.39(%Cu) 2 ，
wherein, the element symbol in parentheses is the mass percentage of the corresponding element, and the% element symbol represents the mass percentage of the corresponding element multiplied by 100.
In conclusion, compared with the corrosion-resistant steel in the prior art, the corrosion-resistant steel has a low alloy component system formed by compounding low-C, low-Mn and low-S corrosion-resistant elements with Sb + Cr + Ni + Cu + P or Sb + Cr + Ni + Cu + P + Sn, and has a small addition amount of alloy elements, the adopted alloy system greatly reduces the raw material cost and the production difficulty of the steel plate on the premise of ensuring the corrosion resistance of the steel plate, and can effectively improve the low-temperature toughness and the welding performance of the steel plate, thereby obtaining the 390 MPa-grade steel plate for construction with excellent comprehensive performance and industrial atmospheric corrosion resistance.
The present invention also provides a method for producing the aforementioned steel sheet, which, in the present embodiment, comprises the steps of: the method comprises the steps of molten iron pre-desulfurization, converter smelting, LF refining, RH refining, continuous casting, heating, controlled rolling and controlled cooling.
Wherein, the rolling procedure is controlled to specifically include:
two-stage controlled rolling is adopted, including first-stage austenite recrystallization region rolling and second-stage austenite non-recrystallization region rolling, wherein the first-stage rolling is repeatedly staggered for deformation and recrystallization to fully recrystallize prior austenite grains, and the second-stage rolling is carried out at a high reduction below the recrystallization temperature to promote strain-induced precipitation of microalloy elements and realize refinement and processing hardening of the austenite grains, and deformation bands and a large number of dislocations are generated while the austenite grains are elongated, so that enough deformation energy is accumulated in the austenite grains, more nucleation positions are provided for phase transformation, and the grains are refined.
Specifically, in the second stage of rolling, the finishing temperature is controlled at 820 +/-15 ℃, and the micro-alloy element components and the addition amount are combined, so that the crystal grains can be effectively refined, and the low-temperature toughness of the steel plate is improved.
The controlled cooling process specifically comprises:
and (3) performing water cooling by adopting a multifunctional intermittent cooling system, and controlling the final cooling temperature of the steel plate to be 580 +/-30 ℃.
A Multi-purpose intermittent cooling system (MULPIC) is a rapid cooling device located after a finishing mill, which performs rapid cooling of a steel sheet according to a cooling model, and has main functions of controlling a cooling speed and a final cooling temperature, cooling the steel sheet to a prescribed quality and density, and ensuring balance of mechanical properties of the entire steel sheet. In the embodiment, the final cooling temperature is controlled at 580 +/-30 ℃, so that the deformed austenite is finally transformed into ferrite and pearlite, wherein the ferrite comprises polygonal ferrite, quasi-polygonal ferrite and acicular ferrite, and the pearlite content is less than or equal to 8%.
Pearlite is a eutectoid of ferrite and cementite, and the potential difference between ferrite and cementite is large, so that a corrosion micro-battery is easily formed, and thus, the corrosion resistance of pearlite is poor. The final rolling temperature of rolling control and the final cooling temperature of a cooling process are controlled to enable the pearlite content in the steel plate to be less than or equal to 8%, so that the adverse effect on the corrosion resistance of the steel plate caused by excessive pearlite content can be avoided, and the excellent corrosion resistance of the whole steel plate is ensured.
Furthermore, the grades of A, B, C, D type inclusions of the steel plate under the GB/T10561 standard are controlled to be less than or equal to 1.5, the sum of the grades of A, B, C, D type inclusions is controlled to be less than or equal to 3.0, and the surface density of the inclusions with the size of more than or equal to 15 mu m on the cross section of the steel plate is controlled to be less than or equal to 0.1/mm 2 。
The inclusions are the most sensitive sites of the initiation pitting, the size of the inclusions affects the initial formation size of pitting at the induction stage, wherein non-metallic inclusions having a circle equivalent diameter of more than 20 μm have the greatest influence on corrosion resistance, and therefore, the size and number of the inclusions need to be strictly controlled in order to ensure the corrosion resistance of the steel sheet.
