CN109097685A - A kind of high input energy welding steel plate and preparation method thereof - Google Patents
A kind of high input energy welding steel plate and preparation method thereof Download PDFInfo
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- CN109097685A CN109097685A CN201811008618.7A CN201811008618A CN109097685A CN 109097685 A CN109097685 A CN 109097685A CN 201811008618 A CN201811008618 A CN 201811008618A CN 109097685 A CN109097685 A CN 109097685A
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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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—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
- 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
- C22C38/06—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
-
- 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
Abstract
The invention discloses a kind of high input energy welding steel plate and its manufacturing methods, belong to polar low-temperature shipping steel technical field, the present invention uses low-carbon V-N-Ti microalloying and B micro-alloying technology, V, N, Ti, B rational proportion, optimized alloy constituent content, and prepared using three stage rolling techniques, to refine steel plate ferrite grain size, steel plate low-temperature flexibility, intensity are improved, the low-temperature flexibility of welding point is improved.It is C:0.07~0.10%, Si:0.10~0.30%, Mn:0.5-2.0%, S :≤0.001%, P :≤0.005, Als:0.02~0.06%, Ti:0.008~0.015%, B:0.0008~0.0015%, N:0.007~0.009%, V:0.04~0.1% that it is formed by percentage to the quality, remaining is Fe and inevitable impurity element；It is dissolved nitrogen content=N-0.28Ti-1.27B-0.03V, is dissolved nitrogen content less than 0.003%, wherein N, Ti, B, V are the mass percentage content of each element.Above-mentioned high input energy welding steel plate can be used for the construction of polar region ship.
Description
Technical field
The invention belongs to polar low-temperature shipping steel technical field more particularly to a kind of high input energy welding steel plate and its
Preparation method.
Background technique
It peters out as routine can exploit the oil gas energy, Arctic energy reserve abundant is by more and more passes
Note.The investigation that the United States Geological office of surveying in 2008 completes shows that petroleum, natural gas and liquefied natural gas reserves reach respectively in the Arctic Circle
To 90,000,000,000 barrels, 47 tcms and 4,400,000,000 barrels, account for about energy total amount is not verified in the whole world 22%.Meanwhile global greenhouse is imitated
It should make arctic heating aggravation, sea ice area coverage is reduced continuously and healthily, is increasingly conducive to development of resources and ship's navigation.Cause
This, polar region ship gradually has from the high-grade reinforced direction of icebreaking characteristics from the reinforced court in inferior grade ice formation and sends out in recent years
Exhibition, the novel business ice breaker demands such as polar region oil carrier, polar region LNG ship, polar region container ship with ice-breaking capacity obtain quickly
Increase.
Arctic navigation meteorological condition and sea situation are extremely severe, are related to sea ice, low temperature, wind and snow, sea fog etc., and phase polar night in winter is flat
Equal about -40 DEG C, -53 DEG C of the lowest temperature of temperature；Meanwhile ship must endure as hitting repeatedly for ice sheet with ice sheet contact line with lower portion
It hits.Existing steel is difficult to meet the comprehensive performances such as the prerequisite low-temperature flexibility of polar region shipping steel institute, intensity, weldability.
Summary of the invention
In view of the above analysis, aiming at the shortcomings in the prior art, the present invention is intended to provide a kind of high input energy welding steel
Plate and preparation method thereof improves steel plate low-temperature flexibility, intensity, big line energy using low-carbon V-N-Ti microalloying and B microalloying
Measure Low Temperature Impact Toughness of Heat-affected Zone.
The purpose of the present invention is mainly achieved through the following technical solutions:
A kind of high input energy welding steel plate, the ingredient of steel plate is by percentage to the quality are as follows: C:0.07~0.10%, Si:
0.10~0.30%, Mn:0.5-2.0%, S :≤0.001%, P :≤0.005, Als:0.02~0.06%, Ti:0.008~
0.015%, B:0.0008~0.0015%, N:0.007~0.009%, V:0.04~0.1%, remaining is for Fe and unavoidably
Impurity element；Be dissolved nitrogen content=N-0.28Ti-1.27B-0.03V, be dissolved nitrogen content less than 0.003%, wherein N, Ti, B,
V is the mass percentage content of each element.
