WO2017200083A1 - ダウンホール部材用棒鋼、及び、ダウンホール部材 - Google Patents
ダウンホール部材用棒鋼、及び、ダウンホール部材 Download PDFInfo
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- WO2017200083A1 WO2017200083A1 PCT/JP2017/018804 JP2017018804W WO2017200083A1 WO 2017200083 A1 WO2017200083 A1 WO 2017200083A1 JP 2017018804 W JP2017018804 W JP 2017018804W WO 2017200083 A1 WO2017200083 A1 WO 2017200083A1
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- 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
- C21D2211/008—Martensite
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
Definitions
- the present invention relates to a steel bar and a downhole member, and more particularly to a steel bar for a downhole member and a downhole member for use in a downhole member used with an oil well pipe in an oil well and a gas well.
- oil well pipes and downhole members are used in the oil well environment.
- FIG. 1 is a diagram showing an example of an oil well pipe and a downhole member used in an oil well environment.
- the oil well pipe is, for example, a casing, a tubing or the like.
- two tubes 2 are arranged in the casing 1.
- the tip of each tubing 2 is fixed in the casing 1 by a packer 3, a ball catcher 4, a blast joint 5, and the like.
- the downhole members are, for example, the packer 3, the ball catcher 4, the blast joint 5, and the like, and are used as accessories of the casing 1 and the tubing 2.
- the downhole member is usually made of a round bar (steel bar for downhole member) which is a solid material. A part of the round bar is cut or cut out to produce a downhole member having a predetermined shape.
- the size of the downhole member bar depends on the size of the downhole member. For example, the diameter of the downhole member bar is 152.4 to 215.9 mm, and the length of the downhole member bar is, for example, 3000 to 6000 mm.
- the downhole member is used in an oil well environment like an oil well pipe.
- the production fluid contains a corrosive gas such as hydrogen sulfide gas or carbon dioxide gas. Therefore, the downhole member, like the oil well pipe, has excellent stress corrosion cracking resistance (hereinafter referred to as SCC resistance; SCC: Stress Corrosion Cracking) and excellent sulfide stress cracking resistance (hereinafter referred to as SSC resistance).
- SCC resistance Stress Corrosion Cracking
- SSC resistance Sulfide Stress Cracking is required.
- Ni-based alloy represented by Alloy 718 (trademark) is usually used as the round bar for the downhole member.
- Alloy 718 (trademark)
- a manufacturing cost becomes high. Therefore, downhole members using stainless steel that is less expensive than Ni-based alloys have been studied.
- Patent Document 1 proposes martensitic stainless steel for downhole members having excellent resistance to sulfide stress corrosion cracking.
- the martensitic stainless steel disclosed in Patent Document 1 is mass%, C: 0.02% or less, Si: 1.0% or less, Mn: 1.0% or less, P: 0.03% or less, S: 0.01% or less, Cr: 10-14%, Mo: 0.2-3.0%, Ni: 1.5-7%, N: 0.02% or less, the balance being Fe and inevitable impurities
- the formula 4Sb / Sa + 12Mo ⁇ 25 (Sb: cross-sectional area before forging and / or partial rolling, Sa: cross-sectional area after forging and / or partial rolling, Mo: containing Mo Forging and / or split rolling so as to satisfy (mass% value).
- Patent Document 1 Even with the martensitic stainless steel for downhole members proposed in Patent Document 1, a certain degree of SSC resistance can be obtained. However, a steel bar for a downhole member having good SCC resistance and SSC resistance due to a configuration different from that of Patent Document 1 is also desired.
- An object of the present invention is to provide a steel bar for a downhole member having excellent SCC resistance and SSC resistance.
- the steel bar for downhole members of this embodiment is in mass%, C: 0.020% or less, Si: 1.0% or less, Mn: 1.0% or less, P: 0.03% or less, S: 0 0.01% or less, Cu: 0.10 to 2.50%, Cr: 10 to 14%, Ni: 1.5 to 7.0%, Mo: 0.2 to 3.0%, Ti: 0.05 -0.3%, V: 0.01-0.10%, Nb: 0.1% or less, Al: 0.001-0.1%, N: 0.05% or less, B: 0-0. 005%, Ca: 0 to 0.008%, and Co: 0 to 0.5%, and the balance has a chemical composition composed of Fe and impurities.
- the Mo content of the above chemical composition of the downhole member steel bar is defined as [Mo amount] (% by mass), and the surface of the downhole member bar steel and the downhole in the cross section perpendicular to the longitudinal direction of the downhole member bar steel
- [total Mo amount in R / 2 position precipitate] mass%
- the formula (1) is satisfied.
- the Mo content in the precipitate at the center position of the cross section perpendicular to the longitudinal direction of the steel bar for the downhole member is defined as [total Mo amount in the center position precipitate] (mass%)
- the formula (2) Meet. [Mo amount] -4 ⁇ [total Mo amount in R / 2 position precipitate] ⁇ 1.30 (1)
- the downhole steel bar according to the present embodiment has excellent SCC resistance and SSC resistance.
- FIG. 1 is a diagram illustrating an example of an oil well pipe and a downhole member used in an oil well environment.
- FIG. 2 shows the Mo content in the chemical composition of the steel for the downhole member and the Mo content in the precipitate (intermetallic compound such as Laves phase) at the R / 2 position of the steel for the downhole member ([R / It is a figure which shows the relationship between corrosion resistance (SCC resistance and SSC resistance) and the total Mo amount in 2 position deposits].
- the present inventors investigated and examined the SCC resistance and SSC resistance of the downhole steel bar. As a result, the present inventors obtained the following knowledge.
- the downhole member is manufactured from a steel bar that is a solid material, not a steel pipe that is a hollow material.
- tempering a steel bar that is a solid material the tempering time must be set longer than in the case of a steel pipe that is a hollow material. The reason is as follows.
- the central part of the cross section perpendicular to the axial direction (longitudinal direction) of the steel bar tends to have a different structure from other parts due to segregation during steel making.
- Many of the actual downhole members are manufactured by hollowing out the central portion of the steel bar. However, some downhole members are used without the hollow steel bar being hollowed out.
- the structure of the central portion can greatly affect the performance of the downhole member. Therefore, it is preferable that the structure of the central part in the cross section perpendicular to the longitudinal direction of the downhole member is uniform with the structure around the central part. Therefore, the tempering time is lengthened as compared with the case of the steel pipe so that the structure is as uniform as possible from the surface to the center in the cross section perpendicular to the longitudinal direction of the steel bar.
- Laves phase contains Mo, which is an element that enhances corrosion resistance. Therefore, if a Laves phase is generated, the amount of solid solution Mo in the base material decreases. If the amount of dissolved Mo in the base material decreases, the SCC resistance and SSC resistance of the downhole member will decrease. Therefore, if the precipitation of the Laves phase can be suppressed, the decrease in the amount of solid solution Mo in the base material can be suppressed, and the SCC resistance and the SSC resistance are improved.
- C 0.020% or less
- Si 1.0% or less
- Mn 1.0% or less
- P 0.03% or less
- S 0.01% or less
- Cr 10 to 14 %
- Ni 1.5 to 7.0%
- Mo 0.2 to 3.0%
- Ti 0.05 to 0.3%
- V 0.01 to 0.10%
- Nb 0.0.
- the N content is not increased, but the same austenite as N It contains 0.10 to 2.50% by mass of Cu as a forming element.
- the precipitation amount of the Laves phase is reduced by containing Cu. Furthermore, since Cu does not increase the strength of the steel material as much as solute N, tempering time can be suppressed. If the Cu content is 0.10 to 2.50%, these effects can be sufficiently obtained.
- the Mo content in the chemical composition of the downhole steel bar is defined as [Mo amount] (mass%), and the surface of the downhole steel bar and the downhole in the cross section perpendicular to the longitudinal direction of the downhole steel bar.
- the Mo content in the precipitate at a position that bisects the center of the steel bar for members is defined as [total Mo amount in the R / 2 position precipitate] (mass%).
- the Mo content in the precipitate is the total content of Mo in the precipitate (mass%) when the total mass of the precipitate in the microstructure at the R / 2 position is 100% (mass%). ).
- the steel bar for downhole members which has the said chemical composition further satisfy
- FIG. 2 shows the Mo content ([Mo amount]) in the chemical composition of the steel bar for the downhole member, and the Mo content in the precipitate at the R / 2 position (the total Mo amount in the [R / 2 position precipitate). ]) And the corrosion resistance (SCC resistance and SSC resistance).
- FIG. 2 was obtained by the examples described below.
- “ ⁇ ” in the figure indicates that neither SCC nor SSC was observed in the SCC resistance evaluation test and the SSC resistance evaluation test (that is, SCC resistance and SSC resistance It is excellent).
- the “ ⁇ ” mark in the figure indicates that either SCC or SSC was observed in the SCC resistance evaluation test and the SSC resistance evaluation test (that is, SCC resistance or SSC resistance is low).