The specific process parameters related to other process steps of the present invention may refer to the production process parameters of similar specification steel plates in the prior art, which is not specifically limited by the present invention.
Specifically, for the steel sheet finally obtained, the properties thereof were characterized as follows:
in the aspect of mechanical property, the yield strength of the steel plate is more than or equal to 390MPa, the tensile strength is 510-660 MPa, the yield ratio is less than or equal to 0.80, the elongation after fracture is more than or equal to 25 percent, and the impact absorption energy KV at minus 40℃ is more than or equal to KV 2 ≥150J。
In the aspect of corrosion resistance, in a periodic infiltration corrosion test, the average corrosion weight loss rate of the steel plate is less than or equal to 1.2 g/(m) 2 H), where periodic immersion corrosion tests are referenced TB/T2375-93Periodic infiltration corrosion test method of weathering steel for railway, the test conditions are:
temperature: 45. + -.2 ℃ humidity: 70. + -.5% RH, corrosion medium: (1.0. + -. 0.05). Times.10 -2 mol/L sodium bisulfite aqueous solution, cycle period: 60 +/-3 min, infiltration time: 12 ± 1.5min, duration of the experiment: for 72 hours.
In the aspect of welding performance, when the welding heat input of the steel plate is less than or equal to 100kJ/cm, the impact absorption energy KV of a heat affected zone at 40 ℃ below zero after welding 2 ≥80J。
In conclusion, the corrosion-resistant low-alloy component system with low C, low Mn and low S, sb + Cr + Ni + Cu + P or Sb + Cr + Ni + Cu + P + Sn adopted by the invention, which is compounded with Sb + Cr + Ni + Cu + P or Sb + Cr + Ni + Cu + P + Sn corrosion-resistant elements, is less in alloy element addition amount compared with the corrosion-resistant high-P, high-N, high-Ni, high-Cu or rare earth element-added alloy component system of the corrosion-resistant steel in the prior art, the adopted alloy system greatly reduces the raw material cost and the production difficulty of the steel plate on the premise of ensuring the corrosion resistance of the steel plate, and in the production flow, the microstructure, the size and the number of inclusions of the steel plate are accurately controlled by controlling the finish rolling temperature and the finish cooling temperature, so that the industrial atmospheric corrosion resistance, the low-temperature toughness and the welding performance of the steel plate are improved, and finally the 390 MPa-grade building plate with good comprehensive performance and industrial atmospheric corrosion resistance is obtained.
The following description will further describe embodiments of the present invention by 4 examples and 4 comparative examples.
Examples 1 to 4 and comparative examples 1 to 4 each provide a steel sheet whose chemical composition, carbon equivalent CE and atmospheric corrosion resistance index I are shown in Table 1.
Wherein, the Sb content of the comparative example 1 is less than 0.05 to 0.10 percent of the requirement of the invention, the Ni content is less than 0.5 to 0.6 percent of the requirement of the invention, the Cu content is less than 0.2 to 0.3 percent of the requirement of the invention, and the atmospheric corrosion resistance index I is less than 6.3 percent of the requirement of the invention.
The P content of the comparative example 2 is less than 0.015 to 0.025 percent of the requirement of the invention, the Cu content is less than 0.2 to 0.3 percent of the requirement of the invention, and the atmospheric corrosion resistance index I is less than 6.3 percent of the requirement of the invention.
The Si content of the comparative example 3 is less than 0.4-0.5%, the Cu content is less than 0.2-0.3%, and the atmospheric corrosion resistance index I is less than 6.3%.
Comparative example 4 is a conventional 390MPa grade construction steel, which does not contain Sb, cr, ni, cu, sn corrosion resistance elements.
The steel plate production methods in example 1~4 and comparative example 1~4 are both: the method comprises the steps of pre-desulfurizing molten iron, smelting in a converter, LF refining, RH refining, continuous casting, heating, controlled rolling and controlled cooling, wherein a finished steel plate is prepared after the controlled cooling process is finished.
