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US20170349982A1 - Steel material and expandable oil country tubular goods - Google Patents

Steel material and expandable oil country tubular goods Download PDF

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US20170349982A1
US20170349982A1 US15/513,224 US201515513224A US2017349982A1 US 20170349982 A1 US20170349982 A1 US 20170349982A1 US 201515513224 A US201515513224 A US 201515513224A US 2017349982 A1 US2017349982 A1 US 2017349982A1
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steel material
content
tubular goods
country tubular
oil country
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Kenji Kobayashi
Yusaku Tomio
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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Publication of US20170349982A1 publication Critical patent/US20170349982A1/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/002—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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a steel material and expandable oil country tubular goods, and more particularly, to a steel material excellent in pipe expendability and sulfide stress cracking resistance, which is used in oil well and gas well environments and the like environments containing hydrogen sulfide (H 2 S) and expandable oil country tubular goods using the same.
  • H 2 S hydrogen sulfide
  • oil wells In drilling of oil wells and gas wells (hereinafter, collectively referred to simply as “oil wells”), a general method employed is to insert and bury casings after a drill hole reaches a predetermined depth in order to prevent a well wall from collapsing. Furthermore, the operation of inserting casings having smaller outside diameter one by one is repeated while performing the drilling. Therefore, conventionally, in the case where it is necessary to perform drilling up to a large depth, a drilling area of the oil well in a stratum-near-surface portion becomes larger in an outside-diameter direction because of the increase in the number of times a casing is inserted, which increases drilling cost and construction period, and is thus economically disadvantageous.
  • SSC sulfide stress cracking
  • casings are exposed to a corrosive environment after it is subjected to working for expansion without being subjected to heat treatment or the like. Therefore, a material used for casings has to be excellent in expandability and also in corrosion resistance after cold working.
  • Patent Documents 1 to 3 propose materials that are excellent in expansion capability and corrosion resistance.
  • Patent Document 1 JP2008-202128A
  • Patent Document 2 JP2002-266055A
  • Patent Document 3 JP2006-9078A
  • Patent Documents 1 and 2 disclose steel pipes that are excellent in SSC resistance but have room for improvement because no examination is made about uniform elongation.
  • Patent Document 3 discloses the value of uniform elongation. The value, however, indicates a result which is 21% or less. In addition, no examination has been made about SSC resistance.
  • An objective of the present invention is to provide a steel material that has a high expandability, is excellent in SSC resistance after cold working and moreover has a high economic efficiency, and expandable oil country tubular goods using the same.
  • the present inventors examined the chemical composition of a steel material that satisfies the above-described conditions. As the result, the present inventors came to obtain the following findings.
  • (A) In order to assure a high SSC resistance and uniform elongation, it is effective to contain Mn and C, which are austenite stabilizing elements. In particular, it is effective to contain a large amount of Mn.
  • An austenitic structure has a high resistance to SSC, and if the contents of C and Mn are properly selected, the austenitic structure is stable in cold working and difficult to cause strain induced martensitic transformation. Therefore, the occurrence of SSC, which is likely to occur in the presence of a BCC (body-centered cubic) micro-structure, can be suppressed.
  • (B) Mn has a problem in that it brings about the deterioration in general corrosion resistance in wet hydrogen sulfide environments.
  • the deterioration of general corrosion resistance can be suppressed by containing Cu in a steel material.
  • the present invention has been accomplished on the basis of the above-described findings, and involves a steel material and expandable oil country tubular goods described below.
  • Mn more than 25.0% and 45.0% or less
  • a metal micro-structure is consisting of an austenite single phase
  • a yield strength is 241 MPa or higher, and a uniform elongation is 40% or higher;
  • the symbol of an element in the formula represents the content (mass %) of the element contained in the steel material, and is made zero in the case where the element is not contained.
  • Ni 0.1 to 1.5%.
  • Ta 0.005 to 0.5%
  • Expandable oil country tubular goods which are comprised of the steel material according to any one of (1) to (4).
  • the steel material according to the present invention can be used suitably for expandable oil country tubular goods in wet hydrogen sulfide environments.
  • FIG. 1 is a graph showing the relationship between Mn content and uniform elongation.
  • FIG. 2 is a graph showing the relationship between Cu content and corrosion rate.
  • Carbon (C) has an effect of stabilizing austenite phase at a low cost even if the content of Mn or Ni is reduced, and also can improve the work hardening property and uniform elongation by means of promotion of plastic deformation by twinning, so that C is a very important element in the present invention. Therefore, 0.6% or more of C has to be contained.
