CN101215669A - High-strength thick steel plate for large-scale petroleum storing tank and low-cost manufacturing method thereof - Google Patents
High-strength thick steel plate for large-scale petroleum storing tank and low-cost manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a method for preparing a high strength thick steel plate for a large oil storage tank in a low cost, the method particularly applies to a high strength thick steel plate for a large oil storage tank, which is welded by line energy which is equal or less than 120 KJ/cm. The weight percentages of chemical constituents are that carbon is 0.01-0.12 percent, silicon is 0.15-0.35 percent, manganese is 1.45-1.80 percent, phosphorus is equal or less than 0.010 percent, sulfur is equal or less than 0.003 percent, aluminum is 0.02-0.06 percent, vanadium is 0.02-0.06 percent, nickel is 0.20-0.40 percent, nitrogen is 0.003-0.006 percent, and the other is ferric, other alloying elements and inevitable impurities. The invention uses on-line quenching and off-line tempering processes, thereby reducing valuable alloying elements, obtaining high strength high toughness thick steel plate which has excellent welding performance and does not need to preheat above 0 DEG C, reducing the producing cost, saving energy, increasing production efficiency and improving welding construction conditions, and the invention is capable of being widely used for constructions of a 10-30 cubic myriametre of large oil storage tank.
Description
Technical field
The invention belongs to steel plate low alloy steel production technique field, relate to a kind of high-strength thick steel plate for large-scale petroleum storing tank and manufacture method thereof, particularly be adapted to the petroleum storage tank high tensile steel plate of 80～120KJ/cm large-line energy welding.
Background technology
Along with continuous demand to the energy, constantly development and of the construction of petroleum storage tank both at home and abroad, 10～300,000 m to large scale development
3The construction of large-scale petroleum storing tank enters the peak period.Medium in the petroleum storage tank belongs to inflammable hazardous substance, and building the required steel of storage tank needs can use after the specified authoritative quality testing department authentication of country.
In order to reduce material and manufacturing cost, petroleum storage tank mainly adopts the modified plate of high strength, and require the welding procedure high-level efficiency, as main electro-gas (enclosed) welding and the union-melt weld horizontal position welding technology that adopts large-line energy in the wallboard construction, weld heat input is imported at 80～120KJ/cm.Therefore, the high-strength steel that petroleum storage tank adopted should satisfy: (1) high surrender and tensile strength, high tenacity, high uniformity and stability; (2) must adapt to the large-line energy welding, after the large-line energy welding of employing 80～120KJ/cm, the not obvious reduction of its HAZ (welded heat affecting zone) plasticity and toughness; (3) in order to be fit to site welding, do not need preheating before the welding, postwelding does not produce welding cold cracking; (4) 580 ℃ of SR handling properties of postwelding do not reduce.
Because the technical requirements height of this steel, the production difficulty is big, for satisfying the needs of the large-scale petroleum storing tank construction that constantly develops, a large amount of research and discoveries has been carried out in aspects such as domestic and international welded heat affecting zone structure property feature to Hi-Stren steel, austenite crystal growth dynamics, has obtained certain achievement.
Before the present invention, the spy opens to be disclosed as in clear 49-37814 communique and the special fair 4-13406 communique and reduces welding crack sensibility and the technology of carbon drop C and interpolation titanium one boron (Ti-B), guarantees the hardening capacity of steel by the interpolation boron.It is that low-carbon (LC) C adds vanadium V and the method for the 600MPa grade high-strength steel of low welding susceptibility is produced in direct quenching that the spy opens clear 61-12970 communique, but does not all relate to the large-line energy welding, is not suitable for the large-line energy weldprocedure in the large-scale petroleum storing tank site operation.
Open clear 60-9086 the spy, the spy opens flat 2-254119, and the spy opens clear 59-113120, and the spy opens the technology that has proposed not add boron in the clear 61-12970 communique.Technology in the communique all is the technology of the non-modified shaped steel of 600MPa level, but finds out that from embodiment the thickness of slab upper limit that these technology are suitable for all is about 20mm, can not satisfy large-scale petroleum storing tank steel plate maximum ga(u)ge 30～50mm requirement.
Te Kaiping 10-68045 communique is the production method with good welds crack sensitivity and large-line energy welding back HI high impact value steel of 570MPa high intensity levels.This hardness of steel is on the low side.Te Kaiping 10-298706 communique is 600MPa high strength, high heat input energy welding low-crackle sensitive steel and production method thereof.The two is all limited with formula 625 (effectively Nb)+250V+210Ceq 〉=t+40 (t is steel plate thickness mm) niobium Nb, vanadium V content in the steel, the alloy content height, and cost is higher, belongs to different alloy designs theories with the object of the invention.
Domestic also have some to be applicable to the research of petroleum storage tank with high tensile steel plate and production method thereof.As " the welding crack sensibility Series Steel and the production method thereof of large-line energy " (ZL 02115877.0), " but the superstrength Plate Steel and the manufacture method thereof of large-line energy welding " (ZL 200410017255.5), " but a kind of Plate Steel and manufacture method of large-line energy welding " (application number 200510023216.0), " great line energy and low welding crack responsive type Plate Steel and production method thereof " (application number 200510047195.6), " a kind of Nb-Ti micro-alloyed steel and smelting process of suitable large-line energy welding " (application number 200510047672.9), " unmodified high-toughness low-temp steel for high-energy line welding and production method thereof " (ZL 01128316.5), " a kind of soldering not quenching and tempering steel plate in high intensity by large line energy and manufacture method thereof " (application number 200710052134.8).These prior aries, mainly there are the following problems:
(1) weld heat input is low, generally only is applicable to 〉=low temperature spherical tank of the weld heat input of 50KJ/cm～80KJ/cm, the construction of storage tank, and is not suitable for the more large-scale petroleum storing tank of large-line energy welding input.Though heat input the higher person (application number 200710052134.8) is also arranged, and its intensity is lower than 600MPa, can not satisfy large-scale petroleum storing tank armor plate strength requirement.
