CN106756543A - A kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high and its manufacture method - Google Patents
A kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high and its manufacture method Download PDFInfo
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- CN106756543A CN106756543A CN201611137904.4A CN201611137904A CN106756543A CN 106756543 A CN106756543 A CN 106756543A CN 201611137904 A CN201611137904 A CN 201611137904A CN 106756543 A CN106756543 A CN 106756543A
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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
- 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
- C21C7/10—Handling in a vacuum
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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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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 present invention is a kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high, and its chemical component weight percentage is：C：0.04~0.12%, Si：0.15~0.35%, Mn：1.10~1.70%, P：≤ 0.020%, S：≤ 0.0030%, V：0.030~0.060%, Alt：0.005~0.060%, Ceq：0.32~0.41%, Ti：0.005~0.030%, Ca：0.0005~0.0040%, Ni：0.05~0.40%, remaining is Fe and inevitable impurity.Steel plate yield strength >=400MPa of the present invention, tensile strength >=510MPa, it is adapted to high strength ship plate steel of the weld heat input in the range of 150 250kJ/cm, under the conditions of the Large Heat Input Welding of 150kJ/cm and 250kJ/cm, average impact work(of the HAZ of steel plate at 40 DEG C is in more than 150J, without heat treatment, low production cost.
Description
Technical field
The invention belongs to metallurgical technology field, it is related to a kind of Large Heat Input Welding strength ship plate steel high and its manufacture method,
Specifically a kind of 60mm thickness E40 rank TMCP states low cost Large Heat Input Welding strength ship plate steel high and its manufacture method.
Background technology
High input energy welding steel is widely used, such as, in shipbuilding industry, the shipbuilding efficiency using the common deck of boat is only
The a quarter of the high heat input welding deck of boat.The country can only be from external import but expensive when cannot produce.Large-line energy
Welding method is the mode for improving welding procedure efficiency and reduces cost the most practical,《2006~the year two thousand twenty China Steel work
Industry science and technology develops guide》Propose, high heat input welding steel is one of target that China's steel industry is given priority to, tool
There are wide market prospects.
When thermal weld stress is referred to as Large Heat Input Welding more than 50kJ/cm, conventional steel plates are more than 50kJ/ in thermal weld stress
In the case of cm, due to welding heat affected zone tissue it is excessive coarsening, the mechanical property of welding point can occur degradation, or even
Less than the standard requirement of mother metal steel plate, it is to solve Large Heat Input Welding heat affected area that research and development meet high input energy welding steel
The effective way that low-temperature flexibility deteriorates.
Existing high input energy welding steel plate patent document, such as CN1946862A, CN1338528A,
CN101050502A, CN101050504A contain alloy element Nb, and its main purpose is to improve the intensity of mother metal steel plate and tough
Property, high cost.
The content of the invention
The technical problem to be solved in the present invention is：Propose a kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high
And its manufacture method, without adding Nb in the chemical composition of steel, the intensity and toughness of steel are improved using V, Ni micro alloying element,
Product intensity on the premise of Large Heat Input Welding is ensured reaches more than 510MPa, and with short production cycle, rhythm of production is fast, with weight
Big economic implications.
The present invention solve above technical problem technical scheme be：
A kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high, its chemical component weight percentage is：C：
0.04~0.12%, Si：0.15~0.35%, Mn：1.10~1.70%, P：≤ 0.020%, S：≤ 0.0030%, V：0.030
~0.060%, Alt：0.005~0.060%, Ceq：0.32~0.41%, Ti：0.005~0.030%, Ca：0.0005~
0.0040%, Ni：0.05~0.40%, remaining is Fe and inevitable impurity.
The more preferred chemical component weight percentage of the present invention is：C：0.060%, Si：0.24%, Mn：1.52%, P：
0.008%, S：0.001%, V：0.030%, Alt：0.022%, Ceq：0.36%, Ti：0.012%, Ca：0.0008%, Ni：
0.33%, remaining is Fe and inevitable impurity.
