CN117144253B - Niobium microalloyed hot rolled ribbed steel bar and production method thereof - Google Patents
Niobium microalloyed hot rolled ribbed steel bar and production method thereof Download PDFInfo
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- CN117144253B CN117144253B CN202311149198.5A CN202311149198A CN117144253B CN 117144253 B CN117144253 B CN 117144253B CN 202311149198 A CN202311149198 A CN 202311149198A CN 117144253 B CN117144253 B CN 117144253B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 127
- 239000010959 steel Substances 0.000 title claims abstract description 127
- 239000010955 niobium Substances 0.000 title claims abstract description 77
- 229910052758 niobium Inorganic materials 0.000 title claims abstract description 60
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 title claims abstract description 54
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 22
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 22
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 14
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 14
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 133
- 238000001816 cooling Methods 0.000 claims description 59
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 43
- 238000009749 continuous casting Methods 0.000 claims description 37
- 238000010438 heat treatment Methods 0.000 claims description 32
- 229910052742 iron Inorganic materials 0.000 claims description 20
- 238000007670 refining Methods 0.000 claims description 15
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 15
- 238000000034 method Methods 0.000 claims description 13
- 239000011572 manganese Substances 0.000 claims description 11
- 238000005266 casting Methods 0.000 claims description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 8
- 230000009467 reduction Effects 0.000 claims description 8
- 238000010079 rubber tapping Methods 0.000 claims description 8
- 238000002791 soaking Methods 0.000 claims description 8
- 238000007664 blowing Methods 0.000 claims description 7
- 239000007789 gas Substances 0.000 claims description 7
- 238000009628 steelmaking Methods 0.000 claims description 7
- 230000001681 protective effect Effects 0.000 claims description 6
- 229910000914 Mn alloy Inorganic materials 0.000 claims description 5
- 238000003723 Smelting Methods 0.000 claims description 5
- PYLLWONICXJARP-UHFFFAOYSA-N manganese silicon Chemical compound [Si].[Mn] PYLLWONICXJARP-UHFFFAOYSA-N 0.000 claims description 5
- 230000008569 process Effects 0.000 claims description 5
- 239000000654 additive Substances 0.000 claims description 4
- 230000000996 additive effect Effects 0.000 claims description 4
- 229910052786 argon Inorganic materials 0.000 claims description 4
- 238000006477 desulfuration reaction Methods 0.000 claims description 4
- 230000023556 desulfurization Effects 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- 229910000592 Ferroniobium Inorganic materials 0.000 claims description 3
- 238000005520 cutting process Methods 0.000 claims description 3
- 238000004806 packaging method and process Methods 0.000 claims description 3
- 239000000843 powder Substances 0.000 claims description 3
- 238000007599 discharging Methods 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 description 13
- 229910001566 austenite Inorganic materials 0.000 description 12
- 238000001556 precipitation Methods 0.000 description 11
- 238000005728 strengthening Methods 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910001294 Reinforcing steel Inorganic materials 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 230000003014 reinforcing effect Effects 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 230000007547 defect Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910001341 Crude steel Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 239000004743 Polypropylene Substances 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- CKUAXEQHGKSLHN-UHFFFAOYSA-N [C].[N] Chemical compound [C].[N] CKUAXEQHGKSLHN-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000008878 coupling Effects 0.000 description 1
- 238000010168 coupling process Methods 0.000 description 1
- 238000005859 coupling reaction Methods 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000006386 neutralization reaction Methods 0.000 description 1
- 229910017464 nitrogen compound Inorganic materials 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- -1 polypropylene Polymers 0.000 description 1
- 229920001155 polypropylene Polymers 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000012795 verification Methods 0.000 description 1
Classifications
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
- B21B1/18—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section in a continuous process
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- 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
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
-
- 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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- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a niobium microalloyed hot rolled ribbed steel bar and a production method thereof. The chemical components in the niobium microalloyed hot rolled ribbed steel bar are as follows by weight percent: c:0.20 to 0.25 percent, si:0.20 to 0.30 percent of Mn:1.10 to 1.30 percent, 0.005 to 0.010 percent of Nb, and P: <0.045%, S: <0.045%, N <0.008%; the balance of Fe and impurity elements, wherein the metallographic structure of the niobium microalloyed hot rolled ribbed steel bar only comprises ferrite and pearlite.
