US20080226396A1 - Seamless steel tube for use as a steel catenary riser in the touch down zone - Google Patents

Seamless steel tube for use as a steel catenary riser in the touch down zone Download PDF

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US20080226396A1
US20080226396A1 US12/073,879 US7387908A US2008226396A1 US 20080226396 A1 US20080226396 A1 US 20080226396A1 US 7387908 A US7387908 A US 7387908A US 2008226396 A1 US2008226396 A1 US 2008226396A1
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upset
max
seamless steel
pipe body
steel pipe
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Alfonso Izquierdo Garcia
Hector Manuel Quintanilla Carmona
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Tubos de Acero de Mexico SA
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Tubos de Acero de Mexico SA
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Priority to US12/073,879 priority Critical patent/US20080226396A1/en
Priority to CA2680943A priority patent/CA2680943C/en
Priority to EP08741588A priority patent/EP2157197A2/en
Priority to MX2009009905A priority patent/MX340352B/es
Priority to PCT/MX2008/000041 priority patent/WO2008111828A2/es
Priority to BRPI0808963-9A priority patent/BRPI0808963A2/pt
Assigned to TUBOS DE ACERO DE MEXICO S.A. reassignment TUBOS DE ACERO DE MEXICO S.A. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: CARMONA, HECTOR MANUEL QUINTANILLA, GARCIA, ALFONSO IZQUIERDO
Publication of US20080226396A1 publication Critical patent/US20080226396A1/en
Priority to NO20093020A priority patent/NO20093020L/no
Abandoned legal-status Critical Current

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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
    • 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
    • E—FIXED CONSTRUCTIONS
    • E21—EARTH DRILLING; MINING
    • E21B—EARTH DRILLING, e.g. DEEP DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
    • E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings
    • E21B17/01—Risers
    • E21B17/015—Non-vertical risers, e.g. articulated or catenary-type

Definitions

  • This invention relates to seamless steel tubes for use as steel catenary riser.
  • SCR Steel Catenary Risers
  • Steel Catenary Riser is a proven and economic riser system solution, as a tie-back production riser and as an export riser from Floating Production Systems (FPS) in the development of oil and gas fields in deepwater and ultra-deepwater.
  • FPS Floating Production Systems
  • the application of SCRs is challenged by, in some cases, the high fatigue damage at the Touch Down Zone (TDZ) from a combination of field specific parameters such as riser size, fluid characteristics, vessel motions, metocean parameters, soil conditions, and water depth.
  • TDZ Touch Down Zone
  • the most severe design requirement for SCRs is the fatigue life of the girth welds at the Touch-Down Zone (TDZ) region where the riser touches the seafloor and it connects with the rest of the pipeline, as is illustrated in FIG. 1 .
  • the riser experiences the highest level of cumulative fatigue damage. This is due to the fact that in said zone the highest bending of the catenary line is experienced, contrary to the total absence of bending of the portion of the line lying on the seabed. Due to the various movements of FPS (waves, tides, currents, etc.), the line segment in the TDZ experiences cycles of bending between maximum riser bending and zero bending (straight).
  • the severity of fatigue loading in the TDZ is further complicated by the presence of continuous impacts of the portion of the line when entering in contact with the ground. Moreover, it has to be considered that the same impact of the line could dig a hole just in correspondence of the TDZ, amplifying the amplitude of bending cycle.
  • the upsetting process is commonly used in the industry for casing and riser joints with threaded ends. Steel grades with higher carbon content are normally used for these applications.
  • the upsetting process has not been used so far for weldable pipe of SCR quality. In most of threaded cases, though, the increase in fatigue life has been limited to a factor between 2 to 3. In the case of clad steel applications, a higher increase in fatigue life can be achieved.
  • alternative catenary riser design has been developed by changing the riser pipe material (composite, titanium) or by hybrid designs (titanium and steel), or by changing the shape near seabed through provision of significant buoyancy (WO97/06341).
  • upset pipes to be used in welded joints have been developed.
  • the simple concept for the improved fatigue performance consists, in this case, in locally decreasing the stress experienced by the welding with respect to the stress range generally experienced by the pipe body and, hence, the section of the riser in the TDZ.
  • An upset SCR of novel low carbon chemical composition and microstructure was thus devised to achieve higher improvement in the fatigue life as it is comprised with the riser pipe section.
  • Sour Service is the performance of the Riser in H 2 S environments.
  • Metallurgical properties known to affect performance in H 2 S containing environments include: chemical composition, steel cleanliness, method of manufacturing, strength, amount of cold work, heat treatment conditions and microstructure. Since the upset pipe manufacturing process involves additional steps subsequent to the manufacture of the seamless pipe, the end product has to accomplish these requirements.
