CN110408845A - A kind of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar and preparation method thereof - Google Patents
A kind of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- 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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Abstract
The present invention relates to a kind of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bars and preparation method thereof, based on mass percentage, it is composed of the following components: C 0.26-0.30%, V 0.16-0.25%, Si 0.40-0.80%, Mn 1.20-1.60%, Nb 0-0.04%, Cr 0-0.40%, N 200-400ppm, surplus are Fe and inevitable impurity.The present invention makes full use of the synergistic effect of each element by compound addition V-N steel, in conjunction with the control of each process temperature in the operation of rolling, has obtained the reinforcing bar product that tissue is pearlite+ferrite and grain size >=10 grade.Gained reinforcing bar has a good application prospect with excellent mechanical property, yield strength >=700MPa, tensile strength >=850MPa, elongation after fracture A >=14.0%, maximum, force percentage of total elongation >=7.5%.
Description
Technical field
The invention belongs to Ferrous Metallurgy and technical field of steel rolling, it is related to a kind of reinforcing bar and preparation method thereof more particularly to one
Kind vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar and preparation method thereof.
Background technique
With the rapid development of building industry, the engineering structures such as Municipal engineering and skyscraper want reinforcement property
Ask higher and higher, the safety of building structure, shock resistance problem cause common concern, and improve building safety and shock resistance
Key be improve reinforcing bar intensity and comprehensive performance.In the case where country advocates energy-saving and emission-reduction, environmentally protective background energetically, as
The construction industry of resource consumption rich and influential family, regular tenacity reinforcing bar have been unable to satisfy the need of development as the situation of construction(al)steel main material
Want, thus development of high strength, high performance steel have become there is an urgent need to.
Reinforcing bar is currently the maximum rolling shapes of China's volume of production and marketing, and the quality level of reinforcing bar is first intake already close to international
It is flat, but there are also a certain distance for use intensity and developed country.China's hot rolled ribbed bars are divided into 400,500 and by strength grade
600 3 kinds of intensity ranks.It is commonly used in the major projects such as nuclear power, landmark by the popularization and application of many years
HRB500(E).With the implementation that issues of GB 1499.2-2018, national standard reinforcing bar interior tissue is proposed in new standard higher
It is required that and preventing to wear the techniques such as water production national standard reinforcing bar product.
Reinforcing bar grade used by external concrete structure is substantially with 400MPa grades, 500MPa grades, 600MPa grade three
400MPa grades and the above high tensile reinforcement are generallyd use based on grade, in engineering, some developed countries (such as Britain, Germany) have used
600MPa grades of reinforcing bars.Developed countries obviously surmount China in high tensile reinforcement research and development and application aspect, and reinforcing bar application is universal
1-2 grade higher than China, and corresponding rebar standards are also being constantly updated, reinforcing bar rank highest have reached 700Mpa grades with
On.As Korea Spro marks the GR100 of SD700 and SD600S in (KS D3504:2016), American Standard (ASTM A615-A615M-2015ae1)
Deng so high tensile reinforcement will will gradually become the development trend of building bar.
Therefore, in order to which the market demand and higher and higher industry requirement, urgent need that meet sharp increase are studied and produced more
High-strength building reinforcing bar.
Summary of the invention
In view of problems of the prior art, the purpose of the present invention is to provide a kind of vanadium micro-alloying hot rolling 700MPa
Grade high-strength reinforcing bar and preparation method thereof, gained reinforcing bar interior tissue are ferrite and pearlite, and stable mechanical property meets work
Industry batch steady production demand.
To achieve this purpose, the present invention adopts the following technical scheme:
In a first aspect, the present invention provides a kind of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bars, by quality percentage
Content meter, the reinforcing bar are composed of the following components: C 0.26-0.30%, V 0.16-0.25%, Si 0.40-0.80%, Mn
1.20-1.60%, Nb 0-0.04%, Cr 0-0.40%, N 200-400ppm, surplus are Fe and inevitable impurity.
Hot-rolled reinforced bar production technology is different from producing process of sheet and strip, and almost ausrolling, especially small dimension fine grain is strong
Change effect is unobvious, therefore is difficult to for reinforced steel bar strength to be increased to 700MPa or more rank using the V-N steel of single-element.
The present invention selects the mode of compound addition V-N steel to improve, and obtains a large amount of deformation bands and position in roughing and finish rolling stage
Wrong band, and there is part precipitate (VC, VN, Nb (V, N) etc.) to be precipitated along crystal boundary, Zona transformans and dislocation, these precipitates nail
Crystal boundary is pricked, the roughening of austenite grain is prevented, so that phase transformation generates fine and closely woven ferrite in cooling procedure, ultimately forms pearl
Body of light+ferritic reinforcing bar tissue, grain size >=10 grade, gained vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcement yielding are strong
Degree >=700MPa, tensile strength >=850MPa, elongation after fracture A >=14.0%, maximum, force percentage of total elongation Agt >=7.5%.