Description
Technical Field
The invention belongs to the technical field of hot rolled steel bar production, and provides a niobium microalloyed hot rolled ribbed steel bar and a production method thereof.
Background
The hot rolled ribbed steel bar (hereinafter referred to as steel bar) for concrete is the largest single steel variety in China, and accounts for more than 20% of crude steel output in China for a long time, and more than 60% of the area in China is in an earthquake prone area, so that the product upgrading and quality improvement of the anti-seismic steel bar are not only related to the life and property safety of buildings and people, but also have great significance for the high-quality development of the steel industry and the strategy of carbon peak and carbon neutralization.
In the prior art, the national standard of the concrete hot rolled ribbed steel bar implemented in China is GB/T1499.2-2018, the standard provides requirements on the strength grade, the production process, the metallographic structure and the like of the steel bar, the yield strength under the requirements of the HRB400 (E) with the lowest strength grade in the standard is more than 400MPa, the tensile strength is more than 540MPa, the HRB400E meeting the earthquake-resistant requirements also requires that the yield ratio (actually measured tensile strength/actually measured yield strength) is not lower than 1.25, the Qu Biao ratio (actually measured yield strength/400 MPa) is not higher than 1.30, and the maximum force total extension rate is not lower than 9%.
At present, the method for producing HRB400E steel bars in steel mills mainly adopts vanadium or niobium microalloying. Since niobium can expand the austenite non-recrystallization region, performance improvement is achieved by low temperature controlled rolling. Patent publication No. CN100465321C, entitled steel for controlled cooling reinforcing bar containing micro niobium and production method thereof, discloses that 400MPa grade reinforcing bar is obtained by adding 0.005-0.015% Nb and combining controlled cooling of rolled piece in rolling process. However, the hot-rolled steel bar produced by this method has a microstructure of ferrite+pearlite of 85% or more, and it is unavoidable to have a microstructure such as bainite (granular bainite). This can result in an insignificant yield stress of the tensile curve in the mechanical property test of the obtained bar, thereby affecting the performance. In addition, the higher Si content in this patent also results in higher alloy costs.
Patent publication No. CN 113373377B, the invention name is "low-cost high-speed bar threaded steel with surface iron scale thickness more than 10 μm and production method", discloses that Nb is added in an amount of 0.015-0.035% for component design, and the Nb-contained HRB400E straight threaded steel bar with phi 10-phi 25 is obtained through high-speed bar rolling. However, the addition amount of Nb is high in the manufacturing process of the reinforcing steel bar, so that the reinforcing steel bar is not beneficial to wide popularization and application.
Disclosure of Invention
In order to solve at least one of the problems and defects in the prior art, the invention provides a niobium microalloyed hot rolled ribbed steel bar and a production method thereof, and under the condition of keeping adding a trace amount of niobium, the niobium microalloyed hot rolled ribbed steel bar is obtained, and the metallographic structures of the niobium microalloyed hot rolled ribbed steel bar are ferrite and pearlite.
According to one aspect of the present invention, there is provided a niobium micro-alloyed hot rolled ribbed steel bar comprising the following chemical components in weight percent: c:0.20 to 0.25 percent, si:0.20 to 0.30 percent of Mn:1.10 to 1.30 percent, 0.005 to 0.010 percent of Nb, and P: <0.045%, S: <0.045%, N <0.008%; the balance of Fe and impurity elements, wherein the metallographic structure of the niobium microalloyed hot rolled ribbed steel bar only comprises ferrite and pearlite.
Further, in the case of niobium as a trace additive element, the niobium microalloyed hot rolled ribbed steel bar is obtained by controlling parameters of rolling and cooling.
Further, a billet for producing the niobium microalloyed hot rolled ribbed steel bar is discharged from a furnace and subjected to a continuous rolling process after water descaling, wherein the continuous rolling process comprises roughing mill rolling, intermediate mill rolling, pre-finishing mill rolling and finishing mill rolling.
