US20100230017A1 - Ultra-High Strength, Corrosion Resistant Wire, a Method of Making Same, and a Method of Using Same - Google Patents

Ultra-High Strength, Corrosion Resistant Wire, a Method of Making Same, and a Method of Using Same Download PDF

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US20100230017A1
US20100230017A1 US12/721,844 US72184410A US2010230017A1 US 20100230017 A1 US20100230017 A1 US 20100230017A1 US 72184410 A US72184410 A US 72184410A US 2010230017 A1 US2010230017 A1 US 2010230017A1
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wire
max
sectional area
temperature
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Richard B. Frank
Lyndon W. Burleson
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    • H—ELECTRICITY
    • H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
    • H05K—PRINTED CIRCUITS; CASINGS OR CONSTRUCTIONAL DETAILS OF ELECTRIC APPARATUS; MANUFACTURE OF ASSEMBLAGES OF ELECTRICAL COMPONENTS
    • H05K9/00—Screening of apparatus or components against electric or magnetic fields
    • H05K9/0073—Shielding materials
    • H05K9/0098—Shielding materials for shielding electrical cables
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/02—Layer formed of wires, e.g. mesh
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/07—Alloys based on nickel or cobalt based on cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/29—Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof
    • Y10T428/2913—Rod, strand, filament or fiber
    • Y10T428/2922—Nonlinear [e.g., crimped, coiled, etc.]
    • Y10T428/2925—Helical or coiled

Definitions

  • This invention generally relates to fine gauge, high strength wire, and in particular, it relates to a wire product that provides a unique combination of very high strength, excellent ductility, and good corrosion resistance for use in armored cable.
  • Armored communication cable has been used for transmission of communication and control signals to equipment operating in oil wells, particularly in deep sour gas wells.
  • One type of armored cable for the oil well application is described in U.S. Pat. No. 6,255,592, the entire disclosure of which is incorporated herein by reference.
  • the armor portion of such cables is made from steel wire that contains a medium to high amount of carbon. It is also known to use stainless steel wire for the armoring portion of armored cable used in oil wells.
  • the wire used for making armored cable sheath is typically used at a tensile strength level of 275-295 ksi. However, the users of such cables are now demanding even higher strength levels for this application.
  • the alloy designated UNS R00035 is a corrosion resistant Ni—Co base alloy that provides a tensile strength of up to about 300 ksi. At least one specification for cable armor requires the use of the UNS R00035 alloy. However, when that alloy is processed to produce wire having a tensile strength in excess of 300 ksi, the alloy lacks sufficient ductility to resist breaking in a standard wire-wrap test. Accordingly, it would be advantageous to produce a corrosion resistant Ni—Co base alloy wire that can be processed to wire form, that provides a tensile strength in excess of 300 ksi, and which also provides sufficient ductility to meet the wire-wrap test.
  • a method of making steel wire includes the step of forming a length of wire from a high strength, corrosion resistant alloy.
  • the alloy preferably has the following composition in weight percent.
  • the wire is annealed at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer. The annealed wire is then drawn such that the cross-sectional area of the wire is reduced by about 50 to 80%.
  • the as-drawn wire is then heat treated at a second combination of temperature and time effective to provide the wire with high strength and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially commensurate with the diameter of the wire and then unwrapped, the wire does not crack or break.
  • a method of making flexible armored cable includes the step of forming a length of wire from an alloy comprising, in weight percent, about
  • the wire is then annealed at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer. The annealed wire is then drawn such that the cross-sectional area of the wire is reduced by about 50 to 80%.
  • the wire is then heat treated at a second combination of temperature and time that is effective to provide the alloy with high strength and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially commensurate with the diameter of the wire and then unwrapped, the wire does not crack or break.
  • the heat treated wire is then helically wound around an elongated core member to form a flexible encasement around the elongated core member.
  • a wire formed from a high strength, corrosion resistant alloy having the following composition in weight percent, about
  • the wire is characterized by a tensile strength in excess of 300 ksi and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially equal to the diameter of the wire and then unwrapped, the wire does not crack or break.
  • the drawing FIGURE is a chart that shows the effects of cold working and aging temperature on the ultimate tensile strength and wrap test performance of high strength wire.
  • the known composition and the known processing of UNS R00035 alloy are modified to provide a wire product having a novel combination of tensile strength and ductility as well as good corrosion resistance.
  • an alloy having the following weight percent composition is melted, refined, and cast into an ingot mold.
  • the process according to this invention is designed to produce a wire product from the alloy which has a fine, recrystallized grain structure prior to cold drawing.
  • a lower annealing temperature preferably about 1750-1850° F. provides a finer grain size (ASTM 6 or finer) which is believed to result in a better combination of strength and ductility even when the alloy is in the cold-worked condition.
  • the annealing step is preferably carried out for about 0.5 to 2 hours.
  • the alloy After solution annealing, the alloy is heavily cold drawn in the range of about 50-80% reduction in cross-sectional area (R.C.S.A.), preferably about 65-75% R.C.S.A. to obtain a tensile strength exceeding about 300 ksi.
  • armoring cable products are then used in the as-cold-drawn condition.
  • Another aspect of this invention is to age-harden the alloy wire at a temperature of 900-1400° F. to improve the overall combination of strength and ductility. In the age-hardened condition, the alloy provides an ultimate tensile strength of at least about 310 ksi together with excellent ductility as demonstrated by the wire's resistance to breaking in the wrap test. Furthermore, it is also believed that overaging the wire at a temperature greater than 1100° F. provides better ductility than the standard aging temperature of 1000-1050° F.
  • the processing steps used to obtain the desired combination of strength and bendability do not appear to adversely affect the corrosion resistance provided by the alloy used to make wire products in accordance with this invention.
  • the corrosion resistance of the wire product is affected by the cleanliness of the wire surface after processing. Therefore, the annealing and aging heat treatments of the wire are preferably carried out under a subatmospheric pressure to substantially avoid oxidation or other contamination of the wire surface.
  • a subatmospheric pressure of less than about 1 torr (130 Pa) is preferred.
  • Triple melting is a known technique that includes the steps of vacuum induction melting (VIM), followed by electroslag remelting (ESR), and then vacuum arc remelting (VAR).
  • VIM vacuum induction melting
  • ESR electroslag remelting
  • VAR vacuum arc remelting
  • Wire samples cut from the annealed coils were cold drawn to 50%, 55%, 60%, 64%, and 67% reductions in cross-sectional area (R.C.S.A.) to provide wire diameters of 0.040 in., 0.038 in., 0.036 in., 0.034 in., and 0.032 in., respectively.
  • Cold drawing is performed with the wire at room (ambient) temperature.
  • the wire samples were then aged at temperatures in the range of 1050° F.-1250° F. in argon-filled SEN/PAK® heat treating containers.
  • Fine wire tensile tests and wrap tests were conducted to determine the strength and ductility of the wire.
  • the wrap test consists of wrapping the wire around its own circumference five times followed by unwrapping. The test sample passes if the wire does not crack or break during wrapping or unwrapping.
  • Example 2 C 0.010 0.008 Mn 0.01 0.01 Si 0.03 0.03 P 0.002 ⁇ 0.001 S 0.002 0.002 Cr 20.75 20.57 Ni 34.76 34.75 Mo 9.53 9.52 Co 33.36 33.86 Cb 0.03 0.06 Al 0.12 — Ti 0.81 0.76 B 0.0096 0.0106 Fe 0.50 0.45 O ⁇ 10 ppm — N 41 ppm 41 ppm
  • Tables II and III below show the results of the room temperature tensile and wrap tests for the cold-drawn and aged fine wire samples including the 0.2% offset yield strength (0.2% Y.S.) and the ultimate tensile strength (U.T.S.) in ksi, the percent elongation (% El.), and the reduction in cross-sectional area (% R.A.). It should be noted that the tensile ductility values are approximate because of the difficulty in measuring the percent elongation and percent reduction in area of fine wire samples.
  • Table IV shows the room-temperature tensile and wrap test results for the aged wire samples with and without the exposures at 500° F. for 24 hours and for 30 days at 500° F.
  • the results presented in Table IV indicate that the simulated well-aged exposures at 500° F. had no detrimental effect on the tensile or wrap properties and, in some cases, the percent reduction in area (% R.A.) values were higher in the well-aged condition.
  • the 500° F. exposures had no adverse effect on the tensile strength (U.T.S.) of aged wire material. An increase of up to about 30 ksi in the U.T.S. was observed for some of the cold-drawn-only wire after the 500° F. exposure.
  • wire from another production heat of the UNS R00035 alloy was processed into fine wire.
  • the heat chemistry of the additional wire material (Example 2) is presented in Table I above.
  • the wire was cold drawn 68% R.C.S.A. to 0.031′′ in diameter.
  • the cold drawn wire was aged at various combinations of temperature and time as shown in Table V.
  • set forth in Table V are the results of room temperature tensile and wrap tests including the 0.2% offset yield strength (0.2% Y.S.) and the ultimate tensile strength (U.T.S.) in ksi, the percent elongation (% El.), the percent reduction in area (% R.A.), together with an indication whether the wire passed or failed the wrap test (Wrap Test).
  • the aging heat treatment given to each test sample is shown in the column labeled “Age Treatment”.
  • Some of the wire samples were given underaging heat treatments at 600° F. and 750° F., respectively, for 4 hours.
  • the underaged samples were evaluated to determine if the desired properties could be achieved.
  • the results for the underaged samples are also shown in Table V.
  • the data presented in Table V confirm that the combination of at least about 325 ksi U.T.S. with acceptable wrap test ductility is obtained for the 68% cold-drawn samples aged at 1250-1325° F., although the most consistent results are obtained when the wire is aged at 1300° F. While two of the underaged samples provided acceptable results, most of the underaged samples did not achieve the desired combination of properties.
  • Table VI shows the results of room temperature tensile and wrap tests including the 0.2% offset yield strength (0.2% Y.S.) and the ultimate tensile tensile strength (U.T.S.) in ksi, the percent elongation (% El.), the percent reduction in area (% R.A.), together with an indication whether the wire passed or failed the wrap test (Wrap Test).
  • the aging heat treatment given to each test sample is shown in the column labeled “Age Treatment”.
  • the data presented in Table VI show that the best combination of properties is obtained by aging at about 1300° F. for 4 hours.
  • Vacuum aging trials of small coils of the 68% cold drawn wire from Example 2 were performed. Small quantities of wire were coiled onto standard production spools so that the mass was comparable to that of a typical production order.
  • the furnace setpoints were reduced to 1275° F. for 2 hours to avoid overheating the wire.
  • the first trial resulted in lower % R.A. and some susceptibility to breakage during handling for subsequent corrosion testing. The wire breakage is believed to be attributable to more severe bending of the wire for the corrosion testing in combination with surface damage from the tool used to bend the wire specimens.
  • a second trial was conducted using the preferred set point of 1300° F. for 4 hours. Table VII shows tensile and wrap test results for the two vacuum aged trials.
  • the present invention may suitably comprise, consist essentially of, or consist of the steps of forming, annealing, drawing, and hardening as described herein.
  • the invention illustratively disclosed herein suitably may be practiced in the absence of any step or parameter which is not specifically disclosed herein.