V is a kind of important V-N steel element, and Austenite Grain Refinement effect is weaker.V element energy in the present invention
It is enough that nanoscale V (C, N) compound is precipitated during the rolling process, increase ferrite nucleation point, prevents ferrite crystal grain from growing up, have
Extremely strong precipitation precipitation enhancement, can significantly improve the yield strength of reinforcing bar.
The content of V is 0.16-0.25% in reinforcing bar of the present invention, for example, can be 0.16%, 0.17%, 0.18%,
0.19%, 0.20%, 0.21%, 0.22%, 0.23%, 0.24% or 0.25% etc..It is determined according to rolling specs difference different
Content of vanadium, improve that reinforced steel bar strength is superfluous, and the too low reinforced steel bar strength of V content is not achieved as will lead to smelting cost when V content is excessively high
Intensity requirement.
Nb element can migrate ferrite/Austenite Interfacial and generate strong drag interaction, improve austenite recrystallization
Temperature, refine crystal grain, improve steel strength, have stronger refined crystalline strengthening effect, and in the operation of rolling precipitation nanoscale Nb (C,
N) compound forms precipitation strength.Simultaneously under the condition of high temperature, niobium, which is in solid solution condition, significantly reduces ferrite transformation temperature, high
It is dissolved niobium under warm natural cooling state to be precipitated, promotes the raising of low temperature phase change product-pearlite percentage, makes Steel Bar Tensile Strength
It is improved.
The content of Nb is 0-0.04% in reinforcing bar of the present invention, for example, can be 0%, 0.001%, 0.005%,
0.01%, 0.015%, 0.02%, 0.025%, 0.03%, 0.035% or 0.04% etc..When the content of Nb in reinforcing bar is 0%
When, Nb is not contained in the reinforcing bar.The content of Nb is preferably 0.001-0.04% in the reinforcing bar.Not only make when Nb too high levels
Cost of alloy increases, at the same because the raising of niobium will caused by slab quality decline, such as chink, transverse fissure cause rebar surface to occur
Crack defect.
The compound addition vanadium of the present invention and niobium can increase the solid solubility of reinforcing bar, reduce solution modeling temperature, pass through refined crystalline strengthening
So that reinforcing bar is reached higher yield strength with precipitation precipitation enhancement while keeping good plasticity.
Carbon is a kind of effective intensified element, and carbon can be dissolved improves its yield strength and tensile strength, price in the base
It is cheap, while carbon can form carboritride with elements such as vanadium, niobiums in steel, improve the intensity of steel matrix, but carbon contains
The excessively high plasticity and toughness that can reduce reinforcing bar is measured, the welding performance of reinforcing bar is reduced；When carbon content is too low, it can not be formed enough
Nb (C, N) compound and V (C, N) compound, reinforced steel bar strength are insufficient, it is difficult to reach 700MPa grades of requirement；Therefore, of the invention
Carbon content in the reinforcing bar is 0.26-0.30%, for example, can be 0.26%, 0.27%, 0.28%, 0.29% or
0.30%.
Nitrogen can generate mating reaction with V and Nb in the present invention, promote the precipitation of V and Nb compound, refine precipitated phase
Size can give full play to the potentiality of compound precipitation strength, be produced into raising screw thread hardness of steel, and the usage amount of reduction V, reduction
This has obvious effect.
In conjunction with best vanadium nitrogen ratio, the present invention controls nitrogen content in 200-400ppm, for example, can be 200ppm, 210ppm,
220ppm、230ppm、240ppm、250ppm、260ppm、270ppm、280ppm、290ppm、300ppm、310ppm、320ppm、
330ppm, 340ppm, 350ppm, 360ppm, 370ppm, 380ppm, 390ppm or 400ppm etc..When the content of N element is too low
When, Nb (C, the N) compound and V (C, N) compound met the requirements can not be formed in the reinforcing bar, the intensity of steel matrix can not
Meet 700MPa grades of reinforcing bar requirements；When the too high levels of N element, N element can make the timeliness of reinforcing bar be deteriorated；Therefore, this hair
The bright content for needing to control N element in reinforcing bar is 200-400%.
Chromium is a kind of common intensified element, and the present invention can significantly improve the intensity, hard of reinforcing bar by addition Cr element
Degree and wearability, while the formation of carbide in steel can be promoted, tensile strength is effectively contributed, product strong flexor ratio index is improved.
The content of Cr is 0-0.40% in reinforcing bar of the present invention, for example, can be 0%, 0.01%, 0.03%,
0.05%, 0.07%, 0.10%, 0.12%, 0.15%, 0.18%, 0.20%, 0.22%, 0.25%, 0.27%, 0.30%,
0.32%, 0.35%, 0.38% or 0.40% etc., preferably 0.01-0.40%.The through hardening of reinforcing bar can be improved when Cr too high levels
Property, the tissue such as bainite is generated in cooling procedure, to reduce reinforcing bar comprehensive performance.