- the microstructure in the center is preferably as uniform as possible in the other regions.
- the central portion corresponds to the final solidification position. In the final solidification position, more Cr and Mo are segregated than in other regions. Furthermore, the center portion tends to have a smaller degree of hot working than other regions. Therefore, the structure of the central portion is likely to become coarser than other regions. The Laves phase precipitates at the grain boundaries. Therefore, if the structure is coarse, the Laves phase is likely to become coarse.
- the Mo content in the precipitate at the center position of the cross section perpendicular to the longitudinal direction of the downhole member steel bar is defined as [total Mo amount in center position precipitate] (mass%).
- the Mo content in the precipitate is the total content (% by mass) of Mo in the precipitate when the total mass of the precipitate in the microstructure at the center position is 100% (% by mass). means.
- the steel bar for downhole members of the present embodiment further satisfies the formula (2) on the premise that the steel bar has the above chemical composition and satisfies the formula (1). [Total Mo amount in R / 2 position precipitate] ⁇ [Total Mo amount in center position precipitate] ⁇ 0.03 (2)
- the steel bar for downhole members of the present embodiment satisfies the above chemical composition and satisfies the formula (1) and the formula (2), so that it has excellent SCC resistance and SSC resistance at the center position and the R / 2 position.
- the above-mentioned steel bar for downhole members can be manufactured by the following manufacturing method, for example.
- a hot working process is implemented with respect to the raw material which has the said chemical composition, and the tempering process including quenching and tempering is implemented after that.
- the forging ratio is defined by the formula (A).
- Forging forming ratio cross-sectional area of the material before hot working (mm 2 ) / cross-sectional area of the material after completion of hot working (mm 2 ) (A)
- the Larson-Miller parameter LMP is set to 16000-18000 in tempering after quenching.
- the steel bar for the downhole member of the present embodiment completed based on the above knowledge is in mass%, C: 0.020% or less, Si: 1.0% or less, Mn: 1.0% or less, P: 0. 0.03% or less, S: 0.01% or less, Cu: 0.10-2.50%, Cr: 10-14%, Ni: 1.5-7.0%, Mo: 0.2-3. 0%, Ti: 0.05 to 0.3%, V: 0.01 to 0.10%, Nb: 0.1% or less, Al: 0.001 to 0.1%, N: 0.05%
- B: 0 to 0.005%, Ca: 0 to 0.008%, and Co: 0 to 0.5% are contained, and the balance has a chemical composition composed of Fe and impurities.
- the Mo content in the chemical composition of the downhole steel bar is defined as [Mo amount] (mass%), and the surface of the downhole steel bar and the downhole in the cross section perpendicular to the longitudinal direction of the downhole steel bar
- the Mo content in the precipitate at the position that bisects the center of the steel bar for members is defined as [total Mo amount in R / 2 position precipitate] (mass%)
- the formula (1) is satisfied.
- the Mo content in the precipitate at the center position of the cross section perpendicular to the longitudinal direction of the steel bar for the downhole member is defined as [total Mo amount in the center position precipitate] (mass%)
- the formula (2) Meet. [Mo amount] -4 ⁇ [total Mo amount in R / 2 position precipitate] ⁇ 1.30 (1)
- the chemical composition contains at least one selected from the group consisting of B: 0.0001 to 0.005% and Ca: 0.0001 to 0.008% instead of part of Fe. Also good.
- the above chemical composition may contain Co: 0.05 to 0.5% instead of a part of Fe.
- the downhole member of this embodiment has the above-described chemical composition.
- the Mo content in the chemical composition of the downhole member is defined as [Mo amount] (mass%), and the surface of the downhole member and the center of the downhole member in the cross section perpendicular to the longitudinal direction of the downhole member are When the Mo content in the precipitate at the equally dividing position is defined as [total amount of Mo in R / 2 position precipitate] (mass%), the formula (1) is satisfied. [Mo amount] ⁇ 4 ⁇ [total Mo amount in R / 2 position precipitate] ⁇ 1.3 (1)
- C 0.020% or less Carbon (C) is inevitably contained. C increases the strength of the steel, but produces Cr carbides during tempering. Cr carbide reduces corrosion resistance (SCC resistance, SSC resistance). Accordingly, a lower C content is preferred.
- the C content is 0.020% or less.
- the upper limit of the preferable C content is 0.015%, more preferably 0.012%, and further preferably 0.010%.
- Si 1.0% or less Silicon (Si) is inevitably contained. Si deoxidizes steel. However, if the Si content is too high, the hot workability decreases. Furthermore, the amount of ferrite produced increases and the strength of the steel material decreases. Therefore, the Si content is 1.0% or less.
- the preferred Si content is less than 1.0%, more preferably 0.50% or less, and even more preferably 0.30% or less. If the Si content is 0.05% or more, Si acts particularly effectively as a deoxidizer. However, even if the Si content is less than 0.05%, Si deoxidizes the steel to some extent.
- Mn 1.0% or less
- Manganese (Mn) is inevitably contained. Mn deoxidizes and desulfurizes steel and improves hot workability. However, if the Mn content is too large, segregation is likely to occur in the steel, and the toughness and the SCC resistance in a high-temperature chloride aqueous solution are reduced. Furthermore, Mn is an austenite forming element. Therefore, when the steel contains Ni and Cu, which are austenite forming elements, if the Mn content is too large, the retained austenite increases and the strength of the steel decreases. Therefore, the Mn content is 1.0% or less.
- the minimum of preferable Mn content is 0.10%, More preferably, it is 0.30%.
- the upper limit of the preferable Mn content is 0.8%, more preferably 0.5%.
- P 0.03% or less Phosphorus (P) is an impurity. P decreases the SSC resistance and SCC resistance of the steel. Therefore, the P content is 0.03% or less.
- the upper limit of the preferable P content is 0.025%, more preferably 0.022%, and further preferably 0.020%. It is preferable that the P content is as small as possible.
- S 0.01% or less Sulfur (S) is an impurity. S decreases the hot workability of steel. Further, S combines with Mn and the like to form inclusions. The formed inclusions serve as starting points for SCC and SSC, and reduce the corrosion resistance of the steel. Therefore, the S content is 0.01% or less.
- the upper limit of the preferable S content is 0.0050%, more preferably 0.0020%, and still more preferably 0.0010%. It is preferable that the S content is as small as possible.
- Cu 0.10 to 2.50% Copper (Cu) suppresses the generation of Laves phase.
- Cu is finely dispersed in the matrix as Cu particles. Generation and growth of the Laves phase are suppressed by the pinning effect of the dispersed Cu particles. Thereby, the precipitation amount of a Laves phase is suppressed and the fall of the amount of solid solution Mo is suppressed. As a result, the SCC resistance and the SSC resistance are increased in the steel bar. If the Cu content is too low, this effect cannot be obtained. On the other hand, if the Cu content is too high, the center segregation of Cr and Mo is excessively promoted, and as a result, the formula (2) is not satisfied.
- the Cu content is 0.10 to 2.50%.
- the minimum with preferable Cu content is 0.15%, More preferably, it is 0.17%.
- the upper limit with preferable Cu content is 2.00%, More preferably, it is 1.50%, More preferably, it is 1.20%.
- Chromium (Cr) increases the SCC resistance and SSC resistance of steel. If the Cr content is too low, this effect cannot be obtained. On the other hand, Cr is a ferrite forming element. Therefore, when there is too much Cr content, a ferrite will produce
- the lower limit of the preferable Cr content is 11%, more preferably 11.5%, and further preferably 11.8%.
- the upper limit of the preferable Cr content is 13.5%, more preferably 13.0%, and further preferably 12.5%.
- Nickel (Ni) is an austenite forming element. Therefore, austenite in steel at high temperature is stabilized, and the amount of martensite at normal temperature is increased. Thereby, Ni raises the intensity
- Mo 0.2-3.0%
- Molybdenum (Mo) increases SSC resistance. Mo further enhances the SCC resistance of the steel in the presence of Cr. If the Mo content is too low, these effects cannot be obtained.
- Mo is a ferrite-forming element, if the Mo content is too large, ferrite in the steel is generated and the strength of the steel is reduced. Therefore, the Mo content is 0.2 to 3.0%.
- the minimum of preferable Mo content is 1.0%, More preferably, it is 1.5%, More preferably, it is 1.8%.
- the upper limit of the Mo content is preferably 2.8%, more preferably less than 2.8%, still more preferably 2.7%, still more preferably 2.6%, and even more preferably 2.%. 5%.
- Titanium (Ti) forms carbides and increases the strength and toughness of the steel. If the diameter of the downhole member steel bar is large, the Ti carbide further reduces the strength variation of the downhole member bar steel. Ti further fixes C, suppresses the formation of Cr carbide, and improves the SCC resistance. If the Ti content is too low, these effects cannot be obtained. On the other hand, if the Ti content is too high, the carbides are coarsened and the toughness and corrosion resistance of the steel are reduced. Therefore, the Ti content is 0.05 to 0.3%. The minimum with preferable Ti content is 0.06%, More preferably, it is 0.08%, More preferably, it is 0.10%. The upper limit with preferable Ti content is 0.2%, More preferably, it is 0.15%, More preferably, it is 0.12%.
