CN110129539A - A kind of production technology of 500MPa grades of ocean engineering H profile steel - Google Patents
A kind of production technology of 500MPa grades of ocean engineering H profile steel Download PDFInfo
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- CN110129539A CN110129539A CN201910472158.1A CN201910472158A CN110129539A CN 110129539 A CN110129539 A CN 110129539A CN 201910472158 A CN201910472158 A CN 201910472158A CN 110129539 A CN110129539 A CN 110129539A
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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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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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
- C21D2211/002—Bainite
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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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Abstract
The invention belongs to metallurgical material technical field, in particular to a kind of production technology of 500MPa grades of ocean engineering H profile steel.A kind of production technology of 500MPa grades of ocean engineering H profile steel, it is characterised in that: slab is heated to 1100~1200 DEG C, keeps the temperature at least 2 hours, forges steel billet；Two-phase control rolling is carried out respectively in austenite recrystallization area and Unhydrated cement after heating steel billet is kept the temperature at least 2 hours to 1200~1250 DEG C, 5~7 passages are rolled altogether, after the completion of rolling bainitic transformation area Ms~650 DEG C are cooled to the cooling rate of 30~150 DEG C/s, after be air-cooled to room temperature, both.The present invention provides a kind of production technologies of 500MPa grades of ocean engineering H profile steel, develop 500MPa ocean engineering H profile steel, improve intensity on the basis of the original, and performance is stablized, and compensate for domestic blank.
Description
Technical field
The invention belongs to metallurgical material technical field, in particular to a kind of production of 500MPa grades of ocean engineering H profile steel
Technique.
Background technique
A large amount of H profile steels are applied in ocean engineering field, offshore platform, are rushed for carrying gravitational load and lateral
Load is hit, guarantees the smooth probing and exploitation of marine oil and gas.Since the active time of offshore platform is than seas such as ship classes
Tooling is for high by 50%, therefore it is required that the steel used must have higher obdurability.The country generallys use " microalloying+control
System rolling " technology produces high strength steel, and the production technology of High Strength H-Beam mainly uses " V-N " or " V-Nb " microalloy
Meter and recrystallization zone controlled rolling are set up in chemical conversion separately.Product tissue is mainly ferrite and pearlite, and grain size is bent at 9 grades or more
Intensity is taken lower than 450MPa.Domestic H profile steel can satisfy the needs of most of ocean engineering, but high strength and large specification ocean work
Journey is still needed to H profile steel from external import.Up to the present, industrialization is still not implemented with H profile steel in China 500MPa grades of ocean engineerings
The continuous casting billet size that production, mainly reason have the production line of force to use is limited, and the bigger H profile steel rolling reduction of specification is smaller,
Edge of a wing thickness is more than the H profile steel of 24mmH700 × 300, and mechanical property is generally low.In addition, most of large H-shaped steel production line
Lack the ability of regulation and control to rolled piece performance.In terms of the development trend and user's service condition that current steel produces, ocean engineering H
The product of steel can develop to Limit specifications.To meet tomorrow requirement, burning optimization on line is carried out to rolled piece and effectively controls cooling and property
Energy regulation is an important directions of H profile steel development.
Summary of the invention
In order to solve the above technical problems, proposing a kind of sea 500MPa grades of for the H profile steel more than specification of H700 × 300
The manufacturing technique method of foreign engineering H profile steel mainly includes ingredient design, Unhydrated cement controlled rolling, rolls rear ultrafast quickly cooling
But three aspects of technology.The present invention is based on ingredient-technique-structure property modulation process to complete 500MPa grades of ocean engineering H-types
The exploitation of steel, ingredient, which designs, reduces carbon content, and carbon equivalent control increases the alloys such as Nb, Ti, Cu, Cr, Ni 0.42~0.52
Element, addition microalloy element improve the harden ability of steel itself, promote the generation of bainitic transformation, inhibit ferrite transformation,
Make it can be obtained bainite structure under the conditions of natural air cooling.Using Unhydrated cement controlled rolling technique+ultrafast quickly cooling
But technology makes the microscopic structure for testing steel be changed to bainite+acicular ferrite structure by conventional ferrite+pearlite, mentions
High intensity improves toughness.Using Unhydrated cement controlled rolling method can effective refining grain size, improve H profile steel
Mechanical property；Ultra Fast Cooling is used after the completion of rolling, is cooled to bainite transformation section, is brought it about bainite phase
Become, subsequent natural air cooling to room temperature.
