CN106011361B - Improve the Mo-Nb-Ti-Mg steel smelting methods of welding performance - Google Patents
Improve the Mo-Nb-Ti-Mg steel smelting methods of welding performance Download PDFInfo
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- CN106011361B CN106011361B CN201610532216.1A CN201610532216A CN106011361B CN 106011361 B CN106011361 B CN 106011361B CN 201610532216 A CN201610532216 A CN 201610532216A CN 106011361 B CN106011361 B CN 106011361B
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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
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/28—Manufacture of steel in the converter
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0006—Adding metallic additives
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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 kind of Mo Nb Ti Mg steel smelting methods improving welding performance, and the smelting process detailed process technique includes pneumatic steelmaking, LF refining and continuous casting working procedure；The chemical composition and mass percentage of the Mo Nb Ti Mg micro alloyed steels are as follows：C：0.06~0.08%, Mn：1.25~1.60%, S≤0.010%, P≤0.025%, Si：0.20~0.40%, Als：0.010~0.030%, Mo：0.060~0.080%, Ti：0.010~0.020%, Mg：0.002~0.005%, Nb：0.020~0.035%, surplus is Fe and other inevitable impurity.The present invention uses Al final deoxidizings, carries out Mo Nb Ti Mg microalloyings, hence it is evident that improves the obdurability of steel, the control of this forwarding method is simple, and production cost is low, can industrialized production high input energy welding steel.
Description
Technical field
The invention belongs to low-alloy steel manufacturing technology fields, and in particular to improve the Mo-Nb-Ti-Mg steel smeltings of welding performance
Smelting method.
Background technology
Steel plate is widely used in the infrastructures such as building, bridge, pressure vessel, storage tank, pipeline and ship and large size
In building.The enlargement of building element and high stratification development trend require the thickness of steel plate to increase, while having higher synthesis
Performance, including higher mechanical property, efficient processing performance and excellent corrosion resistance and antifatigue destructive characteristics etc..
But as the raising of armor plate strength, impact toughness and welding performance are remarkably decreased, welding crack sensibility increases
Add.The problem of in order to improve the welding efficiency of engineering structure, use Large Heat Input Welding technology in succession in industry, bring therewith, is just
It is that the intensity, toughness of welding heat affected zone declines to a great extent with the raising of weld heat input.Welding heat affected zone（HAZ）Occur tight
Grain coarsening, local softening and the embrittlement of weight, general performance are that the toughness of heat affected area is greatly lowered, and threaten engineering structure
Safety in utilization.It is therefore prevented that the deterioration of welding process heat affected area performance is the key that exploitation high input energy welding steel.
Studies have shown that grain coarsening is the main reason for steel plate toughness is low when welding, the most effectual way of solution is refinement
Austenite grain.Oxides Metallurgy Technology utilizes the fine oxide in steel, by promoting Intragranular Acicular Ferrite forming core to be obviously improved
The tissue of welding heat affected zone becomes the most effective technological approaches for solving high input energy welding steel technical barrier, while steel
Microalloy treatment generates tiny, disperse, refractory oxide and carbon, nitride particle, is precipitated in grain boundary precipitate, inhibits brilliant
Grain length is big, can refine welding heat affected zone crystal grain, improves the strength and toughness of steel, to increase substantially Large Heat Input Welding
Energy.
Japanese data and Chinese patent CN102191429A " a method of improving high heat input welding performance of thick steel plates ",
Chinese patent CN102191356A " inclusion control method of Large Heat Input Welding steel plate ", Chinese patent
CN102296147A " control method of nano-scaled precipitate in thick steel plate for high heat input welding " is mentioned to be carried out using MgO particles
Pinning forms 1400 DEG C of high temperatures（Fusing point is high, is not dissolved, does not grow up）And tiny, Dispersed precipitate oxide containing Mg, sulphur
Compound carrys out pinning austenite grain growing up at high temperature, while promoting the formation of austenite intragranular acicular ferrite, improves
HAZ toughness.And Chinese patent carries out in 50Kg vaccum sensitive stoves, can not try out in industrialized production.
