WO2007007678A1 - 耐硫化物応力割れ性に優れた低合金油井管用鋼 - Google Patents
耐硫化物応力割れ性に優れた低合金油井管用鋼 Download PDFInfo
- Publication number
- WO2007007678A1 WO2007007678A1 PCT/JP2006/313590 JP2006313590W WO2007007678A1 WO 2007007678 A1 WO2007007678 A1 WO 2007007678A1 JP 2006313590 W JP2006313590 W JP 2006313590W WO 2007007678 A1 WO2007007678 A1 WO 2007007678A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- steel
- content
- less
- oil well
- low alloy
- Prior art date
Links
Classifications
-
- 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
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
Definitions
- the present invention relates to a low alloy oil well pipe steel, and more particularly to a low alloy oil well pipe steel used as an oil well pipe for an oil well or a gas well.
- Oil well pipes are used for extraction and production of crude oil and natural gas. Both ends of the oil well pipe are threaded, and new oil well pipes will be added as the oil and gas wells deepen. At this time, since the oil well pipe is subjected to stress due to its own weight, the oil well pipe needs to have high strength. Recently, l lOksi class (yield strength: 758-861MPa) oil well pipes and 125ksi class (yield strength: 861 ⁇ 965MPa) oil well pipes have been used due to deep wells in oil and gas wells. Has been developed.
- SSC Sulfide stress cracking
- crystal grains of steel are refined by quenching twice or by induction heating heat treatment.
- An object of the present invention is to provide a steel for a low alloy oil country tubular good having excellent SSC resistance.
- the present inventors examined measures for improving SSC resistance different from conventional improvements in internal quality, and thought that SSC resistance could be further improved if hydrogen penetration into the steel was suppressed. . Therefore, in order to suppress hydrogen intrusion, we investigated alloy elements that affect hydrogen intrusion.
- test pieces having various yield strengths were produced from steels having respective chemical numbers having chemical compositions shown in Table 1.
- a DCB (Double Cantilever Beam) test was performed on each test piece based on the test conditions described later, and the stress intensity factor K of each steel was determined.
- Figures 1 and 2 show the DCB test.
- Mn and Cr are usually contained in high-strength steel in order to improve hardenability.
- Mn decreases SSC resistance.
- Cr also decreases the SSC resistance.
- Mn and Cr decrease the SSC resistance because Mn and Cr are actively dissolved in a hydrogen sulfide environment. This is considered to promote corrosion and promote the penetration of hydrogen into the steel.
- the Mn and Cr contents are limited to the extent necessary for ensuring hardenability. Specifically, in principle, only Mn is contained, and Cr is contained as necessary.
- Mo suppresses the penetration of hydrogen. Specifically, Mo promotes the formation of a dense iron sulfide layer on the steel surface, and the formation of this iron sulfide layer suppresses corrosion and suppresses the entry of hydrogen. In addition, the iron pig iron layer increases the hydrogen overvoltage of the steel, and the increase of the hydrogen overvoltage also suppresses the entry of hydrogen. Therefore, in order to improve the SSC resistance, the Mo content is increased.
- V combines with Mo and C
- the present inventors further conducted the above-described DC B test using a plurality of steels having different Mo and V contents, and investigated the SSC resistance. As a result, if the following equation (1) is satisfied, Mo C
- the element symbol in the formula is the content (% by mass) of each element.
- the present inventors have used the above-mentioned DCs by using a plurality of steels having different Mn, Cr and Mo contents.
- a B test was conducted to investigate SSC resistance. As a result, it was found that if the Mo content satisfies the following formula (2), the decrease in SSC resistance due to Cr and Mn content can be suppressed.
- the element symbol in the formula is the content (% by mass) of each element.
- the steel for a low alloy oil country tubular good according to the present invention is, in mass%, C: 0.20-0.35%, Si: 0.05 to 0.5%, Mn: 0.05 to 0.6%, P: 0.025% or less, S: 0.01% or less, A1: 0.005 ⁇ 0.100%, Mo: 0.8 ⁇ 3.0%, V: 0.05 ⁇ 0.25%, B: 0.0001 ⁇ 0.005%, N: 0.01% or less, 0: 0.01% or less, the balance is Fe
- the impurity power also satisfies the formula (1).
