CN101045976A - Thick steel plate for low temperature use and capable of being welded in superhigh energy and its production process - Google Patents
Thick steel plate for low temperature use and capable of being welded in superhigh energy and its production process Download PDFInfo
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Abstract
The thick steel plate for low temperature use and capable of being welded in superhigh energy has the material comprising C 0.030-0.050 wt%, Si not more than 0.2 wt%, Mn 1.50-1.80 wt%, P not more than 0.01 wt%, S not more than 0.002 wt%, Nb 0.010-0.020 wt%, Als 0.040-0.060 wt%, Ti 0.008-0.012 wt%, N not more than 0.0035 wt%, Ca 0.001-0.005 wt%, B 0.001-0.003 wt%, and Fe and inevitable impurity for the rest, with Pcm not more than 0.18 wt%. The present invention has low alloy steel as basis, properly raised Als content, C/Mn ratio of 0.020-0.050, Ti-B microalloying, Ca or REM treatment, Ti/N ratio of 3.0-3.5, optimized TMCP treatment, microscopic structure comprising small amount of ferrite and diffused bainite crystal of average crystal grain size below 15 micron, excellent mechanical performance and welding performance, and is especially suitable for being used as high strength ship deck, low temperature pressure container, offshore platform, etc.
Description
Technical field
But the present invention relates to the Plate Steel and the manufacture method thereof that in the high Als-Ti-B alloy system of the high Mn-of a kind of low C-, obtain yield strength 〉=415MPa ultra-large linear energy input welding.
Background technology
As everyone knows, low-carbon (LC) (high strength) low alloy steel is one of most important structural timber, is widely used among petroleum natural gas pipeline, ocean platform, shipbuilding, bridge, pressurized vessel, building structure, automotive industry, transportation by railroad and the machinofacture.Low-carbon (LC) (high strength) low alloy steel performance depends on the process system of its chemical ingredients, manufacturing processed, and wherein intensity, toughness and weldability are the most important performances of low-carbon (LC) (high strength) low alloy steel, and its final decision is in the microstructure state of finished steel.Along with science and technology constantly advances, people propose higher requirement to the obdurability and the weldability of steel, promptly improve performance when steel plate is being kept lower manufacturing cost significantly, save cost with the consumption that reduces steel, alleviate the own wt of steel construction, improve the security of structure.
Started development ferrous materials research of new generation climax at present in the world wide, requirement is not increasing valuable alloying element, as Ni, Cr, Mo, Cu equal size, obtain better tissue coupling by alloy combination design optimization and innovation TMCP Technology, thereby obtain higher obdurability and better weldability.
Have now when making yield strength 〉=415MPa ,-60 ℃ the Plate Steel of low-temperature impact toughness 〉=34J, generally in steel, add a certain amount of Ni or Cu+Ni element (content generally equal 〉=0.30%) [The Firth (1986) international Symposium and Exhibit on OffshoreMechanics and Arctic Engineering, 1986, Tokyo, Japan, 354; " DEVELOPMENTS IN MATERIALS FOR ARCTIC OFFSHORESTRUCTURES "; " Structural Steel Plates for Arctic Use Produced byMultipurpose Accelerated Cooling System " (Japanese), Kawasaki Steel skill newspaper, 1985, No.1 68～72; " Application of Accelerated Cooling For Producing 360MPaYield Strength Steel plates of up to 150mm in Thickness with Low CarbonEquivalent ", Accelerated Cooling Rolled Steel, 1986,209～219; " HighStrength Steel Plates For Ice-Breaking Vessels Produced by Thermo-Mechanical Control Process ", Accelerated Cooling Rolled Steel, 1986,249～260; " 420MPa Yield Strength Steel Plate with Superior Fracture Toughnessfor Arctic Offshore Structures ", Kawasaki steel technical report, 1999, No.40,56; " 420MPa and 500MPa Yield Strength Steel Plate with High HAZtoughness Produced by TMCP for Offshore Structure ", Kawasaki steeltechnical report, 1993, No.29,54; " Toughness Improvement in BainiteStructure by Thermo-Mechanical Control Process " (Japanese) Sumitomo Metal Industries, Vol.50, No.1 (1998), 26; " the offshore platform structure steel plate that ice Haiti district uses " (Japanese), steel research, 1984, No. 314,19～43], have excellent low-temperature flexibility to guarantee the mother metal steel plate, when the heat input of employing＜100KJ/cm welded, the toughness of heat affected zone HAZ also can reach-60 ℃ of Akv 〉=34J; But the employing ultra-large linear energy input (〉=when 200KJ/cm) welding, the low-temperature flexibility of welded heat affecting zone (HAZ) is general difficult to reach, and serious deterioration takes place in heat affected zone (HAZ) low-temperature flexibility.A large amount of patent documentations just illustrate the low-temperature flexibility that how to realize the mother metal steel plate, for how under welding conditions, obtain the less of good heat affected zone (HAZ) low-temperature flexibility explanation, how to guarantee that the low-temperature flexibility of heat affected zone (HAZ) is few when especially adopting the ultra-large linear energy input welding, and in order to guarantee the low-temperature flexibility of steel plate, generally all add a certain amount of Ni or Cu+Ni element in the steel, steel plate ultra-large linear energy input welded heat affecting zone (HAZ) low-temperature flexibility also seldom can reach-60 ℃ of [clear 63-93845, clear 63-79921, clear 60-258410, Te Pingkai 4-285119, Te Pingkai 4-308035, flat 3-264614, flat 2-250917, flat 4-143246, US Patent4855106, US Patent5183198, US Patent4137104].The company of Japanese Nippon Steel that has only that improves ultra-large linear energy input welding steel heat affected zone (HAZ) low-temperature flexibility at present adopts oxide compound metallurgical technology [USPatent 4629505, WO 01/59167A1].