Particle as pinning must have two kinds of characteristics of stability under dispersibility and welding high temperature in steel.In
State patent ZL 200710052135.2 " a kind of soldering steel plate in high intensity in use for ocean by large line energy and its manufacturing method " is used
Ti2O3、A12O3Particle pinning austenite grain boundary, particle exists in Thermal Cycle area high temperatures, but these particle diameters
It is larger, growing up for austenite grain cannot be inhibited well.
The studies above is in control inclusion particle pinning austenite grain boundary and intragranular acicular ferrite is promoted to be formed in effect
It is all not enough, is not directed to certain inclusion particles when promoting Intragranular Acicular Ferrite formation, can also promote to a certain extent
Into the formation of austenite grain boundary pro-eutectoid ferrite, austenite grain boundary pro-eutectoid ferrite equally makes the toughness of steel plate heat affected area
It is greatly lowered.Accordingly, it is determined that microalloy element control inclusion particle pinning austenite grain boundary and the transgranular needle-shaped iron element of promotion
The effect that body is formed inhibits the formation of austenite grain boundary pro-eutectoid ferrite, is the pass for improving high input energy welding steel performance
Key.
Invention content
In order to solve the above technical problems, the object of the present invention is to provide a kind of raising Large Heat Input Welding performance Mo-Nb-
The smelting process of Ti-Mg micro alloyed steels, this method form tiny, Dispersed precipitate refractory oxide in steel, promote transgranular
Ferrite forming core, simultaneous oxidation object and carbon, nitride particle are precipitated in grain boundary precipitate, and inhibition crystal grain is grown up and austenite grain boundary
Pro-eutectoid ferrite is formed, to reach the requirement of industrialized production high input energy welding steel plate.
The present invention is achieved through the following technical solutions：A kind of Mo-Nb-Ti- improving high input energy welding steel performance
Mg microalloying production methods, the smelting process detailed process technique include pneumatic steelmaking, LF refining and continuous casting working procedure；It is described
The chemical composition and mass percentage of Mo-Nb-Ti-Mg micro alloyed steels are as follows：C：0.06~0.08%, Mn：1.25~
1.60%, S≤0.010%, P≤0.025%, Si：0.20~0.40%, Als：0.010~0.030%, Mo：0.060~0.080%,
Ti：0.010~0.020%, Mg：0.002~0.005%, Nb：0.020~0.035%, surplus is Fe and other are inevitably miscellaneous
Matter.
Pneumatic steelmaking process of the present invention, tapping process are added Mo, Mn, Si, Nb, Al final deoxidizings are used in combination.
LF refining process of the present invention adjusts Al to target content, and Ca processing, then progress Ti, Mg microalloying.
LF refining process of the present invention, refining time >=35min, net argon blowing time >=5min after Calcium treatment, when blowing only
Avoid liquid steel level exposed.
LF refining process of the present invention, enter the station liquid steel temperature, the first 1580~1590 DEG C of stove, and stove 1575~1585 pours in company
℃；Aluminum steel feed quantity 1.5-2.5m/t steel after entering the station adds lime, fluorite, drops electrode slugging, aluminium powder is added to make white slag.
LF refining process of the present invention, molten steel before Calcium treatment：S≤0.010%, Als=250~350ppm, T=1580~
1590℃；Calcium treatment uses Ca-Si lines, Ca-Si line feed quantity 1.5-2.5m/t steel；Molten steel Als=150 after Calcium treatment~
300ppm, Ca=25~40ppm.When Als is low, Ca-Si line feed quantities remove the limit, and when the first stove of Als high or continuous casting, Ca-Si lines are fed
Enter to measure the upper limit.
LF refining process of the present invention carries out Ti, Mg alloying after Calcium treatment, and it is outbound to blow 5min only, out-station temperature
1570~1580 DEG C, the first stove or subcontract in non-week out-station temperature than the upper limit improve 5~10 DEG C.
Pneumatic steelmaking process of the present invention makes steel molten iron [P]≤0.090% used, [S]≤0.045%.
Pneumatic steelmaking process of the present invention, terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤
0.030%, molybdenum-iron, ferromanganese, ferrosilicon, niobium is added in [O]=500~800ppm, 1660~1690 DEG C of tapping temperature in tapping process
Iron, ferro-aluminum.
