CA2682959A1 - A seamless steel tube for the application as work-over riser - Google Patents
A seamless steel tube for the application as work-over riser Download PDFInfo
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- CA2682959A1 CA2682959A1 CA002682959A CA2682959A CA2682959A1 CA 2682959 A1 CA2682959 A1 CA 2682959A1 CA 002682959 A CA002682959 A CA 002682959A CA 2682959 A CA2682959 A CA 2682959A CA 2682959 A1 CA2682959 A1 CA 2682959A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 31
- 239000010959 steel Substances 0.000 title claims abstract description 31
- 238000000034 method Methods 0.000 claims abstract description 33
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 16
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 13
- 239000011651 chromium Substances 0.000 claims abstract description 10
- 239000010949 copper Substances 0.000 claims abstract description 10
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 10
- 239000001257 hydrogen Substances 0.000 claims abstract description 10
- 239000010955 niobium Substances 0.000 claims abstract description 10
- 239000010936 titanium Substances 0.000 claims abstract description 10
- 239000011575 calcium Substances 0.000 claims abstract description 9
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 9
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 8
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 8
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 8
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 8
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 8
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 8
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 8
- 229910052785 arsenic Inorganic materials 0.000 claims abstract description 8
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 8
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 239000011733 molybdenum Substances 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 8
- 239000011574 phosphorus Substances 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 239000010703 silicon Substances 0.000 claims abstract description 8
- 125000004435 hydrogen atom Chemical class [H]* 0.000 claims abstract 4
- 238000012360 testing method Methods 0.000 claims description 35
- 229910000734 martensite Inorganic materials 0.000 claims description 33
- 239000000463 material Substances 0.000 claims description 27
- 238000004519 manufacturing process Methods 0.000 claims description 25
- 238000010791 quenching Methods 0.000 claims description 19
- 230000009466 transformation Effects 0.000 claims description 18
- 238000010438 heat treatment Methods 0.000 claims description 16
- 238000007689 inspection Methods 0.000 claims description 15
- 238000003754 machining Methods 0.000 claims description 11
- 238000009659 non-destructive testing Methods 0.000 claims description 10
- 239000011572 manganese Substances 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 230000000171 quenching effect Effects 0.000 claims description 8
- 238000005096 rolling process Methods 0.000 claims description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- 239000011593 sulfur Substances 0.000 claims description 7
- 238000009658 destructive testing Methods 0.000 claims description 6
- 238000009864 tensile test Methods 0.000 claims description 6
- 238000011179 visual inspection Methods 0.000 claims description 6
- 238000005303 weighing Methods 0.000 claims description 6
- 239000008186 active pharmaceutical agent Substances 0.000 claims description 5
- 238000005496 tempering Methods 0.000 claims description 5
- 239000012085 test solution Substances 0.000 claims description 5
- 230000003750 conditioning effect Effects 0.000 abstract 2
- 239000005864 Sulphur Substances 0.000 abstract 1
- 239000004411 aluminium Substances 0.000 abstract 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract 1
- 230000007797 corrosion Effects 0.000 description 11
- 238000005260 corrosion Methods 0.000 description 11
- 238000012512 characterization method Methods 0.000 description 5
- 238000005553 drilling Methods 0.000 description 5
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 150000002431 hydrogen Chemical class 0.000 description 4
- 239000003921 oil Substances 0.000 description 4
- 230000001066 destructive effect Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 235000019441 ethanol Nutrition 0.000 description 2
- 229910017604 nitric acid Inorganic materials 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
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
- 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
-
- 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
- C21D9/085—Cooling or quenching
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- E—FIXED CONSTRUCTIONS
- E21—EARTH OR ROCK DRILLING; MINING
- E21B—EARTH OR ROCK 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Geology (AREA)
- Life Sciences & Earth Sciences (AREA)
- Mining & Mineral Resources (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Environmental & Geological Engineering (AREA)
- Fluid Mechanics (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Extraction Processes (AREA)
- Rod-Shaped Construction Members (AREA)
Abstract
The present invention relates to seamless steel tubing for conditioning risers, said tubing comprising, in percentage by weight, 0.23-0.29 carbon, 0.45-0.65 manganese, 0.15-0.35 silicon, 0.90-1.20 chromium, 0.70-0.90 molybdenum, maximum 0.20 nickel, maximum 0.010 nitrogen, 0.0010-0.0030 boron, 0.010-0.045 aluminium, maximum 0.005 sulphur, maximum 0.015 phosphorus, 0.005-0.030 titanium, 0.020-0.035 niobium, maximum 0.15 copper, maximum 0.20 arsenic, maximum 0.0040 calcium, maximum 0.020 tin, maximum 2.4 ppm hydrogen, the remainder being iron and inevitable impurities. The geometry of the pipe is such that the ends thereof have increasing wall thickness and outer diameter, and the pipe has an elasticity limit of at least 620 MPa (90 ksi) throughout the length of the pipe body and at the pipe ends. The present invention also relates to methods for producing seamless steel piping for conditioning risers having an elasticity limit of at least 620 MPa (90 ksi) both in the pipe body and at the pipe ends.
Description
A SEAMLESS STEEL TUBE FOR THE APPLICATION AS WORK-OVER RISER
FIELD OF THE INVENTION
This invention relates to a seamless steel tube for risers used in work-over operations.
BACKGROUND OF THE INVENTION
The requirements for operating a well in the seabed involve a plurality or systems and equipment including drilling, production and work-over risers.
A drilling riser is a pipe between a seabed blow-out preventer (BOP) and a floating drilling rig which is a drilling unit not permanently fixed to the seabed such as a drillship, a semi-submersible or jack-up unit. A drilling rig is meant to be the derrick and its associated machinery.
A production riser is a pipeline carrying oil or gas that joins a seabed wellhead to a deck of a production platform or a tanker loading platform.
A work-over riser is a flowline which is used to carry on a well work-over, which is performed on an existing well and may involve re-evaluating the production formation, clearing sand from producing zones, jet lifting, replacing downhole equipment, deepening the well, acidizing or fracturing or improving the drive mechanism.
In recent years such work-over operations have been increasingly carried out using coiled or continuous reel tubing as disclosed in US4281716 (Standard Oil Co. Indiana).
However, according to W09816715 (Kvaerner Eng.), there are several advantages using a continuous single tube when entering a live oil or gas well. This means the well does not have to be killed, (i.e. a heavy fluid does not have to be pumped down the production tubing to control the oil or gas producing zone by the effect of its greater hydrostatic pressure). Continuous tubing has the advantage of also being able to pass through the tubing through which the oil and/or gas is being produced, without disturbing the tubing in place.
Taking in account that work-over risers are subjected to fatigue and load stresses besides of corrosion attack, pipes used in this environment are likely to have fatigue and corrosion resistance properties to accomplish a good performance, reduce both, the weight of the riser string and the bending loads in the wellhead and the platform interface.
FIELD OF THE INVENTION
This invention relates to a seamless steel tube for risers used in work-over operations.
BACKGROUND OF THE INVENTION
The requirements for operating a well in the seabed involve a plurality or systems and equipment including drilling, production and work-over risers.
A drilling riser is a pipe between a seabed blow-out preventer (BOP) and a floating drilling rig which is a drilling unit not permanently fixed to the seabed such as a drillship, a semi-submersible or jack-up unit. A drilling rig is meant to be the derrick and its associated machinery.
A production riser is a pipeline carrying oil or gas that joins a seabed wellhead to a deck of a production platform or a tanker loading platform.
A work-over riser is a flowline which is used to carry on a well work-over, which is performed on an existing well and may involve re-evaluating the production formation, clearing sand from producing zones, jet lifting, replacing downhole equipment, deepening the well, acidizing or fracturing or improving the drive mechanism.
In recent years such work-over operations have been increasingly carried out using coiled or continuous reel tubing as disclosed in US4281716 (Standard Oil Co. Indiana).
However, according to W09816715 (Kvaerner Eng.), there are several advantages using a continuous single tube when entering a live oil or gas well. This means the well does not have to be killed, (i.e. a heavy fluid does not have to be pumped down the production tubing to control the oil or gas producing zone by the effect of its greater hydrostatic pressure). Continuous tubing has the advantage of also being able to pass through the tubing through which the oil and/or gas is being produced, without disturbing the tubing in place.
Taking in account that work-over risers are subjected to fatigue and load stresses besides of corrosion attack, pipes used in this environment are likely to have fatigue and corrosion resistance properties to accomplish a good performance, reduce both, the weight of the riser string and the bending loads in the wellhead and the platform interface.
Also, these pipes need to have a good welding performance just to be welded to weld-on-connectors to build the string.
OBJECT OF THE INVENTION
A first object of the invention is to provide a seamless steel tube to be used as a riser in work-over operations with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter to reduce the weight of the riser string.
A second object is to provide a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter to reduce the bending loads in the wellhead and the platform interface.
A third object of the invention is to provide a method of manufacturing of a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter using upsetting techniques.