Silicon is reducing agent and deoxidier common in steel, can significantly improve the elastic limit, yield point and tensile strength of steel,
Mainly play solution strengthening by being solid-solubilized in ferrite, and can reduce the diffusion speed of carbon in austenite
Degree postpones ferrite and pearlite phase transformation, yield strength and tensile strength can be improved, but element silicon can improve ductile-brittle transiton temperature
Degree, therefore its content is unsuitable excessively high.
The zone of reasonableness of silicone content is 0.40-0.80% in the present invention, for example, can be 0.40%, 0.45%, 0.50%,
0.55%, 0.60%, 0.65%, 0.70%, 0.75% or 0.80% etc..
Manganese is main solution strengthening element, and improves the effective element of the harden ability of steel.Manganese is as one in the present invention
The main solution strengthening element of kind improves the intensity of matrix, and excessively high manganese content can reduce ferrite and generate temperature, makes precipitated phase too
It crosses tiny and influences strengthening effect, meanwhile, manganese content is higher equally to improve carbon equivalent, influence welding performance.
Manganese content zone of reasonableness is 1.20-1.60% in the present invention, for example, can be 1.20%, 1.25%, 1.30%,
1.35%, 1.40%, 1.45%, 1.50%, 1.55% or 1.60% etc..
For the present invention, the content of impurity element is no more than 350ppm, otherwise can seriously to the intensity of reinforcing bar and
Toughness, it is difficult to reach requirement.
P and s, which are two kinds, common are harmful element, and phosphorus can increase the cold brittleness of steel, welding performance is made to degenerate, and reduce modeling
Property, so that cold-bending property is degenerated.Sulphur can make steel generate red brittleness, reduce the ductility and toughness of steel, cause in forging and rolling
Crackle, it is also unfavorable to welding performance, reduce corrosion resistance.Therefore the present invention in p and s zone of reasonableness≤0.035%.
Second aspect, the present invention provides a kind of preparation method of reinforcing bar as described in relation to the first aspect, the method includes
The process that next coming in order carry out: converter smelting, LF refining, continuous casting, slab cooling, slab heating, rolling and cold bed are cooling.
For the present invention, based on components described above scheme, slab is obtained by converter smelting, LF refining, continuous casting
Process use this field conventional technology, the present invention do not do particular determination to it.Illustratively, above-mentioned to smelt
Process to slab can use following scheme, but non-be only limitted to this:
After oxygen coverter is added in molten iron or half steel, steel scrap, top bottom blowing is carried out, lime, dolomite, slugging is added
Ball carries out slag making；Control aim carbon >=0.06wt%, 1650~1680 DEG C of tapping temperature；Using wash heat and whole bottom blowing when tapping
Deoxidier is added into ladle when molten steel goes out to more than when 1/4 in argon, silicomangan, ferrosilicon, and ferrovanadium nitride optionally adds niobium
Iron, ferrochrome etc. are added when ladle molten steel goes out to 3/4, to carry out deoxidation alloying.Molten steel send LF furnace to carry out essence after tapping
Then refining, pre- Argon 3 minutes carry out electrode slugging, lime is added, and control basicity of slag is 5.0-8.0, are added and close after slag making
Gold fine tuning ingredient reaches target control ingredient；To molten steel Argon 8 minutes；After heating molten steel to temperature is 1570-1590 DEG C, it is added
Conventional coverture send continuous casting working procedure, and tundish temperature is 1520-1540 DEG C, is casting continuously to form small billet.
After obtaining the slab that ingredient determines, the cooling process conditions pair of subsequent slab cooling, slab heating, rolling, cold bed
The performance of gained reinforcing bar of the invention has large effect.
Wherein, in slab cooling process, the present invention selects to carry out slab into slow cooling processing, and the time of slow cooling >=for 24 hours.Steel
Middle nitride VN, NbN etc. can be precipitated in phase transition process along austenite grain boundary due to the different solubility in its γ phase and α phase,
To destroy the ductility of steel, make steel that there is crack sensitivity, crack during the rolling process, as the promotion of reinforced steel bar strength is closed
Gold addition is more, and this phenomenon is caused to be more obvious.Therefore, 1) being fully cooled reduces it during heating in crack-sensitivity area
Domain long-time heating expands cracking trend, if cooling time, the short slab high-temperature that will lead to entered stove heating, in crack-sensitivity area
Domain heating time is too long；2) slab extremely cold such as wind or water spray, will lead to that generate internal stress inside the too fast slab of cooling rate excessive,
Occur the problems such as cracking and irregular deformation in the operation of rolling, while leading to the compound analysis such as V, Nb, N inside slab because cooling rate is too fast
It is abnormal out, influence final finished performance.