Continuous casting working procedure of the present invention, but, straightening temperature >=900 DEG C, tundish uses carbon-free covering to two cold use weak colds
Agent, tundish is suitable for 15~35 DEG C of the degree of superheat；It opens after pouring normally, casting speed control is between 0.90~1.10m/min.
The present invention adjusts the inventive principle of each element composition：
C：It is the essential element for determining steel strength and welding heat affected zone tissue.When C is less than 0.06%, it is difficult to obtain
Required intensity；Enter peritectoid when as C high, being not easy to form Intragranular Acicular Ferrite, and steel of the C higher than 0.08% should be avoided to solidify
Area influences continuous casting billet quality, therefore designs C 0.06%~0.08%.
Si：It is added as deoxidant element, deoxidation effect is poor when Si is low, but as Si high, promotes microstructure coarsening, and weld
It connects hot and cold crack sensitivity to increase, therefore designs Si 0.20%~0.40%.
Mn：It is to ensure the important element of armor plate strength, and increase the important element of carbon equivalent.When Mn is low, intensity drops
It is low, and the illeffects enhancing of S compounds；Excessively high Mn makes heat affected area toughness degenerate, therefore design Mn 1.25%~
1.60%。
P：Be impurity element, increase the cold brittleness of steel, but P is too low can increase smelting cost, thus design P≤
0.025%。
S：It is the essential element for influencing steel toughness, good de- S not only facilitates the plasticity and toughness for improving steel plate, also helps
In control TiN size to inhibit growing up for heat affected area crystal grain.Certain S contents are intentional to inducing intragranular acicular ferrite
Justice, the excessively high effects that can influence Mg alloyings of S can also influence the effect of Ca processing, therefore design S≤0.010%.
Mo：Mo postpones pro-eutectoid ferrite transformation, promotes the formation of acicular ferrite and bainite, improves low-alloy steel weldering
Stitch the obdurability of metal.Mo improves microalloy element（Nb、Ti）Solid solubility in austenite, delay microalloy carbonitride
Precipitation is precipitated under more microalloy elements will be enable to retain to lower temperature from ferrite, so as to generate
The precipitation enhancement of bigger.Mo can dissolve in the lattice for the microalloy carbonitride being precipitated in ferrite, be formed（M, Mo）
（C, N）（M is microalloy element）, precipitate volume fraction is not only increased, and significantly refine microalloy precipitation size, from
And enhance precipitation strength effect.The better heat stability of the carbonitride of microalloy containing Mo is not easy to be roughened under high temperature.Mo is to iron element
Body has solution strengthening effect, so that the softening after working hardening and recovery temperature and recrystallization temperature is improved, and improve iron strongly
The creep resistance of ferritic effectively inhibits aggregation of the cementite at 450 DEG C~600 DEG C to promote the precipitation of alloy carbide, thus
As the most effective alloying element for the heat resistance for improving steel.Mo can improve the hardenability of steel, cold to welding to improve steel
The sensibility of crackle, according to national standard, Mo should be controlled 0.08% hereinafter, therefore designing Mo 0.06%~0.08%.
Nb：In microalloy element, Nb is that crystal grain thinning is most effective, is mainly reflected in austenite crystal during reheating
Growing up for grain is suppressed, and in the case where not losing toughness, intensity improves.After adding micro Nb, the crystal grain and group of hot rolled steel plate
It knitting and is significantly refined, Nb can be effectively reduced the crystallite dimension after recrystallization, for the long large interface of crystal grain after recrystallization,
For tiny NbC precipitated phases to it with certain pinning effect, effect of dragging is played in the migration for being dissolved Nb atom pair crystal boundaries.Containing
Micro Nb elements are added in the steel for having TiN, the formation of grain boundary ferrite is suppressed, to reduce embrittlement region, sweating heat
The toughness of the zone of influence is improved.Nb too high levels promote lath ferrite to be formed, unfavorable to toughness, therefore design Nb
0.020%~0.035%.