Chemical composition is one of key factor of influence continuous casting billet internal soundness and plate property, and the present invention is in order that described
Steel obtains excellent combination property, and the chemical composition to the steel is limited, and reason is：
(1) carbon is most important element in steel, while being also one of generally the least expensive element.Carbon is Qianghian gap solid solution element,
Carbon is added in steel can significant gap solution strengthening effect to steel, so that the intensity of Hi-Stren steel is improved, and
Intensity contribution to steel is maximum.Carbon combines to form carbide with the microalloy element (Nb, Ti, V etc.) in steel, especially in Ovshinsky
Tiny, Dispersed precipitate carbide inclusion is formed in body, plays a part of crystal grain refinement and precipitation strength, improve steel hardness and
Intensity.When phosphorus content increases in steel, surrender and tensile strength are raised, but plasticity and impact flexibility can be reduced, its welding performance
Can be damaged.In order to adapt to Large Heat Input Welding, improve the toughness of steel, the appropriate phosphorus content for reducing Hi-Stren steel can
To improve the low-temperature impact toughness and welding performance of steel plate.For the low-alloy structural steel for welding, phosphorus content is usually no more than
0.20%.Carbon content is reduced to less than 0.10%, even lower, can be effectively improved the tough of Large Heat Input Welding heat affected area
Property, reduce the welding crack sensibility of steel.Designed using low-carbonization in Hi-Stren steel, loss of strength will necessarily be caused.
Still there is high intensity, it is necessary at using rational microalloying on the premise of low-carbon (LC) in order to ensure high input energy welding steel
Reason, intensity is improved by adding micro alloying element.So carbon content of the present invention is limited to 0.04~0.09%.
(2) manganese is weak carbide former, except minority is dissolved in carburizing in vitro, is nearly all dissolved in ferrite and austenite
In, the hardness and intensity of ferrite and austenite in steel are improved, generally increase manganese content come caused by making up because reducing carbon content
Partial intensities lose.Manganese can substantially reduce transition temperature, and the strong grain boundary ferrite that reduces starts transition temperature, promotes needle-like iron
The formation of ferritic.Manganese or good deoxidier and desulfurizing agent, normal same silicon, titanium add carry out complex deoxidization together, and formation has
The duplex impurity of higher sulfur capacity amount, effectively induction intragranular acicular ferrite forming core.Manganese forms fusing point MnS higher with sulphur, can prevent
Only form FeS and produce hot-short phenomenon.Other manganese can increase the tendency of crystalline grain of steel roughening, temper brittleness sensitiveness and excessively thermo-responsive
Property.
(3) silicon can be dissolved in ferrite and austenite so as to improve the hardness and intensity of steel, and making up reduces what carbon content was caused
Partial intensities lose.Silicon has good deoxidation in molten steel, is good deoxidier.Drunk plus a certain amount of during with aluminium deoxidation
Silicon, can significantly improve the deoxidizing capacity of aluminium.But silicone content crosses high energy and promotes imitative grain boundary ferrite forming core, suppresses acicular ferrite
Formed, increase M-A constituent element contents, reduce the plasticity and toughness of steel so that the welding performance reduction of steel.Therefore Large Heat Input Welding
With the composition of steel should low silication, promote fine bainite and ferritic structure to be formed.
(4) aluminium, with stability very high, can generate tiny dispersed oxide and be dispersed in steel as a kind of strong oxidizer
In.These oxides as field trash nucleating center, can induce the attachment of nitride, carbide and sulfide to separate out.Meanwhile, aluminium
Or it is a kind of it is strong determine nitrogen agent, form nano level aluminium nitride precipitate, improve the heat endurance of steel, suppress steel and reheating
AUSTENITE GRAIN COARSENING in journey.But aluminium nitride is only confined within 1100 DEG C to the pinning effect of austenite grain boundary.In Ovshinsky
When body is decomposed, the duplex impurity of aluminium can effectively induce acicular ferrite nucleating, crystal grain thinning and improve toughness.Add in steel
Plus appropriate aluminium, M-A islands quantity is reduced in heat affected area, the reduction of its average length, and retained austenite quantity increases in M-A
Plus, so as to improve the toughness of heat affected area.When aluminium content is higher, the oxide of aluminium is mingled with aggregation cluster, forms thick grain
Son, easily forms formation of crack.Meanwhile, aluminum concentration increase can make to form unfavorable institutional framework in steel, such as promote to form side in steel
Lath ferritic structure, reduces the toughness of steel.