Further, the niobium microalloyed hot rolled ribbed steel bar is obtained by controlling the mill power of the pre-finish rolling stage and controlling the parameters of the cooling conditions.
Further, in the continuous rolling process, the steel billet passes through a water cooling device, the initial rolling temperature of the steel billet is 960-980 ℃, the temperature of the steel billet after rolling by a middle rolling mill group is 850-880 ℃, the steel billet after the pre-finish rolling is cooled to 750-800 ℃ by water and is rolled by a finish rolling mill group, and the reduction rate of the total cross section area in the finish rolling stage is more than 70%.
Further, after finish rolling, cooling the surface of the steel bar to 550-600 ℃ by graded cooling, wherein the cooling rate is more than 100 ℃/s; after the temperature is returned, the surface temperature of the steel bar is 750-780 ℃ and the steel bar is slowly cooled by a cooling bed.
Further, before continuous rolling, the billet is further subjected to molten iron pretreatment, converter steelmaking, refining, continuous casting and continuous casting billet heating, wherein in the continuous casting billet heating, the continuous casting billet is heated in a walking beam heating furnace, the soaking temperature is controlled between 980 ℃ and 1000 ℃, and the heating time is 60min to 80min.
According to another aspect of the present invention, there is provided a method for producing a niobium micro-alloyed hot-rolled ribbed steel bar, which is the above-mentioned niobium micro-alloyed hot-rolled ribbed steel bar,
The production method comprises the following steps:
(1) Providing blast furnace molten iron;
(2) And (3) molten iron pretreatment: the weight percentage of S content of the blast furnace molten iron after the desulfurization process is controlled to be less than 0.015 percent;
(3) Converter steelmaking: adding desulphurized molten iron into a converter, controlling the loading amount of scrap steel to be not more than 15% of the total loading amount, and finishing converting after reaching the end point component and tapping temperature; adding a deoxidizer to deoxidize molten steel when the steel is tapped 1/3, adding a silicon-manganese alloy element and a carburant, adding the molten steel when the steel is tapped 2/3, and transferring to refining after the steel tapping is finished;
(4) Refining: blowing protective gas into the ladle to refine for at least 10min, adding ferrocolumbium after the blowing protective gas is refined and deoxidized well, stopping refining after the smelting components are qualified, and starting pouring;
(5) Continuous casting: the continuous casting tundish adopts alkaline casting powder, the continuous casting ladle and the tundish adopt long water gap protection casting, the superheat degree of the tundish is not more than 15 ℃, and finally a continuous casting blank is obtained;
(6) Heating a continuous casting blank: heating the continuous casting blank in a heating furnace, wherein the soaking temperature is controlled between 980 ℃ and 1000 ℃ and the heating time is 60-80 min;
(7) Controlling rolling and cooling control: the billet is discharged from the furnace and subjected to water descaling, and then is continuously rolled, wherein the continuous rolling comprises rough rolling unit rolling, intermediate rolling unit rolling, pre-finishing rolling unit rolling and finishing rolling unit rolling, during which, a water cooling device is used for cooling the billet, the rough rolling start temperature of the billet in the rough rolling unit is 960-980 ℃, the temperature of the billet in the intermediate rolling unit rolling is 850-880 ℃, the billet enters the pre-finishing rolling unit, and after the billet exits the pre-finishing rolling unit, the billet is cooled to 750-800 ℃ by water and then is fed into the finishing rolling unit for finish rolling;
(8) Cooling after rolling: and after finish rolling, cooling the surface of the steel bar in a grading way, controlling the cooling speed to be 550-600 ℃, wherein the cooling speed is more than 100 ℃/s, the temperature of the surface of the steel bar after temperature return is 750-780 ℃, and slowly cooling the steel bar on a cooling bed to obtain the niobium microalloyed hot rolled ribbed steel bar.
Further, the shielding gas comprises argon, and the cross section size of the continuous casting blank is 150mm multiplied by 150mm to 170mm multiplied by 170mm;
the heating furnace in the step of heating the casting blank is a walking beam heating furnace.
Further, the reduction rate of the total cross-sectional area of the finish rolling stage is more than 70%;
In the controlled cooling step after rolling, after the steel bar is slowly cooled by a cooling bed, the niobium microalloyed hot rolled ribbed steel bar is obtained after cutting to length, bundling and packaging.
