US20230416884A1 - Linepipe Steel With Alternative Carbon Steel Compositions For Enhanced Sulfide Stress Cracking Resistance - Google Patents
Linepipe Steel With Alternative Carbon Steel Compositions For Enhanced Sulfide Stress Cracking Resistance Download PDFInfo
- Publication number
- US20230416884A1 US20230416884A1 US18/249,502 US202118249502A US2023416884A1 US 20230416884 A1 US20230416884 A1 US 20230416884A1 US 202118249502 A US202118249502 A US 202118249502A US 2023416884 A1 US2023416884 A1 US 2023416884A1
- Authority
- US
- United States
- Prior art keywords
- carbon steel
- carbon
- steel composition
- present disclosure
- range
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000975 Carbon steel Inorganic materials 0.000 title claims abstract description 307
- 239000010962 carbon steel Substances 0.000 title claims abstract description 243
- 239000000203 mixture Substances 0.000 title claims abstract description 233
- 229910000831 Steel Inorganic materials 0.000 title abstract description 67
- 239000010959 steel Substances 0.000 title abstract description 67
- 238000005336 cracking Methods 0.000 title abstract description 10
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 title abstract description 7
- 239000011572 manganese Substances 0.000 claims abstract description 90
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 80
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 55
- 239000010955 niobium Substances 0.000 claims description 60
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 54
- 229910052758 niobium Inorganic materials 0.000 claims description 48
- 229910052720 vanadium Inorganic materials 0.000 claims description 45
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 42
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 42
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 39
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 34
- 239000011651 chromium Substances 0.000 claims description 30
- 229910052759 nickel Inorganic materials 0.000 claims description 23
- 229910052796 boron Inorganic materials 0.000 claims description 19
- 239000010936 titanium Substances 0.000 claims description 19
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 18
- 229910052804 chromium Inorganic materials 0.000 claims description 17
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 15
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 15
- 229910052750 molybdenum Inorganic materials 0.000 claims description 15
- 239000011733 molybdenum Substances 0.000 claims description 15
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 14
- 239000011575 calcium Substances 0.000 claims description 13
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 10
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- 239000011593 sulfur Substances 0.000 claims description 7
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 6
- 229910052791 calcium Inorganic materials 0.000 claims description 6
- BHEPBYXIRTUNPN-UHFFFAOYSA-N hydridophosphorus(.) (triplet) Chemical compound [PH] BHEPBYXIRTUNPN-UHFFFAOYSA-N 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 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 claims description 2
- 238000000034 method Methods 0.000 abstract description 115
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 abstract description 28
- 229910052739 hydrogen Inorganic materials 0.000 abstract description 20
- 239000001257 hydrogen Substances 0.000 abstract description 20
- 239000002244 precipitate Substances 0.000 abstract description 20
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 18
- 239000010779 crude oil Substances 0.000 abstract description 14
- 239000003345 natural gas Substances 0.000 abstract description 14
- 238000010438 heat treatment Methods 0.000 description 90
- 230000008569 process Effects 0.000 description 45
- 229910001566 austenite Inorganic materials 0.000 description 29
- 238000001816 cooling Methods 0.000 description 29
- 238000011282 treatment Methods 0.000 description 26
- 229910001563 bainite Inorganic materials 0.000 description 24
- 230000015572 biosynthetic process Effects 0.000 description 17
- 239000000470 constituent Substances 0.000 description 17
- 238000004519 manufacturing process Methods 0.000 description 14
- 229910000859 α-Fe Inorganic materials 0.000 description 14
- 238000001000 micrograph Methods 0.000 description 13
- 239000011203 carbon fibre reinforced carbon Substances 0.000 description 12
- 229910052751 metal Inorganic materials 0.000 description 12
- 239000002184 metal Substances 0.000 description 12
- 238000010791 quenching Methods 0.000 description 12
- 230000000171 quenching effect Effects 0.000 description 12
- 238000012360 testing method Methods 0.000 description 10
- 239000000463 material Substances 0.000 description 9
- 230000009467 reduction Effects 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 230000003247 decreasing effect Effects 0.000 description 6
- 229910000037 hydrogen sulfide Inorganic materials 0.000 description 6
- 230000001965 increasing effect Effects 0.000 description 6
- 230000032258 transport Effects 0.000 description 6
- 230000008901 benefit Effects 0.000 description 5
- 230000006698 induction Effects 0.000 description 5
- 238000003303 reheating Methods 0.000 description 5
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 4
- YZCKVEUIGOORGS-UHFFFAOYSA-N Hydrogen atom Chemical compound [H] YZCKVEUIGOORGS-UHFFFAOYSA-N 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 150000002739 metals Chemical class 0.000 description 4
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 230000001737 promoting effect Effects 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 238000005496 tempering Methods 0.000 description 4
- QTBSBXVTEAMEQO-UHFFFAOYSA-N Acetic acid Chemical compound CC(O)=O QTBSBXVTEAMEQO-UHFFFAOYSA-N 0.000 description 3
- 239000008186 active pharmaceutical agent Substances 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 230000001747 exhibiting effect Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 229910052723 transition metal Inorganic materials 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
- 229910052729 chemical element Inorganic materials 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 239000012530 fluid Substances 0.000 description 2
- 150000002431 hydrogen Chemical class 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 230000002195 synergetic effect Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 241000284156 Clerodendrum quadriloculare Species 0.000 description 1
- RWDBMHZWXLUGIB-UHFFFAOYSA-N [C].[Mg] Chemical compound [C].[Mg] RWDBMHZWXLUGIB-UHFFFAOYSA-N 0.000 description 1
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 231100001261 hazardous Toxicity 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000006798 recombination Effects 0.000 description 1
- 238000005215 recombination Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- -1 tensile stresses Chemical compound 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 150000003624 transition metals Chemical class 0.000 description 1
Images
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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Definitions
- This application relates to methods and treatments of linepipe steels that transport crude oil and natural gas.
- High-strength metallic materials such as high-strength steels, are commonly used, cost-effective materials for forming linepipe for transporting crude oil and natural gas mined from oil or gas fields. These high-strength, cost-effective materials may be selected to permit transportation of large volumes of crude oil or natural gas without compromising the integrity of the linepipe. That is, the high-strength nature of the materials may permit transportation at relatively higher pressures, or the use of relatively thinner linepipe wall thickness having relatively larger diameters to increase flow volume, and the like. As such, significant cost reduction may be realized from use of such high-strength materials in terms of, for example, material and construction costs.
- crude oil and natural gas may comprise, among other components, hydrogen sulfide (H 2 S) (which may be in relatively high or low concentrations, e.g., extreme to mild sour conditions), as well as other components, such as water, carbon dioxide, chloride, and the like.
- H 2 S hydrogen sulfide
- SSC sulfide stress cracking
- SSC is a form of hydrogen embrittlement induced by atomic hydrogen that is produced by sour corrosion due to the presence of H 2 S on a metal's (e.g., steel's) surface.
