CN104630625B - Low-temperature-resistant hot-rolled H-shaped steel and preparation method thereof - Google Patents
Low-temperature-resistant hot-rolled H-shaped steel and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The invention discloses a low-temperature-resistant hot-rolled H-shaped steel and a preparation method thereof. The hot-rolled H-shaped steel comprises the following chemical components in percentage by weight: 0.07-0.10% of C, 0.2-0.4% of Si, 1.30-1.60% of Mn, at most 0.020% of P, at most 0.015% of S, 0.015-0.070% of V, 0.010-0.030% of Ti, and the balance of Fe and inevitable impurities. The production method comprises the following steps: converter smelting, LF (ladle furnace) refining, continuous casting, rolling and the like. The structure of the H-shaped steel is a polygonal ferrite and pearlite structure, the yield strength is 350-450 MPa, the tensile strength is 480-600 MPa, the percentage elongation after fracture is greater than or equal to 22%, and the -40-DEG C V-notch Charpy impact energy is greater than or equal to 200J.
Description
Technical field
The invention belongs to the technical field of smelting of low temperature resistant H profile steel, in particular it relates to a kind of low temperature resistant hot rolling H
Shaped steel and preparation method thereof.
Background technology
China starts to build the offshore platform of oneself from the eighties in 20th century, in offshore oil, gas extraction
Aspect quickly grows, this also strong demand for having promoted offshore oil drilling platform steel.High intensity, low temperature resistant ocean platform
Demand with steel is increasing, and China's technical capability in this respect is also relatively backward, possesses certainly in the urgent need to researching and developing series
The high intensity of main intellectual property, high tenacity offshore platform steel, this realizes the energy of country for China's sea area resources are made full use of
Source strategy has far-reaching significance.Ocean with it is hot rolled H-shaped will consider wind load, seaway load, river load, ice load,
Seismic (seismal etc. affects, and this just determines the particularity of offshore platform steel, special requirement high intensity, high tenacity.
Because offshore platform is built among sea, its working environment is very severe.Therefore, offshore platform pair
The prescription of steel is very high, in addition to intensity requirement, resistance to low temperature is required also very high.To ensure that offshore platform is used
Steel has good combination property, the external main technology path using Nb or Nb-V microalloyings, the such as A572/ in the U.S.
The Steels For Offshore Oil Platforms such as A572M and EH36, the BS4360-50D of Britain, the StE355 of Germany are Nb-V microalloyings
Steel.China's H profile steel production kind is relatively simple compared with foreign countries, and in 235-345MPa, wherein 235MPa accounts for big absolutely intensity rank
Part yield.The hot rolled H-shaped development of microalloying currently produces high-strength low temperature resistant hot rolled H-shaped except adding in the starting stage
Beyond strong controlled rolling, the suitable micro-alloying technology of introducing is the key is to.
It is used in the patent of the low temperature resistant hot rolled H-shaped of marine petroleum exploitation platform in published relevant microalloying,
Chinese patent application CN103667910A describes a kind of hot rolled H-shaped and its manufacturer with favorable low-temperature impact toughness
Method, by weight percentage, the chemical composition of its molten steel is：C0.05~0.18, Si0.15~0.40, Mn1.0~1.5,
V0.010~0.050, Nb0.015~0.050, Ti0.005~0.025, Al≤0.035, P≤0.020, S≤0.015, surplus
For Fe and trace impurity.The invention mainly by low carbon content, using niobium vanadium titanium-combined microalloying technique, realizes high finish to gauge
Low temperature resistant hot rolled H-shaped production under temperature conditionss.Its problem is that although the steel grade has used microalloy Nb, but intensity
Rank is too high, and -40 DEG C of toughness is nor very high, adds the production cost after Nb increased.
Chinese patent application CN101760704A discloses a kind of economical high-strength and high-weather-resistance hot rolled H-shaped containing vanadium, its
The content of middle V is 0.07%~0.12%, but because it controls less in steel-making and casting process, its low-temperature flexibility is not
It is very high, does not make full use of effects of the V in steel.
