CN101440461A - Casinghead gas corrosion resistant pumping rod steel and manufacturing method thereof - Google Patents
Casinghead gas corrosion resistant pumping rod steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides steel for a pumping rod resisting casinghead gas corrosion and a manufacture method thereof. The steel comprises the following chemical compositions by mass percentage: 0.05 to 0.25 percent of carbon, 0.50 to 2.00 percent of silicon, 1.10 to 2.50 percent of manganese, 0.02 to 0.50 percent of molybdenum, 0.02 to 0.50 percent of nickel, 0.50 to 1.50 percent of chromium, 0.01 to 0.10 percent of vanadium, 0.005 to 0.050 percent of aluminum, 0.02 to 0.10 percent of niobium, 0.05 to 0.50 percent of copper, 0.01 to 0.10 percent of titanium, less than or equal to 0.015 percent of sulphur, less than or equal to 0.020 percent of phosphorus, and the balance being ferrum. The method is to manufacture a pumping rod wire through a design of adding the niobium and other trace alloy elements and corresponding compositions into steel, and controlled rolling and controlled cooling organization control technology. The pumping rod manufactured by the wire has excellent oilwell medium corrosion resistance, proper strength, excellent plastic tenacity and excellent welding performance, thereby improving the service life and reliability of the pumping rod, and improving the whole stability of pumping equipment, and further solving the problem that the prior pumping rod has repeated stress failure caused by endurance of complex casinghead gas corrosion.
Description
Technical field
The present invention relates to the composition design and the manufacture method thereof of metallurgy industry structure iron, refer in particular to a kind of Casinghead gas corrosion resistant pumping rod steel and manufacturing technology thereof.
Background technology
Production on artificial lift is the main means of oil-field development, and rod pumping system occupies critical role in production on artificial lift.Sucker rod is the strength member of sucker rod pumping equipment, and its function is to give downhole pump with the transmission of power of oil pumper, by oil well pipe extraction oil.
Sucker rod generally adopts the manufacturing of steel wire rod, and it can be divided into two kinds on D level bar, H level bar by intensity rank, and wherein, latter's intensity is higher.The steel grade of making the employing of D level bar has 35Mn2,35CrMo, 42CrMo steel etc., and the D grade pumping rod that API is recommended has: 1536 and 4142 (being equivalent to 35Mn2 and 42CrMo steel respectively).Make H level bar and mainly adopt 12Mn2SiCr, 16Mn2SiCr, 20Cr2MoNi steel etc.Although H grade pumping rod intensity is higher, might not be higher than D level bar its work-ing life.Reason is that although along with the intensity of steel improves, the intensity of sucker rod, abrasion resistance properties improve, and when improving strength of oil pump rod, often is accompanied by and reduces toughness as cost.
At present, in the performance history of oil and gas, CO
2+ H
2S+CL
-In gas and medium the corrosion of sucker rod has been become the subject matter of Casinghead gas corrosion resistant, it has not only caused enormous economic loss to the oil field, and has often brought some catastrophic consequences, as loss of life and personal injury, shut-down, stopping production and environmental pollution etc.All there is serious CO2 corrosion in oil fields such as China Tarim Basin, long celebrating, Sichuan, North China, Jiang-Han Area at present, and also there is even more serious CO in oil fields such as Sichuan, long celebrating
2+ H
2S+CL
-Comprehensive corrosion.The domestic and international research document shows: adopt the stainless steel that contains alloying elements such as high Cr, Ni, Mo to be considered to anti-CO
2+ H
2S+CL
-Ideal material, but contain expensive strategic elements such as a large amount of Cr, Ni, Mo, improved the manufacturing cost of field mining equipment greatly, this generally can not accepted by oil exploration industry.Particularly for the oil exploration industry of China, most oil fields are lean ore low permeability oil fields, use that expensive field mining equipment one-time investment is too big, economy is relatively poor.At present, because the difficulty of exploratory development strengthens, the exploratory development environment is more and more abominable, and the user is more and more higher to the requirement of well rod.