The niobium microalloyed hot rolled ribbed steel bar and the method of producing the same according to embodiments of the invention have at least one of the following advantages:
(1) The invention adopts the component design of Nb microalloying, and combines the control of rolling to control the performance index of the steel bar produced by cooling to meet the requirements that the lower yield strength is more than or equal to 425MPa, the tensile strength is more than or equal to 570MPa, the total maximum force elongation is more than or equal to 12 percent, the tensile strength/yield strength is more than or equal to 1.30, and the characteristic value of yield strength/yield strength is less than or equal to 1.12; all meet the performance requirements of HRB400E in GB/T1499.2, the metallographic structure is ferrite and pearlite, and the size covers the diameter of 6 mm-16 mm.
(2) In the embodiment of the invention, the alloy is economical only through microalloying of the silicon-manganese alloy and the Nb.
Drawings
These and/or other aspects and advantages of the present invention will become apparent and readily appreciated from the following description of the preferred embodiments, taken in conjunction with the accompanying drawings, in which:
FIG. 1A is a metallographic photograph of a microstructure of a hot rolled earthquake-resistant steel bar having a yield strength of 425MPa grade, obtained according to example 1 of the present invention;
FIG. 1B is a metallographic photograph of a microstructure of a hot rolled earthquake-resistant steel bar having a yield strength of 425MPa grade, obtained in example 2 according to the present invention;
FIG. 1C is a metallographic photograph of a microstructure of a hot rolled earthquake-resistant steel bar having a yield strength of 425MPa grade, obtained in example 3 according to the present invention;
Fig. 2 is a flowchart of a method of producing a niobium microalloyed hot rolled ribbed steel bar in accordance with another embodiment of the invention.
Detailed Description
The technical scheme of the invention is further specifically described below through examples and with reference to the accompanying drawings. In the specification, the same or similar reference numerals denote the same or similar components. The following description of embodiments of the present invention with reference to the accompanying drawings is intended to illustrate the general inventive concept and should not be taken as limiting the invention.
In order to realize the performance improvement of the niobium micro-alloyed hot rolled ribbed steel bar, the invention provides the niobium micro-alloyed hot rolled ribbed steel bar and a corresponding production method.
In particular, the invention provides a high-performance reinforcing steel bar material by controlling rolling and cooling parameters in the reinforcing steel bar production method under the condition of keeping the addition of trace niobium elements, and the metallographic structures of the high-performance reinforcing steel bar material are ferrite and pearlite. Or only the metallographic structure of the steel bar provided by the invention can be seen as ferrite and pearlite in the metallographic photograph of the steel bar, and no bainite structure is seen.
In a preferred embodiment, the invention achieves that the metallographic structure of the steel bar is only ferrite and pearlite by controlling the power and cooling conditions of the finish rolling stage of the steel billet in the production method.
In a preferred embodiment, the rebars may be HRB400 (E) rebars meeting the performance requirements of HRB400E in GB/T1499.2, the structure being ferrite and pearlite, the dimensions being in the range 6mm to 16mm in diameter.
In one example, the chemical composition in the niobium microalloyed hot rolled ribbed steel bar is as follows by weight percent: c:0.20 to 0.25 percent, si:0.20 to 0.30 percent of Mn:1.10 to 1.30 percent, 0.005 to 0.010 percent of Nb, and P: <0.045%, S: <0.045%, N <0.008%; the balance of Fe and impurity elements, wherein the metallographic structure of the niobium microalloyed hot rolled ribbed steel bar only comprises ferrite and pearlite.
In the case of niobium as a trace additive element, the niobium microalloyed hot rolled ribbed bar is obtained by controlling parameters of rolling and cooling.
Further, a billet for producing the niobium microalloyed hot rolled ribbed steel bar is discharged from a furnace and subjected to a continuous rolling process after water descaling, wherein the continuous rolling process comprises roughing mill rolling, intermediate mill rolling, pre-finishing mill rolling and finishing mill rolling.
Specifically, the niobium microalloyed hot rolled ribbed steel bar is obtained by controlling the mill power of the pre-finish rolling stage and controlling the parameters of the cooling conditions.