- V 0.01 to 0.10% Vanadium (V) forms carbides and increases the strength and toughness of the steel. V further fixes C, suppresses the formation of Cr carbide, and enhances the SCC resistance. If the V content is too low, these effects cannot be obtained. On the other hand, if the V content is too high, the carbides are coarsened and the toughness and corrosion resistance of the steel are reduced. Therefore, the V content is 0.01 to 0.10%.
- the minimum with preferable V content is 0.03%, More preferably, it is 0.05%.
- the upper limit with preferable V content is 0.08%, More preferably, it is 0.07%.
- Niobium (Nb) is an impurity. Although Nb has the effect of forming carbides to increase the strength and toughness of the steel material, if the Nb content is too high, the carbides become coarse and the toughness and corrosion resistance of the steel material decrease. Therefore, the Nb content is 0.1% or less.
- the upper limit with preferable Nb content is 0.05%, More preferably, it is 0.02%, More preferably, it is 0.01%.
- Al 0.001 to 0.1%
- Aluminum (Al) deoxidizes steel. If the Al content is too low, this effect cannot be obtained. On the other hand, if the Al content is too high, the amount of ferrite in the steel increases and the strength of the steel decreases. Furthermore, a large amount of alumina inclusions are produced in the steel, and the toughness of the steel material is reduced. Therefore, the Al content is 0.001 to 0.1%.
- the minimum with preferable Al content is 0.005%, More preferably, it is 0.010%, More preferably, it is 0.020%.
- the upper limit of the preferable Al content is 0.080%, more preferably 0.060%, and still more preferably 0.050%.
- the Al content means the acid-soluble Al (sol. Al) content.
- N 0.05% or less Nitrogen (N) is an impurity. N has the effect of increasing the strength of the steel, but if the N content is too high, the toughness of the steel decreases and the strength of the steel material becomes excessively high. In this case, the tempering time must be lengthened to adjust the strength, and a Laves phase is easily generated. If a Laves phase is generated, the amount of dissolved Mo is reduced, so that SCC resistance and SSC resistance are reduced. Therefore, the N content is 0.05% or less.
- the upper limit with preferable N content is 0.030%, More preferably, it is 0.020%, More preferably, it is 0.010%.
- the balance of the chemical composition of the steel bar according to the present embodiment is composed of Fe and impurities.
- impurities are mixed from ore, scrap, or production environment as raw materials when industrially manufacturing steel bars for downhole members, and have an adverse effect on the steel bars of this embodiment. It means what is allowed in the range.
- the steel bar of the present embodiment may further contain one or more selected from the group consisting of B and Ca instead of a part of Fe. Any of these elements is an arbitrary element, and suppresses generation of defects and defects in hot working.
- B 0 to 0.005%
- Ca 0 to 0.008%
- B and Ca suppress the generation of wrinkles and defects in hot working. If at least one of B and Ca is contained even a little, the above effect can be obtained to some extent.
- the B content is too high, Cr carboboride precipitates at the grain boundaries and the toughness of the steel decreases.
- Ca content is 0 to 0.005%, and the Ca content is 0 to 0.008%.
- the preferable lower limit of the B content is 0.0001%, and the preferable upper limit is 0.0002%.
- the minimum with preferable Ca content is 0.0005%, and a preferable upper limit is 0.0020%.
- the steel bar material of the present embodiment may further contain Co instead of a part of Fe.
- Co 0 to 0.5%
- Co is an optional element and may not be contained. When contained, Co increases the hardenability of the steel and ensures a stable high strength, especially during industrial production. More specifically, Co suppresses retained austenite and suppresses variation in strength. If Co is contained even a little, the above effect can be obtained to some extent. However, if there is too much Co content, the toughness of the steel will decrease. Therefore, the Co content is 0 to 0.5%.
- the minimum with preferable Co content is 0.05%, More preferably, it is 0.07%, More preferably, it is 0.10%.
- the upper limit with preferable Co content is 0.40%, More preferably, it is 0.30%, More preferably, it is 0.25%.
- [Mo amount] (mass%) and [total Mo amount in R / 2 position precipitate] (mass%) are defined as follows.
- the total Mo content (% by mass) in the precipitate when the total mass of the precipitate in the microstructure at 100% is 100%
- F1 [Mo amount] ⁇ 4 ⁇ [total Mo amount in R / 2 position precipitate].
- F1 is an index of the amount of dissolved Mo in the steel bar for downhole members.
- the total amount of Mo in the R / 2 position precipitate means the amount of Mo absorbed in the Laves phase when the steel bar for downhole members is viewed macroscopically. If F1 is 1.30 or more, a sufficient amount of solute Mo is present. Therefore, as shown in FIG. 2, excellent SCC resistance and SSC resistance can be obtained.
- the minimum with preferable F1 is 1.40, More preferably, it is 1.45.
- Mo amount is the Mo content (%) in the chemical composition. Therefore, it can be determined by a known component analysis method. Specifically, for example, the following method is used. Cut down perpendicular to the longitudinal direction of the steel bar for the downhole member, and take a sample with a length of 20 mm. The sample is cut into chips and dissolved in acid to obtain a solution. An ICP-OES (Inductively Coupled Plasma Optical Emission Spectrometry) analysis method is performed on the solution to perform elemental analysis of the chemical composition. In addition, about C content and S content in a chemical composition, specifically, for example, the above-mentioned solution is burned by high-frequency heating in an oxygen stream, carbon dioxide and sulfur dioxide generated are detected, and C The content and the S content are determined.
- ICP-OES Inductively Coupled Plasma Optical Emission Spectrometry
- [total amount of Mo in R / 2 position precipitate] is measured by the following method.
- a sample (diameter 9 mm ⁇ length 70 mm) including an R / 2 position is taken in an arbitrary cross section perpendicular to the longitudinal direction of the downhole member steel bar.
- the longitudinal direction of the sample is parallel to the longitudinal direction of the downhole member steel bar, and the center of the cross section of the sample (circle having a diameter of 9 mm) is the R / 2 position of the downhole member steel bar.
- the test material is electrolyzed using a 10% AA-based electrolytic solution (10% acetylacetone-1% tetramethylammonium chloride-methanol electrolytic solution).
- the current during electrolysis is 20 mA / cm 2 .
- the electrolytic solution is filtered through a 200 nm filter, and the mass of the residue is measured to determine [R / 2 position deposit total mass]. Further, the amount of Mo contained in the solution obtained by acid decomposition of the residue is determined by ICP emission spectroscopic analysis. Based on the amount of Mo in the solution and the [total mass of R / 2 position precipitate], the total Mo content in the precipitate when the total mass of the precipitate at the R / 2 position is 100 (mass%) ( Mass%).
- F2 [total amount of Mo in center position precipitate] ⁇ [total amount of Mo in R / 2 position precipitate].
- F2 is an index related to the uniformity of the microstructure in the cross section perpendicular to the longitudinal direction of the downhole steel bar. If F2 is 0.03 or less, it means that the precipitation amount of the Laves phase at the center position is substantially equal to the precipitation amount of the Laves phase at the R / 2 position. This means that the crystal grain size of the microstructure at the center position is almost equal to the crystal grain size of the microstructure at the R / 2 position, and in the cross section perpendicular to the longitudinal direction of the steel bar for downhole member , Which means that the microstructure is almost uniform.
- Total Mo amount in center position precipitate is measured by the following method.
- a sample (diameter 9 mm, length 70 mm) including the center position of an arbitrary cross section perpendicular to the longitudinal direction of the downhole member steel bar is collected.
- the longitudinal direction of the sample is parallel to the longitudinal direction of the downhole member steel bar, and the center of the cross section (9 mm diameter circle) of the sample is the center position in the cross section perpendicular to the longitudinal direction of the downhole member steel bar.
- the test material is electrolyzed using a 10% AA-based electrolytic solution (10% acetylacetone-1% tetramethylammonium chloride-methanol electrolytic solution). The current during electrolysis is 20 mA / cm 2 .
- the electrolyte is filtered through a 200 nm filter, the mass of the residue is measured, and the [total mass at the center position deposit] is obtained. Further, the amount of Mo contained in the solution obtained by acid decomposition of the residue is determined by ICP emission spectroscopic analysis. Based on the amount of Mo in the solution and [total mass of precipitates at the center position], the total Mo content (mass%) in the precipitates when the total mass of precipitates at the center position is 100 (mass%). Ask. Five samples are collected at an arbitrary location, and the average value of the total Mo content in the precipitate obtained from each sample is defined as [total Mo amount in center position precipitate] (mass%).
- the steel bar for downhole member of the present embodiment has the above-described chemical composition, and the Cu content is 0.10 to 2.50%. Furthermore, formula (1) and formula (2) are satisfied on the assumption that the chemical composition is satisfied. Therefore, sufficient solid solution Mo can be ensured in the base material, and it has a uniform structure in the central portion and the R / 2 portion. As a result, excellent SCC resistance and SSC resistance can be obtained at the center portion and the R / 2 portion.