- the element symbol in a formula shows content (mass%) of each element.
- the low alloy oil well tubular steel further contains Cr: 0.6% or less and satisfies the formula (2).
- the element symbol in a formula shows content (mass%) of each element.
- the steel for low alloy oil country tubular goods is further Nb: 0.1% or less, Ti: 0.1% or less, Zr: 0
- the steel for low alloy oil country tubular goods further contains Ca: 0.01% or less.
- the low alloy well pipe steel has a yield strength of 86 IMPa or more.
- MPa is equivalent to 125 ksi.
- FIG. 1 is a diagram showing the influence of Cr on the stress intensity factor obtained by a DCB test.
- FIG. 2 is a diagram showing the influence of Mo on the stress intensity factor obtained by the DCB test.
- the steel for low alloy oil country tubular goods according to the embodiment of the present invention has the following chemical composition.
- % related to elements means “% by mass”.
- C increases hardenability and improves the strength of the steel. However, if C is contained excessively, carbides are generated excessively and the SSC resistance is lowered. Therefore, the C content is 0.20-0.35%. The preferred C content is 0.25-0.30%.
- Si is effective for deoxidizing steel. Si also increases the temper soft resistance. However, if Si is contained excessively, the precipitation of the soft phase, which is the soft phase, is promoted, and the SSC resistance decreases. Therefore, the Si content should be 0.05-0.5%. Favorable! / ⁇ Si content is 0.05-5.35%.
- Mn is an important element in the present invention. Mn improves hardenability and contributes to improved strength. However, Mn actively dissolves in hydrogen sulfide and promotes hydrogen penetration by promoting corrosion. Therefore, in the present invention, the Mn content is preferably set to the minimum amount necessary for ensuring the strength. Therefore, the Mn content shall be 0.05-0.6%. The preferred Mn content is 0.3-0.5%.
- P is an impurity. P convinceds to the grain boundaries and decreases the SSC resistance. Therefore, it is preferable that the P content is low.
- the P content is not more than 0.025%.
- S is an impurity. S, like P, prays to the grain boundaries and reduces SSC resistance. Therefore, it is preferable that the S content is small. S content shall be 0.01% or less.
- A1 is effective for deoxidizing steel. However, even if A1 is contained excessively, the effect is saturated. Therefore, the A1 content is set to 0.005-0.100%. A preferable A1 content is 0.01 to 0.05%.
- the A1 content referred to in the present invention is acid-soluble Al (sol. A1). [0045] Mo: 0.8-3.0%
- Mo is an important element in the present invention. Mo enhances hardenability. Mo further promotes the formation of a dense iron sulfide layer on the steel surface. The formation of an iron sulfide layer suppresses corrosion and increases hydrogen overvoltage, so that hydrogen intrusion can be suppressed. However, even if Mo is contained excessively, the effect is saturated. Also, from the viewpoint of production cost, it is not preferable to contain excessive Mo. Therefore, the Mo content is set to 0.8 to 3.0%. A preferable Mo content is 1.0 to 2.5%.
- V 0.05-0.25%
- V is an important element in the present invention. V improves hardenability. V further combines with C together with Mo to produce fine carbide MC (M is V and Mo). The formation of fine carbide MC suppresses the formation of acicular Mo C, which is the starting point of SSC generation. V is tempered
- V contributes to the improvement of SSC resistance.
- coarse VC precipitates.
- Coarse VCs occlude hydrogen and reduce SSC resistance.
- Fine VC contributes to precipitation hardening, but coarse VC does not contribute to precipitation hardening. Therefore, the V content should be 0.05-0. 25%.
- a preferable V content is 0.05 to 0.20%.
- B improves hardenability. However, in high-strength steels such as the present invention, B promotes the formation of coarse carbides M C (M is Fe, Cr or Mo), which is the starting point of SSC generation.
- M C is Fe, Cr or Mo
- the B content is 0.0001-0.005%.
- the preferred B content is 0.0005 to 0.002%.
- N 0.01% or less
- N is an impurity. N forms coarse nitrides, and toughness reduces SSC resistance. Therefore, it is preferable that the N content is low. In the present invention, the N content is 0.01% or less.