In slab heating process, the slab after cooling treatment is sent into heating furnace, preheating section, bringing-up section and soaking zone are divided
It is heated.Wherein preheating section furnace gas temperature be≤900 DEG C, such as can be 700 DEG C, 710 DEG C, 720 DEG C, 730 DEG C, 740 DEG C,
750℃、760℃、770℃、780℃、790℃、800℃、810℃、820℃、830℃、840℃、850℃、860℃、870
DEG C, 880 DEG C, 890 DEG C or 900 DEG C etc.；Bringing-up section furnace gas temperature be 1100-1250 DEG C, such as can be 1110 DEG C, 1120 DEG C,
1130℃、1140℃、1150℃、1160℃、1170℃、1180℃、1190℃、1200℃、1210℃、1220℃、1230℃、
1240 DEG C or 1250 DEG C etc.；Soaking zone furnace gas temperature be 1150-1250 DEG C, such as can be 1150 DEG C, 1160 DEG C, 1170 DEG C,
1180 DEG C, 1190 DEG C, 1200 DEG C, 1210 DEG C, 1220 DEG C, 1230 DEG C, 1240 DEG C or 1250 DEG C etc.；Slab tapping temperature is
1100-1200 DEG C, such as can be 1100 DEG C, 1130 DEG C, 1150 DEG C, 1180 DEG C or 1200 DEG C etc..
Above-mentioned heating process temperature control be the key that it is of the invention,
In rolling process, successively carry out roughing, in roll and finish rolling, water is not worn after rolling.Wherein, start rolling temperature 1100-
1180 DEG C, for example, can be 1100 DEG C, 1110 DEG C, 1120 DEG C, 1130 DEG C, 1140 DEG C, 1150 DEG C, 1160 DEG C, 1170 DEG C or
1180 DEG C etc..
The influence of start rolling temperature: start rolling temperature and heating tapping temperature are close in detail, in order to occur playing addition alloy
Complex intensifying effect need to be strict with hot-rolled process, and the low then tapping temperature of start rolling temperature is low, causes during heating
The intensified elements back dissolving such as vanadium niobium is not thorough, and secondary precipitation, which is strengthened, contributes small reinforced steel bar strength low；The high initial austenite of start rolling temperature is brilliant
Granularity is small, and Grain refinement is unobvious, and reinforced steel bar strength is low.
In cold bed cooling process, temperature on cooling table is 1100-1180 DEG C, such as can be 1100 DEG C, 1110 DEG C, 1120
DEG C, 1130 DEG C, 1140 DEG C, 1150 DEG C, 1160 DEG C, 1170 DEG C or 1180 DEG C etc.；Lower cold bed temperature is 350-460 DEG C, such as can
To be 350 DEG C, 380 DEG C, 400 DEG C, 430 DEG C, 450 DEG C or 460 DEG C etc..
The influence of cooling bed tempertaure: because rod hot rolling process system is essentially ausrolling, the temperature of upper cold bed is substantially etc.
In start rolling temperature；Consider after cold bed speed of service influence of rolled rhythm and lower high bed temperature cause reinforcing bar to be packaged in steel bundle from
Lower cold bed temperature is defined by the problems such as tempering.
Compared with prior art, the present invention is at least had the advantages that
(1) synergistic effect of the elements such as V, Nb, C, N is utilized by compound addition V-N steel in the present invention, and
The cooperation of the elements such as Cr, Mn, Si adequately achieves refined crystalline strengthening and precipitating in conjunction with the control of each process temperature in the operation of rolling
Strengthen, has obtained tissue as pearlite+ferrite, and the reinforcing bar product of grain size >=10 grade, be finally reached 700MPa grades of indexs.
(2) present invention gained reinforcing bar has excellent mechanical property, yield strength (Rel) >=700MPa, tensile strength
(Rm) >=850MPa, elongation after fracture (A) >=14.0%, maximum, force percentage of total elongation (Agt) >=7.5% have good application
Prospect.
(3) smelting procedure of the present invention does not need special process, easy to operate, rolling mill practice and low-intensity rank screw-thread steel phase
Than the requirement of no complexity can carry out large-scale promotion and use.
Detailed description of the invention
Fig. 1 is the metallographic structure figure of 1 gained reinforcing bar of the embodiment of the present invention, and scale is 100 μm；
Fig. 2 is the metallographic structure figure of 1 gained reinforcing bar of the embodiment of the present invention, and scale is 20 μm, in figure: dark-coloured tissue is pearl
Body of light, the tissue of light tone are ferrite.
The present invention is described in more detail below.But following examples is only simple example of the invention, not generation
Table or limitation the scope of the present invention, protection scope of the present invention are subject to claims.
Specific embodiment
To further illustrate the technical scheme of the present invention below with reference to the accompanying drawings and specific embodiments.