Further, the ingredient of steel plate is by percentage to the quality are as follows: C:0.08~0.09%, Si:0.16~0.20%, Mn:
1.2~1.5%, S :≤0.001%, P :≤0.005, Als:0.03~0.04%, Ti:0.014~0.015%, B:0.0008
~0.0010%, N:0.0081~0.0089%, V:0.06~0.1%, remaining is Fe and inevitable impurity element；Solid solution
Nitrogen content=N-0.28Ti-1.27B-0.03V is dissolved nitrogen content less than 0.003%, and wherein N, Ti, B, V are the quality of each element
Degree.
Further, the tissue signature of steel plate is ferrite, the isometric ferrite and pearlite of phase transformation with sub boundary, is had
The ferrite of sub boundary has the function of improving armor plate strength.
Further, forging stock is heated to 1100 DEG C of heat preservation 0.5h, using three stage rollings, first stage roughing, second-order
Section finish rolling, the rolling of phase III two-phase section.
Further, for the ferrite crystal grain average-size of steel plate less than 7 μm, steel plate tensile strength is 490~520MPa, surrender
Intensity is 400~420MPa, and elongation percentage is 32%~36%, and v-notch ballistic work at -60 DEG C is 200~240J.
Further, exist in welding heat affected zone of steel plate under the conditions of 100kJ/cm thermal weld stress having a size of 0.2~
0.4 μm of BN-MnS- (Ti, V) (C, N) and BN-MnS-Al2O3Particle, and as Intragranular Acicular Ferrite forming core core.
Further, in welding heat affected zone with area percentage bainite content be 5~7%, polygonal ferrite contains
Amount is 70~85%.
Further, the v-notch ballistic work of -50 DEG C of welding heat affected zone be 210~230J, welding heat affected zone it is tough crisp
- 50 DEG C of transition temperature or less.
The present invention also provides a kind of preparation methods of high input energy welding steel plate, and forging stock is heated to 1100 DEG C of heat preservations
0.5h, using three stage rollings, first stage roughing, second stage finish rolling, the rolling of phase III two-phase section.
Further, 1050~1070 DEG C of first stage roughing start rolling temperature, first stage roughing finishing temperature 950~970
DEG C, second stage finish rolling start rolling temperature 810~820,790~800 DEG C of second stage finish rolling finishing temperature, phase III two-phase section
770~780 DEG C of start rolling temperature, 750~760 DEG C of finishing temperature.First stage adds up deflection 40~50%, and second stage is accumulative
Deflection 30~40%, phase III add up deflection 20~30%.
Compared with prior art, the present invention has the beneficial effect that:
1) a kind of high input energy welding steel plate provided by the invention, the TiN being precipitated using low-carbon V-N-Ti microalloying,
On the one hand the particles such as vanadium nitrogen compound are used for pinning austenite grain, on the other hand the particle as Intragranular Acicular Ferrite forming core, mentions
The high low-temperature flexibility of steel plate, intensity；
2) B micro-alloying technology, the elements rational proportion such as V, N, Ti, B, Al, optimized alloy element are used in nitrogen-increasing steel
BN-MnS- (Ti, V) (C, N) and BN-MnS-Al is precipitated in welding heat affected zone in content2O3Particle, as Intragranular Acicular Ferrite forming core
Core promotes ferritic formation, reduces the tissue area percentage such as ferrite side plate tissue, granular bainite, M-A,
Improve Low Temperature Impact Toughness of Heat-affected Zone.V-notch ballistic work >=200J when -50 DEG C of welding heat affected zone, it is welding heat affected
Ductile-brittle transition temperature≤- 50 DEG C in area, the construction of the ship, offshore platform structure that can be used for being on active service in polar region region.
3) high input energy welding steel plate preparation method of the invention, takes three stage rollings, steel plate is greatly improved
Yield strength, tensile strength and low-temperature flexibility, after Large Heat Input Welding, -50 DEG C of welding heat affected zone excellent in low temperature toughness.