- o is an impurity. O forms coarse oxides, and toughness decreases SSC resistance. So Therefore, it is preferable that the O content is small. In the present invention, the O content is 0.01% or less.
- the balance may be composed of Fe and may contain impurities other than P, S, N, and O due to various factors in the manufacturing process.
- the low alloy oil country tubular good of the present invention further satisfies the following formula (1).
- the element symbol in a formula shows content (mass%) of each element.
- Mo in the steel combines with C to form Mo C. Especially with Mo
- Mo C has a needle shape
- V combines with Mo and C to produce fine (V, Mo) C, and Mo forms Mo C.
- the steel for a low alloy oil country tubular good of the present invention further contains Cr as necessary. In other words, is an optional element.
- Cr improves hardenability. However, Cr, like Mn, promotes hydrogen penetration. For this reason, if Cr is excessively contained, the SSC resistance decreases. Therefore, Cr content is 0
- a preferable upper limit of the Cr content is 0.3%, and a preferable lower limit of the Cr content is 0.1%.
- the element symbol in a formula shows content (mass%) of each element.
- the steel for a low alloy oil country tubular good of the present invention further contains at least one of Nb, Ti, and Zr as required. That is, these elements are arbitrary elements. These elements contribute to the improvement of mechanical properties such as toughness.
- Nb 0.1% or less
- Nb, Ti and Zr combine with C and N to form carbonitrides.
- This pinning effect based on carbonitrides refines crystal grains and improves mechanical properties such as toughness.
- the effect is saturated. Therefore, the Nb content is 0.1% or less, the Ti content is 0.1% or less, and the Zr content is 0.1% or less.
- the Nb content is 0.002 to 0.1%, the Ti content is 0.002 to 0.1%, and the Zr content is 0.002 to 0.1%. .
- Nb content is 0.01 to 0.05 percent
- women Mashi ⁇ Ti 3 ⁇ 43 ⁇ 4i3 ⁇ 4 is 0.01 to 0.05 0/0
- women Mashi ⁇ Zr ⁇ 3 ⁇ 43 ⁇ 4i3 ⁇ 4 0. 01 ⁇ 0 05%.
- the steel for a low alloy oil country tubular good of the present invention further contains Ca as required. So Ca is an optional element.
- Ca is a coarse AlO.
- the Ca content should be 0.01% or less.
- a preferable Ca content is 0.0003-0.01%, and a more preferable Ca content is 0.0005 to 0.003%.
- the low alloy oil well tubular steel of the present invention has a yield strength of 110 ksi (758 MPa) or more, and preferably a yield strength of 125 ksi (861 MPa) or more.
- the strength of the low alloy oil well pipe steel of the present invention is at least lOksi class, preferably 125 ksi class (yield strength is 125 ksi to 140 ksi, ie 861 to 965 MPa).
- the steel for low alloy oil country tubular goods of the present invention has excellent SSC resistance by using the above-described chemical composition even with such high strength. [0065] 3. Manufacturing method
- the steel having the above chemical composition is melted and refined by a well-known method. Subsequently, the molten steel is made into a continuous forging material by a continuous forging method.
- slabs and blooms are billets
- the molten steel is made into an ingot by the ingot-making method.
- Slabs, blooms, and ingots are hot-worked into billets.
- the billet may be formed by hot rolling, or may be formed by hot forging.
- a billet obtained by continuous forging or hot working is hot worked into a steel for low alloy oil country tubular goods.
- the Mannesmann method is implemented as hot working to form an oil well pipe.
- Low alloy oil country tubular goods may be produced by other hot working methods. Cool the low-alloy oil well pipe steel after hot working to room temperature.
- quenching and tempering are performed. If the quenching temperature is set to 900-950 ° C and the tempering temperature is appropriately adjusted according to the chemical composition of the steel, the yield strength of the low alloy oil well tubular steel can be adjusted to the range described in 2.
- Expression (3) is the left side of Expression (1)
- Expression (4) is the left side of Expression (2).
- any of the chemical compositions of the steels with test numbers 13 to 23 was outside the scope of the present invention.