Al：Infrastructure elements of the Al as molten-steel deoxidation agent and crystal grain thinning can be formed largely after adding Al deoxidations in steel
Al2O3Particle, can be used as steel solidification, phase transformation process Heterogeneous Nucleation core, also can be used as the element being subsequently added
The support of oxide forming core.Al content is required in most standard, therefore designs Al 0.010%~0.035%.
Ti：Austenite recrystallization and effect and the Nb of precipitation strength are controlled in low-carbon structure as microalloy element（C、
N）Similar, at 1400 DEG C, the effect of fining austenite grains is most strong.Under conditions of Nb, Ti compound addition, TiN is utilized
Heat affected area austenite grain is refined, ideal Ti/N is 2.73.The content for determining Ti, N with this condition, had both ensured TiN's
Content is again precipitated its liquid in molten steel.The TiN particles that small and dispersed distribution is precipitated under high temperature effectively hinder austenite
Crystal grain is grown up, and the Enhancing Nucleation Density of intragranular acicular ferrite is increased.On the other hand, contain Ti by core of refractory oxide2O3's
In matrix phase around duplex impurity, the microcell of poor C, poor Mn are formed, improves ferritic phase temperature（Ac3）, increase ferrite
Nuclear driving force（Ac3-Ar3）, promote ferrite crystal grain forming core, therefore design Ti 0.010%~0.020%.
Mg：Appropriate Mg is added, the microinclusions largely containing MgO cores are generated in steel matrix, MgO particles have
2800 DEG C of high-melting-point fully meets the field trash requirement for not dissolving and rising pinning effect at 1400 DEG C, effectively inhibits Austria
The growth of family name's body crystal grain.The addition of Mg will disperse, improve the form of Ti oxides simultaneously, remarkably promote intragranular acicular ferrite
It is formed, to achieve the purpose that improve heat affected area toughness, therefore designs Mg 0.002%~0.005%.
The advantageous effect generated using above-mentioned technical proposal is：The present invention uses Al final deoxidizings, carries out Mo-Nb-Ti-Mg
Microalloying is to form disperse, abundant, tiny MgO, Al2O3、Ti2O3Refractory oxide is core, outer layer attachment
Based on the complex inclusion of MnO, MnS, contain Ti2O3Duplex impurity around the poor area existing Mn promote in austenite crystal
The formation of acicular ferrite.On the other hand, Mo, Nb of certain content inhibits while crystal grain thinning improves the obdurability of steel
The formation of crystal boundary pro-eutectoid ferrite.The tiny inclusion particle of this outer portion and carbon, nitride pinning austenite grain boundary, several sides
Face collective effect has fully refined heat affected area crystal grain, hence it is evident that improves the obdurability of steel.The control of this forwarding method is simple, is produced into
This is low, can industrialized production high input energy welding steel.
Description of the drawings
Fig. 1 is 200 times of 1 high input energy welding steel heat affected area of embodiment tissue；
Fig. 2 is 200 times of 2 high input energy welding steel heat affected area of embodiment tissue；
Fig. 3 is 200 times of 3 high input energy welding steel heat affected area of embodiment tissue；
Fig. 4 is 1 high input energy welding steel as-cast structure duplex impurity shape appearance figure of embodiment；
Fig. 5 is 1 high input energy welding steel as-cast structure duplex impurity energy spectrum diagram of embodiment；
Fig. 6 is 2 high input energy welding steel as-cast structure duplex impurity shape appearance figure of embodiment；
Fig. 7 is 2 high input energy welding steel as-cast structure duplex impurity energy spectrum diagram of embodiment；
Fig. 8 is 3 high input energy welding steel as-cast structure duplex impurity shape appearance figure of embodiment.
Specific implementation mode
With reference to specific embodiment, the present invention is described in further detail.
Embodiment 1
A kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance, it is specific as follows：
Smelting high input energy welding steel process is 120t top and bottom combined blown converters -120tLF ladle furnace refinings-continuous casting.
Molten iron condition：Molten iron [P]≤0.090%, [S]≤0.045%.