In order to better illustrate the present invention, it is easy to understand technical solution of the present invention, of the invention is typical but non-limiting
Embodiment is as follows:
Embodiment 1
Present embodiments provide a kind of preparation method of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, the preparation
Method comprises the following steps:
(1) smelting procedure: by the process of ingredient, converter smelting, LF refining and continuous casting, obtain 165mm × 165mm's
Rectangular slab, based on mass percentage, the chemical component of slab are as follows: C 0.26%, Si 0.65%, Mn 1.40%, V
0.163%, Nb 0.005%, Cr 0.006%, N 0.0210%, surplus are iron and inevitable impurity, wherein S
0.025%, P 0.025%；
(2) slab cooling process: the qualified slab slow cooling that step (1) is obtained through continuous casting is for 24 hours；
(3) slab heating process: step (2) slab after cooling is sent into heating furnace and is heated, wherein preheating section
Furnace gas temperature is 900 DEG C, and bringing-up section furnace gas temperature is 1180 DEG C, and soaking zone furnace gas temperature is 1220 DEG C, slab tapping temperature
1175℃；
(4) rolling process: the slab after step (3) heating is rolled using continous way bar wire rod rolling mill, rolling rule
Lattice areBlank start rolling temperature be 1151 DEG C, successively carry out roughing, in roll, finish rolling, water is not worn after rolling；
(5) cold bed cooling process: 1150 DEG C of temperature on cooling table of control, 400 DEG C of lower cold bed temperature is cooled down.
Fig. 1 and Fig. 2 is the metallographic structure of gained reinforcing bar.As shown in Figure 1, the crystallite dimension of reinforcing bar is small, 10 grades of grain size >；
As shown in Fig. 2, the tissue of reinforcing bar is ferrite and pearlite.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by the present embodiment, is taken
Four groups are tested,700MPa grades of steel bar mechanics performances are as shown in table 1.
Table 1
Embodiment 2
Present embodiments provide a kind of preparation method of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, the preparation
Method comprises the following steps:
(1) smelting procedure: by the process of ingredient, converter smelting, LF refining and continuous casting, obtain 165mm × 165mm's
Rectangular slab, based on mass percentage, the chemical component of slab are as follows: C 0.27%, Si 0.71%, Mn 1.53%, V
0.19%, Nb 0.001%, Cr 0.08%, N 0.031%, surplus are iron and inevitable impurity, wherein S:
0.015%, P:0.028%；
(2) slab cooling process: the qualified slab slow cooling that step (1) is obtained through continuous casting is for 24 hours；
(3) heating process: step (2) slab after cooling is sent into heating furnace and is heated, wherein preheating section furnace gas
Temperature is 870 DEG C, and bringing-up section furnace gas temperature is 1230 DEG C, and soaking zone furnace gas temperature is 1235 DEG C, 1185 DEG C of slab tapping temperature；
(4) rolling process: the slab after step (3) heating is rolled using continous way bar wire rod rolling mill, rolling rule
Lattice areBlank start rolling temperature be 1135 DEG C, successively carry out roughing, in roll, finish rolling, water is not worn after rolling；
(5) cold bed cooling process: 1123 DEG C of temperature on cooling table of control, 425 DEG C of lower cold bed temperature is cooled down.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by the present embodiment, is taken
Four groups are tested,700MPa grades of steel bar mechanics performances are as shown in table 2.
Table 2
Embodiment 3
Present embodiments provide a kind of preparation method of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, the preparation
Method comprises the following steps:
(1) smelting procedure: by the process of ingredient, converter smelting, LF refining and continuous casting, obtain 165mm × 165mm's
Rectangular slab, based on mass percentage, the chemical component of slab are as follows: C 0.28%, Si 0.71%, Mn 1.49%, V
0.19%, Nb 0.005%, Cr 0.30%, N 0.03%, surplus are iron and inevitable impurity, wherein S 0.023%,
P 0.022%；
(2) slab cooling process: the qualified slab slow cooling that step (1) is obtained through continuous casting is for 24 hours；
(3) slab heating process: step (2) slab after cooling is sent into heating furnace and is heated, wherein preheating section
Furnace gas temperature is 870 DEG C, and bringing-up section furnace gas temperature is 1210 DEG C, and soaking zone furnace gas temperature is 1210 DEG C, slab tapping temperature
1180℃；
(4) rolling process: the slab after step (3) heating is rolled using continous way bar wire rod rolling mill, rolling rule
Lattice areBlank start rolling temperature be 1155 DEG C, successively carry out roughing, in roll, finish rolling, water is not worn after rolling；
(5) cold bed cooling process: 1140 DEG C of temperature on cooling table of control, 360 DEG C of lower cold bed temperature is cooled down.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by the present embodiment, is taken
Four groups are tested,700MPa grades of steel bar mechanics performances are as shown in table 3.