Abstract

A method of making steel wire is described that includes the step of forming a length of wire from a high strength, corrosion resistant alloy. The alloy preferably has the following composition in weight percent.
Carbon 0.03 max. Manganese 0.15 max. Silicon 0.15 max. Phosphorus 0.015 max. Sulfur 0.010 max. Chromium 19.00-21.00 Nickel 33.00-37.00 Molybdenum  9.00-10.50 Titanium 1.00 max. Boron 0.010 max. Iron 1.00 max.
The balance of the alloy is cobalt and usual impurities. The wire is annealed at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer. The annealed wire is then drawn such that the cross-sectional area of the wire is reduced by about 50 to 80%. The as-drawn wire is then heat treated at a second combination of temperature and time effective to provide the wire with high strength and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially commensurate with the diameter of the wire and then unwrapped it does not crack or break.

Description

    CROSS-REFERENCE TO RELATED APPLICATIONS
  • This application claims the benefit of U.S. Provisional Application No. 61/159,577, filed Mar. 12, 2009, the entirety of which is incorporated herein by reference.
    • BACKGROUND OF THE INVENTION
  • 1. Field of the Invention
  • This invention generally relates to fine gauge, high strength wire, and in particular, it relates to a wire product that provides a unique combination of very high strength, excellent ductility, and good corrosion resistance for use in armored cable.
  • 2. Description of the Related Art
  • Armored communication cable has been used for transmission of communication and control signals to equipment operating in oil wells, particularly in deep sour gas wells. One type of armored cable for the oil well application is described in U.S. Pat. No. 6,255,592, the entire disclosure of which is incorporated herein by reference. Typically, the armor portion of such cables is made from steel wire that contains a medium to high amount of carbon. It is also known to use stainless steel wire for the armoring portion of armored cable used in oil wells. The wire used for making armored cable sheath is typically used at a tensile strength level of 275-295 ksi. However, the users of such cables are now demanding even higher strength levels for this application.
  • The alloy designated UNS R00035 is a corrosion resistant Ni—Co base alloy that provides a tensile strength of up to about 300 ksi. At least one specification for cable armor requires the use of the UNS R00035 alloy. However, when that alloy is processed to produce wire having a tensile strength in excess of 300 ksi, the alloy lacks sufficient ductility to resist breaking in a standard wire-wrap test. Accordingly, it would be advantageous to produce a corrosion resistant Ni—Co base alloy wire that can be processed to wire form, that provides a tensile strength in excess of 300 ksi, and which also provides sufficient ductility to meet the wire-wrap test.
    • SUMMARY OF THE INVENTION
  • In accordance with a first aspect of the present invention there is provided a method of making steel wire. The method according to this invention includes the step of forming a length of wire from a high strength, corrosion resistant alloy. The alloy preferably has the following composition in weight percent.
  •
    Carbon 0.03 max.
    Manganese 0.15 max.
    Silicon 0.15 max.
    Phosphorus 0.015 max.
    Sulfur 0.010 max.
    Chromium 19.00-21.00
    Nickel 33.00-37.00
    Molybdenum  9.00-10.50
    Titanium 1.00 max.
    Boron 0.010 max.
    Iron 1.00 max.