It is this method simple production process, low in cost.
Other features and advantages of the present invention will illustrate in the following description, also, part can become from specification
It obtains it is clear that understand through the implementation of the invention.The objectives and other advantages of the invention can be by written explanation
Specifically noted structure is achieved and obtained in book and claims.
Detailed description of the invention
Fig. 1 comparative example base material metallographic structure；
The 1 base material metallographic structure of Fig. 2 embodiment；
The v-notch ballistic work of Fig. 3 comparative example and 1 welding heat affected zone 100kJ/cm of embodiment welding；Fig. 4 embodiment 1
Welding heat affected zone metallographic structure；
The welding heat affected zone metallographic structure of Fig. 5 comparative example；
The SEM shape appearance figure of the transgranular polygonal ferrite of Fig. 6 embodiment 1 forming core on BN-MnS- (Ti, V) (C, N) particle；
The SEM energy spectrum diagram of the transgranular polygonal ferrite of Fig. 7 embodiment 1 forming core on BN-MnS- (Ti, V) (C, N) particle；
The N element Surface scan of the transgranular polygonal ferrite of Fig. 8 embodiment 1 forming core on BN-MnS- (Ti, V) (C, N) particle
Figure；
The B element Surface scan figure of Fig. 9 embodiment 1 BN-MnS- (Ti, V) (C, N) particle；
The V element Surface scan figure of Figure 10 embodiment 1 BN-MnS- (Ti, V) (C, N) particle；
The Ti element surface scan figure of Figure 11 embodiment 1 BN-MnS- (Ti, V) (C, N) particle；
The S element surface scan figure of Figure 12 embodiment 1 BN-MnS- (Ti, V) (C, N) particle；
The Mn element surface scan figure of Figure 13 embodiment 1 BN-MnS- (Ti, V) (C, N) particle；
1 intragranular acicular ferrite of Figure 14 embodiment is in BN-MnS-Al2O3The SEM shape appearance figure of forming core on particle；
1 intragranular acicular ferrite of Figure 15 embodiment is in BN-MnS-Al2O3The SEM shape appearance figure of forming core on particle；
1 intragranular acicular ferrite of Figure 16 embodiment is in BN-MnS-Al2O3The energy spectrum diagram of forming core on particle；
1 BN-MnS-Al of Figure 17 embodiment2O3The N element Surface scan figure of particle；
1 BN-MnS-Al of Figure 18 embodiment2O3The B element Surface scan figure of particle；
1 BN-MnS-Al of Figure 19 embodiment2O3The Al element surface scan figure of particle；
1 BN-MnS-Al of Figure 20 embodiment2O3The S element surface scan figure of particle；
1 BN-MnS-Al of Figure 21 embodiment2O3The Mn element surface scan figure of particle；
1 BN-MnS-Al of Figure 22 embodiment2O3Particle structure schematic diagram.
Appended drawing reference:
1- bainite；2- polygonal ferrite；3- acicular ferrite.
Specific embodiment
A kind of high input energy welding steel plate and preparation method thereof is made into one below in conjunction with specific embodiment and comparative example
The detailed description of step, these embodiments are served only for the purpose for comparing and explaining, the present invention is not limited in these embodiments.
The ingredient of steel plate forging stock of the present invention designs, based on the principle that
Carbon: carbon is the element for guaranteeing armor plate strength, and by the weldability of significant impact material.C content is lower than
The intensity of 0.07%, TMCP steel plate will reduce；When C content is excessively high, the M-A content of welding heat affected zone increases, sweating heat shadow
That rings area appoints toughness to reduce.Therefore, C content control is 0.07~0.10%, preferably 0.08~0.09%.
Manganese: Mn is solid-solution in the intensity that steel will be improved in steel, and Mn content should control the intensity for guaranteeing steel 0.5% or more.
When Mn content is more than 2.0%, center segregation will be generated, Large Heat Input Welding heat affected area is made to generate hardened structure, reduces welding
Heat affected area toughness.Therefore, the control of Mn content is 0.5~2.0%, preferably 1.2~1.5%.