- the steel bar for downhole members of this embodiment can be manufactured by the following manufacturing method, for example.
- the manufacturing method of the downhole member of this embodiment is not limited to this example.
- an example of the manufacturing method of the steel bar for downhole members of this embodiment is demonstrated.
- This manufacturing method adjusts the strength by carrying out a process (hot working process) of manufacturing an intermediate material (billet) by hot working and quenching and tempering the intermediate material to obtain a steel bar for a downhole member.
- Process tempering heat treatment process
- An intermediate material having the above chemical composition is prepared. Specifically, molten steel having the above-described chemical composition is manufactured. The raw material is manufactured using molten steel. You may manufacture the slab which is a raw material with a continuous casting method. You may manufacture the ingot which is a raw material using molten steel.
- Hot processing is performed on the heated material to produce an intermediate material.
- Hot working is, for example, free forging, rotary forging and hot rolling.
- the hot rolling may be split rolling or rolling using a continuous rolling mill provided with a plurality of rolling stands arranged in a row.
- the cross-sectional area of the material before hot working refers to an area of 1000 mm in the axial direction of the material from the front end of the material (tip portion) and an area of 1000 mm in the axial direction of the material from the rear end of the material (
- a material portion referred to as a material main body portion
- mm 2 sectional area
- the forge forming ratio is 4.0 or more.
- the forging ratio is set to 6.0 or more. If the forging ratio in free forging is less than 4.0, or if the forging ratio in rotary forging or hot rolling is less than 6.0, the cross section in which the reduction in hot working is perpendicular to the longitudinal direction of the material Difficult to penetrate to the center of In this case, the microstructure at the center position of the cross section perpendicular to the longitudinal direction of the downhole member steel bar becomes coarser than the microstructure at the R / 2 position, and F2 does not satisfy the formula (2).
- the forging ratio in free forging is 4.0 or more, or if the forging ratio in rotary forging or hot rolling is 6.0 or more, the reduction in hot working sufficiently penetrates to the center of the material. . Therefore, the crystal grain size of the microstructure at the center position of the downhole member steel bar is substantially equal to the crystal grain size of the microstructure at the R / 2 position, and F2 satisfies the formula (2).
- a preferable forging ratio FR in free forging is 4.2, more preferably 5.0, and still more preferably 6.0.
- a preferred forging ratio FR in the swivel forging or hot rolling is 6.2 or more, more preferably 6.5 or more.
- the tempering heat treatment step includes a quenching step and a tempering step.
- the quenching temperature in the quenching process is equal to or higher than the Ac 3 transformation point.
- the preferable lower limit of the quenching temperature is 800 ° C.
- the preferable upper limit is 1000 ° C.
- Tempering is performed on the intermediate material after the quenching process.
- a preferable tempering temperature T is 550 to 650 ° C.
- a preferable holding time at the tempering temperature T is 4 to 12 hours.
- the Larson-Miller parameter LMP in the tempering process is 16000-18000.
- the Larson-Miller parameter LMP is too small, tempering is insufficient and strain remains in the steel. Therefore, desirable mechanical characteristics cannot be obtained. Specifically, the strength is too high, and as a result, the SCC resistance and the SSC resistance are lowered. Therefore, a preferred lower limit for the Larson-Miller parameter LMP is 16000. On the other hand, if the Larson-Miller parameter LMP is too large, an excessive amount of Laves phase is generated. As a result, F1 does not satisfy the formula (1). In this case, SCC resistance and SSC resistance are lowered. Therefore, the upper limit of the Larson-Miller parameter LMP is 18000. A preferred lower limit of the Larson-Miller parameter LMP is 16500, more preferably 17000, and even more preferably 17500. A preferred upper limit of the Larson-Miller parameter LMP is 17970, more preferably 17940.
- the downhole member by this embodiment is manufactured using the above-mentioned steel bar for downhole members. Specifically, the downhole member having a desired shape is manufactured by cutting the steel bar for the downhole member.
- the downhole member has the same chemical composition as the steel bar for the downhole member.
- the downhole member further defines the Mo content in the chemical composition of the downhole member as [Mo amount] (% by mass), and the surface of the downhole member and the downhole in a cross section perpendicular to the longitudinal direction of the downhole member
- Mo amount % by mass
- mass the Mo content in the precipitate at a position that bisects the center of the member
- the formula (1) is satisfied.
- the downhole member having the above configuration has a sufficient amount of solid solution Mo in a cross section perpendicular to the longitudinal direction, and has a uniform microstructure. Therefore, the entire cross section perpendicular to the longitudinal direction has excellent SCC resistance and SSC resistance.
- the downhole member when the center part of the steel bar for downhole members remains, the downhole member satisfy
- test numbers 1 to 22 slabs were manufactured by a continuous casting method.
- the hot work shown in Table 2 any of free forging, rotary forging, and hot rolling is performed on the slab, and the cross section perpendicular to the longitudinal direction is circular.
- a solid intermediate material (bar) having a diameter was produced.
- test numbers 23 to 26 slabs were manufactured by the continuous casting method using the above molten steel. The slab was rolled into billets and then subjected to piercing and rolling by the Mannesmann method to produce an intermediate material (seamless steel pipe) having the outer diameter shown in Table 2 and having a through hole in the center. .
- the wall thickness of test numbers 23, 24, and 26 was 17.78 mm, and the wall thickness of test number 25 was 26.24 mm.
- the manufactured intermediate material (bar steel, seamless steel pipe) was kept at the quenching temperature (° C.) shown in Table 2 for 0.5 hour and then quenched (rapidly cooled).
- the quenching temperature was equal to or higher than the Ac 3 transformation point in any of the test numbers.
- the intermediate material was tempered at 550 to 650 ° C. with a holding time of 4 to 12 hours and the Larson-Miller parameter LMP shown in Table 2 was tempered.
- An example is a seamless steel pipe.
- the component analysis method was implemented by the following method with respect to the steel material of each test number, and the chemical composition containing [Mo amount] was analyzed.
- a sample having a length of 20 mm was taken by cutting perpendicularly to the longitudinal direction of the steel material of each test number.
- the sample was cut into chips and dissolved in acid to obtain a solution.
- the solution was subjected to ICP-OES (Inductively Coupled Plasma Optical Emission Spectrometry) to perform elemental analysis of chemical composition. About C content and S content, the said solution was burned by high frequency heating in oxygen stream, the generated carbon dioxide and sulfur dioxide were detected, and C content and S content were calculated
- ICP-OES Inductively Coupled Plasma Optical Emission Spectrometry
- Sample including a position (referred to as R / 2 position) that bisects the surface and center of the downhole member steel bar in an arbitrary cross section perpendicular to the longitudinal direction of the downhole member steel bars of test numbers 1 to 22 9 mm and length 70 mm).
- the longitudinal direction of the sample was parallel to the longitudinal direction of the downhole member steel bar, and the center of the cross section of the sample (circle having a diameter of 9 mm) was the R / 2 position of the downhole member steel bar.
- the test material was electrolyzed using a 10% AA electrolyte (10% acetylacetone-1% tetramethylammonium chloride-methanol electrolyte). The current during electrolysis was 20 mA / cm 2 .
- the electrolyte was filtered through a 200 nm filter, and the mass of the residue was measured to determine [R / 2 position precipitate total mass].
- the amount of Mo contained in the solution obtained by acid decomposition of the residue was determined by ICP emission spectroscopic analysis. Based on the amount of Mo in the solution and the [total mass of R / 2 position precipitate], the total Mo content in the precipitate when the total mass of the precipitate at the R / 2 position is 100 (mass%) ( Mass%). Five samples were collected at arbitrary locations, and the average value of the total Mo content in the precipitate obtained from each sample was defined as [total Mo amount in the R / 2 position precipitate] (mass%).
- a sample (diameter 9 mm, length 70 mm) including the center position of the downhole member steel bar in an arbitrary cross section perpendicular to the longitudinal direction of the downhole member steel bars of test numbers 1 to 22 was collected.
- the center of the cross section of the sample (circle with a diameter of 9 mm) coincided with the central axis of the downhole member steel bar.
- Five samples were collected at arbitrary locations.
- the amount of Mo in the solution and [Total mass of precipitate at center position] are obtained, and the total mass of precipitate at the center position is 100 (mass%).
- the total Mo content (% by mass) in the precipitate was determined.
- the average value of the total Mo content in the precipitate obtained from each sample (total of 5) was defined as [total Mo amount in center position precipitate] (mass%).
- the test material was electrolyzed using a 10% AA electrolyte (10% acetylacetone-1% tetramethylammonium chloride-methanol electrolyte). The current during electrolysis was 20 mA / cm 2 . The electrolyte was filtered through a 200 nm filter, and the mass of the residue was measured to determine [thickness / 2-position precipitate total mass]. Furthermore, the amount of Mo contained in the solution obtained by acid decomposition of the residue was determined by ICP emission spectroscopic analysis.