Chinese patent application 200410079237.X is anti-corrosion oil pumping rod and manufacture method thereof, its carbon content is 0.40～0.45%, Chinese patent application numbers 200410062593.0 is a kind of pumping rod and the technology of making super-strength sucker rod, its carbon content is 0.25～0.30%, and this welding property to sucker rod is disadvantageous; And Chinese patent application numbers 90104471.7,200410062593.0, the clear 60-238416 intensity of Japanese Patent can not satisfy the requirement of sucker rod high-strong toughness; The patent of application number 92102405.3,96101923.9,01106092.1 is a non-hardened and tempered steel, and it contains higher carbon content and manganese content, and this is disadvantageous to toughness and welding property; Chinese patent application numbers 200410024409.3 is unique coiled rod steel, have comparatively outstanding toughness, but it does not possess corrosion resistance nature; Cr content is 8.0～15.0% among the clear 60-238418 of Japanese Patent, the clear 61-295319, sees to have certain corrosion resistance nature from composition design, but its valuable alloying constituent is too high and cost is not generally adopted by oil equipment factory.
Table 1
| Number of patent application | C (wt％) | Si (wt％) | Mn (wt％) | Cr (wt％) | Mo (wt％) | Other elements (wt%) |
| 200410062593.0 | 0.25～ 0.30 | 0.20～ 0.40 | 0.40～ 0.70 | 0.80～ 1.10 | 0.15～ 0.25 | / |
| 200410079237. X | 0.40-0.45 | 0.15-0.35 | 0.65-1.10 | 0.80-1.10 | 0.15-0.25 | P0.010-0.035 S0.015-0.040 Ni0.015-0.045 |
| 95111888.9 | 0.27～0.35 | 0.90～1.20 | 1.20～1.50 | / | / | V：0.10～0.20 |
| 90104471.7 | 0.36～0.44 | 0.31～0.40 | 1.20～1.80 | / | / | Nb：0.02～0.05 |
| 92102405.3 | 0.10～0.24 | 0.40～1.40 | 2.00～3.00 | 0.40～1.10 | 0.15～0.35 | V：0.05～0.20 Ti：0.01～0.03 |
| 96101923.9 | 0.08～0.20 | 0.50～1.00 | 1.60～2.10 | 0.80～1.20 | / | Ti0.04～0.10 B0.0005～0.003 0 |
| 01106092.1 | 0.26～0.35 | 0.80～1.05 | 1.30～1.50 | / | ≤0.04 | Cr+Ni≤0.02 Cu≤0.25 V：0.08～0.15 Ti：0.02～0.05 |
| 200410024409.3 | 0.18～0.23 | 0.15～0.30 | 0.40～0.60 | 1.80～2.00 | 0.17～0.25 | Al：0.02～0.05 Cu≤0.30 |
| Clear 60-238416 | 0.25～0.35 | 0.20～0.40 | 0.40～0.60 | 0.80～1.20 | 0.30～0.50 | Nb≥0.015 |
| Clear 60-238418 | 0.10～0.30 | 0.10～0.80 | 0.30～1.20 | 8.0～15.0 | Al：0.001～0.050 | |
| Clear 61-295319 | 0.10～0.30 | 0.10～0.80 | 0.30～1.20 | 8.0～15.0 | 0.05～2.0 | Al：0.001～0.050 |
In sum, existing steel for sucker rod still has the following disadvantages: (1) general pumping rod does not generally possess the requirement of Casinghead gas corrosion resistant, even 200410079237.X has erosion-resisting characteristics, but its welding property is bad; (2) good anti-casing-head gas corrosive nature being arranged in high-grade pumping rod, be 8.0～15.0% as Cr content among the clear 61-295319, but its alloy proportion height can not be accepted by oil equipment factory; (3) coupling of existing pumping rod intensity and plasticity is not very desirable, and particularly on the low side (tensile strength of general sucker rod is 740～900Mpa to the unit elongation of tension test, and unit elongation is 12～19%, and relative reduction in area is 50～70%; Intensity rank satisfies the demands, but plasticity index is bad); The tendency of repeated stress failure takes place in (4) impact resistance (being between 70～100J at Aku generally) generally on the low side of existing sucker rod under the complex stress condition that easily causes sucker rod to bear under complex operating environment.