(2) add the hardening capacity that boron guarantees steel.So far, tensile strength 600MPa level low welding crack sensibility high-strength steel plate adopts the quenching and tempering type production technology basically, nearly all be the hardening capacity that guarantees steel by interpolation B, the mother metal unstable properties, particularly the hardness of welded heat affecting zone can significantly improve, and the toughness of welding fusion line is degenerated, when particularly carrying out the welding of large-line energy single face a time, owing to do not have the reheat of follow-up welding passage, the toughness of steel significantly degenerated.Also have and do not add B and guarantee welding property, as application number be 200510047195.6, ' application number is 200510047672.9 related technology, but it contains alloying elements such as more chromium Cr, niobium Nb, molybdenum Mo, cost of alloy is higher.
(3) adopt off-line hardening and tempering process or thermo-mechanical rolling technology TMCP.The modified production process complexity of off-line, link is many, surface quality is poor, production cost height, cycle long, be difficult to guarantee the time of delivery; TMCP technology is owing to cooled off condition effect, plate property poor stability.
(4) contain more expensive metal, cost of alloy is higher.For example ZL 200410017255.5, its composition C 0.01%～0.06%, Si 0.10%～0.50%, Mn 1.00%～1.40%, Nb 0.010%～0.050%, V 0.040%～0.090%, Cu 0.60%～1.00%, Cr 0.20%～0.50%, Mo 0.20%～0.50%, Ni 0.50%～0.80%, B 5PPm～30PPm, Ti 0.005%～0.020%, Al[S] 0.040%～0.070%, wherein Nb content is higher, also contain elements such as Cu, Cr, B, the content of noble metal Mo is also higher, and cost is higher.
(5) steel grade contains rare earth element, and for example ZL 01128316.5.Rare earth element is very active element, is not easy control, and pollutes molten steel easily, is unfavorable for the raising of quality product.
Summary of the invention
In view of the foregoing, the purpose of this invention is to provide a kind of petroleum storage tank high-strength steel plate and low cost production method thereof, this method is by reducing noble metal content in the composition, cooperate suitable smelting, rolling technique, make full use of the energy, reduce production costs, reduce the organization of production difficulty, reduce production process, shorten the production cycle; And the steel plate that obtains is adapted to the more welding of large-line energy, and (80～120KJ/cm), this steel plate can be applicable to 10～30 ten thousand stere petroleum storage tanks.
Technical scheme of the present invention is: this kind high-strength thick steel plate for large-scale petroleum storing tank, it is characterized in that its main chemical compositions weight percent is: C:0.01～0.12%, Si:0.15～0.35%, Mn:1.45～1.80%, P≤0.010%, S≤0.003%, Al:0.02～0.06%, V:0.02～0.06%, Ni:0.20～0.40%, N:0.003～0.006%, all the other are Fe and other alloying element and unavoidable impurities.
In described a kind of high-strength thick steel plate for large-scale petroleum storing tank, add following weight percent in the chemical ingredients of steel: Nb≤0.02%, Mo≤0.12%, Ti:0.010～0.040%, and satisfy Ti/N=2.0～3.4; Simultaneously, the chemical ingredients of steel satisfies:
Reheat crack(ing) sensitivity coefficient PSR=Cr+Cu+2Mo+10V+7Nb+5Ti-2≤0; Welding crack sensibility FACTOR P cm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.21%.
Described large-scale petroleum storing tank is characterized in that with the manufacture method of high tensile steel plate the a.KR molten iron is handled; The b.LF+VD refining techniques; C. slab continuous casting technology; D. slab heating; E. the abundant recrystallize of realization is depressed in hot rolling greatly in the austenite recrystallization district; F. direct quenching cooling; G. powerful hot straightening switchboard shape; H. non-oxidation roller hearth furnace temper.
In described high-strength thick steel plate for large-scale petroleum storing tank manufacture method, fully adding Nb at LF after the deoxidation, add Ti among VD or the RH, and handle by adding Ca, the nodularization inclusion morphology has been realized the smelting of Clean Steel, purifies steel.
In described high-strength thick steel plate for large-scale petroleum storing tank manufacture method, steel billet is heated to 1100～1250 ℃; At austenite the recrystallization zone can taking place, billet rolling is become steel plate; The recrystallization zone does not take place with steel plate rolling at austenite, 860～950 ℃ of finishing temperatures; Utilize the cooling of steam fog and two stages of water curtain to realize the quick cooling of 25～45 ℃/s of steel plate after rolling, realize the steel plate press quenching; Steel plate after quenching is carried out 600 ℃～650 ℃ high temperings.
The present invention is Nb, Ti, the V element microalloying by minute quantity, reduce the welding crack sensibility component, do not add the B element, with the Composition Control of steel at C≤0.15%, Pcm≤0.21%, and generate the fine particle TiN that disperse distributes by high temperature in the control smelting process, the microtexture and the particle amount of separating out of control steel plate, suppress steel plate the growing up of crystal grain in welding process, improve its HAZ low temp area toughness, improve the ability of Chinese People's Anti-Japanese Military and Political College's heat input welding input.By the content of control smelting process O, N, H, the addition sequence of alloying element utilizes the rolling abundant crystal grain thinning of steel plate high temperature recrystallize, utilizes the online direct quenching of waste heat of rolling back steel plate, and large-line energy welding high tensile steel plate is produced in the off-line tempering.Quickening cooling can energy efficient, reduce production costs.When steel plate is produced, utilize the waste heat that rolls the back steel plate, give certain speed of cooling and control its phase transition process, thereby can replace and roll back normalizing treatment and quenching and add tempering and handle, save the energy consumption of second-heating, reduce operation, shorten the production cycle, thereby reduced production cost.