- the [total amount of Mo in the thickness / 2-position precipitate] of the test numbers 23 to 26 is described in the [total amount of Mo in the R / 2-position precipitate] column of Table 2.
- F1 of test numbers 23 to 26 was obtained by the following formula.
- F1 of test numbers 23 to 26 [Mo amount] ⁇ 4 ⁇ [thickness / 2-position total Mo amount in precipitates]
- Tensile test pieces were taken from the R / 2 position of the steel bars for downhole members of test numbers 1 to 22.
- the longitudinal direction of the tensile test pieces of test numbers 1 to 22 was parallel to the longitudinal direction of the downhole member steel bar, and the central axis coincided with the R / 2 position of the downhole member steel bar.
- tensile test pieces were collected from the center of the thickness of the seamless steel pipes having test numbers 23 to 26.
- the longitudinal direction of the tensile test pieces of test numbers 23 to 26 was parallel to the longitudinal direction of the seamless steel pipe, and the central axis coincided with the thickness / 2 position of the seamless steel pipe.
- each tensile test piece was 35.6 mm or 25.4 mm.
- a tensile test was carried out at room temperature (25 ° C.) and in the atmosphere to determine yield strength (MPa, ksi) and tensile strength (MPa, ksi).
- the longitudinal direction of the round bar specimens taken from the thickness / 2 position of the seamless steel pipes of test numbers 23 to 26 was parallel to the longitudinal direction of the seamless steel pipe, and the central axis coincided with the thickness / 2 position.
- the outer diameter of the parallel part of each round bar test piece was 6.35 mm, and the length of the parallel part was 25.4 mm.
- the SSC resistance of each round bar test piece was evaluated by a constant load test.
- Each round bar specimen was loaded with a load stress corresponding to 90% of the actual yield stress (AYS) of each steel number and immersed in the test bath for 720 hours. After 720 hours, it was confirmed by an optical microscope with a 100 ⁇ field of view whether or not each round bar specimen was broken. When it was not broken, it was judged that the SSC resistance of the steel was high (indicated as “No SSC” in Table 2). When it was fractured, it was judged that the SSC resistance of the steel was low (indicated as “SSC” in Table 2).
- the longitudinal direction of the rectangular specimens taken from the thickness / 2 position of the seamless steel pipes of test numbers 23 to 26 was parallel to the longitudinal direction of the seamless steel pipe, and the central axis coincided with the thickness / 2 position.
- Each rectangular test piece had a thickness of 2 mm, a width of 10 mm, and a length of 75 mm.
- Each test piece was subjected to a stress corresponding to 100% of the actual yield stress (AYS) of the steel material of each test number by four-point bending according to ASTM G39.
- each test piece was examined for the presence of stress corrosion cracking (SCC). Specifically, the cross section of each test piece to which a tensile stress was applied was observed with an optical microscope with a 100 ⁇ field of view, and the presence or absence of cracks was determined. When SCC was confirmed, it was judged that the SCC resistance was low (indicated as “No SCC” in Table 2). When SCC was not confirmed, it was judged that SCC resistance was high (displayed as “SCC” in Table 2).
- SCC stress corrosion cracking
- test number 19 the Cu content was too high. For this reason, F2 did not satisfy the formula (2) even though the forging ratio in hot working was appropriate. As a result, SCC and SSC were confirmed at the center position, and SSC resistance and SCC resistance were low.
- test numbers 21 and 22 the chemical composition was appropriate, but the forging ratio in hot working was too low. Therefore, F2 did not satisfy the formula (2). As a result, SCC and SSC were confirmed at the center position, and SSC resistance and SCC resistance were low.
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Abstract
Description
[Mo量]-4×[R/2位置析出物中総Mo量]≧1.30 (1)
[中心位置析出物中総Mo量]-[R/2位置析出物中総Mo量]≦0.03 (2)
本実施形態では、C:0.020%以下、Si:1.0%以下、Mn:1.0%以下、P:0.03%以下、S:0.01%以下、Cr:10~14%、Ni:1.5~7.0%、Mo:0.2~3.0%、Ti:0.05~0.3%、V:0.01~0.10%、Nb:0.1%以下、Al:0.001~0.1%、及び、N:0.05%以下を含有するダウンホール部材用棒鋼に対して、N含有量を増加するのではなく、Nと同じオーステナイト形成元素であるCuを0.10~2.50質量%含有する。この場合、上記化学組成のステンレス棒鋼において、Cu含有によりラーベス相の析出量が低減される。さらに、Cuは固溶Nほど鋼材の強度を高めないため、焼戻し時間を抑制できる。Cu含有量が0.10~2.50%であれば、これらの効果を十分に得ることができる。
ダウンホール部材用棒鋼の化学組成でのMo含有量を[Mo量](質量%)と定義し、ダウンホール部材用棒鋼の長手方向に垂直な断面における、ダウンホール部材用棒鋼の表面とダウンホール部材用棒鋼の中心とを二等分する位置(以下、R/2位置という)での析出物中のMo含有量を[R/2位置析出物中総Mo量](質量%)と定義する。ここで、析出物中のMo含有量とは、R/2位置のミクロ組織の析出物の総質量を100%(質量%)とした場合の、析出物中のMoの総含有量(質量%)を意味する。このとき、上記化学組成を有するダウンホール部材用棒鋼はさらに、式(1)を満たす。
[Mo量]-4×[R/2位置析出物中総Mo量]≧1.3 (1)
上述のとおり、ダウンホール部材用棒鋼の長手方向に垂直な断面において、中心部のミクロ組織は、その他の領域のミクロ組織となるべく均一である方が好ましい。以下、この点について説明する。
[R/2位置析出物中総Mo量]-[中心位置析出物中総Mo量]≦0.03 (2)