  • the present invention describes an upset SCR of novel low carbon chemical composition and microstructure which achieves higher improvement in the fatigue life as it is integral with the riser pipe section at the Touch Down Zone.
  • the low carbon upset SCR achieves its desired properties by the thermal treatment which it is subjected to.
  • the novel low carbon chemical composition and microstructure comprises in weight per cent, carbon 0.04-0.10, manganese 0.40-0.70, silicon 0.15-0.35, chromium 0.40-0.70, molybdenum 0.40-0.70, nickel 0.10-0.40, nitrogen 0.008 max, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.020 max, titanium 0.003-0.020, niobium 0.020-0.035, vanadium no more than 0.10, copper 0.20 max, tin 0.020 max, and carbon equivalent 0.43 max and PCM no more than 0.23 and having a yield strength of at least of 65000 psi, the ultimate tensile strength of at least 77000 psi and YS/UTS ratio below 0.89 in material representing the pipe body, the transition zone and the upset end.
  • the present invention also describes a method for manufacturing a seamless steel tube for steel catenary riser with upset ends having a yield strength at least of 65000 psi both in the pipe body, transition and the upset-zone comprising the steps of: (a) providing a steel tube comprising in weight per cent, carbon 0.04-0.10, manganese 0.40-0.70, silicon 0.15-0.35, chromium 0.40-0.70, molybdenum 0.40-0.70, nickel 0.10-0.40, nitrogen 0.008 max, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.020 max, titanium 0.003-0.020, niobium 0.020-0.035, vanadium no more than 0.10, copper 0.20 max, tin 0.020 max, and carbon equivalent 0.43 max and PCM no more than 0.23; (b) upsetting the tube ends in multiple steps with intermediate heating cycles in between to achieve the required thickness (c) quenching and tempering between 630-710° C.; (d) machining the
  • FIG. 1 shows the Steel Catenary Riser Configuration of a preferred embodiment of the present invention.
  • FIG. 2 illustrates an embodiment of the tube with an upset end of a preferred embodiment of the present invention.
  • FIG. 3 shows typical macro sections of RP2Z welds for different welding conditions of the tube of a preferred embodiment of the present invention.
  • FIGS. 4( a ) and ( b ) show the tensile test results for the longitudinal direction and the transverse direction of a preferred embodiment of the present invention.
  • FIG. 5 illustrates the longitudinal and transverse Y/T ratio results of a preferred embodiment of the present invention.
  • FIG. 6 shows the Hardness Vickers HV10 of a preferred embodiment of the present invention.
  • FIG. 7 illustrates the Transverse Charpy V Notch Impact Test at ⁇ 30° C. of a preferred embodiment of the present invention.
  • FIG. 8 shows the Mean curve for specimens 103 ⁇ 4′′ ⁇ 0.866′′ ⁇ 65 of a preferred embodiment of the present invention.
  • FIGS. 9( a ) and ( b ) show the tensile test results for the longitudinal direction and the transverse direction of a preferred embodiment of the present invention
  • FIG. 10 illustrates the longitudinal and transverse Y/T ratio results of a preferred embodiment of the present invention.
  • FIG. 11 shows the Hardness Vickers HV10 of a preferred embodiment of the present invention.
  • FIG. 12 illustrates the Transverse Charpy V Notch Impact Test at ⁇ 30° C. of a preferred embodiment of the present invention.
  • FIG. 13 shows the Mean curve for specimens 103 ⁇ 4′′ ⁇ 1.250′′ ⁇ 65 of a preferred embodiment of the present invention.
  • the present invention describes an upset SCR of novel low carbon chemical composition and microstructure which achieves higher improvement in the fatigue life as it is integral with the riser pipe section at the Touch Down Zone.
  • the low carbon upset SCR achieves its desired properties by the thermal treatment which it is subjected to.
  • the steel grade contemplated for use in the upset SCR of the present invention is X-65 (a yield strength of at least 65000 psi in the pipe body and in the upset ends).
  • the alloy design consists of a low-C (0.13 max), low-Mn (1.5 max) steel with additions of microalloying elements such as Niobium, Titanium (Nb+Ti 0.1 max), Chromium and Molybdenum (Cr+Mo 1.2 max).
  • the purpose of adding these last two alloying elements is to increase hardenability and promote a martensitic-bainitic transformation on thick upset ends and pipe body achieving high strength.
  • the carbon equivalent (CE) is designed not to exceed 0.43 as requested by API 5L. More preferably, the carbon equivalent is limited to 0.41. The most preferred embodiment of the present invention is not to exceed 0.39.
