US20140161658A1 - High Strength Precipitation Hardenable Stainless Steel - Google Patents

High Strength Precipitation Hardenable Stainless Steel Download PDF

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US20140161658A1
US20140161658A1 US13/706,800 US201213706800A US2014161658A1 US 20140161658 A1 US20140161658 A1 US 20140161658A1 US 201213706800 A US201213706800 A US 201213706800A US 2014161658 A1 US2014161658 A1 US 2014161658A1
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alloy
max
recited
alloy recited
toughness
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US13/706,800
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David E. Wert
Michael L. Schmidt
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CRS Holdings LLC
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CRS Holdings LLC
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Priority to US13/706,800 priority Critical patent/US20140161658A1/en
Assigned to CRS HOLDINGS, INC. reassignment CRS HOLDINGS, INC. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: SCHMIDT, MICHAEL L., WERT, DAVID E.
Priority to CA2893272A priority patent/CA2893272C/en
Priority to PCT/US2013/073542 priority patent/WO2014089418A1/en
Priority to KR1020157015534A priority patent/KR101780875B1/en
Priority to EP13814314.4A priority patent/EP2929062A1/en
Priority to BR112015013006A priority patent/BR112015013006A2/en
Priority to CN201380072413.4A priority patent/CN105102649A/en
Priority to JP2015545869A priority patent/JP6117372B2/en
Priority to AU2013355066A priority patent/AU2013355066B2/en
Publication of US20140161658A1 publication Critical patent/US20140161658A1/en
Priority to US15/210,107 priority patent/US20160319406A1/en
Priority to US16/033,324 priority patent/US20180320256A1/en
Abandoned legal-status Critical Current

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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C21D2211/008—Martensite
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/04—Hardening by cooling below 0 degrees Celsius
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below

Definitions

  • This invention relates to precipitation hardenable, martensitic stainless steel alloys and in particular to a martensitic stainless steel alloy and an article made therefrom, having a novel combination of strength and corrosion resistance.
  • the aerospace industry has been looking for a stainless steel alloy for landing gear for many years.
  • the main alloy currently used for the commercial landing gear application is 300M alloy.
  • 300M alloy can be quenched and tempered to provide an ultimate tensile strength of at least 280 ksi and fracture toughness (K Ic ) of at least 50 ksi ⁇ in.
  • K Ic fracture toughness
  • 300M alloy does not provide effective corrosion resistance. Therefore, it has been necessary to plate the landing gear components with a corrosion resistant metal such as cadmium.
  • Cadmium is a highly toxic, carcinogenic material and its use has presented significant environmental risks in the manufacture and maintenance of aircraft landing gear and other components made from 300M alloy.
  • Precipitation hardenable stainless steel alloys having commercially acceptable combinations of strength and toughness are known and used for various aerospace applications. However, some of those alloys do not provide strength equivalent to 300M, so they cannot be considered as “drop-in” replacements for that alloy.
  • the other known precipitation hardenable stainless steels may provide adequate strength for the landing gear application, but leave something to be desired in the resistance to corrosion they provide.
  • the corrosion resistance desired for the aircraft landing gear application includes general corrosion resistance, pitting corrosion resistance, and resistance to stress corrosion cracking.
  • the alloy according to the present invention is a precipitation hardening Cr—Ni—Ti—Mo martensitic stainless steel alloy that provides a unique combination of strength, toughness, and corrosion resistance.
  • compositional ranges of the alloy according to the present invention are set forth below in weight percent.
  • the foregoing tabulation is provided as a convenient summary and is not intended thereby to restrict the lower and upper values of the ranges of the individual elements of the alloy of this invention for use in combination with each other, or to restrict the ranges of the elements for use solely in combination with each other.
  • one or more of the element ranges of the broad composition can be used with one or more of the other ranges for the remaining elements in the preferred composition.
  • a minimum or maximum for an element of one preferred embodiment can be used with the maximum or minimum for that element from another preferred embodiment.
  • the alloy according to this invention may comprise, consist essentially of, or consist of the constituent elements described above and throughout this specification.