Silicon: deoxidier when Si is usually as steel-making uses, and when silicone content is lower than 0.1%, molten steel is oxidizable.Si is also
Solution strengthening element, but the Si of volume be usually to welding performance it is unfavorable, for guarantee welding heat influence area toughness, Si content
It should control less than 0.3%.Therefore, the control of Si content is 0.1~0.3%, preferably 0.16~0.20%.
Sulphur and phosphorus: S and P is impurity element in steel, the serious toughness for damaging base material and welding heat affected zone.Therefore, sulphur, phosphorus
Content should control below 0.001% and 0.005% or less respectively.
Nitrogen: N is micro alloying element crucial in the steel, and the N of certain content can form TiN with Ti, inhibit welding
Heat affected area Austenite Grain Growth, and BN-MnS- (Ti, V) (C, N) and BN-MnS- are formed with elements such as Ti, V, B, N, Al
Al2O3Intragranular Acicular Ferrite is promoted to be formed, lower N content cannot function as described above；If the N content in steel is higher, sweating heat
Solid solution nitrogen content in the zone of influence, which increases heat affected area toughness, to be reduced.Therefore N content should be controlled 0.007%~0.009%,
It is preferred that 0.0081~0.0089%.
Titanium: Ti forms TiN in conjunction with N, inhibits the Austenite Grain Growth process of forging stock during heating, in sweating heat
Pinning austenite grain size in cyclic process, to improve the toughness of steel plate and welding heat affected zone.Furthermore TiN can be used as
V, the forming core core of the elements such as B, S, Mn forms complicated BN-MnS- (Ti, V) (C, N) particle.Ti content is lower than 0.008%,
It is not easy to play above-mentioned effect；Excessive Ti causes TiN that time reduction, temperature raising is precipitated, and makees to the pinning of austenite grain
With reduction.Therefore, the content of Ti is controlled 0.008%~0.015%, preferably 0.014~0.015%.
Dissolved aluminum: Als is the important deoxidant element of one of steelmaking process, and the prior art generally aoxidizes to generate Ti
Object, it is as few as possible without containing Als or content as much as possible, if Als content is high, Ti oxide, sweating heat will not be generated
Zone of influence ground austenite grain coarsening, toughness decline.Als of the present invention and oxygen act on forming Al2O3, and as B, N, S, Mn member
The core of element generates BN-MnS-Al2O3Particle is generated, is improved tough as the forming core core of Intragranular Acicular Ferrite with promoting ferrite
Property.When Als content is less than 0.02%, it is difficult to by Control for Oxygen Content below 0.004%；When Als content is higher, it will formed
The oxide of coarse Al is mingled with, and is gathered into cluster-shaped, and the blocking of steel-making nozzle occurs, or leads to toughness as formation of crack
Reduction.Therefore, Als content should be controlled 0.02~0.06%, preferably 0.03~0.04%.
Vanadium: the members such as V and C, N are known as extremely strong affinity, mainly exist in the form of carbide and nitride in steel, can
To improve intensity by precipitation strength, the vanadium nitrogen compound being precipitated in austenite is able to suppress Austenite Grain Growth.?
The vanadium nitrogen compound that ferrite area is precipitated can increase the forming core core of Intragranular Acicular Ferrite, and two aspects collectively promote crystal grain refinement,
Improve the welding performance of low-carbon low-alloy steel significantly.Simultaneously in Large Heat Input Welding, the carbonitride of vanadium depends on TiN
Son forms (Ti, V) (C, N) particle, as the forming core core of B, N, S, Mn element, generates BN-MnS- (Ti, V) (C, N) particle,
As the forming core core of Intragranular Acicular Ferrite, generates with promoting ferrite, refine the crystal grain of welding heat affected zone, improve sweating heat shadow
Ring low temp area toughness.When V content be lower than 0.04%, the effect of crystal grain refinement can not be played.When V content is higher than 0.1%, vanadium unit
Plain excessive, solid solution vanadium will promote the formation of bainite structure.Therefore, V content should be controlled 0.04%~0.1%, preferably 0.06
~0.1%.