    The balance of the alloy is cobalt and usual impurities. The wire is annealed at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer. The annealed wire is then drawn such that the cross-sectional area of the wire is reduced by about 50 to 80%. The as-drawn wire is then heat treated at a second combination of temperature and time effective to provide the wire with high strength and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially commensurate with the diameter of the wire and then unwrapped, the wire does not crack or break.
  • In accordance with another aspect of the present invention there is provided a method of making flexible armored cable. This method includes the step of forming a length of wire from an alloy comprising, in weight percent, about
  •
    Carbon 0.03 max.
    Manganese 0.15 max.
    Silicon 0.15 max.
    Phosphorus 0.015 max.
    Sulfur 0.010 max.
    Chromium 19.00-21.00
    Nickel 33.00-37.00
    Molybdenum  9.00-10.50
    Titanium 1.00 max.
    Boron 0.010 max.
    Iron 1.00 max.

    The balance of the alloy is cobalt and the usual impurities. The wire is then annealed at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer. The annealed wire is then drawn such that the cross-sectional area of the wire is reduced by about 50 to 80%. The wire is then heat treated at a second combination of temperature and time that is effective to provide the alloy with high strength and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially commensurate with the diameter of the wire and then unwrapped, the wire does not crack or break. The heat treated wire is then helically wound around an elongated core member to form a flexible encasement around the elongated core member.
  • In accordance with a further aspect of the present invention, there is provided a wire formed from a high strength, corrosion resistant alloy having the following composition in weight percent, about
  •
    Carbon 0.03 max.
    Manganese 0.15 max.
    Silicon 0.15 max.
    Phosphorus 0.015 max.
    Sulfur 0.010 max.
    Chromium 19.00-21.00
    Nickel 33.00-37.00
    Molybdenum  9.00-10.50
    Titanium 1.00 max.
    Boron 0.010 max.
    Iron 1.00 max.

    The balance of the alloy is cobalt and the usual impurities. The wire is characterized by a tensile strength in excess of 300 ksi and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially equal to the diameter of the wire and then unwrapped, the wire does not crack or break.
  • Here and throughout this specification the following definitions apply unless otherwise indicated. The term “percent” and the symbol “%” are used in expressing weight percent, mass percent, or percent reduction in cross-sectional area, except as otherwise indicated. ASTM grain size numbers are those determined in accordance with ASTM Standard E112-96 (2004), “Standard Test Methods for Determining Average Grain Size” (DOI: 10.1520/E0112-96R04).
    • BRIEF DESCRIPTION OF THE DRAWING
  • The drawing FIGURE is a chart that shows the effects of cold working and aging temperature on the ultimate tensile strength and wrap test performance of high strength wire.
    •  DETAILED DESCRIPTION
  • In accordance with the present invention, the known composition and the known processing of UNS R00035 alloy are modified to provide a wire product having a novel combination of tensile strength and ductility as well as good corrosion resistance. In accordance with the first step in the process according to this invention, an alloy having the following weight percent composition is melted, refined, and cast into an ingot mold.
  •
    Carbon 0.03 max.
    Manganese 0.15 max.
    Silicon 0.15 max.
    Phosphorus 0.015 max.
    Sulfur 0.010 max.
    Chromium 19.00-21.00
    Nickel 33.00-37.00
    Molybdenum  9.00-10.50
    Titanium 1.00 max.
    Boron 0.010 max.
    Iron 1.00 max.
    Cobalt + Impurities Balance