  • the C content is set to 1.8% or less.
  • the C content is preferably more than 0.65%, further preferably 0.7% or more. Also, the C content is preferably 1.6% or less, further preferably 1.4% or less.
  • Silicon (Si) is an element necessary for deoxidation of steel. If the content of Si is less than 0.05%, the deoxidation is insufficient and many nonmetallic inclusions remain, and therefore desired SSC resistance cannot be achieved. On the other hand, if the content of Si is more than 1.00%, the grain boundary strength is weakened, and the SSC resistance is decreased. Therefore, the content of Si is set to 0.05 to 1.00%.
  • the Si content is preferably 0.10% or more, further preferably 0.20% or more. Also, the Si content is preferably 0.80% or less, further preferably 0.60% or less.
  • Mn More than 25.0% and 45.0% or Less
  • Manganese (Mn) is an element capable of stabilizing austenite phase at a low cost and important element to assure high uniform elongation. In order to exert the effects, more than 25.0% of Mn has to be contained. On the other hand, Mn dissolves preferentially in wet hydrogen sulfide environments, and stable corrosion products are not formed on the surface of material. As a result, the general corrosion resistance is deteriorated with the increase in the Mn content. In the present invention, if more than 45.0% of Mn is contained, even though a fixed amount or more of Cu is contained, the corrosion rate becomes higher than the standard corrosion rate of low-alloy oil well pipe. Therefore, the Mn content has to be set to 45.0% or less. The Mn content is preferably 40.0% or less.
  • the “standard corrosion rate of low-alloy oil well pipe” means a corrosion rate converted from the corrosion loss at the time when a steel is immersed in solution A (5% NaCl+0.5% CH 3 COOH aqueous solution, 1-bar H 2 S saturated) specified in NACE TM0177-2005 for 336 h, being 1.5 g/(m 2 ⁇ h).
  • Aluminum (Al) is an element necessary for deoxidation of steel, and therefore 0.003% or more of Al has to be contained. However, if the content of Al is more than 0.06%, oxides are liable to be mixed in as inclusions, and the oxides may exert an adverse influence on the toughness and corrosion resistance. Therefore, the Al content is set to 0.003 to 0.06%.
  • the Al content is preferably 0.008% or more, further preferably 0.012% or more. Also, the Al content is preferably 0.05% or less, further preferably 0.04% or less.
  • Al means acid-soluble Al (sol.Al).
  • Phosphorus (P) is an element existing unavoidably in steel as an impurity. However, if the content of P is more than 0.03%, P segregates at grain boundaries, and deteriorates the SSC resistance. Therefore, the content of P has to be set to 0.03% or less.
  • the P content is desirably as low as possible, being preferably 0.02% or less, further preferably 0.012% or less. However, an excessive decrease in the P content leads to a rise in production cost of steel material. Therefore, the lower limit of the P content is preferably 0.001%, further preferably 0.005%.
  • S Sulfur
  • the S content is desirably as low as possible, being preferably 0.015% or less, further preferably 0.01% or less.
  • the lower limit of the S content is preferably 0.001%, further preferably 0.002%.
  • Copper (Cu) is an element that promotes local corrosion, and is liable to form a stress concentrating zone on the surface of steel material, in the case where the Mn content of the steel material is low.
  • Cu has an effect of suppressing the corrosion by forming sulfides on the surface of material in wet hydrogen sulfide environments.
  • the Mn content is high and the increase of a corrosion rate can be easily induced 0.5% or more of Cu has to be contained.
  • the content of Cu is set to 3.0% or less.
  • the Cu content is preferably 0.6% or more, further preferably 0.7% or more.
  • the Cu content is preferably 2.5% or less, more preferably 2.0% or less, further preferably 1.5% or less.
  • Vanadium (V) may be contained as necessary because it is an element that strengthen the steel material by performing heat treatment at an appropriate temperature and time and precipitating fine carbides (V 4 C 3 ) in the steel.
  • V Vanadium
  • the V content is preferably 1.8% or less, more preferably 1.6% or less.
  • the productivity may be reduced with the increase in the V content.
  • the V content is further preferably less than 0.5%. In the case where it is desired to achieve the above-described effect, the V content is preferably set to 0.03% or more.