OBJECT OF THE INVENTION
A first object of the invention is to provide a seamless steel tube to be used as a riser in work-over operations with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter to reduce the weight of the riser string.
A second object is to provide a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter to reduce the bending loads in the wellhead and the platform interface.
A third object of the invention is to provide a method of manufacturing of a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter using upsetting techniques.
A fourth object of the invention is to provide a method of manufacturing of a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter using machining techniques.
A fifth object of the invention is to provide a method of manufacturing of a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter able to guarantee the mechanical characteristics to have high fatigue and corrosion resistance and a good welding performance.
Also, the tubes used as work-over risers may be reused meaning an economical saving.
BRIEF DESCRIPTION OF THE DRAWINGS
Figure 1 illustrates a preferred embodiment of the work over riser of the present invention with upset ends.
Figure 2 shows a graphical representation of the Tensile test results (YS and UTS) from upset and pipe body sections from material in the as-quenched and tempered condition of the different industrial trials.
Figure 3 shows a graphical representation of the HRC
hardness values from upset and pipe body sections showing the achievement of the minimum % of martensitic transformation from material in the as-quenched condition of the production of both dimensions.
Figures 4 and 5 show a graphical representation of the HRC
hardness values from upset and pipe body sections showing the individual hardness readings dispersion as a function of the location through the thickness (OD, MW & ID) from material in the as- tempered condition of the production of 7"OD x 17.5 mm WT
dimension and 8 5/8" OD x 15.9mm WT dimension, respectively.
Figure 6 shows a graphical representation of the transverse CVN impact testing results at -20 C from upset and pipe body sections of the production of both dimensions showing the individual toughness values dispersion as per specification from material in the as-tempered condition.
Figure 7 shows the austenitic grain size reported in 9/10 ASTM in the pipe body and 8/9 ASTM in the upset end.
Figure 8 shows transverse section photomicrographs showing a microstructure constituted by martensite through the wall thickness of the pipe body section of quenched material for Nital 2% in 300X magnification.
Figure 9 shows transverse section photomicrographs showing a microstructure constituted by martensite in the upset end of as-quenched material for Nital 2% in 300X magnification.
Figure 10 shows transverse section photomicrographs, showing a microstructure constituted by tempered martensite in the pipe body of quenched & tempered material for Nital 2% in 300X magnification.
Figure 11 shows transverse section photomicrographs, showing a microstructure constituted by tempered martensite in the upset end of quenched & tempered material for Nital 2% in 300X magnification.
Figure 12 shows microstructural observations of as quenched material at the pipe machined body and the end zones revealing a prior austenitic grain size of 8/9 in both zones measured by the saturation method as per ASTM E-1 12.
Figure 13 shows transverse section photomicrographs showing a microstructure constituted by martensite through the wall thickness of the machined pipe body section of quenched material for Nital 2% in 300X magnification.
Figure 14 shows transverse section photomicrographs showing a microstructure constituted by martensite through the wall thickness of the pipe end section of quenched material for Nital 2% in 300X magnification.
Figure 15 shows transverse . section photomicrographs showing a microstructure constituted by tempered martensite through the thickness of the pipe body section of quenched and tempered material. for Nital 2% in 300X magnification.
Figure 16 shows transverse section photomicrographs showing a microstructure constituted by tempered martensite through the thickness of the pipe end section of quenched and tempered material for Nital 2% in 300X magnification.
BRIEF SUMMARY OF THE INVENTION
The present invention describes a seamless steel tube to be used as a riser in work-over operations with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter. The alloy design is based on high strength requirements. The main features of the chemical composition of the tube include 0.23-0.28 wt % C, 0.45 -0.65 wt % Mn, and other alloying elements such as Mo, and Cr to achieve the required percentage of martensitic transformation. In addition, microalloying elements such as Ti and Nb are used as grain refiners. Low content of residual elements such as S and residual elements such as Cu and P are used to avoid any corrosion problem related to inclusions promotion and segregation at grain boundaries which decrease the corrosion performance, the hydrogen content was kept below 2.4 ppm to avoid any problem related to hydrogen entrapment and decrease of the corrosion performance.
The production route for manufacturing the upset seamless pipe for the application of as Work Over Riser, includes the following steps: steel casting (Continuous Cast Bar), seamless pipe rolling (MPM process), pipe ends upsetting, heat treatment, destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC testing), dimensional control of pipe body and upset ends (outside diameter, out of roundness, excentricity, straightness, internal diameter, length), machining of external and internal upset end, dimensional control (internal diameter, outside diameter and machined length), drift testing at the upset ends, non-destructive testing (NDT) of upset ends, weighing, measuring and marking, external surface visual inspection, UT
inspection of pipe body and UT inspection of upset ends (cylindrical section only).
The production route for manufacturing the machining seamless pipe for the application of as Work Over Riser includes the following steps: steel casting (Continuous Cast Bar), seamless pipe rolling (MPM process), heat treatment, destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC testing), dimensional control of pipe body (outside diameter, out of roundness, straightness, internal diameter, length), machining from external surface the complete length of the pipe by programming CNC lath machine in order to achieve final dimensions at the ends, dimensional control (internal diameter, outside diameter, out of roundness, straightness, and length) of pipe body and machined ends, drift testing at the ends, non-destructive testing (NDT) of ends, weighing, measuring and marking, external surface visual inspection, UT inspection of machined pipe body and UT
inspection of ends (cylindrical section only).
The combination of chemical composition and tight control of heat treatment parameters allows achieving the adequate microstructure after quench and temper in order to achieve the mechanical properties and pass the SSC Method A tests requirements described above.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
OF THE INVENTION
The chemical composition of the seamless steel tube of the present invention comprises in weight per cent: carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities.
A more preferred composition comprises: carbon 0.25-0.28, manganese 0.48-0.58, silicon 0.20-0.30, chromium 1.05-1.15, molybdenum 0.80- 0.83, nickel 0.10 max, nitrogen 0.008 max, boron 0.0016-0.0026, aluminum 0.015-0.045, sulfur 0.0030 max, phosphorus 0.010 max, titanium 0.016-0.026, niobium 0.025-0.030, copper 0.10 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.015 max, hydrogen 2.0 ppm max, the rest are iron and inevitable impurities.
The seamless steel tubes have a geometry, in which ends of tubes have an increased wall thickness and outer diameter, and following mechanical properties:
In the as-quench condition 90% of martensitic transformation when evaluated according to the following formulae: HRCmin = (58 x %C) + 27 Austenitic grain size as per ASTM minimum 5 or finer In the as-quench and temper condition Longitudinal Tensile Test (round standard specimens when wall thickness equal or above 1" and longitudinal strip specimens when wall thickness below 1").
Minimum Yield Strength: 90ksi (620 MPa) Maximum Yield Strength: 105ksi (724 MPa) Minimum Ultimate Tensile Strength: lOOksi (690 MPa) Minimum Elongation (L = 4D): 18%
Yield to Tensile Ratio < 0.92 Transverse Charpy Test (using 10x10 mm specimen) Minimum individual Absorbed Energy: 30 Joules Minimum Average Absorbed Energy: 40 Joules Maximum Hardness value: 25.4 Hrc (value as per API 5CT
means average per row) Microcleanliness acceptance criteria as per ASTM E-45 A:
A, B, C, D all below 2 Compliance with NACE, acceptance criteria: Passing SSC
Method A test as per NACE TM0177-2005, using test solution (A), testing at 85%SMYS, test period 720 hours.
The geometry of seamless steel tube of the present invention and the mechanical characteristics are obtained by two methods of manufacturing: upsetting and machining.
The upsetting manufacturing method comprises the following steps:
(a) providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities, obtained by rolling process (MPM process) (b) upsetting of tube ends;
(c) austenitizing between 850-930 C the full length of the tube; and (d) quenching and tempering between 630-720 C
(e) destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, according to the formulae HRCmin _(58 x %C) + 27 , tensile, hardness, toughness, SSC testing) (f) dimensional control of pipe body and upset ends (outside diameter, out of roundness, eccentricity, straightness, internal diameter, length) (g) machining of external and internal upset end (h) dimensional control (internal diameter, outside diameter and machined end) (i) drift testing at the upset ends (j) non-destructive testing of upset ends, weighing, measuring and marking, external surface visual inspection, UT inspection of pipe body and UT
inspection of upset ends.
The machining manufacturing method comprises the following steps:
(a) providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities, obtained by rolling process (MPM process (b) heat treatment o pipes (austenitizing between 850-930 C the full length of the tube; and quenching and tempering between 630-720 C) (c) destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation according to the formulae , tensile, hardness, toughness, SSC testing) (d) dimensional control of pipe body (OD, out of roundness, straightness, ID, length) (e) machining from external surface the complete length of the pipe by programming CNC lath machine in order to achieve final dimensions at the ends, (f) dimensional control (ID, OD, out of roundness, straightness and length) of pipe body and machined ends (g) drift testing at the ends, (h) non destructive testing (NDT) of ends, weighing, measuring and marking, external surface visual inspection, UT inspection of machined pipe body and UT inspection of machined ends (cylindrical section only).