Table 3
Embodiment 4
Present embodiments provide a kind of preparation method of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, the preparation
Method comprises the following steps:
(1) smelting procedure: by the process of ingredient, converter smelting, LF refining and continuous casting, obtain 165mm × 165mm's
Rectangular slab, based on mass percentage, the chemical component of slab are as follows: C 0.28%, Si 0.65%, Mn 1.52%, V
0.22%, Nb 0.017%, Cr 0.16%, N 0.036%, surplus are iron and inevitable impurity, wherein S
0.018%, P 0.03%；
(2) slab cooling process: the qualified slab slow cooling that step (1) is obtained through continuous casting is for 24 hours；
(3) slab heating process: step (2) slab after cooling is sent into heating furnace and is heated, wherein preheating section
Furnace gas temperature is 890 DEG C, and bringing-up section furnace gas temperature is 1200 DEG C, and soaking zone furnace gas temperature is 1220 DEG C, slab tapping temperature
1165℃；
(4) rolling process: the slab after step (3) heating is rolled using continous way bar wire rod rolling mill, rolling rule
Lattice areBlank start rolling temperature be 1145 DEG C, successively carry out roughing, in roll, finish rolling, water is not worn after rolling；
(5) cold bed cooling process: 1150 DEG C of temperature on cooling table of control, 380 DEG C of lower cold bed temperature is cooled down.
Comprehensive performance inspection is carried out to reinforcing bar product obtained by the present embodiment, takes four groups to test,700MPa
Grade steel bar mechanics performance is as shown in table 4.
Table 4
Embodiment 5
Present embodiments provide a kind of preparation method of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, the preparation
Method comprises the following steps:
(1) smelting procedure: by the process of ingredient, converter smelting, LF refining and continuous casting, obtain 165mm × 165mm's
Rectangular slab, based on mass percentage, the chemical component of slab are as follows: C 0.30%, Si 0.70%, Mn 1.55%, V
0.25%, Nb 0.039%, Cr 0.40%, N 0.0400%, surplus are iron and inevitable impurity, wherein S
0.018%, P 0.030%；
(2) slab cooling process: the qualified slab slow cooling that step (1) is obtained through continuous casting is for 24 hours；
(3) slab heating process: step (2) slab after cooling is sent into heating furnace and is heated, wherein preheating section
Furnace gas temperature is 900 DEG C, and bringing-up section furnace gas temperature is 1230 DEG C, and soaking zone furnace gas temperature is 1240 DEG C, slab tapping temperature
1195℃；
(4) rolling process: the slab after step (3) heating is rolled using continous way bar wire rod rolling mill, rolling rule
Lattice areBlank start rolling temperature be 1190 DEG C, successively carry out roughing, in roll, finish rolling, water is not worn after rolling；
(5) cold bed cooling process: 1185 DEG C of temperature on cooling table of control, 460 DEG C of lower cold bed temperature is cooled down.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by the present embodiment, is taken
Four groups are tested,700MPa grades of steel bar mechanics performances are as shown in table 5.
Table 5
Comparative example 1
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method comprises the following steps:
(1) smelting procedure: by the process of ingredient, converter smelting, LF refining and continuous casting, obtain 165mm × 165mm's
Rectangular slab, based on mass percentage, the chemical component of slab are as follows: C 0.26%, Si 0.65%, Mn 1.40%, V
0.155%, Nb 0.005%, Cr 0.006%, N 0.0210%, surplus are iron and inevitable impurity, wherein S
0.025%, P 0.025%；
(2) slab cooling process: the qualified slab slow cooling that step (1) is obtained through continuous casting is for 24 hours；
(3) slab heating process: step (2) slab after cooling is sent into heating furnace and is heated, wherein preheating section
Furnace gas temperature is 900 DEG C, and bringing-up section furnace gas temperature is 1180 DEG C, and soaking zone furnace gas temperature is 1220 DEG C, slab tapping temperature
1175℃；
(4) rolling process: the slab after step (3) heating is rolled using continous way bar wire rod rolling mill, rolling rule
Lattice areBlank start rolling temperature be 1151 DEG C, successively carry out roughing, in roll, finish rolling, water is not worn after rolling；
(5) cold bed cooling process: 1150 DEG C of temperature on cooling table of control, 400 DEG C of lower cold bed temperature is cooled down.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 6.
Table 6
By the data of table 6 it is found that when the V content in reinforcing bar is too low, the yield strength < of gained hot-rolled high-strength reinforcing bar
700MPa is unable to satisfy the >=requirement of 700MPa.
Comparative example 2
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (1) described slab
Chemical component be C 0.26%, Si 0.65%, Mn 1.40%, V 0.163%, Nb 0.055%, Cr 0.006%, N
0.0210%, surplus is iron and inevitable impurity, wherein S 0.025%, P 0.025%；Remaining with 1 phase of embodiment
Together.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 7.