Slab is heated to 1100~1200 DEG C by a kind of production technology of 500MPa grades of ocean engineering H profile steel, and heat preservation is extremely
It is 2 hours few, forge steel billet；In austenite recrystallization area and not after heating steel billet is kept the temperature at least 2 hours to 1200~1250 DEG C
Recrystallization zone carries out two-phase control rolling respectively, rolls 5~7 passages altogether, cold with the cooling rate of 30~150 DEG C/s after the completion of rolling
But to bainitic transformation area Ms~650 DEG C, after be air-cooled to room temperature, both,
First stage recrystallization zone: start rolling temperature is 1020~1100 DEG C, and 2 or 3 passes are completed in first stage rolling,
Total reduction is 35~50%；
Second stage Unhydrated cement: start rolling temperature is 920~950 DEG C, and finishing temperature is 820~880 DEG C, second stage
3 or 4 passages are completed in rolling, and total reduction is 50~65%.
The production technology of 500MPa grades of ocean engineering H profile steel of the present invention is preferred, and slab is heated to 1100 DEG C, is protected
Temperature 2 hours forges steel billet；It is distinguished after heating steel billet is kept the temperature 2 hours to 1250 DEG C in austenite recrystallization area and non-recrystallization
Not carry out two-phase control rolling, roll 7 passages altogether, bainite phase be cooled to the cooling rate of 30~150 DEG C/s after the completion of rolling
Become area Ms~650 DEG C, after be air-cooled to room temperature, both,
First stage recrystallization zone: start rolling temperature is 1050 DEG C, and 3 passes, total reduction are completed in first stage rolling
It is 42%；
Second stage Unhydrated cement: start rolling temperature is 950 DEG C, and finishing temperature is 850 DEG C, and second stage rolling completes 4
Passage, total reduction 58.6%.
Technique of the present invention is not using in the method for crystal region controlled rolling, as far as possible increase austenite Unhydrated cement
950 DEG C~Ar3Deflection, finishing temperature control at 820~880 DEG C, make test structure of steel retain to the greatest extent refinement.It is difficult to understand
Family name's body Unhydrated cement controlled rolling is when temperature is in 950 DEG C~Ar3When, it is tied again since austenite does not occur for this temperature range
The plastic deformation of crystalline substance, accumulation can be such that austenite grain is elongated, and form Zona transformans in intra-die.The increasing of grain boundary area in this way
Add the Enhancing Nucleation Density for improving austenite, carbonitride Second Phase Particles are preferentially precipitated at the austenite and Zona transformans being elongated
Growing up for crystal grain can be prevented, the austenite grain after phase transformation attenuates to improve steel with the increase of Unhydrated cement reduction ratio
Intensity, improve the toughness of steel.In Rolling Production, most of deformation exists existing high strength and large specification ocean engineering H profile steel
950 DEG C or so are just complete, and only last a time is rolled at 850 DEG C, and Unhydrated cement deflection is smaller.The present invention uses
Unhydrated cement controlled rolling, the deflection for increasing 950 DEG C or less Unhydrated cements can be obviously improved the obdurability of steel.This
Austenite recrystallization does not occur for temperature range, and the plastic deformation of accumulation can be such that austenite grain is elongated, in intra-die shape
At Zona transformans.The increase of grain boundary area in this way improves the Enhancing Nucleation Density of austenite, excellent at the austenite and Zona transformans being elongated
Carbonitride Second Phase Particles, which are first precipitated, can also prevent growing up for crystal grain, and the austenite grain after phase transformation is with Unhydrated cement pressure
The increase of lower rate and attenuate to improve the intensity of steel, improve the toughness of steel.