  • N Nitrogen
  • N is usually handled as an impurity element in iron and steel materials, and is decreased by denitrification. Since N is an element for stabilizing austenite phase, a large amount of N may be contained to stabilize austenite. However, since the present invention intends to stabilize austenite by means of C and Mn, N need not be contained positively. Also, if N is contained excessively, the high-temperature strength is raised, the work stress at high temperatures is increased, and the hot workability is deteriorated. Therefore, the content of N has to be set to 0.10% or less. From the viewpoint of refining cost, denitrification need not be accomplished unnecessarily, so that the lower limit of the N content is preferably 0.0015%.
  • Chromium (Cr) may be contained as necessary because it is an element for improving the general corrosion resistance. However, if the content of Cr is more than 3.0%, Cr segregates at grain boundaries, and thereby the SSC resistance is deteriorated. Therefore, the content of Cr, if being contained, is set to 3.0% or less. As described above, in the present invention, a corrosion is promoted by the increase in the Mn content and the corrosion is suppressed by forming Cu sulfides. Therefore, Cr need not be contained positively, and the Cr content is preferably less than 1.0%. In the case where it is desired to achieve the above-described effect, the Cr content is preferably set to 0.1% or more, further preferably set to 0.2% or more, and still further preferably set to 0.5% or more.
  • Molybdenum (Mo) may be contained as necessary because it is an element having an effect of suppressing the corrosion by forming sulfides on the surface of material in wet hydrogen sulfide environments in the case where a corrosion rate of parent phase of the steel material is high as is the case with Cu.
  • Mo since the effect of Mo is small compared to that of Cu and also Mo is very expensive element, Mo should not be contained excessively. If the content of Mo is more than 3.0%, the effect is saturated and economic efficiency is deteriorated. Therefore, the content of Mo, if being contained, is set to 3.0% or less.
  • the Mo content is preferably set to 0.1% or more, further preferably set to 0.2% or more, and still further preferably set to 0.5% or more.
  • Nickel (Ni) may be contained as necessary because it is an element capable of stabilizing austenite phase as is the case with Cu and having an effect of suppressing cracks during hot rolling that sometimes occur in Cu containing steel.
  • Ni is an element that promotes local corrosion, and is liable to form a stress concentrating zone on the surface of steel material. Therefore, if Ni is contained excessively, the SSC resistance may be deteriorated. For this reason, the content of Ni, if being contained, is set to 1.5% or less. The effect of suppressing the cracks can be obtained even by a small amount, and the Ni content is preferably set to 0.1% or more, further preferably set to 0.2% or more.
  • Niobium (Nb), tantalum (Ta), titanium (Ti) and zirconium (Zr) may be contained as necessary because these are elements that contribute to the strength of the steel by combining with C or N to form micro carbides or carbonitrides.
  • the steel material can be strengthened by precipitation strengthening during aging heat treatment when the elements having abilities to form carbides and carbonitrides are contained.
  • the content of each element is 0.5% or less and preferably 0.35% or less.
  • the content of one or more elements selected from these elements is preferably 0.005% or more, further preferably 0.1% or more.
  • Calcium (Ca) and magnesium (Mg) may be contained as necessary because these are elements that have effects to improve toughness and corrosion resistance by controlling the form of inclusions, and further enhance casting properties by suppressing nozzle clogging during casting. However, if these elements are contained excessively, the effects are saturated and the inclusions are liable to be clustered to deteriorate toughness and corrosion resistance. Therefore, the content of each element is 0.005% or less. The content of each element is preferably 0.003% or less. In order to obtain the effect, the content of one or two elements from these elements is preferably 0.0003% or more, further preferably 0.0005% or more.
  • Rare earth metal may be contained as necessary because these are elements that have effects to improve toughness and corrosion resistance by controlling the form of inclusions as is the case with Ca and Mg.
  • the content of REM is 0.01% or less.
  • the REM content is preferably 0.005% or less.
  • the REM content is preferably 0.001% or more, further preferably 0.002% or more.
  • REM is the general term of a total of 17 elements consisting of Sc (scandium), Y (yttrium), and lanthanoids, and the REM content means the total content of one or more elements from the 17 elements.
  • the total content of these elements is preferable 0.008% or less.
  • B Boron
  • B Boron
  • B may be contained as necessary because this is an element that has effects to refine the precipitates and the austenite grain size.
  • B is contained excessively, low-melting-point compounds may be formed to deteriorate hot workability.