Table 7
By the data in table 7 it is found that when the Nb too high levels in reinforcing bar, the surface of gained hot-rolled high-strength reinforcing bar easily goes out
Existing crack defect is easy to appear stress in cracks and concentrates, and leads to the intensity and plasticity drop of gained hot-rolled high-strength reinforcing bar
It is low, tensile strength the < 850MPa, elongation after fracture < 14.0% of gained hot-rolled high-strength reinforcing bar.
Comparative example 3
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (1) described slab
Chemical component be C 0.26%, Si 0.65%, Mn 1.40%, V 0.163%, Nb 0.005%, Cr 0.50%, N
0.0210%, surplus is iron and inevitable impurity, wherein S 0.025%, P 0.025%；Remaining with 1 phase of embodiment
Together.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 8.
Table 8
By the data of table 8 it is found that bainite group when the Cr content in reinforcing bar is excessive, in gained hot-rolled high-strength reinforcing bar
Knit it is more, cause gained reinforcing bar maximum, force percentage of total elongation < 7.5, be unable to satisfy >=7.5 requirement.
Comparative example 4
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (1) described slab
Chemical component be C 0.26%, Si 0.65%, Mn 1.40%, V 0.163%, Nb 0.005%, Cr 0.006%, N
0.0180%, surplus is iron and inevitable impurity, wherein S 0.025%, P 0.025%；Remaining with 1 phase of embodiment
Together.
Comprehensive performance inspection is carried out to reinforcing bar product obtained by this comparative example, takes four groups to test,Reinforcing bar power
It is as shown in table 9 to learn performance.
Table 9
By the data in table 9 it is found that when the N content in reinforcing bar is lower, it can not be formed in gained hot-rolled high-strength reinforcing bar
Enough VN compounds, the yield strength < 700MPa of gained hot-rolled high-strength reinforcing bar are unable to satisfy the >=requirement of 700MPa.
Comparative example 5
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (1) described slab
Chemical component be C 0.26%, Si 0.65%, Mn 1.40%, V 0.163%, Nb 0.005%, Cr 0.006%, N
0.0420%, surplus is iron and inevitable impurity, wherein S 0.025%, P 0.025%；Remaining with 1 phase of embodiment
Together.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 10.
Table 10
By the data in table 10 it is found that when the too high levels of N in reinforcing bar, the free N in reinforcing bar increases, and gained hot rolling is high
The tough brittle transition temperature of intensity steel improves, and so that the plasticity index of hot-rolled high-strength reinforcing bar is deteriorated, gained hot-rolled high-strength steel
The elongation after fracture A < 14 of muscle, maximum, force percentage of total elongation Agt < 7.5%.
Comparative example 6
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (1) described slab
Chemical component be C 0.24%, Si 0.65%, Mn 1.40%, V 0.163%, Nb 0.005%, Cr 0.006%, N
0.0210%, surplus is iron and inevitable impurity, wherein S 0.025%, P 0.025%；Remaining with 1 phase of embodiment
Together.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 11.
Table 11
By the data in table 11 it is found that when the C content in reinforcing bar is lower, the yield strength of gained hot-rolled high-strength reinforcing bar
< 700MPa, tensile strength < 850MPa.
Comparative example 7
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (1) described slab
Chemical component be C 0.33%, Si 0.65%, Mn 1.40%, V 0.163%, Nb 0.005%, Cr 0.006%, N
0.0210%, surplus is iron and inevitable impurity, wherein S 0.025%, P 0.025%；Remaining with 1 phase of embodiment
Together.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 12.
Table 12
By the data in table 12 it is found that when the C content in reinforcing bar is higher, the yield strength of gained hot-rolled high-strength reinforcing bar
It improves a lot with tensile strength, but plasticity index declines, elongation after fracture < 14.0%.
Comparative example 8
This comparative example provides a kind of preparation method of high strength cast iron, and the preparation method removes step (2) described slow cooling
Time be 18h, remaining is same as Example 1.
Comprehensive performance inspection is carried out using the method for inspection corresponding in GB/T 28900 to reinforcing bar product obtained by this comparative example, is taken
Four groups are tested,Steel bar mechanics performance is as shown in table 13.
Table 13
By the data in table 13 it is found that when slow cooling fast speed, abnormal structure is generated in gained hot-rolled high-strength reinforcing bar,
Lead to the maximum, force percentage of total elongation < 7.5% of gained hot-rolled high-strength reinforcing bar.
In conclusion the synergistic effect of the elements such as V, Nb, C, N is utilized by compound addition V-N steel in the present invention,
And the cooperation of the elements such as Cr, Mn, Si, in conjunction with the control of each process temperature in the operation of rolling, adequately achieve refined crystalline strengthening and
Precipitation strength has obtained tissue as pearlite+ferrite, and the reinforcing bar product of grain size >=10 grade, is finally reached 700MPa grades
Index；Gained reinforcing bar has excellent mechanical property, yield strength >=700MPa, tensile strength >=850MPa, elongation of having no progeny
Rate >=14.0%, maximum, force percentage of total elongation >=7.5%, has a good application prospect；And smelting procedure of the present invention does not need
Special process, easy to operate, compared with low-intensity rank screw-thread steel, the requirement of no complexity can be pushed away rolling mill practice on a large scale
Wide and use.