In sum, on the hot rolled H-shaped research and development production in microalloying ocean traditional process at home, from
The species of composition design to the relatively low rank of controlling of production process technology is in developmental stage.For Q345E and above rank
The composition design and technique of high-strength low temperature resistant hot rolled H-shaped at home and abroad has not been reported.Due to Q345E and the heat of above rank
Roll the metallurgical process and technical process of H profile steel has difference with traditional process, mainly easily occur low-temperature flexibility it is unstable or
Intensity is nonconforming, it is therefore desirable to metallurgically design and technology controlling and process on take new design and processes route, with compared with
Low cost production is suitable for low temperature resistant hot rolled H-shaped Q345E of ocean platform, to meet the market demand.
The content of the invention
It is an object of the present invention to provide a kind of low temperature resistant hot rolled H-shaped, being organized as H profile steel prepared by the present invention is more
Side shape ferrite and pearlite tissue, yield strength is 350~450MPa, and tensile strength is 480~600MPa, elongation after fracture
>=22%, -40 DEG C of V-type Charpy-V impact power >=200J.
To reach the purpose of foregoing invention, following technical scheme is present invention employs：
A kind of low temperature resistant hot rolled H-shaped, described is hot rolled H-shaped, and by weight percentage its chemical composition is：C0.07
~0.10%, Si0.2~0.4%, Mn1.30~1.60%, P≤0.020%, S≤0.015%, V0.015~0.070%,
Ti0.010~0.030%, balance of Fe and inevitable impurity.
The organization type of H profile steel of the present invention is polygonal ferrite tissue and a small amount of pearlitic structrure, and is not required to
Carry out heat treatment step, yield strength is 350~450MPa, tensile strength is 480~600MPa, elongation after fracture >=22% ,-
40 DEG C of V-type Charpy-V impact power >=200J.
Hereinafter the effect of contained component in the present invention and the selection of consumption are made that and are illustrated：
C：It is mild steel tradition, economic intensified element, the intensity of steel is improved with the increase of carbon content, but it is to steel
Welding performance, mechanical property and corrosion resisting property affect very big, and carbon equivalent Ceq and crack-sensitivity specified from International Institute of Welding refers to
Number Pcm can be seen that carbon is to affect the most sensitive element of welding performance, and impact flexibility also with the increase of carbon content
It is decreased obviously, is designed using low carbon content, the toughness and ductility of steel plate can be improved, and with good weldability and corrosion resistance
Energy.Therefore, it is the matched well that meets high intensity and high tenacity, most basic approach is to reduce carbon content, and by other handss
Duan Tigao intensity, therefore the C content control in the present invention is between 0.07~0.10%.
Si：It is the basic element in steel, deoxidation is mainly played in steelmaking process, generally, in killed steel
Si contents all more than 0.1%.But, si content is higher in steel, can make the toughness of steel, low-temperature flexibility is substantially dropped
It is low and unfavorable to the welding performance of steel during too high levels, the intensity of comprehensive steel, toughness, decay resistance and welding performance etc.
Many considerations, the Si contents in the present invention are controlled between 0.2~0.4%.
Mn：Used as carbon steel and the basic component of low-alloy structural steel, it serves deoxidizer in steelmaking process
Effect, in addition Mn solution strengthening effect is played in steel, it is relatively low due to make steel that there is good solderability then to require that it has
Carbon content, therefore generally by improving manganese content ensureing its intensity, but have data display Mn too high levels (＞ 1.5%) to steel
Welding performance is unfavorable, and may increase center segregation, and the higher easy formation MnS of manganese element is mingled with, and the corrosion resistance of steel is produced
Mn contents in adverse effect, therefore the present invention are controlled between 1.30~1.60%.
P：It is considered as cheap raising resistance to corrosion seawater element, but it can be to the low-temperature flexibility of mother metal and welding hot shadow
Ring area's malleable band and carry out detrimental effect, consider, the P content of various countries' offshore platform steel has stricter upper line traffic control,
0.030% is usually no more than, the P content in the present invention is reached the standard grade and is set to 0.020%.
S：It is the harmful element in steel, MnS is easily formed in steel and is mingled with, its lateral performance, Z-direction performance, resistance to sea to steel
Aqueous corrosion performance etc. is harmful to, and in minimum content, the S contents in the present invention are reached the standard grade positioning for the control that should try one's best in actual production
0.015%.