Both methods are also performed providing a seamless steel pipe with the preferred composition, as disclosed above.
The seamless steel tube of the present invention may be divided into two zones. As shown in Figure 1, there is an increased wall thickness and diameter end with internal and external length (upsetting or machined zone) and the tube body.
Due to a combination of the manufacturing methods and the chemistry design, both the whole tube body and the ends have the same yield strength of at least 620 MPa (90 ksi) (YS) and at most 724 MPa (105 ksi), a Yield to Tensile Ratio not greater than 0.92, also, the same ultimate tensile strength (UTS) of at least 690 MPa (100 ksi), elongation of at least 18%, hardness Rockwell of at most 25.4 HRC (value as per API 5CT means average per row) and corrosion resistance (Compliance with NACE, acceptance criteria: Passing SSC Method A test as per NACE
TM0177-2005, using test solution (a), testing at 85%SMYS, test period 720 hours). Prior Austenitic Grain Size is 5 or less. The product after the quench heat treatment process shall comply with Prior Austenitic Grain Size (PAGS) is 5 or less a microstructure of at least 90% martensite in the as-quench condition.
The tubes may be utilized in sour and non-sour service.
The tubes' nominal diameter to be upsetted ends may be from 4'/z" to 10 W.
The tubes' nominal diameter which ends will to be machined may be from 4'/z" to 18" due to the manufacturing facilities.
The tubes' thickness ranges from 10 mm to 50 mm.
Examples Example 1 Two industrial development trials for two dimensions of tubes (8 5/8" ODx15.9 mm WT and 7" OD x 17.5 mm WT) were carried on. The chemistry design is shown in Table 1 and the desired ranges of mechanical properties are shown in Table 2.
Table 1 Element Minimum Maximum C 0.25 0.28 Mn 0.48 0.58 Si 0.20 0.30 P 0 0.010 S 0 0.0030 Mo 0.80 0.83 Cr 1.05 1.15 Nb 0.025 0.030 Ni 0 0.10 Cu 0 0.10 Sn 0 0.015 Al 0.015 0.045 Ti 0.016 0.026 As 0 0.020 Ca 0 0.0040 B 0.0016 0.0026 N 0 0.008 H 0 2.0 Table 2 Property Min Max Yield Strength EUL 0.5% (MPa) 620 724 Ultimate Tensile Strength (MPa) 690 n/a Yield to Tensile Ratio (Y/T) 0.92 Elongation (%) (L=4D) 18 -Individual Absorbed Energy At -20 C (J) 30 -Average Absorbed Energy At -20 C (J) 40 -Hardness Rockwell HRC-value (tempered n/a 25.4*
condition) Microcleanliness (acceptance criteria as - 2 per ASTM E-45A: A, B, C, D) Corrosion Test Solution period NACE TM0177-2005 SSC Method A- 85% 720 hrs. A
SMYS
*API 5CT: value= average per row The upsetting manufacturing operation was performed following the steps of:
a) The pipe ends in the as-rolled condition were heated up to the appropriate forging temperature heating the calculated pipe length. The upsetting operation takes place at a minimum temperature of 1000 C.
b) Once the heating cycle was accomplished, pipe ends were upset with the appropriate die and tooling design for each particular dimension.
C) Inspection was then made on pipes' external and internal surfaces after each strike/punch in order to find any possible defect generated by the upsetting operation.
Special care was taken into consideration when designing the heating curve to be use during the heat treatment process in the austenitizing furnace (860-940 C) and the tempering furnace (640-720 C) for the upset ends of the 8 5/8"OD product. After austenitizing heat treatment process, the pipe must enter the quenching process above AC3 to guaranteed through-wall transformation. Then, for the 7"OD product, a few heat treatment adjustments were made on the heating curves based on the results obtained from the other dimension 8 5/8" OD pipe.
The actual temperatures from the pipe body and upset ends outer surface were carefully measured throughout the trial stages right at the entrance of the pipes into the quenching head by using a manual pyrometer in addition to the furnace pyrometers.
After the heat treatments, a mechanical characterization was performed. From the as-quenched material, the % of martensitic transformation was calculated. Tensile, hardness, and toughness tests were performed on the quenched and tempered material on both upset and pipe body sections. Specifications were met; good hardenability, yield strength values of over 92 ksi as-tempered HRC values below the maximum allowed (25.4 HRC) and absorbed energy higher than 100 Joules at the specified temperature of -20 C.
Extensive destructive characterization and corrosion SSC
Method A (NACE Standard Tensile Test, TM0177-96) were also conducted.
Homogeneity in tensile properties, hardness and toughness test results are a consequence of a very homogenous microstructure through the wall on both upset end and pipe body in the as quenched and tempered condition. Figures 2 through 5 illustrate several graphical representations of the mechanical properties including hardness.
The austenitic grain size was measured on as-quenched material by the saturation method as per ASTM E-112. As shown in Figure 6, the grain size reported on the samples were 9/10 in the pipe body which was above the required size since the minimum required was 5. The upset samples showed a grain size of 8/9 and 9/10 complying with the specifications as illustrated in Figure 6.
The transversal face to the rolling axis was metallographically prepared and etched with Nital 2% to perform microstructural observations with an optical microscope. (Nital:
Solution of 2% of Nitric acid in Ethyl Alcohol).
In the as-quenched samples, a martensitic microstructure was observed on OD, ID and MW sections through the thickness achieving a martensitic transformation of over 90% measured from the HRC hardness values as shown in Figures 8 and 9.
In the as-quench and tempered material, a microstructure constituted by tempered martensite was observed through the thickness as shown in Figures 10 and 11.
The microstructures observed in as-quenched material were mainly martensitic with over 95% of martensitic transformation through the entire thickness of the pipe on both pipe body and upset which indicates that the temperature at which the pipe entered the quenching stage and the quenching itself were homogeneous. On the other hand, the microstructures observed in tempered material, tempered martensite was present through the thickness.
The material passed the SSC Method A test at 85%SMYS
as per NACE TM0177-96 accomplishing the 720 hours.
Corrosion Testing Results as per NACE Method A
NACE TM-0177-96 Method A
Initial Final Stress Sample Location Heat Specimen Diameter Initial PH Diameter Final PH Applied Result SMYS %
98449 Upset 19874 A 6,39 2,69 6,21 3,64 85 NF*
98449 Upset 19874 B 6,42 2,69 6,33 3,62 85 NF*
98449 Upset 19874 C 6,4 2,69 6,29 3,69 85 NF*
8448 Pipe Body 19874 A 6,36 2,66 6,24 3,53 85 NF*
8448 Pipe Body 19874 B 6,41 2,66 6,31 3,51 85 NF*
8448 Pipe Body 19874 C 6,4 2,66 6,29 3,52 85 NF*
98448 Upset 19874 A 6,37 2,66 6,22 3,5 85 NF*
98448 Upset 19874 B 6,37 2,66 6,2 3,5 85 NF*
98448 Upset 19874 C 6,4 2,66 6,33 3,49 85 NF*
*NF: Not failed Example 2 An industrial development trial for a dimension of tube (8.26" OD x 44 mm WT and 9.97" OD x 41 mm WT) were carried on. The chemistry design is shown in Table 1 and the desired ranges of mechanical properties are shown in Table 2 of Example 1.
The pipe was rolled in a heavy wall condition. The wall thickness was about 44 mm.
After rolling, heat treatment is performed. Similar considerations about this step were made such as in Example 1 to obtain through wall transformation.
After heat treatment of pipes, detail mechanical characterization was performed such as in Example 1.
Dimensional control of the outside diameter (OD), out of roundness, inside diameter (ID) and length of pipes was carried on followed by the UT inspection.
In order to achieve final dimensions, the complete length of pipe body was machined from external surface by programming CNC lath machine.
Once again, a dimensional control of pipes after machining was carried out.
For quality purposes, non destructive inspection of straight pipe body section using automatic UT and manual for the cylindrical ends.
As in Example 1, a mechanical characterization was performed, calculating the % of martensitic transformation from the as-quenched material. On the quenched and tempered material, tensile, hardness, and toughness tests were performed on both machined ends and pipe body sections. Specifications were met; good hardenability, yield strength values of over 94 ksi as-tempered HRC values below the maximum allowed (25.4 HRC) and absorbed energy higher than 100 Joules at the specified temperature of -20 C.
Extensive destructive characterization and corrosion SSC
Method A (NACE Standard Tensile Test, TM0177-96) were also conducted.
Homogeneity in tensile properties, hardness and toughness test results are a consequence of a very homogenous microstructure through the wall on both machined ends and pipe body in the as quenched and tempered condition.
Microstructural observations of as-quenched material at the pipe machined body and the ends zones reveal a prior austenitic grain size of 8/9 in both zones measured by the saturation method as per ASTM E-112. The modified end on the analyzed sample showed a grain size of 8/9 complying with the specifications as shown in Figure 12.
The transversal face to the rolling axis was metallographically prepared and etched with Nital 2% to perform microstructural observations with an optical microscope. (Nital:
Solution of 2% of Nitric acid in Ethyl Alcohol).