In the continuous rolling process, the billet is subjected to a water cooling device, the initial rolling temperature of the billet is 960-980 ℃, the temperature of the billet is 850-880 ℃ after being rolled by a middle rolling mill group, the billet after being subjected to the pre-finish rolling is subjected to water cooling to 750-800 ℃ and is rolled by a finish rolling mill group, and the reduction rate of the total section area in the finish rolling stage is more than 70%.
Further, after finish rolling, cooling the surface of the steel bar to 550-600 ℃ by graded cooling, wherein the cooling rate is more than 100 ℃/s; after the temperature is returned, the surface temperature of the steel bar is 750-780 ℃ and the steel bar is slowly cooled by a cooling bed.
Before continuous rolling, the billet is further subjected to molten iron pretreatment, converter steelmaking, refining, continuous casting and continuous casting heating, wherein in the continuous casting heating, the continuous casting is heated in a walking beam heating furnace, the soaking temperature is controlled between 980 ℃ and 1000 ℃, and the heating time is 60min to 80min.
The action and proportion of each additive element in the steel bar are as follows:
Carbon (C): carbon is the most effective and cheap element for improving the strength of the steel bar, and the tensile strength and the yield strength of the steel are improved along with the increase of the content of C, so that the strength of the steel bar is ensured, and the welding performance is not reduced due to the excessively high content of the carbon, so that the content of C in the steel bar is limited to be 0.20-0.25%.
Silicon (Si): silicon is a common deoxidizing element, has a strong solid solution strengthening effect, is beneficial to improving the strength of steel, but is not beneficial to generating iron scales with protective effect on the outer surface of the steel bar when the content of Si is too high, and can increase the alloy cost.
Manganese (Mn): manganese is an important toughening element, a good deoxidizing agent and a good desulfurizing agent, too low Mn can not ensure the strength of steel, too high Mn has adverse effect on the center segregation of a steel billet, and for the invention, the content range of the Mn is limited to 1.10-1.30%, so that the content ratio of silicon to manganese of the steel bar can be achieved by directly adding the Si-Mn alloy element.
Phosphorus (P) and sulfur (S): the impurity elements in the steel obviously reduce the plasticity, toughness and welding performance, and the lower the content of the impurity elements is, the better the content is, and the content is controlled below 0.045 percent under the condition of not obviously increasing the cost.
Niobium (Nb): niobium is a strong carbon nitrogen compound forming element and can raise the austenitic non-recrystallization temperature of steel. The rolling of the austenite non-recrystallization zone can be carried out at a higher rolling temperature, so that austenite grains with more nucleation positions are obtained, and fine tissues are obtained through austenite transformation; in addition, during the controlled rolling process, the Nb can spike austenite grains through strain-induced precipitation of carbonitrides of Nb, refine the austenite grains and enhance the strength through precipitation strengthening in austenite and ferrite. Meanwhile, on the premise of meeting the performance requirement, the invention is economically used, and the content of the modified polypropylene is set to be 0.005-0.010%.
Nitrogen (N): the nitrogen content is generally 0.0050% in converter steelmaking, which is limited in the invention
N <0.008% mainly for reducing the temperature at which niobium carbonitride is solid-dissolved in austenite and the precipitation temperature
The steel billet heating temperature during rolling is not excessively high, and the strengthening effect of niobium is more fully exerted.
The niobium microalloyed hot rolled ribbed bar of the invention may be an earthquake resistant threaded HRB400E bar.
According to another embodiment of the present invention, there is provided a method of producing a niobium microalloyed hot rolled ribbed bar. As shown in fig. 2, the production method includes the following steps: (1) providing blast furnace molten iron (blast furnace molten iron), 2 molten iron pretreatment, 3 converter smelting, 4 refining, 5 continuous casting, 6 continuous casting billet heating, 7 controlled rolling and controlled cooling, and 8 controlled cooling after rolling.