V：V can improve the quenching degree of steel, dissolve in and have in ferrite invigoration effect, can form stable carbide,
Crystal grain thinning.But V does not have Nb obvious the obstruction effect of austenite recrystallization.There is ability to recrystallization when V is only below 900 DEG C
Retardation function, after austenite transformation, V has almost been completely dissolved, and V only usually affects austenite to ferrum element as a unit
The transformation of body.V can produce the precipitation strength of moderate strength and weaker crystal grain refinement, and be with the percent shared by it into than
Example.N can strengthen the effect of V, in order to obtain bigger reinforcing effect, it is possible to use the precipitation strength of V and the crystal grain of Nb are thin
The method that change combines.Add after V in steel, ductile-brittle transition temperature can be improved, affect low-temperature flexibility, generally require control and exist
Less than 0.10%, in the case where V, Ti coexist, properly increase V to improve welding seam toughness play the role of it is good,
Ti：It is micro alloying element, adds a small amount of Ti to improve the intensity of steel in steel, improves the cold formability energy of steel
And welding performance, can also produce strong precipitation strength and moderate Grain Refinement Effect.The chemism of Ti is very strong, easily
Compound is formed with C, N, O, the S in steel, TiN can effectively prevent austenite crystal growing up in heating process, play refinement
The effect of austenite crystal, and the toughness of welding heat affected zone can be improved, additionally, Ti is alternatively arranged as sulfide modifying element in steel
Use, to improve the performance difference in length and breadth of steel plate.But the addition of Ti, less than 0.005%, DeGrain, addition is excessively easily produced
Raw slab defects.To sum up consider, the Ti contents in the present invention are controlled between 0.010~0.030%.
Another object of the present invention is to, there is provided a kind of preparation method of low temperature resistant hot rolled H-shaped, methods described is wrapped successively
Converter smelting-LF refining-continuous casting-roll forming is included, wherein：
1) converter smelting：
A. Terminal Process Control：[S]<0.020%, [P]<0.015%；
B. slag-stopping tapping, wraps interior thickness of slag layer≤70mm；
C. deoxidation alloying；
2) LF refining：
A. refining cycle：More than 30 minutes (not including the soft blow time)；
B. deoxidation and slag making is operated：Using high voltage low current slugging, Calx 8~12kg/t steel is added；Add Acetylenogen.
1.5~2.5kg/t steel, 2.0~3.0kg/t of Si-Ca-Ba steel-deoxidizings simultaneously adjust slag；Refining process slag and finishing slag basicity 2.0~
3.0；Take and determine after first sample oxygen ＜ 20ppm and then feed 60~90m of titanium wire, wire-feeding velocity >=3m/s；
C. Calcium treatment and soft blow：Before molten steel is outbound, one, gas sample is taken, and according to the real core calcium line of aluminium content feeding in steel
100~150m carries out calcification processing, carries out " soft blow " after line feeding, soft blow time >=10 minute；
3) continuous casting process：
A. pouring basket liquid level >=800mm, whole process protection cast, tundish protection is using " carbon-free alkaline covering agent+rice husk "；
B. covering slag uses mild steel mould flux：Crystallizer inflow temperature >=25 DEG C；Crystallizer cooling, cooling twice
Using weak cold mode；The degree of superheat of control molten steel so as to less than 25 DEG C；
4) technique of rolling：
A. continuous casting billet adds section time >=120min, 30~50min of soaking time, the control of tapping temperature steel billet in heating furnace
At 1160~1240 DEG C；
B. rolled using recrystallization zone, start rolling temperature is controlled at 1020~1060 DEG C, and finishing temperature control is 850~1000
℃；
C. cold temperature control is opened after rolling at 850~950 DEG C, final cooling temperature control at 100 DEG C, rate of cooling is 3~7 DEG C/
s；
D. 100 DEG C of straightening temperature ＜, after carry out stacking slow cooling.
Further, the step 1) deoxidation alloying in, initially with aluminium manganese-ferro deoxidation, aluminum ferromanganese addition is
Secondly 2.5~4kg/t steel, carries out alloying using manganese metal and ferrosilicon and vanadium nitrogen or vanadium iron.