  • the B content is more than 0.015%, the hot workability may be deteriorated remarkably. Therefore, the B content is 0.015% or less.
  • the B content is preferably 0.0001% or more.
  • the steel material of the present invention has the chemical composition consisting of the above-described elements ranging from C to B, the balance being Fe and impurities.
  • impurities means components that are mixed in on account of various factors in the production process including raw materials such as ore and scrap when the steel is produced on an industrial basis, which components are allowed in the range in which the components does not exert an adverse influence on the present invention.
  • the C content is regulated within the above-described range in order to stabilize an austenite phase
  • a steel material is strengthened by precipitating V carbides
  • V carbides are all V 4 C 3
  • an effective amount of C that contributes to the stabilization of austenite is expressed by C ⁇ 0.18V as shown in the formula (i), and it is necessary to adjust the contents of C and V such that the effective amount of C exceeds 0.6.
  • an effective amount of C of 1.44 or more poses problems of the inhomogeneity of a micro-structure and the deterioration in hot workability with the formation of cementite, and it is necessary to adjust the contents of C and V such that the effective amount of C is less than 1.44.
  • the effective amount of C is preferably 0.65 or more, more preferably, 0.7 or more.
  • the effective amount of C is preferably 1.4 or less, more preferably, 1.3 or less.
  • the metal micro-structure is made an austenite single phase, which has an FCC (face-centered cubic) structure.
  • the volume amounts of the fearite and the ⁇ ′ martensite having BCC structures are measured and evaluated using a ferrite meter made by Helmut Fischer (model number FE8e3).
  • the steel material according to the present invention has a yield strength of 241 MPa or higher.
  • the yield strength of a steel material is lower than 862 MPa.
  • the yield strength of the steel material is lower than 758 MPa, and more desirably, lower than 654 MPa.
  • the steel material according to the present invention has to have a high uniform elongation in order to assure a good expandability.
  • a pipe expansion rate is about 25%, but it is practically desirable that the material shows a sufficient elongation after being subjected to cold working of 25%. Therefore, the steel material of the present invention has a uniform elongation of 40% or higher.
  • the uniform elongation of a steel material generally tends to be in inverse proportion to the yield strength thereof. Therefore, for a steel material having a low yield strength, it is desirable to have a higher uniform elongation corresponding to the yield strength. Therefore, the steel material according to the present invention desirably satisfies the following formula (ii).
  • uEl means the uniform elongation (%) of the steel material
  • YS means the yield strength (MPa) thereof.
  • the yield strength is less than 500 MPa
  • steel pipes having been subjected to solid solution heat treatment are strengthened by cold working in advance before shipment, and it is therefore desirable to satisfy the formula (ii).
  • the steel material according to the present invention is excellent in expandability and, in addition, has a feature that the corrosion resistance thereof does not deteriorate after expansion even without being subjected to heat treatment. Therefore, the steel material according to the present invention is suitable to be used as expandable oil country tubular goods.
  • the kind of the tubular goods is not specifically limited, and a seamless steel pipe, an electric resistance welded steel tube, an are welded steel pipe, or the like can be used.
  • the steel material according to the present invention has characteristics of being considerably hardened by working. Therefore, in the case of expanding a steel pipe having variations in thickness, a thin portion is first expanded to be hardened, and the further elongation thereof is restricted. A thick portion is then expanded, and the steel pipe is uniformly expanded as a consequence. Therefore, the steel material according to the present invention can be suitably used for seamless steel pipes. In addition, it is more desirable that seamless steel pipes include no weld zone to stably exhibit a good SSC resistance.
  • the steel material according to the present invention can be manufactured, for example, by the method described below, but the method is not subject to any special restriction.
  • a method carried out in the method for producing general austenitic steel materials can be employed, and either ingot casting or continuous casting can be used.
  • a steel may be cast into a round billet form for pipe making by round continuous casting.
  • hot working such as forging, piercing, and rolling is performed.
  • a circular billet is cast by the round continuous casting, processes of forging, blooming, and the like for forming the circular billet are unnecessary.
  • rolling is performed by using a mandrel mill or a plug mill.
  • the process is such that, after a slab has been rough-rolled, finish rolling is performed.
  • the desirable conditions of hot working such as piercing and rolling are as described below.
  • the heating of billet may be performed to a degree such that hot piercing can be performed on a piercing-rolling mill; however, the desirable temperature range is 1000 to 1250° C.