In the controlled rolling process, steel plates with the thicknesses shown in the table 2 are prepared by adopting two-stage controlled rolling, and the finishing rolling temperature is 820 +/-15 ℃.
In the controlled cooling process, a multifunctional intermittent cooling system is adopted for water cooling, and the final cooling temperature is 580 +/-30 ℃.
The finishing temperatures and cold finishing temperatures for example 1~4 and comparative example 1~4 are specified in table 2.
After each of the steel sheets of example 1~4 and comparative example 1~4 was cooled, sampling test was performed, and the test results are described below.
The results of the inclusion test for example 1~4 and comparative example 1~4 are shown in table 3. As can be seen from Table 3, the surface densities of inclusions with a size of 15 μm or more in the cross-section of example 1~4 and comparative example 1~3 are 0.1 piece/mm or less 2 And the grade sum of A, B, C, D type inclusion is controlled to be less than or equal to 3.0 grade. In comparative example 4, the contents of Mn, S and O are higher than those required in the present invention, so that the inclusion content is more than 1.5 grade, and the sum of the grades of the four types of inclusions is more than 3.0 grade.
Yield strength, tensile strength, yield ratio, elongation after fracture, -40 ℃ impact absorption energy KV of steel plates in example 1~4 and comparative example 1~4 2 As shown in table 4. As can be seen from Table 4, the mechanical properties of the steel sheets in example 1~4 and comparative example 1~4 both satisfy the requirements of the present invention. In comparative example 4, the C content is higher than the requirement of the invention, the structure is ferrite plus pearlite, and the pearlite content is higher than 8 percent, so that the impact absorption energy KV at 40 ℃ below zero is KV 2 Below 150J.
Referring to TB/T2375-93 periodic infiltration Corrosion test method for Weathered Steel for railways, industrial atmosphere corrosion resistance of the steel sheets of example 1~4 and comparative example 1~4 was examined using a periodic infiltration Corrosion tester at 45. + -. 2 ℃ with a humidity of 70. + -.5 RH in a medium of (1.0. + -. 0.05). Times.10 RH -2 The test time of the mol/L sodium bisulfite aqueous solution is 72 hours, each cycle period is 60 plus or minus 3min, wherein the infiltration time is 12 plus or minus 1.5min. The average corrosion weight loss for example 1~4 and comparative example 1~4 are shown in table 5.
As can be seen from Table 5, the average corrosion weight loss ratios of the steel sheets of example 1~4 are all less than or equal to 1.2 g/(m) 2 H). The average corrosion weight loss ratios of the comparative examples 1~4 are all higher than the requirements of the present invention, with the industrial atmospheric corrosion resistance of comparative example 4 being the worst.
The results of the-40 ℃ low-temperature impact power measurements at the weld joint heat affected zone weld lines FL, FL +2mm, FL +5mm and FL +20mm, which were obtained by twin wire submerged arc welding in example 4, with an ambient temperature of 2 ℃, without preheating before welding, without heat insulation or heat treatment after welding, and with a weld heat input of 97. + -.3 kJ/cm, are shown in Table 4. As is clear from table 6, example 4 is excellent in welding performance.
As shown in fig. 1, the metallographic structure picture at the 1/4 thickness of the steel plate provided in example 4 of the present invention is shown in fig. 2, the metallographic structure picture at the 1/2 thickness of the steel plate provided in example 4 of the present invention is shown in fig. 3, and the metallographic structure picture at the 1/4 thickness of the steel plate provided in comparative example 4 of the present invention is shown in fig. 4. As can be seen from comparison between fig. 1 and fig. 3, the grains of the steel sheet after the addition of the alloy elements are significantly finer, and it can be observed in fig. 3 that the amount of pearlite appearing black is greater and the distribution is denser.
By combining the detection results, the 390 MPa-grade corrosion-resistant steel plate provided by the invention has the advantages of controllable cost, simple and efficient process flow, excellent industrial atmosphere corrosion resistance, low-temperature toughness and excellent welding performance, and is favorable for popularization and application in the field of steel structure buildings.