(5) niobium is typical precipitation strength element, and carbon, nitrogen have strong affinity.During normal temperature, the big portion of niobium in steel
Divide is present with carbide, nitride, carbonitride form.Appropriate niobium element can form the second phase grain of small and dispersed
Son, there is extraordinary refined crystalline strengthening and precipitation strength effect in the operation of rolling.These tiny second phase particles can also be in weldering
Pinning austenite crystal in termination process, suppresses grain coarsening.Part niobium can be solid-solution in austenitic matrix, be segregated in austenite crystal
Boundary, suppresses austenite grain boundary and moves to limit growing up for crystal grain, crystal grain thinning by solute drageffect, improves intensity and tough
Property.Meanwhile, niobium has remarkable effect to the tissue of heat affected area and the morphological feature of M-A constituent elements.But niobium can cause the second phase grain
Effect that is sub thick and losing suppression grain coarsening, can also suppress ferritic transformation, promote the formation of granular bainite, cause tough
Property severe exacerbation.So the present invention is not added with niobium.
(6) the unit such as vanadium and carbon, nitrogen have extremely strong affinity, main in steel to exist in the form of carbide and nitride,
Intensity can be improved by precipitation strength.The VN separated out in austenite can suppress Austenite Grain Growth.In ferrite
The VN that area separates out, can increase the forming core core of Intragranular Acicular Ferrite, and two aspects collectively promote crystal grain refinement, significantly improve low-carbon (LC)
The welding performance of low-alloy steel.But in Large Heat Input Welding, the carbonitride of vanadium can not be separated out fully.
(7) titanium and oxygen, nitrogen, carbon have extremely strong affinity, are effective units of a kind of good deoxidier and fixed nitrogen and carbon
Element.Titanyl compound be considered as in steel maximally effective forming core be mingled with, acicular ferrite nucleating can be effectively facilitated.
(8) nickel is to improve the very important element of steel low-temperature flexibility.It is pure solid solution element in steel, can reinforced ferrite base
Body, and with substantially reducing the effect of tough crisp conversion temperature.In liquid or solid-state, can be dissolved each other with iron arbitrary proportion, energy
The pro-eutectoid ferrite for suppressing thick is formed, fining ferrite grains, improves the low-temperature flexibility of steel.Nickel is to expand austenite phase field
Element, can influence the diffusion velocity of carbon and alloying element, prevent pearlite from being formed, improve quenching degree, quenching when slowing down welding
Hard cracking tends to.
(9) sulphur is the harmful element in steel, and it exists in the form of the relatively low FeS of fusing point, is easily caused steel generation hot-short existing
As so as to crack, the S in steel is easily combined with Mn, forms the stratified segregation that MnS is mingled with, and makes intensity and the modeling in thickness of slab direction
Property be greatly lowered, produce lamellar tearing, endanger steel performance.Meanwhile, the MnS in steel under given conditions, with VN, TiN mono-
Play pinning Austenite Grain Growth and induce Intragranular Acicular Ferrite forming core, effectively refined crystal grain and improved toughness.
(10) phosphorus is impurity element, and its maximum harm is serious segregation, the plasticity and toughness of steel is significantly reduced, to weldability
Also there is harmful effect.When being worked with copper one in steel, the atmospheric corrosion resistance of steel can be improved.
By above-mentioned analysis, different elements plays the role of different in high input energy welding steel.According to unit
The feature of element, designs the high input energy welding steel of economical, high intensity, high tenacity and superior weldability.It is of the invention big
The basic ideas of heat input welding steel composition design are to be not added with niobium to ensure weldability, increase manganese and micro alloying element content
The impurity contents such as intensity, control phosphorus, sulphur are improved, crystal grain has effectively been refined and has been improved toughness, the resistance to air for improving steel is rotten
Corrosion energy；Using Oxide Metallurgy method, form the fine of small and dispersed and be mingled with, suppress in welding process austenite grow up and
Control structural transformation so that high input energy welding steel coarse grain zone toughness is maintained at a preferable level.Present invention use V,
Ni micro alloying elements improve the intensity and toughness of steel, without adding Nb, reduce cost.