Boron: B, which can be reduced, is dissolved nitrogen content in welding heat affected zone, improves the low-temperature flexibility of welding heat affected zone, TiN particle
(peak temperature >=1400 DEG C) are dissolved at melt run, and the solid solution nitrogen-atoms of generation is unfavorable to HAZ (heat affected area) toughness.
B is formed by BN and is attached to MnS- (Ti, V) (C, N), MnS-Al easily in conjunction with N2O3Forming core, formation BN-MnS- (Ti, V) (C,
) and BN-MnS-Al N2O3Particle is generated, is refined welding heat affected as the forming core core of Intragranular Acicular Ferrite with promoting ferrite
The crystal grain in area improves toughness.When B content is lower than 0.0008%, the effect of the forming core core of Intragranular Acicular Ferrite cannot be played；When
When B content is greater than 0.0015%, BN will be precipitated in crystal boundary, influence the craftsmanship of forging stock.Therefore, B content should control
0.0008%~0.0015%, preferably 0.0008~0.0010%.
Addition Nb can be improved the intensity of material, but when Nb content >=0.01%, Nb will promote ferrite side plate group
Knit, bainite, M-A etc. are unfavorable to toughness organizes the formation of, reduce Low Temperature Impact Toughness of Heat-affected Zone.As Nb content < 0.01%
When, the carbonitride of niobium vanadium will be formed after Thermal Cycle, drops (Ti, V) (C, N) as the ability of the nucleation site BN
It is low, the decline of Intragranular Acicular Ferrite forming core significant effect.
The basic principle of controlled rolling and controlled cooling technique is as follows:
Facilitate to control original austenite grains Size growth using low relation reheating temperature, first stage rolling is mainly
Austenite grain is set adequately to refine.Two-stage, which rolls main purpose, to be rolled in Unhydrated cement, passes through to be formed
A large amount of Zona transformans and dislocation, to promote ferritic forming core.The purpose of three stage rollings is deformed in two-phase section, is promoted with this
Continuous dynamic recrystallization occurs for pro-eutectoid ferrite, on the other hand one side fining ferrite grains are formed big in ferrite
The substructure of amount improves the intensity and toughness of steel plate.
The embodiment of the present invention and the chemical component of comparative example steel plate are shown in Table 1.Embodiment and comparative example steel plate are all made of 50 public affairs
The vacuum induction furnace smelting of jin is prepared into the steel plate that plate thickness is 12mm through smelting, forging and rolling, and comparative example uses two stages
Rolling, forging stock heating cycle are 1200 DEG C × 0.5h, and finishing temperature is 870 DEG C, 1100 DEG C of embodiment forging stock relation reheating temperature ×
0.5h, the parameters such as rolling mill practice are as shown in table 2.
Embodiment 1: slab is heated to 1100 DEG C, soaking time 0.5h, 1050 DEG C of first stage roughing start rolling temperature, is passed through
3 passage roughing, 950 DEG C of first stage roughing finishing temperature, 820 DEG C of second stage finish rolling start rolling temperature, through 2 passage finish rolling,
800 DEG C of two-stage finish rolling finishing temperature, through 2 passes, steel plate thickness is rolled for 780 DEG C of phase III two-phase section start rolling temperature
It is made as 12mm, 760 DEG C of finishing temperature, is then air-cooled to room temperature.
Embodiment 2: slab is heated to 1100 DEG C, soaking time 0.5h, 1058 DEG C of first stage roughing start rolling temperature, is passed through
3 passage roughing, 965 DEG C of first stage roughing finishing temperature, 816 DEG C of second stage finish rolling start rolling temperature, through 2 passage finish rolling,
796 DEG C of two-stage finish rolling finishing temperature, through 2 passes, steel plate thickness is rolled for 776 DEG C of phase III two-phase section start rolling temperature
It is made as 12mm, 757 DEG C of finishing temperature, is then air-cooled to room temperature.