In order to guarantee purpose of the present invention, make steel plate have the high-intensity while, have high toughness, good welding property, at first to design suitable tissue-bainite, tempered sorbite.The steel plate of low-carbon-equivalent, low crackle sensitivity coefficient component has good low-temperature flexibility and welding property.Details are as follows for the reason that each element is limited the quantity of among the present invention:
C produces remarkably influenced to intensity, low-temperature impact toughness, the welding property of steel, and C can improve intensity on the one hand, and on the other hand, along with increasing of C content, low-temperature impact toughness, welding property can decrease.When C is higher than 0.12%, the hardened structure of volume appears in the welded heat affecting zone, and make toughness obtain worsening, and be easy to generate welding crack during high C.C content of the present invention is limited in 0.01～0.12%.
Mn mainly plays the solution strengthening effect, improves the tensile strength that manganese content can significantly improve steel, and manganese can also be postponed ferrite, pearlitic transformation, and reduces the transition temperature of bainite, helps forming fine grain structure; When Mn content was higher than 1.80%, heat affected zone toughness degenerated.Mn content of the present invention is limited in 1.45～1.80%.
Add micro-Nb, V, Ti element in the steel, can suppress steel weld affected zone flexible and descend.Nb, V, Ti are strong carbon, nitride forming element, in steel, can form tiny, dispersion, hard carbide or the nitride of matter, play the effect of dispersion-strengthened, crystal grain thinning and precipitation strength, can effectively improve intensity, hardness, toughness, wear resistance, erosion resistance, ductility and the welding property of steel, reduce the superheated susceptivity and the timeliness tendency of steel.
Niobium can produce the grain refining of highly significant and moderate precipitation strength effect, easily combine and generate carbonitride with C, N, in the operation of rolling, separate out the pinning crystal boundary and stop growing up of crystal grain, postpone austenitic recrystallize, improve intensity and flexible effect to play by disperse.But add too much, cause the recrystallization temperature of steel to raise.Nb content of the present invention≤0.02%.
The Ti chemically reactive is very strong, and the C among the Yi Yugang, N, O, S form compound.Add trace Ti, make itself and N in the steel form TiN, TiN particle and ferritic mismatch very little (3.8%) can be used as the matrix of heterogeneous nucleation, generation intensive precipitation strength and moderate grain refining effect.TiN can stop steel billet the growing up of crystal grain in heating, rolling, welding process, improves the toughness of mother metal and welded heat affecting zone.Simultaneously, TiN can effectively stop austenite crystal growing up in heat-processed, plays the effect of refine austenite crystal grain, and can improve the toughness of welded heat affecting zone.The strict control of the present invention Ti, N constituent content are respectively 0.010～0.030%, 0.003～0.006%, and control Ti/N=2.0～3.4.
The solubleness of vanadium is lower, to stop austenite crystal grow up and the effect of recrystallize very weak, mainly be to produce moderate precipitation strength effect by separating out of C, N compound in the ferrite.An amount of interpolation of V can guarantee the intensity of mother metal and welding joint, but content can reduce base metal tenacity and welding property greater than 0.06% o'clock.V content of the present invention is restricted to 0.02～0.06%.
Mo can improve the hardening capacity of Plate Steel, helps austenite crystal refinement when rolling and and the generation of fine bainite.The main effect of Ni is the low-temperature flexibility that improves steel.But these two kinds of elements all can significantly improve carbon equivalent, cause the welding property of steel to descend, and Mo, Ni alloy are comparatively valuable.For reducing production costs under the prerequisite that guarantees the every performance of steel plate, the present invention is respectively 0.08～0.12%, 0.20～0.40% to Mo, Ni constituent content limited field.
Al is a deoxidant element, and the AlN that forms in the steel is crystal grain thinning effectively, and content 0.02%～0.06% is comparatively suitable.
Impurity element P, S in the steel, N are low as far as possible, avoid occurring steel inclusion, influence the toughness of steel plate.The present invention requires P≤0.010%, S≤0.003%.
By above-mentioned analysis, the present invention is the effect that makes full use of manganese, improve the content of manganese, reduction carbon, reduce Mo and Ni, utilize the Nb of trace to digest a part of N, add the Ti element, utilize the proportioning that forms Ti/N=2.0～3.4 when smelting to come under the condition of high temperature, to generate tiny TiN particle, the stability of TiN guarantees in the steel plate evenly tiny TiN in thereafter controlled rolling and modified process, and crystal grain is thick during the welding of control steel plate, improves the welding property of steel plate.
1, the present invention adopts high Clean Steel production technique to produce low-sulfur, phosphorus content, low-carbon high-manganese, the composition design of niobium, titanium-combined microalloying.Chemical composition content per-cent by weight sees Table 1.
