CN116875888A - Coiled plate for 520 MPa-level hydrogen induced cracking-resistant petroleum casing pipe and manufacturing method thereof - Google Patents

Coiled plate for 520 MPa-level hydrogen induced cracking-resistant petroleum casing pipe and manufacturing method thereof Download PDF

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Publication number
CN116875888A
CN116875888A CN202310783057.2A CN202310783057A CN116875888A CN 116875888 A CN116875888 A CN 116875888A CN 202310783057 A CN202310783057 A CN 202310783057A CN 116875888 A CN116875888 A CN 116875888A
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percent
grade
petroleum casing
induced cracking
coiled plate
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黄明浩
黄国建
孔祥磊
于洋
王杨
张英慧
刘干
孙杭
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Angang Steel Co Ltd
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Angang Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

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  • Heat Treatment Of Steel (AREA)

Abstract

The invention relates to the technical field of petroleum casing production, in particular to a 520 MPa-level hydrogen-induced cracking-resistant coiled plate for petroleum casing and a manufacturing method thereof. The chemical components of the paint are as follows by weight percent: c:0.02% -0.045%, si:0.15 to 0.30 percent of Mn:1.6 to 1.9 percent, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, nb:0.06% -0.10%, ti:0.01 to 0.03 percent of Mg:0.0005% -0.002%, B:0.0008 to 0.002 percent of Mo:0.1 to 0.3 percent, als:0.02% -0.05%, N: less than or equal to 0.008 percent, pcm is lower than 0.15 percent, and the balance is Fe and unavoidable elements. The material has good weldability and excellent HIC resistance, ensures that the steel pipe has better impact toughness, prevents the brittle failure of the oil well pipe, and has higher safety. The final structure of the coiled plate is ferrite-pearlite, and the volume fraction proportion of the pearlite is lower than 3%; the class A/B/C/D inclusion grade is below 1.0 grade, class sum grade is below 1.5 grade, and band structure is below 0.5 grade.

Description

Coiled plate for 520 MPa-level hydrogen induced cracking-resistant petroleum casing pipe and manufacturing method thereof
Technical Field
The invention relates to the technical field of petroleum casing production, in particular to a 520 MPa-level hydrogen-induced cracking-resistant coiled plate for petroleum casing and a manufacturing method thereof.
Background
The petroleum casing pipe is a steel pipe for supporting the well wall of an oil and gas well so as to ensure the normal operation of the whole oil well after the well drilling process and the well completion, and is an indispensable construction material in the drilling and production operation of the oil and gas field. Compared with seamless tubes, the HFW (high frequency welding) sleeve has the remarkable advantages of uniform wall thickness, high dimensional accuracy, good perforating performance, strong anti-extrusion capability, low cost and the like, and is gradually replacing the traditional seamless steel tubes.
The world energy demand is growing day by day, the petroleum and natural gas yield is increasing year by year, and the problems of corrosion and protection of petroleum casings are becoming the focus of general attention. H of oil casing 2 S corrosion has becomeThe method has the advantages that the method has great economic loss for the main corrosion types facing the oil and gas field, not only causes shutdown and production stoppage and increases maintenance cost, but also pollutes the environment and even endangers the life, and has great social and economic significance for developing the petroleum casing pipe with good corrosion resistance.
A coiled plate with tensile strength of 520MPa belongs to J55 steel grade specified by API Spec 5 CT. API Spec 5CT specifies: the J55 grade yield strength is between 379 and 552MPa, the tensile strength is more than or equal to 517MPa, the elongation is more than or equal to 24 percent, the impact energy is more than or equal to 20J, akv (21 ℃ C., transverse direction) can be selected, the HIC resistance performance is tested by adopting A solution according to NACE TM0284, and the CSR is less than or equal to 2 percent, the CLR is less than or equal to 15 percent and the CTR is less than or equal to 5 percent. In order to ensure that the J55 straight welding oil sleeve is required to be subjected to resistance welding, good welding performance is required, and the cold crack sensitivity coefficient Pcm is as low as possible; in order to ensure impact resistance and extrusion, a certain impact toughness is required; to ensure HIC resistance, it is necessary to control the degree of fineness and uniformity of inclusions and structures; to ensure strength, it is necessary to add certain alloys to refine the grains and provide hardenability.