- the steels with test numbers 24 and 25 had chemical compositions within the range of the present invention, but the F 1 value was negative, and thus the formula (1) was not satisfied.
- the steels of test numbers 26 and 27 containing Cr had a chemical composition within the scope of the present invention and satisfied the formula (1), but had a negative F2 value and satisfied the formula (2). I helped.
- Each manufactured ingot was heated to 1250 ° C, and then a block having a thickness of 60 mm was formed by hot forging. Subsequently, after each block was heated to 1250 ° C, it was hot rolled into a steel plate having a thickness of 12 mm. A plurality of steel plates were produced for each test number shown in Table 2.
- each manufactured steel sheet was adjusted to 110 ksi to 140 ksi (758 to 965 ksi). Specifically, each steel plate was held at 920 ° C for 15 minutes, and then water quenching was performed. After quenching, tempering was performed at various temperatures within the temperature range of 670-720 ° C. In tempering, each steel plate was kept at the tempering temperature for 30 minutes and then air-cooled. Thereby, in each test number, a plurality of steel plates having different yield strengths (steel plate 1 and steel plate 2, or steel plates 1 to 3 in the “Experimental Values” column in Table 2) were prepared.
- a DCB test was conducted using each steel plate to evaluate the SSC resistance.
- a DCB specimen having a thickness of 10 mm, a width of 25 mm, and a length of 100 mm was taken from each steel plate.
- a DCB test was conducted in accordance with NACE (National Association of Corrosion Engineers) TMO T-9oMethodD.
- NACE National Association of Corrosion Engineers
- TMO T-9oMethodD normal temperature 5% salt + 0.5% acetic acid aqueous solution saturated with latm hydrogen sulfide gas was used.
- the DCB test was carried out by immersing the DCB specimen in the test bath for 336 hours. After the test, the crack growth length a generated on the DCB specimen was measured. Based on the measured crack growth length a and wedge opening stress P, the stress expansion is based on the following equation (5). The large coefficient K (ksi in) was obtained.
- h is the height of each arm of the DCB specimen
- B is the thickness of the DCB specimen
- B is the web of the DCB specimen. It is the thickness (web thi ckness).
- Estimated stress intensity factor K (hereinafter referred to as approximate value K) when the strength is 140 ksi
- Approximate value ⁇ is calculated based on the same yield strength in each test number steel.
- the standard yield strength is 140 ksi.
- the reason is to compare the stress intensity factor ⁇ at high strength.
- the approximate value ⁇ is
- the ISSC 140 calculation method will be described.
- the stress intensity factor K depends on the strength. For example, as shown in Figure 1 and Figure 2.
- Equation (6) The approximate equation shown in Equation (6) was derived.
- YS in the equation is the yield strength (ksi) of the steel sheet, and K is the stress obtained in equation (5).
- the magnification factor is K.
- the steels with test numbers 1 to 6 and 10 to 12 have the chemical composition within the range of the present invention and satisfy the formula (1), so the estimated value K force is 3 ⁇ 42 ksi in or more. Good resistance
- the steels of test numbers 7 to 9 containing Cr had a chemical composition within the scope of the present invention and satisfied the formulas (1) and (2), so the estimated value K was 22 ksi in That's it.
- the steels with test numbers 13 to 23 had poor SSC resistance because any of their chemical compositions was outside the scope of the present invention.
- the steel with test number 15 had poor SSC resistance because the Mn content exceeded the upper limit of the present invention.
- the steels of test numbers 18 and 19 had poor SSC resistance because the Mo content was less than the lower limit of the present invention.
- the steel with test number 20 had poor SSC resistance because the V content was below the lower limit of the present invention.
- the steel of test number 21 had poor SSC resistance because the V content exceeded the upper limit of the present invention.
- Test No. 23 had poor SSC resistance because the Cr content exceeded the upper limit of the present invention.