Summary of the invention
The objective of the invention is to design a kind of Casinghead gas corrosion resistant pumping rod, make pumping rod wire promptly by trace alloying element and the designs of corresponding composition such as adding niobiums in steel, and by controlled rolling and controlled cooling organizational controls technology.The sucker rod that adopts this wire rod to make has good oil resistant well dielectric corrosion performance, suitable intensity and good plasticity and toughness, good welding property, thereby improve sucker rod work-ing life and reliability, improve the resistance to overturning of pumping equipment, further solve the problem that repeated stress failure takes place because of the casing-head gas corrosion of bearing complexity existing sucker rod.
Technical scheme of the present invention is,
A kind of Casinghead gas corrosion resistant pumping rod steel, its chemical ingredients mass percent is: carbon 0.05～0.25, silicon 0.50～2.00, manganese 1.10～2.50, molybdenum 0.02～0.50, nickel 0.02～0.50, chromium 0.50～1.50, vanadium 0.01～0.10, aluminium 0.005～0.050, niobium 0.02～0.10, copper 0.05～0.50, titanium 0.01～0.10, sulphur≤0.015, phosphorus≤0.020, surplus are iron and inevitable impurity.
The effect of its main chemical elements in steel is as follows:
Carbon: it is generally acknowledged that 0.08～0.40% carbon content does not influence the hydrogen sulfide corrosion cracking sensitivity of steel is obvious.Carbon is the principal element that improves hardness of steel, guarantee the necessary certain carbon content of certain intensity, but carbon is unfavorable to plasticity, simultaneously greater than the unfavorable welding property of 0.30% carbon content.The C content of control 0.05～0.25% can guarantee to obtain enough intensity, makes steel have good toughness and weldability simultaneously.
Manganese: as the solution strengthening element, also can reduce the austenite-ferrite transformation temperature simultaneously, effectively improve steel hardenability.But manganese has the austenitizing grain growth shortcoming of promotion and is unfavorable for welding property in steel, the content of manganese is controlled at 1.10～2.50% can bring into play good effect in steel of the present invention.
Silicon: be main alloy element in the steel, but silicon does not have clear and definite final conclusion to hydrogen sulfide corrosion cracking sensitivity in the steel.Silicon can significantly improve ferritic intensity, can change the form of separating out, quantity and the size of carbide in the drawing process, improves the temper resistance of steel, promotes precipitation strength indirectly.Silicon has detrimentally affect to the plasticity and the toughness of steel to a certain extent, but silicon can promote the reallocation of carbon in the phase transition process, improves the stability of residual austenite, thereby improves toughness.The silicone content of control 0.50～2.00% improves toughness when can play solution strengthening.
Molybdenum: the anti-sulfide that can improve steel in the low alloy steel ability of breaking, it can postpone ferritic transformation strongly simultaneously, significantly improves the quenching property of steel.Can reduce the temper brittleness of steel, improve the thermal treatment process performance, improve the fatigue property of steel.Molybdenum can reduce the activity of hydrogen in the steel, reduces the suction hydrogen tendency of steel greatly.Can hinder the forming core of carbide consumingly and grow up the storage hydrogen trap in the minimizing steel.The molybdenum of steel adding 0.02～0.50% of the present invention is most economical effective content.
Chromium: the anti-sulfide ability of breaking that can significantly improve steel significantly improves the hardening capacity of steel, the common result of use of chromium and Mn is good, because Cr reduces the carbon activity in the steel, is again carbide forming element simultaneously, put forward the high-carbon diffusion activation energy, so can alleviate the decarburizing tendency of steel.Can change the electropotential of steel, improve corrosion resistance nature.0.50～1.50% chromium is cost-effective optimum content.
Copper: can improve austenitic stability, not increase martensite hardness but can form copper-rich phase and improve secondary hardening hardness, and improve corrosion resistance nature by precipitation strength.The general interpolation with remaining copper is in the steel of the present invention: 0.05～0.50%.
Nickel: it is deleterious that the anti-sulfide of low alloy steel is broken, and the overpotential of hydrogen evolution that contains on the nickel steel is minimum, and hydrogen ion is easy to discharge, thereby has strengthened the liberation of hydrogen process, makes the sulfide cracking sensitivity increase of steel.But the Cu that can suppress in the hot procedure is crisp, reduces the solid solution degree of carbon in matrix, reduces the cooling transformation temperature, promotes separating out of Cr, Mo carbide.Add 0.02～0.50% nickel among the present invention and can play the alloy effect of expection.