- the products of the sour corrosion include atomic hydrogen, which may be absorbed by the linepipe material, resulting in subsequent SSC.
- the H 2 S in crude oil and natural gas can further act as an SSC catalyst because the sulfur in the H 2 S prevents recombination of atomic hydrogen into H 2 , thereby maintaining a high concentration of atomic hydrogen available for absorption by the linepipe and, thus, formation of SSC.
- SSC susceptibility of linepipe carbon steels may be dependent on a number of factors such as, for example, the microstructure of the compositional metal, inclusion and precipitate distribution, chemical composition, and the like, and combinations thereof.
- High-strength metallic materials such as high-strength carbon steels and/or weldments, having heat affected zones with high hardness (e.g., a hardness greater than 248 Vickers hardness number) commonly used to form linepipe may be particularly susceptible to SSC.
- SSC can cause linepipe to lose ductility (e.g., elongation to rupture) and increase cracking susceptibility, thereby causing the linepipe to fail at stresses below its nominal yield strength when subjected to the mechanical stresses of transporting crude oil and/or natural gas (e.g., tensile stresses, residual or applied, and the like). Structural failure of formed parts can result in severely hazardous environmental and operational conditions, as well as substantial economic losses. Accordingly, metallic materials for use as linepipe for transporting crude oil and natural gas comprising H 2 S require high resistance to sour corrosion and/or high resistance to SSC per industry standard requirements.
- This application relates to structural carbon steels that are used to form linepipe that transport crude oil and/or natural gas and, more particularly, to linepipe carbon steels comprising alternative steel compositions and methods and treatments thereof for enhanced sulfide stress cracking resistance.
- FIGS. 2 A- 2 D show representative reconstructed austenite structures at Finishing Rolling Temperature (FRT) and resultant micrographs of carbon steel formed according to the ltTMCP and the htTMCP of FIG. 1 .
- FRT Finishing Rolling Temperature
- FIGS. 3 A- 3 C show representative micrographs of conventional carbon steels formed according to either ltTMCP or the htTMCP of the present disclosure
- FIGS. 3 D and 3 E show representative micrographs of low-manganese carbon steels comprising vanadium formed according to the htTMCP of the present disclosure.
- FIGS. 4 A and 4 B show representative micrographs of low-carbon carbon steels comprising vanadium formed according to the htTMCP of the present disclosure.
- This application relates to linepipe steels that transport crude oil and/or natural gas and, more particularly, to linepipe steels comprising alternative steel compositions and methods and treatments thereof for enhanced sulfide stress cracking resistance.
- linepipe refers to any tubular linepipe steel that transports crude oil and/or natural gas (or other liquids and/or gases), including pipelines, flowlines, risers, any other transport conduit, and the like, without limitation.
- pipeline for example, the disclosure is equally applicable to any other type of linepipe, without limitation, unless specified otherwise.
- the present disclosure advantageously enhances the sulfide stress cracking (SSC) resistance of carbon steels for use as linepipe in transporting crude oil and natural gas by alternative steel compositions comprising one or both of relatively low-manganese contents and/or low-carbon contents, either of which may be alone or in combination with (1) hydrogen trapping precipitates (e.g., niobium, vanadium, and the like) and/or (2) one or more transition metal elements (e.g., nickel, chromium, molybdenum, and the like) and/or (3) the chemical element boron.
- SSC sulfide stress cracking
- the present disclosure provides for alternative steel compositions having relatively low-manganese contents alone or in combination with any one or all of the aforementioned (1), (2), and (3); relatively low-carbon contents alone or in combination with any one or all of the aforementioned (1), (2), and (3); and both relatively low-manganese contents and low-carbon contents alone or in combination with any one or all of the aforementioned (1), (2), and (3).
- hydrogen trapping precipitates and grammatical variants thereof, refers to solid precipitates precipitated during manufacturing of a formed carbon steel, which are capable of trapping and reducing hydrogen diffusion.
- the present disclosure further advantageously enhances the SSC resistance of carbon steels having the alternative compositions described herein by providing one or more alternative thermo-mechanically controlled processes (TMCP) and/or one or both of two post-steel plate or pipe (e.g., welded or seamless) production heat treatment processes (termed either (1) “interim austenitization treatment processes” or (2) “final heat treatment processes,” as discussed hereinbelow, and grammatical variants thereof).
- TMCP thermo-mechanically controlled processes
- two post-steel plate or pipe e.g., welded or seamless production heat treatment processes
- the present disclosure provides alternative carbon steel compositions, which may be used to produce formed carbon steel (e.g., plates, seamless pipes, and the like) using, for example, TMCP as described herein, among other alternative steel manufacturing processes.
- formed carbon steel e.g., plates, seamless pipes, and the like
- TMCP TMCP as described herein
- the alternative carbon steel compositions described herein advantageously enhance the SSC resistance of the produced linepipe without compromising desired mechanical properties.
- the present disclosure provides carbon steel compositions for use as linepipe that have lower manganese (Mn) content and/or lower carbon (C) content, alone or in combination with (1) hydrogen trapping precipitates and/or (2) one or more transition metal elements and/or (3) the chemical element boron (B), as compared to traditional carbon steel compositions.
- the alternative carbon steel compositions described herein further meet industry requirements for the chemical composition of carbon steels used as linepipe (e.g., API 5L, EN ISO 3183, CSA Z245.1, and the like), including minimum yield strength of greater than 52 ksi.
- the lower manganese and/or lower carbon content carbon steel compositions described herein enhance SSC resistance by reducing microstructural constituents, such as martensite/austenite constituents (M/A constituents), among other potential constituents, believed to be detrimental to SSC resistance.
- the alternative carbon steel compositions of the present disclosure comprising reduced manganese and/or reduced carbon can minimize or otherwise eliminate the formation of these hard phases.
- the alternative lower manganese and/or lower carbon content carbon steel compositions may further comprise one or more transition metals (e.g., nickel, niobium, vanadium, niobium+vanadium, chromium+molybdenum, and the like) and/or boron.
- the inclusion of nickel in low-manganese content compositions may increase hardenability to promote the formation of lath bainite, and may further increase the intrinsic toughness of the formed carbon steel (although nickel may be included in the alternative low-carbon content carbon steels described herein, as well).
- the inclusion of Cr and/or Mo in low manganese content compositions may increase hardenability to promote the formation of lath bainite, and may produce the precipitates of Cr/Mo carbides potentially resulting in the increase of yield strength and/or acting as hydrogen trapping sites.
- the inclusion of boron in low-manganese content compositions may increase hardenability to promote the formation of lath bainite.
- the alternative lower manganese content carbon steel compositions may further have the carbon range of about 0.01 wt. % to about 0.15 wt. % (e.g., about 0.03 wt. % to about 0.12 wt. %), encompassing any value and subset therebetween, to provide higher strength (YS 52100 ksi) by promoting lath bainite, such as having equal to or greater than about 50 vol. % lath bainite, including up to 100 vol. %, encompassing any value and subset therebetween.