上述のダウンホール部材用棒鋼は、たとえば、次の製造方法により製造できる。上記化学組成を有する素材に対して熱間加工工程を実施し、その後、焼入れ及び焼戻しを含む調質熱処理工程を実施する。
鍛錬成形比=熱間加工実施前の素材の断面積(mm2)/熱間加工完了後の素材の断面積(mm2) (A)
LMP=(T+273)×(20+log(t)) (B)
[Mo量]-4×[R/2位置析出物中総Mo量]≧1.30 (1)
[中心位置析出物中総Mo量]-[R/2位置析出物中総Mo量]≦0.03 (2)
[Mo量]-4×[R/2位置析出物中総Mo量]≧1.3 (1)
本実施形態のダウンホール部材用棒鋼の化学組成は、次の元素を含有する。
炭素(C)は、不可避に含有される。Cは、鋼の強度を高めるものの、焼戻し時にCr炭化物を生成する。Cr炭化物は、耐食性(耐SCC性、耐SSC性)を低下する。したがって、C含有量は低い方が好ましい。C含有量は0.020%以下である。好ましいC含有量の上限は0.015%であり、さらに好ましくは0.012%であり、さらに好ましくは0.010%である。
シリコン(Si)は、不可避に含有される。Siは鋼を脱酸する。しかしながら、Si含有量が高すぎれば、熱間加工性が低下する。さらに、フェライト生成量が増加し、鋼材の強度が低下する。したがって、Si含有量は1.0%以下である。好ましいSi含有量は1.0%未満であり、さらに好ましくは0.50%以下であり、さらに好ましくは0.30%以下である。Si含有量が0.05%以上であれば、Siは脱酸剤として特に有効に作用する。しかしながら、Si含有量が0.05%未満であっても、Siは、鋼をある程度脱酸する。
マンガン(Mn)は、不可避に含有される。Mnは鋼を脱酸及び脱硫し、熱間加工性を向上する。しかしながら、Mn含有量が多すぎると、鋼中に偏析が生じやすくなり、靭性及び高温塩化物水溶液中での耐SCC性が低下する。さらに、Mnはオーステナイト形成元素である。そのため、鋼が、オーステナイト形成元素であるNi及びCuを含有する場合、Mn含有量が多すぎれば、残留オーステナイトが増加し、鋼の強度が低下する。したがって、Mn含有量は1.0%以下である。好ましいMn含有量の下限は0.10%であり、さらに好ましくは0.30%である。好ましいMn含有量の上限は0.8%であり、さらに好ましくは0.5%である。
燐(P)は、不純物である。Pは、鋼の耐SSC性及び耐SCC性を低下する。したがって、P含有量は0.03%以下である。好ましいP含有量の上限は0.025%であり、さらに好ましくは0.022%であり、さらに好ましくは0.020%である。P含有量はなるべく少ない方が好ましい。
硫黄(S)は、不純物である。Sは、鋼の熱間加工性を低下する。Sはさらに、Mn等と結合し介在物を形成する。形成された介在物はSCCやSSCの起点となり、鋼の耐食性を低下する。したがって、S含有量は0.01%以下である。好ましいS含有量の上限は0.0050%であり、さらに好ましくは0.0020%であり、さらに好ましくは0.0010%である。S含有量はなるべく少ない方が好ましい。
銅(Cu)は、ラーベス相の生成を抑制する。その理由は定かではないが、次の事項が考えられる。Cuは、Cu粒子としてマトリクス中に微細分散する。分散したCu粒子のピンニング効果により、ラーベス相の生成及び成長が抑制される。これにより、ラーベス相の析出量が抑制され、固溶Mo量の低下が抑制される。その結果、棒鋼において、耐SCC性及び耐SSC性が高まる。Cu含有量が低すぎればこの効果が得られない。一方、Cu含有量が高すぎれば、Cr及びMoの中心偏析が過剰に促進され、その結果、式(2)が満たされなくなる。この場合、ダウンホール部材用棒鋼の全体で優れた耐SCC性及び耐SSC性が得られない場合がある。Cu含有量が高ければさらに、鋼材の熱間加工性が低下する。したがって、Cu含有量は0.10~2.50%である。Cu含有量の好ましい下限は0.15%であり、さらに好ましくは0.17%である。Cu含有量の好ましい上限は2.00%であり、さらに好ましくは1.50%であり、さらに好ましくは1.20%である。
クロム(Cr)は、鋼の耐SCC性及び耐SSC性を高める。Cr含有量が低すぎればこの効果が得られない。一方、Crはフェライト形成元素である。そのため、Cr含有量が多すぎると、鋼中にフェライトが生成して鋼の降伏強度が低下する。したがって、Cr含有量は10~14%である。好ましいCr含有量の下限は11%であり、さらに好ましくは11.5%であり、さらに好ましくは11.8%である。好ましいCr含有量の上限は13.5%であり、さらに好ましくは13.0%であり、さらに好ましくは12.5%である。
ニッケル(Ni)は、オーステナイト形成元素である。そのため、高温での鋼中のオーステナイトを安定化し、常温でのマルテンサイト量を増加する。これにより、Niは鋼の強度を高める。Niはさらに、鋼の耐食性(耐SCC性及び耐SSC性)を高める。Ni含有量が低すぎれば、これらの効果が得られない。一方、Ni含有量が高すぎれば、残留オーステナイトが増加しやすくなり、特に工業生産時において、高強度のダウンホール部材用棒鋼を安定的に得ることが困難になる。したがって、Ni含有量は1.5~7.0%である。Ni含有量の好ましい下限は3.0%であり、さらに好ましくは4.0%である。Ni含有量の好ましい上限は6.5%であり、さらに好ましくは6.2%である。
油井において生産流体の生産が一時停止したとき、油井管内の流体の温度は低下する。このとき、ダウンホール部材の硫化物応力腐食割れ感受性は高くなる。モリブデン(Mo)は、耐SSC性を高める。Moはさらに、Crとの共存下において鋼の耐SCC性を高める。Mo含有量が低すぎれば、これらの効果が得られない。一方、Moはフェライト形成元素であるため、Mo含有量が多すぎれば、鋼中のフェライトが生成して鋼の強度が低下する。したがって、Mo含有量は0.2~3.0%である。好ましいMo含有量の下限は1.0%であり、さらに好ましくは1.5%であり、さらに好ましくは1.8%である。好ましいMo含有量の上限は2.8%であり、さらに好ましくは2.8%未満であり、さらに好ましくは2.7%であり、さらに好ましくは2.6%であり、さらに好ましくは2.5%である。
チタン(Ti)は炭化物を形成して鋼の強度及び靭性を高める。ダウンホール部材用棒鋼の直径が大きければさらに、Ti炭化物はダウンホール部材用棒鋼の強度ばらつきを低減する。Tiはさらに、Cを固定してCr炭化物の生成を抑制し、耐SCC性を高める。Ti含有量が低すぎれば、これらの効果が得られない。一方、Ti含有量が高すぎれば、炭化物が粗大化して鋼の靭性及び耐食性が低下する。したがって、Ti含有量は0.05~0.3%である。Ti含有量の好ましい下限は0.06%であり、さらに好ましくは0.08%であり、さらに好ましくは0.10%である。Ti含有量の好ましい上限は0.2%であり、さらに好ましくは0.15%であり、さらに好ましくは0.12%である。
バナジウム(V)は、炭化物を形成して鋼の強度及び靭性を高める。Vはさらに、Cを固定してCr炭化物の生成を抑制し、耐SCC性を高める。V含有量が低すぎれば、これらの効果が得られない。一方、V含有量が高すぎれば、炭化物が粗大化して鋼の靭性及び耐食性が低下する。したがって、V含有量は0.01~0.10%である。V含有量の好ましい下限は0.03%であり、さらに好ましくは0.05%である。V含有量の好ましい上限は0.08%であり、さらに好ましくは0.07%である。
ニオブ(Nb)は不純物である。Nbは炭化物を形成して鋼材の強度及び靭性を高める効果があるものの、Nb含有量が高すぎれば、炭化物が粗大化して鋼材の靭性及び耐食性が低下する。したがって、Nb含有量は0.1%以下である。Nb含有量の好ましい上限は0.05%であり、さらに好ましくは0.02%であり、さらに好ましくは0.01%である。
アルミニウム(Al)は、鋼を脱酸する。Al含有量が低すぎれば、この効果が得られない。一方、Al含有量が高すぎれば、鋼中のフェライト量が増加して鋼の強度が低下する。さらに、アルミナ系介在物が鋼中に多量に生成され、鋼材の靭性が低下する。したがって、Al含有量は0.001~0.1%である。Al含有量の好ましい下限は0.005%であり、さらに好ましくは0.010%であり、さらに好ましくは0.020%である。好ましいAl含有量の上限は0.080%であり、さらに好ましくは0.060%であり、さらに好ましくは0.050%である。なお、本実施形態の棒鋼材において、Al含有量は酸可溶Al(sol.Al)含有量を意味する。
窒素(N)は不純物である。Nは、鋼の強度を高める効果があるものの、N含有量が高すぎれば、鋼の靭性が低下するとともに、鋼材の強度が過剰に高くなる。この場合、強度調整のために焼戻し時間を長くしなければならず、ラーベス相が生成しやすくなる。ラーベス相が生成すれば固溶Mo量が低下するため、耐SCC性、耐SSC性が低下する。したがって、N含有量は0.05%以下である。N含有量の好ましい上限は0.030%であり、さらに好ましくは0.020%であり、さらに好ましくは0.010%である。
本実施形態の棒鋼はさらに、Feの一部に代えて、B及びCaからなる群から選択される1種以上を含有してもよい。これらの元素はいずれも任意元素であり、熱間加工における疵や欠陥の発生を抑制する。
Ca:0~0.008%
ボロン(B)及びカルシウム(Ca)はいずれも任意元素であり、含有されなくてもよい。含有される場合、B及びCaはいずれも、熱間加工における疵や欠陥の発生を抑制する。B及びCaの少なくとも1種以上が少しでも含有されれば、上記効果がある程度得られる。一方、B含有量が高すぎれば、結晶粒界にCrの炭硼化物が析出し、鋼の靭性が低下する。また、Ca含有量が高すぎれば、鋼中の介在物が増加して、鋼の靭性及び耐食性が低下する。したがって、B含有量は0~0.005%であり、Ca含有量は0~0.008%である。B含有量の好ましい下限は0.0001%であり、好ましい上限は0.0002%である。Ca含有量の好ましい下限は0.0005%であり、好ましい上限は0.0020%である。
コバルト(Co)は任意元素であり、含有されなくてもよい。含有される場合、Coは鋼の焼入性を高め、特に工業生産時において、安定した高強度を確保する。より具体的には、Coは残留オーステナイトを抑制し、強度のばらつきを抑制する。Coが少しでも含有されれば、上記効果がある程度得られる。しかしながら、Co含有量が多すぎれば、鋼の靭性が低下する。したがって、Co含有量は、0~0.5%である。Co含有量の好ましい下限は0.05%であり、さらに好ましくは0.07%であり、さらに好ましくは0.10%である。Co含有量の好ましい上限は0.40%であり、さらに好ましくは0.30%であり、さらに好ましくは0.25%である。
本実施形態のダウンホール部材用棒鋼において、[Mo量](質量%)と、[R/2位置析出物中総Mo量](質量%)とを次のとおり定義する。
[Mo量]:ダウンホール部材用棒鋼の化学組成におけるMo含有量(質量%)
[R/2位置析出物中総Mo量]:ダウンホール部材用棒鋼の長手方向に垂直な断面において、ダウンホール部材用棒鋼の表面と中心とを二等分する位置(R/2位置という)でのミクロ組織における、析出物の総質量を100%とした場合の、析出物中の総Mo含有量(質量%)
[Mo量]-4×[R/2位置析出物中総Mo量]≧1.30 (1)