Table 1 chemical composition content (per-cent of weight)
| C | Si | Mn | P | S | Nb | Ti | V | Mo | Ni | N | Als |
| 0.01～ 0.12 | 0.15～ 0.35 | 1.45～ 1.80 | ≤ 0.010 | ≤ 0.003 | ≤0.02 | 0.010～ 0.030 | 0.02～ 0.06 | 0.08～ 0.12 | 0.20 0.40 | 0.003～ 0.006 | 0.02～ 0.06 |
Steel chemical composition of the present invention satisfies:
PSR＝Cr+Cu+2Mo+10V+7Nb+5Ti-2≤0，
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.21％。
Have good anti-reheat cracking susceptibility and welding property.
The composition design that press quenching, off-line tempering process adopt is: utilize Nb, the V of minute quantity, the combined microalloying of Ti, add the hardening capacity of a small amount of Mo raising Plate Steel, cooperate the controlled rolling in later stage, make full use of the waste heat of rolling back steel plate, utilize the cooling of steam fog and two stages of water curtain to realize the quick cooling of steel plate 〉=25 ℃/s, make the steel plate press quenching, saved the energy, save the operation that similar steel plate rolls off the production line and quenches, improved production efficiency, saved the energy.
2, the mechanical property of steel of the present invention sees Table 2.
After the large-line energy welding of 80～120KJ/cm, tensile strength 〉=610MPa, heat affected zone-20 ℃ ballistic work mean value 〉=47J, monodrome 〉=33J.
Table 2 mechanical property
| Specification mm | Rp 0.2，MPa | Rm，MPa | A，％ | 180 ° of clod washes | A KV, J ,-20 ℃ are vertically |
| 12～50 | ≥490 | 610～730 | ≥17 | d＝3a | ≥100 |
3, the production technique of steel of the present invention: the a.KR molten iron is handled; The b.LF+VD refining techniques; C. slab continuous casting technology; D. slab heating; E. the abundant recrystallize of realization is depressed in hot rolling greatly in the austenite recrystallization district; F. direct quenching cooling; G. powerful hot straightening switchboard shape; H. non-oxidation roller hearth furnace temper.
4, smelting steel process of the present invention is handled by adding Ca, and the nodularization inclusion morphology has been realized the smelting of Clean Steel, has purified steel.
5, smelting steel process alloying element addition sequence of the present invention: Nb, V, Ti are more valuable alloying elements, after finishing, vacuum-treat later stage or vacuum-treat add again, can greatly improve the microalloy element specific absorption on the one hand, also can reduce the content of hydrogen in the steel simultaneously.
6, the production process of steel of the present invention is: steel billet is heated to 1100～1250 ℃; At austenite the recrystallization zone can taking place, billet rolling is become steel plate; The recrystallization zone does not take place with steel plate rolling at austenite, 860～950 ℃ of finishing temperatures; To be not less than the rate of cooling press quenching of about 25 ℃/s, to being lower than about 150～300 ℃ quenching final temperature; Steel plate after quenching is carried out high tempering.
Beneficial effect outstanding behaviours of the present invention exists:
1, chemical composition design is simple, by element addition and kind few principle of trying one's best, rationally adjusts the proportional quantity of each element, guarantees the performance of steel plate, reduces production cost.
2, do not add the B element, avoided the influence of B, guaranteed the large-line energy welding property of steel plate welded heat affecting zone hardness and mother metal stability.
3, back direct-on-line quenching technology is rolled in employing.Being not less than the rate of cooling press quenching of 25 ℃/s, plate property is stable, and is with short production cycle, cost is low, organize difficulty little.
4, adopt rational valuable alloy addition sequence, improve the alloying element specific absorption, reduce cost of alloy.
5, realized the organic unity of steel plate high strength, high tenacity and superior weldability, but realized the large-line energy welding, welding steel need not to carry out preheating more than 0 ℃.
Description of drawings
Fig. 1 is an example light plate impact fracture pattern (SEM);
Fig. 2 is a 21.5mm steel plate OPM tissue (thickness 1/4 * 500) in the example;
Fig. 3 is a 21.5mm steel plate SEM tissue (thickness 1/4 * 3000) in the example;
Fig. 4 is a 21.5mm steel plate SEM tissue (thickness 1/4 * 2000) in the example;
Fig. 5 is for comparing steel plate SEM tissue (thickness 1/4 * 2000).
Embodiment
The employing press quenching of steel of the present invention+tempered explained hereafter oil tank steel, its technical process is as follows:
High-quality molten iron-KR hot metal pretreatment-120 ton top and bottom combined blown converter-CAS station Argon processing-LF stove refining-VD vacuum outgas processing-slab casting-walking beam furnace-high-pressure water descaling-3200mm milling train roughing-3500mm milling train finish rolling-press quenching-brute force aligning-finishing-spray number sign-flaw detection-tempering-inspection by sampling-warehouse-in-delivery.
Smelting technology: adopt converter smelting,, carry out dark decarburization by top blast or top bottom blowing; Adopt LF stove and the vacuum-treat of VD stove, reduce the content of obnoxious flavour such as O, H, N and S; Add alloying element, carry out microalloying; Ca handles, and feeds Si-Ca line 1～6m/t, and the control oxide morphology improves ductility and toughness, reduces the horizontal and vertical poor performance of steel plate; Continuous casting adopts induction stirring.The chemical ingredients of final steel of the present invention is (by weight percentage): C:0.01～0.12%, Si:0.15～0.35%, Mn:1.45～1.80%, P≤0.010%, S≤0.003%, Al:0.02～0.06%, Nb≤0.02%, V:0.02～0.06%, Ti:0.010～0.040%, Ni:0.20～0.40%, Mo≤0.12%, N:0.003～0.006% and satisfy Ti/N=2.0～3.4.In addition, steel chemical composition of the present invention also must satisfy:
PSR＝Cr+Cu+2Mo+10V+7Nb+5Ti-2≤0，
Pcm＝C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B≤0.21(％)
All the other are Fe and unavoidable impurities.
