EP0998591A1 - Linepipe and structural steel produced by high speed continuous casting - Google Patents
Linepipe and structural steel produced by high speed continuous castingInfo
- Publication number
- EP0998591A1 EP0998591A1 EP98921241A EP98921241A EP0998591A1 EP 0998591 A1 EP0998591 A1 EP 0998591A1 EP 98921241 A EP98921241 A EP 98921241A EP 98921241 A EP98921241 A EP 98921241A EP 0998591 A1 EP0998591 A1 EP 0998591A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- range
- high strength
- recited
- ksi
- 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.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—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
- C22C38/12—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
Definitions
- the present invention is directed to a high-strength linepipe and structural steel that is resistant to hydrogen-induced cracking (HIC) in sour service.
- HIC hydrogen-induced cracking
- High strength linepipe for this sour service has heretofore been produced from low carbon-manganese steel, and strengthened by the addition of niobium and/or vanadium.
- Manganese levels for such steels have typically been in the range of 0.90 to 1.20 weight percent, when it is expected that the linepipe will be used in the most severe service conditions.
- manganese levels in the aforesaid range of 0.90-1.20 weight percent will be referred to as being "relatively high" manganese contents for low carbon- manganese steels.
- FIG. 1 is a graph depicting the results of a NACE TM0284-96 stepwise cracking test, plotting the weight percent of manganese against the yield strengths of the samples .
- a composition that yields a high-strength, high toughness steel, without relying on the use of a relatively high manganese content to provide the relatively high strength characteristics is provided.
- the manganese content in the steels according to the present invention can be very low, such as 0.15 weight percent or less, thereby virtually eliminating manganese segregation and the tendency of the steel to form manganese sulfide. Further, the low manganese-to-sulfur ratio present in the steels, which is preferably approximately 3,000:1 to 5,000:1, minimizes the tendency of any MnS that may be formed, to form into stringers.
- the steel of the present invention relies on the addition of niobium to provide the high strength characteristics, and, optionally, any one or more of vanadium, molybdenum, chromium, boron, copper and nickel, used in combination with the niobium. These elements combine to lower the austenite-to-ferrite ( ⁇ ) transformation temperature and to prevent the formation of coarse ferrite grains at the very low manganese and carbon levels employed in the steel. The benefits derived from these strengthening mechanisms are enhanced or maximized by water cooling the steel after the strip or plate rolling.
- the steel can be more consistently produced due to the reliance on niobium, and optionally also vanadium, precipitation hardening, and on control of the austenite to ferrite transformation temperature.
- the normally- experienced variations in mechanical properties in coiled product resulting from coiling temperature variations and head-to-tail (leading end to trailing end) temperature variations are minimized or eliminated by the strengthening elements (principally niobium) and mechanisms used in producing this steel.
- the steel of the present invention can be treated with calcium or rare earth metals for sulfide inclusion shape control, as in conventional practice.
- the use of titanium reduces manganese sulfide plasticity, especially at low manganese and nitrogen contents, and when the manganese-to-sulfur ratio is very low, which are both features of the steel of the present invention.
- the very-low carbon and manganese contents in the steel maximize delta ( ⁇ ) ferrite formation during solidification and facilitate solute redistribution. Tolerance for phosphorous impurity is increased and there is a virtual absence of pearlite banding.
- the steels can be rolled on plate mills or strip mills using either direct hot charging or conventional reheating practices
- compositional range is as follows:
- Steels having compositions within the ranges set forth above can be cast at high casting speeds, in the range of 0.8 to 3.0 m/min, that are desired for production efficiency, by conventional (200 to 300 mm thick) or thin (50-90 mm thick) slab caster.
- the steels cast at such high speeds exhibit low segregation intensity, and, as noted previously, high strength, high toughness, and resistance to degradation or failure in sour service applications.
- the steels of the present invention have the notable advantage of providing excellent resistance to stepwise cracking and sulfide stress cracking even when calcium and/or copper are not employed in the steel.
- the high strength properties can be obtained in the absence of molybdenum.
- molybdenum is present within the stated range, the high strength and excellent resistance to stepwise cracking and sulfide stress corrosion cracking can be obtained in the absence of calcium.
- Table VI presents data from drop weight tear testing, as well as the 50% and 85% values for brittle/ductile fracture transition temperatures as demonstrated in the Charpy V-notch impact tests and in the drop weight tear tests (DWTT) . Again, the steels demonstrate excellent notch toughness characteristics with the pipe made from Heat B demonstrating truly outstanding results.
- the yield strengths and ultimate tensile strengths of tensile specimens from heats A-D, as well as from heats E-G, are reported in Table VII below.
- the desired range for yield strength is about 36-80 ksi, and the desired range of ultimate tensile strengths is 45-90 ksi.