The Chinese patent document with publication number CN102260834A discloses an anti-H 2 S-corrosion hot-rolled steel sheet for oil well pipe and method for producing same, although being resistant to H 2 S corrodes, but HFW weldability is poor, and control of casting blank segregation is unfavorable, and HIC performance is not good. The Chinese patent document with publication number CN109023045A discloses a high H resistance 2 Production method of S-corrosion petroleum well casing J55 ", although resistant to H 2 S corrosion, but is detrimental to the control of casting blank segregation, and is detrimental to HIC performance.
In conclusion, the coiled plate with the tensile strength of 520MPa is guaranteed to have good welding performance and excellent SSC resistance; meanwhile, the steel pipe is guaranteed to have better impact toughness, and the steel pipe becomes a technical problem to be solved by the system.
Disclosure of Invention
In order to overcome the defects of the prior art, the invention provides the 520 MPa-grade hydrogen-induced cracking-resistant coiled plate for the petroleum casing pipe and the manufacturing method thereof, the weldability of the material is good, the HIC resistance is excellent, the steel pipe is ensured to have better impact toughness, the brittle failure of the oil well pipe is prevented, and the safety is higher.
In order to achieve the above purpose, the invention is realized by adopting the following technical scheme:
a520 MPa grade hydrogen induced cracking resistant coiled plate for petroleum casing pipe comprises the following chemical components in percentage by weight:
c:0.02% -0.045%, si:0.15 to 0.30 percent of Mn:1.6 to 1.9 percent, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, nb:0.06% -0.10%, ti:0.01 to 0.03 percent of Mg:0.0005% -0.002%, B:0.0008 to 0.002 percent of Mo:0.1 to 0.3 percent, als:0.02% -0.05%, N: less than or equal to 0.008 percent, pcm is lower than 0.15 percent, and the balance is Fe and unavoidable elements.
A manufacturing method of a 520 MPa-level hydrogen induced cracking resistant coiled plate for a petroleum casing pipe specifically comprises the following steps:
1) Smelting:
and (5) molten iron pretreatment.
The converter smelting is performed by top blowing or top-bottom combined blowing.
Refining outside the furnace, light desulfurization treatment in an LF furnace and calcium treatment.
2) Continuous casting:
continuous casting slab is made into continuous casting blank by electromagnetic stirring or dynamic soft reduction.
3) Rolling:
the continuous casting slab is heated to 1150-1250 ℃ by a heating furnace and then subjected to thermomechanical rolling.
The rough rolling finishing temperature is 990-1050 ℃, the finish rolling starting temperature is 950-980 ℃, and the finishing temperature is 860-900 ℃.
4) And (3) cooling:
and after rolling, adopting laminar cooling with the cooling speed of 9-14 ℃/s.
5) And (3) coiling:
and after cooling, coiling, wherein the coiling temperature is 580-650 ℃.
The final structure of the coiled plate is ferrite-pearlite, and the volume fraction proportion of the pearlite is lower than 3%; the class A/B/C/D inclusion grade is below 1.0 grade, class sum grade is below 1.5 grade, band structure is below 0.5 grade, and impact energy at-20 ℃ is greater than 150J.
Compared with the prior art, the invention has at least the following technical effects or advantages:
1. the invention has low C content and good HIC resistance. The existing J55 is generally designed with the C content of over 0.15 percent, and has high pearlite content, high hardness and poor HIC resistance. When the Mn content is high, mn segregation generates a band structure, and a pearlite band having high hardness is formed during hot rolling, severely deteriorating HIC performance. When the C content is lower than 0.05%, the formed punctiform uniform distribution lean pearlite structure has the proportion lower than 3%, and the HIC resistance is improved. At this time, the effect that the increase in Mn content does not deteriorate the HIC resistance is also achieved.