The TMCP states of the present invention low cost Large Heat Input Welding production technology of strength ship plate steel high, including following operation：Iron
Water desulfurization pretreatment → converter smelting → LF refining → RH refining → continuous castings → strand inspection, judgement → strand examination → continuous casting billet
Heating → de-scaling → rolling → cooling → flaw detection → cutting, sampling → spray printing mark → storage；
Sulfur content control is in S≤0.005%, converter smelting control P content≤0.013%, LF after desulfurizing iron pretreatment
Refining carries out Control and Inclusion Removal and alloying component adjustment, after LF stoves are adjusted to appropriate oxygen content with Si iron, in strict accordance with Ti
The order addition of iron-Al lines-Ca lines, and interval time is no more than 5min；RH refine vacuumize process condition of high vacuum degree≤
Retention time >=30 minute under the conditions of 5.0mbar, continuous casting controls tundish temperature in 8~22 DEG C of liquidus curve, continuous casting billet stacking slow cooling
More than 48 hours；
Continuous blank heating temperature be 1150 DEG C~1250 DEG C, the heat time be 300~400min, tapping temperature be 1130~
1230℃；Rolling uses austenite recrystallization area and Unhydrated cement two-phase control rolling, and roughing is broken using passage heavy reduction
Austenite crystal, reduction in pass >=30mm, roughing start rolling temperature >=1050 DEG C, roughing is into the centre of >=2.0h times of finished product thickness
Base, at 900~1050 DEG C, finish rolling start rolling temperature is 780~880 DEG C to roughing finishing temperature control, every time reduction ratio is 10~
15%；Cooling is controlled after rolling, using section cooling, red temperature is 600~700 DEG C, subsequent air cooling.
So, by the smelting process based on Oxides Metallurgy Technology, tinyization, dispersion, Composite are formed in steel
Oxide particle, using welding hot shadow under the conditions of the small and dispersed inclusion particle pinning high heat input of these high-temperature thermal stabilities
Ring the austenite grain boundary in area, fining austenite grains, while by the use of these oxides as the forming core of intragranular acicular ferrite IAF
Point, makes to form the preferable IAF tissues of obdurability in welding heat affected zone, and then improve the tough of Large Heat Input Welding heat affected area
Property.
Rationally, steel plate comprehensive mechanical property is good, is embodied in for present component：Yield strength >=400MPa, tension
Intensity >=510MPa, is adapted to high strength ship plate steel of the weld heat input in the range of 150-250kJ/cm, in 150kJ/cm and
Under the conditions of the Large Heat Input Welding of 250kJ/cm, the average impact work(of the HAZ of steel plate at -40 DEG C in more than 150J, without heat
Treatment, production cost is relatively low.
The beneficial effects of the invention are as follows：(1) low-carbon (LC) is used without niobium composition design by rational, by based on oxide smelting
The smelting process of technology for gold, forms the oxide particle of tinyization, dispersion, Composite in steel, steady using these high warms
The austenite grain boundary of welding heat affected zone under the conditions of fixed small and dispersed inclusion particle pinning high heat input, refines austenite crystal
Grain.Simultaneously by the use of these oxides as the forming core point of intragranular acicular ferrite IAF, make to form obdurability in welding heat affected zone
Preferable IAF tissues, and then significantly improve the toughness of high heat-input welding heat affected zone.(2) the present invention is combined using TMCP technologies
The big pressure Rolling Production strength ship plate steel high of high temperature low speed, without heat treatment, reduces cost, production process stabilization.
Brief description of the drawings
Fig. 1 is embodiment of the present invention 60mm thickness E40 ranks Large Heat Input Weldings strength ship plate steel welded thin-wall box component coarse grain zone high gold
Phase picture.
Specific embodiment
Embodiment
Embodiment 1-3 is the 60mm thickness E40 ranks Large Heat Input Weldings manufacture method of strength ship plate steel high, using low-carbon (LC) without
Niobium, Oxide Metallurgy technique, add trace element Ni, V, while using Controlled Rolling And Controlled Cooling.