In the as-quenched sample, a martensitic microstructure was observed on OD, ID and MW sections through the thickness achieving a martensitic transformation of over 90% measured from the HRC hardness values as shown in Figures 13 and 14.
In the as-quench and tempered material, a microstructure constituted by tempered martensite was observed through the thickness as shown in Figures 15 and 16.
The material passed the SSC method A test at 85%SMYS
as per NACE TM0177-2005 accomplishing the 720 hours.
A fifth object of the invention is to provide a method of manufacturing of a seamless steel tube for the application as a work-over riser with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter able to guarantee the mechanical characteristics to have high fatigue and corrosion resistance and a good welding performance.
Also, the tubes used as work-over risers may be reused meaning an economical saving.
BRIEF DESCRIPTION OF THE DRAWINGS
Figure 1 illustrates a preferred embodiment of the work over riser of the present invention with upset ends.
Figure 2 shows a graphical representation of the Tensile test results (YS and UTS) from upset and pipe body sections from material in the as-quenched and tempered condition of the different industrial trials.
Figure 3 shows a graphical representation of the HRC
hardness values from upset and pipe body sections showing the achievement of the minimum % of martensitic transformation from material in the as-quenched condition of the production of both dimensions.
Figures 4 and 5 show a graphical representation of the HRC
hardness values from upset and pipe body sections showing the individual hardness readings dispersion as a function of the location through the thickness (OD, MW & ID) from material in the as- tempered condition of the production of 7"OD x 17.5 mm WT
dimension and 8 5/8" OD x 15.9mm WT dimension, respectively.
Figure 6 shows a graphical representation of the transverse CVN impact testing results at -20 C from upset and pipe body sections of the production of both dimensions showing the individual toughness values dispersion as per specification from material in the as-tempered condition.
Figure 7 shows the austenitic grain size reported in 9/10 ASTM in the pipe body and 8/9 ASTM in the upset end.
Figure 8 shows transverse section photomicrographs showing a microstructure constituted by martensite through the wall thickness of the pipe body section of quenched material for Nital 2% in 300X magnification.
Figure 9 shows transverse section photomicrographs showing a microstructure constituted by martensite in the upset end of as-quenched material for Nital 2% in 300X magnification.
Figure 10 shows transverse section photomicrographs, showing a microstructure constituted by tempered martensite in the pipe body of quenched & tempered material for Nital 2% in 300X magnification.
Figure 11 shows transverse section photomicrographs, showing a microstructure constituted by tempered martensite in the upset end of quenched & tempered material for Nital 2% in 300X magnification.
Figure 12 shows microstructural observations of as quenched material at the pipe machined body and the end zones revealing a prior austenitic grain size of 8/9 in both zones measured by the saturation method as per ASTM E-1 12.
Figure 13 shows transverse section photomicrographs showing a microstructure constituted by martensite through the wall thickness of the machined pipe body section of quenched material for Nital 2% in 300X magnification.
Figure 14 shows transverse section photomicrographs showing a microstructure constituted by martensite through the wall thickness of the pipe end section of quenched material for Nital 2% in 300X magnification.
Figure 15 shows transverse . section photomicrographs showing a microstructure constituted by tempered martensite through the thickness of the pipe body section of quenched and tempered material. for Nital 2% in 300X magnification.
Figure 16 shows transverse section photomicrographs showing a microstructure constituted by tempered martensite through the thickness of the pipe end section of quenched and tempered material for Nital 2% in 300X magnification.
BRIEF SUMMARY OF THE INVENTION
The present invention describes a seamless steel tube to be used as a riser in work-over operations with a specific chemistry design and microstructure consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter. The alloy design is based on high strength requirements. The main features of the chemical composition of the tube include 0.23-0.28 wt % C, 0.45 -0.65 wt % Mn, and other alloying elements such as Mo, and Cr to achieve the required percentage of martensitic transformation. In addition, microalloying elements such as Ti and Nb are used as grain refiners. Low content of residual elements such as S and residual elements such as Cu and P are used to avoid any corrosion problem related to inclusions promotion and segregation at grain boundaries which decrease the corrosion performance, the hydrogen content was kept below 2.4 ppm to avoid any problem related to hydrogen entrapment and decrease of the corrosion performance.
The production route for manufacturing the upset seamless pipe for the application of as Work Over Riser, includes the following steps: steel casting (Continuous Cast Bar), seamless pipe rolling (MPM process), pipe ends upsetting, heat treatment, destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC testing), dimensional control of pipe body and upset ends (outside diameter, out of roundness, excentricity, straightness, internal diameter, length), machining of external and internal upset end, dimensional control (internal diameter, outside diameter and machined length), drift testing at the upset ends, non-destructive testing (NDT) of upset ends, weighing, measuring and marking, external surface visual inspection, UT
inspection of pipe body and UT inspection of upset ends (cylindrical section only).
The production route for manufacturing the machining seamless pipe for the application of as Work Over Riser includes the following steps: steel casting (Continuous Cast Bar), seamless pipe rolling (MPM process), heat treatment, destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC testing), dimensional control of pipe body (outside diameter, out of roundness, straightness, internal diameter, length), machining from external surface the complete length of the pipe by programming CNC lath machine in order to achieve final dimensions at the ends, dimensional control (internal diameter, outside diameter, out of roundness, straightness, and length) of pipe body and machined ends, drift testing at the ends, non-destructive testing (NDT) of ends, weighing, measuring and marking, external surface visual inspection, UT inspection of machined pipe body and UT
inspection of ends (cylindrical section only).
The combination of chemical composition and tight control of heat treatment parameters allows achieving the adequate microstructure after quench and temper in order to achieve the mechanical properties and pass the SSC Method A tests requirements described above.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
OF THE INVENTION
The chemical composition of the seamless steel tube of the present invention comprises in weight per cent: carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities.
A more preferred composition comprises: carbon 0.25-0.28, manganese 0.48-0.58, silicon 0.20-0.30, chromium 1.05-1.15, molybdenum 0.80- 0.83, nickel 0.10 max, nitrogen 0.008 max, boron 0.0016-0.0026, aluminum 0.015-0.045, sulfur 0.0030 max, phosphorus 0.010 max, titanium 0.016-0.026, niobium 0.025-0.030, copper 0.10 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.015 max, hydrogen 2.0 ppm max, the rest are iron and inevitable impurities.
The seamless steel tubes have a geometry, in which ends of tubes have an increased wall thickness and outer diameter, and following mechanical properties:
In the as-quench condition 90% of martensitic transformation when evaluated according to the following formulae: HRCmin = (58 x %C) + 27 Austenitic grain size as per ASTM minimum 5 or finer In the as-quench and temper condition Longitudinal Tensile Test (round standard specimens when wall thickness equal or above 1" and longitudinal strip specimens when wall thickness below 1").
Minimum Yield Strength: 90ksi (620 MPa) Maximum Yield Strength: 105ksi (724 MPa) Minimum Ultimate Tensile Strength: lOOksi (690 MPa) Minimum Elongation (L = 4D): 18%
Yield to Tensile Ratio < 0.92 Transverse Charpy Test (using 10x10 mm specimen) Minimum individual Absorbed Energy: 30 Joules Minimum Average Absorbed Energy: 40 Joules Maximum Hardness value: 25.4 Hrc (value as per API 5CT
means average per row) Microcleanliness acceptance criteria as per ASTM E-45 A:
A, B, C, D all below 2 Compliance with NACE, acceptance criteria: Passing SSC
Method A test as per NACE TM0177-2005, using test solution (A), testing at 85%SMYS, test period 720 hours.
The geometry of seamless steel tube of the present invention and the mechanical characteristics are obtained by two methods of manufacturing: upsetting and machining.
The upsetting manufacturing method comprises the following steps:
(a) providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities, obtained by rolling process (MPM process) (b) upsetting of tube ends;
(c) austenitizing between 850-930 C the full length of the tube; and (d) quenching and tempering between 630-720 C
(e) destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, according to the formulae HRCmin _(58 x %C) + 27 , tensile, hardness, toughness, SSC testing) (f) dimensional control of pipe body and upset ends (outside diameter, out of roundness, eccentricity, straightness, internal diameter, length) (g) machining of external and internal upset end (h) dimensional control (internal diameter, outside diameter and machined end) (i) drift testing at the upset ends (j) non-destructive testing of upset ends, weighing, measuring and marking, external surface visual inspection, UT inspection of pipe body and UT
inspection of upset ends.
The machining manufacturing method comprises the following steps:
(a) providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities, obtained by rolling process (MPM process (b) heat treatment o pipes (austenitizing between 850-930 C the full length of the tube; and quenching and tempering between 630-720 C) (c) destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation according to the formulae , tensile, hardness, toughness, SSC testing) (d) dimensional control of pipe body (OD, out of roundness, straightness, ID, length) (e) machining from external surface the complete length of the pipe by programming CNC lath machine in order to achieve final dimensions at the ends, (f) dimensional control (ID, OD, out of roundness, straightness and length) of pipe body and machined ends (g) drift testing at the ends, (h) non destructive testing (NDT) of ends, weighing, measuring and marking, external surface visual inspection, UT inspection of machined pipe body and UT inspection of machined ends (cylindrical section only).