2. Mg refines the inclusion, can effectively change the shape and size of the inclusion, and is beneficial to HIC performance and impact. Carrying out multiphase desulfurization reaction on the interface of the magnesium bubbles and molten steel; on the other hand, magnesium is dissolved in molten steel and carries out homogeneous desulfurization reaction with sulfur in the molten steel, the dispersion and refinement effects of inclusions in the steel after magnesium is added are obvious, and the fine dispersed inclusions can improve HIC sensitivity; meanwhile, as the influence of MnS on HIC is the greatest, the reaction of magnesium and sulfur reduces the content of MnS, and the HIC resistance is further improved.
3. Proper amount of Nb obviously refines grains and improves the strength of the hot rolled state. Niobium reduces a gamma-phase region, enters a solid solution, has strong solid solution strengthening effect, and remarkably improves the hardenability of steel in solid solution and austenite. The strength of the steel can be improved without affecting the plasticity or toughness of the steel. Refining the grains may increase the impact toughness and lower the brittle transition temperature of the steel. The niobium reaches a certain content or more, so that the growth of crystal grains can be prevented, the steel can be rolled in a high-temperature interval, and good strength and low-temperature toughness are still obtained. Since a certain amount of carbon can be fixed, the steel has good hydrogen resistance, and in austenite, intergranular corrosion of the steel by the oxidizing medium can be prevented.
4. The Pcm of the invention is lower than 0.15%, and the welding property is good. The existing J55 generally adopts the materials with the C content of more than 0.15 percent, the Mn content of more than 1.0 percent and the Pcm close to 0.25 percent. When the Pcm value is more than 0.25, the cold cracking tendency is remarkably increased and the weldability is lowered. The lower Pcm is, the better the weldability is, the lower Pcm is, the better the weldability is.
5. The invention adopts the design of low carbon, medium manganese and high Nb magnesium, and fully utilizes solid solution strengthening, fine crystal strengthening and precipitation strengthening by improving the manganese content and the niobium content, thereby ensuring the strength and the toughness of the product; low carbon and magnesium containing to address HIC resistance; low carbon and low Pcm, and solves the technical problem of material weldability.
6. The rough rolling finishing temperature is 990-1050 ℃, the finish rolling starting temperature is 950-980 ℃, the finishing temperature is 860-900 ℃, and the cooling speed is 9-14 ℃/s. The alloy design for reducing the carbon content and improving the niobium content simultaneously utilizes solid solution niobium to improve the recrystallization temperature of austenite, so that controlled rolling can be carried out at a higher temperature, and the finish rolling starting temperature achieves the aim of reducing the load of a rolling mill to produce high-strength steel; meanwhile, by matching with a proper post-rolling cooling system, the formation of acicular ferrite structure is promoted by utilizing the influence of solid solution niobium on phase transformation, and the aims of finally improving the toughness, the welding performance and the hydrogen sulfide stress corrosion resistance are achieved.
Detailed Description
The invention discloses a 520 MPa-level hydrogen induced cracking resistant coiled plate for a petroleum casing pipe and a manufacturing method thereof. Those skilled in the art can, with the benefit of this disclosure, suitably modify the process parameters to achieve this. It is expressly noted that all such similar substitutions and modifications will be apparent to those skilled in the art, and are deemed to be included in the present invention. While the methods and applications of this invention have been described in terms of preferred embodiments, it will be apparent to those skilled in the relevant art that variations and modifications can be made in the methods and applications described herein, and in the practice and application of the techniques of this invention, without departing from the spirit or scope of the invention.
A520 MPa grade hydrogen induced cracking resistant coiled plate for petroleum casing pipe comprises the following chemical components in percentage by weight:
c:0.02% -0.045%, si:0.15 to 0.30 percent of Mn:1.6 to 1.9 percent, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, nb:0.06% -0.10%, ti:0.01 to 0.03 percent of Mg:0.0005% -0.002%, B:0.0008 to 0.002 percent of Mo:0.1 to 0.3 percent, als:0.02% -0.05%, N: less than or equal to 0.008 percent, and the balance of Fe and unavoidable elements.
Compared with the prior art, the scheme C has low content and good HIC performance; mg refines the inclusion, can effectively change the shape and size of the inclusion, and is beneficial to HIC performance and impact; proper amount of Ti obviously refines grains and improves the strength of the hot rolled state; pcm is less than 0.15%, and the weldability is good.