The main chemical compositions of embodiment 1-3 are as shown in table 1：
The main chemical compositions (wt%) of the embodiment of the present invention of table 1
| Embodiment | C | Si | Mn | P | S | Alt | V | Ti | Ni | Ceq |
| Embodiment 1 | 0.08 | 0.24 | 1.52 | 0.008 | 0.0010 | 0.022 | 0.030 | 0.012 | 0.33 | 0.36 |
| Embodiment 2 | 0.10 | 0.20 | 1.40 | 0.010 | 0.0018 | 0.025 | 0.045 | 0.022 | 0.25 | 0.36 |
| Embodiment 3 | 0.05 | 0.28 | 1.60 | 0.014 | 0.0020 | 0.040 | 0.050 | 0.020 | 0.28 | 0.35 |
The rolling cooling technique parameter of each embodiment is as shown in table 2：
Table 2 rolls cooling technique parameter
| Embodiment | Thickness mm | Roughing finishing temperature DEG C | Finish rolling start rolling temperature DEG C | Finishing temperature DEG C | Red temperature DEG C |
| Embodiment 1 | 60 | 1081 | 835 | 826 | 640 |
| Embodiment 2 | 60 | 1073 | 848 | 843 | 580 |
| Embodiment 3 | 60 | 1053 | 827 | 833 | 600 |
Steel billet is wrapped using the E40 rank Large Heat Input Welding strength ship plate steels high of cooling controlling and rolling controlling process production thickness 60mm
Include following operation：Desulfurizing iron pretreatment → converter smelting → LF refining → RH refining → continuous castings → strand inspection, judgement → casting
Base examination → continuous casting billet heating → de-scaling → rolling → cooling → flaw detection → cutting, sampling → spray printing mark → storage；Main work
Skill main points are as follows：
Sulfur content control is in S≤0.005%, converter smelting control P content≤0.013%, LF after desulfurizing iron pretreatment
Refining carries out Control and Inclusion Removal and alloying component adjustment, after LF stoves are adjusted to appropriate oxygen content with Si iron, in strict accordance with Ti
The order addition of iron-Al lines-Ca lines, and interval time is no more than 5min；RH refine vacuumize process condition of high vacuum degree≤
Retention time >=30 minute under the conditions of 5.0mbar, continuous casting controls tundish temperature in 8~22 DEG C of liquidus curve, continuous casting billet stacking slow cooling
More than 48 hours；
Continuous blank heating temperature be 1150 DEG C~1250 DEG C, the heat time be 300~400min, tapping temperature be 1130~
1230℃；Rolling uses austenite recrystallization area and Unhydrated cement two-phase control rolling, and roughing is broken using passage heavy reduction
Austenite crystal, reduction in pass >=30mm, roughing start rolling temperature >=1050 DEG C, roughing is into the centre of >=2.0h times of finished product thickness
Base, at 900~1050 DEG C, finish rolling start rolling temperature is 780~880 DEG C to roughing finishing temperature control, every time reduction ratio is 10~
15%；Cooling is controlled after rolling, using section cooling, red temperature is 600~700 DEG C, subsequent air cooling.The offline slow cooling work of high temperature
Skill：Steel plate hot is placed in cold bed cooling after rectifying, 250~500 DEG C of offline temperature, heap cool time 48 hours obtains the E40 ranks of 60mm
Large Heat Input Welding strength ship plate steel high.
In the present embodiment, heating-up temperature is 1220 DEG C, and soaking time is 140min, and tapping temperature is 1200 DEG C；Roughing is every
Reduction in pass 35mm, middle base of the roughing into 2.2 finished product thicknesses；820~850 DEG C of finish rolling start rolling temperature, every time reduction ratio
＞ 10%；650~680 DEG C of final cooling temperature；440 DEG C of offline temperature, cold using heap after steel plate is offline, heap cool time 48 hours.
Mechanical property of steel plate is as shown in table 3 implemented according to the invention.Embodiment of the present invention steel plate comprehensive mechanical property is good
Good, its yield strength >=400MPa, tensile strength >=510MPa is adapted to height of the weld heat input in the range of 150-250kJ/cm
Strength ship plate steel, under the conditions of the Large Heat Input Welding of 150 and 250kJ/cm, the average impact work(of the HAZ of steel plate at -40 DEG C exists
More than 150J, without heat treatment, production cost is relatively low.
The object performance of the embodiment of the present invention of table 3
In addition to the implementation, the present invention can also have other embodiment.All use equivalents or equivalent transformation shape
Into technical scheme, all fall within the protection domain of application claims.
Claims (5)
1. a kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high, it is characterised in that：Its chemical component weight percentage
Than for：C：0.04~0.12%, Si：0.15~0.35%, Mn：1.10~1.70%, P：≤ 0.020%, S：≤ 0.0030%, V：
0.030~0.060%, Alt：0.005~0.060%, Ceq：0.32~0.41%, Ti：0.005~0.030%, Ca：0.0005~
0.0040%, Ni：0.05~0.40%, remaining is Fe and inevitable impurity.