Niobium: the anti-sulfide ability of breaking that can significantly improve steel significantly improves the hardening capacity of steel, can form tiny NbCN particle at steel grade, and not molten NbCN particle can stop growing up of austenite crystal during the steel billet reheat; Nb can significantly improve the recrystallization temperature of steel, makes steel carry out the non-recrystallization controlled rolling in higher, bigger heat-drawn wire scope, promotes the refinement of crystal grain, improves the obdurability of steel.0.02～0.50% niobium can play above-mentioned effect.
Titanium: act on similarly to niobium, but it is stronger carbonitride forming element, and the effect that austenite crystal was grown up when tiny TiCN particle effectively stoped the steel billet reheat is more remarkable.0.01 the useful effect of breaking that～0.10% titanium is anti-sulfide.
Vanadium: can produce intensive disperse precipitation strength effect, improve the intensity of steel, and have with the prevention austenite crystal that Ti, Nb are similar and grow up the effect of the recrystallization temperature of raising steel.Consider the coupling of other elements, 0.01～0.10% vanadium is an ideal content.
Aluminium: belong to the crystal grain thinning element.Aluminium element cooperates further crystal grain thinning with above-mentioned element, increase hardening capacity, and improves obdurability.Aluminium obviously reduces the solubleness of carbon in ferrite, makes the hydrogen diffusion slack-off, makes distribution of carbides more even, thereby improves the destructiveness of resisting sulfide.But too much aluminium easily increases the chance that steel inclusion produces, and therefore 0.005～0.050% aluminium is the suitable content of steel of the present invention.
Sulphur, phosphorus: sulphur is very harmful to the anti-hydrogen sulfide performance of breaking, and brings out the disruptive starting point because the sulfide inclusion in the steel both can become hydrogen, also causes stress corrosion crack along the sulfide inclusion border easily.Therefore, to be controlled at below 0.015% be necessary to sulphur.Phosphorus also is deleterious to the anti-hydrogen sulfide performance of breaking, and phosphorus is the promotor of inhaling hydrogen.Phosphorus can block hydrogen atom and be combined to molecule, thereby increases the hydrogen degree of oozing, the anti-hydrogen sulfide that the reduces steel performance of breaking, so phosphorus should be controlled at below 0.020%.
Lead, antimony, bismuth are the impurity elements in the steel simultaneously, should reduce its content as far as possible under technical qualification permission situation.
Carbon, manganese, silicon, chromium, molybdenum are principal element among the present invention, and are equipped with in niobium, vanadium, molybdenum, aluminium, the titanium one or more as trace alloying element.Suitable carbon content can guarantee to obtain enough intensity, makes steel have good toughness and weldability simultaneously, must consider the solution strengthening effect of silicon, manganese simultaneously.
Limiting hardening capacity if desired then considers to reduce carbon and manganese content and improves the loss that element silicon remedies intensity; Improve hardening capacity if desired and reduce the temper brittleness of steel, then improve manganese content and reduce silicone content, but to consider fragility can increase and the stability of toughness, residual austenite can reduce; Cr can significantly improve the hardening capacity and the corrosion resistance nature of steel, and is all comparatively favourable to intensity and toughness simultaneously, adds but consider that the content of carbon, silicon, manganese and performance need can select between 0.50～1.50%; Molybdenum element bigger with the manganese element dependency, comparatively obvious to the hardening capacity influence, go up in limited time in the control manganese 1.10～2.50%, consider the lower limit of control molybdenum 0.02～0.50%; In niobium, vanadium, molybdenum, aluminium, the titanium one or more are as trace alloying element, these trace alloying elements can form very strong carbonitride, austenite crystal grew up when tiny carbonitride particle can effectively stop the steel billet reheat, can improve the recrystallization temperature of steel, make steel carry out the non-recrystallization controlled rolling in higher, bigger heat-drawn wire scope, promote the refinement of crystal grain, improve the obdurability of steel; Copper can improve austenitic stability, produces the precipitation strength effect, and improve corrosion resistance nature but as add copper and must prevent copper brittleness, prevent that copper brittleness from generally adding nickel element, but nickel element is unfavorable to corrosion resistance nature; Sulphur, phosphorus are the impurity elements in the steel, can significantly reduce the plasticity and the toughness of steel, must be controlled under certain content.