    The ingot is removed from the mold upon solidification and then mechanically worked into intermediate product forms having progressively smaller cross sections. Processes for melting, casting, and mechanically working the alloy are known and described in U.S. Pat. No. 3,356,542 and U.S. Pat. No. 3,562,042, the entire disclosures of which are incorporated herein by reference. It is believed that a low Ti grade of this alloy, i.e., 0.01% max. Ti, will also provide acceptable results.
  • The process according to this invention is designed to produce a wire product from the alloy which has a fine, recrystallized grain structure prior to cold drawing. Commercial specifications for the UNS R00035 alloy, such as AMS 5844 which relates to bar products, require an annealing treatment at 1900-1925° F. for 4 to 8 hours. That annealing heat treatment provides a medium grain size in the range of ASTM 4 to 6. We have discovered that a lower annealing temperature, preferably about 1750-1850° F. provides a finer grain size (ASTM 6 or finer) which is believed to result in a better combination of strength and ductility even when the alloy is in the cold-worked condition. The annealing step is preferably carried out for about 0.5 to 2 hours. After solution annealing, the alloy is heavily cold drawn in the range of about 50-80% reduction in cross-sectional area (R.C.S.A.), preferably about 65-75% R.C.S.A. to obtain a tensile strength exceeding about 300 ksi. Typically, armoring cable products are then used in the as-cold-drawn condition. Another aspect of this invention is to age-harden the alloy wire at a temperature of 900-1400° F. to improve the overall combination of strength and ductility. In the age-hardened condition, the alloy provides an ultimate tensile strength of at least about 310 ksi together with excellent ductility as demonstrated by the wire's resistance to breaking in the wrap test. Furthermore, it is also believed that overaging the wire at a temperature greater than 1100° F. provides better ductility than the standard aging temperature of 1000-1050° F.
  • The processing steps used to obtain the desired combination of strength and bendability do not appear to adversely affect the corrosion resistance provided by the alloy used to make wire products in accordance with this invention. However, it is believed that the corrosion resistance of the wire product is affected by the cleanliness of the wire surface after processing. Therefore, the annealing and aging heat treatments of the wire are preferably carried out under a subatmospheric pressure to substantially avoid oxidation or other contamination of the wire surface. A subatmospheric pressure of less than about 1 torr (130 Pa) is preferred.
    • WORKING EXAMPLES Example 1
  • Experimental trials were performed using 0.0565 in rd. wire from a triple melted heat having the weight percent composition set forth in Table I below. Triple melting is a known technique that includes the steps of vacuum induction melting (VIM), followed by electroslag remelting (ESR), and then vacuum arc remelting (VAR). The wire was annealed at subatmospheric pressure at 1800° F. for 90 minutes and then quenched in argon gas. The grain size of the annealed wire was about ASTM size 6-8. Wire samples cut from the annealed coils were cold drawn to 50%, 55%, 60%, 64%, and 67% reductions in cross-sectional area (R.C.S.A.) to provide wire diameters of 0.040 in., 0.038 in., 0.036 in., 0.034 in., and 0.032 in., respectively. Cold drawing is performed with the wire at room (ambient) temperature. The wire samples were then aged at temperatures in the range of 1050° F.-1250° F. in argon-filled SEN/PAK® heat treating containers. Fine wire tensile tests and wrap tests were conducted to determine the strength and ductility of the wire. The wrap test consists of wrapping the wire around its own circumference five times followed by unwrapping. The test sample passes if the wire does not crack or break during wrapping or unwrapping.
  • TABLE I
    Element Example 1 Example 2
    C 0.010 0.008
    Mn 0.01 0.01
    Si 0.03 0.03
    P 0.002 <0.001
    S 0.002 0.002
    Cr 20.75 20.57
    Ni 34.76 34.75
    Mo 9.53 9.52
    Co 33.36 33.86
    Cb 0.03 0.06
    Al 0.12 —
    Ti 0.81 0.76
    B 0.0096 0.0106
    Fe 0.50 0.45
    O <10 ppm —
    N  41 ppm 41 ppm
  • Initial results were promising for the greatest cold reduction used (67%) and for the higher aging temperatures. Additional testing was conducted using R.C.S.A.'s of 69%, 73%, and 78% and aging temperatures up to 1350° F. Tables II and III below show the results of the room temperature tensile and wrap tests for the cold-drawn and aged fine wire samples including the 0.2% offset yield strength (0.2% Y.S.) and the ultimate tensile strength (U.T.S.) in ksi, the percent elongation (% El.), and the reduction in cross-sectional area (% R.A.). It should be noted that the tensile ductility values are approximate because of the difficulty in measuring the percent elongation and percent reduction in area of fine wire samples.
  • TABLE II
    Wire % Cold Aging 0.2%
    Diameter Drawn Treatment Y.S. U.T.S. % El. % R.A. Wrap Test
    0.0565 in.  0 None 66 156 50 54 passed
    ″ 0 67 157 48 54
    ″ 0 68 159 48 54
    0.040 in. 50 None 207 268 5 — passed
    ″ 50 ″ 214 269 5 —
    ″ 50 ″ 215 268 5 —
    ″ 50 1050° F./4 h/AC 313 323 3 67 passed
    ″ 50 ″ 305 317 3 67 passed
    ″ 50 ″ 313 323 3 67
    ″ 50 1150° F./4 h/AC 305 309 1 40 passed
    ″ 50 ″ 306 308 1 40 passed
    ″ 50 ″ 305 307 1 32 passed
    ″ 50 1250° F./4 h/AC 279 286 1 32 passed
    ″ 50 ″ 287 290 1 36 passed
    ″ 50 ″ 288 292 1 44 passed
    0.038 in. 55 None 200 279 3 60 passed
    ″ 55 ″ 196 279 3 60
    ″ 55 ″ 198 279 3 60
    ″ 55 1050° F./4 h/AC 317 331 2 45 failed
    ″ 55 ″ 327 340 2 45 failed
    ″ 55 ″ 322 336 2 45
    ″ 55 1150° F./4 h/AC 279 325 1 37 passed
    ″ 55 ″ 285 327 1 41 passed
    ″ 55 ″ 300 327 1 41 passed
    ″ 55 1250° F./4 h/AC 286 301 1 41 passed