- the alternative carbon steel compositions comprising the alternative low-carbon content of the present disclosure can be used to produce formed carbon steels that are substantially hard phase free, such as having equal to or greater than about 90 vol. % ferrite, including up to 100 vol. % ferrite, encompassing any value and subset therebetween, depending on the particular manufacturing process selected (e.g., traditional v. the alternative TMCP process and/or additional heat treatment process(es)).
- the amount of manganese included in a carbon steel composition for use as linepipe may be in the range of equal to or less than about 1.6 wt. % of the carbon steel composition in total, such as about 0.6 wt. % to about 1.6 wt. % or about wt. % to about 1.3 wt. %, or about 0.8 wt. % to about 1.2 wt. %, encompassing any value and subset therebetween.
- the amount of carbon included in a carbon steel composition for use as linepipe may be in the range of equal to or less than about 0.025 wt. % of the carbon steel composition in total, such as about 0.01 wt. % to about 0.025 wt. %, or about wt. % to about 0.02 wt. %, or about 0.01 wt. % to about 0.015 wt. %, encompassing any value and subset therebetween.
- an alternative carbon steel composition may have a manganese content in the range of about 0.6 wt. % to about 1.6 wt. % or about 0.6 wt. % to about 1.3 wt. % of the carbon steel composition, in combination with a carbon content in the range of about 0.01 wt. % to about 0.025 wt. % of the carbon steel composition, encompassing any value and subset therebetween.
- one or more additional elements may be included.
- a carbon range of about 0.03 wt. % to about 0.15 wt. %, encompassing any value and subset therebetween, may increase hardness and/or strength of the alternative low manganese content carbon steels described herein.
- one or more additional elements may be included.
- the inclusion of nickel may increase hardness and/or toughness of the alternative low manganese and/or low carbon content carbon steels described herein.
- the alternative carbon steel compositions may have a nickel content in the range of about 0.15 wt. % to about 1.0 wt. % of the carbon steel composition in total, encompassing any value and subset therebetween.
- the inclusion of nickel may be particularly preferred for inclusion in the low-manganese content carbon steel compositions described herein.
- the hydrogen trapping precipitates may be in the form of niobium carbonitride (NbCN) or vanadium carbonitride (VCN).
- niobium and vanadium may be present in the alternative carbon steel compositions of the present disclosure in an amount of about 0.02 wt. % to about 0.15 wt. % wt. % of the carbon steel composition in total, such as about 0.02 wt. % to about 0.04 wt. %, or about 0.04 wt. % to about 0.08 wt. %, or about 0.05 wt. % to about 0.10 wt. %, encompassing any value and subset therebetween.
- phosphorous may be present in the alternative carbon steel compositions in an amount of less than or equal to about 0.015 wt. %, such as in the range of about 0.0005 wt. % to about 0.015 wt. %; sulfur may be present in an amount of less than or equal to about 0.025 wt. %, such as in the range of about 0.0005 wt. % to about 0.025%; silicon may be present in an amount of equal to or less than 0.45 wt. %, such as in the range of about 0.01 wt. % to about 0.45 wt. %; aluminum may be present in an amount of equal to or less than about 0.1 wt.
- the alternative low manganese and/or low carbon content carbon steel compositions of the present disclosure may include one or more of nickel, vanadium, and/or niobium. In one or more aspects, the alternative low manganese and/or low carbon content carbon steel compositions of the present disclosure may include one or more of boron, chromium, and/or molybdenum. In some aspects, the inclusion of a particular element may be more advantageous when the resultant formed carbon steel is a seamless pipe, such as nickel, niobium, vanadium, boron, chromium, and/or molybdenum.
- the inclusion of a particular element may be more advantageous when the resultant formed carbon steel is a non-seamless pipe (e.g., a plate formed into a tubular linepipe, such as by welding), such as nickel, niobium, and/or vanadium.
- a non-seamless pipe e.g., a plate formed into a tubular linepipe, such as by welding
- nickel, niobium, and/or vanadium such as nickel, niobium, and/or vanadium.
- the present disclosure provides a TMCP process that employs relatively higher RHT and/or higher FRT temperatures compared to traditional TMCP, including one or more deformation (e.g., hot rolling) steps at relatively higher temperatures. It is to be appreciated that small variations in RHT and FRT can have significant effect on microstructure, strength, and SSC resistance of a carbon steel. For these reasons, traditional low temperature RHT ( ⁇ 1150° C.) and low temperature FRT ( ⁇ 900° C.) have been used to minimize austenite grain growth. The present disclosure establishes that higher RHT and higher FRT, even if by several degrees, can advantageously alter the microstructure of the resultant steel and its SSC resistance, as described hereinbelow.
- the TMCP described herein further employs one or more relatively longer extended interpass times, as well, to promote recovery and or recrystallization of deformed austenite; extended interpass time parameters are described hereinbelow and, unlike traditional interpass practice, the extended interpass times described herein are controlled such that the interpass time is managed and not otherwise random.
- the TMCP methods include quenching or cooling at a cooling rate. Quenching includes accelerated cooling, wherein a fluid is used to increase cooling rate (as opposed to air cooling); other quenching methods may also be employed, without departing from the scope of the present disclosure. Accelerated cooling may enhance various performance properties of the TMCP-produced steel, such as enhanced low temperature toughness and high fracture toughness. After quenching, a formed carbon steel is produced.
- the term “formed carbon steel” or “formed steel,” and grammatical variants thereof, refers to a carbon steel composition (i.e., the alternative carbon steel compositions of the present disclosure) that has been formed into the shape of a plate (also referred to as a sheet) or seamless pipe and quenched (e.g., cooling by any means, such as to room temperature or other appropriate temperature), such as by the TMCP methods described herein.
- the formed steel is suitable for use as linepipe for use as pipeline, as described herein, and meet required industry standards (e.g., API 5L, EN ISO 3183, CSA Z245.1, and the like).
- the methods of the present disclosure promote lath bainite, other microstructure, such as acicular ferrite and/or granular bainite, may also be present in the produced metal, without departing from the scope of the present disclosure.
- the alternative low manganese and/or low carbon content carbon steel compositions of the present disclosure may be formed using traditional manufacturing processes (e.g., traditional TMCP), which may produce carbon steels having equal to or greater than about 90 vol. % ferrite.
- TMCP TMCP
- TMCP methodologies of the present disclosure for enhancing SSC resistance are applicable to any and all steel compositions for use in manufacturing linepipe and meeting required industry standards (e.g., API 5L, EN ISO 3183, CSA Z245.1, and the like), without limitation.
- FIG. 1 illustrated are comparative TMCP methods graphically demonstrating the differences between a traditional low temperature TMCP (tTMCP) methodology and the higher temperature TMCP (htTMCP) methodology of the present disclosure.
- Representative, and non-limiting, deformation (e.g., hot rolling) steps are shown as starbursts, further illustrating extended non-limiting interpass times as part of the htTMCP methods of the present disclosure.