Casinghead gas corrosion resistant pumping rod steel manufacture method of the present invention, it comprises the steps:
1) electric arc furnace smelting, ladle refining, continuous casting,
1.1 smelt the tapping condition: T 〉=1620 ℃; [P]≤0.010%, [C] 〉=0.05%;
1.2 ladle refining guarantees [O]≤0.0025%, [H]≤0.00015%; All the components enters the scope of requirement;
Outpour continuously cast bloom 1.3 water; Tundish superheating temperature≤35 ℃;
2) rolling becoming a useful person,
2.1 process furnace heating, 1150～1250 ℃ of soaking temperatures, heat tracing time〉2 hours, because tiny NbCN particle effect in the steel, suppressed under the high temperature austenite crystal of steel and grown up, make steel billet obtain less initial grain fineness number;
2.2 controlled rolling after the steel billet of homogeneous heating is come out of the stove, after de-scaling, enters the roughing unit in 1050～1150 ℃ of temperature ranges; Between 900～980 ℃, enter the finish rolling of multi-pass, the district is rolling at the austenite non-recrystallization, the speed of cooling of control wire rod makes it go out finish rolling in 780～850 ℃ of temperature ranges in the operation of rolling, and it is rolling to enter the reducing sizing mill group in 780～850 ℃ of temperature ranges; Conventional structure steel soaking temperature is 1070～1200 ℃, soaking time 2 hours, and 1050～1180 ℃ of tapping temperatures, the present invention compares soaking temperature with prior art and improves 50 ℃, to implement controlled rolling.
2.3 controlled chilling, be rolled into line up to specification footpath after, wire rod is online slow cooling on roller-way, 40～80 ℃/h of speed of cooling, temperature is reduced to and is adopted air cooling to room temperature below 500 ℃.Make and separate out a large amount of tiny pro-eutectoids in the deformation austenite, all the other austenites change bainite in cooling subsequently.
Again, the steel billet tapping temperature is 1130～1230 ℃ step 2);
Steel billet goes out breaking down unit temperature and is controlled at 1030～970 ℃;
In the breaking down process, make the steel billet homogeneous deformation on the one hand, control the cooling rate of steel billet on the one hand, make steel billet go out breaking down unit temperature and be controlled at 1030～970 ℃.The control steel billet advances the speed of cooling before the finishing train, makes the deformation austenite in the steel finish recrystallize in this process.
In addition, wire rod online slow cooling on roller-way can be adopted and add a cover the stay-warm case delayed quench.
In the manufacturing processed of the present invention,
(1) the controlled rolling and controlled cooling technology of control hardening capacity pumping rod wire
This pumping rod steel billet carries out roughing in 1050～1150 ℃ of temperature ranges, carry out finish rolling in 780 ℃～950 ℃ temperature ranges, and controls the cooling rate of steel in the operation of rolling, makes its finish rolling be controlled at the non-recrystallization district of steel.
(2) the strain-induced ferrite of control hardening capacity sucker rod is separated out technology
This steel the non-recrystallization district finish rolling after, online slow cooling on roller-way is separated out ferrite in high strain austenite, in process of cooling (air cooling) subsequently, supercooled austenite changes bainite structure into.
(3) control hardening capacity sucker rod structure refinement technology
By the integrated use of following technology, obtain to organize the pumping rod wire tiny, that plasticity and toughness are good.Steel billet because small titanium, niobium carbonitride suppressed growing up of austenite crystal, makes steel billet obtain less initial crystal grain in 1150～1250 ℃ of reheat processes.Dynamic recovery and recrystallize take place in this pumping rod steel billet in 1000～1100 ℃ of thermal deformation process.After the static recrystallize of thermal distortion was finished, because the effect of titanium, niobium precipitate, recrystallize was grown up and is inhibited.Because the effect of niobium, vanadium precipitate, the recrystallize of steel billet in 780 ℃～850 ℃ operations of rolling suppressed, and deformation energy is being accumulated in the deformation austenite in a large number, separates out a large amount of tiny ferrites in being cooled to 650～750 ℃ of scopes, and crystal grain obtains refinement greatly.