    ″ 55 ″ 293 309 1 41 passed
    ″ 55 ″ 308 312 1 37 passed
    0.036 in. 60 None 225 282 4 — passed
    ″ 60 ″ 222 280 4 — passed
    ″ 60 ″ 225 281 4 —
    ″ 60 1050° F./4 h/AC 315 344 2 59 failed
    passed on retest
    ″ 60 ″ 326 345 2 63 passed
    ″ 60 ″ 325 342 2 56
    ″ 60 1150° F./4 h/AC 329 334 1 36 passed
    ″ 60 ″ 315 328 1 36 passed
    ″ 60 ″ 311 327 1 32 passed
    ″ 60 1250° F./4 h/AC 317 322 1 45 passed
    ″ 60 ″ 307 307 1 50 passed
    ″ 60 ″ 307 316 1 54 passed
    ″ 60 ″ 322 333 2 45 passed
    ″ 60 ″ 311 329 2 49
    ″ 60 ″ 331 338 2 31
    0.034 in. 64 None 244 295 4 57 passed
    ″ 64 ″ 252 299 4 57
    ″ 64 ″ 246 295 4 57
    ″ 64 1050° F./4 h/AC 348 360 2 49 did not wrap
    ″ 64 ″ 343 359 2 50 failed
    ″ 64 ″ 349 360 2 50
    ″ 64 1150° F./4 h/AC 302 339 2 50 failed
    ″ 64 ″ 307 341 1 45 passed
    ″ 64 ″ 306 345 1 45 passed
    ″ 64 1250° F./4 h/AC 312 318 2 49 passed
    ″ 64 ″ 311 317 2 53
    ″ 64 ″ 304 311 2 49
    ″ 64 1250° F./4 h/AC 331 335 2 26 passed
    ″ 64 ″ 324 328 1 21 passed
    ″ 64 ″ 324 331 1 26 passed
    ″ 64 1300° F./4 h/AC 325 326 1 26 passed
    ″ 64 ″ 328 331 1 31 passed
    ″ 64 ″ 316 320 1 31 passed
  • TABLE III
    Wire % Cold Aging 0.2%
    Diameter Drawn Treatment Y.S. U.T.S. % El. % R.A. Wrap Test
    0.0325 in. 67 None 273 299 3 — passed
    ″ 67 ″ 264 304 4 —
    ″ 67 ″ 274 306 3 —
    ″ 67 1050° F./4 h/AC 337 358 2 58 did not wrap
    ″ 67 ″ 340 359 2 54 failed
    ″ 67 ″ 335 360 2 58
    ″ 67 1150° F./4 h/AC 346 354 1 50 failed
    ″ 67 ″ 348 357 1 46 failed
    ″ 67 ″ 356 358 1 46 failed
    ″ 67 1200° F./4 h/AC 338 358 1 41 failed
    ″ 67 ″ 351 358 1 46 failed
    ″ 67 ″ 338 346 1 41 failed
    ″ 67 1250° F./4 h/AC 325 342 3 40 passed
    ″ 67 ″ 330 343 2 45
    ″ 67 ″ 307 338 2 54 passed
    ″ 67 ″ 355 358 1 46 passed
    ″ 67 ″ 331 344 1 54 passed
    ″ 67 ″ 312 321 1 46 passed
    ″ 67 1275° F./4 h/AC 343 passed
    ″ 67 ″ 345 passed
    ″ 67 ″ 331 passed
    ″ 67 1300° F./4 h/AC 335 341 1 41 passed
    ″ 67 ″ 327 330 1 36 passed
    ″ 67 ″ 340 342 1 36 passed
    ″ 67 1300° F./4 h/AC 328 332 1 36 passed
    ″ 67 ″ 325 328 1 41 passed
    ″ 67 ″ 336 338 1 31 passed
    ″ 67 1350° F./4 h/AC 227 240 4 66 passed
    ″ 67 227 239 4 66
    ″ 67 226 241 4 62
    0.0316 in. 69 None 278 303 1 47 passed
    ″ 69 1250° F./4 h/AC 356 361 1 27 passed
    ″ 69 ″ 362 364 1 27 failed
    ″ 69 ″ 350 356 1 22 passed
    ″ 69 1275° F./4 h/AC 346 348 1 32 passed
    ″ 69 ″ 339 345 1 22 failed
    on unwrap
    ″ 69 ″ 348 353 1 27 passed
    ″ 69 1300° F./4 h/AC 325 337 1 32 passed
    ″ 69 ″ 321 334 1 27 passed
    ″ 69 ″ 343 347 1 33 passed
    ″ 69 1325° F./4 h/AC 329 334 2 42 passed
    ″ 69 ″ 321 328 1 37 passed
    ″ 69 ″ 315 316 2 37 passed
    ″ 69 1350° F./4 h/AC 223 235 2 47 passed
    ″ 69 ″ 257 266 2 52 passed
    ″ 69 ″ 227 238 2 51 passed
    0.0293 in. 73 None 263 306 1 44 passed
    ″ 73 1150° F./4 h/AC 207 213 1 48 failed
    ″ 73 ″ 205 207 1 49 failed
    ″ 73 ″ 203 213 1 38 failed
    ″ 73 1250° F./4 h/AC 366 370 1 38 failed
    ″ 73 ″ 362 365 1 38 passed
    ″ 73 ″ 358 366 1 38 passed
    ″ 73 1275° F./4 h/AC 328 334 1 48 pass
    ″ 73 ″ 339 341 1 43 pass
    ″ 73 ″ 325 345 1 38 failed
    on unwrap
    ″ 73 1300° F./4 h/AC 352 357 2 43 passed
    ″ 73 ″ 342 353 1 38 passed
    ″ 73 ″ 353 356 1 43 passed
    ″ 73 1325° F./4 h/AC 313 320 2 48 passed
    ″ 73 ″ 293 303 1 38 passed
    ″ 73 ″ 285 292 1 38 passed
    ″ 73 1350° F./4 h/AC 220 234 2 43 passed
    ″ 73 ″ 215 237 2 38 passed
    ″ 73 ″ 189 213 2 43 passed
    0.0263 in. 78 None 286 320 1 53 passed
    ″ 78 1250° F./4 h/AC 350 358 1 53 failed
    ″ 78 ″ 328 346 1 42 failed
    ″ 78 ″ 350 355 1 53 failed
    ″ 78 1275° F./4 h/AC 337 352 1 47 failed
    ″ 78 ″ 332 338 1 42 failed
    ″ 78 ″ 339 343 1 42 failed
    ″ 78 1300° F./4 h/AC 347 362 1 17 passed
    ″ 78 ″ 352 357 1 17 passed
    ″ 78 ″ 358 362 1 30 passed
    ″ 78 1325° F./4 h/AC 314 317 2 53 passed
    ″ 78 ″ 319 320 2 48 passed
    ″ 78 ″ 317 319 2 53 passed
    ″ 78 1350° F./4 h/AC 210 214 10 48 passed
    ″ 78 ″ 182 214 12 48 passed
    ″ 78 ″ 180 213 9 53 passed
  • Some of the aged wire samples representing cold reductions of 67-78% and aging treatments of 1250° F./4 hours and 1300° F./4 hours, respectively, were heated at 500° F. to simulate oil well conditions. Table IV shows the room-temperature tensile and wrap test results for the aged wire samples with and without the exposures at 500° F. for 24 hours and for 30 days at 500° F. The results presented in Table IV indicate that the simulated well-aged exposures at 500° F. had no detrimental effect on the tensile or wrap properties and, in some cases, the percent reduction in area (% R.A.) values were higher in the well-aged condition. The 500° F. exposures had no adverse effect on the tensile strength (U.T.S.) of aged wire material. An increase of up to about 30 ksi in the U.T.S. was observed for some of the cold-drawn-only wire after the 500° F. exposure.
  • TABLE IV
    Wire % Cold Aging 0.2% Wrap
    Diameter Drawn Treatment Exposure Y.S. U.T.S. % El. % R.A. Test
    0.034 in. 64 1250° F./4 h/AC — 331 335 2 26 passed
    ″ 64 1250° F./4 h/AC — 324 328 1 21 passed
    ″ 64 1250° F./4 h/AC — 324 331 1 26 passed
    ″ 64 1250° F./4 h/AC 500° F./30 days 332 334 1 41 passed
    ″ 64 1250° F./4 h/AC 500° F./30 days 328 334 1 36 passed
    ″ 64 1250° F./4 h/AC 500° F./30 days 323 328 1 31 passed
    0.032 in. 67 1250° F./4 h/AC — 355 358 1 46 passed
    ″ 67 1250° F./4 h/AC — 331 344 1 54
    ″ 67 1250° F./4 h/AC — 312 321 1 46
    ″ 67 1250° F./4 h/AC 500° F./30 days 342 352 1 54 passed
    ″ 67 1250° F./4 h/AC 500° F./30 days 335 344 1 54 passed
    ″ 67 1250° F./4 h/AC 500° F./30 days 347 350 1 54 passed
    0.0316 in. 69 None — 278 303 1 47 pass
    ″ 69 None 500° F./24 h 293 327 1 32 pass
    ″ 69 None 500° F./24 h 297 333 2 37 pass
    ″ 69 None 500° F./24 h 302 329 2 37 pass
    ″ 69 1250° F./4 h/AC — 356 361 1 27 pass
    ″ 69 1250° F./4 h/AC — 362 364 1 27 fail