Hot steel bloom furnaceman skill: after the continuously cast bloom cutting finishes, directly be delivered to process furnace, 300～500 ℃ of billet surface charging temperatures, steel billet be in stove heat-up time 〉=3 hour, makes fully molten getting back in the austenite of the alloying elements such as Nb of separating out.1150～1200 ℃ of the final Heating temperatures of steel billet.
Rolling process for cooling: adopt the controlled rolling of two-shipper frame, it is rolling that roughing mill carries out 〉=980 ℃ perfect recrystallization, reduces the waiting time of intermediate blank, prevents to be out of shape the back austenite and too grow up.Finishing mill carries out the recrystallize controlled rolling, and rolling temperature is controlled at 930 ℃～(Ar
3+ 100 ℃), cumulative deformation 〉=60%, pass deformation rate 25～30% before extreme trace is inferior.Roll the back steel plate and carry out the high speed cooling immediately, 25～40 ℃/s of cooling rate, final cooling temperature is controlled between 150～300 ℃.With fine-grannular bainite and the thin ferrite bainite that obtains high dislocation density.
Tempering process: reveal last high strength of steel plate and good plasticity, toughness properties together with alloying element design, cooling controlling and rolling controlling process community.After steel plate has been aligned, in 580 ℃～400 ℃ temperature ranges, finish fast and shear and collection process, bell-type stacking insulation before heat treatment furnace then enters heat treatment furnace in temperature more than 300 ℃ and carries out tempering in 600 ℃～650 ℃ stoves, time inside furnace 1.5～2.0m/mm.Air cooling after steel plate is come out of the stove.
1, steel mother metal performance of the present invention
Conventional mechanical property: be positioned at 1/4 place of invention steel plate width, mechanical properties test is carried out in sampling to steel plate head, and its mechanical property is as shown in table 3.
Table 3 invention steel plate mechanical property
| Heat (batch) number | Rolling lot number | Thickness of slab mm | The position | Rp 0.2 MPa | Rm MPa | A％ | The clod wash experiment |
| D＝3a 180° | |||||||
| 06S6-04220 | 06HR38095 | 15 | Head | 545 | 645 | 18.5 | Qualified |
| 06HR39225 | 21.5 | Head | 580 | 655 | 18.5 | Qualified | |
| 06HR39089 | 21.5 | Head | 580 | 650 | 19 | Qualified | |
| 06HR39223 | 32 | Head | 565 | 660 | 19 | Qualified |
Low-temperature flexibility test: to 15,21.5,32mm invention steel plate, having carried out normal temperature～-60 ℃ is the check of temperature shock toughness, and experimental result sees Table 4.
Table 4 invention steel series of temperatures impelling strength
| Heat (batch) number (lot number) | 06S6-04220 (06HR38095) | 06S6-04220 (06HR39225) | 06S6-04220 (06HR39223) | ||||
| Steel plate specification (mm) | 15 | 21.5 | 32 | ||||
| Test temperature, ℃ | Sampling point | A KV，J | Fiber rate % | A KV，J | Fiber rate % | A KV，J | Fiber rate % |
| 20 | Steel plate head | 249 | 100 | 230 | 100 | 239 | 100 |
| 256 | 100 | 228 | 100 | 226 | 100 | ||
| 198 | 90 | 256 | 100 | 223 | 100 | ||
| The steel plate afterbody | 234 | 100 | 241 | 100 | 209 | 100 | |
| 265 | 100 | 236 | 100 | 239 | 100 | ||
| 235 | 100 | 209 | 100 | 228 | 100 | ||
| 0 | Steel plate head | 231 | 100 | 220 | 100 | 236 | 100 |
| 205 | 100 | 250 | 100 | 221 | 100 | ||
| 254 | 100 | 253 | 100 | 208 | 100 | ||
| The steel plate afterbody | 246 | 100 | 223 | 100 | 251 | 100 | |
| 245 | 100 | 239 | 100 | 231 | 100 | ||
| 258 | 100 | 247 | 100 | 215 | 100 | ||
| -20 | Steel plate head | 214 | 100 | 198 | 100 | 210 | 100 |
| 242 | 100 | 238 | 100 | 198 | 100 | ||
| 204 | 95 | 256 | 100 | 258 | 100 | ||
| The steel plate afterbody | 211 | 100 | 220 | 100 | 220 | 95 | |
| 237 | 100 | 236 | 100 | 204 | 100 | ||
| 228 | 95 | 248 | 100 | 232 | 100 | ||
| -40 | Steel plate head | 258 | 100 | 255 | 100 | 252 | 100 |
| 178 | 90 | 188 | 95 | 176 | 90 | ||
| 244 | 100 | 248 | 100 | 250 | 100 | ||
| The steel plate afterbody | 248 | 100 | 231 | 100 | 256 | 100 | |
| 256 | 100 | 246 | 100 | 232 | 100 | ||
| 207 | 100 | 227 | 100 | 203 | 100 | ||
| -60 | Steel plate head | 193 | 69 | 163 | 58 | 224 | 74 |
| 165 | 30 | 162 | 55 | 201 | 59 | ||
| 124 | 25 | 129 | 47 | 138 | 45 | ||
| The steel plate afterbody | 202 | 70 | 200 | 70 | 201 | 68 | |
| 217 | 65 | 212 | 65 | 216 | 70 | ||
| 174 | 45 | 241 | 59 | 149 | 35 | ||
As can be seen from Table 4, the same area ballistic work is more even in 20 ℃～-40 ℃ temperature ranges; The impact toughness value of steel plate head, afterbody is higher, and the impact value of head, afterbody differs and be no more than 20J, sees that thus the low-temperature flexibility of whole steel plate is high and very even.