- the traditional ltTMCP demonstrates lower slab reheating temperature (ltRHT) in order to minimize austenite grain growth (keeping the grain size small), and also demonstrates relatively lower finishing rolling temperature (ltFRT) in order to maximize hot deformation below the non-recrystallization temperature (Tnr) and achieve a pancaked or fine grain austenite structure.
- ltRHT slab reheating temperature
- ltFRT finishing rolling temperature
- the ltTMCP produces a primarily fine grained microstructure composed of acicular ferrite, granular bainite or ferrite, or combinations thereof.
- the htTMCP of the present disclosure demonstrates a higher slab reheating temperature (htRHT) to optimize austenite grain growth (encouraging large(r) austenite grain size), and also demonstrates relatively higher finishing rolling temperature (htFRT) in order to minimize hot deformation below the Tnr and prevent pancaking or deformation of the formed grain structures.
- the extended interpass time shown (one, non-limiting example shown) in the htTMCP plot of FIG. 1 may promote austenite recovery and recrystallization at the higher temperatures used (e.g., greater than about 1000° C.).
- FIGS. 2 A- 2 D show representative reconstructed austenite structures at FRT and resultant micrographs of formed steel according to the ltTMCP and the htTMCP of FIG. 1 .
- FIG. 2 A and FIG. 2 B show reconstructed austenite structure at ltFRT and htFRT, respectively of FIG. 1 .
- the reconstruction of austenite structure was completed through the use of typical orientation relationships between parent austenite phase and daughter bainitic phases based on Electron Back Scattered Diffraction (EBSD) techniques.
- EBSD Electron Back Scattered Diffraction
- FIG. 2 A the average prior austenite grain size (PAG) according to the traditional ltTMCP method was measured at 13.7 ⁇ m ( FIG. 2 A ), whereas the average PAG according to the htTMCP method of the present disclosure was measured at 24.9 ⁇ m ( FIG. 2 B ).
- the average PAG according to the htTMCP methods of the present disclosure are in the range of about 20 ⁇ m to about 50 ⁇ m, encompassing any value and subset therebetween, such as about 30 ⁇ m, or about 40 ⁇ m.
- FIGS. 2 C and 2 D show micrographs of the resultant formed steel after accelerated cooling according to the ltTMCP and the htTMCP, respectively, of FIG. 1 .
- the coarser austenite structure of the htTMCP method of the present disclosure promoted a lath bainite microstructure, as shown in FIG. 2 D , which is absent or less apparent in the traditional ltTMCP microstructure shown in FIG. 2 C comprising primarily fine(r) grained ferritic and granular bainitic microstructures.
- the RHT may be in the range of greater than or equal to about 1175° C. to about 1350° C., encompassing any subset and value therebetween, such as in the range of about 1200° C. to about 1300° C., more preferably between 1200° C. to 1250° C.
- the heating rate is not considered to be particularly limiting to reach the desired RHT; in some aspects, the heating rate to RHT may be in the range of about 0.1° C. per second (° C./sec) to about 100° C./sec, encompassing any value and subset therebetween.
- the RHT may be maintained stable for a predetermined length of time (e.g., depending on the steel composition and part size to be produced therefrom, depending on the RHT, and the like, and any combination thereof), such as greater than about one (1) minute to about ten (10) hours, encompassing any value and subset therebetween, such as greater than about 1 hour to about 5 hours.
- the time period in which the RHT is maintained is also referred to in the industry as the period of “austenitizing.” Accordingly, the austenitizing period described in the present disclosure is performed at a relatively higher temperature compared to traditional TMCP.
- the FRT may be in the range of the RHT to greater than about Ar3, encompassing any subset and value therebetween, such as about 910° C. to about 1000° C., encompassing any value and subset therebetween.
- At least one or more extended interpass durations may be in the range of about 10 seconds to about 10 minutes, such as about 30 seconds to about 10 minutes, encompassing any value and subset therebetween.
- the at least one or more extended interpass durations are performed at or above a temperature in the range of about Tnr (the non-recrystallization temperature) to about (Tnr+200° C.° C.) (i.e., the Tnr temperature plus 200° C.), such as in the range of about Tnr to about Tnr+100° C.), or in the range of about Tnr to about Tnr+50° C.), encompassing any value and subset therebetween.
- at least one or more extended interpass durations are performed at or above a temperature of about 950° C., encompassing any subset and value therebetween, such as about 30 seconds to about 10 minute.
- one or more of the extended interpass durations may be in the temperature range of at least about 950° C. to about 1175° C., encompassing any value and subset therebetween.
- the accelerated cooling for use in various aspects of the TMCP methods of the present disclosure may be in the range of about 1° C./sec to about 300° C./sec, encompassing any value and subset therebetween, such as about 5° C./sec to about 100° C./sec.
- the accelerated cooling may be to a temperature of equal to or less than about 500° C., such as in the range of about 100° C. to about 400° C., or about 20° C. (room temperature) to about 400° C., encompassing any value and subset therebetween.
- the present disclosure incorporates a final heat treatment step after completion of a high temperature TMCP process (i.e., after cooling, and whether the cooled steel is formed or otherwise welded into a pipe).
- the high temperature TMCP and the final heat treatment step synergistically further enhance SSC resistance without compromising desired mechanical properties (e.g., tensile properties, low temperature toughness/resistance, hydrogen induced cracking, and the like) and with minimal manufacturing costs.
- steel formed after completion of a high temperature TMCP process may be subsequently heated (after accelerated cooling to a desired temperature) to a temperature in the range of about (Ac1 ⁇ 300° C.) (i.e., the Ac1 temperature less 300° C.) to about Ac1, such as in the range of about (Ac1 ⁇ 200° C.) to about Ac1, or in the range of about (Ac1 ⁇ 100° C.) to about Ac1, and preferably in the range of about (Ac1 ⁇ 300° C.) to less than Ac1, encompassing any value and subset therebetween.
- Ac1 is the lowest temperature at which austenite begins to form during heating at a specified rate and, accordingly, is not a static temperature.
- the heating rate may be in the range of about per second (° C./sec) to about 100° C./sec, encompassing any value and subset therebetween; such rates may depend on a number of factors including, but not limited to, the type of heating used (e.g., induction heating v. non-induction heating).
- the heating temperature for the final heating step after high temperature TMCP may be preferably relatively close to but less than the Ac1 temperature to maximize SSC resistance. Heat treatment above Ac1 may potentially cause the formation of hard phase from reverted austenite during cooling, which may deteriorate SSC resistance.
- the desired temperature Upon reaching the desired temperature, it is maintained stable for a predetermined length of time, such as in the range of greater than about one (1) minute to about 10 hours, encompassing any value and subset there between, such as about 10 minutes to about 8 hours, or about 10 minutes to about 6 hours, or about 10 minutes to about 5 hours, or preferably about 10 minutes to about 3 hours, or about 10 minutes to about 2 hours, and thereafter allowed to cool.