Embodiment 3: slab is heated to 1100 DEG C, soaking time 0.5h, 1065 DEG C of first stage roughing start rolling temperature, is passed through
3 passage roughing, 960 DEG C of first stage roughing finishing temperature, 800 DEG C of second stage finish rolling start rolling temperature, through 2 passage finish rolling,
795 DEG C of two-stage finish rolling finishing temperature, through 2 passes, steel plate thickness is rolled for 773 DEG C of phase III two-phase section start rolling temperature
It is made as 12mm, 754 DEG C of finishing temperature, is then air-cooled to room temperature.
Embodiment 4: slab is heated to 1100 DEG C, soaking time 0.5h, 1070 DEG C of first stage roughing start rolling temperature, is passed through
3 passage roughing, 970 DEG C of first stage roughing finishing temperature, 810 DEG C of second stage finish rolling start rolling temperature, through 2 passage finish rolling,
790 DEG C of two-stage finish rolling finishing temperature, through 2 passes, steel plate thickness is rolled for 770 DEG C of phase III two-phase section start rolling temperature
It is made as 12mm, 750 DEG C of finishing temperature, is then air-cooled to room temperature.
The slab first stage adds up deflection 40~50%, and second stage adds up deflection 30~40%, and the phase III is tired
Count deflection 20~30%.
Facilitate to inhibit original austenite grains Size growth using low relation reheating temperature；First stage rolling is mainly
Austenite grain is set adequately to refine；Second stage, which rolls main purpose, to be rolled in Unhydrated cement, and shape is passed through
At a large amount of Zona transformans and dislocation, to promote ferritic forming core；The purpose of phase III rolling is deformed in two-phase section, with this
Pro-eutectoid ferrite is promoted to occur continuous dynamic recrystallization, one side fining ferrite grains, the on the other hand shape in ferrite
Intensity is improved at a large amount of substructure.
The chemical component Wt.% of 1 steel of table
2 steel plate preparation process of table
Embodiment steel plate and comparative example steel plate are sampled, according to GB/T 13239-2006 standard, used
MTSNEW810 cupping machine is stretched with the collet rate travel that 3mm/min is constant, tests tensile performance in wale-wise, sampling
Position is at steel plate 1/2, and test result takes the average value of two samples.According to GB/T 229-2007 standard, using NCS series
500J instrumentation Charpy impact machine tester, v-notch ballistic work when testing -60 DEG C, sample position are coupon results at 1/2
For the average value of 3 samples.
Mechanical property of steel plate is shown in Table 3, and in above-described embodiment, at room temperature, the tensile strength of high input energy welding steel plate is
490~520MPa, yield strength are 400~420MPa, and elongation percentage is 32%~36%, and v-notch ballistic work at -60 DEG C is
200~240J.
The base material metallographic structure of comparative example and embodiment 1 is as depicted in figs. 1 and 2, and steel plate ferrite crystal grain average-size is shown in
Table 4, the average-size of embodiment ferrite crystal grain is 6.5~6.8 μm, less than 7 μm, hence it is evident that flat lower than comparative example ferrite crystal grain
16.7 μm of equal size.Ferrite Refinement can effectively improve the intensity and toughness of base material.
The elongation percentage of embodiment is suitable with comparative example, and tensile strength, yield strength and -60 DEG C of v-notch ballistic work are equal
It is significantly higher than comparative example, -60 DEG C of v-notch ballistic work is 4~5 times of comparative example.
3 mechanical property of steel plate of table
4 steel plate ferrite crystal grain average-size of table
Above-mentioned steel plate is carried out to the weld thermal simulation test of 100kJ/cm using the method for weld thermal simulation.Then basis
GB/T 229-2007 standard, using NCS series 500J instrumentation Charpy impact machine tester, when testing -50 DEG C of welding point
The v-notch ballistic work of welding heat affected zone.The results are shown in Table 5 for it, applies the v-notch of -50 DEG C of the welding heat affected zone of example
Ballistic work is 210~230J, is 5~6 times of comparative example steel plate welding heat affected zone v-notch ballistic work, with excellent low
Warm toughness meets polar region environment requirement.Fig. 3 is 0 DEG C~-50 DEG C welding heat affected zone v-notch of embodiment 1 and comparative example
Ballistic work, it can be seen that the welding heat affected zone ductile-brittle transition temperature of 1 steel plate of embodiment is at -50 DEG C or less.