(4) control hardening capacity pumping rod wire structure property feature and process characteristic
The controlling hot rolling hardening capacity pumping rod wire grain fineness number that adopts above-mentioned technology to produce is 9～11 grades, is organized as proeutectoid ferrite, bainite, and wherein bainite structure is made up of bainite ferrite, martensite and residual austenite.The hardness of this hot rolling wire has good plasticity and toughness at 210～290HB, and hot rolling need not be annealed.
Beneficial effect of the present invention
1. the oil resistant well dielectric corrosion that adopts the technology of stating to produce can obtain bainite structure with pumping rod in the cooling range of 900 ℃ of complete austenitizings, 30～300 ℃/min, be lower than this cooling rate and can obtain ferrite and bainite mixed structure, be higher than that this cooling rate then obtains martensite and bainite mixed structure controlling hot rolling hardening capacity pumping rod wire grain fineness number is 8～11 grades, be organized as proeutectoid ferrite, bainite, wherein bainite structure is made up of bainite ferrite, martensite and residual austenite.This tissue helps the break raising of performance of Casinghead gas corrosion resistant.
2. after implementing controlled rolling and cooling off, carry out slow cooling, obtain the mixed structure of bainite structure, the hardness of hot rolling wire is at 210～290HB, have good plasticity and toughness, hot rolling wire (wire rod) directly carries out can carrying out modifier treatment after the uncoiling (release conventional annealing) on the continuous induction heat treatment facility.
3. steel clarity height: inclusion rank low (detect and to satisfy according to GB/T1056: A≤2, B≤2, C≤1, D≤1); Gas content (oxygen≤15ppm, hydrogen≤1.5ppm).
4. the carbon equivalent of invention steel is suitable, therefore has good welding property, and sucker rod mechanical property of its commissure after flash welding is not less than the mechanical property of former bar.
5. the sucker rod that steel of the present invention is made has low cost, characteristics such as easy to operate, particularly has good Casinghead gas corrosion resistant performance, and comprehensive work-ing life is good.
Description of drawings
Fig. 1 is the metallographic structure after the pumping rod hot rolling slow cooling of the present invention, and its metallographic structure constitutes mixed structure such as proeutectoid ferrite, bainite, and wherein bainite structure is made up of bainite ferrite, martensite and residual austenite.
Embodiment
The embodiment of Casinghead gas corrosion resistant pumping rod steel manufacture method of the present invention,
1, electric arc furnace smelting, ladle refining, continuous casting,
(1) molten steel just refines: furnace charge is selected low P, S steel scrap, crop and high duty pig iron for use; Alloy need be prepared low-carbon (LC) chromium, low Carbon Manganese, molybdenum-iron, aluminium ingot etc.; Reductive agent: calcium carbide, carbon dust, aluminium powder; Oxidation period: diligent stream slag removes P, decarburized amount 〉=0.30%; Slag tap condition: T 〉=1650 ℃; P≤0.004%, Al:0.5Kg/t; Tapping condition: T 〉=1620 ℃; [P]≤0.010%, [C] 〉=0.05%.The tapping later stage adds an amount of lime or synthetic slag;
(2) ladle refining: on ladle refining furnace (capacity and electric furnace are complementary), carry out the refining of molten steel, remove obnoxious flavour and inclusion in the steel, ladle is taken a seat, thermometric, analysis, according to circumstances adjusts argon pressure; LF deoxidation just adds Al to 0.05%, stirs 〉=5 minutes, adjusts chemical ingredients and advances internal control.When molten steel thermometric T 〉=1620 ℃, enter the vacuum degassing, vacuum tightness is that 0.5 torr kept 〉=15 minutes; Guarantee [O]≤0.0025%, [H]≤0.00015%; All the components enters optimizes beginning bull ladle in the scope that requires;
(3) continuous casting: high-temperature molten steel waters into tundish by protective casing in the ladle, tundish superheating temperature≤35 ℃.Before tundish uses fully the cleaning, internal surface is as fire-resistant coating and the crack must not be arranged; Molten steel in the tundish, waters and outpours 90 * 90mm with rational speed through continuous cast mold
2～360 * 360mm
2The qualified continuously cast bloom of cross dimensions is 0.90～2.10m/min according to different ingot shape size pouring speeds;
2, rod rolling
1. process furnace heating, 1150～1250 ℃ of soaking temperatures, heat tracing time〉2 hours, 1130～1230 ℃ of steel billet tapping temperatures, the male and female face temperature difference≤30 ℃; Steel billet is heated to 1150～1250 ℃;
2. rolling, after the steel billet of homogeneous heating was come out of the stove, high pressure descaling subtracted the fixed diameter rolling inlet temperature: 780～850 ℃.Come out of the stove after the steel billet soaking, after de-scaling, in 1050～1150 ℃ of temperature ranges, enter the roughing unit, in the breaking down process, make the steel billet homogeneous deformation on the one hand, control the cooling rate of steel billet on the one hand, make steel billet go out breaking down unit temperature and be controlled at 970～1030 ℃.The control steel billet advances the speed of cooling before the finishing train, makes the deformation austenite in the steel finish recrystallize in this process.