- the cooling temperature and cooling rate is non-limiting and, therefore, does not constrain the process to any particular cooling equipment or staffing requirement, thereby limiting costs.
- the cooling may be performed to reach ambient temperature by any suitable means, including air cooling or other passive cooling techniques, in some aspects.
- cooled high temperature TMCP steel has not been formed into a pipe (e.g., welded) prior to performing the final heat treatment process, after allowing further cooling from the final heat treatment, it may thereafter be formed into a tubular linepipe (e.g., welded).
- TMCP process described herein may be applied to steel compositions manufactured into linepipe by tubular welding techniques, alone or in combination with the final heat treatment process of the present disclosure.
- present disclosure is equally applicable to steel compositions manufactured into linepipe by tubular seamless techniques (“seamless formed steel”), requiring the combination of both the TMCP process (e.g., hot deformation process) and the final heat treatment processes described herein.
- TMCP process e.g., hot deformation process
- final heat treatment processes described herein eamless formed carbon steel” or “seamless formed steel,” and grammatical variants thereof, refers to a formed steel, as described hereinabove.
- Seamless formed steel is shaped during the TMCP processes into a tubular pipe having a hollow section and no seams (as opposed to welded pipe comprising seam welds) and quenched.
- the final heat treatment process is mandatory and not optional.
- Seamless formed steel is manufactured using TMCP by reheating a steel billet at a RHT. While hot, the steel billet is pierced through the center (e.g., with a rotary piercer and a set of roller arrangements to maintains the piercer at the center of the billet). The billet is rolled and stretched until it meets a desired length, diameter, and wall thickness.
- the inner diameter of the seamless formed steel may be approximately equivalent to the outer diameter of the rotary piercer, and the outer diameter of the seamless formed steel may be controlled using an external roller arrangement. By controlling the inner and outer diameter of the seamless formed steel, the wall thickness is also controlled.
- traditional seamless formed steel is manufactured using traditional TMCP utilizing relatively low RHT (e.g., equal to or less than or equal to 1150° C.) to reheat the billet and austenitize and relatively low FRT (e.g., less than or equal to 900° C.) to roll and stretch the billet, including one or more hot deformation steps at these relatively low temperatures, along with relatively short interpass times (i.e., time between two consecutive deformation steps) to minimize austenite grain growth, and provide fine ferrite/bainite microstructure, as described hereinabove.
- relatively low RHT e.g., equal to or less than or equal to 1150° C.
- FRT e.g., less than or equal to 900° C.
- the present disclosure provides for seamless steel formed using the high temperature TMCP process and the additional (mandatory) heat treatment described hereinabove, with an interim austenitization treatment (mandatory) step therebetween.
- the term “interim austenitization treatment process,” and grammatical variants thereof, refers to a non-deforming steel heat treatment held at a temperature above Ac3 (i.e., the critical temperature at which free ferrite is completely transformed into austenite) for a period of time, followed by quenching. It is to be understood that while the present disclosure discusses the interim austenitization treatment process with reference to the formation of seamless steel, the interim austenitization treatment may equally be applied to form any type of linepipe without limitation.
- steel formed after completion of a high temperature TMCP process may be subsequently interim austenitization treatment processed (i.e., prior to the final heat treatment described herein) at a temperature in the range of about (Ac3+50° C.) (i.e., the Ac3 temperature plus 50° C.) to about (Ac3+200° C.), such as in the range of about (Ac3+50° C.) to about (Ac3+150° C.), or in the range of about (Ac3+75° C.) to about (Ac3+100° C.), encompassing any value and subset therebetween.
- Quenching includes accelerated cooling, wherein a fluid is used to increase cooling rate (as opposed to air cooling); other quenching methods may also be employed, without departing from the scope of the present disclosure.
- the carbon steel may be thereafter processed according to the final heat treatment process described hereinabove.
- the interim austenitization treatment and the final heat treatment process are both mandatory.
- the formed carbon steel is a non-seamless pipe (e.g., a plate formed into a tubular linepipe, such as by welding)
- the interim austenitization treatment and the final heat treatment are both optional after the high temperature TMCP of the present disclosure, alone or in combination.
- a carbon steel composition comprising: manganese in an amount of equal to or less than about 1.6% by weight or less than about 1.3% by weight of the carbon steel composition.
- Clause 2 The carbon steel composition of Clause 1, wherein the manganese is in a range of about 0.6 wt. % to about 1.6 wt. % or about 0.6% to about 1.3% by weight of the carbon steel composition.
- Clause 3 The carbon steel composition of Clause 1, further comprising one or more elements selected from the group consisting of carbon, phosphorous, sulfur, silicon, aluminum, chromium, molybdenum, niobium, titanium, nitrogen, calcium, nickel, vanadium, boron, and any combination thereof.
- Clause 4 The carbon steel composition of Clause 3, wherein the carbon steel comprises at least nickel in an amount in the range of about 0.15% to about 1.0% by weight of the carbon steel composition.
- Clause 5 The carbon steel composition of Clause 3, wherein the carbon steel comprises at least carbon in an amount in the range of about 0.01% to about 0.15% by weight of the carbon steel composition.
- Clause 10 The carbon steel composition of Clause 3 to Clause 9, wherein the carbon steel composition comprises at least niobium and vanadium, and the combined amount of niobium and vanadium is in an amount of about 0.02% to about 0.15% by weight of the carbon steel composition.
- Clause 13 The carbon steel composition of Clause 3 to Clause 12, wherein the carbon steel comprises at least molybdenum in an amount in the range of about 0.1% to about 0.5% by weight of the carbon steel composition.
- Clause 14 The carbon steel composition of Clause 3 to Clause 13, wherein the carbon steel comprises at least titanium in an amount in the range of about 0.005% to about 0.1% by weight of the carbon steel composition.
- a carbon steel composition comprising: carbon in an amount of equal to or less than about 0.025% by weight of the carbon steel composition.
- Clause 16 The carbon steel composition of Clause 15, wherein the carbon is in a range of about 0.01% to about 0.025% by weight of the carbon steel composition.
- Clause 17 The carbon steel composition of Clause 15, further comprising one or more elements selected from the group consisting of manganese, phosphorous, sulfur, silicon, aluminum, chromium, molybdenum, niobium, titanium, nitrogen, calcium, nickel, vanadium, boron, and any combination thereof.
- Clause 18 The carbon steel composition of Clause 17, wherein the carbon steel comprises at least manganese in an amount of equal to or less than about 1.6% by weight or less than about 1.3% by weight of the carbon steel composition.
- Clause 19 The carbon steel composition of Clause 17 or Clause 18, wherein the manganese is in a range of about 0.6% to about 1.6% or about 0.6% to about 1.3% by weight of the carbon steel composition.
- Clause 20 The carbon steel composition of Clause 17 to Clause 19, wherein the carbon steel composition comprises at least niobium in an amount of about 0.02% to about 0.10% by weight of the carbon steel composition.