ダウンホール部材用棒鋼の長手方向に垂直な断面の中心位置において、析出物の総質量を100(質量%)とした場合の析出物中の総Mo含有量(質量%)を[中心位置析出物中総Mo量](質量%)と定義する。このとき、本実施形態のダウンホール部材用棒鋼は、上記化学組成を有し、かつ、式(1)を満たすことを前提として、さらに式(2)を満たす。
[中心位置析出物中総Mo量]-[R/2位置析出物中総Mo量]≦0.03 (2)
本実施形態のダウンホール部材用棒鋼はたとえば、次の製造方法により製造可能である。ただし、本実施形態のダウンホール部材の製造方法は本例に限定されない。以下、本実施形態のダウンホール部材用棒鋼の製造方法の一例を説明する。本製造方法は、熱間加工により中間材(ビレット)を製造する工程(熱間加工工程)と、中間材に対して焼入れ及び焼戻しを実施して強度を調整し、ダウンホール部材用棒鋼とする工程(調質熱処理工程)とを含む。以下、各工程について説明する。
上述の化学組成を有する中間材を準備する。具体的には、上述の化学組成を有する溶鋼を製造する。溶鋼を用いて、素材を製造する。連続鋳造法により素材である鋳片を製造してもよい。溶鋼を用いて素材であるインゴットを製造してもよい。
鍛錬成形比=熱間加工実施前の素材の断面積(mm2)/熱間加工完了後の素材の断面積(mm2) (A)
中間材に対して調質熱処理を実施する(調質熱処理工程)。調質熱処理工程は、焼入れ工程と焼戻し工程とを含む。
熱間加工工程により製造された中間材に対して、周知の焼入れ処理を実施する。焼入れ処理における焼入れ温度はAc3変態点以上である。上記化学組成を有する中間材において、焼入れ温度の好ましい下限は800℃であり、好ましい上限は1000℃である。
焼入れ工程後の中間材に対して、焼戻しを実施する。好ましい焼戻し温度Tは550~650℃である。焼戻し温度Tでの好ましい保持時間は4~12時間である。
LMP=(T+273)×(20+log(t)) (B)
式(B)中のTは焼戻し温度(℃)であり、tは焼戻し温度Tでの保持時間(hr)である。
本実施形態によるダウンホール部材は、上述のダウンホール部材用棒鋼を用いて製造される。具体的には、ダウンホール部材用棒鋼に対して切削加工を実施して、所望の形状のダウンホール部材を製造する。
[Mo量]-4×[R/2位置析出物中総Mo量]≧1.3 (1)
各試験番号の鋼材に対して、次の方法により成分分析法を実施して、[Mo量]を含む化学組成の分析を実施した。各試験番号の鋼材の長手方向に対して垂直に切断し、長さ20mmのサンプルを採取した。サンプルを切粉にして、酸に溶解させて溶液を得た。溶液に対して、ICP-OES(Inductively Coupled Plasma Optical Emission Spectrometry)を実施して、化学組成の元素分析を実施した。C含有量及びS含有量については、上記溶液を酸素気流中で高周波加熱により燃焼して、発生した二酸化炭素、二酸化硫黄を検出して、C含有量及びS含有量を求めた。
試験番号1~22のダウンホール部材用棒鋼の長手方向に垂直な任意の断面において、ダウンホール部材用棒鋼の表面と中心とを二等分する位置(R/2位置という)を含むサンプル(直径9mm、長さ70mm)を採取した。サンプルの長手方向はダウンホール部材用棒鋼の長手方向に平行であり、サンプルの横断面(直径9mmの円)の中心は、ダウンホール部材用棒鋼のR/2位置であった。10%AA系電解液(10%アセチルアセトン‐1%テトラメチルアンモニウムクロライド‐メタノール電解液)を用いて供試材を電解した。電解時の電流は20mA/cm2とした。電解液を200nmのフィルターでろ過して残渣の質量を測定し、[R/2位置析出物総質量]を求めた。さらに、残渣を酸分解した溶液中に含まれるMo量を、ICP発光分光分析で求めた。溶液中のMo量及び[R/2位置析出物総質量]に基づいて、R/2位置での析出物の総質量を100(質量%)としたときの析出物中の総Mo含有量(質量%)を求めた。サンプルは任意の箇所で5つ採取し、各サンプルから求めた析出物中の総Mo含有量の平均値を、[R/2位置析出物中総Mo量](質量%)と定義した。
試験番号23~26のF1=[Mo量]-4×[肉厚/2位置析出物中総Mo量]
試験番号1~22のダウンホール部材用棒鋼のR/2位置から、引張試験片を採取した。試験番号1~22の引張試験片の長手方向は、ダウンホール部材用棒鋼の長手方向と平行であり、中心軸はダウンホール部材用棒鋼のR/2位置に一致した。また、試験番号23~26の継目無鋼管の肉厚中央位置から、引張試験片を採取した。試験番号23~26の引張試験片の長手方向は、継目無鋼管の長手方向と平行であり、中心軸は、継目無鋼管の肉厚/2位置と一致した。各引張試験片の平行部の長さは35.6mm又は25.4mmであった。引張試験片を用いて、常温(25℃)、大気中にて引張試験を実施して、降伏強度(MPa、ksi)及び引張強度(MPa、ksi)を求めた。
試験番号1~22のダウンホール部材用棒鋼のR/2位置、及び、中心位置から、及び、試験番号23~26の継目無鋼管の肉厚/2(肉厚中央位置)から、丸棒試験片を採取した。試験番号1~22のダウンホール部材用棒鋼のR/2位置から採取した丸棒試験片の長手方向はダウンホール部材用棒鋼の長手方向と平行であり、中心軸はR/2位置と一致した。試験番号1~22のダウンホール部材用棒鋼の中心位置から採取した丸棒試験片の長手方向はダウンホール部材用棒鋼の長手方向と平行であり、中心軸はダウンホール部材用棒鋼の中心位置と一致した。試験番号23~26の継目無鋼管の肉厚/2位置から採取した丸棒試験片の長手方向は継目無鋼管の長手方向と平行であり、中心軸は肉厚/2位置と一致した。各丸棒試験片の平行部の外径は6.35mm、平行部の長さは25.4mmであった。
試験番号1~22のダウンホール部材用棒鋼のR/2位置、及び、中心位置から、及び、試験番号23~26の継目無鋼管の肉厚/2(肉厚中央位置)から、矩形試験片を採取した。試験番号1~22のダウンホール部材用棒鋼のR/2位置から採取した矩形試験片の長手方向はダウンホール部材用棒鋼の長手方向と平行であり、中心軸はR/2位置と一致した。試験番号1~22のダウンホール部材用棒鋼の中心位置から採取した矩形試験片の長手方向はダウンホール部材用棒鋼の長手方向と平行であり、中心軸はダウンホール部材用棒鋼の中心位置と一致した。試験番号23~26の継目無鋼管の肉厚/2位置から採取した矩形試験片の長手方向は継目無鋼管の長手方向と平行であり、中心軸は肉厚/2位置と一致した。各矩形試験片の厚さは2mmであり、幅は10mmであり、長さは75mmであった。
表2を参照して、試験番号1~12のダウンホール部材用鋼材の化学組成は適切であり、特に、Cu含有量が0.10~2.50の範囲内であった。さらに、F1が式(1)を満たし、F2が式(2)を満たした。その結果、降伏強度YSは758MPa(110ksi)以上であり、高強度が得られた。さらに、高強度であるにもかかわらず、R/2位置及び中心位置のいずれにおいてもSCC及びSSCが発生せず、耐SCC性及び耐SSC性に優れた。
Claims (3)
- ダウンホール部材用棒鋼であって、
質量%で、
C:0.020%以下、
Si:1.0%以下、
Mn:1.0%以下、
P:0.03%以下、
S:0.01%以下、
Cu:0.10~2.50%、
Cr:10~14%、
Ni:1.5~7.0%、
Mo:0.2~3.0%、
Ti:0.05~0.3%、
V:0.01~0.10%、
Nb:0.1%以下、
Al:0.001~0.1%、
N:0.05%以下、
B:0~0.005%、
Ca:0~0.008%、及び、
Co:0~0.5%、
を含有し、残部はFe及び不純物からなる化学組成を有し、
前記ダウンホール部材用棒鋼の前記化学組成でのMo含有量を[Mo量](質量%)と定義し、前記ダウンホール部材用棒鋼の表面と前記ダウンホール部材用棒鋼の長手方向に垂直な断面の中心とを二等分する位置での析出物中のMo含有量を[R/2位置析出物中総Mo量](質量%)と定義したとき、式(1)を満たし、
前記ダウンホール部材用棒鋼の長手方向に垂直な断面の中心位置での析出物中のMo含有量を[中心位置析出物中総Mo量]と定義したとき、式(2)を満たす、ダウンホール部材用棒鋼。
[Mo]-4×[R/2位置析出物中総Mo量]≧1.30 (1)
[中心位置析出物中総Mo量]-[R/2位置析出物中総Mo量]≦0.03 (2) - 請求項1に記載のダウンホール部材用棒鋼であって、
前記化学組成は、Feの一部に代えて、
B:0.0001~0.005%、及び、
Ca:0.0005~0.008%、
からなる群から選択される1種以上を含有する、ダウンホール部材用棒鋼。 - 請求項1又は請求項2に記載のダウンホール部材用棒鋼であって、
前記化学組成は、Feの一部に代えて、
Co:0.05~0.5%、
を含有する、ダウンホール部材用棒鋼。
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AU2017266359A AU2017266359B2 (en) | 2016-05-20 | 2017-05-19 | Steel bar for downhole member and downhole member |
CA3024694A CA3024694A1 (en) | 2016-05-20 | 2017-05-19 | Steel bar for downhole member, and downhole member |
JP2017548488A JP6264521B1 (ja) | 2016-05-20 | 2017-05-19 | ダウンホール部材用棒鋼、及び、ダウンホール部材 |
EP17799507.3A EP3460087B1 (en) | 2016-05-20 | 2017-05-19 | Steel bar for downhole member and downhole member |
MX2018014132A MX2018014132A (es) | 2016-05-20 | 2017-05-19 | Barra de acero para miembro de fondo de pozo y el miembro de fondo de pozo. |
RU2018144619A RU2710808C1 (ru) | 2016-05-20 | 2017-05-19 | Стальной сортовой прокат для скважинного элемента и скважинный элемент |
BR112018072904-3A BR112018072904B1 (pt) | 2016-05-20 | 2017-05-19 | Barra de aço para membro de fundo de poço e membro de fundo de poço |
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EP (1) | EP3460087B1 (ja) |
JP (1) | JP6264521B1 (ja) |
CN (1) | CN109154054B (ja) |
AU (1) | AU2017266359B2 (ja) |
BR (1) | BR112018072904B1 (ja) |
CA (1) | CA3024694A1 (ja) |
MX (1) | MX2018014132A (ja) |