Meanwhile the present invention is cooled to bainite using rear Ultra Fast Cooling is rolled with the cooling rate of 30~150 DEG C/s
Phase change zone Ms~650 DEG C make to test the more refinement bainite+acicular ferrite structures of steel acquisition.
Ultra-rapid cooling is carried out to the hardening austenite for completing continuous large deformation and strain accumulation, rolled piece is made to run through Austria
The area Shi Ti terminates cooling in the transformation temperature of ferritic transformation in austenite, to restrained effectively austenite crystal before phase change
Grain length is big.Phase transformation under ultra-rapid cooling technique, which can control, to be conducive to generate tiny phase in relatively low temperature range
Become tissue；Meanwhile the amount of precipitation that microalloy element occurs in During Ultra Fast Cooling after rolling is reduced, and microalloy element is caused to exist
Low-temperature region Precipitation.With the continuous development of H profile steel continually developed with rolling technique, it is desirable that realize during the rolling process
In short-term, quickly, accurate temperature control, and technologies such as conventional section cooling, aerosol be cooling are difficult to full since cooling velocity is not high
This requirement of foot.The Ultra Fast Cooling cooling velocity that the present invention uses is sufficiently large, has unconventional cooling capacity, rationally
The high pressure water that the cooling nozzles intensively arranged spray acts on H profile steel surface and breaks the steam blanket that H profile steel rolls rear surface, makes to cool down
The heat exchange of water and H profile steel is more abundant, effectively contacts steel, reduces finishing temperature in a very short period of time, promotes H profile steel
Comprehensive performance, solve the problems such as current H profile steel rhythm of production is slow, at high cost, properties of product are low.
In the production technology of 500MPa grades of ocean engineering H profile steel of the present invention, the slab ingredient is according to weight hundred
Point than containing C:0.04~0.1%, Si:0.15~0.35%, Mn:1.4~2.0%, Nb:0.03~0.1%, Ti:0.01~
0.03%, Cr:0.1~0.5%, Ni:0.1~0.5%, Cu:0.1~0.4%, Mo:0.1~0.4%, surplus Fe, carbon equivalent
Control is 0.42~0.52.
Further, the carbon equivalent control is 0.48.
C0.04~0.1%, Si0.15~0.35%, Mn1.4~2.0%, Nb0.03~0.1%, Ti0.01~
0.03%, Cr0.1~0.5%, Ni0.1~0.5%, Cu0.1~0.4%, Mo0.1~0.4%, surplus Fe, carbon equivalent control
0.42~0.52.Ingredient design uses the mentality of designing for replacing ferrite and pearlite with bainite and acicular ferrite, mentions
The intensity rank of high ocean engineering H profile steel.
C0.04~0.1%: improving intensity, stable austenite, and content excessively will form excessive carbide damage toughness；
Si0.15~0.35%: solution strengthening effect is very strong, and the intensity and hardness of steel can be improved, and a small amount of Si can be refined
Pearlite, also can be improved harden ability, and the harden ability and resistance to tempering that can be further improved steel is added in Si and Mn simultaneously.Si is because strong
Change ferrite and wearability is contributed, meanwhile, Si can also improve the corrosion resistance of steel, after the conditioned processing of silico-manganese steel steel,
There is good anti-seawater corrosion ability.Si can reduce bainite transformation temperature, and move to right bainite transformation C curve.Si can hinder
Hinder the precipitation of carbide and increase the retained austenite scale of construction in steel, form carbide-free Bainite, while also improving the low of steel
The temperature range that warm temper brittleness occurs, allows steel to carry out tempering heat treatment at a higher temperature；
Mn1.4~2.0%: austenite former improves harden ability, promotes bainitic transformation, improves intensity；
Nb0.03~0.1%: the Nb in steel can refine crystal grain, especially austenite grain and recrystallized structure, increase
Phase interface improves intensity.Nb can form NbC in conjunction with C, by NbC to the pinning effect of crystal boundary and the Nb atom of solid solution
Inhibit the recrystallization of high temperature deformation process to the drag interaction of crystal boundary, expands Unhydrated cement range, final fining ferrite
Crystal grain.In addition, the precipitation enhancement of Xiang Keqi containing Nb that low-temperature space is precipitated；
Ti0.01~0.03%:Ti can be formed in steel highly stable, disperse, high melting-point, high rigidity carbide, from
And improve the intensity of steel.Tiny alloying element Ti, in steel in conjunction with N, the TiN of formation small and dispersed distribution is particle stabilized to be present in
At austenite grain boundary, growing up for austenite grain is prevented in heating process, guarantees to obtain fine austenite crystal grain, after guaranteeing to roll
The toughness of steel plate；
Cr0.1~0.5%: it is slow to spread mobile comparison in iron, while also reducing Carbon diffusion rate, and Cr increases, makes
Isothermal curve moves right, and extends incubation time, reduces critical cooling rate, improves harden ability.Meanwhile with the increasing of Cr amount
Add, perlitic transformation temperature increases, and bainite transformation temperature reduces.Cr can improve the harden ability of steel, through hardening effect not as good as Mn,
Mo, but it is stronger than Si, Ni, and Cr can exist in the form of carbide.