  • Pipes are hot rolled using a recrystallization controlled rolling scheme manufactured from round billets obtained by continuously cast (CC) process. After hot rolling, the pipes are then inspected with non-destructive methods such as electromagnetic inspection, wet magnetic particle inspection and ultrasonic testing with the purpose of finding any longitudinal or transverse defects on internal or external surfaces and to verify wall thickness.
  • the pipes are then upsetted by reheating the pipe ends above the dissolution temperature of Nb (C, N) to provide adequate plastic flow during each upset operation whilst controlling austenite grain size by precipitation of fine TiN particles.
  • the optimum radius at the upset-pipe body transition is modeled thru Finite Element Analysis (FEA), where the Stress Concentration Factor (SCF) resulted 1.135 and 1.12 for Case 1 (273.1 mm OD by 22.0 mm WT Pipe body, 28 mm WT as machined Upset Ends and 35 mm as upset ends, steel grade X65 for non-sour service application, 10.75′′ ⁇ 0.866′′) and Case 2 (273.1 mm OD by 31.8 mm WT Pipe body, 45 mm WT as machined Upset Ends and 53 mm as upset ends, steel grade X65 for sour service application, 10.75′′ ⁇ 1.250′′), respectively.
  • SCF Stress Concentration Factor
  • a critical quench and temper heat treatment is designed and used to provide the final mechanical properties.
  • Non-destructive testing is again carried out in the pipe body, and the OD and ID surface of the upset ends are machined and then inspected with wet magnetic particle inspection and manual ultrasonic testing. Finally, the pipes are bevel machined for girth welding. Welding and fatigue behavior are thoroughly characterized.
  • the Yield Strength (YS), the Ultimate Tensile Strength (UTS) and the YS/UTS ratio at room temperature are evaluated using both longitudinal and transverse round specimens taken from the Upset End, Slope Transition and Pipe Body regions in two quadrants, 0° and 180°.
  • Hardness Vickers HV10 are measured on the OD (outside diameter), MW (mid-wall) and ID (internal diameter) sections in 4 quadrants are taken from the Upset End, Slope Transition and Pipe Body regions. The hardness readings are taken at 1.5 mm from OD and ID.
  • transverse Charpy V notch impact testing is carried out at ⁇ 30° C. and ⁇ 40° C. for case 1 and case 2 respectively using 10 ⁇ 10 mm specimens. Sour service resistance is assessed in both pipe body and upset ends by the Hydrogen Induced Cracking (HIC) and Four Point Bend Tests (FPBT).
  • HIC Hydrogen Induced Cracking
  • FPBT Four Point Bend Tests
  • the present invention thus describes a seamless steel tube for a steel catenary riser with upset ends comprising in weight per cent, carbon 0.04-0.10, manganese 0.40-0.70, silicon 0.15-0.35, chromium 0.40-0.70, molybdenum 0.40-0.70, nickel 0.10-0.40, nitrogen 0.008 max, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.020 max, titanium 0.003-0.020, niobium 0.020-0.035, vanadium no more than 0.10, copper 0.20 max, Tin 0.020 max, and carbon equivalent 0.43 max and PCM no more than 0.23 and having a yield strength of at least of 65000 psi in material representing the pipe body, the transition zone and the upset end.
  • the novel microstructure of the upset SCR which enables the seamless steel tube to achieve a higher improvement in the fatigue life includes the following mechanical properties and corrosion requirements for Upset SCR as shown in Table 1.
  • the minimum requirements are following the API 5L, 43 rd edition specification.
  • Table 2 shows a summary of observed microstructures. All microstructures are homogeneous at midwall, which is the most critical section where mainly bainite, and a mixture of acicular and non-polygonal ferrite is observed independent of the section (pipe body, transition or upset). There is a slight presence of martensite close to the OD and ID sections.
  • a specific alloy design is developed and heat treatment parameters are set to obtain the desired microstructural characteristics in both pipe body and heavy wall upset sections.
  • the combination of the above mentioned parameters results in excellent mechanical properties which meet the strength and corrosion objectives.
  • the present invention also describes a method for manufacturing a seamless steel tube for steel catenary riser with upset ends having a yield strength at least of 65000 psi both in the pipe body, transition and the upset-zone comprising the steps of: (a) providing a steel tube comprising in weight per cent, carbon 0.04-0.10, manganese 0.40-0.70, silicon 0.15-0.35, chromium 0.40-0.70, molybdenum 0.40-0.70, nickel 0.10-0.40, nitrogen 0.008 max, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.020 max, titanium 0.003-0.020, niobium 0.020-0.035, vanadium no more than 0.10, copper 0.20 max, Tin 0.020 max, and carbon equivalent 0.43 max and PCM no more than 0.23; (b) quenching and tempering between 630-710° C.