It should be understood that although the present description refers to embodiments, not every embodiment contains only a single technical solution, and such description is for clarity only, and those skilled in the art should make the description as a whole, and the technical solutions in the embodiments can also be combined appropriately to form other embodiments understood by those skilled in the art.
The above-listed detailed description is merely a detailed description of possible embodiments of the present invention and is not intended to limit the scope of the invention, which is intended to include within the scope of the invention all equivalent embodiments or modifications that do not depart from the technical spirit of the present invention.
Claims (11)
1. A390 MPa-grade corrosion-resistant steel plate is characterized in that the chemical components of the steel plate comprise the following components in percentage by mass: 0.05 to 0.10 percent of Sb, 0.07 to 0.10 percent of C, 0.4 to 0.5 percent of Si, 1.15 to 1.25 percent of Mn, 0.2 to 0.3 percent of Cr, 0.5 to 0.6 percent of Ni, 0.2 to 0.3 percent of Cu, 0.02 to 0.04 percent of Nb, 0.02 to 0.04 percent of Al, 0.015 to 0.025 percent of P and the balance of Fe and inevitable impurities, wherein the impurities comprise: s is less than or equal to 0.002%, O is less than or equal to 0.002%, and N is less than or equal to 0.004%;
the atmospheric corrosion resistance index I of the steel plate is more than or equal to 6.3, wherein the calculation formula of the atmospheric corrosion resistance index is as follows:
I=26.01(%Cu)+3.88(%Ni)+1.20(%Cr)+1.49(%Si)+17.28(%P)-7.29(%Cu)(%Ni)-9.10(%Ni)(%P)-33.39(%Cu) 2 ，
wherein, the element symbol in the bracket is the mass percent of the corresponding element, the% element symbol represents the mass percent of the corresponding element multiplied by 100;
the microstructure of the steel plate comprises ferrite and pearlite, wherein the content of the pearlite is less than or equal to 8%, and the ferrite comprises polygonal ferrite, quasi-polygonal ferrite and acicular ferrite;
the thickness of the steel plate is not more than 100mm;
the yield strength of the steel plate is more than or equal to 390MPa, and when the welding heat input of the steel plate is less than or equal to 100kJ/cm, the impact absorption energy KV at 40 ℃ below zero in the heat affected zone after welding 2 ≥80J。
2. The 390MPa grade corrosion resistant steel plate of claim 1, wherein the chemical composition of the steel plate further comprises, in mass percent: 0.02 to 0.10 percent of Sn.
3. The 390MPa grade corrosion resistant steel plate of claim 1, wherein the carbon equivalent CE of the steel plate is less than or equal to 0.40, wherein the calculation formula of the carbon equivalent CE is as follows:
CE=(%C)+(%Mn)/6+(%Cr+%Mo+%V)/5+(%Ni+%Cu)/15，
wherein, the symbol of the element in parentheses is the mass percentage of the corresponding element, and the symbol of% element represents the mass percentage of the corresponding element multiplied by 100.
4. The 390 MPa-grade corrosion-resistant steel plate of claim 1, wherein the grades of A, B, C, D inclusions of the steel plate under GB/T10561 standard are respectively less than or equal to 1.5 grades, the sum of the grades of A, B, C, D inclusions is less than or equal to 3.0 grades, and the surface density of the inclusions with the size of more than 15 μm on the cross section of the steel plate is less than or equal to 0.1 piece/mm 2 。
5. The 390 MPa-grade corrosion-resistant steel plate according to claim 1, wherein the steel plate has a tensile strength of 510-660 MPa, a yield ratio of not more than 0.80, an elongation after fracture of not less than 25%, and an impact absorption energy KV at-40 ℃ of absorbed energy 2 ≥150J。
6. The 390MPa grade corrosion resistant steel plate of claim 1, wherein the average corrosion weight loss rate of the steel plate is less than or equal to 1.2 g/(m) in periodic immersion corrosion test 2 H), wherein the test conditions of the periodic immersion corrosion test are:
temperature: 45. + -.2 ℃ humidity: 70. + -.5% RH, corrosive medium: (1.0. + -. 0.05). Times.10 -2mol L aqueous sodium bisulfite, cycle period: 60 +/-3 min, infiltration time: 12 ± 1.5min, duration of the test: for 72 hours.