Fig. 1 strikes off a mouthful scanning pattern for steel drift of the present invention.Observe from the SEM fracture, the impact specimen fracture is tough break, illustrates that the low-temperature flexibility of steel plate is good.
The steel plate uniformity test: for the homogeneity of check invention plate property, to the thick invention steel plate of 15mm, at its head, middle part, afterbody, intensity and low-temperature flexibility check are carried out in wide two the limit portions of plate, two 1/4 places and the sampling of 1/2 place.Assay sees Table 5.Test-results shows that each position performance of invention steel plate is even.
Table 5 15mm invention steel plate mechanical property
| Sampling point | Steel plate head | The steel plate middle part | The steel plate afterbody | |||||||||||||||
| Rp 0.2 MPa | Rm MPa | A ％ | Ballistic work, A KV，J | Rp 0.2 MPa | Rm MPa | A ％ | Ballistic work, A KV，J | Rp 0.2 MPa | Rm MPa | A ％ | Ballistic work, A KV，J | |||||||
| -20℃ | -40℃ | -60℃ | -20℃ | -40℃ | -60℃ | -20℃ | -40℃ | -60℃ | ||||||||||
| Width edge portion | 555 | 645 | 19 | 210 | 245 | 198 | 569 | 643 | 19 | 270 | 225 | 190 | 560 | 634 | 20 | 287 | 265 | 190 |
| 1/4 width | 550 | 645 | 20 | 215 | 250 | 200 | 565 | 644 | 21 | 214 | 200 | 176 | 546 | 628 | 20 | 250 | 258 | 185 |
| 1/2 width | 545 | 642 | 20 | 230 | 246 | 196 | 569 | 645 | 20 | 221 | 215 | 140 | 574 | 653 | 22 | 272 | 225 | 177 |
| 3/4 width | 550 | 650 | 19 | 225 | 235 | 187 | 560 | 645 | 20 | 225 | 221 | 169 | 550 | 630 | 21 | 264 | 251 | 182 |
| Width edge portion | 550 | 645 | 19 | 214 | 221 | 201 | 566 | 648 | 19 | 239 | 201 | 183 | 565 | 645 | 20 | 275 | 264 | 191 |
Annotate: ballistic work is a mean value.
Nil-ductility temperature NDTT test: 21mm and the thick invention steel plate of 32mm are carried out drop weight test, and sample is laterally taken a sample.Test-results sees Table 6.
Table 6 different thickness JGR610E steel plate drop weight test result
| Thickness of slab mm | The position | Test temperature ℃ | NDTT ℃ | ||||
| -20 | -25 | -30 | -35 | -40 | |||
| 21 | The top layer | ○，○ | × | × | -30 | ||
| 32 | The top layer | ○ | ○ | ○，○ | × | × | -35 |
Annotate: zero expression is not disconnected, * expression fracture
The above results shows that the invention steel plate has lower nil-ductility temperature, can satisfy the design requirements that prevents brittle rupture and crack arrest, can satisfy-40 ℃ with the requirement of steel to nil-ductility temperature.
Microstructure test: the thick invention steel plate of 21.5mm is materialsed along rolling direction, utilize GX71 type inversion type system gold phase microscope, XL-30 scanning electronic microscope that tempering attitude steel plate 1/4th places are carried out fabric analysis, organizing mainly is tempered sorbite and low-carbon bainite, and homogeneous microstructure is tiny.
The opticmicroscope metallograph is shown in Fig. 2,3.
2, solderability test
The welding heat simulation test: under 100KJ/cm and 120KJ/cm weld heat input condition, the invention steel sample after the thermal analogy is processed into the v-notch impact specimen of standard, carries out shock test at-20 ℃.Test-results sees Table 7.
-20 ℃ of Impulse Test Result of table 7 thermal analogy sample
The above results as can be seen, when the peak value Heating temperature was 1300 ℃, when weld heat input was 100KJ/cm and 120KJ/cm, the mean value of impact absorbing energy can both reach 80J, single minimum value 47J 〉=33J.Illustrate that the invention steel still can keep high ballistic work through heat affected zone, large-line energy welding back.
The electro-gas (enclosed) welding welding joint mechanical property: the invention steel plate adopts the electro-gas (enclosed) welding welding, and heat input is controlled at 100KJ/cm, stretches and cold bending test to welding joint is as-welded by the requirement of JB4708-2000 " steel pressure vessel welding technology evaluation ".Its stretching, cold bending test the results are shown in Table 8.
Table 8 invention steel welded joint mechanical property test result
| Test plate (panel) thickness | R m MPa | A% (50.8mm gauge length) | Fracture position | Bending angle | Lateral bending |
| 21.5mm | 655、660 | 42、41.9 | Weld seam | 180° | All qualified |
Invention steel welding series of temperatures Impulse Test Result sees Table 9 respectively.