3. cooling control technology: roll into online slow cooling behind the wire rod, 40～80 ℃/h of speed of cooling.Steel billet enters the finishing train of multi-pass between 980～900 ℃, the district is rolling at the austenite non-recrystallization, the speed of cooling of control wire rod in the operation of rolling, make it in 780～850 ℃ of temperature ranges, go out finish rolling, entering the slow cooling district after being cooled to 650～750 ℃ on the transfer limes slowly cools off, make and separate out a large amount of tiny pro-eutectoids in the deformation austenite, all the other austenites change bainite in cooling subsequently.
Steel billet is heated to 1150～1250 ℃.Come out of the stove after the steel billet soaking, after de-scaling, in 1050～1100 ℃ of temperature ranges, enter the roughing unit, in the breaking down process, make the steel billet homogeneous deformation on the one hand, control the cooling rate of steel billet on the one hand, make steel billet go out breaking down unit temperature and be controlled at 1030～1000 ℃.
Steel billet enters the finishing train of multi-pass between 910～980 ℃, the district is rolling at the austenite non-recrystallization, the speed of cooling of control wire rod makes it go out finish rolling in 850～800 ℃ of temperature ranges in the operation of rolling, enters the slow cooling district and slowly cool off after being cooled to 660～750 ℃ on the transfer limes.
This pumping rod wire diameter is Φ 23mm, and hardness is 235HB, and 9 grades of grain fineness numbers are organized as proeutectoid ferrite, bainite, and wherein bainite structure is made up of bainite ferrite, martensite and residual austenite, referring to Fig. 1,
The chemical ingredients of table 2 embodiment rod iron, wt%
| Embodiment | C | Mn | Si | Cr | Al | Mo | Ni | S | Cu | P | Nb | Ti | Fe |
| 1 | 0.08 | 1.18 | 1.98 | 0.70 | 0.015 | 0.50 | 0.08 | 0.006 | 0.12 | 0.008 | 0.03 | 0.02 | Surplus |
| 2 | 0.05 | 1.41 | 1.69 | 0.50 | 0.025 | 0.04 | 0.18 | 0.008 | 0.10 | 0.010 | 0.02 | 0.04 | Surplus |
| 3 | 0.13 | 1.65 | 1.01 | 1.50 | 0.035 | 0.15 | 0.25 | 0.002 | 0.20 | 0.006 | 0.04 | 0.10 | Surplus |
| 4 | 0.18 | 1.99 | 0.79 | 1.05 | 0.010 | 0.20 | 0.38 | 0.010 | 0.35 | 0.020 | 0.10 | 0.07 | Surplus |
| 5 | 0.25 | 2.50 | 0.50 | 0.58 | 0.005 | 0.25 | 0.50 | 0.004 | 0.50 | 0.006 | 0.06 | 0.06 | Surplus |
| 6 | 0.12 | 1.15 | 2.00 | 1.00 | 0.035 | 0.03 | 0.02 | 0.003 | 0.08 | 0.007 | 0.02 | 0.03 | Surplus |
| 7 | 0.14 | 1.10 | 1.89 | 1.01 | 0.050 | 0.02 | 0.08 | 0.015 | 0.09 | 0.020 | 0.05 | 0.01 | Surplus |
The mechanical property of table 3 embodiment rod iron
| Embodiment | Rp0.2(Mpa) | Rm(Mpa) | A5(％) | Z(％) | Aku(J) |
| 1 | 690 | 856 | 23 | 70 | 140 |
| 2 | 704 | 848 | 25 | 74 | 138 |
| 3 | 725 | 879 | 22 | 68 | 125 |
| 4 | 780 | 923 | 23 | 68 | 107 |
| 5 | 757 | 916 | 22 | 70 | 112 |
| 6 | 786 | 996 | 25 | 75 | 118 |
| 7 | 715 | 890 | 26 | 76 | 120 |
Can draw steel of the present invention by table 3 and have good combination of strength and toughness, product can significantly improve plasticity and toughness when keeping intensity not reduce, tiny and uniform in addition mixing microstructure (comprising residual austenite) can obtain good fatigue lifetime and Casinghead gas corrosion resistant ability thereof.
