CN102534372B - 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 that a kind of oil and gas exploitation is used 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 been subjected to serious restriction, its reason is, original protector string is made up of the sleeve pipe of multiple size, the taper that its hole structure is big up and small down, increase along with well depth, be 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, 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 has been finished the commercial applications of expansion pipe first in the world in the heavy duty service of the ocean in the Gulfian 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 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, what make the size of the hole that caused by the tubing string that is lowered in the well reduces to reach bottom line, thereby make more traditionally can't the economic exploitation the deep-seated oil gas reservoir exploited, greatly reduce the cost of development of such oil-gas field, simultaneously can greatly reduce oil gas well shaft building cost, according to statistics, adopt this technology can reduce by 44% drilling fluid consumption, 42% cement consumption, 38% sleeve pipe consumption and 59% drilling cuttings growing amount (Yang Chuanyong. 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 company limited have all developed inflatable tubing and have tested; Aspect the test of going into the well of inflatable sleeves Manifold technology (Li Zuohui. the research of expansion pipe gordian technique and first Application. oil drilling technology, 2004,26(3): 17-18), on January 7th, 1 2004 on December 5th, 2003, units such as Shengli Oil Field drilling technology research institute have adopted the practical expandable sleeve of Φ 107.95mm * 6.35mm of Envebture company production 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 expansion pipe construction back to the influence of oil offtake and down-hole difficulty of construction, need to use the expansion pipe that has than the imperial palace latus rectum, but if improve the interior latus rectum of expansion pipe, must reduce the wall thickness of expansion pipe.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 high strength, high-ductility has well solved the problems referred to above, therefore, by 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 describes in detail 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 popularization and the development of the high grade of steel bulged tube technology of P110.
In recent years, Q﹠amp; Good mechanical properties such as the high strength that P (quenching and Partitioning quenches-distribute) steel has because of himself and high-plasticity have been subjected to the extensive concern of international community.Utilize Q﹠amp; Characteristics such as intensity height, good-extensibility, the impelling strength that the steel that P two steps processing obtains have is good make it become nova dazzling in the field of iron and steel.Existing research is as " M.J.Santofimia, T.Nguyen-Minh, L.Zhao, R.Petrov, I.Sabirov, J.Sietsma.New low carbon Q﹠amp; 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 " all put down in writing and utilized Q﹠amp; P two step is handled the method that obtains high-strength, high-ductility, high-toughness steel, its technical process is: air cooling is to room temperature → partial austenitizing → quenching → partition (being equal to low-temperaturetempering) → quenching behind hot rolling → roll bending, 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 ferrite 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 by the DIL805A quenching dilatometer that the hot analysis of German Baehr company produces and obtain.Publication number is that CN101775470A, name are called " low-alloy complex phase Q﹠amp; The production method of P steel " Chinese invention patent in a few class Q﹠amp of mentioning; The alloying element content of P steel is moderate, uniform elongation and elongation after fracture two-value are all higher, have reached 19% and 32% respectively, and tensile strength and yield strength have reached 605MPa and 810MPa respectively, its strength and ductility product has reached 25920MPa%, has realized the two fine combination of intensity and plasticity.