But, the at present above-mentioned Plate Steel C/Mn that uses in the world is generally on the low side, generally more than 0.05, and do not adopt special compound Al, Ti, B, N microalloying to handle, show the quantitative relationship that does not provide between Al, Ti, B, the N, cause low-temperature flexibility (below the 50 ℃) instability of Plate Steel, especially the low-temperature flexibility of welding steel heat affected zone (HAZ) is low, cause slab can not bear the ultra-large linear energy input welding, make the efficient and the scope of application thereby influence steel construction.
Summary of the invention
Purpose of the present invention is exactly will be by the unitized design of simple alloying element, do not add noble element such as Ni, Cr, Mo, Cu etc., optimize the TMCP manufacturing process, when obtaining excellent mother metal steel plate low-temperature flexibility, the low-temperature flexibility of HAZ is excellent too during the ultra-large linear energy input welding.This not only can reduce the steel plate manufacturing cost, shorten the steel plate production cycle, steel plate organization of production difficulty [Ni, Cu, the higher steel plate of Mo constituent content have also been reduced, surface quality of continuously cast slab is relatively poor, generally all needing rolls off the production line carries out surface-conditioning, sometimes also need to carry out surface colour penetration inspection (be so-called PT check) and the cutting of band temperature etc.], also eliminated the difficulty of the steel scrap recovery that contains Cu, Ni in a large number; The more important thing is and greatly improved site welding efficient, saved the cost that user's member is made, shortened the time that user's member is made, for the user has created huge value, thereby this type of steel plate is not only the product of high added value, green environmental protection, the more important thing is to have formed senior Plate Steel core manufacturing technology, promoted the brand image and the core competitiveness of Baosteel with Baosteel characteristic.
Technical scheme of the present invention is, but the Plate Steel of ultra-large linear energy input welding, and its composition weight percent is:
C：0.030％～0.050％
Si：≤0.20％
Mn：1.50％～1.80％
P：≤0.010％
S：≤0.002％
Nb：0.010％～0.020％
Als：0.040％～0.060％
Ti：0.008％～0.012％
N：≤0.0035％
Ca：0.001％～0.005％
B:0.001%～0.003%, preferred 0.0015%～0.0025%;
Simultaneously: 0.02≤C/M≤0.06 is lower than-60 ℃ to guarantee fracture transition temperature; Ti/N between 3.0～3.5,
Relation between B, Ti, the N: 10ppm+0.714 (N-0.292Ti)≤B≤20ppm+0.714 (N-0.292Ti) guarantees to exist in the steel excessive B atom;
Relation between Als, Ti and the N: Als 〉=30 * (N-0.292Ti) are eaten up by Als to guarantee solid solution N, guarantee that B is present in the steel with solid solution B atomic form;
All the other are iron and inevitably being mingled with,
Wherein, welding cold cracking Sensitivity Index Pcm≤0.18%, Pcm=wt%C+wt%Si/30+ (wt%Mn+wt%Cu+wt%+Cr)/20+wt%Ni/60+wt%Mo/15+wt%V/10+5wt%B wherein is to guarantee heat affected zone (HAZ) low-temperature flexibility of ultra-large linear energy input welding steel.