The present invention is allowed to compared with prior art, with advantages below and positive effect as a result of above technical scheme
Really：
(1) the invention provides a kind of low temperature resistant H profile steel that can be produced under traditional hot rolling technology and preparation method thereof,
The method rolling when do not need controlled rolling and controlled cooling, only by appropriate composition design and technology controlling and process, make yield strength 350~
450MPa, the ballistic work ＞ 200J of 40 DEG C of the Charpy-type test ﹣ of employing；
(2) the steel plate organization type that the present invention is manufactured is biphase polygonal ferrite tissue and a small amount of pearlite group
Knit, and the precipitate containing V, Ti, play a part of precipitation strength, employ this microalloying technique, steel making working procedure work
Skill control is simple, and alloy recovery is stable, and the operation of rolling is not required to carry out low temperature controlled rolling, is not required to carry out controlling cold and heat treatment after rolling,
Complete composition design and the production of high level low temperature resistant (40 DEG C of ﹣) ballistic work H profile steel；
(3) the Plate Production low cost that the present invention is manufactured, stable performance is matched and resistance to low with excellent obdurability
Warm ability, resistance to low temperature is good, by composition and technique adjustment, solves original steel-making, steel rolling equipment aging, it is difficult to adapt to
A difficult problem for high added value shaped steel production production, is to realize that general carbon type steel production line establishes base to high-performance type steel production line transformation
Plinth.
The present invention adopts V, Ti microalloying, can improve the quenching degree of steel, dissolves in and have in ferrite invigoration effect, can
To form stable carbide, crystal grain thinning.N can strengthen the effect of V, in order to obtain bigger reinforcing effect, it is possible to use V
Precipitation strength and N the method that combines of crystal grain refinement, in the case where V, Ti coexist, properly increase V tough to improving weld seam
Property plays the role of good.In addition the present invention strictly controls the content of C element, because ductile-brittle transition temperature is with the increase of C content
Improve, and reduce C content and be also beneficial to improve the welding performance of steel.And V can be separated out in a large number at a lower temperature, rise
To the effect for improving intensity.
Description of the drawings
Fig. 1 is the metallograph of the gained H profile steel of embodiment 1；
Fig. 2 is the TEM precipitate figures of the gained H profile steel of embodiment 1；
Fig. 3 is gained H profile steel M of embodiment 13C-type precipitate particle size distribution figure；
Fig. 4 is the gained H profile steel MC type precipitate particle size distribution figure of embodiment 1.
Specific embodiment
Below with the drawings and specific embodiments, the present invention is further detailed explanation.
Embodiment 1：Chemical composition according to steel in the present invention requires that the chemical composition of acquisition is shown in Table 1：
The chemical composition (wt.%) of the steel of 1 embodiment of table 1
Converter smelting endpoint [S]:0.020%, [P]:0.010%.Slag-stopping tapping, thickness of slag layer 50mm in bag.When putting steel
Add aluminum ferromanganese 4kg/t steel.Manganese metal, ferrosilicon, vanadium nitrogen is added to carry out alloying.
Ladle enters the station and adds Calx 8kg/t steel.Acetylenogen. 2.5kg/t steel, aluminum shot, Si-Ca-Ba 3.0kg/t steel carry out slag making
Deoxidation.Refining process slag and finishing slag basicity are 2.5.Take and determine after first sample oxygen 19ppm, feed titanium wire 90m, wire-feeding velocity >=3m/s.
Refining time 31min.Reality core calcium line 150m is fed before soft blow carries out calcification processing, 10 minutes soft blow time.
Pouring basket liquid level:810~815mm, tundish protection adopts " carbon-free alkaline covering agent+rice husk ".Covering slag is used
Mild steel mould flux.25~26.5 DEG C of crystallizer inflow temperature.Crystallizer cooling, cooling twice adopt weak cold mode.Control
The degree of superheat of molten steel processed so as to less than 25 DEG C；It is strict to suppress casting process slag, molten steel is casting continuously to form into 275 × 380mm rectangles
Base, carries out stacking slow cooling to room temperature.
Continuous casting billet is heated to into 1240 DEG C, time inside furnace 240min.Soaking time 30min, entrance finishing temperature is 1040
DEG C, finish rolling final temperature be 1000 DEG C, temperature on cooling table be 900 DEG C, final cooling temperature be 100 DEG C, into aligning, after carry out stacking
Slow cooling, its mechanical property is shown in Table 2.