  • the properties of the upset pipes subject to different thermal cycles induced by welding operations are evaluated initially by welding on a 35 mm wall thickness pipe with the chemistry as the upset ends.
  • This specific welding preparation with one of the bevel at 0° enables to quantify the toughness (impact and CTOD testing) of the HAZ in conditions more severe than with the conventional V or U bevel (the fatigue crack is placed in the prescribed coarse-grain HAZ material for at least 15% of the central two thirds of the specimen thickness).
  • the weldability test requires characterization of the HAZ for two cases subject to different combinations of heat using an API RP2Z bevel: Preproduction Qualification for Steel Plates for Offshore Structures [8]. All tests passes or exceeds the requirements including hardness HV10 below 250 for the sour service case (Case 2).
  • the HAZ characterization has been run on both upset pipes with 28 mm and 45 mm thickness at the upset ends, with the welding conditions listed in table 4.
  • the consumables and heat input used are:
  • hardness indentations in HAZ are located in lines parallel to the pipe body, at 1.5 mm from inner and outer diameter of pipe and each 4 mm across the thickness.
  • the last bead is not on a side of a bevel but is deposited within the width of the weld preparation so that each cap passing at the edges of the bevel gets the benefit of a tempering effect of the subsequent cap passes.
  • the hardness in HAZ does not exceed 250 HV10.
  • Impact testing is run at ⁇ 40° C., from fusion line+1 mm to fusion line+3 mm, on welds run on 35 mm thick pipe and high heat input (2 and 3 kJ/mm). Absorbed energy obtained is above 200 J for each specimen.
  • CTOD testing (SENB, Bx2B specimens) in HAZ as per API RP2Z is run at ⁇ 10° C.
  • the achieved CTOD values are from 1.0 to 1.5 mm, which shows an excellent ductility of the HAZ.
  • Case 1 273.1 mm OD by 22.0 mm WT Pipe body, 28 mm WT as machined Upset Ends and 35 mm as upset ends, steel grade X65 for non-sour service application (10.75′′ ⁇ 0.866′′)
  • Case 2 273.1 mm OD by 31.8 mm WT Pipe body, 45 mm WT as machined Upset Ends and 53 mm as upset ends, steel grade X65 for sour service application (10.75′′ ⁇ 1.250′′).
  • FIGS. 4( a ) and ( b ) and 5 show the Yield Strength (YS), Ultimate Tensile Strength (UTS) and the YS/UTS ratio evaluated at room temperature for quenched and tempered material.
  • YS Yield Strength
  • UTS Ultimate Tensile Strength
  • FIGS. 4( a ) and ( b ) and 5 show the Yield Strength (YS), Ultimate Tensile Strength (UTS) and the YS/UTS ratio evaluated at room temperature for quenched and tempered material.
  • YS. 4( a ) and ( b ) and 5 show the Yield Strength (YS), Ultimate Tensile Strength (UTS) and the YS/UTS ratio evaluated at room temperature for quenched and tempered material.
  • Longitudinal and transverse round specimens taken from sections representing the Upset End, Slope Transition and Pipe Body are tested in two quadrants, 0° and 180°. All specimens are standard round except by those from the pipe body in the transverse direction
  • FIGS. 4( a ) and ( b ) show that all Yield Strength values obtained are above 65,000 psi minimum and do not exceed the 80,000 psi maximum. All the Ultimate Tensile strength values obtained are above 77,000 psi minimum established.
  • FIG. 5 shows that, for the YS/UTS ratio, all the values are below 0.89 which is established as maximum YS/UTS specification.
  • the values of YS/UTS ratio are shown in FIG. 5 for both the longitudinal and transverse directions.
  • Hardness Vickers HV10 (3 readings per row) are measured on the OD, MW and ID sections in 4 quadrants taken from the Upset End, Slope Transition and Pipe Body regions. The hardness readings are taken at 1.5 mm from outer diameter (OD) and inner diameter (ID). As quenched and tempered material HV10 test results are shown in FIG. 6 .
  • the fracture mechanics characteristic is evaluated using the Transverse Charpy V Notch Impact Test.
  • the test temperature is ⁇ 30° C.
  • Sets of three full size specimens (10 ⁇ 10 mm) are taken from upset end, slope transition and pipe body regions in two quadrants, 0° and 180°, for each sample of quenched and tempered material.
  • FIG. 7 shows that all the individual values of Absorbed Energy are above 70 Joules which is established as minimum target and 90 Joules as minimum average of 3 specimens.