Both methods are also performed providing a seamless steel pipe with the preferred composition, as disclosed above.
The seamless steel tube of the present invention may be divided into two zones. As shown in Figure 1, there is an increased wall thickness and diameter end with internal and external length (upsetting or machined zone) and the tube body.
Due to a combination of the manufacturing methods and the chemistry design, both the whole tube body and the ends have the same yield strength of at least 620 MPa (90 ksi) (YS) and at most 724 MPa (105 ksi), a Yield to Tensile Ratio not greater than 0.92, also, the same ultimate tensile strength (UTS) of at least 690 MPa (100 ksi), elongation of at least 18%, hardness Rockwell of at most 25.4 HRC (value as per API 5CT means average per row) and corrosion resistance (Compliance with NACE, acceptance criteria: Passing SSC Method A test as per NACE
TM0177-2005, using test solution (a), testing at 85%SMYS, test period 720 hours). Prior Austenitic Grain Size is 5 or less. The product after the quench heat treatment process shall comply with Prior Austenitic Grain Size (PAGS) is 5 or less a microstructure of at least 90% martensite in the as-quench condition.
The tubes may be utilized in sour and non-sour service.
The tubes' nominal diameter to be upsetted ends may be from 4'/z" to 10 W.
The tubes' nominal diameter which ends will to be machined may be from 4'/z" to 18" due to the manufacturing facilities.
The tubes' thickness ranges from 10 mm to 50 mm.
Examples Example 1 Two industrial development trials for two dimensions of tubes (8 5/8" ODx15.9 mm WT and 7" OD x 17.5 mm WT) were carried on. The chemistry design is shown in Table 1 and the desired ranges of mechanical properties are shown in Table 2.
Table 1 Element Minimum Maximum C 0.25 0.28 Mn 0.48 0.58 Si 0.20 0.30 P 0 0.010 S 0 0.0030 Mo 0.80 0.83 Cr 1.05 1.15 Nb 0.025 0.030 Ni 0 0.10 Cu 0 0.10 Sn 0 0.015 Al 0.015 0.045 Ti 0.016 0.026 As 0 0.020 Ca 0 0.0040 B 0.0016 0.0026 N 0 0.008 H 0 2.0 Table 2 Property Min Max Yield Strength EUL 0.5% (MPa) 620 724 Ultimate Tensile Strength (MPa) 690 n/a Yield to Tensile Ratio (Y/T) 0.92 Elongation (%) (L=4D) 18 -Individual Absorbed Energy At -20 C (J) 30 -Average Absorbed Energy At -20 C (J) 40 -Hardness Rockwell HRC-value (tempered n/a 25.4*
condition) Microcleanliness (acceptance criteria as - 2 per ASTM E-45A: A, B, C, D) Corrosion Test Solution period NACE TM0177-2005 SSC Method A- 85% 720 hrs. A
SMYS
*API 5CT: value= average per row The upsetting manufacturing operation was performed following the steps of:
a) The pipe ends in the as-rolled condition were heated up to the appropriate forging temperature heating the calculated pipe length. The upsetting operation takes place at a minimum temperature of 1000 C.
b) Once the heating cycle was accomplished, pipe ends were upset with the appropriate die and tooling design for each particular dimension.
C) Inspection was then made on pipes' external and internal surfaces after each strike/punch in order to find any possible defect generated by the upsetting operation.
Special care was taken into consideration when designing the heating curve to be use during the heat treatment process in the austenitizing furnace (860-940 C) and the tempering furnace (640-720 C) for the upset ends of the 8 5/8"OD product. After austenitizing heat treatment process, the pipe must enter the quenching process above AC3 to guaranteed through-wall transformation. Then, for the 7"OD product, a few heat treatment adjustments were made on the heating curves based on the results obtained from the other dimension 8 5/8" OD pipe.
The actual temperatures from the pipe body and upset ends outer surface were carefully measured throughout the trial stages right at the entrance of the pipes into the quenching head by using a manual pyrometer in addition to the furnace pyrometers.
After the heat treatments, a mechanical characterization was performed. From the as-quenched material, the % of martensitic transformation was calculated. Tensile, hardness, and toughness tests were performed on the quenched and tempered material on both upset and pipe body sections. Specifications were met; good hardenability, yield strength values of over 92 ksi as-tempered HRC values below the maximum allowed (25.4 HRC) and absorbed energy higher than 100 Joules at the specified temperature of -20 C.
Extensive destructive characterization and corrosion SSC
Method A (NACE Standard Tensile Test, TM0177-96) were also conducted.
Homogeneity in tensile properties, hardness and toughness test results are a consequence of a very homogenous microstructure through the wall on both upset end and pipe body in the as quenched and tempered condition. Figures 2 through 5 illustrate several graphical representations of the mechanical properties including hardness.
The austenitic grain size was measured on as-quenched material by the saturation method as per ASTM E-112. As shown in Figure 6, the grain size reported on the samples were 9/10 in the pipe body which was above the required size since the minimum required was 5. The upset samples showed a grain size of 8/9 and 9/10 complying with the specifications as illustrated in Figure 6.
The transversal face to the rolling axis was metallographically prepared and etched with Nital 2% to perform microstructural observations with an optical microscope. (Nital:
Solution of 2% of Nitric acid in Ethyl Alcohol).
In the as-quenched samples, a martensitic microstructure was observed on OD, ID and MW sections through the thickness achieving a martensitic transformation of over 90% measured from the HRC hardness values as shown in Figures 8 and 9.
In the as-quench and tempered material, a microstructure constituted by tempered martensite was observed through the thickness as shown in Figures 10 and 11.
The microstructures observed in as-quenched material were mainly martensitic with over 95% of martensitic transformation through the entire thickness of the pipe on both pipe body and upset which indicates that the temperature at which the pipe entered the quenching stage and the quenching itself were homogeneous. On the other hand, the microstructures observed in tempered material, tempered martensite was present through the thickness.
The material passed the SSC Method A test at 85%SMYS
as per NACE TM0177-96 accomplishing the 720 hours.
Corrosion Testing Results as per NACE Method A
NACE TM-0177-96 Method A
Initial Final Stress Sample Location Heat Specimen Diameter Initial PH Diameter Final PH Applied Result SMYS %
98449 Upset 19874 A 6,39 2,69 6,21 3,64 85 NF*
98449 Upset 19874 B 6,42 2,69 6,33 3,62 85 NF*
98449 Upset 19874 C 6,4 2,69 6,29 3,69 85 NF*
8448 Pipe Body 19874 A 6,36 2,66 6,24 3,53 85 NF*
8448 Pipe Body 19874 B 6,41 2,66 6,31 3,51 85 NF*
8448 Pipe Body 19874 C 6,4 2,66 6,29 3,52 85 NF*
98448 Upset 19874 A 6,37 2,66 6,22 3,5 85 NF*
98448 Upset 19874 B 6,37 2,66 6,2 3,5 85 NF*
98448 Upset 19874 C 6,4 2,66 6,33 3,49 85 NF*
*NF: Not failed Example 2 An industrial development trial for a dimension of tube (8.26" OD x 44 mm WT and 9.97" OD x 41 mm WT) were carried on. The chemistry design is shown in Table 1 and the desired ranges of mechanical properties are shown in Table 2 of Example 1.
The pipe was rolled in a heavy wall condition. The wall thickness was about 44 mm.
After rolling, heat treatment is performed. Similar considerations about this step were made such as in Example 1 to obtain through wall transformation.
After heat treatment of pipes, detail mechanical characterization was performed such as in Example 1.
Dimensional control of the outside diameter (OD), out of roundness, inside diameter (ID) and length of pipes was carried on followed by the UT inspection.
In order to achieve final dimensions, the complete length of pipe body was machined from external surface by programming CNC lath machine.
Once again, a dimensional control of pipes after machining was carried out.
For quality purposes, non destructive inspection of straight pipe body section using automatic UT and manual for the cylindrical ends.
As in Example 1, a mechanical characterization was performed, calculating the % of martensitic transformation from the as-quenched material. On the quenched and tempered material, tensile, hardness, and toughness tests were performed on both machined ends and pipe body sections. Specifications were met; good hardenability, yield strength values of over 94 ksi as-tempered HRC values below the maximum allowed (25.4 HRC) and absorbed energy higher than 100 Joules at the specified temperature of -20 C.
Extensive destructive characterization and corrosion SSC
Method A (NACE Standard Tensile Test, TM0177-96) were also conducted.
Homogeneity in tensile properties, hardness and toughness test results are a consequence of a very homogenous microstructure through the wall on both machined ends and pipe body in the as quenched and tempered condition.
Microstructural observations of as-quenched material at the pipe machined body and the ends zones reveal a prior austenitic grain size of 8/9 in both zones measured by the saturation method as per ASTM E-112. The modified end on the analyzed sample showed a grain size of 8/9 complying with the specifications as shown in Figure 12.