Ni0.1~0.5%: among the austenite stabilizing elements can be such that C curve moves to right, and improve the harden ability of steel.Ni is because improving
γ/α phase transformation nucleating work improves γ, α two-phase free energy difference and reduces critical transition temperature.Ni can reduce each element in steel
Diffusion rate, and austenite decomposition is delayed to change, to improve the harden ability of steel.Intensity is improved, is caused when reducing rolling by Cu
Defect, improve the weatherability under the effect of a degree of salinity；
Cu0.1~0.4%:Ni, Cu are added simultaneously, can improve the toughness of steel while improving bainitic steel intensity.
In addition, addition Cu and Ni can also improve the corrosion resistance of steel.With the corrosion rate drop of the steel of inch addition Cr, Ni and Cu element
It is low.
Mo0.1~0.4%: the harden ability of steel can be improved in the Mo of solid solution, and the Carbide Precipitation of Mo improves intensity；
Plate can be used in order to reduce experimentation cost in the actual production and test that technique of the present invention is suitable for H profile steel
Blank simulates the edge of a wing deformation of H profile steel, specifically:
By heating steel billet to austenitizing temperature, heating and temperature control keeps the temperature 2 hours, is forged into section at 1100 DEG C
It having a size of 80 × 100 steel billet, is rolled with slab rolling instead of shaped blank, simulates the edge of a wing deformation of H profile steel.
Slab of the present invention is made by method disclosed in the prior art, i.e., smelts, refines and be poured according to set component
Slab is made.
A preferred technical solution of the invention are as follows: a kind of production technology of 500MPa grades of ocean engineering H profile steel, it is described
Technique includes following processing steps:
Step 1: slab is made according to ingredient smelting, refining and the casting of setting, slab ingredient contains C according to weight percent
0.06%, Si 0.25%, Mn 1.65%, Nb 0.08%, Ti 0.015%, Cu 0.25%, Cr 0.3%, Ni 0.3%,
Mo 0.25%, surplus Fe, carbon equivalent 0.48；
Step 2: steel billet being reheated to austenitizing temperature, heating and temperature control keeps the temperature 2 hours at 1100 DEG C, forging
Causing sectional dimension is 80 × 100 steel billet, is rolled with slab rolling instead of shaped blank, and the edge of a wing deformation of H profile steel is simulated；
Step 3: heating steel billet is kept the temperature 2 hours to 1250 DEG C, austenite recrystallization area and Unhydrated cement respectively into
Row two-phase control rolling rolls 7 passages altogether, and first stage recrystallization zone start rolling temperature is 1050 DEG C, and first stage rolling completes three
Passes, second stage Unhydrated cement start rolling temperature are 950 DEG C, and finishing temperature is 850 DEG C, and second stage rolling completes four
Passage；The total reduction of first stage is 42%, and the total reduction of second stage is 58.6%；
Step 4: be directly entered Ultrafast cooling device after the completion of rolling and cooled down, after the completion of rolling with 30~150 DEG C/
The cooling rate of s is cooled to bainitic transformation area Ms~650 DEG C, after be air-cooled to room temperature, obtain experiment steel.