Specifically, the main content of each step is as follows:
(1) Smelting molten iron in a blast furnace;
(2) And (3) molten iron pretreatment: the weight percentage control of S content of the blast furnace molten iron after the desulfurization process is as follows: less than 0.015%;
(3) Converter steelmaking: adding the molten iron subjected to desulfurization treatment in the step (2) into a converter, controlling the steel scrap loading to be less than 15% of the total loading, and reaching a final component (or target component) and a tapping temperature
After the blowing is finished, the sliding plate stops slag and taps, deoxidizing agent is added to deoxidize molten steel when tapping is carried out for 1/3, silicon-manganese alloy element and carburant with proper content are added, the adding is finished when tapping is carried out for 2/3, and the refining is carried out after tapping is finished;
(4) Refining: blowing protective gas such as argon into the ladle to refine for not less than 10min, adding ferrocolumbium after the argon blowing refining deoxidization is good, stopping refining after the smelting components are qualified, and starting pouring;
(5) Continuous casting: the continuous casting tundish adopts alkaline casting powder, the continuous casting ladle and the tundish adopt long nozzle for protection casting, the superheat degree of the tundish is not more than 15 ℃, and the cross section size is 150mm multiplied by 150mm
-170 Mm x 170mm continuous casting;
(6) Heating a continuous casting blank: heating the continuous casting blank in a walking beam heating furnace, and controlling the soaking temperature to be the same as that of the continuous casting blank
The heating time is 60 min-80 min at 980-1000 ℃.
The invention can control the soaking temperature of the continuous casting blank to ensure that the micro-niobium casting blank
Nb (C, N) is completely dissolved and uniformly diffused, and can effectively prevent the growth of austenite grains from being excessively large. At the same time, the method comprises the steps of,
The lower soaking temperature also reduces the starting rolling temperature of the continuous casting blank, and is beneficial to the effect of refining grains by rolling in each pass.
(7) Rolling stage (controlled rolling controlled cooling): the billet is continuously rolled after being discharged from the furnace and water is removed from the scale,
The continuous rolling comprises rough rolling unit rolling, intermediate rolling unit rolling, pre-finishing rolling unit rolling and finishing rolling unit rolling
During the process, the steel billet passes through a water cooling device, and the rough rolling start temperature of the steel billet in a rough rolling unit is
After rolling in a middle rolling mill set, the temperature in a prefinishing mill set is 850-880 ℃, after the billet is discharged from the prefinishing mill set, the billet is water-cooled to 750-800 ℃ and then fed into a finishing mill set for finish rolling,
Wherein the reduction rate of the total cross-sectional area in the finish rolling stage is more than 70% (total cross-sectional area reduction rate= (cross-sectional area before finish rolling-cross-sectional area after finish rolling)/cross-sectional area before finish rolling);
According to the invention, through implementing the temperature requirement on the billet into the pre-finishing mill, fine austenite grains can be obtained, and preparation is made for the subsequent finish rolling process. When finish rolling is performed according to the above process, nb (C, N) can be induced to precipitate by deformation, while the precipitation temperature of Nb (C, N) is coupled with ferrite transformation temperature, and fine Nb (C, N) precipitated alternately at the time of transformation from austenite to ferrite is utilized to prevent growth of phase-change ferrite grains, thereby improving strength of the steel bar by obtaining fine grain structure on one hand, and fine precipitation on the other hand
Nb (C, N) plays a role in precipitation strengthening.
Through actual production verification, the larger the reduction rate of the cross section surface of the steel billet in the finish rolling deformation stage is, the higher the precipitation temperature of Nb (C, N) is, the higher the defect density of deformed austenite is, the higher the temperature for promoting ferrite transformation is, and when the temperature is more than 70%, the coupling between Nb (C, N) precipitation and ferrite transformation can be realized, and the strengthening effect brought by precipitation strengthening and grain refinement is obvious.
(8) Cooling after rolling: after finish rolling, cooling the surface of the steel bar in a grading way, and cooling the steel bar until the steel bar is cooled
550-600 ℃, And the cooling speed is more than 100 ℃/s; after the temperature is returned, the surface temperature of the steel bar is 750-780 ℃, the steel bar is slowly cooled by a cooling bed, and the steel bar is obtained after cutting to length, bundling and packaging.