  • the piercing-rolling and the rolling using a mill such as a mandrel mill or a plug mill are also not subject to any special restriction.
  • the upper limit of finishing temperature is also not subject to any special restriction; however, the finishing temperature is preferably lower than 1100° C.
  • the heating temperature of a slab or the like is enough to be in a temperature range in which hot rolling can be performed, for example, in the temperature range of 1000 to 1250° C.
  • the pass schedule of hot rolling is optional.
  • the finishing temperature is preferably lower than 1100° C. as in the case of seamless steel pipe.
  • the steel material having been hot-worked is heated to a temperature enough for carbides and the like to be dissolved completely, and thereafter is rapidly cooled.
  • the steel material be rapidly cooled after being held in the temperature range of 1000 to 1200° C. for 10 min or longer. That is, if the heating temperature is lower than 1000° C., carbides, especially Cr—Mo based carbides in the case where Cr and Mo are contained, cannot be dissolved completely. Therefore, a Cr and Mo deficient layer is formed around the Cr—Mo based carbide, and stress corrosion cracking caused by the occurrence of pitting occurs, so that in some cases, desired SSC resistance cannot be achieved.
  • the heating temperature is higher than 1200° C.
  • a heterogeneous phase of ferrite and the like is precipitated, so that in some cases, desired SSC resistance cannot be achieved.
  • the holding time is shorter than 10 min, the effect of solutionizing is insufficient, and thereby carbides cannot be dissolved completely. Therefore, in some cases, desired SSC resistance cannot be achieved for the same reason as that in the case where the heating temperature is lower than 1000° C.
  • the upper limit of the holding time depends on the size and shape of steel material, and cannot be determined unconditionally. Therefore, the time for soaking the whole of steel material is necessary. From the viewpoint of reducing the production cost, too long time is undesirable, and it is proper to usually set the time within 1 h. Also, concerning cooling, to prevent carbides (cementite or Cr—Mo based carbides) during cooling, other intermetallic compounds, and the like from precipitating, the steel material is desirably cooled at a cooling rate higher than the oil cooling rate.
  • the above-described lower limit value of the holding time is holding time in the case where the steel material is reheated to the temperature range of 1000 to 1200° C. after the steel material having been hot-worked has been cooled once to a temperature lower than 1000° C.
  • the finish temperature of hot working finishing temperature
  • supplemental heating is performed at that temperature for 5 min or longer, so that rapid cooling can be performed as it is without reheating. Therefore, the lower limit value of the holding time in the present invention includes the case where the finish temperature of hot working (finishing temperature) is made in the range of 1000 to 1200° C., and supplemental heating is performed at that temperature for 5 min or longer.
  • aging heat treatment can be performed with the purpose of precipitation strengthening by mainly precipitating carbides and carbonitrides.
  • it is effective in the case where one or more elements selected from V, Nb, Ta, Ti and Zr is contained.
  • exceeding aging heat treatment induces formation of excess carbides and reduce C concentration in parent phase to lead destabilization of austenite.
  • it is preferable to heat the steel material about several ten min to several h at the temperature range of 600 to 800° C.
  • Cold working may be performed as necessary for the steel material having been subjected to solid solution heat treatment or further aging beat treatment.
  • a working ratio reduction of area
  • a working ratio is not subject to any special restriction but, in particular, in order to obtain a yield strength of 400 MPa or higher and lower than 862 MPa, it is preferable to make the working ratio about 10%.
  • a working ratio is preferably set to 25% or less, in order to assure high expandability. Excessively high working ratio makes it difficult to expand the tubular goods uniformly in the oil wells because a uniform elongation is reduced and a strength is enhanced.
  • the cold working method is not subject to any special restriction as far as the steel material can be worked evenly by the method.
  • the steel material is a steel pipe
  • a cold rolling mill called a cold Pilger rolling mill, or the like.
  • the steel material is a plate material
  • annealing can be performed.
  • annealing can be applied with a view to reducing a strength when the excess strength is obtained by the cold working, and recovering an elongation.
  • test materials Twenty-three kinds of steels of A to P and AA to AG having the chemical compositions given in Table 1 were melted in a 50 kg vacuum furnace to produce ingots. Each of the ingots was heated at 1180° C. for 3 h, and thereafter was forged and cut by electrical discharge cutting-off. Thereafter, the cut ingots were further soaked at 1150° C. for 1 h, and were hot-rolled into plate materials having a thickness of 20 mm. Subsequently, the plate materials were subjected to solid solution heat treatment at 1100° C. for 1 h to obtain test materials (test Nos. 1 to 23). Additionally, test materials produced in the same manner as test Nos. 1 to 23 are further cold-rolled at a working ratio of 10% to obtain strengthened test materials (test Nos. 24 to 46).