The yield strength of steel obtained by the production technology of 500MPa grades of ocean engineering H profile steel of the present invention is 500~
700MPa, tensile strength are 650~900MPa, and -40 DEG C of side knock function are 50~300J, -40 DEG C of impact of collision function are 50~
350J or more, elongation percentage are 14~25%.
The invention has the benefit that the present invention provides a kind of production technology of 500MPa grades of ocean engineering H profile steel,
It develops 500MPa ocean engineering H profile steel, improves intensity on the basis of the original, and performance is stablized, and compensates for domestic sky
It is white.Technique of the present invention, which rolls rear Ultra Fast Cooling, can fundamentally accelerate the cooling velocity after rolling, and improve production speed
Rate reduces the use of microalloy element, saves production cost, and the adjustable extent of technique is big, is suitable for industrial applications.
Detailed description of the invention
Fig. 1 is the microscopic structure tested at steel thickness direction 1/8 in embodiment 1；
Fig. 2 is the microscopic structure tested at steel thickness direction 1/4 in embodiment 1；
Fig. 3 is the microscopic structure tested at steel thickness direction 1/2 in embodiment 1；
Fig. 4 is the microscopic structure tested at steel thickness direction 1/8 in embodiment 2；
Fig. 5 is the microscopic structure tested at steel thickness direction 1/4 in embodiment 2；
Fig. 6 is the microscopic structure tested at steel thickness direction 1/2 in embodiment 2；
Fig. 7 is the microscopic structure tested at steel thickness direction 1/8 in embodiment 3；
Fig. 8 is the microscopic structure tested at steel thickness direction 1/4 in embodiment 3；
Fig. 9 is the microscopic structure tested at steel thickness direction 1/2 in embodiment 3.
Specific embodiment
Following non-limiting embodiments can with a person of ordinary skill in the art will more fully understand the present invention, but not with
Any mode limits the present invention.
Test method described in following embodiments is unless otherwise specified conventional method；The reagent and material, such as
Without specified otherwise, commercially obtain.
" Ultrafast cooling device " used in following embodiments is that Authorization Notice No. is that CN202185466U China is practical new
" the rolling rear ultra-fast cooling device of Ultra Fast Cooling " of type patent disclosure.
Embodiment 1
Step 1: slab is made according to ingredient smelting, refining and the casting of setting, slab ingredient contains C according to weight percent
0.06%, Si 0.25%, Mn 1.65%, Nb 0.08%, Ti 0.015%, Cu 0.25%, Cr 0.3%, Ni 0.3%,
Mo 0.25%, Fe are surplus, carbon equivalent 0.48；
Step 2: steel billet being reheated to austenitizing temperature, heating and temperature control keeps the temperature 2 hours at 1100 DEG C, forging
Causing sectional dimension is 80 × 100 steel billet, is rolled with slab rolling instead of shaped blank, and the edge of a wing deformation of H profile steel is simulated；
Step 3: heating steel billet is kept the temperature 2 hours to 1250 DEG C, austenite recrystallization area and Unhydrated cement respectively into
Row two-phase control rolling rolls 7 passages altogether, and first stage recrystallization zone start rolling temperature is 1050 DEG C, and first stage rolling completes three
Passes, second stage Unhydrated cement start rolling temperature are 950 DEG C, and finishing temperature is 850 DEG C, and second stage rolling completes four
Passage；The total reduction of first stage is 42%, and the total reduction of second stage is 58.6%；
Step 4: being directly entered Ultrafast cooling device after the completion of rolling and cooled down, by 6.7s, final cooling temperature 530
DEG C, returning hot temperature is 575 DEG C, is air-cooled to room temperature later, obtains experiment steel.
The yield strength that gained tests steel is 517MPa, and tensile strength 764MPa, -40 DEG C of side knock function are 158J, -
40 DEG C of impact of collision function are 231J, elongation percentage 21.3%.Tissue at the experiment steel thickness direction 1/8 of acquisition is mainly with lath
Based on bainite and tiny granular bainite, mainly with Dispersed precipitate M/ on bainite ferrite at thickness direction 1/4 and 1/2
Based on the island A.