According to the invention, through controlling and cooling after finish rolling of the steel bar, the growth of the phase-change ferrite and the deformed ferrite after recrystallization is prevented by rapid cooling, and refined grains after finish rolling are reserved; while suppressing precipitation
Coarsening of Nb (C, N) ensures fine-grain strengthening and precipitation strengthening effects. When the surface of the steel bar is cooled to
At 550-600 ℃, macroscopic metallographic phase of the alloy is not closed, and metallographic phase structures at all positions are ferrite and pearlite, so that the requirements of the structure and the performance of GB1499.2-2018 are met.
The actual chemical compositions of the niobium microalloyed hot rolled ribbed steel bar (hereinafter referred to as steel bar) prepared according to the above production method of the present invention are shown in table 1.
TABLE 1 chemical composition (wt%) of the reinforcing bars of the present invention
| Examples | C | Si | Mn | P | S | Nb | N |
| 1 | 0.020 | 0.20 | 1.10 | 0.025 | 0.015 | 0.005 | 0.0050 |
| 2 | 0.024 | 0.28 | 1.20 | 0.031 | 0.026 | 0.007 | 0.0053 |
| 3 | 0.025 | 0.30 | 1.30 | 0.040 | 0.020 | 0.010 | 0.0051 |
The actual technological parameters of the steel bars with various specifications produced by the invention are shown in table 2, and the performance index results of the steel bars after rolling the steel bars to be subjected to the line drawing are shown in table 3. As can be seen from table 3, the various indexes of the steel bars of various specifications produced by the invention reach: the yield strength is more than or equal to 425MPa, the tensile strength is more than or equal to 570MPa, the maximum force total elongation is more than or equal to 12%, the tensile strength/yield strength is more than or equal to 1.30, and the characteristic value of yield strength/yield strength is less than or equal to 1.12. The metallographic structures of the examples are shown in FIGS. 1A to 1C, respectively, and the metallographic structures are ferrite and pearlite structures.
Table 2 rolling process parameters of the steel bars of the present invention
TABLE 3 results of various Performance indicators of the reinforcing bars of the present invention
Compared with the related prior art, the niobium microalloyed hot rolled ribbed steel bar and the production method thereof provided by the embodiment of the invention have at least one of the following advantages:
(1) The invention adopts the component design of Nb microalloying, and combines the control of rolling to control the performance index of the steel bar produced by cooling to meet the requirements that the lower yield strength is more than or equal to 425MPa, the tensile strength is more than or equal to 570MPa, the total maximum force elongation is more than or equal to 12 percent, the tensile strength/yield strength is more than or equal to 1.30, and the characteristic value of yield strength/yield strength is less than or equal to 1.12; all meet the performance requirements of HRB400E in GB/T1499.2, the structure is ferrite and pearlite, and the size covers the diameter of 6 mm-16 mm.
(2) In the embodiment of the invention, the alloy is economical only through microalloying of the silicon-manganese alloy and the Nb.
Although a few embodiments of the present general inventive concept have been shown and described, it would be appreciated by those skilled in the art that changes may be made in these embodiments without departing from the principles and spirit of the general inventive concept, the scope of which is defined in the claims and their equivalents.