- Clause 21 The carbon steel composition of Clause 17 to Clause 20, wherein the carbon steel composition comprises at least vanadium in an amount of about 0.02% to about 0.10% by weight of the carbon steel composition.
- Clause 22 The carbon steel composition of Clause 17 to Clause 21, wherein the carbon steel composition comprises at least niobium and vanadium, and the combined amount of niobium and vanadium is in an amount of about 0.02% to about 0.15% by weight of the carbon steel composition.
- Clause 23 The carbon steel composition of Clause 17 to Clause 22, wherein the carbon steel comprises at least nickel in an amount in the range of about 0.15% to about 1.0% by weight of the carbon steel composition.
- Clause 24 The carbon steel composition of Clause 17 to Clause 23, wherein the carbon steel comprises at least boron in an amount in the range of about 0.0005% to about 0.003% by weight of the carbon steel composition.
- Clause 26 The carbon steel composition of Clause 17 to Clause 25, wherein the carbon steel comprises at least molybdenum in an amount in the range of about 0.1% to about 0.5% by weight of the carbon steel composition.
- ID1 ID2 ID3 ID4 C 0.064 0.047 0.043 0.042 Mn 1.41 0.98 1.03 0.98 P 0.010 0.009 0.008 0.008 S 0.001 0.001 0.005 0.005 Si 0.261 0.378 0.372 0.394 Al 0.008 0.032 0.039 0.031 Cr 0.21 0.19 0.20 0.20 Mo 0.10 0.10 0.10 0.10 0.10 Nb 0.030 0.029 0.029 0.030 Ti 0.014 0.014 0.009 0.009 N 0.0049 0.0030 0.0025 0.0024 Ca 0.0008 0.0020 0.0010 0.0009
- the FRT was selected at a temperature greater than Ara, the temperature at which austenite begins phase transformation onset during cooling (transformation to ferrite and/or bainite) and with various interpass durations, including at least one extended interpass duration, as defined hereinabove (temperature and time), followed by accelerated cooling control (ACC) at a cooling rate of greater than about 5° C./sec (e.g., in the range of about 5° C./sec to about 50° C./sec, or about 20° C./sec to about 50° C./sec) to ambient temperature.
- ACC accelerated cooling control
- the specific TMCP parameters for this Example are provided in Table 2; actual extended interpass temperatures ranged between 950° C. to 1150° C. due to production conditions and equipment requirements.
- TMCP treated ID1-ID4 carbon steels were evaluated for mechanical properties and SSC resistance.
- Mechanical properties including yield strength (YS) measured in kip per square inch (ksi), tensile strength (TS) measured in ksi, and percent elongation (EL), were tested according to sub-size round bar with 1′′ gauge length of ASTM-E8.
- the mechanical properties of the low-manganese produced steels are suitable for use as linepipe.
- the steel plates formed in accordance with the methods of the present disclosure may have a K ISSC of greater than about 35 ksi-in 0.5 , such as in the range of greater than about 35 ksi-in 0.5 to about 60 ksi-in 0.5 , or about 36 ksi-in 0.5 to about 60 ksi-in 0.5 , encompassing any value and subset therebetween.
- each of ID1-ID4 exhibited enhanced SSC resistance after final heat treatment, as shown in Table 4.
- ID1 improved by about 22%;
- ID2 improved by about 21%;
- ID3 improved by about 25%;
- ID4 improved by about 8%.
- the final heat treatment step generally resulted in increased yield strength and elongation and, if at all, comparable or marginally decreased tensile strength while improving K ISSC .
- the final heat treatment reveals a synergistic effect when combined with the high temperature TMCP process of the present disclosure, including, if not an even more pronounced synergistic effect at higher temperatures within the ranges of the TMCP process of the present disclosure (e.g., higher FRT).
- the final heat treatment methods of the present disclosure may provide comparatively (e.g., to identical compositions without the final heat treatment) enhanced SSC resistance by greater than about 4%, including greater than about 5%, such as in the range of greater than about 5% to about 45%, or greater than about 5% to about 40%, encompassing any value and subset therebetween, including the alternative carbon steel compositions of the present disclosure as well as traditional carbon steels.
- the low-manganese carbon steel compositions of the present disclosure are suitable for use as linepipe and meet required industry standards.
- ID5-ID7 represent standard, commercially available API-5L sour grade carbon steel compositions used for linepipe; ID9 and ID10 represent low-manganese carbon steel compositions.
- ID5-ID10 include niobium and vanadium.
- ID5 ID6 ID7 ID9 ID10 C 0.044 0.043 0.039 0.041 0.043 Mn 1.37 1.36 1.39 1.00 1.01
- P 0.007 0.008 0.008 0.008 0.008 S 0.005 0.005 0.005 0.004 0.004 Si 0.257 0.243 0.253 0.403 0.418
- FIGS. 3 A- 3 C show representative micrographs of the conventional carbon steels ID5-ID7, respectively, formed according to either ltTMCP or htTMCP of this example;
- FIGS. 3 E and 3 F show representative micrographs of low-manganese carbon steels comprising niobium and vanadium ID9 and ID10, respectively, formed according to htTMCP of this example.
- each of the carbon steels have bainite matrices (granular bainite) with M/A constituents and ferrite.
- FIGS. 3 D and 3 E the low-manganese carbon steels comprising niobium and vanadium of ID9 and ID10 promote the formation of ferrite with reduced M/A constituents.
- the ID5-ID10 carbon steels were evaluated for mechanical properties and SSC resistance (using NACE A) as described in Example 1. The results are reported in Table 7.
- the steel plates formed in accordance with the methods of the present disclosure may have a K ISSC of greater than about 35 ksi-in 0.5 , such as in the range of greater than about 35 ksi-in 0.5 to about 60 ksi-in 0.5 , or about 36 ksi-in 0.5 to about 60 ksi-in 0.5 , encompassing any value and subset therebetween.
- ID5-ID10 was exposed to a final heat treatment at 575° C. and the results are shown in Table 8; ID5-ID10 were exposed to a final heat treatment at 675° C. and the results are shown in Table 9. Where a “-” is shown, the particular test was not performed.
- each of ID6-ID10 exhibited enhanced SSC resistance after final heat treatment of 575° C., as shown in Table 8. Moreover, the final heat treatment step generally resulted in increased yield strength and elongation and, if at all, comparable or marginally decreased tensile strength while improving K ISSC . ID6 improved by about 23%; ID7 improved by about 27%; ID9 improved by about 22%; and ID10 improved by 19%. Accordingly, as consistent with Example 1, the final heat treatment methods of the present disclosure may provide comparatively (e.g., to identical compositions without the final heat treatment) enhanced SSC resistance by greater than about 4%, including the alternative carbon steel compositions of the present disclosure as well as traditional carbon steels.
- each of ID6, ID9, and ID10 exhibited enhanced SSC resistance after final heat treatment of 675° C., as shown in Table 9.
- the amount of V and Nb present in the low-manganese compositions ID9 and ID10 in combination with the final heat treatment may at least partially contribute to the SSC resistance by forming fine precipitates that trap hydrogen.