Converter：Terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤0.030%, [O]=500~800ppm,
Molybdenum-iron, ferromanganese, ferrosilicon, ferro-niobium, ferro-aluminum is added in 1685 DEG C of tapping temperature in tapping process.
LF：Refining time 40min, net argon blowing time 8min, avoids liquid steel level exposed when blowing only after Calcium treatment.Enter the station steel
1580 DEG C of stove pours in coolant-temperature gage, the first 1585 DEG C of stove, company.Aluminum steel feed quantity 2.0m/t steel after entering the station adds lime, fluorite, drops electrode
Slugging adds aluminium powder to make white slag according to slag condition.Molten steel before Calcium treatment：S≤0.010%, Als=280ppm, T=1585 DEG C.Calcium treatment is adopted
With Ca-Si lines, Ca-Si line feed quantity 1.85m/t steel, molten steel Als=260ppm after Calcium treatment, Ca=32ppm are carried out after Calcium treatment
Ti, Mg alloying, it is outbound to blow 5min only, 1575 DEG C of out-station temperature.
Continuous casting：But, 920 DEG C of straightening temperature, tundish uses carbon-free covering agent to two cold use weak colds, and tundish is suitable for overheat
20 DEG C of degree.It opens after pouring normally, casting speed control is in 1.0m/min.
The chemical composition of the big line energy welding steel of gained is shown in Table 1, and impact property is shown in Table 2.
Embodiment 2
A kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance, it is specific as follows：
Smelting high input energy welding steel process is 120t top and bottom combined blown converters -120tLF ladle furnace refinings-continuous casting.
Molten iron condition：Molten iron [P]≤0.090%, [S]≤0.045%.
Converter：Terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤0.030%, [O]=500~800ppm,
Molybdenum-iron, ferromanganese, ferrosilicon, ferro-niobium, ferro-aluminum is added in 1680 DEG C of tapping temperature in tapping process.
LF：Refining time 45min, net argon blowing time 10min, avoids liquid steel level exposed when blowing only after Calcium treatment.It enters the station
1575 DEG C of stove pours in liquid steel temperature, the first 1580 DEG C of stove, company.Aluminum steel feed quantity 1.5m/t steel after entering the station adds lime, fluorite, drop electricity
Polarize slag, adds aluminium powder to make white slag according to slag condition.Molten steel before Calcium treatment：S≤0.010%, Als=300ppm, T=1580 DEG C.Calcium treatment
Using Ca-Si lines, Ca-Si line feed quantity 1.9m/t steel, molten steel Als=280ppm, Ca=34ppm, Calcium treatment are laggard after Calcium treatment
Row Ti, Mg alloying, it is outbound to blow 5min only, 1572 DEG C of out-station temperature.
Continuous casting：But, 905 DEG C of straightening temperature, tundish uses carbon-free covering agent to two cold use weak colds, and tundish is suitable for overheat
22 DEG C of degree.It opens after pouring normally, casting speed control is in 1.0m/min.
The chemical composition of the big line energy welding steel of gained is shown in Table 1, and impact property is shown in Table 2.
Embodiment 3
A kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance, it is specific as follows：
Smelting high input energy welding steel process is 120t top and bottom combined blown converters -120tLF ladle furnace refinings-continuous casting.
Molten iron condition：Molten iron [P]≤0.090%, [S]≤0.045%.
Converter：Terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤0.030%, [O]=500~800ppm,
Molybdenum-iron, ferromanganese, ferrosilicon, ferro-niobium, ferro-aluminum is added in 1670 DEG C of tapping temperature in tapping process.
LF：Refining time 42min, net argon blowing time 6min, avoids liquid steel level exposed when blowing only after Calcium treatment.Enter the station steel
1585 DEG C of stove pours in coolant-temperature gage, the first 1590 DEG C of stove, company.Aluminum steel feed quantity 1.9m/t steel after entering the station adds lime, fluorite, drops electrode
Slugging adds aluminium powder to make white slag according to slag condition.Molten steel before Calcium treatment：S≤0.010%, Als=320ppm, T=1590 DEG C.Calcium treatment is adopted
With Ca-Si lines, Ca-Si line feed quantity 1.75m/t steel, molten steel Als=300ppm after Calcium treatment, Ca=30ppm are carried out after Calcium treatment
Ti, Mg alloying, it is outbound to blow 5min only, 1575 DEG C of out-station temperature.