Implement wire rod (wire rod) steel that the present invention produces, make sucker rod and be applied to domestic certain large-scale oil field through domestic certain sucker rod factory, every performance all meets service requirements, common relatively sucker rod has the performance of Casinghead gas corrosion resistant preferably, can solve the insurmountable problem of common sucker rod preferably, the trend that substitutes common sucker rod is arranged, particularly crucial realistic meaning is arranged for corrosion well and hyposmosis well etc.
Claims (5)
1. Casinghead gas corrosion resistant pumping rod steel, its chemical ingredients mass percent is:
Carbon 0.05～0.25,
Silicon 0.50～2.00,
Manganese 1.10～2.50,
Molybdenum 0.02～0.50,
Nickel 0.02～0.50,
Chromium 0.50～1.50,
Vanadium 0.01～0.10,
Aluminium 0.005～0.050,
Niobium 0.02～0.10,
Copper 0.05～0.50,
Titanium 0.01～0.10,
Sulphur≤0.015,
Phosphorus≤0.020,
Surplus is iron and inevitable impurity.
2. the manufacture method of Casinghead gas corrosion resistant pumping rod steel as claimed in claim 1, it comprises the steps:
1) electric arc furnace smelting, ladle refining, continuous casting,
1.1 smelt the tapping condition: T 〉=1620 ℃; [P]≤0.010%, [C] 〉=0.05%;
1.2 ladle refining guarantees [O]≤0.0025%, [H]≤0.00015%; All the components enters the scope of requirement;
Outpour continuously cast bloom 1.3 water, tundish superheating temperature≤35 ℃;
2) rolling becoming a useful person,
2.1 process furnace heating, 1150～1250 ℃ of soaking temperatures, heat tracing time 〉=2 hour;
2.2 controlled rolling after the steel billet of homogeneous heating is come out of the stove, after de-scaling, enters the roughing unit in 1050～1150 ℃ of temperature ranges; Between 900～980 ℃, enter the finish rolling of multi-pass, the district is rolling at the austenite non-recrystallization, the speed of cooling of control wire rod makes it go out finish rolling in 780～850 ℃ of temperature ranges in the operation of rolling, and it is rolling to enter the reducing sizing mill group in 780～850 ℃ of temperature ranges;
2.3 controlled chilling, be rolled into line up to specification footpath after, wire rod is online slow cooling on roller-way, 40～80 ℃/h of speed of cooling, temperature is reduced to and is adopted air cooling to room temperature below 500 ℃.
3. the manufacture method of Casinghead gas corrosion resistant pumping rod steel as claimed in claim 2 is characterized in that, 1130 ℃～1230 ℃ of steel billet tapping temperatures.
4. the manufacture method of Casinghead gas corrosion resistant pumping rod steel as claimed in claim 2 is characterized in that, steel billet goes out breaking down unit temperature and is controlled at 970 ℃～1030 ℃.
5. the manufacture method of Casinghead gas corrosion resistant pumping rod steel as claimed in claim 2 is characterized in that, wire rod online slow cooling on roller-way is adopted and added a cover the stay-warm case delayed quench.
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