But the manufacture method of ultra-large linear energy input welding Plate Steel of the present invention, it comprises the steps:
A. casting, tundish molten steel casting temperature≤1540 ℃;
B. slab heating temperature is controlled between 1050 ℃～1150 ℃;
C. in the perfect recrystallization temperature range, big rolling pass draft continuous rolling guarantees that deformable metal takes place dynamically/static recrystallize, refine austenite crystal grain, rolling pass draft 〉=12%, recrystallization zone (〉=980 ℃) total draft 〉=55%; Carry out controlled rolling in the non-recrystallization district, percentage pass reduction 〉=10%, non-recrystallization district (＜900 ℃) total draft 〉=50%;
D. should control shortly as far as possible from rolling the end to the biography time of putting beginning to quicken to cool off, be controlled in 20 seconds, and when particularly importantly quickening the cooling beginning, steel billet temperature must be at Ar
3More than the point, Ar
3(℃)=910-310[%C]-80[%Mn]-20[%Cu]-15[%Cr]-55[%Ni]-80[%Mo]-0.35 (t-8), wherein t is thickness of slab (mm);
E. carrying out direct quenching with 〉=10.0 ℃/s speed of cooling is cooled to quench and stops temperature (QST-Quenching Stop Temperature), quenching stops temperature (QST) and is controlled at 200～450 ℃, make steel plate that cooling bainitic transformation continuously fully take place in＞200 ℃ of scopes, suppress the proeutectoid ferrite phase transformation, to obtain high tensile steel plate under the condition that is implemented in low-carbon-equivalent;
F. then below the slow cooling to 100 ℃, average slow cooling speed≤10 ℃/hr, natural air cooling is to room temperature subsequently, and the slow cooling time must not be lower than 24 hours.
Further, casting technique adopts continuous casting process, gently depresses technology with induction stirring or continuously cast bloom, and light draught is controlled between 3%～10%.
It is 380 ℃～430 ℃ that step e quenching stops temperature range.
The physical metallurgy analysis of steel plate composition System Design:
Adopt the high Mn-Nb series low-alloy of low-carbon (LC) C-steel as the basis, content, the C/Mn ratio that suitably improves Als is controlled at 0.020～0.050, the Ti-B microalloying, Ca handles and control Ti/N metallurgical technology means such as between 3.0～3.5, optimize TMCP (Thermo-mechanical control process, the mechanical control process of heat) technology, the microstructure that makes the finished product steel plate is the bainite colony that a spot of ferrite (20%～30%)+disperse distributes, and average grain size is below 15 μ m.Composition design metallurgy is analyzed as follows in detail:
C is very big to intensity, low-temperature flexibility and the weldability influence of steel, from low-temperature flexibility and the weldability of improving steel, wishes that C content is controlled lowlyer in the steel; But microstructures Control angle from the intensity of steel and manufacturing process, C content should not be low excessively, and low excessively C content (＜0.030%) not only causes Ac
1, Ac
3, Ar
1, Ar
3The point temperature is higher, and the austenite grain boundary mobility is too high, brings very big difficulty to grain refining, forms mixed grain structure easily, cause the low and serious deterioration of ultra-large linear energy input welded heat affecting zone low-temperature flexibility of steel low-temperature flexibility, so C content lower control limit should not be lower than 0.030% in the steel.When C content improves, though help the steel plate microstructure thinning, damage the weldability of steel plate, especially under the ultra-large linear energy input welding conditions; Because the speed of cooling in serious alligatoring of heat affected zone (HAZ) crystal grain and the Thermal Cycle process of cooling very, (HAZ) easily forms thick ferrite side plate bar (FSP) in the heat affected zone, the family name organizes (WF), upper bainite abnormal structures such as (Bu), and M-A island quantity increases, size increases, the toughness of grievous injury heat affected zone (HAZ), so C content should not be higher than 0.05%.
Mn as most important alloying element in steel except that the intensity that improves steel plate, also have the austenite of expansion phase region, reduce Ar
3Point temperature, refinement ferrite crystal grain and improve the steel plate low-temperature flexibility effect, promote bainite to form and the effect that improves armor plate strength; Therefore under the condition of not adding other alloying element (Cu, Ni, Cr, Mo, V etc.), adopt TMCP technology to make the steel plate of yield strength 〉=415MPa, internal control Mn content can not be lower than 1.50% in the steel.Segregation takes place in Mn easily in the solid process of molten steel, especially too high Mn content (when Mn content＞1.80%), not only can cause the continuous casting operational difficulty, and easily and element generation conjugation segregation phenomenas such as C, P, S, the segregation that increases the weight of the continuously cast bloom center is with loose, and serious continuously cast bloom center segregation easily forms abnormal structure in follow-up controlled rolling and welding process; Simultaneously, the Mn too high levels also can form thick MnS particle, roll to extension on this thick MnS particle edge in course of hot rolling, the impelling strength of severe exacerbation mother metal steel plate (especially horizontal), welded heat affecting zone (HAZ) [especially under the ultra-large linear energy input welding conditions] causes Z to low, the anti-lamellar tearing poor performance of performance; In addition, cross hardenability that high Mn content also can improve steel, improve welding cold crack sensitivity coefficient (Pcm) in the steel, the weldprocedure that influence steel (when less heat input welds, easily forms crisp sclerous tissues such as martensite; When bigger heat input welds, easily form thick upper bainite).Therefore, the upper limit of Mn content can not surpass 1.80% in the steel.