    ″ 69 1250° F./4 h/AC — 350 356 1 22 pass
    ″ 69 1250° F./4 h/AC 500° F./24 h 350 354 1 43 pass
    ″ 69 1250° F./4 h/AC 500° F./24 h 349 352 1 33 pass
    ″ 69 1250° F./4 h/AC 500° F./24 h 352 356 1 43 pass*
    ″ 69 1300° F./4 h/AC — 325 337 1 32 pass
    ″ 69 1300° F./4 h/AC — 321 334 1 27 pass
    ″ 69 1300° F./4 h/AC — 343 347 1 33 pass
    ″ 69 1300° F./4 h/AC 500° F./24 h 342 347 1 28 pass
    ″ 69 1300° F./4 h/AC 500° F./24 h 343 346 1 27 pass
    ″ 69 1300° F./4 h/AC 500° F./24 h 332 337 1 32 pass
    0.0293 in. 73 None — 263 306 1 44 pass
    ″ 73 None 500° F./24 h 322 334 1 48 pass
    ″ 73 None 500° F./24 h 314 335 2 43 pass
    ″ 73 None 500° F./24 h 300 316 2 48 pass
    ″ 73 1250° F./4 h/AC — 366 370 1 38 fail
    ″ 73 1250° F./4 h/AC — 362 365 1 38 pass
    ″ 73 1250° F./4 h/AC — 358 366 1 38 pass
    ″ 73 1250° F./4 h/AC 500° F./24 h 325 350 1 27 pass
    ″ 73 1250° F./4 h/AC 500° F./24 h 347 354 1 27 pass
    ″ 73 1250° F./4 h/AC 500° F./24 h 343 352 1 27 pass
    ″ 73 1300° F./4 h/AC — 352 357 2 43 pass
    ″ 73 1300° F./4 h/AC — 342 353 1 38 pass
    ″ 73 1300° F./4 h/AC — 353 356 1 43 pass
    ″ 73 1300° F./4 h/AC 500° F./24 h 333 344 1 33 pass
    ″ 73 1300° F./4 h/AC 500° F./24 h 344 349 1 27 pass
    ″ 73 1300° F./4 h/AC 500° F./24 h 337 346 1 33 Pass
    0.0263 in. 78 None — 286 320 1 53 Pass
    ″ 78 None 500° F./24 h 331 344 2 42 Fail
    ″ 78 None 500° F./24 h 318 328 2 30 fail
    ″ 78 None 500° F./24 h 328 335 2 36 fail
    ″ 78 1250° F./4 h/AC — 350 358 1 53 fail
    ″ 78 1250° F./4 h/AC — 328 346 1 42 fail
    ″ 78 1250° F./4 h/AC — 350 355 1 53 fail
    ″ 78 1250° F./4 h/AC 500° F./24 h 333 350 1 48 fail
    ″ 78 1250° F./4 h/AC 500° F./24 h 347 354 1 53 pass
    ″ 78 1250° F./4 h/AC 500° F./24 h 332 337 1 42 fail
    ″ 78 1300° F./4 h/AC — 347 362 1 17 pass
    ″ 78 1300° F./4 h/AC — 352 357 1 17 pass
    ″ 78 1300° F./4 h/AC — 358 362 1 30 pass
    ″ 78 1300° F./4 h/AC 500° F./24 h 357 362 1 42 pass
    ″ 78 1300° F./4 h/AC 500° F./24 h 337 354 1 36 pass
    ″ 78 1300° F./4 h/AC 500° F./24 h 347 349 1 36 pass
  • The effects of the various combinations of cold reduction and aging temperature on both tensile strength and wrap test ductility are illustrated in the drawing FIGURE. Lower amounts of cold reduction in combination with lower aging temperatures resulted in high U.T.S. levels of 330-360 ksi, but with a greater number of wrap test failures. Aging temperatures higher than 1300° F. resulted in lower tensile strength. However, aging the wire at 1300° F. for 4 hours resulted in consistently good wrap test performance at U.T.S. levels up to about 360 ksi. The best combinations of properties were obtained with cold reductions of about 67-78%.
    • Example 2
  • In a second set of tests, wire from another production heat of the UNS R00035 alloy was processed into fine wire. The heat chemistry of the additional wire material (Example 2) is presented in Table I above. The wire was cold drawn 68% R.C.S.A. to 0.031″ in diameter. The cold drawn wire was aged at various combinations of temperature and time as shown in Table V. Also, set forth in Table V are the results of room temperature tensile and wrap tests including the 0.2% offset yield strength (0.2% Y.S.) and the ultimate tensile strength (U.T.S.) in ksi, the percent elongation (% El.), the percent reduction in area (% R.A.), together with an indication whether the wire passed or failed the wrap test (Wrap Test). The aging heat treatment given to each test sample is shown in the column labeled “Age Treatment”. Some of the wire samples were given underaging heat treatments at 600° F. and 750° F., respectively, for 4 hours. The underaged samples were evaluated to determine if the desired properties could be achieved. The results for the underaged samples are also shown in Table V. The data presented in Table V confirm that the combination of at least about 325 ksi U.T.S. with acceptable wrap test ductility is obtained for the 68% cold-drawn samples aged at 1250-1325° F., although the most consistent results are obtained when the wire is aged at 1300° F. While two of the underaged samples provided acceptable results, most of the underaged samples did not achieve the desired combination of properties.
  • TABLE V
    Wire % Cold Aging Wrap
    Diameter Drawn Treatment 0.2% Y.S. U.T.S. % El. % R.A. Test
    0.0312 in. 68%  600° F./4 h/AC 318 324 1 14 failed
    ″ ″ ″ 313 332 1 19 passed
    ″ ″ ″ 309 327 2 14 passed
    ″ ″  750° F./4 h/AC 342 347 1 14 failed
    ″ ″ ″ 286 298 1 13 failed
    ″ ″ ″ 276 284 1 14 failed
    ″ ″ 1250° F./1 h/AC 332 346 1 30 failed
    ″ ″ ″ 336 339 1 35 passed
    ″ ″ ″ 323 335 1 46 failed
    ″ ″ 1250° F./4 h/AC 337 339 1 25 failed
    ″ ″ ″ 324 328 1 25 passed
    ″ ″ ″ 341 345 1 25 failed
    ″ ″ 1275° F./1 h/AC 335 349 2 25 failed
    ″ ″ ″ 315 341 1 19 passed
    ″ ″ ″ 340 347 1 19 passed
    ″ ″ 1275° F./4 h/AC 334 339 1 40 passed
    ″ ″ ″ 328 340 1 25 passed
    ″ ″ ″ 320 344 1 36 passed
    ″ ″ 1300° F./1 h/AC 329 342 1 41 passed
    ″ ″ ″ 330 335 1 30 passed
    ″ ″ ″ 329 340 1 30 passed
    ″ ″ 1300° F./4 h/AC 336 337 1 33 passed
    ″ ″ ″ 336 338 1 25 passed
    ″ ″ ″ 321 333 1 41 passed
    ″ ″ 1325° F./1 h/AC 339 340 1 25 passed
    ″ ″ ″ 288 324 1 19 passed
    ″ ″ ″ 324 331 1 19 passed
    ″ ″ 1325° F./4 h/AC 301 304 1 25 passed
    ″ ″ ″ 305 306 2 25 passed
    ″ ″ ″ 303 308 1 31 passed
  • The effects of heating rate and aging time were evaluated using additional samples of the 68% cold-drawn wire. Table VI shows the results of room temperature tensile and wrap tests including the 0.2% offset yield strength (0.2% Y.S.) and the ultimate tensile tensile strength (U.T.S.) in ksi, the percent elongation (% El.), the percent reduction in area (% R.A.), together with an indication whether the wire passed or failed the wrap test (Wrap Test). The aging heat treatment given to each test sample is shown in the column labeled “Age Treatment”. The data presented in Table VI show that the best combination of properties is obtained by aging at about 1300° F. for 4 hours.