Embodiment 2
Step 1: slab is made according to ingredient smelting, refining and the casting of setting, slab ingredient contains C according to weight percent
0.06%, Si 0.25%, Mn 1.65%, Nb 0.08%, Ti 0.015%, Cu 0.25%, Cr 0.3%, Ni 0.3%,
Mo 0.25%, Fe are surplus, carbon equivalent 0.48；
Step 2: steel billet being reheated to austenitizing temperature, heating and temperature control keeps the temperature 2 hours at 1100 DEG C, forging
Causing sectional dimension is 80 × 100 steel billet, is rolled with slab rolling instead of shaped blank, and the edge of a wing deformation of H profile steel is simulated；
Step 3: heating steel billet is kept the temperature 2 hours to 1250 DEG C, austenite recrystallization area and Unhydrated cement respectively into
Row two-phase control rolling rolls 7 passages altogether, and first stage recrystallization zone start rolling temperature is 1050 DEG C, and first stage rolling completes three
Passes, second stage Unhydrated cement start rolling temperature are 950 DEG C, and finishing temperature is 850 DEG C, and second stage rolling completes four
Passage；The total reduction of first stage is 42%, and the total reduction of second stage is 58.6%；
Step 4: being directly entered Ultrafast cooling device after the completion of rolling and cooled down, by 8s, final cooling temperature 500
DEG C, returning hot temperature is 550 DEG C, is air-cooled to room temperature later, obtains experiment steel.
The yield strength that gained tests steel experiment steel is 521MPa, tensile strength 765MPa, and -40 DEG C of side knock function are
244J, -40 DEG C of impact of collision function are 263J, elongation percentage 21.3%.Tissue at the experiment steel thickness direction 1/8 of acquisition is main
Based on ferrite bainite and tiny granular bainite, mainly with disperse on bainite ferrite at thickness direction 1/4 and 1/2
It is distributed based on the island M/A.
Embodiment 3
Step 1: slab is made according to ingredient smelting, refining and the casting of setting, slab ingredient contains C according to weight percent
0.06%, Si 0.25%, Mn 1.65%, Nb 0.08%, Ti 0.015%, Cu 0.25%, Cr 0.3%, Ni 0.3%,
Mo 0.25%, Fe are surplus, carbon equivalent 0.48；
Step 2: steel billet being reheated to austenitizing temperature, heating and temperature control keeps the temperature 2 hours at 1100 DEG C, forging
Causing sectional dimension is 80 × 100 steel billet, is rolled with slab rolling instead of shaped blank, and the edge of a wing deformation of H profile steel is simulated；
Step 3: heating steel billet is kept the temperature 2 hours to 1250 DEG C, austenite recrystallization area and Unhydrated cement respectively into
Row two-phase control rolling rolls 7 passages altogether, and first stage recrystallization zone start rolling temperature is 1050 DEG C, and first stage rolling completes three
Passes, second stage Unhydrated cement start rolling temperature are 950 DEG C, and finishing temperature is 850 DEG C, and second stage rolling completes four
Passage；The total reduction of first stage is 42%, and the total reduction of second stage is 58.6%；
Step 4: being directly entered Ultrafast cooling device after the completion of rolling and cooled down, by 10s, final cooling temperature 480
DEG C, returning hot temperature is 520 DEG C, is air-cooled to room temperature later, obtains experiment steel.
The yield strength that gained tests steel experiment steel is 546MPa, tensile strength 762MPa, and -40 DEG C of side knock function are
244J, -40 DEG C of impact of collision function are 254J, elongation percentage 21.3%.Tissue at the experiment steel thickness direction 1/8 of acquisition is main
Based on ferrite bainite and tiny granular bainite, mainly with disperse on bainite ferrite at thickness direction 1/4 and 1/2
It is distributed based on the island M/A.