Si promotes deoxidation of molten steel and can improve armor plate strength, but adopt the molten steel of Al deoxidation, the desoxydatoin of Si is little, though Si can improve the intensity of steel plate, but the low-temperature flexibility and the weldability of Si grievous injury steel plate, especially under the ultra-large linear energy input welding conditions, Si not only promotes the M-A island to form, and the M-A island size that forms is big, skewness, the toughness of grievous injury welded heat affecting zone (HAZ), therefore the Si content in the steel should be controlled lowly as far as possible, considers the economy and the operability of steelmaking process, and Si content is controlled at below 0.20%.
P is as harmful mechanical property that is mingled with steel in the steel, especially low-temperature impact toughness and weldability have huge detrimental effect, it is low more good more to require in theory, but consider steel-making operability and steel-making cost, but for requiring large-line energy welding ,-60 ℃ of flexible Plate Steels, P content need be controlled at≤and 0.010%.
S has very big detrimental effect as harmful low-temperature flexibility that is mingled with steel in the steel, the more important thing is that S combines with Mn in steel, form the MnS inclusion, in course of hot rolling, the plasticity-of MnS makes MnS along rolling to extension, form along rolling to MnS inclusion band, the transverse impact toughness of grievous injury steel plate, Z are to performance and weldability, and S produces hot short principal element in the course of hot rolling simultaneously.It is low more good more to require in theory, but considers steel-making operability, steel-making cost and the smooth and easy principle of logistics, but for the Plate Steel that requires-60 ℃ of toughness ultra-large linear energy inputs welding, S content need be controlled at≤0.002%.
Nb: the Nb element purpose of adding trace in the steel is to carry out the non-recrystallization controlled rolling, when the Nb addition is lower than 0.010%, can not bring into play about effective controlled rolling; When the Nb addition surpasses 0.020%, bringing out upper bainite (Bu) under the ultra-large linear energy input welding conditions forms, the low-temperature flexibility of grievous injury ultra-large linear energy input welded heat affecting zone (HAZ), therefore Nb content is controlled between 0.010%～0.020%, when obtaining best controlled rolling effect, do not damage the toughness of ultra-large linear energy input welded H AZ again.
The span of control of N is corresponding with the span of control of Ti, and for the ultra-large linear energy input welding steel, Ti/N is best between 3.0～3.5.N content is low excessively, and generation TiN number of particles is few, size is big, can not play the effect of the weldability of improving steel, and is harmful to weldability on the contrary; But during the N too high levels, free [N] increases in the steel, and especially heat affected zone (HAZ) free [N] content sharply increases under the ultra-large linear energy input welding conditions, grievous injury HAZ low-temperature flexibility, the weldability of deterioration steel.Therefore N content is controlled at below 0.0035%.
The Ti purpose that adds trace in the steel is to combine with N in the steel, generates the very high TiN particle of stability, and inhibition welded H AZ district austenite crystal is grown up and changed the second-order phase transition product, improves the weldability of steel and the low-temperature flexibility of HAZ.The Ti content that adds in the steel will contain flux matched with the N in the steel, and the principle of coupling is that TiN can not separate out in liquid molten steel and must separate out in solid phase; Therefore the separating out temperature and must guarantee to be lower than 1400 ℃ of TiN is according to log[Ti] [N]=-16192/T+4.72 can determine the add-on of Ti.When adding Ti content very few (＜0.008%), form TiN number of particles deficiency, the austenite crystal that is not enough to suppress HAZ is grown up and is changed the second-order phase transition product and improve the low-temperature flexibility of HAZ; When adding Ti content too much (＞0.012%), TiN separates out temperature and surpasses 1400 ℃, and in the solidification of molten steel process, possible liquation goes out large size TiN particle, this large size TiN particle not only can not suppress the austenite crystal of HAZ grows up, and becomes the starting point of crack initiation on the contrary; Therefore the optimum controling range of Ti content is 0.008%～0.012%.