The transversal face to the rolling axis was metallographically prepared and etched with Nital 2% to perform microstructural observations with an optical microscope. (Nital:
Solution of 2% of Nitric acid in Ethyl Alcohol).
In the as-quenched sample, a martensitic microstructure was observed on OD, ID and MW sections through the thickness achieving a martensitic transformation of over 90% measured from the HRC hardness values as shown in Figures 13 and 14.
In the as-quench and tempered material, a microstructure constituted by tempered martensite was observed through the thickness as shown in Figures 15 and 16.
The material passed the SSC method A test at 85%SMYS
as per NACE TM0177-2005 accomplishing the 720 hours.
Claims (9)
1.- A seamless steel tube for work-over risers comprising in weight per cent, carbon 0.25-0.28, manganese 0.48-0.58, silicon 0.20-0.30, chromium 1.05-1.15, molybdenum 0.80- 0.83, nickel 0.10 max, nitrogen 0..008 -max, boron 0.0016-0.0026, aluminum 0.015-0.045, sulfur 0.0030 max, phosphorus 0.010 max, titanium 0.016-0.026, niobium 0.025-0.030, copper 0.10 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.015 max, hydrogen 2.0 ppm max, the rest are iron and inevitable impurities consisting of a geometry in which ends of the tube have an increased wall thickness and outer diameter and having a yield strength of at least 620 MPa (90 ksi) throughout the whole length of a tube body and in tube ends.
2.- A seamless steel tube for work-over risers according to claim 1 wherein the following mechanical properties in the as-quench condition 90% of martensitic transformation when evaluated according to the following formulae: HRCmin = (58 x %C) + 27, austenitic grain size as per ASTM minimum 5 or finer in the as-quench and temper condition, longitudinal Tensile Test (round standard specimens when wall thickness equal or above 1" and longitudinal strip specimens when wall thickness below 1"), at least Yield Strength of 620 MPa (90ksi), Maximum, Yield Strength of 724 MPa (105ksi), Minimum Ultimate Tensile Strength,690 MPa (100 ksi), Minimum Elongation (L = 4D), 18%, Yield to Tensile Ratio <= 0.92, Transverse Charpy Test, Minimum individual Absorbed Energy: 30 Joules, Minimum Average Absorbed Energy: 40 Joules, Maximum Hardness value, 25.4 HRC (value as per API 5CT means average per row), Microcleanliness acceptance criteria as per ASTM, E-45 A: A, B, C, D all below 2, Passing SSC Method A test as per NACE
TM0177-2005, using test solution (A), testing at 85%SMYS, test period 720 hours, throughout the whole length of a tube body and in tube ends.
TM0177-2005, using test solution (A), testing at 85%SMYS, test period 720 hours, throughout the whole length of a tube body and in tube ends.
3.- A seamless steel tube for work-over risers according to claim I wherein the following mechanical properties in the as-quench condition at least 90% of martensitic transformation when evaluated according to the following formulae: HRCmin = (58 x %C) + 27, austenitic grain size as per ASTM minimum 5 or finer in the as-quench and temper condition, longitudinal Tensile Test (round standard specimens when wall thickness equal or above 1" and longitudinal strip specimens when wall thickness below 1"), at least a Yield Strength of -620 MPa (90ksi), a Maximum Yield Strength of 724 MPa (105ksi), a Minimum Ultimate Tensile Strength,690- MPa (100 ksi), a Minimum Elongation (L = 4D), 18%, Yield to Tensile Ratio <= 0.92, Transverse Charpy Test, Minimum , individual Absorbed Energy: 30 Joules, Minimum Average Absorbed Energy: 40 Joules, Maximum Hardness value, 25.4 HRC (value as per API 5CT means average per row), Microcleanliness acceptance criteria as per ASTM E-45 A: A, B, C, D all below 2, Passing SSC Method A test as per NACE
TM0177-2005, using test solution (A), testing at 85%SMYS, test period 720 hours, throughout the whole length of a tube body and in tube ends.
TM0177-2005, using test solution (A), testing at 85%SMYS, test period 720 hours, throughout the whole length of a tube body and in tube ends.
4.- A method for manufacturing a seamless steel tube for work-over risers having a yield strength at least of 620 MPa (90ksi) both in a tube body and in tube ends comprising the following steps of:
(a)providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities;
(b)upsetting of tube ends;
(c)austenitizing between 850-930°C the full length of the tube;
and (d)quenching and tempering between 630-720°C
(a)providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.020 max, calcium 0.0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities;
(b)upsetting of tube ends;
(c)austenitizing between 850-930°C the full length of the tube;
and (d)quenching and tempering between 630-720°C
5.- A method for manufacturing a seamless steel tube for, work-over risers according to claim 4 further comprising the following steps:
(e)destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC testing) (f) dimensional control of pipe body and upset ends (outside diameter, out of roundness, eccentricity, straightness, internal diameter, length) (g)machining of external and internal upset end (h)dimensional control (internal diameter, outside diameter and machined end) (i) drift testing at the upset ends (j) non-destructive testing of upset ends, weighing, measuring and marking, external surface visual inspection, UT
inspection of pipe body and UT inspection of upset ends.
(e)destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC testing) (f) dimensional control of pipe body and upset ends (outside diameter, out of roundness, eccentricity, straightness, internal diameter, length) (g)machining of external and internal upset end (h)dimensional control (internal diameter, outside diameter and machined end) (i) drift testing at the upset ends (j) non-destructive testing of upset ends, weighing, measuring and marking, external surface visual inspection, UT
inspection of pipe body and UT inspection of upset ends.
6.- A method for manufacturing a seamless steel tube for work-over risers -having a yield strength at least of 620- MPa (90ksi) both in a tube body and in tube ends comprising the following steps of:
(i) providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.Ø20, calcium 0..0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities, obtained by rolling process (MPM process (j) heat treatment o pipes (austenitizing between 850-930°C the full length of the tube; and quenching and tempering between 630-720°C) (k) destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC
testing) (l) dimensional control of pipe body (OD, out of roundness, straightness, ID, length) (m) machining from external surface the complete length of the pipe by programming CNC lath machine in order to achieve final dimensions at the ends.
(i) providing a steel tube containing a composition in weight per cent, carbon 0.23-0.29, manganese 0.45-0.65, silicon 0.15-0.35, chromium 0.90-1.20, molybdenum 0.70- 0.90, nickel 0.20 max, nitrogen 0.010 max, boron 0.0010-0.0030, aluminum 0.010-0.045, sulfur 0.005 max, phosphorus 0.015 max, titanium 0.005-0.030, niobium 0.020-0.035, copper 0.15 max, arsenic 0.Ø20, calcium 0..0040 max, tin 0.020 max, hydrogen 2.4 ppm max, the rest are iron and inevitable impurities, obtained by rolling process (MPM process (j) heat treatment o pipes (austenitizing between 850-930°C the full length of the tube; and quenching and tempering between 630-720°C) (k) destructive testing (including microcleanliness, austenitic grain size, calculate % of martensitic transformation, tensile, hardness, toughness, SSC
testing) (l) dimensional control of pipe body (OD, out of roundness, straightness, ID, length) (m) machining from external surface the complete length of the pipe by programming CNC lath machine in order to achieve final dimensions at the ends.
7.- A method for manufacturing a seamless steel tube for work-over risers according to claim 6, further comprising the following steps:
(n) dimensional control (ID, OD, out of roundness, straightness and length) of pipe body and machined ends (o) drift testing at the ends, (p) non destructive testing (NDT) of ends, weighing, measuring and marking, external surface visual inspection, UT inspection of machined pipe body and UT inspection of machined ends (cylindrical section only).
(n) dimensional control (ID, OD, out of roundness, straightness and length) of pipe body and machined ends (o) drift testing at the ends, (p) non destructive testing (NDT) of ends, weighing, measuring and marking, external surface visual inspection, UT inspection of machined pipe body and UT inspection of machined ends (cylindrical section only).
8.- A seamless steel tube for work-over riser according to claim 1, wherein the as-quenched and tempered material has a microstructure constituted by tempered martensite through the thickness, throughout the whole length of a tube body and in tube ends.