The mechanism of action of each alloy component of the invention is described in detail below, wherein the percent symbol represents weight percent:
c: the carbide forming element is the most effective element for ensuring the strength, can improve the hardenability and ensures the strength and the hardness of the material. Only enough carbon is ensured, enough carbon-rich residual austenite is formed and can be stabilized to room temperature, and a small amount of uniform and fine pearlite structure is finally formed. If the carbon content is too low, the hardness of the material cannot be ensured, resulting in poor threading performance. The content is too high, which affects the weldability, plasticity and impact toughness of the product, and the optimal range is 0.02% -0.045%.
Si: can be dissolved into ferrite and austenite to play a certain solid solution strengthening role, can obviously improve the hardness and strength of steel and improve the fatigue strength and fatigue ratio, but the plasticity and toughness of the steel can be obviously reduced when the content is too high, and the optimal range is 0.15-0.30%.
Mn: manganese has solid solution strengthening effect, can increase austenite stability, is beneficial to improving hardenability, and effectively ensures the strength of steel. Manganese and iron form a solid solution of people, so that the hardness and strength of ferrite and austenite in steel are improved, meanwhile, carbide forming elements are adopted, cementite is adopted to replace part of iron atoms, and manganese plays a role in refining pearlite due to reduction of critical transformation temperature in steel. However, the excessive manganese content can increase the center segregation tendency of the continuous casting blank, so that the strip-shaped structure in the steel plate is increased, and finally the steel plate contains a certain amount of strip-shaped structure, so that the brittleness of the steel plate is increased, the plasticity is reduced, and the corrosion resistance is deteriorated. Meanwhile, mnS is easy to form, the influence on HIC resistance is bad, and the optimal range is 1.6% -1.9%.
P, S, N: the lower the content is, the better the content is, but the lower the content is, the production cost is increased, the P is less than or equal to 0.015%, the S is less than or equal to 0.004% and the N is less than or equal to 0.006%.
Nb: niobium reduces a gamma-phase region, enters a solid solution, has strong solid solution strengthening effect, and remarkably improves the hardenability of steel in solid solution and austenite; when the carbide exists in the form of fine carbide particles, grains are refined, hardenability of steel is reduced, tempering stability of the steel is improved, and the secondary hardening effect is achieved. The strength of the steel can be improved without affecting the plasticity or toughness of the steel. Refining the grains may increase the impact toughness and lower the brittle transition temperature of the steel. The niobium reaches a certain content or more, so that the growth of crystal grains can be prevented, the steel can be rolled in a high-temperature interval, and good strength and low-temperature toughness are still obtained. Since a certain amount of carbon can be fixed, the steel has good hydrogen resistance, and in austenite, intergranular corrosion of the steel by the oxidizing medium can be prevented. The high temperature properties of the steel can be improved due to the carbon and precipitation hardening effects of the fixed steel. A suitable range is 0.06% to 0.10%.
Ti: titanium is a strong nitrogen fixation element, when about 0.015% of Ti is added, a high-temperature stable fine TiN precipitated phase can be formed during slab continuous casting, the fine TiN precipitated phase can effectively prevent austenite grains of a continuous casting slab from growing up in the heating process, and the titanium alloy has an obvious effect of improving the toughness of a heat affected zone during steel welding. More Ti content can obtain more TiC particles, and the strength of the steel is improved through strain-induced precipitation and phase-change precipitation. Meanwhile, the precipitated TiC has a strong precipitation strengthening effect, so that the crystal grains of the steel pipe after the subsequent normalizing heat treatment are not obviously grown, and the strength of the whole pipe after the heat treatment is ensured to meet the J55 performance requirement. The optimal range is 0.01% -0.03%.
Mg: magnesium has strong chemical activity, has strong affinity with oxygen and sulfur, is an effective refining agent, can reduce the oxygen and sulfur content and the number of inclusions in steel, purify molten steel, can play an obvious role in modifying the inclusions in steel, and improves the performance of steel. Trace amounts of magnesium can change the number, type, size, distribution of sulfides, carbides, and carbonitrides. The inclusion treated by magnesium is a mixed phase, the core of the inclusion is magnesium oxide, and the structure is finely dispersed and distributed in steel to form the inclusion, thereby improving the performance and corrosion resistance of the steel. A suitable range is 0.0005% to 0.002%.