Table 6 is that quantitative statistics result is organized in embodiment and comparative example welding heat affected zone.Embodiment is with area percentage
Polygonal ferrite content is 70~85%, and acicular ferrite content is 4~8%, side spot ferrite 1~2%, bainite 5
~7%, pearlite 7~10%；Embodiment bainite average-size is 24~26 μm, and 33.9 μm compared with comparative example reduce 30%
Left and right, steel plate of the present invention refine bainite；Fig. 4 is the welding heat affected zone metallographic structure of embodiment 1, Fig. 5 comparison
Example welding heat affected zone metallographic structure, there are the bainite of more coarse grains in comparative example, polygonal ferrite size is bright
It shows and is less than bainite size, content >=70% of steel plate welding heat affected zone of the present invention polygonal ferrite, bainite content≤
10%, polygonal ferrite content is improved, bainite content is reduced, has further refined crystal grain, effectively increase steel plate
The low-temperature flexibility of welding heat affected zone.
The low-temperature flexibility of 5 welding heat affected zone of table
Organize quantitative statistics in 6 welding heat affected zone of table
Fig. 6-Figure 13 is transgranular polygonal ferrite in 1 welding heat affected zone of embodiment in BN-MnS- (Ti, V) (C, N) grain
The SEM observation of forming core is as a result, Figure 14-Figure 21 is 1 welding heat affected zone intragranular acicular ferrite of embodiment in BN-MnS- on son
Al2O3The SEM of forming core observes result on particle.Figure 22 is BN-MnS-Al2O3The structural schematic diagram of particle.It can from figure
Out, there is BN-MnS- (Ti, V) (C, N) and BN-MnS-Al having a size of 0.3 μm in welding heat affected zone2O3Particle, and conduct
Intragranular Acicular Ferrite forming core core, promote ferritic formation, transgranular polygonal ferrite and acicular ferrite BN-MnS- (Ti,
V) (C, N) and BN-MnS-Al2O3Forming core on particle, hence it is evident that improve the tissue and low-temperature flexibility of welding heat affected zone.
The foregoing is only a preferred embodiment of the present invention, but scope of protection of the present invention is not limited thereto,
In the technical scope disclosed by the present invention, any changes or substitutions that can be easily thought of by anyone skilled in the art,
It should be covered by the protection scope of the present invention.
Claims (10)
1. a kind of high input energy welding steel plate, which is characterized in that the ingredient of the steel plate is by percentage to the quality are as follows: C:0.07
~0.10%, Si:0.10~0.30%, Mn:0.5-2.0%, S :≤0.001%, P :≤0.005, Als:0.02~0.06%,
Ti:0.008~0.015%, B:0.0008~0.0015%, N:0.007~0.009%, V:0.04~0.1%, remaining is Fe
With inevitable impurity element；Be dissolved nitrogen content=N-0.28Ti-1.27B-0.03V, be dissolved nitrogen content less than 0.003%,
Wherein N, Ti, B, V are the mass percentage content of each element.
2. high input energy welding steel plate according to claim 1, which is characterized in that the ingredient of the steel plate is with quality hundred
Ratio is divided to be calculated as: C:0.08~0.09%, Si:0.16~0.20%, Mn:1.2~1.5%, S :≤0.001%, P :≤0.005,
Als:0.03~0.04%, Ti:0.014~0.015%, B:0.0008~0.0010%, N:0.0081~0.0089%, V:
0.06~0.1%, remaining is Fe and inevitable impurity element；It is dissolved nitrogen content=N-0.28Ti-1.27B-0.03V, Gu
Molten nitrogen content is less than 0.003%, and wherein N, Ti, B, V are the mass percentage content of each element.