  • TABLE VI
    Wire % Cold 0.2%
    Diameter Drawn Aging Treatment Y.S. U.T.S. % El. % R.A. Wrap Test
    Effects of Slow Heating
    0.0312 in. 68% slow heat 900-1250° F. (2 h), 336 340 1 30 Passed
    1250-1300° F. (3.5 h)/AC
    ″ ″ slow heat 900-1250° F. (2 h), 347 351 1 30 Passed
    1250-1300° F. (3.5 h)/AC
    ″ ″ slow heat 900-1250° F. (2 h), 350 352 1 25 Failed
    1250-1300° F. (3.5 h)/AC
    ″ ″ slow heat 900-1225° F. (4 h), 331 341 2 19 Passed
    1225-1275° F. (7 h)/AC
    ″ ″ slow heat 900-1225° F. (4 h), 314 338 2 14 Passed
    1225-1275° F. (7 h)/AC
    ″ ″ slow heat 900-1225° F. (4 h), 330 336 1 19 Passed
    1225-1275° F. (7 h)/AC
    ″ ″ slow heat 900-1250° F. (4 h), 336 338 1 36 Passed
    1250-1300° F. (7 h)/AC
    ″ ″ slow heat 900-1250° F. (4 h), 336 341 1 30 Passed
    1250-1300° F. (7 h)/AC
    ″ ″ slow heat 900-1250° F. (4 h), 337 342 1 30 Passed
    1250-1300° F. (7 h)/AC
    ″ ″ slow heat 900-1250° F. (4 h), 337 339 1 25 Passed
    1250-1300° F. (7 h)/4 h/AC
    ″ ″ slow heat 900-1250° F. (4 h), 315 337 1 25 Passed
    1250-1300° F. (7 h)/4 h/AC
    ″ ″ slow heat 900-1250° F. (4 h), 331 337 1 26 Passed
    1250-1300° F. (7 h)/4 h/AC
    ″ ″ slow heat 900-1250° F. (6 h), 330 331 1 30 Passed
    1250-1300° F. (10 h)/AC
    ″ ″ slow heat 900-1250° F. (6 h), 328 329 1 25 Passed
    1250-1300° F. (10 h)/AC
    ″ ″ slow heat 900-1250° F. (6 h), 333 335 1 26 Passed
    1250-1300° F. (10 h)/AC
    Effects of Aging Time
    0.0312 in. ″ 1300° F./5 minutes/AC 323 343 1 19 Failed
    ″ ″ ″ 354 356 1 13 Passed
    ″ ″ ″ 319 341 1 19 Passed
    ″ ″ 1300° F./15 minutes/AC 276 338 1 19 Failed
    ″ ″ ″ 335 355 1 13 Failed
    ″ ″ ″ 307 343 1 19 Passed
    ″ ″ 1300° F./30 minutes/AC 349 349 1 25 Failed
    ″ ″ ″ 329 347 2 19 Passed
    ″ ″ ″ 317 344 1 25 Passed
    ″ ″ 1300° F./1 h/AC 329 342 1 41 Passed
    ″ ″ ″ 330 335 1 30 Passed
    ″ ″ ″ 329 340 1 30 Passed
    ″ ″ 1300° F./2 h/AC 324 342 1 30 Passed
    ″ ″ ″ 334 340 3 19 passed
    ″ ″ ″ 348 348 2 13 failed
    ″ ″ 1300° F./4 h/AC 336 337 1 33 passed
    ″ ″ ″ 336 338 1 25 passed
    ″ ″ ″ 321 333 1 41 passed
    ″ ″ 1300° F./8 h/AC 315 330 2 25 passed
    ″ ″ ″ 299 333 1 19 passed
    ″ ″ ″ 289 329 3 25 passed
    ″ ″ 1300° F./1 h + 315 345 1 30 passed
    500° F./24 h
    ″ ″ 1300° F./1 h + 317 331 1 36 passed
    500° F./24 h
    ″ ″ 1300° F./1 h + 342 348 1 25 passed
    500° F./24 h
    ″ ″ 1300° F./4 h + 341 345 1 30 passed
    500° F./24 h
    ″ ″ 1300° F./4 h + 323 340 1 25 passed
    500° F./24 h
    ″ ″ 1300° F./4 h + 328 344 1 25 passed
    500° F./24 h
    ″ ″ 1300° F./1 h/slow cool + 299 354 1 19 failed
    500° F./24 h
    ″ ″ 1300° F./1 h/slow cool + 340 350 1 25 passed
    500° F./24 h
    ″ ″ 1300° F./1 h/slow cool + 312 355 1 25 passed
    500° F./24 h
  • Vacuum aging trials of small coils of the 68% cold drawn wire from Example 2 were performed. Small quantities of wire were coiled onto standard production spools so that the mass was comparable to that of a typical production order. For the first trial, the furnace setpoints were reduced to 1275° F. for 2 hours to avoid overheating the wire. The first trial resulted in lower % R.A. and some susceptibility to breakage during handling for subsequent corrosion testing. The wire breakage is believed to be attributable to more severe bending of the wire for the corrosion testing in combination with surface damage from the tool used to bend the wire specimens. A second trial was conducted using the preferred set point of 1300° F. for 4 hours. Table VII shows tensile and wrap test results for the two vacuum aged trials. Although the ductility of the wire as indicated by the % Elong. and the % R.A. increased relative to the first trial, none of the 1300° F. aged test samples passed the wrap test. Since the results for the bend test for the second trial were unexpected, the wire samples were analyzed to determine the reason for the failures. The failure analysis revealed that the wrap test breaks occurred because of defects on the surfaces of the wire samples.
  • A third trial was performed on six additional samples of wire that was aged the same way as in the first two trials. All six test samples passed the bend test in this trial. The test results are set forth at the bottom of Table VII.
  • TABLE VII
    Wire % Cold Aging 0.2% % % Wrap
    Diameter Drawn Treatment Y.S. U.T.S. El. R.A. Test
    First Trial
    0.0311 in. 68% 1275° F./2 h/ 344 348 1 19 passed
    Gas Quench
    ″ ″ 1275° F./2 h/ 325 333 1 13 passed
    Gas Quench
    ″ ″ 1275° F./2 h/ 333 354 1 13 passed
    Gas Quench
    Second Trial
    0.0311 in. 68% 1300° F./4 h/ 342 345 2 19 failed*
    Gas Quench
    ″ ″ 1300° F./4 h/ 338 340 2 25 failed*
    Gas Quench
    ″ ″ 1300° F./4 h/ 336 343 2 25 failed*
    Gas Quench
    Third Trial
    0.0312 in. 68% 1300° F./4 h/ 328 352 3 30 passed
    Gas Quench
    ″ ″ 1300° F./4 h/ 329 343 3 25 passed
    Gas Quench
    ″ ″ 1300° F./4 h/ 323 348 3 30 passed
    Gas Quench
    ″ ″ 1300° F./4 h/ 323 353 3 30 passed
    Gas Quench
    ″ ″ 1300° F./4 h/ 326 348 3 25 passed
    Gas Quench
    ″ ″ 1300° F./4 h/ 327 350 3 25 passed
    Gas Quench
    *Failure analysis showed that fracture initiated at wire surface defects.
  • The terms and expressions which are employed herein are used as terms of description and not of limitation. There is no intention in the use of such terms and expressions of excluding any equivalents of the features shown and described or portions thereof. It is recognized that various modifications are possible within the invention described and claimed herein. Thus, the present invention may suitably comprise, consist essentially of, or consist of the steps of forming, annealing, drawing, and hardening as described herein. The invention illustratively disclosed herein suitably may be practiced in the absence of any step or parameter which is not specifically disclosed herein.