9.- A seamless steel tube for work-over riser according to claim 1,-wherein the -as-quenched and tempered material has a microstructure constituted by tempered martensite through the thickness, throughout the Whole length of a tube body and in tube ends.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| MXMX/A/2007/004600 | 2007-04-17 | ||
| MX2007004600A MX2007004600A (en) | 2007-04-17 | 2007-04-17 | Seamless steel pipe for use as vertical work-over sections. |
| PCT/MX2008/000054 WO2008127084A2 (en) | 2007-04-17 | 2008-04-17 | A seamless steel tube for work-over riser and method of manufacturing |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2682959A1 true CA2682959A1 (en) | 2008-10-23 |
Family
ID=39673395
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002682959A Abandoned CA2682959A1 (en) | 2007-04-17 | 2008-04-17 | A seamless steel tube for the application as work-over riser |
Country Status (8)
| Country | Link |
|---|---|
| US (1) | US20100193085A1 (en) |
| EP (1) | EP2143817A2 (en) |
| AR (1) | AR066080A1 (en) |
| BR (1) | BRPI0810005A2 (en) |
| CA (1) | CA2682959A1 (en) |
| MX (1) | MX2007004600A (en) |
| NO (1) | NO20093069L (en) |
| WO (1) | WO2008127084A2 (en) |
Families Citing this family (32)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| BR0318308B1 (en) | 2003-04-25 | 2011-12-13 | Seamless steel pipe and process for its manufacture. | |
| MXPA05008339A (en) | 2005-08-04 | 2007-02-05 | Tenaris Connections Ag | High-strength steel for seamless, weldable steel pipes. |
| CN101506392B (en) | 2006-06-29 | 2011-01-26 | 特纳瑞斯连接股份公司 | Seamless precision steel pipe with enhanced isotropic stiffness at low temperature for hydraulic cylinder and its manufacturing process |
| EP2181240B1 (en) * | 2007-07-02 | 2018-08-29 | Forum US, Inc. | Centering structure for tubular member and method of making same |
| US7862667B2 (en) | 2007-07-06 | 2011-01-04 | Tenaris Connections Limited | Steels for sour service environments |
| US8328960B2 (en) | 2007-11-19 | 2012-12-11 | Tenaris Connections Limited | High strength bainitic steel for OCTG applications |
| MX2009012811A (en) * | 2008-11-25 | 2010-05-26 | 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 |
| EP2325435B2 (en) | 2009-11-24 | 2020-09-30 | Tenaris Connections B.V. | Threaded joint sealed to [ultra high] internal and external pressures |
| US9163296B2 (en) | 2011-01-25 | 2015-10-20 | Tenaris Coiled Tubes, Llc | Coiled tube with varying mechanical properties for superior performance and methods to produce the same by a continuous heat treatment |
| IT1403688B1 (en) | 2011-02-07 | 2013-10-31 | Dalmine Spa | STEEL TUBES WITH THICK WALLS WITH EXCELLENT LOW TEMPERATURE HARDNESS AND RESISTANCE TO CORROSION UNDER TENSIONING FROM SULFUR. |
| IT1403689B1 (en) | 2011-02-07 | 2013-10-31 | Dalmine Spa | HIGH-RESISTANCE STEEL TUBES WITH EXCELLENT LOW TEMPERATURE HARDNESS AND RESISTANCE TO CORROSION UNDER VOLTAGE SENSORS. |
| US8414715B2 (en) | 2011-02-18 | 2013-04-09 | Siderca S.A.I.C. | Method of making ultra 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 |
| RU2464327C1 (en) * | 2011-07-27 | 2012-10-20 | ООО "Компания ИжТехМаш" | Manufacturing method of pipes for process needs of oil wells |
| 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 |
| JP5408389B1 (en) * | 2012-04-27 | 2014-02-05 | 新日鐵住金株式会社 | Seamless steel pipe and manufacturing method thereof |
| RU2500821C1 (en) * | 2012-08-20 | 2013-12-10 | Кирилл Алексеевич Иванов | Thermomechanical pipe treatment method |
| GB2525337B (en) | 2013-01-11 | 2016-06-22 | Tenaris Connections Ltd | 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 |
| 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 |
| EP2789701A1 (en) | 2013-04-08 | 2014-10-15 | DALMINE S.p.A. | High strength medium wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes |
| EP2789700A1 (en) | 2013-04-08 | 2014-10-15 | DALMINE S.p.A. | Heavy wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes |
| KR102197204B1 (en) | 2013-06-25 | 2021-01-04 | 테나리스 커넥션즈 비.브이. | High-chromium heat-resistant steel |
| US20160305192A1 (en) | 2015-04-14 | 2016-10-20 | Tenaris Connections Limited | Ultra-fine grained steels having corrosion-fatigue resistance |
| US11085277B2 (en) * | 2015-10-07 | 2021-08-10 | Benteler Steel/Tube Gmbh | Seamless steel pipe, method of producing a high strength seamless steel pipe, usage of a seamless steel pipe and perforation gun |
| JP6152928B1 (en) * | 2016-02-29 | 2017-06-28 | Ｊｆｅスチール株式会社 | Low alloy high strength seamless steel pipe for oil wells |
| NZ744590A (en) | 2016-02-29 | 2019-04-26 | Jfe Steel Corp | Low alloy high strength seamless steel pipe for oil country tubular goods |
| US11124852B2 (en) | 2016-08-12 | 2021-09-21 | Tenaris Coiled Tubes, Llc | Method and system for manufacturing coiled tubing |
| US10434554B2 (en) | 2017-01-17 | 2019-10-08 | Forum Us, Inc. | Method of manufacturing a coiled tubing string |
| WO2019023536A1 (en) * | 2017-07-27 | 2019-01-31 | Enventure Global Technology, Inc. | Upset expandable connection |
| CN109161650B (en) * | 2018-10-30 | 2020-07-28 | 中车戚墅堰机车车辆工艺研究所有限公司 | Low-alloy cast steel, manufacturing method and application thereof |
Family Cites Families (65)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3413166A (en) * | 1965-10-15 | 1968-11-26 | Atomic Energy Commission Usa | Fine grained steel and process for preparation thereof |
| US3655465A (en) * | 1969-03-10 | 1972-04-11 | Int Nickel Co | Heat treatment for alloys particularly steels to be used in sour well service |
| DE2131318C3 (en) * | 1971-06-24 | 1973-12-06 | Fried. Krupp Huettenwerke Ag, 4630 Bochum | Process for the production of a reinforcement steel bar for prestressed concrete |
| US3915697A (en) * | 1975-01-31 | 1975-10-28 | Centro Speriment Metallurg | Bainitic steel resistant to hydrogen embrittlement |
| FR2424324B1 (en) * | 1978-04-28 | 1986-02-28 | Neturen Co Ltd | STEEL FOR COLD PLASTIC SHAPING AND HEAT TREATMENT PROMOTING THIS DEFORMATION |
| US4231555A (en) * | 1978-06-12 | 1980-11-04 | Horikiri Spring Manufacturing Co., Ltd. | Bar-shaped torsion spring |
| EP0021349B1 (en) * | 1979-06-29 | 1985-04-17 | Nippon Steel Corporation | High tensile steel and process for producing the same |
| US4281716A (en) | 1979-08-13 | 1981-08-04 | Standard Oil Company (Indiana) | Flexible workover riser system |
| JPS5680367A (en) * | 1979-12-06 | 1981-07-01 | Nippon Steel Corp | Restraining method of cracking in b-containing steel continuous casting ingot |
| US4376528A (en) * | 1980-11-14 | 1983-03-15 | Kawasaki Steel Corporation | Steel pipe hardening apparatus |
| JPS58188532A (en) * | 1982-04-28 | 1983-11-04 | Nhk Spring Co Ltd | Manufacture of hollow stabilizer |
| JPS61130462A (en) * | 1984-11-28 | 1986-06-18 | Tech Res & Dev Inst Of Japan Def Agency | High-touchness extra high tension steel having superior stress corrosion cracking resistance as well as yield stress of 110kgf/mm2 and above |
| DE3666461D1 (en) * | 1985-06-10 | 1989-11-23 | Hoesch Ag | Method and use of a steel for manufacturing steel pipes with a high resistance to acid gases |
| US4812182A (en) * | 1987-07-31 | 1989-03-14 | Hongsheng Fang | Air-cooling low-carbon bainitic steel |
| US5538566A (en) * | 1990-10-24 | 1996-07-23 | Consolidated Metal Products, Inc. | Warm forming high strength steel parts |
| IT1263251B (en) * | 1992-10-27 | 1996-08-05 | Sviluppo Materiali Spa | PROCEDURE FOR THE PRODUCTION OF SUPER-DUPLEX STAINLESS STEEL PRODUCTS. |
| US5454883A (en) * | 1993-02-02 | 1995-10-03 | Nippon Steel Corporation | High toughness low yield ratio, high fatigue strength steel plate and process of producing same |
| JPH07266837A (en) * | 1994-03-29 | 1995-10-17 | Horikiri Bane Seisakusho:Kk | Hollow stabilizer manufacturing method |