  • the transition temperature obtained in the transverse direction using Charpy V-notch 10 ⁇ 10 specimens in material representing pipe body and upset end are below ⁇ 60° C. as is shown in Tables 5 (a) (b).
  • Samples from as-quenched and as-quenched and tempered material are prepared for microstructural analysis.
  • the transverse face to the rolling axis is metallographically prepared by sanding down to 600 sand paper and polished to a mirror-like appearance with diamond paste and etched with Nital at 2% to carry out microstructural observations by optical microscope.
  • Microstructures are observed on OD, MW and ID sections of pipe body, slope transition and upset end regions. Two quadrants, 0° and 180°, photomicrographs at 500 ⁇ representing the microstructure from OD, MW and ID are obtained.
  • the observed microstructure in the pipe body after quenching consists of a mixture of predominantly bainite and acicular ferrite through the wall thickness and a slight presence of martensite close to the outer and inner surface.
  • bainite and acicular ferrite and some regions of non-polygonal ferrite are observed through the wall thickness at the upset section.
  • the prior austenitic grain size are measured using image analysis on as-quenched material etched with saturated aqueous picric acid on samples from the pipe body and the upset end at 0° and 180° Quadrants, resulting in an average size of 9/10 ASTM.
  • the microstructure after the tempering treatment consists of predominantly bainite and acicular ferrite are observed through the wall thickness on material representing pipe body, slope transition and upset end.
  • the fatigue test results are shown in FIG. 8 .
  • the test results show very high fatigue performance at upset ends, transition and pipe body.
  • the Charpy test temperature is ⁇ 40° C.
  • Sets of three full size specimens (10 ⁇ 10 mm) are taken from midwall of upset end, slope transition and pipe body regions in two quadrants 0° y 180°, from quenched and tempered material.
  • all results are above the expected minimum absorbed energy values of 70 Joules minimum individual and 90 Joules as minimum average of 3 specimens.
  • Transverse Charpy V-Notch impact transition curves are obtained from 2 samples, one representing upset end and another one representing pipe body from quenched and tempered material for each case.
  • the transition temperature obtained in the transverse direction using Charpy V-notch 10 ⁇ 10 specimens is between ⁇ 50° C. and ⁇ 60° C. for the material representing the upset end and below ⁇ 70° C. for material representing pipe body as shown in Table 9.
  • Transverse Charpy V-Notch impact transition curves are obtained from 2 samples representing upset end and another representing pipe body of quenched and tempered material for each case.
  • the transition temperature obtained in the transverse direction using Charpy V-notch 10 ⁇ 10 specimens is between ⁇ 50° C. and ⁇ 60° C. for the material representing the upset end and below ⁇ 70° C. for material representing pipe body as shown in Table 7.
  • CTOD results from material representing pipe body and upset end are above 0.6 mm at ⁇ 10° C. as shown in Table 8.
  • HIC test is performed on 1 sample representing upset end and another representing pipe body for Case 2.
  • Each set of 3 specimens (3 quadrants, 0°, 120° and 240°) representing pipe body and another set representing upset end is tested as per NACE TM0284 using Solution “A”, test period was 96 hours.
  • the results are shown in Tables 9 and 10.
  • SSC Four Point Bend Test is performed on 1 sample representing upset end and another representing pipe body. Each set of 3 specimens (3 quadrants, 0°, 120° and 240°) representing pipe body and another set representing upset end is tested as per ASTM G48. Test solution “A” of NACE TM0177 is considered. Testing stress is 95% of Specified Minimum Yield Strength (SMYS) and two test periods of 96 hours and 720 hours. The results are shown in Tables 11 and 12.
  • PIPE BODY (a) 1 2418.32 2.72 2503.61 3.57 95 Not failed 2 2418.32 2.72 2503.61 3.57 95 Not failed 3 2418.32 2.72 2503.61 3.57 95 Not failed SULFIDE STRESS CRACKING - FOUR POINT BEND TEST SOLUTION “A” NACE 0177-96 - TEST DURATION: 720 HRS.
  • PIPE BODY (b) 1 2809.95 2.70 2980.25 3.62 95 Not failed 2 2809.95 2.70 2980.25 3.62 95 Not failed 3 2809.95 2.70 2980.25 3.62 95 Not failed
  • UPSET END (a) 1 2418.32 2.72 2503.61 3.57 95 Not failed 2 2418.32 2.72 2503.61 3.57 95 Not failed 3 2418.32 2.72 2503.61 3.57 95 Not failed SULFIDE STRESS CRACKING - FOUR POINT BEND TEST SOLUTION “A” NACE 0177-96 - TEST DURATION: 720 HRS.