7. A 390MPa grade corrosion resistant steel sheet according to claim 1, characterized in that the method of production of said steel sheet comprises the following steps performed in sequence:
pre-desulfurizing molten iron, smelting in a converter, LF refining, RH refining, continuous casting, heating, rolling control and cooling control.
8. The 390MPa grade corrosion resistant steel plate of claim 7, wherein the controlled rolling process adopts two-stage controlled rolling, wherein the finishing temperature is controlled at 820 +/-15 ℃.
9. The 390MPa grade corrosion resistant steel plate of claim 7, wherein in the controlled cooling process, a multifunctional intermittent cooling system is adopted for water cooling, and the final cooling temperature of the steel plate is controlled at 580 +/-30 ℃.
10. The method for producing a corrosion-resistant steel plate of 390MPa grade according to claim 1,
the steel plate comprises the following chemical components in percentage by mass: 0.05 to 0.10 percent of Sb, 0.07 to 0.10 percent of C, 0.4 to 0.5 percent of Si, 1.15 to 1.25 percent of Mn, 0.2 to 0.3 percent of Cr, 0.5 to 0.6 percent of Ni, 0.2 to 0.3 percent of Cu, 0.02 to 0.04 percent of Nb, 0.02 to 0.04 percent of Al, 0.015 to 0.025 percent of P, and the balance of Fe and inevitable impurities, wherein the impurities comprise: s is less than or equal to 0.002%, O is less than or equal to 0.002%, and N is less than or equal to 0.004%;
the production method comprises the following steps: pre-desulfurizing molten iron, smelting in a converter, LF refining, RH refining, continuous casting, heating, rolling control and cooling control;
wherein the controlled rolling process specifically comprises:
two-stage controlled rolling is adopted, wherein the two-stage controlled rolling comprises a first-stage austenite recrystallization region rolling and a second-stage austenite non-recrystallization region rolling, the finishing rolling temperature in the second-stage austenite non-recrystallization region rolling is controlled at 820 +/-15 ℃, and a continuous casting billet obtained through the continuous casting is rolled into a steel plate with the thickness not more than 100mm;
and (2) performing water cooling by adopting a multifunctional intermittent cooling system, controlling the final cooling temperature of the steel plate to be 580 +/-30 ℃, and controlling the microstructure of the steel plate to comprise ferrite and pearlite after a controlled cooling process, wherein the content of the pearlite is less than or equal to 8%, and the ferrite comprises polygonal ferrite, quasi-polygonal ferrite and acicular ferrite.
11. The method for producing the 390MPa grade corrosion resistant steel plate according to claim 10, wherein the chemical composition of the steel plate further comprises, in mass percent: 0.02 to 0.10 percent of Sn.
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| CN112458381A (en) * | 2020-11-04 | 2021-03-09 | 江苏省沙钢钢铁研究院有限公司 | Short-process 500 MPa-grade weather-resistant and earthquake-resistant reinforcing steel bar and preparation method thereof |
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Address after: 215624 Shagang science and technology building, Yongxin Road, Jinfeng Town, Zhangjiagang City, Suzhou City, Jiangsu Province Patentee after: INSTITUTE OF RESEARCH OF IRON & STEEL, JIANGSU PROVINCE/SHA-STEEL, Co.,Ltd. Country or region after: China Patentee after: Jiangsu Shagang Steel Co.,Ltd. Patentee after: JIANGSU SHAGANG GROUP Co.,Ltd. Address before: 215624 Shagang science and technology building, Yongxin Road, Jinfeng Town, Zhangjiagang City, Suzhou City, Jiangsu Province Patentee before: INSTITUTE OF RESEARCH OF IRON & STEEL, JIANGSU PROVINCE/SHA-STEEL, Co.,Ltd. Country or region before: China Patentee before: ZHANGJIAGANG HONGCHANG STEEL PLATE Co.,Ltd. Patentee before: JIANGSU SHAGANG GROUP Co.,Ltd. |