| IT1267243B1 (en) * | 1994-05-30 | 1997-01-28 | Danieli Off Mecc | CONTINUOUS CASTING PROCEDURE FOR PERITECTIC STEELS |
| GB2297094B (en) * | 1995-01-20 | 1998-09-23 | British Steel Plc | Improvements in and relating to Carbide-Free Bainitic Steels |
| JP3755163B2 (en) * | 1995-05-15 | 2006-03-15 | 住友金属工業株式会社 | Manufacturing method of high-strength seamless steel pipe with excellent resistance to sulfide stress cracking |
| IT1275287B (en) * | 1995-05-31 | 1997-08-05 | Dalmine Spa | SUPERMARTENSITIC STAINLESS STEEL WITH HIGH MECHANICAL AND CORROSION RESISTANCE AND RELATED MANUFACTURED PRODUCTS |
| GB9621195D0 (en) | 1996-10-11 | 1996-11-27 | Kvaerner Eng | Off-shore oil or gas production unit |
| WO1998031843A1 (en) * | 1997-01-15 | 1998-07-23 | Mannesmann Ag | Method for making seamless tubing with a stable elastic limit at high application temperatures |
| CA2231985C (en) * | 1997-03-26 | 2004-05-25 | Sumitomo Metal Industries, Ltd. | Welded high-strength steel structures and methods of manufacturing the same |
| ATE250518T1 (en) * | 1997-05-12 | 2003-10-15 | Muhr & Bender | STABILIZER |
| US5993570A (en) * | 1997-06-20 | 1999-11-30 | American Cast Iron Pipe Company | Linepipe and structural steel produced by high speed continuous casting |
| DE19725434C2 (en) * | 1997-06-16 | 1999-08-19 | Schloemann Siemag Ag | Process for rolling hot wide strip in a CSP plant |
| JP3262807B2 (en) * | 1997-09-29 | 2002-03-04 | 住友金属工業株式会社 | Oil well pipe steel and seamless oil well pipe with excellent resistance to wet carbon dioxide gas and seawater corrosion |
| JP3562353B2 (en) * | 1998-12-09 | 2004-09-08 | 住友金属工業株式会社 | Oil well steel excellent in sulfide stress corrosion cracking resistance and method for producing the same |
| JP4331300B2 (en) * | 1999-02-15 | 2009-09-16 | 日本発條株式会社 | Method for manufacturing hollow stabilizer |
| DE60134125D1 (en) * | 2000-02-28 | 2008-07-03 | Nippon Steel Corp | STEEL TUBE WITH EXCELLENT FORMABILITY AND MANUFACTURING METHOD THEREFOR |
| US6384388B1 (en) * | 2000-11-17 | 2002-05-07 | Meritor Suspension Systems Company | Method of enhancing the bending process of a stabilizer bar |
| CN1232672C (en) * | 2001-02-07 | 2005-12-21 | 杰富意钢铁株式会社 | Sheet steel and method for producing thereof |
| ES2295312T3 (en) * | 2001-03-07 | 2008-04-16 | Nippon Steel Corporation | STEEL PIPE WELDED WITH ELECTRICITY FOR HOLLOW STABILIZER. |
| AR027650A1 (en) * | 2001-03-13 | 2003-04-09 | Siderca Sa Ind & Com | LOW-ALLOY CARBON STEEL FOR THE MANUFACTURE OF PIPES FOR EXPLORATION AND PRODUCTION OF PETROLEUM AND / OR NATURAL GAS, WITH IMPROVED LACORROSION RESISTANCE, PROCEDURE FOR MANUFACTURING SEAMLESS PIPES AND SEWLESS TUBES OBTAINED |
| EP1375683B1 (en) * | 2001-03-29 | 2012-02-08 | Sumitomo Metal Industries, Ltd. | High strength steel tube for air bag and method for production thereof |
| JP2003041341A (en) * | 2001-08-02 | 2003-02-13 | Sumitomo Metal Ind Ltd | Steel material having high toughness and method for manufacturing steel pipe using the same |
| US6669789B1 (en) * | 2001-08-31 | 2003-12-30 | Nucor Corporation | Method for producing titanium-bearing microalloyed high-strength low-alloy steel |
| NO315284B1 (en) * | 2001-10-19 | 2003-08-11 | Inocean As | Riser pipe for connection between a vessel and a point on the seabed |
| DE10160942A1 (en) * | 2001-12-12 | 2003-06-18 | Daimler Chrysler Ag | Built valve for reciprocating engines |
| EP1496131B1 (en) * | 2002-03-29 | 2008-08-20 | Sumitomo Metal Industries, Ltd. | Low alloy steel |
| US6669285B1 (en) * | 2002-07-02 | 2003-12-30 | Eric Park | Headrest mounted video display |
| US7074286B2 (en) * | 2002-12-18 | 2006-07-11 | Ut-Battelle, Llc | Wrought Cr—W—V bainitic/ferritic steel compositions |
| US7010950B2 (en) * | 2003-01-17 | 2006-03-14 | Visteon Global Technologies, Inc. | Suspension component having localized material strengthening |
| BR0318308B1 (en) * | 2003-04-25 | 2011-12-13 | Seamless steel pipe and process for its manufacture. | |
| US20050087269A1 (en) * | 2003-10-22 | 2005-04-28 | Merwin Matthew J. | Method for producing line pipe |
| EP1728877B9 (en) * | 2004-03-24 | 2012-02-01 | Sumitomo Metal Industries, Ltd. | Process for producing low-alloy steel excelling in corrosion resistance |
| JP4140556B2 (en) * | 2004-06-14 | 2008-08-27 | 住友金属工業株式会社 | Low alloy steel for oil well pipes with excellent resistance to sulfide stress cracking |
| JP4135691B2 (en) * | 2004-07-20 | 2008-08-20 | 住友金属工業株式会社 | Nitride inclusion control steel |
| JP2006037147A (en) * | 2004-07-26 | 2006-02-09 | Sumitomo Metal Ind Ltd | Oil well pipe steel |
| US20060169368A1 (en) * | 2004-10-05 | 2006-08-03 | Tenaris Conncections A.G. (A Liechtenstein Corporation) | Low carbon alloy steel tube having ultra high strength and excellent toughness at low temperature and method of manufacturing the same |
| US7566416B2 (en) * | 2004-10-29 | 2009-07-28 | Sumitomo Metal Industries, Ltd. | Steel pipe for an airbag inflator and a process for its manufacture |
| JP4792778B2 (en) * | 2005-03-29 | 2011-10-12 | 住友金属工業株式会社 | Manufacturing method of thick-walled seamless steel pipe for line pipe |
| US20060243355A1 (en) * | 2005-04-29 | 2006-11-02 | Meritor Suspension System Company, U.S. | Stabilizer bar |
| MXPA05008339A (en) * | 2005-08-04 | 2007-02-05 | Tenaris Connections Ag | High-strength steel for seamless, weldable steel pipes. |
| CA2620054C (en) * | 2005-08-22 | 2012-03-06 | Sumitomo Metal Industries, Ltd. | Seamless steel pipe for line pipe and a process for its manufacture |
| US7744708B2 (en) * | 2006-03-14 | 2010-06-29 | Tenaris Connections Limited | Methods of producing high-strength metal tubular bars possessing improved cold formability |
| CN101506392B (en) * | 2006-06-29 | 2011-01-26 | 特纳瑞斯连接股份公司 | Seamless precision steel pipe with enhanced isotropic stiffness at low temperature for hydraulic cylinder and its manufacturing process |
| US8322754B2 (en) * | 2006-12-01 | 2012-12-04 | Tenaris Connections Limited | Nanocomposite coatings for threaded connections |
| US20080226396A1 (en) * | 2007-03-15 | 2008-09-18 | Tubos De Acero De Mexico S.A. | Seamless steel tube for use as a steel catenary riser in the touch down zone |
| US7862667B2 (en) * | 2007-07-06 | 2011-01-04 | Tenaris Connections Limited | Steels for sour service environments |
| US8328960B2 (en) * | 2007-11-19 | 2012-12-11 | Tenaris Connections Limited | High strength bainitic steel for OCTG applications |
| MX2009012811A (en) * | 2008-11-25 | 2010-05-26 | 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 |
-
2007
- 2007-04-17 MX MX2007004600A patent/MX2007004600A/en active IP Right Grant
-
2008
- 2008-04-16 AR ARP080101566A patent/AR066080A1/en unknown
- 2008-04-17 BR BRPI0810005A patent/BRPI0810005A2/en not_active IP Right Cessation
- 2008-04-17 CA CA002682959A patent/CA2682959A1/en not_active Abandoned
- 2008-04-17 US US12/595,167 patent/US20100193085A1/en not_active Abandoned
- 2008-04-17 WO PCT/MX2008/000054 patent/WO2008127084A2/en active Application Filing
- 2008-04-17 EP EP08753716A patent/EP2143817A2/en not_active Withdrawn
-
2009
- 2009-09-28 NO NO20093069A patent/NO20093069L/en not_active Application Discontinuation
Also Published As
| Publication number | Publication date |
|---|---|
| US20100193085A1 (en) | 2010-08-05 |
| WO2008127084A3 (en) | 2008-12-31 |
| BRPI0810005A2 (en) | 2015-10-27 |
| AR066080A1 (en) | 2009-07-22 |
| WO2008127084A2 (en) | 2008-10-23 |
| MX2007004600A (en) | 2008-12-01 |
| NO20093069L (en) | 2009-12-30 |
| EP2143817A2 (en) | 2010-01-13 |
| WO2008127084A4 (en) | 2009-03-19 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EEER | Examination request |
Effective date: 20130404 |
|
| FZDE | Discontinued |
Effective date: 20170130 |