The mechanical property of the steel plate of 2 embodiment of table 1
Metallographic structure and Sludge Analysis are carried out to the present embodiment gained H profile steel using conventional method, concrete outcome is shown in figure
1-4；As can be seen from Figure 1 material is made up of ferrite and pearlite, and crystal grain arrangement rule in good order, the shaft-like such as is
Crystal grain, grain size is 12 μm or so, and banded structure bandwidth is very tiny, and the crystal grain uniformity is very high, the anti-ductile deformation of material
Ability is very strong, tenacity excellent.
It can be seen that arrow is designated as vanadium titanium from Fig. 2 (b in Fig. 2 is the energy diagram of arrow indication precipitate in a)
Carbonitride is pinned in dislocation, is shaped as trapezoidal, size 30nm or so, it is further seen that several skewness, size exists
The precipitate of below 50nm, shape has rectangle, spherical and irregularly shaped etc..Precipitate is pinned in dislocation, strong to hinder
Dislocation motion, improves the intensity of material.
As can be seen from Figure 3 precipitate is M3The particle size distribution of c-type, wherein size are in 20nm particles below to material
Intensity be obviously improved, in figure it can be seen that 20nm volume below fraction be 0.15%, according to Ashby-Orowan correct mould
Type formula, is obtained M3C-type precipitate can improve yield strength 296MPa.
As can be seen from Figure 4 precipitate is the particle size distribution of MC types, wherein volume integral of the size in below 20nm granules
Number is 0.00625%, according to Ashby-Orowan correction model formula, M is obtained3C-type precipitate can improve yield strength
58Mpa, illustrates that raising of the compound microalloying system of V, Ti to the strength of materials has more obvious effect.
M is can be seen that in figure3C-type precipitate accounts for main, its mass fraction be 1.3508%, and M (C, N) type precipitates compared with
It is few, only 0.0363%.But the precipitate containing V, Ti has larger carrying in the yield strength to material of below 20nm
It is high, it is possible to use precipitation strength mechanism calculates the reinforcement value that they are brought, by calculating, M3The theoretic precipitation strengths of C can
296MPa is reached, the precipitation strength value of M (C, N) is 58MPa.And, Fig. 1 also illustrate that the precipitate containing V is separated out, and add V
The effect of precipitation strength is served afterwards.
Embodiment 2：Chemical composition according to steel in the present invention requires that the chemical composition of acquisition is shown in Table 3：
The chemical composition (wt.%) of the steel of 3 embodiment of table 2
Converter smelting endpoint [S]：0.0:15%, [P]:0.012%.Slag-stopping tapping, thickness of slag layer 70mm in bag.When putting steel
Aluminum ferromanganese addition is 2.5kg/t steel.Manganese metal, ferrosilicon, vanadium nitrogen is added to carry out alloying.
Ladle enters the station and adds Calx 12kg/t steel.Acetylenogen. 1.5kg/t steel, aluminum shot, Si-Ca-Ba 2.0kg/t steel carry out slag making
Deoxidation.Refining process slag and finishing slag basicity are 3.0.Take and determine after first sample oxygen 15ppm, feed titanium wire 80m, wire-feeding velocity >=3m/s.
Refining time 31min.Reality core calcium line 120m is fed before soft blow carries out calcification processing, 11 minutes soft blow time.
Pouring basket liquid level：803~810mm, tundish protection adopts " carbon-free alkaline covering agent+rice husk ".Covering slag is used
Mild steel mould flux.26~27 DEG C of crystallizer inflow temperature.Crystallizer cooling, cooling twice adopt weak cold mode.Control
The degree of superheat of molten steel so as to less than 25 DEG C；It is strict to suppress casting process slag, molten steel is casting continuously to form into 275 × 380mm rectangular blooms,
Stacking slow cooling is carried out to room temperature.
Continuous casting billet is heated to into 1160 DEG C, time inside furnace 120min.Soaking time 50min, entrance finishing temperature is 1040
DEG C, finish rolling final temperature be 850 DEG C, temperature on cooling table be 840 DEG C, final cooling temperature be 100 DEG C, into aligning, after carry out stacking
Slow cooling, its mechanical property is shown in Table 4.