  • percent or the symbol “%” means percent by weight or mass percent.
  • the alloy according to the present invention provides a unique combination of strength, toughness, and corrosion resistance which results from a novel balancing of the elements chromium, nickel, cobalt, molybdenum and also the elements titanium, aluminum, and columbium. At least about 10%, better yet at least about 10.5%, and preferably at least about 11.0% chromium is present in the alloy to provide corrosion resistance similar to that of a conventional stainless steel. At least about 10.5%, better yet at least about 10.75%, and preferably at least about 10.85% nickel is present in the alloy because nickel benefits the toughness and notch toughness of the alloy. Nickel also contributes to the corrosion resistance by enhancing the ability of the alloy to repassivate.
  • This alloy contains at least about 0.5%, better yet at least about 0.75%, and preferably at least about 0.9% cobalt because cobalt contributes to the high strength and corrosion resistance provided by the alloy. At least about 0.25%, better yet at least about 0.75%, and preferably at least about 0.9% molybdenum is also present in the alloy because molybdenum contributes to the alloy's notch toughness. Molybdenum also benefits the alloy's corrosion resistance in reducing media and in environments which promote pitting attack and stress-corrosion cracking.
  • the alloy of this invention also contains at least about 1.5% titanium to benefit the strength of the alloy through the precipitation of a nickel-titanium-rich phase during aging.
  • Columbium and aluminum also contribute to the strength provided by this alloy. Therefore, the alloy contains at least about 0.3% and better yet at least about 0.4% of each of columbium and aluminum. Preferably the alloy contains at least about 0.45% aluminum.
  • chromium, nickel, cobalt, molybdenum, titanium, columbium, and aluminum are not properly balanced, the alloy's ability to transform fully to a martensitic structure using conventional processing techniques is inhibited. Furthermore, the alloy's ability to remain substantially fully martensitic when solution treated and age-hardened is impaired. Under such conditions the strength provided by the alloy is significantly reduced. Therefore, the amounts of chromium, nickel, cobalt, molybdenum, titanium, columbium, and aluminum present in this alloy are restricted. More particularly, chromium is limited to not more than about 13%, better yet to not more than about 12.5%, and preferably to not more than about 12.0%.
  • Nickel is limited to not more than about 11.6% and preferably to not more than about 11.25%. Too much cobalt adversely affects the strength and toughness provided by this alloy. Therefore, cobalt is restricted to not more than about 1.5%, better yet to not more than about 1.25%, and preferably to not more than about 1.1%. Molybdenum is restricted to not more than about 1.5%, better yet to not more than about 1.25%, and preferably to not more than about 1.1%.
  • Too much titanium adversely affects the toughness and notch toughness of the alloy. Therefore, titanium is restricted to not more than about 1.8% and preferably to not more than about 1.7% in this alloy. Too much aluminum can adversely affect the toughness and corrosion resistance provided by the alloy. Therefore, aluminum is restricted to not more than about 0.8%, better yet to not more than about 0.7%, and preferably to not more than about 0.65%. Too much columbium is likely to result in undesirable alloy segregation and the precipitation of unwanted secondary phases such as Laves phase. Therefore, columbium is restricted to not more than about 0.8%, better yet to not more than about 0.7%, and preferably to not more than about 0.6% in this alloy.
  • Additional elements such as manganese, silicon, and boron may be present in controlled amounts to benefit other desirable properties provided by this alloy. More specifically, up to about 1.0%, better yet up to about 0.5%, still better up to about 0.25%, and preferably up to about 0.10% manganese and/or up to about 0.75%, better yet up to about 0.5%, still better up to about 0.25%, and preferably up to about 0.10% silicon can be present in the alloy as residuals from scrap sources or deoxidizing additions. Such additions are beneficial when the alloy is not vacuum melted. Manganese and/or silicon are preferably kept at low levels because of their adverse effect on toughness, corrosion resistance, and the austenite-martensite phase balance in the matrix material.