  • UPSET END (b) 1 2809.95 2.70 2980.25 3.62 95 Not failed 2 2809.95 2.70 2980.25 3.62 95 Not failed 3 2809.95 2.70 2980.25 3.62 95 Not failed Tables 11 and 12 show that all Four Point Bend specimens passed successfully the SSC test after the test period, stressed at 95% SMYS, no cracks are observed after 96 hours and even after 720 hours.
  • Optical Microscopy and Scanning Electron Microscopy is used for material characterization. Microstructural analysis is performed on OD, MW and ID sections of pipe body, slope transition and upset end regions in two quadrants 0° and 180° for samples in the as-quenched condition and quench and tempered condition.
  • the pipe body as-quenched microstructure consists of predominantly bainite and acicular ferrite at midwall and, close to the outer and inner surface, a slight presence of martensite is observed.
  • the upset as-quenched microstructure consists of predominantly bainite and acicular ferrite through the wall thickness.
  • the PAGS is measured using image analysis on as-quenched material etched with saturated aqueous picric acid on samples from pipe body and upset end. An average PAGS size of 7 ⁇ 8 ASTM is obtained for both pipe body and upset end respectively.
  • the microstructure at mid-wall after tempering consists of predominantly bainite and acicular ferrite at the pipe body and slope transition; and bainite, acicular ferrite, and non-polygonal ferrite at the upset ends.
  • the fatigue test results are plotted in FIG. 13 .
  • the test results show very high fatigue performance at upset ends, transition and pipe body.
US12/073,879 2007-03-15 2008-03-11 Seamless steel tube for use as a steel catenary riser in the touch down zone Abandoned US20080226396A1 (en)

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US12/073,879 US20080226396A1 (en) 2007-03-15 2008-03-11 Seamless steel tube for use as a steel catenary riser in the touch down zone
CA2680943A CA2680943C (en) 2007-03-15 2008-03-14 A seamless steel tube for use as a steel catenary riser in the touch down zone
EP08741588A EP2157197A2 (en) 2007-03-15 2008-03-14 Seamless steel pipe to be used as a steel catenary riser in the touchdown zone
MX2009009905A MX340352B (es) 2007-03-15 2008-03-14 Tuberia de acero sin costura para usarse como una columna ascente catenaria de acero en el area de contacto.
PCT/MX2008/000041 WO2008111828A2 (es) 2007-03-15 2008-03-14 Tuberia de acero sin costura para usarse como un elevador catenario de acero en el area de contacto
BRPI0808963-9A BRPI0808963A2 (pt) 2007-03-15 2008-03-14 Tubo de aço sem costura para ser usado como riser rígido em catenária com extremidades reforçadas, método para fabricar um tubo de aço sem costura para ser usado como riser rígido em catenária com extremidades reforçadas, sequência tubular para ser usada como riser rígido em catenária
NO20093020A NO20093020L (no) 2007-03-15 2009-09-18 Somlost stalror for bruk som fleksibelt stalstigeror i et nedslagsfelt

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US20100136363A1 (en) * 2008-11-25 2010-06-03 Maverick Tube, Llc Compact strip or thin slab processing of boron/titanium steels
US20100193085A1 (en) * 2007-04-17 2010-08-05 Alfonso Izquierdo Garcia Seamless steel pipe for use as vertical work-over sections
US20100294401A1 (en) * 2007-11-19 2010-11-25 Tenaris Connections Limited High strength bainitic steel for octg applications
US20100319814A1 (en) * 2009-06-17 2010-12-23 Teresa Estela Perez Bainitic steels with boron
US20100326557A1 (en) * 2007-07-24 2010-12-30 V & M Deutschland Gmbh Method for the production of hot-finished seamless pipes having optimized fatigue properties in the welded state
US8002910B2 (en) 2003-04-25 2011-08-23 Tubos De Acero De Mexico S.A. Seamless steel tube which is intended to be used as a guide pipe and production method thereof
US8328958B2 (en) 2007-07-06 2012-12-11 Tenaris Connections Limited Steels for sour service environments
US8414715B2 (en) 2011-02-18 2013-04-09 Siderca S.A.I.C. Method of making ultra high strength steel having good toughness
US20130206274A1 (en) * 2010-08-18 2013-08-15 Huntington Alloys Corporation Process for producing large diameter, high strength, corrosion-resistant welded pipe and pipe made thereby
US8636856B2 (en) 2011-02-18 2014-01-28 Siderca S.A.I.C. High strength steel having good toughness