Continuous casting：But, 910 DEG C of straightening temperature, tundish uses carbon-free covering agent to two cold use weak colds, and tundish is suitable for overheat
25 DEG C of degree.It opens after pouring normally, casting speed control is in 1.0m/min.
The chemical composition of the big line energy welding steel of gained is shown in Table 1, and impact property is shown in Table 2.
Embodiment 4
A kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance, it is specific as follows：
Smelting high input energy welding steel process is 80t top and bottom combined blown converters -80tLF ladle furnace refinings-continuous casting.
Molten iron condition：Molten iron [P]≤0.090%, [S]≤0.045%.
Converter：Terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤0.030%, [O]=500~800ppm,
Molybdenum-iron, ferromanganese, ferrosilicon, ferro-niobium, ferro-aluminum is added in 1660 DEG C of tapping temperature in tapping process.
LF：Refining time 38min, net argon blowing time 5min, avoids liquid steel level exposed when blowing only after Calcium treatment.Enter the station steel
1578 DEG C of stove pours in coolant-temperature gage, the first 1586 DEG C of stove, company.Aluminum steel feed quantity 2.0m/t steel after entering the station adds lime, fluorite, drops electrode
Slugging adds aluminium powder to make white slag according to slag condition.Molten steel before Calcium treatment：S≤0.010%, Als=350ppm, T=1586 DEG C.Calcium treatment is adopted
With Ca-Si lines, Ca-Si line feed quantity 2.5m/t steel, molten steel Als=300ppm after Calcium treatment, Ca=25ppm are carried out after Calcium treatment
Ti, Mg alloying, it is outbound to blow 5min only, 1570 DEG C of out-station temperature.First stove or non-week subcontract 1585 DEG C of out-station temperature.
Continuous casting：But, 900 DEG C of straightening temperature, tundish uses carbon-free covering agent to two cold use weak colds, and tundish is suitable for overheat
15 DEG C of degree.It opens after pouring normally, casting speed control is in 0.90m/min.
The chemical composition of the big line energy welding steel of gained is shown in Table 1, and impact property is shown in Table 2.
Embodiment 5
A kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance, it is specific as follows：
Smelting high input energy welding steel process is 160t top and bottom combined blown converters -160tLF ladle furnace refinings-continuous casting.
Molten iron condition：Molten iron [P]≤0.090%, [S]≤0.045%.
Converter：Terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤0.030%, [O]=500~800ppm,
Molybdenum-iron, ferromanganese, ferrosilicon, ferro-niobium, ferro-aluminum is added in 1690 DEG C of tapping temperature in tapping process.
LF：Refining time 35min, net argon blowing time 7min, avoids liquid steel level exposed when blowing only after Calcium treatment.Enter the station steel
1580 DEG C of stove pours in coolant-temperature gage, the first 1590 DEG C of stove, company.Aluminum steel feed quantity 2.5m/t steel after entering the station adds lime, fluorite, drops electrode
Slugging adds aluminium powder to make white slag according to slag condition.Molten steel before Calcium treatment：S≤0.010%, Als=250ppm, T=1590 DEG C.Calcium treatment is adopted
With Ca-Si lines, Ca-Si line feed quantity 1.5m/t steel, molten steel Als=150ppm after Calcium treatment, Ca=40ppm are carried out after Calcium treatment
Ti, Mg alloying, it is outbound to blow 5min only, 1580 DEG C of out-station temperature.First stove or non-week subcontract 1590 DEG C of out-station temperature.
Continuous casting：But, 910 DEG C of straightening temperature, tundish uses carbon-free covering agent to two cold use weak colds, and tundish is suitable for overheat
35 DEG C of degree.It opens after pouring normally, casting speed control is in 1.10m/min.
The chemical composition of the big line energy welding steel of gained is shown in Table 1, and impact property is shown in Table 2.