  • test material that had a uniform elongation being 40% or higher and satisfying the following formula (ii) in relation to a yield strength was evaluated so that the uniform elongation property is good.
  • Table 2 is indicated required elongation (%) which is higher value of 40% and 70 ⁇ 0.06 ⁇ YS.
  • uEl means the uniform elongation (%) of the steel material
  • YS means the yield strength (MPa) thereof.
  • the SSC resistance was evaluated as described below.
  • a plate-shaped smooth test specimen was sampled, and a stress corresponding to 90% of yield stress was applied to one surface of the test specimen by four-point bending method. Thereafter, the test specimen was immersed in a test solution, that is, solution A (5% NaCl+0.5% CH 3 COOH aqueous solution, 1-bar H 2 S saturated) specified in NACE TM0177-2005, and was held at 24° C. for 336 h. Subsequently, it was judged whether or not rupture occurred. As the result, a not-ruptured steel material was evaluated so that the SSC resistance is good (referred to as “ ⁇ ” in Table 2), and a ruptured steel material was evaluated so that the SSC resistance is poor (referred to as “x” in Table 2).
  • the corrosion rate was determined by the method described below.
  • the above-described test material was immersed in the solution A at normal temperature for 336 h, the corrosion loss was determined, and the corrosion loss was converted into the average corrosion rate.
  • the test material that showed the corrosion rate of lower than 1.5 g/(m 2 ⁇ h) was evaluated so that the general corrosion resistance is good.
  • Table 2 shows that for Test Nos. 1 to 16, which are example embodiments of the present invention, a uniform elongation of 60% or higher can be provided and even in the case where the cold working is performed at the working ratio of 25% simulating the expansion, the SSC resistance is excellent, and also the corrosion rate can be kept at lower than 1.5 g/(m 2 ⁇ h).
  • Table 3 shows that for Test Nos. 24 to 39, which are example embodiments of the present invention, a uniform elongation of 47% or higher can be provided in spite of the yield strength of 519 MPa or higher by performing the cold working at the working ratio of 10%, demonstrating that the present steel materials have excellent balance of strength and expendability. Even in the case where the cold working is performed at the working ratio of 25% simulating the expansion, the SSC resistance is excellent, and also the corrosion rate can be kept at lower than 1.5 g/(m 2 h).
  • test result was such that the SSC resistance was poor. Also, for Test Nos. 19 and 42 in which the Cu content was less than the claimed lower limit and Test Nos. 20 and 43 in which the Cr content was more than the claimed upper limit, the test result was such that, although the SSC resistance was good, the corrosion rate was high, and the general corrosion resistance was poor.
  • FIG. 1 is a graph showing the relationships between Mn content and uniform elongation of steels after solid solution heat treatment and after cold working at working ratio of 10%, respectively, for steels A and B satisfying the definition of the present invention and steels AB and AG out of the defined range. These steels have similar chemical composition except for the Mn content. As is apparent from FIG. 1 , the steel material according to the present invention in which the Mn content is more than 25% has high uniform elongation and excellent expandability.
  • FIG. 2 is a graph showing the relationships between Cu content and corrosion rate of steels after solid solution beat treatment and after cold working at working ratio of 10%, respectively, for steels A, C and D satisfying the definition of the present invention and steel AC out of the defined range. These steels have similar chemical composition except for the Cu content. As is apparent from FIG. 2 , for the steel material according to the present invention in which the Cu content is 0.5% or more, the corrosion rate is decreased and the general corrosion resistance is improved.
  • Table 4 demonstrates that for Test Nos. 47 to 49, which are example embodiments of the present invention, a uniform elongation of 40% or higher can be assured while strengthening the steels such that the yield strength is 500 MPa or higher by performing the aging heat treatment for steels that contain V.
  • Test No. 50 which is comparative example, small amount of micro-structure having BCC structure was detected because the effective amount of C was out of the defined range, although the yield strength was 500 MPa or higher due to the aging heat treatment. Consequently the uniform elongation was 34% and the result was such that expandability was poor.
  • the steel material according to the present invention can be used suitably for expandable oil country tubular goods in wet hydrogen sulfide environments.

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