Claims (4)
1. The niobium microalloyed hot rolled ribbed steel bar is characterized in that the chemical components in the niobium microalloyed hot rolled ribbed steel bar are ：C：0.20％~0.25％,Si：0.20％~0.30％,Mn：1.10％~1.30％,Nb: 0.005~0.010%,P：<0 .045％,S：<0 .045％,N<0 .008％; and the balance of Fe and impurity elements in percentage by weight, wherein the metallographic structure of the niobium microalloyed hot rolled ribbed steel bar only comprises ferrite and pearlite;
Under the condition that niobium is used as a trace additive element, the niobium microalloyed hot rolled ribbed steel bar is obtained by controlling parameters of rolling and cooling;
the method comprises the steps of discharging a billet for producing the niobium microalloyed hot rolled ribbed steel bar, and performing continuous rolling process treatment after water descaling, wherein the continuous rolling process comprises rough rolling mill group rolling, middle rolling mill group rolling, pre-finishing mill group rolling and finishing mill group rolling;
Obtaining the niobium microalloyed hot rolled ribbed steel bar by controlling the mill power of the pre-finish rolling stage and controlling the parameters of cooling conditions;
In the continuous rolling process, a billet passes through a water cooling device, the initial rolling temperature of the rough rolling of the billet is 960-980 ℃, the temperature of the billet entering a pre-finishing mill group is 850-880 ℃ after the billet is rolled by a middle rolling mill group, the billet after the pre-finishing mill is water-cooled to 750-800 ℃ and enters the finishing mill group for rolling, wherein the reduction rate of the total cross section area in the finishing mill stage is more than 70%;
After finish rolling, cooling the surface of the steel bar to 550-600 ℃ by graded cooling, wherein the cooling speed is more than 100 ℃/s; after the temperature is returned, the surface of the steel bar is cooled slowly by a cooling bed at 750-780 ℃;
before continuous rolling, the billet is further subjected to molten iron pretreatment, converter steelmaking, refining, continuous casting and continuous casting heating, wherein in the continuous casting heating, the continuous casting is heated in a walking beam heating furnace, the soaking temperature is controlled between 980 ℃ and 1000 ℃, and the heating time is 60min to 80min.
2. A method for producing a niobium microalloyed hot rolled ribbed steel bar, characterized in that the niobium microalloyed hot rolled ribbed steel bar is the niobium microalloyed hot rolled ribbed steel bar according to claim 1,
The production method comprises the following steps:
(1) Providing blast furnace molten iron;
(2) And (3) molten iron pretreatment: the weight percentage of S content of the blast furnace molten iron after the desulfurization process is controlled to be less than 0.015 percent;
(3) Converter steelmaking: adding desulphurized molten iron into a converter, controlling the loading amount of scrap steel to be not more than 15% of the total loading amount, and finishing converting after reaching the end point component and tapping temperature; adding a deoxidizer to deoxidize molten steel when the steel is tapped 1/3, adding a silicon-manganese alloy element and a carburant, adding the molten steel when the steel is tapped 2/3, and transferring to refining after the steel tapping is finished;
(4) Refining: blowing protective gas into the ladle to refine for at least 10min, adding ferrocolumbium after the blowing protective gas is refined and deoxidized well, stopping refining after the smelting components are qualified, and starting pouring;
(5) Continuous casting: the continuous casting tundish adopts alkaline casting powder, the continuous casting ladle and the tundish adopt long water gap protection casting, the superheat degree of the tundish is not more than 15 ℃, and finally a continuous casting blank is obtained;
(6) Heating a continuous casting blank: heating the continuous casting blank in a heating furnace, wherein the soaking temperature is controlled to be 980-1000 ℃ and the heating time is 60-80 min;
(7) Controlling rolling and cooling control: the continuous rolling comprises rough rolling unit rolling, intermediate rolling unit rolling, pre-finishing mill unit rolling and finishing mill unit rolling, wherein the initial rolling temperature of the rough rolling of the billet in the rough rolling unit is 960-980 ℃, the temperature of the billet in the intermediate rolling unit rolling is 850-880 ℃, the billet in the pre-finishing mill unit is cooled to 750-800 ℃ after the billet is discharged from the pre-finishing mill unit, and the billet is subjected to finish rolling in the finishing mill unit;
(8) Cooling after rolling: and after finish rolling, cooling the surface of the steel bar in a grading way, controlling the cooling speed to be 550-600 ℃, wherein the cooling speed is more than 100 ℃/s, the temperature of the surface of the steel bar after temperature return is 750-780 ℃, and slowly cooling the steel bar on a cooling bed to obtain the niobium microalloyed hot rolled ribbed steel bar.
3. The method of claim 2, wherein,
The shielding gas comprises argon, and the cross section size of the continuous casting blank is 150mm multiplied by 150mm to 170mm multiplied by 170mm;
the heating furnace in the step of heating the casting blank is a walking beam heating furnace.
4. The method according to claim 3, wherein,
The reduction rate of the total cross-sectional area of the finish rolling stage is more than 70 percent;
In the controlled cooling step after rolling, after the steel bar is slowly cooled by a cooling bed, the niobium microalloyed hot rolled ribbed steel bar is obtained after cutting to length, bundling and packaging.
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