Chemical composition in 1 embodiment 1-5 of table（mass%）
| C | Mn | S | P | Si | Als | Mo | Ti | Mg | Nb | |
| Embodiment 1 | 0.07 | 1.42 | 0.005 | 0.019 | 0.25 | 0.026 | 0.07 | 0.020 | 0.0025 | 0.035 |
| Embodiment 2 | 0.06 | 1.51 | 0.005 | 0.022 | 0.21 | 0.028 | 0.07 | 0.017 | 0.0031 | 0.027 |
| Embodiment 3 | 0.06 | 1.55 | 0.006 | 0.017 | 0.23 | 0.030 | 0.07 | 0.013 | 0.0022 | 0.029 |
| Embodiment 4 | 0.07 | 1.25 | 0.006 | 0.023 | 0.40 | 0.030 | 0.06 | 0.020 | 0.0050 | 0.020 |
| Embodiment 5 | 0.08 | 1.60 | 0.010 | 0.025 | 0.20 | 0.010 | 0.08 | 0.010 | 0.0020 | 0.035 |
Note：Surplus is iron and inevitable impurity
The impact property of 2 embodiment of table（Heat input 150KJ/cm）
| Gap position | Notch type | Test temperature/DEG C | Impact absorbing energy/J | |
| Embodiment 1 | Melt run+2mm VHT2 | V-type | -20 | 188.4 |
| Embodiment 2 | Melt run+2mm VHT2 | V-type | -20 | 197.1 |
| Embodiment 3 | Melt run+2mm VHT2 | V-type | -20 | 195.5 |
| Embodiment 4 | Melt run+2mm VHT2 | V-type | -20 | 192.6 |
| Embodiment 5 | Melt run+2mm VHT2 | V-type | -20 | 194.1 |
Table 2 list 40mm steel plate weld heat inputs be 150KJ/cm when, embodiment 1-5 welding heat affected low temp area punching
Hit toughness value.Steel plate produced by the invention has rational heat affected zone organization structure, by formed it is abundant it is transgranular it is needle-shaped,
Piece columnar ferrite and granular bainite, and effective inclusion particle have refined heat affecting significantly to the pinning of austenite grain boundary
District's groups are knitted, and the obdurability of steel is made to significantly improve.
Attached drawing 1-3 can be seen that crystal grain is tiny in high input energy welding steel heat affected zone organization, and microscopic structure mainly has
Ferrite and pearlite forms.Fig. 4 is typical acicular ferrite in 1 as-cast structure of embodiment, and size is about 3 μm, induces it
The field trash of generation is mainly Mg, and the duplex impurity that the elements such as Al, Si are formed promotes the shape of austenite intragranular acicular ferrite
At, keep the crystal grain of welding heat affected zone tiny, while crystal grain thinning improves the obdurability of steel, inhibition crystal boundary proeutectoid ferrite
The formation of body, ballistic work absorption value increase several times.The field trash energy spectrum diagram and reality of the induction acicular ferrite of embodiment 3 in Fig. 8
It is similar to apply example 2, therefore omits.Embodiment 4 and 5 product figure of embodiment are similar to embodiment 1-3, therefore omit.
The above embodiments are only used to illustrate and not limit the technical solutions of the present invention, although with reference to above-described embodiment to this hair
It is bright to be described in detail, it will be understood by those of ordinary skill in the art that：Still can the present invention be modified or be waited
With replacing, without departing from the spirit or scope of the invention, or any substitutions, the power in the present invention should all be covered
In sharp claimed range.