- These would be considered as high-strength steels, as the term "high strength" is used herein. Since the higher strength steels can be more susceptible to hydrogen- induced cracking, a more preferred range of yield strengths is about 36-70 ksi, and a more preferred range of ultimate tensile strengths is 45-75 ksi. As can be seen, most of steels A-G fall within the preferred range.
- Resistance to sulfide stress cracking is normally assessed, in accordance with the level of skill in the art , by the test methods set forth in NACE Standard TM0177.
- tests were conducted on heats E-G in accordance with this NACE standard, modified to include a test period of 96 hours at 80% percent of the specified minimum yield strength (SMYS) . No cracking was evidenced in these tests, indicating an acceptable level of resistance to sulfide stress cracking. It is notable that these heats tested for resistance to sulfide stress cracking had manganese contents toward the upper end of the range of manganese content desired for the present invention. It is expected that steels having lower manganese contents, in the more preferred range set forth in Table III above, will exhibit the same or even an improved level of resistance to sulfide stress cracking.
- FIG. 1 presents, in graphical form, a summary of the results of those tests, plotting the manganese content of the steels against their yield strength (in ksi) . It can be seen from that graph that steels having higher manganese contents and steels having yield strengths approaching and exceeding 70 ksi are susceptible to stepwise cracking. This figure substantiates that the increased strength resulting from the use of higher levels of manganese comes at a price, namely, the increased susceptibility to stepwise cracking.
- compositions are those having a manganese content in the range of about 0.10-0.60 wt.% and having a yield strength in the range of about 55-70 ksi. Steels meeting those criteria fall within the shaded region of FIG. 1. Because steels having both 0.60 wt.% manganese and a yield strength of 70 ksi would fall close to the crack/no crack boundary 100, a more conservative set of criteria would include a decreasing maximum yield strength from 70 ksi to 68 ksi maximum as the manganese content increases from 0.50 wt.% to 0.60 wt.%.
- FIG. 1 results presented in FIG. 1 are based on tests conducted using the Solution A (pH 5.2) standard test solution defined in NACE TM 0284-96. Additional tests were conducted in accordance with the standard, but using the lower pH, more severely corrosive, Solution B defined in the standard. Samples from heats A-D, as well as four other samples falling within the steel composition of the present invention, were tested using Solution B in the NACE test, and all samples passed the test, demonstrating a complete absence of stepwise cracking, even under these more severely corrosive conditions.
- Solution A pH 5.2
- API The American Petroleum Institute
- API Specification 5LX is directed to high-strength welded or seamless steel line pipe for oil or gas transmission, a use for which the steel of the present invention is especially well suited.
- API 5LX is hereby incorporated by reference in its entirety. Included in API 5LX are several material grades, such as X46, X52, X56, X60, X65 and X70. The numbers following the "X" in these designations are the minimum yield strengths (in ksi) for materials of the respective grades. Each material grade further has certain compositional requirements and tensile strength requirements .
- the API 5LX material grades are specified when alloy steel pipe is to be used in gas or sour gas service.
- Steels of the present invention having compositions falling within the ranges set forth in Table I meet all compositional limitations set forth in API 5LX, and, as can be seen by the yield strength results set forth in Table VII, steels can be produced to meet the requirements of all grades up through the X70 grade. Accordingly, the steels made in accordance with the present invention can be used as line pipe virtually across the entire spectrum of the API 5LX linepipe specification. Further, with the demonstrated increased resistance to hydrogen-induced cracking over steels currently supplied under the 5LX specification, the steels of the present invention will be especially well suited for use as 5LX linepipe (e.g. X52) in instances where, in addition to the material grade specification, requirements for resistance to hydrogen-induced cracking are specified or imposed.
- 5LX linepipe e.g. X52
- the low carbon/low manganese steels of the present invention possess the desirable properties for use in linepipe applications, especially in sour gas service. Because of its high strength and toughness, the steel is also well suited to being used as structural steel.
- the particular embodiments and compositions discussed above are for illustrative purposes, and the invention is not intended to be limited to specific examples. Modifications may become readily apparent to those of ordinary skill in the art upon reviewing the foregoing specification, without departing from the spirit and scope of the invention. Accordingly, reference should be made to the appended claims to determine the scope of the invention.