2. TMCP states as claimed in claim 1 low cost Large Heat Input Welding strength ship plate steel high, it is characterised in that：Its chemistry
Composition by weight percent is：C：0.060%, Si：0.24%, Mn：1.52%, P：0.008%, S：0.001%, V：0.030%, Alt：
0.022%, Ceq：0.36%, Ti：0.012%, Ca：0.0008%, Ni：0.33%, remaining is Fe and inevitable impurity.
3. TMCP states as claimed in claim 1 or 2 low cost Large Heat Input Welding strength ship plate steel high, it is characterised in that：Its
Yield strength >=400MPa, tensile strength >=510MPa, it is 150-250kJ/cm to be adapted to weld heat input, in 150-250kJ/cm
Large Heat Input Welding under the conditions of, the average impact work(of the HAZ of steel plate at -40 DEG C in more than 150J, without heat treatment.
4. the TMCP states as claimed in claim 1 or 2 low cost Large Heat Input Welding production technology of strength ship plate steel high, including
Following operation：Desulfurizing iron pretreatment → converter smelting → LF refining → RH refining → continuous castings → strand inspection, judgement → strand
Examination → continuous casting billet heating → de-scaling → rolling → cooling → flaw detection → cutting, sampling → spray printing mark → storage；Its feature exists
In：
In S≤0.005%, converter smelting control P content≤0.013%, LF refining is entered for sulfur content control after desulfurizing iron pretreatment
Row Control and Inclusion Removal and alloying component are adjusted, after LF stoves are adjusted to appropriate oxygen content with Si iron, in strict accordance with Ti iron-Al
The order addition of line-Ca lines, and interval time is no more than 5min；RH refines vacuumize process in condition of high vacuum degree≤5.0mbar bars
Part lower retention time >=30 minute, continuous casting controls tundish temperature in 8~22 DEG C of liquidus curve, continuous casting billet stacking slow cooling 48 hours with
On；
Continuous blank heating temperature is 1150 DEG C~1250 DEG C, and the heat time is 300~400min, and tapping temperature is 1130~1230
℃；Rolling uses austenite recrystallization area and Unhydrated cement two-phase control rolling, and roughing crushes Ovshinsky using passage heavy reduction
Body crystal grain, reduction in pass >=30mm, roughing start rolling temperature >=1050 DEG C, roughing into >=2.0h times of finished product thickness middle base,
At 900~1050 DEG C, finish rolling start rolling temperature is 780~880 DEG C to roughing finishing temperature control, and every time reduction ratio is 10~15%；
Cooling is controlled after rolling, using section cooling, red temperature is 600~700 DEG C, subsequent air cooling.
5. the TMCP states as claimed in claim 4 low cost Large Heat Input Welding production technology of strength ship plate steel high, its feature
It is：By the smelting process based on Oxides Metallurgy Technology, the oxide of tinyization, dispersion, Composite is formed in steel
Particle, using Austria of welding heat affected zone under the conditions of the small and dispersed inclusion particle pinning high heat input of these high-temperature thermal stabilities
Family name's body crystal boundary, fining austenite grains, while making weldering as the forming core point of intragranular acicular ferrite IAF by the use of these oxides
Connect and formed in heat affected area the preferable IAF tissues of obdurability, and then improve the toughness of Large Heat Input Welding heat affected area.
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| CN108018476A (en) * | 2017-11-24 | 2018-05-11 | 南京钢铁股份有限公司 | A kind of smelting process for improving deck of boat Large Heat Input Welding performance |
| CN109023021A (en) * | 2018-08-29 | 2018-12-18 | 南京钢铁股份有限公司 | A kind of steel plate and its manufacturing method improving obdurability by regulation Al element |
| CN109321847A (en) * | 2017-07-31 | 2019-02-12 | 东北大学 | One kind can EH420 grades of ocean engineering thick steel plates of Large Heat Input Welding and preparation method thereof |
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| CN112322967A (en) * | 2020-09-25 | 2021-02-05 | 南京钢铁股份有限公司 | E500-W150 ultrahigh-strength ship plate steel and manufacturing method thereof |
| CN112322966A (en) * | 2020-09-25 | 2021-02-05 | 南京钢铁股份有限公司 | E550-W100 ultrahigh-strength ship plate steel and manufacturing method thereof |
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