  • boron up to about 0.010% boron, better yet up to about 0.005% boron, and preferably up to about 0.0035% boron can be present in the alloy to benefit the hot workability of the alloy. In order to provide the desired effect, at least about 0.001% and preferably at least about 0.0015% boron is present in the alloy.
  • the balance of the alloy is essentially iron apart from the usual impurities inevitably found in commercial grades of alloys intended for similar service or use.
  • the levels of such elements are controlled so as not to adversely affect the desired properties.
  • Phosphorus is maintained at a low level because of its adverse effect on toughness and corrosion resistance. Accordingly, not more than about 0.040%, better yet not more than about 0.015%, and preferably not more than about 0.010% phosphorus is present in the alloy.
  • sulfur is present in the alloy.
  • Larger amounts of sulfur promote the formation of non-metallic sulfide inclusions which, like carbon and nitrogen, inhibit the desired strengthening effect provided by titanium, aluminum, and columbium. These sulfide inclusions impair the toughness of the alloy, especially in the transverse direction. Also, a greater amount of sulfur adversely affects the hot workability and corrosion resistance of this alloy.
  • REM rare earth metals
  • the alloy may contain at least about 0.001% REM and better yet, at least about 0.002% REM.
  • the amount of REM present in this alloy is limited to not more than about 0.025%, better yet to not more than about 0.015%, and preferably to not more than about 0.010%, in this alloy. It is further contemplated that magnesium can be added as an alternative to calcium or REM for desulfurization and deoxidation.
  • the alloy contains not more than about 0.75%, better yet not more than about 0.50%, and preferably not more than about 0.25% copper.
  • VIM vacuum induction melting
  • VAR vacuum arc remelting
  • the preferred method of providing calcium in this alloy is through the addition of a nickel-calcium compound during VIM.
  • the nickel-calcium compound such as the Ni-Cal® alloy sold by Chemalloy Co. Inc., is added in an amount effective to combine with available phosphorus, sulfur, and oxygen.
  • Other techniques for adding calcium may also be used.
  • capsules of elemental calcium or calcium master alloys can be added to the melt. It is believed that a slag containing calcium or a calcium compound may also be used.
  • the chemical reactions result in the formation of secondary phase inclusions such as calcium sulfides, calcium oxides, and calcium oxysulfides that are readily removed during primary or secondary melting.
  • REM are added to the molten alloy in the form of mischmetal which is a mixture of rare earth elements, an example of which contains about 50% cerium, about 30% lanthanum, about 15% neodymium, and about 5% praseodymium.
  • the precipitation hardenable alloy of the present invention is processed in multiple steps to develop the desired combination of properties.
  • a first step the alloy is solution annealed.
  • the solution annealing temperature is selected to be high enough to dissolve essentially all of the undesired precipitates into the alloy matrix material and to ensure that the grain structure is fully recrystallized. Unrecrystallized grains can lead to increased anisotropy of the mechanical properties, particularly the ductility and toughness, of the alloy. However, if the solution annealing temperature is too high, it will impair the fracture toughness of the alloy by promoting excessive grain growth.
  • the alloy of the present invention is solution annealed at 1850° F.-1950° F.
  • the alloy is then quenched, preferably in oil.
  • the refrigeration treatment cools the alloy to a temperature sufficiently below the martensite finish temperature to ensure the completion of the martensite transformation.
  • the refrigeration treatment comprises cooling the alloy to about ⁇ 100° F. ( ⁇ 73° C.) or lower for a time sufficient to ensure that the alloy has substantially completely transformed to martensite.
  • the need for a refrigeration treatment will be affected, at least in part, by the martensite finish temperature of the alloy. If the martensite finish temperature is sufficiently high, the transformation to a martensitic structure can proceed without the need for a refrigeration treatment. In addition, the need for a refrigeration treatment may also depend on the section size of the piece being manufactured.
  • the alloy of the present invention is age hardened in accordance with techniques used for the known precipitation hardening, stainless steel alloys, which treatments are known to those skilled in the art.