B: boron can significantly increase hardenability and improve toughness. The ability of boron to improve hardenability is very strong, 0.001% -0.003% of boron is equivalent to 0.6% of manganese, 0.7% of chromium, 0.5% of molybdenum and 1.5% of nickel, so that a small amount of boron can be added to achieve the effect of replacing noble alloy elements. Too high and too low boron content affect hardenability. A suitable range is 0.0008% to 0.002%.
Mo: molybdenum can be dissolved into solid solution to play a role in improving strength. After Mo element is dissolved in austenite, the stability of supercooled austenite is increased, so that the C curve is shifted to the right, and the hardenability of steel is improved. Mo can reduce the transformation temperature, inhibit the formation of polygonal ferrite, promote the transformation of acicular ferrite, improve the precipitation strengthening effect of Nb (C, N), improve the strength of steel, reduce the ductile-brittle transformation temperature and improve the HIC resistance. A suitable range is 0.10% -0.30%.
Als: aluminum is a common deoxidizer, and a small amount of aluminum is added into steel, so that grains can be refined, the impact toughness is improved, and the Als content of the steel is 0.02% -0.05%.
A manufacturing method of a 520MPa grade hydrogen induced cracking resistant coiled plate for petroleum casing pipe comprises the steps of molten iron pretreatment, molten steel smelting, external refining, slab continuous casting, continuous casting slab reheating, rolling, cooling and coiling, and specifically comprises the following steps:
1. smelting continuous casting process:
molten iron pretreatment, converter smelting, top blowing or top-bottom combined blowing, external refining, LF light desulfurization treatment and calcium treatment to control inclusion morphology and improve ductility, toughness and cold bending performance of steel, and continuous casting of slabs to prepare continuous casting slabs adopts electromagnetic stirring or dynamic light pressing to improve quality of continuous casting slabs.
2. Rolling and cooling processes:
the continuously cast slab is heated to 1150-1250 ℃ by a heating furnace and then subjected to thermomechanical rolling. The rough rolling finishing temperature is 990-1050 ℃, the finish rolling starting temperature is 950-980 ℃, and the finishing temperature is 860-900 ℃, and the temperature range is favorable for Nb and Ti precipitation, refining the grain size and improving the strength and toughness; after rolling, laminar cooling is adopted, the cooling speed is 9-14 ℃/s, and the cooling speed is beneficial to refining pearlite, reduces the banded structure to below 0.5 level, can obviously improve the yield strength and the tensile strength, and improves the toughness and the corrosion resistance. And coiling is carried out after cooling, wherein the coiling temperature is 580-650 ℃, and the temperature range is favorable for uniform and refinement of ferrite tissues.
The final structure of the coiled plate is ferrite-pearlite, and the volume fraction proportion of the pearlite is lower than 3%; pcm is lower than 0.15%, the class A/B/C/D inclusion grade is lower than 1.0, the class sum grade is lower than 1.5, and the band structure is lower than 0.5.
[ example ]
A520 MPa grade hydrogen induced cracking resistant coiled plate for petroleum casing and a manufacturing method thereof, and the specific implementation modes are as follows:
wherein table 1 is the chemical composition of the example coil; table 2 shows the process parameters of heating, rolling and cooling in the examples; table 3 shows the results of the mechanical properties of the examples.