US8821653B2 (en) 2011-02-07 2014-09-02 Dalmine S.P.A. Heavy wall steel pipes with excellent toughness at low temperature and sulfide stress corrosion cracking resistance
US9040865B2 (en) 2007-02-27 2015-05-26 Exxonmobil Upstream Research Company Corrosion resistant alloy weldments in carbon steel structures and pipelines to accommodate high axial plastic strains
WO2015128282A1 (de) * 2014-02-25 2015-09-03 Vallourec Deutschland Gmbh Verfahren zur herstellung von warmgewalzten, nahtlosen rohren aus umwandlungsfähigem stahl, insbesondere für rohrleitungen für tiefwasseranwendungen und entsprechende rohre
US9187811B2 (en) 2013-03-11 2015-11-17 Tenaris Connections Limited Low-carbon chromium steel having reduced vanadium and high corrosion resistance, and methods of manufacturing
US9340847B2 (en) 2012-04-10 2016-05-17 Tenaris Connections Limited Methods of manufacturing steel tubes for drilling rods with improved mechanical properties, and rods made by the same
US9598746B2 (en) 2011-02-07 2017-03-21 Dalmine S.P.A. High strength steel pipes with excellent toughness at low temperature and sulfide stress corrosion cracking resistance
US9644248B2 (en) 2013-04-08 2017-05-09 Dalmine S.P.A. Heavy wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US9657365B2 (en) 2013-04-08 2017-05-23 Dalmine S.P.A. High strength medium wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
WO2017106449A1 (en) * 2015-12-16 2017-06-22 Artifex Engineering, Inc. Tubular connection assembly for improved fatigue performance of metallic risers
US9803256B2 (en) 2013-03-14 2017-10-31 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US9970242B2 (en) 2013-01-11 2018-05-15 Tenaris Connections B.V. Galling resistant drill pipe tool joint and corresponding drill pipe
WO2019123017A1 (en) * 2017-12-21 2019-06-27 Technip France Method of preparing a pipe-section
WO2020093129A1 (pt) * 2018-11-07 2020-05-14 Petróleo Brasileiro S.A. - Petrobras Tubo rígido metálico com extremidades mais espessas, riser submarino, processo e sistema de fabricação de tubo rígido metálico com extremidades mais espessas
US10844669B2 (en) 2009-11-24 2020-11-24 Tenaris Connections B.V. Threaded joint sealed to internal and external pressures
US11105501B2 (en) 2013-06-25 2021-08-31 Tenaris Connections B.V. High-chromium heat-resistant steel
US11124852B2 (en) 2016-08-12 2021-09-21 Tenaris Coiled Tubes, Llc Method and system for manufacturing coiled tubing
US11833561B2 (en) 2017-01-17 2023-12-05 Forum Us, Inc. Method of manufacturing a coiled tubing string
US11952648B2 (en) 2011-01-25 2024-04-09 Tenaris Coiled Tubes, Llc Method of forming and heat treating coiled tubing

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US8002910B2 (en) 2003-04-25 2011-08-23 Tubos De Acero De Mexico S.A. Seamless steel tube which is intended to be used as a guide pipe and production method thereof
US9040865B2 (en) 2007-02-27 2015-05-26 Exxonmobil Upstream Research Company Corrosion resistant alloy weldments in carbon steel structures and pipelines to accommodate high axial plastic strains
US20100193085A1 (en) * 2007-04-17 2010-08-05 Alfonso Izquierdo Garcia Seamless steel pipe for use as vertical work-over sections
US8328958B2 (en) 2007-07-06 2012-12-11 Tenaris Connections Limited Steels for sour service environments
US9718116B2 (en) * 2007-07-24 2017-08-01 Vallourec Deutschland Gmbh Method for the production of hot-finished seamless pipes having optimized fatigue properties in the welded state
US20100326557A1 (en) * 2007-07-24 2010-12-30 V & M Deutschland Gmbh Method for the production of hot-finished seamless pipes having optimized fatigue properties in the welded state
US20100294401A1 (en) * 2007-11-19 2010-11-25 Tenaris Connections Limited High strength bainitic steel for octg applications
US8328960B2 (en) 2007-11-19 2012-12-11 Tenaris Connections Limited High strength bainitic steel for OCTG applications
US8221562B2 (en) 2008-11-25 2012-07-17 Maverick Tube, Llc Compact strip or thin slab processing of boron/titanium steels
US20100136363A1 (en) * 2008-11-25 2010-06-03 Maverick Tube, Llc Compact strip or thin slab processing of boron/titanium steels
US20100319814A1 (en) * 2009-06-17 2010-12-23 Teresa Estela Perez Bainitic steels with boron