  • the alloys are preferably aged at about 950-975° F. (510-524° C.) for a time sufficient to ensure that the alloy is substantially uniformly heated to the aging temperature depending on the thickness of the part and typically for an additional 4 to 8 hours to complete the aging reaction and to reach the desired combination of strength and toughness.
  • the specific aging temperature used is selected by considering that: (1) the ultimate tensile strength of the alloy decreases as the aging temperature increases; and (2) the time required to age harden the alloy to a desired strength level increases as the aging temperature decreases.
  • the alloy of the present invention can be formed into a variety of product shapes for a wide variety of uses and lends itself to the formation of billets, bars, rod, wire, strip, plate, or sheet using conventional practices.
  • the alloy of the present invention is useful in a wide range of practical applications which require an alloy having a good combination of corrosion resistance, strength, and toughness.
  • the alloy of the present invention can be used to produce structural members for aircraft, including but not limited to landing gear components and fasteners.
  • the alloy is also well suited for use in medical and dental applications such as dental tools and medical scrapers, cutters, and suture needles.
  • Example 1 The balance of each heat is iron and usual impurities.
  • Examples 1 and 2 are representative of the alloy according to the present invention.
  • Examples A to E are comparative alloys. In particular, Example A is within the scope of the alloy described in U.S. Pat. No. 5,681,526.
  • the VIM heats were melted and cast into 4′′ square ingots.
  • the ingots were charged into a furnace operating at 1500° F. and the furnace temperature was ramped up to 2300° F. Ingots were held at 2300° F. for 16 hours after which the furnace temperature was lowered to 2000° F. The ingots were held at 2000° F. until they were substantially fully equalized in temperature.
  • the ingots were then double-end forged to 23 ⁇ 4′′ square billet from starting temperature of 2000° F. and then hot cut into 3 pieces each. Pieces were re-heated at 2000° F., and double-end forged to 11 ⁇ 4′′ square.
  • the bars were again hot cut into 3 pieces and reheated at 2000° F. The bars were then single-end forged to 11/16′′ square with no reheats. The bars were cooled in air, overage annealed at 1250° F. for 8 hours, and then air cooled.
  • Tables IIA and IIB The results of room temperature tensile testing on the samples of each heat are shown in Tables IIA and IIB below including the 0.2% offset yield strength (Y.S.) and the ultimate tensile strength (U.T.S) in ksi, the percent elongation (% El.), the percent reduction in area (% R.A.), and the notch tensile strength (N.T.S.) in ksi.
  • K Ic room temperature fracture toughness testing
  • stress corrosion cracking testing for Examples 1, 2, A, and D are presented in Table IV below including the plane-strain fracture toughness (K Ic ) in ksi ⁇ in and the threshold stress intensity to produce stress corrosion cracking (K ISCC ) in ksi ⁇ in.
  • K ISCC is reported for each step interval and as a final value. The lowest of the measured values for each example is designated as the final value of K ISCC in accordance with the standard test procedure.
  • the tensile strength values for each example are also reported in Table IV to show that the fracture toughness and stress corrosion cracking resistance were measured on alloys having similar levels of strength.
  • Duplicate salt spray corrosion test cones were finish machined from the bars of Examples 1, 2, A, D after age-hardening. The cone samples were prepared by turning and hand polishing to a 600 grit finish. Prior to testing, all salt spray cones were passivated using 20% Nitric acid+3 oz./gallon Sodium Dichromate at 120/140° F. for 30 minutes. Samples were tested in accordance with ASTM B117, using a 5% NaCl concentration, natural pH, at 95° F. for 200 hour test duration. Time to first rust was noted for all samples, as well as a final rating after the completion of 200 hours test duration.
  • the results of the salt-spray testing are shown in Table V below including the time to first appearance of rust and a final rating after the completion of the test duration.
  • Cyclic polarization (pitting) test samples were finish machined from the aged bars of Examples 1, 2, A, and D. Scans to measure pitting resistance were run on duplicate samples from each of those examples. The samples were tested in 3.5% NaCl solution, natural pH, at room temperature and were cleaned but not passivated prior to testing. Testing was performed with a modified ASTM Standard Test procedure G61 as described below. Voltage values at the knee of the curve and protection potentials were measured for all samples. The results of the potentiodynamic pitting tests are shown in Table VI below including the pitting potential and the protection potential in millivolts (mV).