The as-welded series of temperatures Impulse Test Result of table 9 electro-gas (enclosed) welding welding joint
| The steel plate specification | Sampling point | State | Test temperature ℃ | A KV J | Crystalline section rate % |
| 21.5 mm | Welded bonds | As-welded | 20 | 100，110，105(105) | 12，20，16(16) |
| 0 | 112，100，105(106) | 21，27，28(25) | |||
| -20 | 87，68，90(82) | 41，45，48(45) | |||
| -40 | 45，50，58(51) | 70，64，67(67) | |||
| -60 | 28，26，24(26) | 80，72，75(76) | |||
| The heat affected zone | As-welded | 20 | 225，205，217(216) | 0，0，0(0) | |
| 0 | 214，217，201(211) | 0，0，0(0) | |||
| -20 | 190，200，195(195) | 0，10，13(12) | |||
| -40 | 145，150，152(149) | 24，28，30(27) | |||
| -60 | 100，97，85(94) | 46，54，52(51) |
In sum, the welding of 100KJ/cm large-line energy is adopted in electro-gas (enclosed) welding, and the mechanical property of welding joint meets technical requirements fully, after the large-line energy welding, the ballistic work of welded heat affecting zone-20 ℃ is 195J, and the mother metal ballistic work is 245J, and fall is less than 25% as can be seen.Thereby illustrate that the invention steel satisfies the large-line energy requirement of welding fully.
The welded heat affecting zone maximum hardness test: the making of invention steel test plate (panel) and the mensuration of hardness are undertaken by the relevant regulations of GB4675.5-1984 " solderability test---welded heat affecting zone maximum hardness test method " standard.The PP.J607RH welding rod (oven dry in 400 ℃ * 1 hour) of Φ 4.0mm is adopted in test with welding rod, test plate (panel) weld preheating temperature is respectively 125 ℃ of room temperature (20 ℃), 75 ℃ of preheatings and preheatings, welding electric current kind is a direct current, welding current is 170～180A, arc voltage is 22～24V, and welding speed is 150mm/min.Testing weld carries out on original rolling surface.The postwelding test plate (panel) is 0 point through dissecting to be cut in point of contact, welding welded bonds bottom, about every the measuring point of 0.5mm as hardness.Vickers' hardness is measured and is undertaken by the regulation of GB/T 4340-1984 " Vickers Hardness Test method ", and Vickers' hardness measuring point position and hardness value thereof that test plate (panel) welds under different weld preheating temperature see Table 10.
The welded heat affecting zone maximum hardness test is mainly used in the anti-cold crack performance of estimating steel plate, it is generally acknowledged, the welded heat affecting zone maximum hardness of steel plate promptly has certain cold crack tendency during greater than HV350.By the result as seen: this steel plate is when being preheated to 75 ℃, and the welded heat affecting zone maximum hardness is at 310N/mm
2About, the cold crack tendency is little.
Table 10 Vickers' hardness measuring point position and hardness value thereof
| Preheating temperature | The hardness value HV of each measuring point 10 | ||||||||||||||||
| -5.5 | -4.5 | -3.5 | -2.5 | -2 | -1.5 | -1 | -0.5 | 0 | 0.5 | 1 | 1.5 | 2 | 2.5 | 3.5 | 4.5 | 5.5 | |
| Room temperature | 260 | 261 | 280 | 311 | 319 | 331 | 322 | 310 | 309 | 316 | 299 | 284 | 282 | 293 | 277 | 270 | 270 |
| 75℃ | 238 | 257 | 288 | 300 | 309 | 310 | 300 | 289 | 281 | 269 | 269 | 274 | 295 | 291 | 285 | 257 | 231 |
| 125℃ | 233 | 247 | 249 | 273 | 287 | 290 | 291 | 290 | 295 | 301 | 282 | 268 | 244 | 245 | 230 | 224 | 217 |
Annotate: the data of boldface type are welded heat affecting zone maximum hardness value in the table.
Welding joint SR heat treatment test: the thick invention steel plate of 32mm is selected in test for use, and the test welding rod is the PP.J607RH of φ 4.0mm, and the oven dry through 400 ℃ * 1 hour before the welding rod weldering is handled.Welding pre-heating temperature is 100 ℃, and weld heat input is 30～35KJ/cm, and the hydrogen that disappears that postwelding carried out 250 ℃ * 0.5 hour is immediately handled, and carries out 580 ℃ stress relieving thermal treatment then.There is one group not carry out postweld heat treatment in the test, so that carry out the contrast of mechanical property.
Welding joint to different postweld heat treatment stretches and cold bending test.(specimen size is 32 * 25 * 250mm) welding joint to be carried out tension test to adopt full thickness band scapulet shape tension specimen; Cold bending test adopts the full thickness side bend specimen, and specimen width is 32mm, and sample thickness is 10mm, and side bend specimen is 4; The sampling of welding joint impact specimen is according to the requirement of JB4708-2000.Stretching, impact, cold bending test the results are shown in Table 11 and table 12.
The different weldprocedure mechanical property test of table 11 welding joint result
| The test plate (panel) state | R m MPa | A% (50.8mm gauge length) | Fracture position | Cambered axle diameter mm | Standoff distance mm | Bending angle | Lateral bending |
| Not thermal treatment | 640，650 | 42.0，40.5 | Weld seam | 40 | 63 | 180° | All qualified |
| Thermal treatment | 645，625 | 40.0，38.5 | The heat affected zone | 40 | 63 | 180° | All qualified |
Table 12 welding joint Impulse Test Result
| The test plate (panel) state | 20 ℃ of A of weld metal KV(J) | The 20 ℃ of A in heat affected zone KV(J) | Weld metal-20 ℃ A KV(J) | Heat affected zone-20 ℃ A KV(J) |
| Not thermal treatment | 162，163，176(166) | 212，217，194(208) | 110，80，114(101) | 227，190，219(212) |
| Thermal treatment | 147，145，139(144) | 218，227，223(223) | 79，89，77(83) | 139，171，164(158) |
The result shows that through stress relieving thermal treatment, the tensile strength of joint is compared with as-welded welding joint decline slightly, and weld metal and welded heat affecting zone room temperature and low-temperature impact work also have decline to a certain degree, but still satisfy the requirement of related standards standard.