The mechanical property of the steel plate of 4 embodiment of table 2
Embodiment 3：Chemical composition according to steel in the present invention requires that the chemical composition of acquisition is shown in Table 5：
The chemical composition (wt.%) of the steel of 5 embodiment of table 3
Converter smelting endpoint [S]：0.016%, [P]:0.010%.Slag-stopping tapping, thickness of slag layer 60mm in bag.When putting steel
Aluminum ferromanganese addition is 3.5kg/t steel.Manganese metal, ferrosilicon, vanadium iron is added to carry out alloying.
Ladle enters the station and adds Calx 10kg/t steel.Acetylenogen. 2.0kg/t steel, aluminum shot, Si-Ca-Ba 2.5kg/t steel carry out slag making
Deoxidation.Refining process slag and finishing slag basicity are 2.1.Take and determine after first sample oxygen 9ppm and then feed titanium wire 60m, wire-feeding velocity >=3m/s.
Refining time 31min.Reality core calcium line 120m is fed before soft blow carries out calcification processing, 12 minutes soft blow time.
Pouring basket liquid level:805~810mm, tundish protection adopts " carbon-free alkaline covering agent+rice husk ".Covering slag is used
Mild steel mould flux.25.5~27.0 DEG C of crystallizer inflow temperature.Crystallizer cooling, cooling twice adopt weak cold mode.
The degree of superheat of control molten steel so as to less than 25 DEG C；It is strict to suppress casting process slag, molten steel is casting continuously to form into 275 × 380mm rectangles
Base, carries out stacking slow cooling to room temperature.
Continuous casting billet is heated to into 1200 DEG C, time inside furnace 180min.Soaking time 40min, roughing started temperature is 1060
DEG C, finish rolling final temperature be 910 DEG C, temperature on cooling table be 900 DEG C, final cooling temperature be 100 DEG C, into aligning, after carry out stacking
Slow cooling, its mechanical property is shown in Table 6.
The mechanical property of the steel plate of 6 embodiment of table 3
As fully visible, the steel plate in the present invention has excellent toughness and tenacity, and low-temperature impact work is stable.
It should be noted last that, above example is only to illustrate technical scheme and unrestricted.Although ginseng
The present invention is described in detail according to embodiment, it will be apparent to an ordinarily skilled person in the art that the technical side to the present invention
Case is modified or equivalent, and without departure from the spirit and scope of technical solution of the present invention, it all should cover in the present invention
Right in the middle of.
Claims (3)
1. a kind of preparation method of low temperature resistant hot rolled H-shaped, it is characterised in that described is hot rolled H-shaped, by weight percentage
Its chemical composition is：C 0.07~0.10%, Si 0.2~0.4%, Mn 1.30~1.60%, P≤0.020%, S≤
0.015%th, V 0.015~0.070%, Ti 0.010~0.030%, balance of Fe and inevitable impurity；
The organization type of the H profile steel is that polygonal ferrite is organized and pearlitic structrure, and crystal grain arrangement is regular in good order, is
Etc. shaft-like crystal grain；
The preparation method includes successively converter smelting-LF refining-continuous casting-roll forming, wherein：
1) converter smelting：
A. Terminal Process Control：[S]<0.020%, [P]<0.015%；
B. slag-stopping tapping, wraps interior thickness of slag layer≤70mm；
C. deoxidation alloying；
2) LF refining：
A. refining cycle：More than 30 minutes；
B. deoxidation and slag making is operated：Using high voltage low current slugging, Calx 8~12kg/t steel is added；Addition Acetylenogen. 1.5~
2.5kg/t steel, 2.0~3.0kg/t of Si-Ca-Ba steel-deoxidizings simultaneously adjust slag；Refining process slag and finishing slag basicity 2.0~3.0；Take
Oxygen ＜ 20ppm are determined after first sample and then feeds 60~90m of titanium wire, wire-feeding velocity >=3m/s；
C. Calcium treatment and soft blow：Before molten steel is outbound, take one, gas sample, and according to the real core calcium line 100 of aluminium content feeding in steel~
150m carries out calcification processing, carries out " soft blow " after line feeding, soft blow time >=10 minute；
3) continuous casting process：
A. pouring basket liquid level >=800mm, whole process protection cast, tundish protection is using " carbon-free alkaline covering agent+rice husk "；
B. covering slag uses mild steel mould flux：Crystallizer inflow temperature >=25 DEG C；Crystallizer cooling, cooling twice are adopted
Weak cold mode；The degree of superheat of control molten steel so as to less than 25 DEG C；
4) technique of rolling：
A. continuous casting billet adds section time >=120min, 30~50min of soaking time, tapping temperature steel billet control to exist in heating furnace
1160~1240 DEG C；
B. rolled using recrystallization zone, start rolling temperature is controlled at 1020~1060 DEG C, and finishing temperature control is at 850~1000 DEG C；
C. cold temperature control is opened after rolling at 850~950 DEG C, at 100 DEG C, rate of cooling is 3~7 DEG C/s for final cooling temperature control；