Claims (35)

1. A method of making wire comprising the steps of:
forming a length of wire from an alloy comprising, in weight percent, about
Carbon 0.03 max. Manganese 0.15 max. Silicon 0.15 max. Phosphorus 0.015 max. Sulfur 0.010 max. Chromium 19.00-21.00 Nickel 33.00-37.00 Molybdenum  9.00-10.50 Titanium 1.00 max. Boron 0.010 max. Iron 1.00 max.
the balance being cobalt and the usual impurities;
annealing said wire at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer;
drawing the annealed wire such that the cross-sectional area of the wire is reduced by about 50 to 80%; and then
hardening said alloy by heating the wire at a second combination of temperature and time effective to provide said alloy with a room temperature tensile strength of at least 300 ksi and sufficient ductility that when said wire is wrapped to provide a coil having an inside diameter substantially equal to the diameter of said wire and then unwrapped, said wire does not crack or break.
2. The method as claimed in claim 1 wherein the annealing step comprises the step of heating said wire at a temperature of about 1750 to 1850° F. for about 0.5 to 2 hours.
3. The method as claimed in claim 1 wherein the hardening step comprises heating the wire at a temperature of about 1250° F. to about 1325° F. for up to about 4 hours.
4. The method as claimed in claim 1 wherein the step of drawing the wire is performed such that the cross-sectional area of the wire is reduced by at least about 64%.
5. The method as claimed in claim 4 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by not more than about 78%.
6. The method as claimed in claim 5 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by not more than about 73%.
7. The method as claimed in claim 1 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by at least about 67%.
8. The method as claimed in claim 1 wherein the hardening step comprises heating the wire at not more than about 1300° F.
9. The method as claimed in claim 1 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 64 to 78%; and
the hardening step comprises heating the drawn wire at a temperature of about 1250-1300° F.
10. The method as claimed in claim 9 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by at least about 67%.
11. The method as claimed in claim 1 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 64 to 73%; and
the hardening step comprises heating the drawn wire at a temperature of about 1250-1325° F.
12. The method as claimed in claim 11 wherein the hardening step comprises heating the wire at a temperature not greater than about 1300° F.
13. The method as claimed in claim 12 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by not more then about 68%.
14. The method as claimed in claim 1 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 67 to 78%; and
the hardening step comprises heating the drawn wire at a temperature of about 1275-1300° F.
15. The method as claimed in claim 14 wherein the hardening step comprises heating the drawn wire at a temperature of about 1300° F.
16. The method as claimed in claim 1 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 67 to 68%; and
the hardening step comprises heating the drawn wire at a temperature of about 1275° F.
17. The method as claimed in claim 1 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 67%; and
the hardening step comprises heating the drawn wire at a temperature of about 1250° F.
18. A method of making flexible armored cable comprising the steps of:
forming a length of wire from an alloy comprising, in weight percent, about
Carbon 0.03 max. Manganese 0.15 max. Silicon 0.15 max. Phosphorus 0.015 max. Sulfur 0.010 max. Chromium 19.00-21.00 Nickel 33.00-37.00 Molybdenum  9.00-10.50 Titanium 1.00 max. Boron 0.010 max. Iron 1.00 max.
the balance being cobalt and the usual impurities;
annealing said wire at a combination of temperature and time effective to provide a grain size of about ASTM 6 or finer;
drawing the annealed wire such that the cross-sectional area of the wire is reduced by about 50 to 80%; and then
hardening said alloy by heating the wire at a second combination of temperature and time effective to provide said alloy with a room temperature tensile strength of at least 300 ksi and sufficient ductility that when said wire is wrapped to provide a coil having an inside diameter substantially equal to the diameter of said wire and then unwrapped, said wire does not crack or break; and then
spirally winding the wire around an elongated core member to form a flexible encasement.
19. The method as claimed in claim 18 wherein the annealing step comprises the step of heating said wire at a temperature of about 1750 to 1850° F. for about 0.5 to 2 hours.
20. The method as claimed in claim 18 wherein the hardening step comprises heating the wire at a temperature of about 1250° F. to about 1325° F. for up to about 4 hours.
21. The method as claimed in claim 18 wherein the step of drawing the wire is performed such that the cross-sectional area of the wire is reduced by at least about 64%.
22. The method as claimed in claim 21 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by not more than about 78%.
23. The method as claimed in claim 22 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by not more than about 73%.
24. The method as claimed in claim 18 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by at least about 67%.
25. The method as claimed in claim 18 wherein the hardening step comprises heating the wire at not more than about 1300° F.
26. The method as claimed in claim 18 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 64 to 78%; and
the hardening step comprises heating the drawn wire at a temperature of about 1250-1300° F.
27. The method as claimed in claim 26 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by at least about 67%.
28. The method as claimed in claim 18 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 64 to 73%; and
the hardening step comprises heating the drawn wire at a temperature of about 1250-1325° F.
29. The method as claimed in claim 28 wherein the hardening step comprises heating the wire at a temperature not greater than about 1300° F.
30. The method as claimed in claim 29 wherein the drawing step is performed such that the cross-sectional area of the wire is reduced by not more then about 68%.
31. The method as claimed in claim 18 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 67 to 78%; and
the hardening step comprises heating the drawn wire at a temperature of about 1275-1300° F.
32. The method as claimed in claim 31 wherein the hardening step comprises heating the drawn wire at a temperature of about 1300° F.
33. The method as claimed in claim 18 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 67 to 68%; and
the hardening step comprises heating the drawn wire at a temperature of about 1275° F.
34. The method as claimed in claim 18 wherein:
the drawing step is performed such that the cross-sectional area of the wire is reduced by about 67%; and
the hardening step comprises heating the drawn wire at a temperature of about 1250° F.
35. A wire article comprising wire formed from a high strength, corrosion resistant alloy having the following composition in weight percent, about
Carbon 0.03 max. Manganese 0.15 max. Silicon 0.15 max. Phosphorus 0.015 max. Sulfur 0.010 max. Chromium 19.00-21.00 Nickel 33.00-37.00 Molybdenum  9.00-10.50 Titanium 1.00 max. Boron 0.010 max. Iron 1.00 max.
Wherein the balance of the alloy is cobalt and the usual impurities and the wire is characterized by a tensile strength in excess of 300 ksi and sufficient ductility that when the wire is wrapped to provide a coil having an inside diameter substantially equal to the diameter of the wire and then unwrapped, the wire does not crack or break.
US12/721,844 2009-03-12 2010-03-11 Ultra-High Strength, Corrosion Resistant Wire, a Method of Making Same, and a Method of Using Same Abandoned US20100230017A1 (en)

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CN112941397A (en) * 2021-03-09 2021-06-11 贵州航天新力科技有限公司 Light medium-entropy alloy with excellent high-temperature mechanical properties and processing technology thereof
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