B is strong hardenability element, the solid solution B atom of several ppm gathers partially at austenite grain boundary, the strongly inhibited proeutectoid ferrite forms, and promotes the formation of low temperature phase change tissues such as bainite, thus solid solution B the intensity of raising steel plate is most important for obtaining low temperature phase change tissue such as bainite.B can also improve the low-temperature flexibility of the heat affected zone HAZ of large-line energy welding: I) Ti and B all are the strong forming elements of nitride, but in the Thermal Cycle process, TiN and BN effect fundamental difference, TiN (≤1300 ℃) under higher relatively temperature has higher stability, can effectively suppress the HAZ grain growth far away apart from welded bonds, but in the time of near welded bonds (FL), the Thermal Cycle peak temperature becomes very high (＞1350 ℃), the TiN particle is partly dissolved, and can not effectively suppress the HAZ grain growth.Though at high temperature the BN particle does not have the particle-stabilised and whole solid solutions of TiN in steel, but because the high diffusibility of B in steel, BN separates out fast again in the Thermal Cycle process of cooling that (diffustivity of Ti, Als is very low, TiN, AlN can't separate out in the Thermal Cycle process of cooling again, it is very slow to be that TiN, AlN separate out kinetics speed), the BN particle is because the singularity of crystalline structure, has the low energy orientation relationship with ferrite, the BN particle can become the active position of ferrite forming core, promote ferrite crystal grain forming core in austenite crystal, refinement HAZ tissue; For making the BN particle promote to form tiny ferrite crystal grain, at first to promote the formation of BN, and reach certain quantity, (O, S) inclusion promote separating out of BN to form superfine REM to adopt the REM processing, be be everlasting REM (O, S) heterogeneous nucleation on the inclusion of BN.II) uses B and Ti alloying together, make the Fe that forms small and dispersed in the steel
23(CB)
6+ TiN+MnS composite particles and since the matrix around this composite particles mutually in, form the microcell of poor C, poor Mn, improve ferrite transformation temperature (Ac
3), increase ferrite forming core motivating force (Ac
3-Ar
3), promoting the ferrite crystal grain forming core, tiny acicular ferrite is at Fe
23(CB)
6Forming core on the+TiN+MnS composite particles, refinement HAZ tissue improves the HAZ low-temperature flexibility; Simultaneously, gather several ppm B freely on austenite grain boundary partially, improve the hardenability of steel, suppress the thick ferrite of crystal boundary and form, also promote ferrite forming core in the austenite crystal.To achieve these goals, in the steel B content between 10ppm～30ppm.
Als in the steel is the freedom [N] in the steel fixedly, reduces welded heat affecting zone (HAZ) free [N], improves the low-temperature flexibility effect of HAZ; The more important thing is that Als can combine with free N, prevent that B from combining formation BN with N, lose the hardenability effect of B, but the avidity of B and N is much larger than the avidity of Als and N, therefore Als must be excessive in a large number, and promptly Als 〉=30 * (N-0.292Ti) could stop B to combine with N, B is existed with solid solution atom B in steel, so the Als lower limit is controlled at 0.040%; Not only can cause the casting difficulty but add excessive Als in the steel, and can in steel, form the needle-like Al of a large amount of disperses
2O
3Inclusion, the low-temperature flexibility and the weldability of infringement steel, so the Als upper limit is controlled at 0.060%.
Steel is carried out Ca to be handled, on the one hand can further pure molten steel, on the other hand sulfide in the steel is carried out denaturing treatment, make it to become non deformable, stablize tiny spherical sulfide, suppress the red brittleness of S, the low-temperature flexibility that improves steel and Z to performance, improve steel plate flexible anisotropy.What of Ca add-on are depended on the height of S content in the steel, and the Ca add-on is low excessively, and treatment effect is little; The Ca add-on is too high, and (O, S) oversize, fragility also increases, and can become the fracture crack starting point, reduces the low-temperature flexibility of steel, also reduces purity of steel simultaneously, pollutes molten steel to form Ca.General control Ca content is pressed ESSP=(wt%Ca) [1-124 (wt%O)]/1.25 (wt%S), and wherein ESSP is a sulfide inclusion shape control index, be advisable between the span 0.5～5, so the OK range of Ca content is 0.001%～0.005%.
Casting technique of the present invention recommends to adopt continuous casting process, continuous casting process emphasis control pouring temperature, and tundish molten steel casting temperature≤1540 ℃, the low temperature teeming practice is better, with the original as-cast structure of refinement.For the center Mn segregation of control continuously cast bloom, adopt induction stirring or continuously cast bloom gently to depress technology, light draught is controlled between 3%～10%.
Tiny for guaranteeing the initial austenite uniform crystal particles, when must adopt slab low-temperature heat technology, also to guarantee the complete solid solution of micro alloying element Nb.According to formula T
1(℃)=5833/{1.63-log[%Nb * and (%C+12 * %N/14)] }-273.15, slab heating temperature is controlled between 1050 ℃～1150 ℃, guarantees that original slab autstenitic grain size is even and comparatively tiny.
In the perfect recrystallization temperature range, big rolling pass draft carries out quick continuous rolling, guarantees that refine austenite crystal grain takes place dynamically/static recrystallize deformable metal, rolling pass draft 〉=12% for this reason, recrystallization zone (〉=980 ℃) total draft 〉=55%; Carry out controlled rolling in the non-recrystallization district, percentage pass reduction 〉=10%, non-recrystallization district (＜900 ℃) total draft 〉=50%.