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Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000192203A (ja) * | 1998-10-12 | 2000-07-11 | Sumitomo Metal Ind Ltd | ダウンホ―ル部材用マルテンサイト系ステンレス鋼とその製法 |
JP2010242163A (ja) * | 2009-04-06 | 2010-10-28 | Jfe Steel Corp | 油井管用マルテンサイト系ステンレス継目無鋼管の製造方法 |
JP2011089159A (ja) * | 2009-10-21 | 2011-05-06 | Jfe Steel Corp | 耐粒界応力腐食割れ性に優れたマルテンサイト系ステンレス鋼溶接管の製造方法 |
Family Cites Families (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH1180881A (ja) * | 1997-09-05 | 1999-03-26 | Nkk Corp | 溶接部靭性と耐硫化物腐食割れ性に優れた高クロム溶接 鋼管 |
JP2001107141A (ja) * | 1999-09-30 | 2001-04-17 | Nkk Corp | 溶接部靭性と耐硫化物腐食割れ性に優れた高クロム溶接鋼管 |
JP2001179485A (ja) * | 1999-12-27 | 2001-07-03 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス溶接鋼管およびその製造方法 |
JP4449174B2 (ja) * | 2000-06-19 | 2010-04-14 | Jfeスチール株式会社 | 油井用高強度マルテンサイト系ステンレス鋼管の製造方法 |
AR042494A1 (es) * | 2002-12-20 | 2005-06-22 | Sumitomo Chemical Co | Acero inoxidable martensitico de alta resistencia con excelentes propiedades de resistencia a la corrosion por dioxido de carbono y resistencia a la corrosion por fisuras por tensiones de sulfuro |
CN100532611C (zh) * | 2003-07-22 | 2009-08-26 | 住友金属工业株式会社 | 马氏体不锈钢 |
JP4462005B2 (ja) * | 2003-10-31 | 2010-05-12 | Jfeスチール株式会社 | 耐食性に優れたラインパイプ用高強度ステンレス鋼管およびその製造方法 |
BRPI0416001B1 (pt) * | 2003-10-31 | 2017-04-11 | Jfe Steel Corp | tubo de aço inoxidável sem costura para tubulações de condução |
JP4337712B2 (ja) * | 2004-11-19 | 2009-09-30 | 住友金属工業株式会社 | マルテンサイト系ステンレス鋼 |
CN101506400A (zh) * | 2006-08-22 | 2009-08-12 | 住友金属工业株式会社 | 马氏体系不锈钢 |
JP5040215B2 (ja) * | 2006-08-24 | 2012-10-03 | Jfeスチール株式会社 | 拡管性に優れる油井用ステンレス鋼管 |
WO2008026594A1 (fr) * | 2006-08-31 | 2008-03-06 | Sumitomo Metal Industries, Ltd. | Acier inoxydable martensitique pour structure soudee |
JP5640777B2 (ja) * | 2011-01-31 | 2014-12-17 | Jfeスチール株式会社 | 溶接熱影響部の耐粒界応力腐食割れ性に優れたラインパイプ用Cr含有鋼管 |
MX2014011861A (es) * | 2012-04-05 | 2014-11-21 | Nippon Steel & Sumitomo Metal Corp | Alambron de acero o barra de acero que tienen una excelente capacidad de forjado en frio. |
JP5924256B2 (ja) * | 2012-06-21 | 2016-05-25 | Jfeスチール株式会社 | 耐食性に優れた油井用高強度ステンレス鋼継目無管およびその製造方法 |
JP5861786B2 (ja) * | 2013-01-16 | 2016-02-16 | Jfeスチール株式会社 | 油井用ステンレス継目無鋼管およびその製造方法 |
EP3042968B1 (en) * | 2013-09-04 | 2020-12-09 | JFE Steel Corporation | Method of manufacturing a high-strength stainless steel pipe and high-strength stainless steel pipe |
-
2017
- 2017-05-19 RU RU2018144619A patent/RU2710808C1/ru active
- 2017-05-19 AU AU2017266359A patent/AU2017266359B2/en active Active
- 2017-05-19 JP JP2017548488A patent/JP6264521B1/ja active Active
- 2017-05-19 US US16/099,330 patent/US10995394B2/en active Active
- 2017-05-19 MX MX2018014132A patent/MX2018014132A/es unknown
- 2017-05-19 CA CA3024694A patent/CA3024694A1/en not_active Abandoned
- 2017-05-19 CN CN201780030687.5A patent/CN109154054B/zh active Active
- 2017-05-19 EP EP17799507.3A patent/EP3460087B1/en active Active
- 2017-05-19 BR BR112018072904-3A patent/BR112018072904B1/pt active IP Right Grant
- 2017-05-19 WO PCT/JP2017/018804 patent/WO2017200083A1/ja unknown
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000192203A (ja) * | 1998-10-12 | 2000-07-11 | Sumitomo Metal Ind Ltd | ダウンホ―ル部材用マルテンサイト系ステンレス鋼とその製法 |
JP2010242163A (ja) * | 2009-04-06 | 2010-10-28 | Jfe Steel Corp | 油井管用マルテンサイト系ステンレス継目無鋼管の製造方法 |
JP2011089159A (ja) * | 2009-10-21 | 2011-05-06 | Jfe Steel Corp | 耐粒界応力腐食割れ性に優れたマルテンサイト系ステンレス鋼溶接管の製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP3460087A4 * |
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WO2019065116A1 (ja) * | 2017-09-29 | 2019-04-04 | Jfeスチール株式会社 | 油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法 |
JP6540921B1 (ja) * | 2017-09-29 | 2019-07-10 | Jfeスチール株式会社 | 油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法 |
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EP3862455A4 (en) * | 2018-10-02 | 2022-06-15 | Nippon Steel Corporation | MARTENSITE STAINLESS STEEL SEAMLESS PIPE |
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JP7207557B2 (ja) | 2020-05-18 | 2023-01-18 | Jfeスチール株式会社 | 油井管用ステンレス継目無鋼管およびその製造方法 |
WO2021235087A1 (ja) * | 2020-05-18 | 2021-11-25 | Jfeスチール株式会社 | 油井管用ステンレス継目無鋼管およびその製造方法 |
JPWO2021235087A1 (ja) * | 2020-05-18 | 2021-11-25 | ||
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Also Published As
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US20190177823A1 (en) | 2019-06-13 |
AU2017266359B2 (en) | 2019-10-03 |
CN109154054A (zh) | 2019-01-04 |
EP3460087B1 (en) | 2020-12-23 |
US10995394B2 (en) | 2021-05-04 |
BR112018072904A2 (pt) | 2019-02-19 |
CN109154054B (zh) | 2020-06-05 |
JPWO2017200083A1 (ja) | 2018-06-07 |
RU2710808C1 (ru) | 2020-01-14 |
MX2018014132A (es) | 2019-04-29 |
JP6264521B1 (ja) | 2018-01-24 |
AU2017266359A1 (en) | 2018-12-20 |
BR112018072904B1 (pt) | 2022-09-06 |
EP3460087A4 (en) | 2019-11-06 |
EP3460087A1 (en) | 2019-03-27 |
CA3024694A1 (en) | 2017-11-23 |
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