Table 1 example chemical composition (wt%)
Examples C Si Mn P S Nb Ti Mg B Mo Als N Pcm
1 0.043 0.30 1.63 0.013 0.004 0.06 0.02 0.002 0.001 0.2 0.04 0.006 0.15
2 0.02 0.20 1.88 0.010 0.002 0.09 0.03 0.002 0.002 0.1 0.02 0.004 0.14
3 0.02 0.15 1.70 0.009 0.002 0.07 0.01 0.001 0.002 0.3 0.03 0.005 0.13
4 0.04 0.18 1.61 0.010 0.003 0.07 0.02 0.0008 0.001 0.1 0.05 0.007 0.14
5 0.03 0.22 1.65 0.011 0.003 0.10 0.02 0.002 0.002 0.3 0.04 0.006 0.14
6 0.04 0.28 1.75 0.013 0.004 0.07 0.03 0.001 0.0008 0.1 0.02 0.005 0.15
7 0.03 0.18 1.82 0.009 0.001 0.08 0.01 0.002 0.002 0.2 0.03 0.004 0.15
8 0.02 0.17 1.62 0.008 0.003 0.08 0.01 0.0006 0.002 0.2 0.03 0.007 0.13
TABLE 2 heating, rolling and Cooling Process parameters
TABLE 3 mechanical and corrosion resistance Properties Meter
As can be seen from tables 1-3, the 520MPa grade H2S corrosion resistant coiled plate for oil casing produced by adopting the component design and rolling and coiling process of the invention meets the requirements of API SPEC 5CT standard J55 grade mechanical property and corrosion resistance.
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art, who is within the scope of the present invention, should make equivalent substitutions or modifications according to the technical scheme of the present invention and the inventive concept thereof, and should be covered by the scope of the present invention.

Claims (6)

1. A520 MPa grade hydrogen induced cracking resistant coiled plate for petroleum casing is characterized by comprising the following chemical components in percentage by weight:
c:0.02% -0.045%, si:0.15 to 0.30 percent of Mn:1.6 to 1.9 percent, P: less than or equal to 0.015 percent, S: less than or equal to 0.004%, nb:0.06% -0.10%, ti:0.01 to 0.03 percent of Mg:0.0005% -0.002%, B:0.0008 to 0.002 percent of Mo:0.1 to 0.3 percent, als:0.02% -0.05%, N: less than or equal to 0.008 percent, pcm is lower than 0.15 percent, and the balance is Fe and unavoidable elements.
2. A method for manufacturing a 520MPa grade hydrogen induced cracking resistant coiled sheet for petroleum casing according to claim 1, comprising the steps of:
1) Smelting:
refining outside the furnace, performing light desulfurization treatment in an LF furnace and performing calcium treatment;
2) Continuous casting:
continuous casting of the slab is carried out to prepare a continuous casting blank, and electromagnetic stirring or dynamic soft reduction is adopted in continuous casting;
3) Rolling:
the continuous casting slab is heated to 1150-1250 ℃ and then rolled,
the rough rolling finishing temperature is 990-1050 ℃, the finish rolling starting temperature is 950-980 ℃, and the finishing temperature is 860-900 ℃.
4) And (3) cooling:
laminar cooling is adopted after rolling, and the cooling speed is 9-14 ℃/s;
5) And (3) coiling:
and after cooling, coiling, wherein the coiling temperature is 580-650 ℃.
3. The method for manufacturing the 520 MPa-grade hydrogen induced cracking resistant coiled plate for the petroleum casing pipe, which is characterized in that,
the 1) converter smelting is performed through top blowing or top-bottom combined blowing.
4. The method for manufacturing the 520 MPa-grade hydrogen induced cracking resistant coiled plate for the petroleum casing pipe, which is characterized in that,
and 2) heating the continuous casting slab to 1150-1250 ℃ by a heating furnace.
5. The method for manufacturing the 520 MPa-grade hydrogen induced cracking resistant coiled plate for the petroleum casing pipe, which is characterized in that,
said 3) using thermo-mechanical rolling.
6. The 520MPa grade hydrogen induced cracking resistant coiled plate for petroleum casing according to claim 2, wherein the final structure of the coiled plate is ferrite-pearlite, and the volume fraction ratio of pearlite is lower than 3%; the class A/B/C/D inclusion grade is below 1.0 grade, class sum grade is below 1.5 grade, band structure is below 0.5 grade, and impact energy at-20 ℃ is greater than 150J.
CN202310783057.2A 2023-06-29 2023-06-29 Coiled plate for 520 MPa-level hydrogen induced cracking-resistant petroleum casing pipe and manufacturing method thereof Pending CN116875888A (en)

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