Should control shortly as far as possible from rolling the end to the biography time of putting beginning to quicken to cool off, strive being controlled in 20 seconds, and when particularly importantly quickening the cooling beginning, steel billet temperature must be at Ar
3More than the point, Ar
3(℃)=910-310[%C]-80[%Mn]-20[%Cu]-15[%Cr]-55[%Ni]-80[%Mo]-0.35 (t-8), wherein t is thickness of slab (mm).
Carry out direct quenching cooling (direct quenching) with 〉=10.0 ℃/s speed of cooling and stop temperature (QST-Quenching Stop Temperature) to quenching, quenching stops temperature (QST) and is controlled at Bs-200 ℃ below the temperature, make steel plate that cooling bainitic transformation continuously fully take place in＞200 ℃ of scopes, suppress the proeutectoid ferrite phase transformation, to obtain high tensile steel plate under the condition that is implemented in low-carbon-equivalent, wherein Bs (℃)=830-270[%C]-90[%Mn]-37[%Ni]-70[%Cr]-83[%Mo], it is between 380 ℃～430 ℃ that preferred quenching stops temperature range, then below the slow cooling to 100 ℃, average slow cooling speed≤10 ℃/hr., natural air cooling is to room temperature subsequently, and the slow cooling time must not be lower than 24 hours.
The present invention adopts the low high Mn-Nb series low-alloy of C-steel as the basis, suitably improve the content of Als, the C/Mn ratio is controlled at 0.020～0.050, the Ti-B microalloying, Ca or REM handle, control Ti/N waits the metallurgical technology means between 3.0～3.5, optimize TMCP (Thermo-mechanicalcontrol process, the mechanical control process of heat) technology, the microstructure that makes the finished product steel plate is the bainite colony that a spot of ferrite (20%～30%)+disperse distributes, average grain size is below 15 μ m, obtain the mechanical property of even and excellent and good weldability, be specially adapted to high strength steel plate for ship building, low-temperature pressure container, ocean platform, high-strength building structure and bridge are with steel etc.
Beneficial effect of the present invention
The present invention removes the alloying of noble element such as Ni, Cr, Mo, Cu etc., especially removes the alloying of Ni element, and optimizes TMCP technology, in conjunction with low C, high Mn, and the mother metal steel plate low-temperature flexibility of acquisition excellence; Simultaneously, by determining the quantitative relationship between Al, Ti, B, the N, adopt special microalloying to handle (Al, Ti, B), the B in the steel exists with the solid solution form, and the intensity of the normal steel plate of same carbon is improved more than the 50MPa; Make the low-temperature flexibility of Plate Steel HAZ when ultra-large linear energy input welds excellent too.This not only can reduce manufacturing cost, shorten the production cycle, organization of production difficulty [Ni, Cu, the higher steel plate of Mo constituent content have also been reduced, surface quality of continuously cast slab is relatively poor, generally all needing rolls off the production line carries out surface-conditioning, sometimes also need to carry out surface colour penetration inspection (being that so-called PT checks) and the cutting of band temperature etc.], also eliminate the difficulty of the steel scrap recovery that contains Cu, Ni in a large number simultaneously, realized the environmental protection of manufacturing processed.
Description of drawings
Fig. 1 is the microstructure of steel embodiment 3 of the present invention;
(the welding heat analog parameter is T to Fig. 2 for invention steel embodiment 3 welding heat simulated HAZ microstructures
Max=1350 ℃, t
8/5=250s).
Embodiment
Specific embodiment is referring to table 1～table 3.