- the steel for a low alloy oil country tubular good according to the present invention can be used as an oil well pipe, and in particular, used as a casing for an oil well or a gas well.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Silicon Compounds (AREA)
- Metal Extraction Processes (AREA)
- Luminescent Compositions (AREA)
Abstract
Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
BRPI0613173-5A BRPI0613173A2 (pt) | 2005-07-08 | 2006-07-07 | aço de baixa liga para produtos tubulares para campos petrolìferos tendo alta resistência à fratura por estresse por sulfetos |
EP06768000.9A EP1911857B1 (en) | 2005-07-08 | 2006-07-07 | Low-alloy steel for oil well tube having excellent sulfide stress cracking resistance |
NO20080003A NO343352B1 (no) | 2005-07-08 | 2008-01-02 | Lavlegert stål for oljefeltsrør med utmerket motstand mot sulfidspenningssprekking og anvendelse av V i det lavlegerte stålet |
US12/007,165 US7670547B2 (en) | 2005-07-08 | 2008-01-07 | Low alloy steel for oil country tubular goods having high sulfide stress cracking resistance |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2005200682A JP4725216B2 (ja) | 2005-07-08 | 2005-07-08 | 耐硫化物応力割れ性に優れた低合金油井管用鋼 |
JP2005-200682 | 2005-07-08 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US12/007,165 Continuation US7670547B2 (en) | 2005-07-08 | 2008-01-07 | Low alloy steel for oil country tubular goods having high sulfide stress cracking resistance |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2007007678A1 true WO2007007678A1 (ja) | 2007-01-18 |
Family
ID=37637071
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2006/313590 WO2007007678A1 (ja) | 2005-07-08 | 2006-07-07 | 耐硫化物応力割れ性に優れた低合金油井管用鋼 |
Country Status (8)
Country | Link |
---|---|
US (1) | US7670547B2 (ja) |
EP (1) | EP1911857B1 (ja) |
JP (1) | JP4725216B2 (ja) |
CN (1) | CN101218364A (ja) |
BR (1) | BRPI0613173A2 (ja) |
NO (1) | NO343352B1 (ja) |
RU (1) | RU2378408C2 (ja) |
WO (1) | WO2007007678A1 (ja) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102268602A (zh) * | 2011-07-14 | 2011-12-07 | 无锡西姆莱斯石油专用管制造有限公司 | 3Cr油井管及其生产方法 |
JP2013129879A (ja) * | 2011-12-22 | 2013-07-04 | Jfe Steel Corp | 耐硫化物応力割れ性に優れた油井用高強度継目無鋼管およびその製造方法 |
WO2013191131A1 (ja) | 2012-06-20 | 2013-12-27 | 新日鐵住金株式会社 | 油井管用鋼及びその製造方法 |
WO2015190377A1 (ja) * | 2014-06-09 | 2015-12-17 | 新日鐵住金株式会社 | 低合金油井用鋼管 |
Families Citing this family (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4140556B2 (ja) * | 2004-06-14 | 2008-08-27 | 住友金属工業株式会社 | 耐硫化物応力割れ性に優れた低合金油井管用鋼 |
JP4251229B1 (ja) * | 2007-09-19 | 2009-04-08 | 住友金属工業株式会社 | 高圧水素ガス環境用低合金鋼および高圧水素用容器 |
JP5257233B2 (ja) * | 2008-05-19 | 2013-08-07 | 新日鐵住金株式会社 | 低降伏比高強度電縫鋼管及びその製造方法 |
FR2942808B1 (fr) * | 2009-03-03 | 2011-02-18 | Vallourec Mannesmann Oil & Gas | Acier faiblement allie a limite d'elasticite elevee et haute resistance a la fissuration sous contrainte par les sulfures. |