D. 100 DEG C of straightening temperature ＜, after carry out stacking slow cooling.
2. the preparation method of low temperature resistant hot rolled H-shaped according to claim 1, it is characterised in that the surrender of the H profile steel
Intensity is 350~450MPa, and tensile strength is 480~600MPa, elongation after fracture >=22%, -40 DEG C of V-type Charpy-V impact powers >=
200J。
3. the preparation method of low temperature resistant hot rolled H-shaped according to claim 1, it is characterised in that the step 1) it is de-
In oxygen alloy, initially with aluminium manganese-ferro deoxidation, aluminum ferromanganese addition is 2.5~4kg/t steel, secondly using manganese metal and ferrosilicon
And vanadium nitrogen or vanadium iron carry out alloying.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510044714.7A CN104630625B (en) | 2015-01-28 | 2015-01-28 | Low-temperature-resistant hot-rolled H-shaped steel and preparation method thereof |
Applications Claiming Priority (1)
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| CN105018861B (en) * | 2015-08-10 | 2017-07-14 | 山东钢铁股份有限公司 | A kind of inexpensive normalizing rolling is hot rolled H-shaped and preparation method thereof |
| CN105714201A (en) * | 2016-04-15 | 2016-06-29 | 山东钢铁股份有限公司 | Hot-rolled H profile steel and preparation method thereof |
| CN105886961A (en) * | 2016-06-07 | 2016-08-24 | 蒋南宁 | High-performance hot-rolled H-shape steel capable of resisting marine atmospheric environment corrosion and preparation method thereof |
| CN106244926A (en) * | 2016-09-28 | 2016-12-21 | 河钢股份有限公司承德分公司 | A kind of containing vanadium steel used for vehicle transmission shaft and production method thereof |
| CN106756471B (en) * | 2016-11-11 | 2018-07-10 | 攀钢集团攀枝花钢铁研究院有限公司 | 345MPa grades of vanadium titanium microalloying anti-seismic structure hot continuous rolling steel bands and preparation method thereof |
| CN107299283A (en) * | 2017-05-27 | 2017-10-27 | 内蒙古包钢钢联股份有限公司 | Depth low temperature resistant hot rolled H-shaped and its production technology |
| CN107475494B (en) * | 2017-07-21 | 2019-04-23 | 河钢股份有限公司邯郸分公司 | A kind of curved control method of air-cooled bainitic steels bloom |
| KR20190111920A (en) * | 2018-03-23 | 2019-10-02 | 닛폰세이테츠 가부시키가이샤 | Rolled H-beam and its manufacturing method |
| CN108642381B (en) * | 2018-05-16 | 2020-02-18 | 山东钢铁股份有限公司 | Hot-rolled high-toughness low-temperature-resistant H-shaped steel with yield strength of 460MPa and preparation method thereof |
| KR20230125287A (en) * | 2021-03-03 | 2023-08-29 | 제이에프이 스틸 가부시키가이샤 | H section steel |
| CN113604735B (en) * | 2021-07-20 | 2022-07-12 | 山东钢铁股份有限公司 | Hot-rolled low-temperature-resistant H-shaped steel with yield strength of 420MPa and preparation method thereof |
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| CN103938079A (en) * | 2014-05-16 | 2014-07-23 | 莱芜钢铁集团有限公司 | Low-temperature resistant hot rolling H section bar with low compression ratio and super-thick specification and production method thereof |
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