Table 1 chemical ingredients
| The steel sample | C(％) | Si(％) | Mn(％ ) | P(％) | S(％) | Als(％) | Nb(％) | N(ppm) | Ti(％) | B(ppm) | Ca(ppm) | Cu(％) | Ni(％) |
| Embodiment 1 | 0.045 | 0.16 | 1.70 | 0.010 | 0.0016 | 0.048 | 0.013 | 32 | 0.010 | 19 | 32 | / | / |
| Embodiment 2 | 0.040 | 0.17 | 1.65 | 0.008 | 0.0013 | 0.052 | 0.018 | 28 | 0.009 | 22 | 36 | / | / |
| Embodiment 3 | 0.050 | 0.15 | 1.55 | 0.010 | 0.0019 | 0.057 | 0.015 | 35 | 0.010 | 15 | 42 | / | / |
| Embodiment 4 | 0.035 | 0.13 | 1.75 | 0.008 | 0.0015 | 0.056 | 0.016 | 33 | 0.011 | 28 | 35 | / | / |
| Embodiment 5 | 0.038 | 0.16 | 1.72 | 0.009 | 0.0017 | 0.054 | 0.019 | 26 | 0.008 | 16 | 21 | ||
| Embodiment 6 | 0.031 | 0.20 | 1.80 | 0.010 | 0.0020 | 0.040 | 0.010 | 30 | 0.012 | 11 | 15 | ||
| Comparative example 1 * | 0.06 | 0.27 | 1.47 | 0.008 | 0.001 | 0.038 | / | / | 0.010 | / | 0.006 ** | / | 0.40 |
| Comparative example 2 * | 0.08 | 0.39 | 1.54 | 0.007 | 0.003 | 0.028 | 0.026 | 30 | Add | / | Add | 0.20 | 0.25 |
| Comparative example 3 (Sumitomo Metal Industries) | 0.06 | 0.11 | 1.38 | 0.009 | 0.001 | / | 0.010 | / | 0.020 | / | / | 0.30 | 0.86 |
| Comparative example 4 * | 0.07 | 0.10 | 1.55 | 0.005 | 0.001 | 0.028 | 0.015 | 39 | Add | / | Add REM | 0.29 | 1.09 |
| Comparative example 5 (Nippon Steel) | 0.09 | 0.26 | 1.54 | 0.008 | 0.003 | 0.034 | / | / | 0.010 | / | / | 0.30 | 0.29 |
*The Kawasaki Steel
Table 2 manufacturing process
| The steel sample | Steel plate thickness (mm) | Heating temperature (℃) | The recrystallization zone | The non-recrystallization district | The rolling end to ACC time (s) | Speed of cooling (℃/s) | Quenching end temp QST (℃) | The cooling in heap end temp (℃) | ||
| Percentage pass reduction (%) | Accumulative total draft (%) | Percentage pass reduction (%) | Accumulative total draft (%) | |||||||
| Embodiment 1 | 45 | 1100 | 14 | 63 | 11 | 52 | 13 | 12 | 390 | 85 |
| Embodiment 2 | 60 | 1110 | 12 | 55 | 12 | 62 | 11 | 15 | 410 | 100 |
| Embodiment 3 | 45 | 1140 | 15 | 68 | 10 | 56 | 15 | 13 | 400 | 95 |
| Embodiment 4 | 50 | 1070 | 13 | 65 | 12 | 57 | 12 | 12 | 430 | 90 |
| Embodiment 5 | 50 | 1060 | 14 | 56 | 12 | 65 | 16 | 11 | 300 | 70 |
| Embodiment 6 | 40 | 1050 | 16 | 60 | 11 | 60 | 18 | 14 | 240 | 80 |
Table 3 plate property
| The steel sample | YP MPa | TS MPa | δ ％ | Akv(-60℃) J | Welding flawless preheating temperature ℃ | Welding heat analog parameter: T max＝1350℃、t 8/5＝250s |
| Akv(-60℃)/J | ||||||
| Embodiment 1 | 432 | 551 | 33 | 342 | 0 | 167 |
| Embodiment 2 | 431 | 548 | 30 | 312 | 0 | 156 |
| Embodiment 3 | 426 | 532 | 31 | 298 | 0 | 147 |
| Embodiment 4 | 423 | 538 | 32 | 336 | 0 | 151 |
| Embodiment 5 | 415 | 541 | 35 | 310 | 0 | 152 |
| Embodiment 6 | 420 | 535 | 36 | 293 | 0 | 141 |
| Comparative example 1 * | 382 | 519 | 26 | 294 | 0 | / |
| Comparative example 2 * | 413 | 524 | 35 | 243 | 0 | / |
| Comparative example 3 (Sumitomo Metal Industries) | 370 | 529 | 33 | 203(-75℃) | 0 | / |
| Comparative example 4 * | 442 | 531 | 34 | 400 | 0 | / |
| Comparative example 5 (Nippon Steel) | 441 | 559 | 29 | 169 | 0 | / |
*The Kawasaki Steel
Remove the alloying of noble element such as Ni, Cr, Mo, Cu etc. in the embodiment of the invention plate, especially remove the alloying of Ni element, and optimize TMCP technology, in the mother metal steel plate low-temperature flexibility that obtains even and excellent, the low-temperature flexibility of HAZ is excellent too during the ultra-large linear energy input welding.This not only can reduce manufacturing cost, shorten the production cycle, organization of production difficulty [Ni, Cu, the higher steel plate of Mo constituent content have also been reduced, surface quality of continuously cast slab is relatively poor, generally all needing rolls off the production line carries out surface-conditioning, sometimes also need to carry out surface colour penetration inspection (being that so-called PT checks) and the cutting of band temperature etc., cause manufacturing cost to raise and environmental pollution], also eliminate the difficulty of the steel scrap recovery that contains Cu, Ni in a large number, realized the environmental protection of manufacturing processed, use and removal process; But also improved the user site welding efficient, reduced the user and made the use cost and the scope of application.Because the present invention does not need to add any equipment, production technique is simple, and process control is easy, can have the Heavy Plate Production producer that quickens cooling equipment to all and promote, and has very strong adaptability, the feature of environmental protection and high economy.