Claims (7)
1. a kind of production technology of 500MPa grades of ocean engineering H profile steel, it is characterised in that: slab is heated to 1100~1200
DEG C, at least 2 hours are kept the temperature, steel billet is forged；It is tied again after heating steel billet is kept the temperature at least 2 hours to 1200~1250 DEG C in austenite
Crystalline region and Unhydrated cement carry out two-phase control rolling respectively, 5~7 passages are rolled altogether, with the cold of 30~150 DEG C/s after the completion of rolling
But rate is cooled to bainitic transformation area Ms~650 DEG C, after be air-cooled to room temperature, both,
First stage recrystallization zone: start rolling temperature is 1020~1100 DEG C, and 2 or 3 passes, stagnation pressure are completed in first stage rolling
Lower rate is 35~50%；
Second stage Unhydrated cement: start rolling temperature is 920~950 DEG C, and finishing temperature is 820~880 DEG C, second stage rolling
3 or 4 passages are completed, total reduction is 50~65%.
2. technique according to claim 1, it is characterised in that:
First stage recrystallization zone: start rolling temperature is 1050 DEG C, and 3 passes are completed in first stage rolling, and total reduction is
42%；
Second stage Unhydrated cement: start rolling temperature is 950 DEG C, and finishing temperature is 850 DEG C, and 4 passages are completed in second stage rolling,
Total reduction is 58.6%.
3. technique according to claim 1, it is characterised in that: the slab ingredient according to weight percent containing C:0.04~
0.1%, Si:0.15~0.35%, Mn:1.4~2.0%, Nb:0.03~0.1%, Ti:0.01~0.03%, Cr:0.1~
0.5%, Ni:0.1~0.5%, Cu:0.1~0.4%, Mo:0.1~0.4%, surplus Fe, carbon equivalent control 0.42~
0.52。
4. technique according to claim 1, it is characterised in that: by heating steel billet to austenitizing temperature, heating temperature control
System keeps the temperature 2 hours at 1100 DEG C, is forged into the steel billet that sectional dimension is 80 × 100, is rolled with slab rolling instead of shaped blank
System simulates the edge of a wing deformation of H profile steel.
5. technique according to claim 1, it is characterised in that: smelted according to set component, slab is made in refining and casting.
6. technique according to claim 1, it is characterised in that: the technique includes following processing steps:
Step 1: slab is made according to ingredient smelting, refining and the casting of setting, slab ingredient contains C according to weight percent
0.06%, Si 0.25%, Mn 1.65%, Nb 0.08%, Ti 0.015%, Cu 0.25%, Cr 0.3%, Ni 0.3%,
Mo 0.25%, surplus Fe, carbon equivalent 0.48；
Step 2: steel billet being reheated to austenitizing temperature, heating and temperature control keeps the temperature 2 hours, be forged at 1100 DEG C
The steel billet that sectional dimension is 80 × 100 is rolled with slab rolling instead of shaped blank, simulates the edge of a wing deformation of H profile steel；
Step 3: by heating steel billet to 1250 DEG C keep the temperature 2 hours, carry out two respectively in austenite recrystallization area and Unhydrated cement
Stage rolling rolls 7 passages altogether, and first stage recrystallization zone start rolling temperature is 1050 DEG C, and first stage rolling is completed 3 passages and rolled
System, second stage Unhydrated cement start rolling temperature are 950 DEG C, and finishing temperature is 850 DEG C, and 4 passages are completed in second stage rolling；The
The total reduction in one stage is 42%, and the total reduction of second stage is 58.6%；
Step 4: being directly entered Ultrafast cooling device after the completion of rolling and cooled down, with 30~150 DEG C/s's after the completion of rolling
Cooling rate is cooled to bainitic transformation area Ms~650 DEG C, after be air-cooled to room temperature, obtain experiment steel.
7. technique according to claim 1, it is characterised in that: the yield strength of gained steel is 500~700MPa, tension
Intensity is 650~900MPa, and -40 DEG C of side knock function are 50~300J, and -40 DEG C of impact of collision function are 50~350J or more, are prolonged
Stretching rate is 14~25%.
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