JP5728836B2 (ja) | 2009-06-24 | 2015-06-03 | Jfeスチール株式会社 | 耐硫化物応力割れ性に優れた油井用高強度継目無鋼管の製造方法 |
JP5971435B1 (ja) | 2014-09-08 | 2016-08-17 | Jfeスチール株式会社 | 油井用高強度継目無鋼管およびその製造方法 |
MX2017002976A (es) | 2014-09-08 | 2017-06-19 | Jfe Steel Corp | Tuberia de acero sin costura de alta resistencia para productos tubulares de region petrolifera y metodo de produccion de la misma. |
JP5930140B1 (ja) * | 2014-11-18 | 2016-06-08 | Jfeスチール株式会社 | 油井用高強度継目無鋼管およびその製造方法 |
MX2017008360A (es) * | 2014-12-24 | 2017-10-24 | Jfe Steel Corp | Tubo de acero sin costura de alta resistencia para productos tubulares para paises productores de petroleo y metodo para producir el mismo. |
JP5943164B1 (ja) * | 2014-12-24 | 2016-06-29 | Jfeスチール株式会社 | 油井用高強度継目無鋼管およびその製造方法 |
MX2018007692A (es) | 2015-12-22 | 2018-08-01 | Jfe Steel Corp | Tubo de acero sin costura de alta resistencia para productos tubulares para la industria petrolera, y metodo de produccion para tubo de acero sin costura de alta resistencia para productos tubulares para la industria petrolera. |
NZ744590A (en) | 2016-02-29 | 2019-04-26 | Jfe Steel Corp | Low alloy high strength seamless steel pipe for oil country tubular goods |
WO2018074109A1 (ja) | 2016-10-17 | 2018-04-26 | Jfeスチール株式会社 | 油井用高強度継目無鋼管およびその製造方法 |
CN106435373A (zh) * | 2016-12-21 | 2017-02-22 | 重庆中鼎三正科技有限公司 | 一种低合金高强度抗硫化氢钢及其制备方法 |
AR114708A1 (es) * | 2018-03-26 | 2020-10-07 | Nippon Steel & Sumitomo Metal Corp | Material de acero adecuado para uso en entorno agrio |
AR114712A1 (es) * | 2018-03-27 | 2020-10-07 | Nippon Steel & Sumitomo Metal Corp | Material de acero adecuado para uso en entorno agrio |
DE102019217369A1 (de) * | 2019-11-11 | 2021-05-12 | Robert Bosch Gmbh | Umwandlungsträge Stahllegierung, Verfahren zur Herstellung der umwandlungsträgen Stahllegierung und Wasserstoffspeicher mit einer Komponente aus der umwandlungsträgen Stahllegierung |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61272351A (ja) * | 1985-05-29 | 1986-12-02 | Kawasaki Steel Corp | 高強度高靭性油井用鋼管 |
JPS6240345A (ja) * | 1985-08-13 | 1987-02-21 | Nippon Kokan Kk <Nkk> | 耐遅れ破壊特性の優れた高張力油井用鋼管 |
JPH11335731A (ja) * | 1998-05-21 | 1999-12-07 | Sumitomo Metal Ind Ltd | 耐硫化物応力割れ性に優れた高強度鋼材の製造方法 |
WO2000068450A1 (fr) * | 1999-05-06 | 2000-11-16 | Sumitomo Metal Industries, Ltd. | Produit en acier pour puits de petrole, dote d'une grande solidite et d'une excellente resistance a la corrosion fissurante provoquee par l'hydrogene sulfure |
JP2001271134A (ja) * | 2000-03-24 | 2001-10-02 | Sumitomo Metal Ind Ltd | 耐硫化物応力割れ性と靱性に優れた低合金鋼材 |
JP2004332059A (ja) * | 2003-05-08 | 2004-11-25 | Sumitomo Metal Ind Ltd | 低合金鋼 |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SU730868A1 (ru) | 1977-12-01 | 1980-04-30 | Физико-Механический Институт Ан Украинской Сср | Сталь |
JPH06116635A (ja) * | 1992-10-02 | 1994-04-26 | Kawasaki Steel Corp | 耐硫化物応力腐食割れ性に優れた高強度低合金油井用鋼の製造方法 |
JP3755163B2 (ja) | 1995-05-15 | 2006-03-15 | 住友金属工業株式会社 | 耐硫化物応力割れ性に優れた高強度継目無鋼管の製造方法 |
WO1996036742A1 (fr) * | 1995-05-15 | 1996-11-21 | Sumitomo Metal Industries, Ltd. | Procede de production de tubes d'acier sans soudure a haute resistance, non susceptibles de fissuration par les composes soufres |
JP3680628B2 (ja) | 1999-04-28 | 2005-08-10 | 住友金属工業株式会社 | 耐硫化物割れ性に優れた高強度油井用鋼管の製造方法 |
RU2243284C2 (ru) | 2002-12-02 | 2004-12-27 | Открытое акционерное общество "Волжский трубный завод" | Сталь повышенной коррозионной стойкости и бесшовные трубы, выполненные из нее |
RU2255123C1 (ru) | 2003-12-04 | 2005-06-27 | Открытое акционерное общество "Северсталь" | Способ производства штрипсов из низколегированной стали |
JP4140556B2 (ja) * | 2004-06-14 | 2008-08-27 | 住友金属工業株式会社 | 耐硫化物応力割れ性に優れた低合金油井管用鋼 |
JP4609138B2 (ja) * | 2005-03-24 | 2011-01-12 | 住友金属工業株式会社 | 耐硫化物応力割れ性に優れた油井管用鋼および油井用継目無鋼管の製造方法 |
-
2005
- 2005-07-08 JP JP2005200682A patent/JP4725216B2/ja active Active
-
2006
- 2006-07-07 EP EP06768000.9A patent/EP1911857B1/en active Active
- 2006-07-07 BR BRPI0613173-5A patent/BRPI0613173A2/pt active IP Right Grant
- 2006-07-07 RU RU2008104702/02A patent/RU2378408C2/ru active
- 2006-07-07 CN CNA2006800250212A patent/CN101218364A/zh active Pending
- 2006-07-07 WO PCT/JP2006/313590 patent/WO2007007678A1/ja active Application Filing
-
2008
- 2008-01-02 NO NO20080003A patent/NO343352B1/no not_active IP Right Cessation
- 2008-01-07 US US12/007,165 patent/US7670547B2/en active Active
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61272351A (ja) * | 1985-05-29 | 1986-12-02 | Kawasaki Steel Corp | 高強度高靭性油井用鋼管 |
JPS6240345A (ja) * | 1985-08-13 | 1987-02-21 | Nippon Kokan Kk <Nkk> | 耐遅れ破壊特性の優れた高張力油井用鋼管 |
JPH11335731A (ja) * | 1998-05-21 | 1999-12-07 | Sumitomo Metal Ind Ltd | 耐硫化物応力割れ性に優れた高強度鋼材の製造方法 |
WO2000068450A1 (fr) * | 1999-05-06 | 2000-11-16 | Sumitomo Metal Industries, Ltd. | Produit en acier pour puits de petrole, dote d'une grande solidite et d'une excellente resistance a la corrosion fissurante provoquee par l'hydrogene sulfure |
JP2001271134A (ja) * | 2000-03-24 | 2001-10-02 | Sumitomo Metal Ind Ltd | 耐硫化物応力割れ性と靱性に優れた低合金鋼材 |
JP2004332059A (ja) * | 2003-05-08 | 2004-11-25 | Sumitomo Metal Ind Ltd | 低合金鋼 |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102268602A (zh) * | 2011-07-14 | 2011-12-07 | 无锡西姆莱斯石油专用管制造有限公司 | 3Cr油井管及其生产方法 |
CN102268602B (zh) * | 2011-07-14 | 2013-04-03 | 无锡西姆莱斯石油专用管制造有限公司 | 3Cr油井管及其生产方法 |
JP2013129879A (ja) * | 2011-12-22 | 2013-07-04 | Jfe Steel Corp | 耐硫化物応力割れ性に優れた油井用高強度継目無鋼管およびその製造方法 |
WO2013191131A1 (ja) | 2012-06-20 | 2013-12-27 | 新日鐵住金株式会社 | 油井管用鋼及びその製造方法 |
US10407758B2 (en) | 2012-06-20 | 2019-09-10 | Nippon Steel Corporation | Steel for oil country tubular goods and method of producing the same |
WO2015190377A1 (ja) * | 2014-06-09 | 2015-12-17 | 新日鐵住金株式会社 | 低合金油井用鋼管 |
JPWO2015190377A1 (ja) * | 2014-06-09 | 2017-04-20 | 新日鐵住金株式会社 | 低合金油井用鋼管 |
AU2015272617B2 (en) * | 2014-06-09 | 2017-06-29 | Nippon Steel Corporation | Low alloy steel pipe for oil well |
RU2643735C1 (ru) * | 2014-06-09 | 2018-02-05 | Ниппон Стил Энд Сумитомо Метал Корпорейшн | Низколегированная стальная труба для нефтяной скважины |
US10233520B2 (en) | 2014-06-09 | 2019-03-19 | Nippon Steel & Sumitomo Metal Corporation | Low-alloy steel pipe for an oil well |
Also Published As
Publication number | Publication date |
---|---|
NO20080003L (no) | 2008-04-02 |
JP2007016291A (ja) | 2007-01-25 |
RU2008104702A (ru) | 2009-08-20 |
US20080105337A1 (en) | 2008-05-08 |
US7670547B2 (en) | 2010-03-02 |
JP4725216B2 (ja) | 2011-07-13 |
NO343352B1 (no) | 2019-02-04 |
CN101218364A (zh) | 2008-07-09 |
EP1911857A4 (en) | 2010-03-24 |
EP1911857B1 (en) | 2017-10-04 |
RU2378408C2 (ru) | 2010-01-10 |
EP1911857A1 (en) | 2008-04-16 |
BRPI0613173A2 (pt) | 2010-12-21 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4725216B2 (ja) | 耐硫化物応力割れ性に優れた低合金油井管用鋼 | |
JP5971435B1 (ja) | 油井用高強度継目無鋼管およびその製造方法 | |
JP4609138B2 (ja) | 耐硫化物応力割れ性に優れた油井管用鋼および油井用継目無鋼管の製造方法 | |
KR102267129B1 (ko) | Nb함유 페라이트계 스테인리스 열연 강판 및 그 제조 방법과, Nb함유 페라이트계 스테인리스 냉연 강판 및 그 제조 방법 | |
JP6107437B2 (ja) | 耐硫化物応力腐食割れ性に優れた油井用低合金高強度継目無鋼管の製造方法 | |
AU2014294080B2 (en) | High-strength steel material for oil well and oil well pipes | |
JP6369547B2 (ja) | 低合金油井用鋼管 | |
JP6369662B1 (ja) | 二相ステンレス鋼およびその製造方法 | |
JP6017341B2 (ja) | 曲げ性に優れた高強度冷延鋼板 | |
WO2014068794A1 (ja) | 耐硫化物応力割れ性に優れた低合金油井管用鋼及び低合金油井管用鋼の製造方法 | |
JP2001271134A (ja) | 耐硫化物応力割れ性と靱性に優れた低合金鋼材 | |
JP5316634B2 (ja) | 加工性に優れた高強度鋼板およびその製造方法 | |
WO2016052397A1 (ja) | 高強度油井用鋼材および油井管 | |
JP5971436B1 (ja) | 油井用高強度継目無鋼管およびその製造方法 | |
CN108699656B (zh) | 钢材和油井用钢管 | |
JP7036238B2 (ja) | サワー環境での使用に適した鋼材 | |
JP6468302B2 (ja) | 高強度油井用鋼管用素材および該素材を用いた高強度油井用鋼管の製造方法 | |
JP2021509434A (ja) | 高強度高靭性熱延鋼板及びその製造方法 | |
JP4321434B2 (ja) | 低合金鋼及びその製造方法 | |
JP2008057007A (ja) | 低合金鋼材およびその製造方法 | |
JP7036237B2 (ja) | サワー環境での使用に適した鋼材 | |
JP4396852B2 (ja) | 火災後の強度健全性に優れた建築構造用高張力鋼 | |
JP3969279B2 (ja) | マルテンサイト系鉄基耐熱合金およびその製造方法 | |
JP6519025B2 (ja) | 油井用低合金高強度継目無鋼管 | |
JP2001355037A (ja) | 破壊靱性に優れた高強度鋼材 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 200680025021.2 Country of ref document: CN |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application | ||
WWE | Wipo information: entry into national phase |
Ref document number: MX/a/2007/016249 Country of ref document: MX |
|
WWE | Wipo information: entry into national phase |
Ref document number: 12007165 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
REEP | Request for entry into the european phase |
Ref document number: 2006768000 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2006768000 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2008104702 Country of ref document: RU |
|
ENP | Entry into the national phase |
Ref document number: PI0613173 Country of ref document: BR Kind code of ref document: A2 Effective date: 20080108 |