In sum, from save energy, reduce cost, further improve intensity, plasticity and the weldability of steel, widen Q﹠amp thereby improve the comprehensive properties of rolled steel index; The Application Areas equal angles of P steel is considered, is necessary existing Q﹠amp; Links such as the selection of P steel technology and expansion pipe, preparation and processing treatment combine, adopting cheap low Carbon Manganese silicon steel or low Carbon Manganese sial steel is that starting material are made expansion pipe, simplify the material alloys composition, few with even not using the rare precious metal of China and rare metal, with the Weldability that improves tubing and reduce the tubing cost; Use the Q﹠amp after improving; The P treatment process is handled expansion pipe, improves the over-all properties of expansion pipe, makes its performance meet or exceed the P110 level expansion pipe standard of API, thereby realizes 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 composition design and the thermal treatment process of the P110 grade of steel expansion pipe of lower production cost, by the P110 grade of steel expansion tube steel of rational alloy designs acquisition than lower production cost, and by smelting, rolling acquisition associated alloys plate, alloy sheets is carried out roll bending processing, expansion pipe is made in welding then, handling by quenching after the complete austenitizing and follow-up inferior temperature tempering-quenching-partition at last, totally two cover operations make expansion pipe tubing reach strength criterion and the plastic deformation ability of expection, guarantee that the mechanical property of tubing expansion front and back 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 situations, thereby the thin-walled that solves existing expansion pipe is thick and high strength between contradiction, realize 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 P110 level expansion pipe comprises following composition:
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, described 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 described expansion pipe;
2) the described alloy sheets of step 1) is carried out roll bending processing, expansion pipe is made in welding then;
3) with step 2) described 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);
4) will place the resistance-type process furnace again through the expansion pipe of step 3) quench treatment, be 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 fully from perlite when balance heats
C1Temperature when when balance heats, just taking place perlite to austenitic transformation for steel, when tubing reached design temperature, the insulation time enough made the tubing tissue that partial austenitizing (inferior temperature tempering process) take place; Setting holding temperature is 750 ℃ ~ 780 ℃, and soaking time is 15min;
5) expansion pipe being quenched for the first time in the liquid quenching medium, (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 of different ratios will be arranged to martensitic transformation;
6) expansion pipe being placed furnace temperature rapidly again 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, ferrite, rich carbon residual austenite and disperse are separated out, high-ductility, high plastic-steel expansion pipe.
Step 5), 6), 7) be collectively referred to as 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 kept in the quenching process 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, described to described alloy sheets being carried out roll bending processing, welding is made 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, described heating and the holding temperature that described expansion pipe is carried out normalizing treatment is preferably 900 ℃ ~ 920 ℃, and soaking time is preferably 30min, and described 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 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 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 under preserving after the thermal treatment, 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 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, at Q﹠amp; In the P steel isothermal process, 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
SBe down 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 shows and in the bainite forming process redistributing of alloying element is not taken place.Add the element that does not form carbide, as 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, at Q﹠amp; In the P steel, can add aluminium element to reduce the side effect of silicon.In addition, adopt aluminium not influence coating and the weldprocedure of steel for silicon, so in the steel that requires coating and welding, use aluminium substitution silicon always.
Superheated susceptivity and the temper brittleness of niobium energy crystal grain thinning and reduction 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 and N, O, C have extremely strong avidity.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 not molten 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 molten people γ with α mutually in, form sosoloid, steel is produced strengthens.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 form in the solidification of molten steel process 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 be combined with N and be generated 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, embrittlement easily, usually be called red brittleness, can reduce 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, plasticity-and the toughness of steel 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.
Production method of the present invention obtains the martensite original structure of lath-shaped by 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 the ferritic structure that becomes austenite and needle-like; In the reverse transformation process, austenite is not only at crystal boundary place forming core, but also forms the needle-like austenite at the boundary of lath martensite, thereby makes the tissue of steel obtain further refinement.In addition, quenching-distribution process after this also further impels the rich carbon of the austenite that forms in the temperature process of Asia.After testing, the heterogeneous height of P110 grade of steel that the inventive method is produced evenly extends low-alloy expansion tube steel 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 transformation plasticity (Trip) effect is brought out in the plain deformation that produces in phase transition process of soft phase residual austenite, the heterogeneous height of acquisition evenly extends low alloy steel than existing conventional Q﹠amp; The P steel has higher plasticity, 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 height of P110 grade of steel that the inventive method is produced evenly extends low-alloy expansion tube steel to have than deformation and brings out higher intensity and the improved comprehensive mechanical performance of 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, ferrite, 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 intercritical hardening and the carbon partition technology of the micro-alloyed steel of elements such as manganese, silicon, aluminium, niobium, titanium, made welded tube obtain the method for complete austenitizing quenchings-Ya Wen tempering-quenching-partition processing of heterogeneous, the multiple dimensioned tissue of the nano level carbonization thing of being separated out by martensite, ferrite, 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 yield strength and tensile strength and can be improved 39% and 18% respectively through intercritical hardening and carbon partition technology.When considering between the two balance of the intensity of steel and plasticity 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 described 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 height in the expansion pipe manufacturing in the past, welding property are 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 production 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 that the heterogeneous height of P110 grade of steel that inventive embodiments 1 is produced evenly extends low-alloy expansion tube steel;
Fig. 3 is the SEM(scanning electron microscope that the heterogeneous height of P110 grade of steel that inventive embodiments 1 is produced evenly extends low-alloy expansion tube steel) photo;
Fig. 4 is the X-ray diffraction result schematic diagram that the heterogeneous height of P110 grade of steel that inventive embodiments 1 is produced evenly extends residual austenite in the low-alloy expansion tube steel;
Fig. 5 is that the heterogeneous height of P110 grade of steel that inventive embodiments 1 is produced evenly extends the EBSD analytical results that residual austenite distributes in the low-alloy expansion tube steel, and the white thing in the photo is residual austenite mutually;
Fig. 6 is the metallographic microstructure picture that the heterogeneous height of P110 grade of steel that inventive embodiments 2 is produced evenly extends low-alloy expansion tube steel;
Fig. 7 is the metallographic microstructure picture that the heterogeneous height of P110 grade of steel that inventive embodiments 3 is produced evenly extends low-alloy expansion tube steel;
Fig. 8 is the metallographic microstructure picture that the heterogeneous height of P110 grade of steel that inventive embodiments 4 is produced evenly extends low-alloy expansion tube steel;
Fig. 9 is the metallographic microstructure picture that the heterogeneous height of P110 grade of steel that inventive embodiments 5 is produced evenly extends low-alloy expansion tube steel.