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)
- Heat Treatment Of Articles (AREA)
- Treatment Of Steel In Its Molten State (AREA)
- Rigid Pipes And Flexible Pipes (AREA)
Abstract
Description
Claims
Applications Claiming Priority (7)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US4694197P | 1997-05-19 | 1997-05-19 | |
US46941P | 1997-05-19 | ||
US4869497P | 1997-06-06 | 1997-06-06 | |
US48694P | 1997-06-06 | ||
US879331 | 1997-06-20 | ||
US08/879,331 US5993570A (en) | 1997-06-20 | 1997-06-20 | Linepipe and structural steel produced by high speed continuous casting |
PCT/US1998/010034 WO1998053110A1 (en) | 1997-05-19 | 1998-05-15 | Linepipe and structural steel produced by high speed continuous casting |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0998591A1 true EP0998591A1 (en) | 2000-05-10 |
EP0998591B1 EP0998591B1 (en) | 2006-03-29 |
Family
ID=27367024
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98921241A Expired - Lifetime EP0998591B1 (en) | 1997-05-19 | 1998-05-15 | Linepipe and structural steel produced by high speed continuous casting |
Country Status (8)
Country | Link |
---|---|
EP (1) | EP0998591B1 (en) |
JP (1) | JP2002515093A (en) |
KR (1) | KR100540686B1 (en) |
AT (1) | ATE321897T1 (en) |
BR (1) | BR9809852A (en) |
CA (1) | CA2289084C (en) |
DE (1) | DE69834031T2 (en) |
WO (1) | WO1998053110A1 (en) |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100584748B1 (en) * | 2001-12-22 | 2006-05-30 | 주식회사 포스코 | Continuous Cast Steel Slab for Linepipe with Superior Hydrogen Induced Crack Resistance |
JP4613579B2 (en) * | 2004-10-25 | 2011-01-19 | Jfeスチール株式会社 | Steel casting method |
WO2006086853A1 (en) * | 2005-02-21 | 2006-08-24 | Bluescope Steel Limited | Linepipe steel |
AU2006214807B2 (en) * | 2005-02-21 | 2011-11-03 | Bluescope Steel Limited | Linepipe steel |
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 |
KR101174970B1 (en) | 2010-02-26 | 2012-08-23 | 현대제철 주식회사 | High strength linepipe steel and method of manufacturing the steel |
US11656169B2 (en) * | 2021-03-19 | 2023-05-23 | Saudi Arabian Oil Company | Development of control samples to enhance the accuracy of HIC testing |
US11788951B2 (en) | 2021-03-19 | 2023-10-17 | Saudi Arabian Oil Company | Testing method to evaluate cold forming effects on carbon steel susceptibility to hydrogen induced cracking (HIC) |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5980752A (en) * | 1982-10-28 | 1984-05-10 | Nippon Kokan Kk <Nkk> | Steel material having superior resistance to cracking due to hydrogen embrittlement in hydrogen sulfide environment |
JP2655911B2 (en) * | 1989-04-07 | 1997-09-24 | 川崎製鉄株式会社 | Linepipe steel with excellent hydrogen-induced cracking resistance and sulfide stress corrosion cracking resistance |
JP2870830B2 (en) * | 1989-07-31 | 1999-03-17 | 日本鋼管株式会社 | Method for producing high tensile strength and high toughness steel sheet excellent in HIC resistance |
JPH0681034A (en) * | 1992-08-31 | 1994-03-22 | Sumitomo Metal Ind Ltd | Production of hot rolled steel strip for steel pipe excellent in hic resistance |
JPH06220577A (en) * | 1993-01-26 | 1994-08-09 | Kawasaki Steel Corp | High tensile strength steel excellent in hic resistance and its production |
JP2770718B2 (en) * | 1993-09-03 | 1998-07-02 | 住友金属工業株式会社 | High strength hot rolled steel strip excellent in HIC resistance and method for producing the same |
-
1998
- 1998-05-15 KR KR1019997010184A patent/KR100540686B1/en not_active IP Right Cessation
- 1998-05-15 WO PCT/US1998/010034 patent/WO1998053110A1/en active IP Right Grant
- 1998-05-15 DE DE69834031T patent/DE69834031T2/en not_active Expired - Lifetime
- 1998-05-15 JP JP55047298A patent/JP2002515093A/en active Pending
- 1998-05-15 CA CA002289084A patent/CA2289084C/en not_active Expired - Fee Related
- 1998-05-15 BR BR9809852-7A patent/BR9809852A/en not_active IP Right Cessation
- 1998-05-15 AT AT98921241T patent/ATE321897T1/en active
- 1998-05-15 EP EP98921241A patent/EP0998591B1/en not_active Expired - Lifetime
Non-Patent Citations (1)
Title |
---|
See references of WO9853110A1 * |
Also Published As
Publication number | Publication date |
---|---|
KR20010012235A (en) | 2001-02-15 |
DE69834031D1 (en) | 2006-05-18 |
BR9809852A (en) | 2000-06-27 |
EP0998591B1 (en) | 2006-03-29 |
JP2002515093A (en) | 2002-05-21 |
CA2289084C (en) | 2007-03-13 |
KR100540686B1 (en) | 2006-01-10 |
CA2289084A1 (en) | 1998-11-26 |
ATE321897T1 (en) | 2006-04-15 |
DE69834031T2 (en) | 2007-01-11 |
WO1998053110A1 (en) | 1998-11-26 |
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