US10844669B2 (en) 2009-11-24 2020-11-24 Tenaris Connections B.V. Threaded joint sealed to internal and external pressures
US20130206274A1 (en) * 2010-08-18 2013-08-15 Huntington Alloys Corporation Process for producing large diameter, high strength, corrosion-resistant welded pipe and pipe made thereby
US11952648B2 (en) 2011-01-25 2024-04-09 Tenaris Coiled Tubes, Llc Method of forming and heat treating coiled tubing
US8821653B2 (en) 2011-02-07 2014-09-02 Dalmine S.P.A. Heavy wall steel pipes with excellent toughness at low temperature and sulfide stress corrosion cracking resistance
US9598746B2 (en) 2011-02-07 2017-03-21 Dalmine S.P.A. High strength steel pipes with excellent toughness at low temperature and sulfide stress corrosion cracking resistance
US9188252B2 (en) 2011-02-18 2015-11-17 Siderca S.A.I.C. Ultra high strength steel having good toughness
US8414715B2 (en) 2011-02-18 2013-04-09 Siderca S.A.I.C. Method of making ultra high strength steel having good toughness
US9222156B2 (en) 2011-02-18 2015-12-29 Siderca S.A.I.C. High strength steel having good toughness
US8636856B2 (en) 2011-02-18 2014-01-28 Siderca S.A.I.C. High strength steel having good toughness
US9340847B2 (en) 2012-04-10 2016-05-17 Tenaris Connections Limited Methods of manufacturing steel tubes for drilling rods with improved mechanical properties, and rods made by the same
US9970242B2 (en) 2013-01-11 2018-05-15 Tenaris Connections B.V. Galling resistant drill pipe tool joint and corresponding drill pipe
US9187811B2 (en) 2013-03-11 2015-11-17 Tenaris Connections Limited Low-carbon chromium steel having reduced vanadium and high corrosion resistance, and methods of manufacturing
US11377704B2 (en) 2013-03-14 2022-07-05 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US10378074B2 (en) 2013-03-14 2019-08-13 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US9803256B2 (en) 2013-03-14 2017-10-31 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US10378075B2 (en) 2013-03-14 2019-08-13 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US9644248B2 (en) 2013-04-08 2017-05-09 Dalmine S.P.A. Heavy wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US9657365B2 (en) 2013-04-08 2017-05-23 Dalmine S.P.A. High strength medium wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US11105501B2 (en) 2013-06-25 2021-08-31 Tenaris Connections B.V. High-chromium heat-resistant steel
US20160362759A1 (en) * 2014-02-25 2016-12-15 Vallourec Deutschland Gmbh Method for producing hot-rolled seamless pipes from transformable steel, in particular for pipelines for deep-water applications, and corresponding pipes
AU2015222278B2 (en) * 2014-02-25 2019-01-17 Vallourec Deutschland Gmbh Method for producing hot-rolled seamless pipes from transformable steel, in particular for pipelines for deep-water applications, and corresponding pipes
JP2017512254A (ja) * 2014-02-25 2017-05-18 ヴァローレック ドイチュラント ゲーエムベーハー 特に各種深海用途用の各パイプラインのための変形可能な鋼から各熱間圧延シ−ムレス管材を製造するための方法、および対応する各種管材
CN106232837A (zh) * 2014-02-25 2016-12-14 瓦卢瑞克德国有限公司 用于由可变形钢生产热轧无缝管，特别是用于深水应用的管道的方法，以及相应的管
WO2015128282A1 (de) * 2014-02-25 2015-09-03 Vallourec Deutschland Gmbh Verfahren zur herstellung von warmgewalzten, nahtlosen rohren aus umwandlungsfähigem stahl, insbesondere für rohrleitungen für tiefwasseranwendungen und entsprechende rohre
US10066445B2 (en) 2015-12-16 2018-09-04 Artifex Engineering, Inc. Tubular connection assembly for improved fatigue performance of metallic risers
WO2017106449A1 (en) * 2015-12-16 2017-06-22 Artifex Engineering, Inc. Tubular connection assembly for improved fatigue performance of metallic risers
US11124852B2 (en) 2016-08-12 2021-09-21 Tenaris Coiled Tubes, Llc Method and system for manufacturing coiled tubing
US11833561B2 (en) 2017-01-17 2023-12-05 Forum Us, Inc. Method of manufacturing a coiled tubing string
WO2019123017A1 (en) * 2017-12-21 2019-06-27 Technip France Method of preparing a pipe-section
WO2020093129A1 (pt) * 2018-11-07 2020-05-14 Petróleo Brasileiro S.A. - Petrobras Tubo rígido metálico com extremidades mais espessas, riser submarino, processo e sistema de fabricação de tubo rígido metálico com extremidades mais espessas

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BRPI0808963A2 (pt) 2014-08-26
WO2008111828A3 (es) 2009-01-15

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