- the increase in SSC resistance upon final heat treatment may further be attributable to other metallurgical changes, such as tempering on M/A constituents (e.g., disassociation of M/A constituents), reduction of dislocation density, and the like, and any combination thereof.
- the low-manganese carbon steel compositions of the present disclosure are suitable for use as linepipe and meet required industry standards.
- carbon steel composition comprising low-carbon content, as defined herein, were prepared and tested for mechanical properties and SSC resistance.
- the low-carbon carbon steels of this Example are compared to the conventional carbon steels ID5-ID7 of Example 2.
- Example 2 Two (2) carbon ingots were prepared according to the methods described in Example 1, having the compositions listed in Table 10 and the processing parameters listed in Table 11, using a TMCP method according to various aspects of the present disclosure.
- Each of low-carbon carbon steel compositions ID11-ID12 include niobium and vanadium.
- FIGS. 4 A and 4 B show representative micrographs of low-carbon carbon steels comprising niobium and vanadium ID11 and ID12, respectively, formed according to htTMCP of this example. As compared to FIGS. 3 A- 3 D , the low-carbon carbon steels comprising niobium and vanadium of ID11 and ID12 promote the formation of ferrite with reduced M/A constituents.
- the ID11 and ID12 carbon steels were evaluated for mechanical properties and SSC resistance (using NACE A) as described in Example 1. The results are reported in Table 12.
- each of the low-carbon concentration carbon steels of ID11 and ID12 exhibit comparable SSC resistances compared to the commercially available, higher carbon concentration carbon steels of ID5-ID7 (Example 2), including those prepared using the high RHT/FRT TMCP of the present disclosure (ID6 of Example 2).
- the mechanical properties of the low-carbon produced steels are suitable for use as linepipe, exhibiting comparable mechanical properties to conventional carbon steels.
- the steel plates formed in accordance with the methods of the present disclosure may have a K ISSC of greater than about 35 ksi-in 0.5 , such as in the range of greater than about 35 ksi-in 0.5 to about 60 ksi-in 0.5 , or about 36 ksi-in 0.5 to about 60 ksi-in 0.5 , encompassing any value and subset therebetween.
- ID12 exhibited enhanced SSC resistance after final heat treatment of 675° C., as shown in Table 14.
- the low-carbon carbon steel compositions of the present disclosure are suitable for use as linepipe and meet required industry standards.
- ID 13 represents a low-manganese carbon steel composition prepared according to aspects of the present disclosure
- ID13-ID16 represent combination low-manganese and low-carbon carbon steel compositions prepared according to aspects of the present disclosure.
- Each of ID13-ID16 include niobium and vanadium.
- FIG. 5 A shows a representative micrograph of a low-manganese carbon steel comprising niobium and vanadium of the present disclosure
- FIGS. 5 B- 5 D show representative micrographs of combination low-manganese and low-carbon carbon steels comprising niobium and vanadium of the present disclosure.
- each of the carbon steels have ferrite matrices with M/A constituents. The additional lower carbon contents of ID14-ID16 even further reduces the M/A constituents.
- the ID13-ID16 carbon steels were evaluated for mechanical properties and SSC resistance (using NACE A) as described in Example 1. The results are reported in Table 17.
- each of the low-manganese/low-carbon concentration carbon steels of ID14 and ID16 exhibit comparable SSC resistances compared to the low-manganese only (higher carbon concentration) carbon steel of ID 13.
- the mechanical properties of the low-manganese/low-carbon produced steels are suitable for use as linepipe, exhibiting comparable mechanical properties to conventional carbon steels as provided herein, as well as the low-manganese only carbon steel of ID13.
- ID13-ID16 were exposed to a final heat treatment at 575° C. and the results are shown in Table 18; ID13-ID16 were exposed to a final heat treatment at 675° C. and the results are shown in Table 19. Where a “—” is shown, the particular test was not performed.
- ID14 Compared to the results in Table 17 (without final heat treatment), ID14 exhibited enhanced SSC resistance after final heat treatment of 575° C., as shown in Table 18. Moreover, the final heat treatment step generally resulted in increased yield strength and, if at all, comparable or marginally decreased tensile strength and elongation while improving K ISSC . ID14 improved by about 4%. Accordingly, as consistent with Examples 1, 2, and 3, the final heat treatment methods of the present disclosure may provide comparatively (e.g., to identical compositions without the final heat treatment) enhanced SSC resistance by greater than about 4%, including the alternative carbon steel compositions of the present disclosure as well as traditional carbon steels.
- ID13-ID16 exhibited enhanced SSC resistance after final heat treatment of 675° C., as shown in Table 19.
- the increase in SSC resistance was greater at the higher temperature of 675° C. compared to 525° C., which may be attributable the combined low-carbon and low-manganese content.
- the amount of Nb and V present in the low-carbon compositions ID13 and ID16 in combination with the final heat treatment may at least partially contribute to the SSC resistance by forming fine precipitates that trap hydrogen, promoting the precipitation of NbC and/or VC.
- the increase in SSC resistance upon final heat treatment may further be attributable to other metallurgical changes, such as tempering on M/A constituents (e.g., disassociation of M/A constituents), reduction of dislocation density, and the like, and any combination thereof.
- the low-carbon carbon steel compositions of the present disclosure are suitable for use as linepipe and meet required industry standards.
- carbon steel compositions comprising both low-manganese with Ni content, as defined herein, were prepared and tested for mechanical properties and SSC resistance.
- ID 17-18 represents low-manganese carbon steel composition with Ni content prepared according to aspects of the present disclosure.
- the ID17 and ID18 carbon steels were evaluated for mechanical properties and SSC resistance (using NACE A) as described in Example 1. The results are reported in Table 21. The results indicate that the carbon steels comprising alternative low-manganese content and nickel exhibit greater SSC resistance compared to commercially available carbon steels, such as ID1.
- Example 6 Liow-Manganese Carbon Steels Comprising Carbon, Boron, Niobium, Chromium, Molybdenum and Nickel Produced by Tubular Seamless Technique
- carbon steel compositions were assessed in order to evaluate tensile properties and SSC resistance of materials processed by tubular seamless technique with various alloying elements.
- Nine (9) ingots were prepared according to the methods described in Example 1, having the compositions listed in Table 23.
- ID19-ID22 represent lower carbon/manganese carbon steel composition comprising Nb and B content prepared according to aspects of the present disclosure.
- ID23-ID27 represent the low-manganese carbon steel compositions with the combination of higher C/Cr/Mo/Nb/Ni, prepared according to aspects of the present disclosure.
- the carbon steel compositions shown in Table 23 provide higher strength (YS of about to about 110 ksi) due to the precipitation hardening and/or fraction of lath bainite by higher alloying content (higher hardenability). With the combination of one and/or more disclosed processes hereinabove, these carbon steel compositions have high fraction of tempered bainite with Nb precipitation, which provide a beneficial combination of higher strength and SSC resistance.