Claims (6)
1. a kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance, which is characterized in that the smelting process detailed process
Technique includes pneumatic steelmaking, LF refining and continuous casting working procedure；The chemical composition and quality percentage of the Mo-Nb-Ti-Mg micro alloyed steels
Content is as follows：C：0.06~0.08%, Mn：1.25~1.60%, S≤0.010%, P≤0.025%, Si：0.20~0.40%,
Als：0.010~0.030%, Mo：0.060~0.080%, Ti：0.010~0.020%, Mg：0.002~0.005%, Nb：0.020
~0.035%, surplus is Fe and other inevitable impurity, the pneumatic steelmaking process, tapping process be added Mo, Mn, Si,
Nb, is used in combination Al final deoxidizings, the pneumatic steelmaking process, terminal target [C]=0.04~0.06%, [P]≤0.015%, [S]≤
0.030%, molybdenum-iron, ferromanganese, ferrosilicon, niobium is added in [O]=500~800ppm, 1660~1690 DEG C of tapping temperature in tapping process
Iron, ferro-aluminum, the LF refining process adjustment Al to target content, and Ca processing, then carry out Ti, Mg microalloying, the LF
Refining procedure, molten steel before Calcium treatment：S≤0.010%, Als=250~350ppm, T=1580~1590 DEG C；Calcium treatment uses Ca-
Si lines, Ca-Si line feed quantity 1.5-2.5m/t steel；Molten steel Als=150~300ppm after Calcium treatment, Ca=25~40ppm.
2. a kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance according to claim 1, which is characterized in that
The LF refining process, refining time >=35min, net argon blowing time >=5min, avoids liquid steel level naked when blowing only after Calcium treatment
Dew.
3. a kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance according to claim 2, which is characterized in that
The LF refining process, enter the station liquid steel temperature, the first 1580~1590 DEG C of stove, and 1575~1585 DEG C of stove pours in company；Aluminum steel after entering the station
Feed quantity 1.5-2.5m/t steel adds lime, fluorite, drops electrode slugging, aluminium powder is added to make white slag.
4. a kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance according to claim 3, which is characterized in that
The LF refining process carries out Ti, Mg alloying after Calcium treatment, and it is outbound to blow 5min only, 1570~1580 DEG C of out-station temperature, and first
It subcontracts out-station temperature in stove or non-week and improves 5~10 DEG C than the upper limit.
5. a kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance according to claim 1, which is characterized in that
The pneumatic steelmaking process makes steel molten iron [P]≤0.090% used, [S]≤0.045%.
6. special according to a kind of Mo-Nb-Ti-Mg steel smelting methods improving welding performance of claim 1-5 any one of them
Sign is that the continuous casting working procedure, but, straightening temperature >=900 DEG C, tundish uses carbon-free covering agent to two cold use weak colds, intermediate
Packet is suitable for 15~35 DEG C of the degree of superheat；It opens after pouring normally, casting speed control is between 0.90~1.10m/min.
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| CN1189193A (en) * | 1996-04-17 | 1998-07-29 | 新日本制铁株式会社 | Steel having improved toughness in welding heat-affected zone |
| CN1380910A (en) * | 2000-05-09 | 2002-11-20 | 新日本制铁株式会社 | Thick steel plate being excellent in CTOD characteristic in welding heat affected zone and having yield strength of 460 MPa or more |
| CN1894434A (en) * | 2003-12-19 | 2007-01-10 | 新日本制铁株式会社 | Steel plates for ultra-high-strength linepipes and ultra-high-strength linepipes having excellent low-temperature toughness and manufacturing methods thereof |
| CN102080193A (en) * | 2011-01-10 | 2011-06-01 | 东北大学 | Structural steel for welding with ultra-great heat input and manufacturing method thereof |
| CN104651714A (en) * | 2013-11-19 | 2015-05-27 | 新日铁住金株式会社 | Steel sheet |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1189193A (en) * | 1996-04-17 | 1998-07-29 | 新日本制铁株式会社 | Steel having improved toughness in welding heat-affected zone |
| CN1380910A (en) * | 2000-05-09 | 2002-11-20 | 新日本制铁株式会社 | Thick steel plate being excellent in CTOD characteristic in welding heat affected zone and having yield strength of 460 MPa or more |
| CN1894434A (en) * | 2003-12-19 | 2007-01-10 | 新日本制铁株式会社 | Steel plates for ultra-high-strength linepipes and ultra-high-strength linepipes having excellent low-temperature toughness and manufacturing methods thereof |
| CN102080193A (en) * | 2011-01-10 | 2011-06-01 | 东北大学 | Structural steel for welding with ultra-great heat input and manufacturing method thereof |
| CN104651714A (en) * | 2013-11-19 | 2015-05-27 | 新日铁住金株式会社 | Steel sheet |
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