3, steel of the present invention is with the comparison of other similar steel plates
The invention steel plate is made tissue, mother metal composition performance and welding property relatively with the existing similar steel plate of other enterprises, and the tissue contrast sees that Fig. 4 and Fig. 5, mother metal composition performance and welding property see Table 13 and table 14.From contrasting as can be seen from Fig. 4 and Fig. 5, the homogeneous microstructure of steel of the present invention is tiny, is better than comparative steel; As can be seen from Table 13, guaranteeing that rigidity of the present invention can be not less than on the basis of comparative steel, valuable alloying constituents such as Mo, Nb all are starkly lower than comparative steel, illustrate that invention steel economy is higher.As can be seen from Table 14, compare the steel plate of producing than other enterprises, obvious steel of the present invention is under the heat input greater than 100KJ/cm, even the heat affected zone still has very high low-temperature flexibility after reaching 120KJ/cm, is better than comparative steel greatly.More than explanation is produced this high-strength steel by press quenching+off-line tempering working method, and its economy is higher, and welding property is better than additive method, is a kind of low-cost manufacture method of high-strength thick steel plate for large-scale petroleum storing tank.
Table 13 invention steel and comparative steel composition performance comparison
| Grade of steel | C | Si | Mn | P | S | Als | Ni | Cr | Mo | Ti | V | Nb | Rel (MPa) | Rm (MPa) | A (％) | Akv-20 ℃ horizontal (J) |
| The invention steel | 0.08 | 0.25 | 1.55 | 0.008 | 0.003 | 0.04 | 0.20 | - | 0.09 | 0.018 | 0.04 | 0.018 | 580 | 655 | 19 | 249，255，248 |
| Comparative steel | 0.06 | 0.25 | 1.5 | 0.009 | 0.003 | 0.04 | 0.24 | 0.04 | 0.23 | 0.010 | 0.04 | 0.024 | 570 | 655 | 19 | 288，283，280 |
| The invention steel | 0.09 | 0.26 | 1.60 | 0.008 | 0.003 | 0.039 | 0.22 | - | 0.10 | 0.017 | 0.041 | 0.017 | 580 | 650 | 21 | 239，245，244 |
| Comparative steel | 0.09 | 0.24 | 1.35 | 0.010 | 0.005 | 0.043 | 0.25 | 0.037 | 0.18 | 0.027 | 0.046 | 0.042 | 585 | 635 | 25.5 | 204，192，200 |
Table 14 invention steel and the contrast of comparative steel welding property
| Grade of steel | Heat input KJ/cm | Rm MPa | A％ (50mm) | Angle of bend | Lateral bending | Sampling point | Test temperature | A KV J | Crystalline section rate % |
| The invention steel | 100 | 655，660 | 42，41.9 | 180 | All qualified | The heat affected zone | -20 | 190，200，195(195) | 0，10，13(12) |
| The invention steel | 120 | 620，625 | 40，41 | 180 | All qualified | The heat affected zone | -20 | 226，173，109(169) | 0，12，16(14) |
| Compared steel | ＜100 | 665，655 | 37，36 | 180 | All qualified | The heat affected zone | -20 | 66，51，57，(58) | 62，77，73(71) |
Claims (5)
1. high-strength thick steel plate for large-scale petroleum storing tank, it is characterized in that its chemical component weight per-cent is: C:0.01～0.12%, Si:0.15～0.35%, Mn:1.45～1.80%, P≤0.010%, S≤0.003%, Al:0.02～0.06%, V:0.02～0.06%, Ni:0.20～0.40%, N:0.003～0.006%, all the other are Fe and other alloying element and unavoidable impurities.
2. a kind of high-strength thick steel plate for large-scale petroleum storing tank as claimed in claim 1, it is characterized in that, add following weight percent in the chemical ingredients of steel: Nb≤0.02%, Mo≤0.12%, Ti:0.010～0.040%, and satisfy Ti/N=2.0～3.4; Simultaneously, the chemical ingredients of steel satisfies:
P
SR＝Cr+Cu+2Mo+10V+7Nb+5Ti-2≤0；
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20％。
3. the manufacture method of a large-scale petroleum storing tank usefulness high tensile steel plate as claimed in claim 1 or 2 is characterized in that the a.KR molten iron is handled; The b.LF+VD refining techniques; C. slab continuous casting technology; D. slab heating; E. the abundant recrystallize of realization is depressed in hot rolling greatly in the austenite recrystallization district; F. direct quenching cooling; G. powerful hot straightening switchboard shape; H. non-oxidation roller hearth furnace temper.
4. high-strength thick steel plate for large-scale petroleum storing tank manufacture method as claimed in claim 3 is characterized in that: fully adding Nb at LF after the deoxidation, add Ti among VD or the RH, and handle by adding Ca, the nodularization inclusion morphology has been realized the smelting of Clean Steel, purifies steel.
5. high-strength thick steel plate for large-scale petroleum storing tank manufacture method as claimed in claim 4 is characterized in that: steel billet is heated to 1100～1250 ℃; At austenite the recrystallization zone can taking place, billet rolling is become steel plate; The recrystallization zone does not take place with steel plate rolling at austenite, 860～950 ℃ of finishing temperatures; Utilize the cooling of steam fog and two stages of water curtain to realize the quick cooling of 25～45 ℃/s of steel plate after rolling, realize the steel plate press quenching; Steel plate after quenching is carried out 600 ℃～650 ℃ high temperings.
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| CN101215669B (en) | 2011-07-06 |
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