  • a steel article made from the alloy described above and processed in accordance with the foregoing processing steps provides a combination of properties that make it particularly useful for aircraft landing gear and other aircraft structural components, including but not limited to flap tracks and slat tracks, and for other applications where both high strength and corrosion resistance are required.
  • a steel article fabricated from the alloy that is solution heat treated and age hardened as described above provides a tensile strength of at least 280 ksi and a fracture toughness (K Ic ) of at least 45 ksi ⁇ in when tested with a test machine that meets the requirements of ASTM Standard Test Procedure E1290.
  • a steel article in accordance with this invention is also characterized by a Charpy V-notch impact energy of at least about 4 ft-lbs when tested in accordance with ASTM Standard Test Procedure E23. Further, a steel article in accordance with this invention is characterized by general corrosion resistance such that the article does not rust when tested in accordance with ASTM Standard Test procedure B 117 and by sufficient pitting corrosion resistance such that the article has a pitting potential of at least 62 mV when tested in accordance with a modified ASTM Standard Test procedure G61.
  • the ASTM G61 test procedure was modified by using round bar rather than flat samples. The use of round bar samples exposes the end grains and can be considered to be a more severe test than the standard G61 procedure.

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  • Engineering & Computer Science (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

A precipitation hardenable, martensitic stainless steel alloy is disclosed. The alloy has the following composition in weight percent, about
C  0.03 max Mn  1.0 max Si  0.75 max P 0.040 max S 0.020 max Cr 10-13 Ni 10.5-11.6 Mo 0.25-1.5  Co 0.5-1.5 Cu  0.75 max Ti 1.5-1.8 Al 0.3-0.8 Nb 0.3-0.8 B 0.010 max N 0.030 max
The balance is iron and usual impurities. The disclosed alloy provides a unique combination of corrosion resistance, strength, and toughness.

Description

    BACKGROUND OF THE INVENTION
  • 1. Field of the Invention
  • This invention relates to precipitation hardenable, martensitic stainless steel alloys and in particular to a martensitic stainless steel alloy and an article made therefrom, having a novel combination of strength and corrosion resistance.
  • 2. Description of the Related Art
  • The aerospace industry has been looking for a stainless steel alloy for landing gear for many years. The main alloy currently used for the commercial landing gear application is 300M alloy. 300M alloy can be quenched and tempered to provide an ultimate tensile strength of at least 280 ksi and fracture toughness (KIc) of at least 50 ksi√in. However, 300M alloy does not provide effective corrosion resistance. Therefore, it has been necessary to plate the landing gear components with a corrosion resistant metal such as cadmium. Cadmium is a highly toxic, carcinogenic material and its use has presented significant environmental risks in the manufacture and maintenance of aircraft landing gear and other components made from 300M alloy.
  • Precipitation hardenable stainless steel alloys having commercially acceptable combinations of strength and toughness are known and used for various aerospace applications. However, some of those alloys do not provide strength equivalent to 300M, so they cannot be considered as “drop-in” replacements for that alloy. The other known precipitation hardenable stainless steels may provide adequate strength for the landing gear application, but leave something to be desired in the resistance to corrosion they provide. The corrosion resistance desired for the aircraft landing gear application includes general corrosion resistance, pitting corrosion resistance, and resistance to stress corrosion cracking.
  • In view of the foregoing discussion, there is a need for a steel alloy with mechanical properties comparable to those of 300M, so the new alloy can be used as a drop-in replacement, combined with effective corrosion resistance in the variety of environments in which commercial aircraft are used.
    • SUMMARY OF THE INVENTION
  • The disadvantages associated with the known precipitation hardenable, martensitic stainless steel alloys are solved to a large degree by the alloy in accordance with the present invention. The alloy according to the present invention is a precipitation hardening Cr—Ni—Ti—Mo martensitic stainless steel alloy that provides a unique combination of strength, toughness, and corrosion resistance.