In sum, the present invention has successfully avoided Nippon Steel, JFE, the blockade of house journal's technology such as Sumitomo Metal Industries, start with from alloy designs, adopt the high Mn-Nb series low-alloy of low-carbon (LC) C-steel as the basis, suitably improve the content of Als, the C/Mn ratio is controlled at 0.020～0.050, the Ti-B microalloying, Ca handles and control Ti/N metallurgical technology means such as between 3.0～3.5, optimize TMCP (Thermo-mechanical control process, the mechanical control process of heat) technology, the microstructure that makes the finished product steel plate is the bainite that a spot of ferrite (20%～30%)+disperse distributes, average grain size is below 15 μ m, in the mother metal steel plate low-temperature flexibility that obtains even and excellent, the low-temperature flexibility of HAZ is excellent too during the ultra-large linear energy input welding, be mother metal steel plate-60 ℃ Akv 〉=100J, welding analog heat affected zone (HAZ)-60 ℃ Akv 〉=34J (1350 ℃ of simulated peak temperature, t
8/5〉=200 seconds), be specially adapted to ice extra large geographic ice-breaking vessel housing, LNG ship hull, ocean platform and bridge construction, guarantee the steamer that travels in extremely cold area and the safety of offshore oil production platform.
Claims (5)
1. but ultra-large linear energy input welds thick steel plate for low temperature use, and its composition weight percent is:
C：0.030％～0.050％
Si：≤0.20％
Mn：1.50％～1.80％
P：≤0.010％
S：≤0.002％
Nb：0.010％～0.020％
Als：0.040％～0.060％
Ti：0.008％～0.012％
N：≤0.0035％
Ca：0.001％～0.005％
B：0.001％～0.003％
Simultaneously: 0.02≤C/M≤0.06, Ti/N is between 3.0～3.5;
Relation between B, Ti, the N: 10ppm+0.714 (N-0.292Ti)≤B≤20ppm+0.714 (N-0.292Ti);
Relation between Als, Ti and the N: Als 〉=30 * (N-0.292Ti);
All the other are iron and inevitably being mingled with,
Wherein, Pcm≤0.18%, wherein Pcm=wt%C+wt%Si/30+ (wt%Mn+wt%Cu+wt%+Cr)/20+wt%Ni/60+wt%Mo/15+wt%V/10+5wt%B.
2. but ultra-large linear energy input welding thick steel plate for low temperature use as claimed in claim 1 is characterized in that B:0.0015%～0.0025%.
3. but the manufacture method of ultra-large linear energy input welding thick steel plate for low temperature use as claimed in claim 1, it comprises the steps:
A. casting, tundish molten steel casting temperature≤1540 ℃;
B. slab heating temperature is controlled between 1050 ℃～1150 ℃;
C. in the perfect recrystallization temperature range, big rolling pass draft continuous rolling guarantees that deformable metal takes place dynamically/static recrystallize, refine austenite crystal grain, rolling pass draft 〉=12%, recrystallization zone (〉=980 ℃) total draft 〉=55%; Carry out controlled rolling in the non-recrystallization district, percentage pass reduction 〉=10%, non-recrystallization district (＜900 ℃) total draft 〉=50%;
D. should control shortly as far as possible from rolling the end to the biography time of putting beginning to quicken to cool off, be controlled in 20 seconds, and when particularly importantly quickening the cooling beginning, steel billet temperature must be at Ar
3More than the point, Ar
3(℃)=910-310[%C]-80[%Mn]-20[%Cu]-15[%Cr]-55[%Ni]-80[%Mo]-0.35 (t-8), wherein t is thickness of slab (mm);
E. carrying out direct quenching with 〉=10.0 ℃/s speed of cooling is cooled to quench and stops temperature, quenching stops temperature and is controlled at 200～450 ℃, make steel plate that cooling bainitic transformation continuously fully take place in＞200 ℃ of scopes, suppress the proeutectoid ferrite phase transformation, to obtain high tensile steel plate under the condition that is implemented in low-carbon-equivalent;
F. then below the slow cooling to 100 ℃, average slow cooling speed≤10 ℃/hr, natural air cooling is to room temperature subsequently, and the slow cooling time must not be lower than 24 hours.
4. but the manufacture method of ultra-large linear energy input welding thick steel plate for low temperature use as claimed in claim 3 is characterized in that casting technique adopts continuous casting process, gently depresses technology with induction stirring or continuously cast bloom, and light draught is controlled between 3%～10%.
5. but the manufacture method of ultra-large linear energy input welding thick steel plate for low temperature use as claimed in claim 3 is characterized in that it is 380 ℃～430 ℃ that step e quenching stops temperature range.
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