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 belong to the scope of protection of the invention not making the every other embodiment that obtains under the creative work prerequisite.
Be further detailed below in conjunction with accompanying drawing and specific embodiment composition and the production method thereof to the novel low-alloy polyphase structure of P110 grade of steel of the present invention expansion pipe.
Select for use the chemical component weight per-cent of starting material steel as follows:
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 as follows:
1) casts and the rolled alloy plate according to the composition of the described expansion pipe of technique scheme;
2) described alloy sheets is carried out roll bending processing, expansion pipe is made in welding then;
3) described 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);
4) will place the resistance-type process furnace again through the expansion pipe of quench treatment, be 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 temperature range between 300 ~ 320 ℃, placing rapidly furnace temperature then immediately again is 400 ℃ resistance-type process furnace, be incubated 900s under this temperature, water-cooled is to room temperature (quenching-partition technology) then.
After tested, the tensile strength of expansion pipe tubing is 1030MPa ~ 1100MPa, and yield strength 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 as follows:
1) casts and the rolled alloy plate according to the composition of the described expansion pipe of technique scheme;
2) described alloy sheets is carried out roll bending processing, expansion pipe is made in welding then;
3) described 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);
4) will place the resistance-type process furnace again through the expansion pipe of quench treatment, be 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 temperature range between 300 ~ 320 ℃, placing rapidly furnace temperature then immediately again is 400 ℃ resistance-type process furnace, be incubated 300s under this temperature, water-cooled is to room temperature (quenching-partition technology) then.
After tested, the tensile strength of expansion pipe tubing is 1036MPa ~ 1065MPa, and yield strength 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 as follows:
1) casts and the rolled alloy plate according to the composition of the described expansion pipe of technique scheme;
2) described alloy sheets is carried out roll bending processing, expansion pipe is made in welding then;
3) described 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);
4) will place the resistance-type process furnace again through the expansion pipe of quench treatment, be 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 temperature range between 300 ~ 320 ℃, placing rapidly furnace temperature then immediately again is 400 ℃ resistance-type process furnace, be incubated 900s under this temperature, air cooling is to room temperature (quenching-partition technology) then.
After tested, the tensile strength of expansion pipe tubing is 1016MPa ~ 1018MPa, and yield strength 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 as follows:
1) casts and the rolled alloy plate according to the composition of the described expansion pipe of technique scheme;
2) described alloy sheets is carried out roll bending processing, expansion pipe is made in welding then;
3) described 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);
4) will place the resistance-type process furnace again through the expansion pipe of quench treatment, be 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 temperature range between 300 ~ 320 ℃, placing rapidly furnace temperature then immediately again is 400 ℃ resistance-type process furnace, be incubated 480s under this temperature, air cooling is to room temperature (quenching-partition technology) then.
After tested, the tensile strength of expansion pipe tubing is 1016MPa ~ 1020MPa, and yield strength 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.