3. high input energy welding steel plate according to claim 1 or 2, which is characterized in that the tissue signature of steel plate is band
There are ferrite, the isometric ferrite and pearlite of phase transformation of sub boundary.
4. high input energy welding steel plate according to claim 1 or 2, which is characterized in that by forging stock be heated to 1100 DEG C,
0.5h is kept the temperature, using three stage rollings, first stage roughing, second stage finish rolling, the rolling of phase III two-phase section.
5. high input energy welding steel plate according to claim 4, which is characterized in that the ferrite crystal grain of steel plate is averaged ruler
It is very little less than 7 μm, steel plate tensile strength be 490~520MPa, yield strength be 400~420MPa, elongation percentage be 32%~
36%, v-notch ballistic work at -60 DEG C is 200~240J.
6. high input energy welding steel plate according to claim 4, which is characterized in that steel plate is defeated in 100kJ/cm sweating heat
There is BN-MnS- (Ti, V) (C, N) and BN-MnS-Al having a size of 0.2~0.4 μm in welding heat affected zone under the conditions of entering2O3
Particle, and as Intragranular Acicular Ferrite forming core core.
7. high input energy welding steel plate according to claim 6, which is characterized in that with face in the welding heat affected zone
Product percentages bainite content is 5~7%, and polygonal ferrite content is 70~85%.
8. high input energy welding steel plate according to claim 7, which is characterized in that -50 DEG C of the welding heat affected zone
V-notch ballistic work be 210~230J, -50 DEG C of ductile-brittle transition temperature or less of welding heat affected zone.
9. the preparation method of high input energy welding steel plate according to claim 1-8, which is characterized in that will forge
Base is heated to 1100 DEG C of heat preservation 0.5h, using three stage rollings, first stage roughing, second stage finish rolling, phase III two-phase
Area's rolling.
10. the preparation method of -9 high input energy welding steel plates according to claim 1, which is characterized in that the first stage is thick
Roll 1050~1070 DEG C of start rolling temperature, 950~970 DEG C of first stage roughing finishing temperature, second stage finish rolling start rolling temperature 810
~820,790~800 DEG C of second stage finish rolling finishing temperature, 770~780 DEG C of phase III two-phase section start rolling temperature, finish to gauge temperature
750~760 DEG C of degree；First stage adds up deflection 40~50%, and second stage adds up deflection 30~40%, and the phase III is tired
Count deflection 20~30%.
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| CN114150231A (en) * | 2021-11-16 | 2022-03-08 | 中联先进钢铁材料技术有限责任公司 | Steel plate with high fracture toughness and 420MPa grade for marine platform and preparation method |
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| CN102839320A (en) * | 2011-06-24 | 2012-12-26 | 宝山钢铁股份有限公司 | High-heat input steel plate for welding and manufacturing method thereof |
| CN105296855A (en) * | 2015-11-25 | 2016-02-03 | 钢铁研究总院 | Steel plate capable of performing high heat input welding for ocean platform and preparation method |
| CN106755868A (en) * | 2016-12-13 | 2017-05-31 | 钢铁研究总院 | A kind of low cost can Large Heat Input Welding high-strength and high ductility steel plate manufacture method |
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| CN102839320A (en) * | 2011-06-24 | 2012-12-26 | 宝山钢铁股份有限公司 | High-heat input steel plate for welding and manufacturing method thereof |
| CN105296855A (en) * | 2015-11-25 | 2016-02-03 | 钢铁研究总院 | Steel plate capable of performing high heat input welding for ocean platform and preparation method |
| CN106755868A (en) * | 2016-12-13 | 2017-05-31 | 钢铁研究总院 | A kind of low cost can Large Heat Input Welding high-strength and high ductility steel plate manufacture method |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114150231A (en) * | 2021-11-16 | 2022-03-08 | 中联先进钢铁材料技术有限责任公司 | Steel plate with high fracture toughness and 420MPa grade for marine platform and preparation method |
| CN114150231B (en) * | 2021-11-16 | 2022-09-16 | 中联先进钢铁材料技术有限责任公司 | Steel plate with high fracture toughness and 420MPa grade for marine platform and preparation method |
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