The preferred embodiment of the present invention has been described above in detail, still, during present invention is not limited to the embodiments described above
Detail within the scope of the technical concept of the present invention can be with various simple variants of the technical solution of the present invention are made, this
A little simple variants all belong to the scope of protection of the present invention.
It is further to note that specific technical features described in the above specific embodiments, in not lance
In the case where shield, can be combined in any appropriate way, in order to avoid unnecessary repetition, the present invention to it is various can
No further explanation will be given for the combination of energy.
In addition, various embodiments of the present invention can be combined randomly, as long as it is without prejudice to originally
The thought of invention, it should also be regarded as the disclosure of the present invention.
Claims (10)
1. a kind of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, which is characterized in that based on mass percentage, the vanadium
Micro-alloyed hot-rolled 700MPa grade high-strength reinforcing bar is composed of the following components: C0.26-0.30%, V 0.16-0.25%, Si
0.40-0.80%, Mn 1.20-1.60%, Nb 0-0.04%, Cr0-0.40%, N 200-400ppm, surplus are Fe and can not
The impurity avoided.
2. vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar as described in claim 1, which is characterized in that the micro- conjunction of vanadium
Inevitable impurity content≤350ppm in aurification hot rolling 700MPa grade high-strength reinforcing bar.
3. vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar as claimed in claim 2, which is characterized in that press quality percentage
Content meter, S≤0.035% in the vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar, P≤0.035%.
4. vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar as described in any one of claims 1-3, which is characterized in that institute
State vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcement yielding intensity >=700MPa, tensile strength >=850MPa, elongation of having no progeny
Rate A >=14.0%, maximum, force percentage of total elongation Agt >=7.5% are organized as pearlite+ferrite, grain size >=10 grade.
5. the preparation method of vanadium micro-alloying hot rolling 700MPa grade high-strength reinforcing bar according to any one of claims 1-4,
It is characterized in that, the preparation method includes the process that next coming in order carry out: converter smelting, LF refining, continuous casting, slab cooling, casting
Base heating, rolling and cold bed are cooling.
6. preparation method as claimed in claim 5, which is characterized in that the slab cooling is slow cooling, time >=for 24 hours.
7. such as method described in claim 5 or 6, which is characterized in that the slab heating process include preheating section, bringing-up section and
Soaking zone, wherein preheating section furnace gas temperature≤900 DEG C, the bringing-up section furnace gas temperature are 1100-1250 DEG C, described equal
Hot arc furnace gas temperature is 1150-1250 DEG C, and slab tapping temperature is 1100-1200 DEG C.
8. such as the described in any item methods of claim 5-7, which is characterized in that the rolling process include successively carry out it is thick
Roll, in roll and finish rolling.
9. method according to claim 8, which is characterized in that start rolling temperature is 1100-1180 DEG C in the rolling process.
10. such as the described in any item methods of claim 5-9, which is characterized in that in the cold bed cooling process, temperature on cooling table
It is 1100-1180 DEG C, lower cold bed temperature is 350-460 DEG C.
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| CN110885952A (en) * | 2019-12-16 | 2020-03-17 | 本钢板材股份有限公司 | 400 MPa-grade hot-rolled ribbed steel bar and preparation method thereof |
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| CN111304541A (en) * | 2020-04-20 | 2020-06-19 | 安徽马钢和菱实业有限公司 | Niobium-vanadium composite microalloyed seamless steel tube for semitrailer axle and production method thereof |
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| CN112267071A (en) * | 2020-09-30 | 2021-01-26 | 江苏永钢集团有限公司 | High-strength deformed steel bar for building and production method thereof |
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| CN113462966A (en) * | 2021-06-18 | 2021-10-01 | 马鞍山钢铁股份有限公司 | Economical 630MPa high-strength anti-seismic steel bar steel and production method thereof |
| CN113957324A (en) * | 2021-09-02 | 2022-01-21 | 包头钢铁（集团）有限责任公司 | Smelting and rolling production method of 700 MPa-level pearlite ferrite ultrahigh-strength construction steel bar |
| CN114411061A (en) * | 2022-01-14 | 2022-04-29 | 宝武集团鄂城钢铁有限公司 | High-strength anti-seismic steel bar and preparation method thereof |
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| CN116288060B (en) * | 2023-03-14 | 2024-07-02 | 钢研晟华科技股份有限公司 | 800 MPa-grade high-strength corrosion-resistant steel bar and preparation method thereof |
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