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 as follows:
1) casts and the rolled alloy plate according to the composition of the described expansion pipe of technique scheme;
2) described alloy sheets is carried out roll bending processing, expansion pipe is made in welding then;
3) described 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);
4) will place the resistance-type process furnace again through the expansion pipe of quench treatment, be 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 temperature range between 300 ~ 320 ℃, placing rapidly furnace temperature then immediately again is 400 ℃ resistance-type process furnace, be incubated 300s under this temperature, air cooling is to room temperature (quenching-partition technology) then.
After tested, the tensile strength of expansion pipe tubing is 1043MPa ~ 1061MPa, and yield strength 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.
The microstructure analysis that the heterogeneous height of P110 grade of steel of the various embodiments described above is evenly extended the low-alloy expansion pipe as seen, the heterogeneous height of crossing through this phase art breading of P110 grade of steel evenly extends heterogeneous, the multiple dimensioned weave construction that low-alloy expansion pipe tissue presents the nano level carbonization thing of being separated out by martensite, ferrite, rich carbon residual austenite and the disperse of lath-shaped, by 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 yield strength that the heterogeneous height of P110 grade of steel that the inventive method is produced evenly extends the low-alloy expansion pipe all is not less than 760MPa, tensile strength all is higher than 1000MPa, 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﹠amp; The P steel.
Claims (5)
1. the preparation method of an oil and gas exploitation usefulness P110 level expansion pipe is characterized in that the composition quality per-cent of P110 level expansion pipe is: 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; Preparation process is as follows:
1) casts and the rolled alloy plate according to the composition of described expansion pipe;
2) the described alloy sheets of step 1) is carried out roll bending processing, expansion pipe is made in welding then;
3) with step 2) described 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;
4) will place the resistance-type process furnace again through the expansion pipe of step 3) quench treatment, be 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 fully from perlite when balance heats
C1Temperature when when balance heats, just taking place perlite to austenitic transformation for steel, when tubing reached design temperature, the insulation time enough made the tubing tissue that partial austenitizing take place; The holding temperature of setting is 750 ℃ ~ 780 ℃, and soaking time is 900s;
5) during the expansion pipe after will handling through the inferior temperature insulation of step 4) is quenched liquid quenching medium, adopt online spray quench, cooling rate is 30 ℃/s ~ 60 ℃/s, makes the temperature of tubing reach T
3~ T
4Between temperature range, namely 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 of different ratios will be arranged to martensitic transformation;
6) expansion pipe being placed furnace temperature rapidly again 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, ferrite, 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: yield strength reaches 〉=760MPa; Tensile strength 〉=the 1016MPa of tubing, elongation 〉=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 kept in the quenching process 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) described alloy sheets carries out roll bending processing, welding is made 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 |
| 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 |
| CN104532126B (en) * | 2014-12-19 | 2017-06-06 | 宝山钢铁股份有限公司 | A kind of super high strength hot rolled Q＆P steel of low yield strength ratio and its manufacture method |
| 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 |
| CN109280859A (en) * | 2018-10-19 | 2019-01-29 | 北京科技大学 | A kind of preparation method of the easy expansion sleeve tubing of petroleum drilling and mining |
| CN111235466B (en) * | 2020-02-26 | 2022-02-25 | 江苏省沙钢钢铁研究院有限公司 | TiC dispersion strengthening complex phase reinforcing steel bar and production method thereof |
| CN113005275A (en) * | 2020-09-09 | 2021-06-22 | 刘文西 | Expansion pipe carbon dissimilarity treatment assembly line |
| CN115341130B (en) * | 2022-09-06 | 2023-08-11 | 广西科技大学 | Method for preparing high-strength plastic product hot-rolled cold-formed automobile structural steel |
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| CN101805871A (en) * | 2010-04-09 | 2010-08-18 | 中国石油天然气集团公司 | Steel used for solid expandable casing of oil and gas well and manufacturing method of expandable casing |
| CN101812638A (en) * | 2010-01-21 | 2010-08-25 | 华鼎鸿基石油工程技术(北京)有限公司 | Expansion pipe and method for preparing same |
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| CN101812638A (en) * | 2010-01-21 | 2010-08-25 | 华鼎鸿基石油工程技术(北京)有限公司 | Expansion pipe and method for preparing same |
| CN101805871A (en) * | 2010-04-09 | 2010-08-18 | 中国石油天然气集团公司 | Steel used for solid expandable casing of oil and gas well and manufacturing method of expandable casing |
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