- ID19-ID23 show the combination of YS in the range of 74.3 ksi to 93.3 ksi and K ISSC in the range of 31.1 ksi-in 0.5 to 55.4 ksi-in 0.5 .
- ID19-ID23 Compared with the results of commercial linepipe grades (ID5-ID7) in Table 7, the results of ID19-ID23 exhibited higher strength with comparable (or better) SSC resistance. ID24-27 results in Table 24 show even higher YS in the range of 80 ksi to 108 ksi with K ISSC of 24.6-49.5 ksi-in 0.5 due to higher C/Nb/Cr/Mo/Ni content.
- Example 7 High-Chromium and/or High-Manganese Carbon Steels Produced by Tubular Seamless Technique
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US18/249,502 US20230416884A1 (en) | 2020-12-04 | 2021-12-01 | Linepipe Steel With Alternative Carbon Steel Compositions For Enhanced Sulfide Stress Cracking Resistance |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US202063121371P | 2020-12-04 | 2020-12-04 | |
PCT/US2021/072651 WO2022120337A1 (fr) | 2020-12-04 | 2021-12-01 | Acier de tube de canalisation à compositions d'acier ordinaire différentes pour une résistance améliorée à la fissuration sous contrainte induite par sulfure |
US18/249,502 US20230416884A1 (en) | 2020-12-04 | 2021-12-01 | Linepipe Steel With Alternative Carbon Steel Compositions For Enhanced Sulfide Stress Cracking Resistance |
Publications (1)
Publication Number | Publication Date |
---|---|
US20230416884A1 true US20230416884A1 (en) | 2023-12-28 |
Family
ID=79164619
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US18/249,502 Pending US20230416884A1 (en) | 2020-12-04 | 2021-12-01 | Linepipe Steel With Alternative Carbon Steel Compositions For Enhanced Sulfide Stress Cracking Resistance |
Country Status (2)
Country | Link |
---|---|
US (1) | US20230416884A1 (fr) |
WO (1) | WO2022120337A1 (fr) |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5980752A (ja) * | 1982-10-28 | 1984-05-10 | Nippon Kokan Kk <Nkk> | 硫化水素環境で溶接部の耐水素割れ性及び耐硫化物応力腐食割れ性に優れた鋼 |
AR047467A1 (es) * | 2004-01-30 | 2006-01-18 | Sumitomo Metal Ind | Tubo de acero sin costura para pozos petroliferos y procedimiento para fabricarlo |
JP5776377B2 (ja) * | 2011-06-30 | 2015-09-09 | Jfeスチール株式会社 | 耐サワー性に優れたラインパイプ用溶接鋼管向け高強度熱延鋼板およびその製造方法 |
AR096272A1 (es) * | 2013-05-31 | 2015-12-16 | Nippon Steel & Sumitomo Metal Corp | Tubo de acero sin costura para tubería de conducción utilizado en ambientes agrios |
WO2015174424A1 (fr) * | 2014-05-16 | 2015-11-19 | 新日鐵住金株式会社 | Tuyau d'acier sans soudure pour tube de canalisation et procédé pour le produire |
MX2018010456A (es) * | 2016-03-04 | 2019-01-10 | Nippon Steel & Sumitomo Metal Corp | Material de acero y tubo de acero para pozo de petroleo. |
PL3626841T3 (pl) * | 2018-09-20 | 2022-04-04 | Vallourec Tubes France | Rura bezszwowa z mikrostopowej stali o wysokiej wytrzymałości do zastosowań w warunkach kwaśnych i wysokiej wytrzymałości |
-
2021
- 2021-12-01 WO PCT/US2021/072651 patent/WO2022120337A1/fr active Application Filing
- 2021-12-01 US US18/249,502 patent/US20230416884A1/en active Pending
Also Published As
Publication number | Publication date |
---|---|
WO2022120337A1 (fr) | 2022-06-09 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
Rosado et al. | Latest developments in mechanical properties and metallurgical features of high strength line pipe steels | |
EP2287346B1 (fr) | Aciers bainitiques avec bore | |
AU736037B2 (en) | Method for producing ultra-high strength, weldable steels with superior toughness | |
EP3164516B1 (fr) | Procédé de fabrication d'un tôle d'acier revêtu ou non-revêtu à ultra haute résistance et le tôle ainsi obtenu | |
US9187811B2 (en) | Low-carbon chromium steel having reduced vanadium and high corrosion resistance, and methods of manufacturing | |
JP2022177108A (ja) | 少なくとも100mmの厚さを有する鋼セクション及びその製造方法 | |
JP2020500262A (ja) | 低温用中マンガン鋼材及びその製造方法 | |
JPH01230713A (ja) | 耐応力腐食割れ性の優れた高強度高靭性鋼の製造法 | |
JP7221476B2 (ja) | 水素誘起割れ抵抗性に優れた鋼材及びその製造方法 | |
US4533405A (en) | Tubular high strength low alloy steel for oil and gas wells | |
EP3269837B1 (fr) | Acier micro allié et procédé de production dudit acier | |
US5849116A (en) | Production method for steel material and steel pipe having excellent corrosion resistance and weldability | |
JP2023531248A (ja) | 鋼組成物から高強度鋼管を製造する方法およびその鋼管から作られる構成部品 | |
JP2002256380A (ja) | 脆性亀裂伝播停止特性と溶接部特性に優れた厚肉高張力鋼板およびその製造方法 | |
JPH0499128A (ja) | マルテンサイト系ステンレス鋼ラインパイプの製造方法 | |
US20230416884A1 (en) | Linepipe Steel With Alternative Carbon Steel Compositions For Enhanced Sulfide Stress Cracking Resistance | |
US20230392224A1 (en) | Linepipe Steel With Enhanced Sulfide Stress Cracking Resistance | |
US4453986A (en) | Tubular high strength low alloy steel for oil and gas wells | |
Morozov et al. | Obtaining high-quality properties of rolled material for large-diameter pipes based on formation of ferrite-bainite microstructure | |
JP2024501145A (ja) | 鋼組成物、加工品、及び圧縮ガス用の継ぎ目のない圧力容器の製造方法 | |
JPH0967620A (ja) | 脆性亀裂伝播停止特性に優れた調質型高張力鋼板の製造方法 | |
Nastich et al. | Steels with ferrite-bainite microstructure with improved weldability and cold resistance for main pipelines | |
JPH10121131A (ja) | 脆性破壊伝播停止特性と溶接性に優れた厚肉高張力鋼板の製造方法 | |
Rudy et al. | Hardness and impact energy absorbed produced by Q&T steel and DQ&T teel | |
De Moor et al. | Hole expansion properties of quench and partition steels |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: EXXONMOBIL TECHNOLOGY AND ENGINEERING COMPANY, NEW JERSEY Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:THIRUMALAI, NEERAJ S.;JUN, HYUN JO;OZEKCIN, ADNAN;AND OTHERS;SIGNING DATES FROM 20201209 TO 20201211;REEL/FRAME:063366/0512 |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION |