CN102534372A - Preparation method of P110-grade expansion tube for exploiting petroleum and gas - Google Patents
Preparation method of P110-grade expansion tube for exploiting petroleum and gas Download PDFInfo
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Abstract
The invention relates to a preparation method of a P110-grade expansion tube for exploiting petroleum and gas. The expansion tube comprises the following chemical components by mass percentage: 0.10-0.30 of C, 0.70-2.0 of Mn, 0.3-1.5 of Si, 0-1.0 of Al, 0.02-0.1 of Nb, 0-0.02 of Ti and the balance of Fe and inevitable impurities. The preparation method comprises the following steps of: after performing smelting and rolling to obtain a related alloy plate, performing plate rolling to the alloy plate and welding to prepare the expansion tube, and finally, performing complete austenitizing and then carrying out heat treatment process of quenching and subsequent subtemperature tempering-quenching-partitioning to enable an expansion tube to reach expected strength criterion and plastic deformation ability and ensure the mechanical property of the tube after and before tube expansion to meet provisions of API (American Petroleum Institute) and other relevant standards. Test results show that the P110 steel grade multiphase expansion tube with high uniformity extension has high strength, plasticity, toughness and elongation rate, and has comprehensive mechanical property superior to the conventional quenching-tempering steel, trip steel and Q-P (quenching--partitioning) steel.
Description
Technical field
The invention belongs to field of iron and steel, relate in particular to the preparation method of a kind of oil and gas exploitation with P110 level expansion pipe.
Background technology
In recent years; Flourish along with petroleum drilling and mining industry; Relevant exploratory development has been extended to complicated fields such as ocean operation and land ultra deep well operation, and the appearance of these brand-new problems of exploitation of sea boring and land ultra deep well makes the difficulty of oil-gas exploration and development increase day by day.In these fields, traditional oil gas well operations mode has received serious limit, and its reason is; The original technique sleeve pipe is made up of the sleeve pipe of multiple size; The taper that its hole structure is big up and small down along with the increase of well depth, is lowered to sleeve pipe level in the well also in continuous increase; Thereby make available borehole diameter more and more littler; And increased the cost of drilling well greatly, and in the drilling well of deep-well ultra deep well, constantly the dwindling even might cause finally boring and reach zone of interest of borehole diameter.In this case, late nineteen nineties in last century, Shell Co. Ltd has at first proposed the inflatable sleeves Manifold technology, and in the heavy duty service of the ocean in the Gulfian, has accomplished the commercial applications of expansion pipe first in the world by Enventure company.Expansion pipe is a kind of metal steel pipe with good plasticity, can be widely used in the operation process such as drilling well, completion, oil recovery and well workover, and be the great technological change of 21 century petroleum drilling and mining industry.The inflatable sleeves Manifold technology; Be exactly to pass through in the down-hole with the past radial swelling of well casing (expansion pipe); Its inside and outside footpath is enlarged, realize using the sleeve pipe of same size to replace existing multi-level sleeve pipe, to improve the drilling ability of a plurality of bad grounds of reply; Improve job success ratio, reduce drilling cost.The birth of this technology; Make and to reduce to reach bottom line by what be lowered to the size of the hole that tubing string caused in the well; Thereby make more traditionally can't the economic exploitation the deep-seated oil gas reservoir be able to exploitation; Greatly reduce the cost of development of such fld, can greatly reduce oil gas well shaft building cost simultaneously, according to statistics; Adopt this technology can reduce by 44% drilling fluid consumption, 42% cement consumption, 38% sleeve pipe consumption and 59% the drilling cuttings growing amount (Yang Chuanyong. the development and the application of external inflatable sleeves Manifold technology. petroleum machinery .2006,34 (10): 74-76).Since coming out, bulged tube technology has worldwide obtained vigorous growth, and being lowered to length constantly increases, and process means is constantly progressive.At present, the Duo Jia oil company has all used this technology in the world.For example: (the Peng Zaimei such as Enventure company, Halliburton Company, baker oil tool company, Schlumberger company and READ well services company that Wei Fude company, shell and Halliburton are joint; Zhao Xu; Dou Shubai; Deng. the general situation of development of external inflatable sleeves Manifold technology. welded tube .2010,33 (6): 5-9).China began to introduce the inflatable sleeves Manifold technology in 2000, for this Study on Technology, still was in the starting stage at present.Aspect the trial-production and performance study of expansion pipe material, domestic Xi'an Petroleum University, University Of Tianjin and Shanghai shape memory ltd have all developed inflatable tubing and have tested; Aspect the test of going into the well of inflatable sleeves Manifold technology (Li Zuohui. expansion pipe Study on Key Technique and first Application. oil drilling technology; 2004; 26 (3): 17-18); On January 7th, 1 2004 on December 5th, 2003, the practical expandable sleeve of Φ 107.95mm * 6.35mm that units such as Shengli Oil Field drilling technology research institute have adopted Envebture company to produce at T61-C162 well and W14C20 well, the back cementing quality that expands has all reached good; Two mouthfuls of wells are ordinary production always so far, remarkable benefit.Comprehensive above information is not difficult to find out, in the application of reality; Inflatable sleeves Manifold technology technology is advanced, reliable and economical; The exploitation of bulged tube technology will further promote the product restructuring in China HEW welded tube field, is tool great technological change with broad prospects for development.
According to the general operation or work standard in oil field, the external diameter of expansion pipe before expansion can not surpass 118mm.Therefore, in order to reduce of the influence of expansion pipe construction back, need to use to have expansion pipe, but, must reduce the wall thickness of expansion pipe if improve the interior latus rectum of expansion pipe than the imperial palace latus rectum to oil offtake and down-hole difficulty of construction.For general material, the expansion pipe wall thickness is directly proportional with the intensity that body can reach, and sacrifices the intensity that wall thickness will certainly reduce body.Appearance with P110 grade of steel higher level expansion pipe of HS, high-ductility has well solved the problems referred to above; Therefore; Through the thermal treatment process of composition reasonable in design, formulation optimization, and realize that the production domesticization of P110 grade of steel expansion pipe is of great practical significance.
Make a general survey of current P110 grade of steel expansion pipe composition and relevant production technique; Produce the high grade of steel expansion pipe of taking into account good use properties, military service performance and three aspects of low production cost; Being the maximum difficult point of researching and developing in this field, also is simultaneously one of bottleneck of the high grade of steel expansion pipe of restriction P110 drilling technique development.For example; Publication number is the Chinese patent of CN 101353949A, has added precious metals such as a large amount of Cr, Ni in the composition the inside, and the cost of alloy of raw material is very high; In addition, this patent is not mentioned performances such as the vital impact property of expansion pipe over-all properties, uniform elongation and yield tensile ratios; The patent No. is the Chinese patent of CN 101144141A for special Japanese Patent and the publication number of opening 2003-105441; The alloying constituent the inside has also added the above Cr of 11wt %; Cause the production cost of expansion pipe higher; In addition, above-mentioned patent all specifies for the key propertys such as impact property, uniform elongation and yield tensile ratio of expansion pipe.The cost of alloy of above-mentioned patent raw material is higher, has promoted the cost of expansion pipe drilling technique, is unfavorable for the popularization and the development of the high grade of steel bulged tube technology of P110.
In recent years, Q&P (quenching and Partitioning, quenching-distribution) steel has received the extensive concern of international community because of good mechanical properties such as HS that himself had and high-plasticities.Characteristics such as intensity height, good-extensibility, the impelling strength that the steel that utilize Q&P two steps processing to be obtained have is good make it become nova dazzling in the field of iron and steel.Existing research has all been put down in writing the method for utilizing Q&P two step to handle to obtain high-strength, high-ductility, high-toughness steel like " M.J.Santofimia, T.Nguyen-Minh, L.Zhao; R.Petrov, I.Sabirov, J.Sietsma.New low carbon Q&P steel containing film-like intercritical ferrite, Mater Sci Eng A; 2010,527,6429-6439 " and " H.Y.Li; X.W.Lu, X.C.Wu, Y.A.Min; X.J.Jin. Bainitic transformation during the two-step quenching and partitioning process in a medium carbon steel containing silicon, Mater Sci Eng A, 2010; 527,6255-6259 ", and its technical process is: air cooling to room temperature → partial austenitizing → quenching → partition (being equal to low-temperaturetempering) behind hot rolling → roll bending → quenching; Be about to again with the steel partial austenitizing, be as cold as Ms-M then soon after the steel hot rolling
fFinally obtain by the martensite of lath-shaped between the point, be distributed in the inferior temperature ferritic of the film like between its lath and have the polyphase structure structure that the residual austenite of higher stability is formed.Wherein, Ms is that steel supercooled austenite in quenching process begins to change into martensitic temperature; Factors such as the stressed condition of the carbon content of this critical temperature and steel, the height of alloy element component, austenite grain size, speed of cooling, steel and plastic deformation are relevant, M
fEnd temp for martensitic transformation.These two temperature all can be done temperature-thermal expansion curve to relevant steel through the DIL805A quenching dilatometer that the hot analysis of German Baehr company produces and obtain.It is moderate that publication number is CN101775470A, name is called the alloying element content of several types of Q&P steel of being mentioned in the Chinese invention patent of " working method of low-alloy complex-phase (Q and P) steel "; Uniform elongation and elongation after fracture two-value are all higher; Reached 19% and 32% respectively; Tensile strength and ys have reached 605MPa and 810MPa respectively, and its strength and ductility product has reached 25920MPa%, have realized the two advantageously combined of intensity and plasticity.
In sum; From save energy, reduce cost, further improve intensity, plasticity and the weldableness of steel; Thereby improve the Application Areas equal angles consideration that the comprehensive properties of rolled steel index is widened the Q&P steel; Be necessary the links such as selection, preparation and processing treatment of existing Q&P steel technology and expansion pipe are combined, adopting cheap low Carbon Manganese silicon steel or low Carbon Manganese sial steel is that starting material are made expansion pipe, simplifies the material alloys composition; Few with even not using rare precious metal of China and rare metal, with the Weldability that improves tubing and reduce the tubing cost; Use the Q&P treatment process after improving that expansion pipe is handled; Improve the over-all properties of expansion pipe; Make its performance meet or exceed the P110 level expansion pipe standard of API, thereby realize the production domesticization of the high-strength expansion pipe of P110 grade of steel, will be of great practical significance.
Summary of the invention
The objective of the invention is to propose a kind ofly have higher hole enlargement ability and than the composition design and the thermal treatment process of the P110 grade of steel expansion pipe of lower production cost; Obtain P110 grade of steel expansion tube steel through rational alloy designs than lower production cost; And, alloy sheets carrying out roll bending processing through smelting, rolling acquisition associated alloys plate, expansion pipe is processed in welding then; Handling through quenching after the complete austenitizing and follow-up inferior temperature tempering-quenching-partition at last, totally two cover operations make expansion pipe tubing reach the strength criterion and the plastic deformation ability of expection; Guarantee that the mechanical property before and after the tubing expansion all can satisfy the regulation of API and other related standards, thereby new P110 grade of steel expansion pipe is being waited under the mode of tube reducing by force, bigger viscous deformation takes place; Make tubing obtain bigger interior latus rectum; Final body is reduced at wall thickness that self still can keep higher intensity under a lot of situation, thereby solves the small walled of existing expansion pipe and the contradiction between the HS, realizes the production domesticization of P110 grade of steel higher level expansion pipe; Improve the integral level that China's welded tube is made, the development of China Petroleum is also had important practical significance.
A kind of oil and gas exploitation comprises following composition with P110 level expansion pipe:
The C of 0.1wt% ~ 0.3 wt%;
0.70 the Mn of wt% ~ 2.0 wt%;
0.3 the Si of wt% ~ 1.5 wt%;
The Al of 0 wt% ~ 1.0 wt%;
0.02 the Nb of wt% ~ 0.1 wt%;
The Ti of 0wt% ~ 0.02wt%;
The S of 0wt% ~ 0.01wt%;
The P of 0wt% ~ 0.015wt%;
Surplus is Fe.
Preferably, comprising:
The C of 0.15wt% ~ 0.25wt%;
The Mn of 1.5wt% ~ 2.0%;
The Si of 1.0wt% ~ 1.5wt%;
0.3 the Al of wt% ~ 1.0 wt%;
0.05 the Nb of wt% ~ 0.1 wt%;
The Ti of 0.01wt% ~ 0.02wt%;
Surplus is Fe.
Preferably, said unavoidable impurities is:
The S of 0wt% ~ 0.005wt%;
The P of 0wt% ~ 0.015wt%.
The present invention also provides a kind of preparation method of P110 grade of steel expansion pipe, comprising:
1) casts and the rolled alloy plate according to the composition of said expansion pipe;
2) the said alloy sheets of step 1) is carried out roll bending processing, expansion pipe is processed in welding then;
3) with step 2) said expansion pipe inserts and carries out normalizing treatment in the resistance-type process furnace; Be heated to design temperature and be incubated the enough time with the rate of heating of 5 ℃/s and make it complete austenitizing; After expansion pipe is quenched rapidly in the water of normal temperature attitude (cooling rate be approximately 60 ℃/s) quench to room temperature, make tubing obtain complete martensite (quenching technology fully);
The expansion pipe that 4) will pass through the step 3) quench treatment places the resistance-type process furnace once more, is heated to T with the rate of heating of 5 ℃/s
1~ T
2Between inferior warm area (two-phase region), T wherein
1=A
C3-50 ℃, T
2=A
C1~ A
C1+ 10 ℃, A
C3For steel just is converted into austenitic transformation temperature, A from perlite fully when balance heats
C1For the temperature of perlite when the austenitic transformation just takes place when balance heats steel, when tubing reached design temperature, the insulation time enough made tubing tissue generation partial austenitizing (inferior temperature tempering process); Setting holding temperature is 750 ℃ ~ 780 ℃, and soaking time is 15min;
5) expansion pipe being quenched in the liquid quenching medium for the first time, (can consider to adopt online spray quench, cooling rate is approximately 30 ℃/s ~ 60 ℃/s), make the temperature of tubing reach T
3~ T
4Between temperature range, wherein: T
3Be lower than Ms point, T
4Be higher than M
fPoint, Ms are that steel supercooled austenite in quenching process begins to change into martensitic temperature, M
fBe the end temp of martensitic transformation, the shrend final temperature is 300 ℃ ~ 320 ℃; According to the height of quenching temperature, the austenite that different ratios will be arranged is to martensitic transformation;
6) expansion pipe being placed furnace temperature rapidly once more is T
5(T
5Between 350 ℃ ~ 450 ℃) the resistance-type process furnace in, under this temperature, be incubated 300 ~ 900s, carbon is diffused in the austenite by martensite, makes the rich carbon of austenite;
7) last, expansion pipe is taken out air cooling or shrend to room temperature from stove, acquisition is high-strength by heterogeneous, the multiple dimensioned organizational composition low-alloy of the nano level carbonization thing that martensite, ferritic, rich carbon residual austenite and disperse are separated out, high-ductility, high plastic-steel expansion pipe.
Step 5), 6), 7) close and be called quenching-partition technology.
Further; Step 5) and 6) do not surpass 5s the pitch time between; In order to avoid that part of residual austenite that is able in the quenching process to keep because of the tubing temperature descends too much can't stable existence, finally be converted into martensite or bainite and cause follow-up partition process failure.
According to the present invention, said to said alloy sheets being carried out roll bending processing, welding is processed expansion pipe and is preferably then:
Inside and outside weld seam burr place to expansion pipe in welding process carries out grinder buffing, deburring.
According to the present invention, said heating and the holding temperature that said expansion pipe is carried out normalizing treatment is preferably 900 ℃ ~ 920 ℃, and soaking time is preferably 30min, and said liquid quenching medium is the polyvinyl alcohol water solution of water, oil or different concns (2% ~ 10%).
The embodiment of the invention discloses a kind of brand-new P110 grade of steel expansion pipe, the effect of each main chemical compositions is specially:
Carbon content is to final austenite, martensitic carbon content and volume(tric)fraction important influence in the steel.Only guaranteed have enough carbon, just can form enough rich carbon residual austenites and can stablize to room temperature.In a certain quenching temperature, along with the increase of carbon content, austenitic volume(tric)fraction is increasing.Can reduce transformation temperature when carbon content is higher, present the nanometer grade thickness tissue, the performance of steel is optimized.But when carbon content during greater than 0.5wt%, the welding property variation quenching fragility and martensite fragility can obviously appear.Should select rational carbon content, when guaranteeing that enough residual austenites are arranged, avoid Fe
3C forms the fragility that causes, and improves welding property.
Add manganese and can reduce martensite transformation temperature Ms, increase the content of residual austenite, manganese is little to the toughness influence of steel plate simultaneously, when the manganese that contains 1.5%～2.5% in the steel, can also improve the drag that residual austenite is decomposed effectively.But the manganese (> 2.5% of too many content) stability of residual austenite is improved greatly, residual austenite can not undergo phase transition yet when consequently having higher viscous deformation, and is unfavorable to the ductility that improves workpiece; The increase of manganese content can make that banded structure increases in the steel plate in addition.And preserving after the thermal treatment down, can contain a certain amount of ground banded structure in the final steel plate, and bainite, martensite etc. are assembled in banded structure firmly, make the fragility increase of steel plate, plasticity reduction, mechanical properties decrease.The content of manganese depends on intensity rank. common intensity is during from 590MPa to 780MPa, and the content of manganese is 1.0% to 1.8%, and manganese content is generally between l%～2% usually.
Silicon does not add as alloying element usually, and it plays auxiliary desoxydatoin in the conventional content scope, and content is little to the mechanical property contribution less than 1% o'clock.When Si exist with the form of sosoloid with austenite in the time, can improve the intensity and the hardness of steel, its effect is better than Mn, Ni, Cr, V, Mo etc.Si is as non-carbide forming element, and the solubleness in carbide is extremely low, in Q&P steel isothermal process, and can strongly inhibited Fe
3The formation of C further accumulates in the austenite that does not change carbon, impels martensite to begin transition temperature M
SReduce to below the room temperature, form the residual austenite of rich carbon.When alloy austenite is transformed into bainite, equal the content of austenite interalloy element at the content of formed carbide interalloy element, this is illustrated in the bainite forming process, and redistributing of alloying element do not taken place.Add the element that does not form carbide, like Si, the formation of carbide when stoping bainite transformation owing to it is strong impels not change the rich carbon of part austenite, thereby postpones the formation of bainite.
Aluminium is the same with silicon,, also be the expense carbide forming element, can strongly inhibited Fe
3The formation of C makes not change the rich carbon of austenite.Though the solid solution strengthening effect of aluminium is weaker than silicon, in the Q&P steel, can add aluminium element to reduce the spinoff of silicon.In addition, adopt aluminium not influence the coating and the weldprocedure of steel, so in the steel that requires coating and welding, use aluminium substitution silicon always for silicon.
Niobium ability crystal grain thinning and the superheated susceptivity and the temper brittleness that reduce steel improve intensity, but plasticity and toughness descend to some extent.In ordinary low-alloy steel, add niobium, can improve anti-hydrogen under weather-resistant and the high temperature, nitrogen, ammonia corrosion ability.Niobium can improve welding property.In austenitic stainless steel, add niobium, can prevent the intergranular corrosion phenomenon.
Titanium is the strong carbide forming element, and it all has extremely strong avidity with N, O, C.In addition, the avidity of titanium and S is greater than the avidity of Fe and S, and therefore the preferential titanium sulfide that generates in containing the Ti steel has reduced the probability that generates iron sulphide, can reduce the red brittleness of steel.The carbide bonding force that Ti and C form is extremely strong, stabilizer pole, be difficult for decomposing, and has only when Heating temperature to reach 1 000 C when above, just begins to dissolve in lentamente in the sosoloid, and before dissolving the people, the TiC particulate has the grow up effect of alligatoring of prevention crystalline grain of steel.Ti is as lively as a cricket metallic element, and Ti can also generate the carbide particle of indissoluble with Fe and C, is enriched in the crystal boundary place of steel, stops the grain coarsening of steel, Ti also can dissolve people γ and α mutually in, form sosoloid, make steel produce reinforcement.The add-on of Ti should be greater than 0.025% in the general steel.The TiC particle that a large amount of disperses that in the solidification of molten steel process, form distribute; Solid nucleus in the time of can becoming solidification of molten steel is beneficial to the crystallization of steel, the tissue of refinement steel; Reduce the generation of thick column crystal and treeing, can reduce segregation and reduce the banded structure rank.In addition, Ti also can combine with N to generate stable high diffusive compound, and Ti can also slow down perlite to austenitic transition process.
Unavoidable impurities is preferably S and P
Sulphur also is the harmful element in the steel under general situation, when the higher steel of sulfur-bearing at high temperature carries out press working, and embrittlement easily; Usually be called red brittleness; Can reduce the ductility and the toughness of steel, forge and causing crackle easily when rolling, simultaneously; Sulphur is returned the corrosion resistance that reduces steel, worsens the welding property of steel.The content of sulphur is preferably 0wt% ~ 0.01 wt% among the present invention.
Under the usual condition, phosphorus is the harmful alloying element in the steel, can separate out at the crystal boundary place when phosphorus content in the steel surpasses certain value; Destroy grain-boundary strength, damage its ductility, the plasticity-of steel and toughness are obviously descended; Such situation is particularly serious at low temperatures, and this phenomenon is called cold shortness, and too high phosphorus content can make the welding property of steel degenerate; Reduce the plasticity of steel simultaneously, its cold-bending property is degenerated.The content of phosphorus is preferably 0wt% ~ 0.015 wt% among the present invention.
Working method of the present invention obtains the martensite original structure of lath-shaped through carrying out shrend with after the tubing complete austenitizing, then steel pipe is heated to inferior warm area (two-phase region) and carries out temper.In temperature humidity province, Asia, because Heating temperature is lower, austenite crystal is difficult to grow up; In addition, because soaking time is shorter, part will take place and decompose in the former primary state martensite under this temperature in the steel, reverse to become austenite and acicular ferritic structure; In the reverse transformation process, austenite is the forming core at the crystal boundary place not only, but also forms the needle-like austenite at the boundary of lath martensite, thereby makes the tissue of steel obtain further refinement.In addition, after this quenching-distribution process also further impels the rich carbon of the austenite that in the temperature process of Asia, forms.Through detecting; The heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel that the inventive method is produced is being except existing between the martensite lath the part needle-like residual austenite, at the crystal boundary place and ferrite crystal grain inside also exist part particulate state residual austenite.Because soft phase residual austenite is plain DEFORMATION INDUCED transformation plasticity (Trip) effect that produces in phase transition process; The heterogeneous high uniformly extension low alloy steel that obtains has higher plasticity than existing conventional Q&P steel; And because martensite but not the existence of bainite; And the precipitation strength effect of the carbide of Nb, Ti etc. in the matrix, the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel that the inventive method is produced has than higher intensity and the improved comprehensive mechanical performance of DEFORMATION INDUCED transformation plasticity (Trip) steel.
The present invention is according to the chemical ingredients of tubing itself, changes heterogeneous, the multiple dimensioned tissue of the nano level carbonization thing that martensite, ferritic, rich carbon residual austenite and disperse that primary quenching temperature and isothermal temperature and time obtains different relative contents separate out.In addition, according to the needs of tubing purposes, can select suitable inferior warm area (two-phase region) holding temperature, quenching temperature and partition temperature, in the hope of obtaining optimized polyphase structure proportioning.
The present invention is applicable to the steel alloy of elements such as containing manganese, silicon, aluminium, niobium, titanium.
The present invention is according to the principle of intercritical hardening and carbon partition; Proposed to contain the intercritical hardening and the carbon partition technology of the micro-alloyed steel of elements such as manganese, silicon, aluminium, niobium, titanium, made the method for complete austenitizing quenchings-Ya Wen tempering-quenching-partition processing of heterogeneous, the multiple dimensioned tissue of nano level carbonization thing that welded tube obtains to be separated out by martensite, ferritic, rich carbon residual austenite and disperse.Compare with traditional modified (+550 ℃ of high tempering 30min quench after 900 ℃ of complete austenitizings) technology; The steel of identical component is through intercritical hardening and carbon partition art breading; Impelling strength can improve 100%, and uniform elongation and elongation after fracture can improve 200% and 75% respectively; Compare with the Trip steel, the steel of identical component is handled ys and tensile strength and can be improved 39% and 18% respectively through intercritical hardening and carbon partition technology.During between the two balance of intensity and the plasticity of considering steel at the same time, intercritical hardening and carbon partition technology are suitable selections.
In conjunction with quenching and follow-up inferior temperature tempering-quenching-partition treatment process after the complete austenitizing; The invention provides a kind of composition design and thermal treatment process of novel P110 grade of steel expansion pipe; It is characterized in that the composition of said expansion pipe is: the C of 0.1 wt% ~ 0.3 wt%; 0.70 the Mn of wt% ~ 2.0 wt%; 0.3 the Si of wt% ~ 1.5 wt%; The Al of 0 wt% ~ 1.0 wt%; 0.02 the Nb of wt% ~ 0.1 wt%; The Ti of 0wt% ~ 0.02wt%; The S of 0wt% ~ 0.01 wt%; The P of 0wt% ~ 0.015 wt%; Surplus is Fe.According to composition of the present invention and the prepared expansion pipe of thermal treatment process have that alloying element is few, alloy content is low, intensity is high, good percentage elongation, low cost and other advantages, existing cost is high in the expansion pipe manufacturing in the past, welding property is poor, the back intensity that expands is difficult to technical barriers such as assurance thereby solved.
Description of drawings
Fig. 1 (a), Fig. 1 (b) be in the expansion pipe working method of the present invention the thermal treatment process temperature and time concern synoptic diagram, Fig. 1 (a) is complete quenching technology, Fig. 1 (b) is follow-up inferior temperature tempering-quenching-partition treatment process, T
1=A
C3-50 ℃, T
2=A
C1~ A
C1+ 10 ℃, T
3=Ms-40 ℃, T
4=Mf+50 ℃, T
5=350 ℃ ~ 450 ℃;
Fig. 2 is the metallographic microstructure picture of the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 1;
Fig. 3 is SEM (ESEM) photo of the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 1;
Fig. 4 is the X-ray diffraction synoptic diagram as a result of residual austenite in the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 1;
Fig. 5 is the EBSD analytical results that residual austenite distributes in the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 1, and the white thing in the photo is residual austenite mutually;
Fig. 6 is the metallographic microstructure picture of the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 2;
Fig. 7 is the metallographic microstructure picture of the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 3;
Fig. 8 is the metallographic microstructure picture of the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 4;
Fig. 9 is the metallographic microstructure picture of the heterogeneous high uniformly extension low-alloy expansion tube steel of P110 grade of steel produced of inventive embodiments 5.
Embodiment
Below will in the embodiment of the invention technical scheme carry out clear, complete description, obviously, described embodiment only is a part very little among the present invention, rather than whole embodiment.Based on the embodiment among the present invention, those of ordinary skills are not making the every other embodiment that is obtained under the creative work prerequisite, all belong to the scope of the present invention's protection.
Below in conjunction with accompanying drawing and concrete embodiment the composition and the working method thereof of the novel low-alloy polyphase structure of P110 grade of steel of the present invention expansion pipe are made further detailed description.
Embodiment 1
Select for use the chemical component weight per-cent of starting material steel following:
C：0.15wt%~0.25wt%；Mn：1.5wt%~2.0%；Si：1.0wt%~1.5wt%；Al：0.3?wt%~1.0?wt%；Nb：0.05?wt%~0.1?wt%；Ti：0.01wt%~0.02?wt%；S：0wt%~0.01?wt%；P：0wt%~0.015wt%。
Preferred composition is: C:0.18 wt% ~ 0.25wt%, Mn:1.5wt% ~ 2.0 wt%, Si:1.0wt% ~ 1.5wt%, Al:0.3 wt% ~ 1.0 wt%, Nb:0.1 wt%, Ti:0.02wt%, S:0.0075 wt%, P:0.0060wt%, surplus is Fe and unavoidable impurities.
Production stage after preferred is following:
1) casts and the rolled alloy plate according to the composition of the said expansion pipe of technique scheme;
2) said alloy sheets is carried out roll bending processing, expansion pipe is processed in welding then;
3) said expansion pipe is inserted carry out normalizing treatment in the resistance-type process furnace; Be heated to design temperature and be incubated the enough time with the rate of heating of 5 ℃/s and make it complete austenitizing; The mode of online spray quench is adopted in the back; Expansion pipe is quenched rapidly in the water of normal temperature attitude (cooling rate be approximately 60 ℃/s) quench to room temperature, make tubing obtain complete martensite (quenching technology fully);
The expansion pipe that 4) will pass through quench treatment places the resistance-type process furnace once more, is heated to 760 ~ 780 ℃ inferior warm area (two-phase region) with the rate of heating of 5 ℃/s, the time chien shih tubing tissue generation partial austenitizing (inferior temperature tempering process) of insulation 900s;
5) mode of the online spray quench of employing; The expansion pipe cooling rate of quenching for the first time is approximately in the 40 ℃/s liquid quenching medium; Make the temperature of tubing reach the temperature range between 300 ~ 320 ℃; Placing rapidly furnace temperature then immediately once more is 400 ℃ resistance-type process furnace, under this temperature, is incubated 900s, then water-cooled to room temperature (quenching-partition technology).
Through test, the tensile strength of expansion pipe tubing is 1030MPa ~ 1100MPa, and ys is 770MPa ~ 800MPa, and uniform elongation is 17% ~ 21%, and breaking elongation is 27% ~ 30%.In the time of 0 ℃, horizontal full-scale ballistic work is 56J ~ 65J, and vertical full-scale ballistic work is 87J ~ 96J.
Embodiment 2
The chemical ingredients of selecting the starting material steel for use is with the preferred component among the embodiment 1:
Production stage after preferred is following:
1) casts and the rolled alloy plate according to the composition of the said expansion pipe of technique scheme;
2) said alloy sheets is carried out roll bending processing, expansion pipe is processed in welding then;
3) said expansion pipe is inserted carry out normalizing treatment in the resistance-type process furnace; Be heated to design temperature and be incubated the enough time with the rate of heating of 5 ℃/s and make it complete austenitizing; The mode of online spray quench is adopted in the back; Expansion pipe is quenched rapidly in the water of normal temperature attitude (cooling rate be approximately 60 ℃/s) quench to room temperature, make tubing obtain complete martensite (quenching technology fully);
The expansion pipe that 4) will pass through quench treatment places the resistance-type process furnace once more, is heated to 760 ~ 780 ℃ inferior warm area (two-phase region) with the rate of heating of 5 ℃/s, the time chien shih tubing tissue generation partial austenitizing (inferior temperature tempering process) of insulation 900s;
5) mode of the online spray quench of employing; The expansion pipe cooling rate of quenching for the first time is approximately in the 40 ℃/s liquid quenching medium; Make the temperature of tubing reach the temperature range between 300 ~ 320 ℃; Placing rapidly furnace temperature then immediately once more is 400 ℃ resistance-type process furnace, under this temperature, is incubated 300s, then water-cooled to room temperature (quenching-partition technology).
Through test, the tensile strength of expansion pipe tubing is 1036MPa ~ 1065MPa, and ys is 780MPa ~ 810MPa, and uniform elongation is 20% ~ 22%, and breaking elongation is 28 % ~ 31%.In the time of 0 ℃, horizontal full-scale ballistic work is 55J ~ 62J, and vertical full-scale ballistic work is 80J ~ 87J.
Embodiment 3
The chemical ingredients of selecting the starting material steel for use is with the preferred component among the embodiment 1:
Production stage after preferred is following:
1) casts and the rolled alloy plate according to the composition of the said expansion pipe of technique scheme;
2) said alloy sheets is carried out roll bending processing, expansion pipe is processed in welding then;
3) said expansion pipe is inserted carry out normalizing treatment in the resistance-type process furnace; Be heated to design temperature and be incubated the enough time with the rate of heating of 5 ℃/s and make it complete austenitizing; The mode of online spray quench is adopted in the back; Expansion pipe is quenched rapidly in the water of normal temperature attitude (cooling rate be approximately 60 ℃/s) quench to room temperature, make tubing obtain complete martensite (quenching technology fully);
The expansion pipe that 4) will pass through quench treatment places the resistance-type process furnace once more, is heated to 760 ~ 780 ℃ inferior warm area (two-phase region) with the rate of heating of 5 ℃/s, the time chien shih tubing tissue generation partial austenitizing (inferior temperature tempering process) of insulation 900s;
5) mode of the online spray quench of employing; The expansion pipe cooling rate of quenching for the first time is approximately in the 40 ℃/s liquid quenching medium; Make the temperature of tubing reach the temperature range between 300 ~ 320 ℃; Placing rapidly furnace temperature then immediately once more is 400 ℃ resistance-type process furnace, under this temperature, is incubated 900s, then air cooling to room temperature (quenching-partition technology).
Through test, the tensile strength of expansion pipe tubing is 1016MPa ~ 1018MPa, and ys is 760MPa ~ 782MPa, and uniform elongation is 25% ~ 27%, and breaking elongation is 33% ~ 34%.In the time of 0 ℃, horizontal full-scale ballistic work is 52J ~ 61J, and vertical full-scale ballistic work is 92J ~ 108J.
Embodiment 4
The chemical ingredients of selecting the starting material steel for use is with the preferred component among the embodiment 1:
Production stage after preferred is following:
1) casts and the rolled alloy plate according to the composition of the said expansion pipe of technique scheme;
2) said alloy sheets is carried out roll bending processing, expansion pipe is processed in welding then;
3) said expansion pipe is inserted carry out normalizing treatment in the resistance-type process furnace; Be heated to design temperature and be incubated the enough time with the rate of heating of 5 ℃/s and make it complete austenitizing; The mode of online spray quench is adopted in the back; Expansion pipe is quenched rapidly in the water of normal temperature attitude (cooling rate be approximately 60 ℃/s) quench to room temperature, make tubing obtain complete martensite (quenching technology fully);
The expansion pipe that 4) will pass through quench treatment places the resistance-type process furnace once more, is heated to 760 ~ 780 ℃ inferior warm area (two-phase region) with the rate of heating of 5 ℃/s, the time chien shih tubing tissue generation partial austenitizing (inferior temperature tempering process) of insulation 900s;
5) mode of the online spray quench of employing; The expansion pipe cooling rate of quenching for the first time is approximately in the 40 ℃/s liquid quenching medium; Make the temperature of tubing reach the temperature range between 300 ~ 320 ℃; Placing rapidly furnace temperature then immediately once more is 400 ℃ resistance-type process furnace, under this temperature, is incubated 480s, then air cooling to room temperature (quenching-partition technology).
Through test, the tensile strength of expansion pipe tubing is 1016MPa ~ 1020MPa, and ys is 768MPa ~ 785MPa, and uniform elongation is 20% ~ 21%, and breaking elongation is 28% ~ 30%.In the time of 0 ℃, horizontal full-scale ballistic work is 52J ~ 58J, and vertical full-scale ballistic work is 84J ~ 92J.
Embodiment 5
The chemical ingredients of selecting the starting material steel for use is with the preferred component among the embodiment 1:
Production stage after preferred is following:
1) casts and the rolled alloy plate according to the composition of the said expansion pipe of technique scheme;
2) said alloy sheets is carried out roll bending processing, expansion pipe is processed in welding then;
3) said expansion pipe is inserted carry out normalizing treatment in the resistance-type process furnace; Be heated to design temperature and be incubated the enough time with the rate of heating of 5 ℃/s and make it complete austenitizing; The mode of online spray quench is adopted in the back; Expansion pipe is quenched rapidly in the water of normal temperature attitude (cooling rate be approximately 60 ℃/s) quench to room temperature, make tubing obtain complete martensite (quenching technology fully);
The expansion pipe that 4) will pass through quench treatment places the resistance-type process furnace once more, is heated to 750 ℃ ~ 770 ℃ inferior warm area (two-phase region) with the rate of heating of 5 ℃/s, the time chien shih tubing tissue generation partial austenitizing (inferior temperature tempering process) of insulation 900s;
5) mode of the online spray quench of employing; The expansion pipe cooling rate of quenching for the first time is approximately in the 40 ℃/s liquid quenching medium; Make the temperature of tubing reach the temperature range between 300 ~ 320 ℃; Placing rapidly furnace temperature then immediately once more is 400 ℃ resistance-type process furnace, under this temperature, is incubated 300s, then air cooling to room temperature (quenching-partition technology).
Through test, the tensile strength of expansion pipe tubing is 1043MPa ~ 1061MPa, and ys is 762MPa ~ 776MPa, and uniform elongation is 21% ~ 23%, and breaking elongation is 27% ~ 29%.In the time of 0 ℃, horizontal full-scale ballistic work is 50J ~ 57J, and vertical full-scale ballistic work is 80J ~ 86J.
Microstructure analysis to the heterogeneous high uniformly extension low-alloy expansion pipe of the P110 grade of steel of above-mentioned each embodiment is visible; The heterogeneous high uniformly extension low-alloy expansion pipe tissue of P110 grade of steel that this phase art breading of process is crossed demonstrates heterogeneous, the multiple dimensioned weave construction of the nano level carbonization thing of being separated out by martensite, ferritic, rich carbon residual austenite and the disperse of lath-shaped; Through X-ray diffraction the residual austenite in each embodiment steel is tested simultaneously; The result shows that paralympic content is about 8.7% ~ 12.83%.
The ys of the heterogeneous high uniformly extension low-alloy expansion pipe of P110 grade of steel that the inventive method is produced all is not less than 760MPa, and tensile strength all is higher than 1000MPa, and uniform elongation is between 17% ~ 27%; Breaking elongation is between 27% ~ 34%; In the time of 0 ℃, horizontal full-scale ballistic work is between 50J ~ 65J, and vertical full-scale ballistic work is between 80J ~ 108J; Show good intensity and good plasticity, its comprehensive mechanical property is better than conventional quenching-tempered steel, Trip steel and Q&P steel.
Claims (5)
1. an oil and gas exploitation is characterized in that the composition quality per-cent of P110 level expansion pipe is: the C of 0.1wt%～0.3 wt% with the preparation method of P110 level expansion pipe; 0.70 the Mn of wt%～2.0 wt%; 0.3 the Si of wt%～1.5 wt%; The Al of 0 wt% ~ 1.0 wt%; 0.02 the Nb of wt% ~ 0.1 wt%; The Ti of 0wt% ~ 0.02wt%; The S of 0wt% ~ 0.01wt%; The P of 0wt% ~ 0.015wt%; Surplus is Fe; Preparation process is following:
1) casts and the rolled alloy plate according to the composition of said expansion pipe;
2) the said alloy sheets of step 1) is carried out roll bending processing, expansion pipe is processed in welding then;
3) with step 2) said expansion pipe inserts and carries out normalizing treatment in the resistance-type process furnace, is heated to design temperature and is incubated the enough time with the rate of heating of 5 ℃/s to make it complete austenitizing; Holding temperature is 900 ℃ ~ 920 ℃, and soaking time is 30min ~ 60min; After expansion pipe is quenched rapidly in the water of normal temperature attitude, cooling rate is that 60 ℃/s quenches to room temperature, makes tubing obtain complete martensite;
The expansion pipe that 4) will pass through the step 3) quench treatment places the resistance-type process furnace once more, is heated to T with the rate of heating of 5 ℃/s
1~ T
2Between inferior warm area, T wherein
1=A
C3-50 ℃, T
2=A
C1~ A
C1+ 10 ℃, A
C3For steel just is converted into austenitic transformation temperature, A from perlite fully when balance heats
C1For the temperature of perlite when the austenitic transformation just takes place when balance heats steel, when tubing reached design temperature, the insulation time enough made tubing tissue generation partial austenitizing; The holding temperature of setting is 750 ℃ ~ 780 ℃, and soaking time is 900s;
5) expansion pipe is quenched in the liquid quenching medium for the first time, adopted online spray quench, cooling rate is 30 ℃/s ~ 60 ℃/s, makes the temperature of tubing reach T
3~ T
4Between temperature range, promptly 300 ℃ ~ 320 ℃, wherein: T
3Be lower than Ms point, T
4Be higher than M
fPoint, Ms are that steel supercooled austenite in quenching process begins to change into martensitic temperature, M
fEnd temp for martensitic transformation; According to the height of quenching temperature, the austenite that different ratios will be arranged is to martensitic transformation;
6) expansion pipe being placed furnace temperature rapidly once more is T
5The resistance-type process furnace in, T
5Between 350 ℃ ~ 450 ℃, under this temperature, be incubated 300s ~ 900s, carbon is diffused in the austenite by martensite, makes the rich carbon of austenite;
7) last, expansion pipe is taken out air cooling or shrend to room temperature from stove, acquisition is high-strength by heterogeneous, the multiple dimensioned organizational composition low-alloy of the nano level carbonization thing that martensite, ferritic, rich carbon residual austenite and disperse are separated out, high-ductility, high plastic-steel expansion pipe.
2. a kind of oil and gas exploitation according to claim 1 is characterized in that the composition quality per-cent of P110 level expansion pipe is: the C of 0.15wt% ~ 0.25wt% with the preparation method of P110 level expansion pipe; The Mn of 1.5wt% ~ 2.0%; The Si of 1.0wt% ~ 1.5wt%; 0.3 the Al of wt% ~ 1.0 wt%; 0.05 the Nb of wt% ~ 0.1 wt%; The Ti of 0.01wt% ~ 0.02wt%; The S of 0 wt% ~ 0.005 wt%; The P of 0wt% ~ 0.015 wt%; All the other are Fe.
3. a kind of oil and gas exploitation according to claim 1 and 2 is characterized in that with the preparation method of P110 level expansion pipe the P110 grade of steel expansion pipe tubing index after heat treatment of gained is: ys Da Dao ≧ 760MPa; The Kang of tubing draws Qiang Du ≧ 1016MPa; The Chang Shuai of Shen ≧ 27% that tubing is total.
4. a kind of oil and gas exploitation according to claim 1 is with the preparation method of P110 level expansion pipe; It is characterized in that; Step 5) and 6) do not surpass 5s the pitch time between; In order to avoid that part of residual austenite that is able in the quenching process to keep because of the tubing temperature descends too much can't stable existence, finally be converted into martensite or bainite and cause follow-up partition process failure.
5. a kind of oil and gas exploitation according to claim 1 is with the preparation method of P110 level expansion pipe; It is characterized in that; To step 2) said alloy sheets carries out roll bending processing; Welding is processed expansion pipe inside and outside weld seam burr place to expansion pipe in welding process and is carried out grinder buffing, deburring then.
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| CN102776333A (en) * | 2012-07-16 | 2012-11-14 | 张家港海锅重型锻件有限公司 | Process for manufacturing 20Mn2 steel forgings |
| CN103334000A (en) * | 2013-06-24 | 2013-10-02 | 山西煤矿机械制造有限责任公司 | Heat-treatment quenching method for mining ring chain |
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| CN103334000B (en) * | 2013-06-24 | 2014-10-29 | 山西煤矿机械制造有限责任公司 | Heat-treatment quenching method for mining ring chain |
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| CN105296864A (en) * | 2015-11-15 | 2016-02-03 | 丹阳市蓝锐粉末合金制品有限公司 | High-speed steel containing carbon |
| CN105619025A (en) * | 2015-12-30 | 2016-06-01 | 浙江吉利汽车研究院有限公司 | Thermoforming method for high-strength fatigue-resisting torsion beam |
| CN107130087B (en) * | 2017-05-31 | 2019-02-12 | 江苏金基特钢有限公司 | A kind of heat treatment process weakening austenitic stainless steel grain-boundary brittleness |
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