  • The broad, intermediate, and preferred compositional ranges of the alloy according to the present invention are set forth below in weight percent.
  • Broad Intermediate Preferred
    C  0.03 max 0.02 max 0.015 max
    Mn  1.0 max 0.25 max  0.10 max
    Si  0.75 max 0.25 max  0.10 max
    P 0.040 max 0.015 max  0.010 max
    S 0.020 max 0.010 max  0.005 max
    Cr 10-13 10.5-12.5 11.0-12.0
    Ni 10.5-11.6 10.75-11.25 10.85-11.25
    Mo 0.25-1.5  0.75-1.25 0.9-1.1
    Cu  0.75 max 0.50 max  0.25 max
    Co 0.5-1.5 0.75-1.25 0.9-1.1
    Ti 1.5-1.8 1.5-1.7 1.5-1.7
    Al 0.3-0.8 0.4-0.7 0.45-0.65
    Cb 0.3-0.8 0.4-0.7 0.4-0.6
    B 0.010 max 0.001-0.005 0.0015-0.0035
    N 0.030 max 0.015 max  0.010 max

    The balance of the alloy is essentially iron except for the usual impurities found in commercial grades of such steels and minor amounts of additional elements which may vary from a few thousandths of a percent up to larger amounts that do not adversely affect the desired combination of properties provided by this alloy.
  • The foregoing tabulation is provided as a convenient summary and is not intended thereby to restrict the lower and upper values of the ranges of the individual elements of the alloy of this invention for use in combination with each other, or to restrict the ranges of the elements for use solely in combination with each other. Thus, one or more of the element ranges of the broad composition can be used with one or more of the other ranges for the remaining elements in the preferred composition. In addition, a minimum or maximum for an element of one preferred embodiment can be used with the maximum or minimum for that element from another preferred embodiment. Moreover, the alloy according to this invention may comprise, consist essentially of, or consist of the constituent elements described above and throughout this specification. Here and throughout this application, unless otherwise indicated, the term percent or the symbol “%” means percent by weight or mass percent.
    • DETAILED DESCRIPTION
  • The alloy according to the present invention provides a unique combination of strength, toughness, and corrosion resistance which results from a novel balancing of the elements chromium, nickel, cobalt, molybdenum and also the elements titanium, aluminum, and columbium. At least about 10%, better yet at least about 10.5%, and preferably at least about 11.0% chromium is present in the alloy to provide corrosion resistance similar to that of a conventional stainless steel. At least about 10.5%, better yet at least about 10.75%, and preferably at least about 10.85% nickel is present in the alloy because nickel benefits the toughness and notch toughness of the alloy. Nickel also contributes to the corrosion resistance by enhancing the ability of the alloy to repassivate. This alloy contains at least about 0.5%, better yet at least about 0.75%, and preferably at least about 0.9% cobalt because cobalt contributes to the high strength and corrosion resistance provided by the alloy. At least about 0.25%, better yet at least about 0.75%, and preferably at least about 0.9% molybdenum is also present in the alloy because molybdenum contributes to the alloy's notch toughness. Molybdenum also benefits the alloy's corrosion resistance in reducing media and in environments which promote pitting attack and stress-corrosion cracking.
  • The alloy of this invention also contains at least about 1.5% titanium to benefit the strength of the alloy through the precipitation of a nickel-titanium-rich phase during aging. Columbium and aluminum also contribute to the strength provided by this alloy. Therefore, the alloy contains at least about 0.3% and better yet at least about 0.4% of each of columbium and aluminum. Preferably the alloy contains at least about 0.45% aluminum.
  • When chromium, nickel, cobalt, molybdenum, titanium, columbium, and aluminum are not properly balanced, the alloy's ability to transform fully to a martensitic structure using conventional processing techniques is inhibited. Furthermore, the alloy's ability to remain substantially fully martensitic when solution treated and age-hardened is impaired. Under such conditions the strength provided by the alloy is significantly reduced. Therefore, the amounts of chromium, nickel, cobalt, molybdenum, titanium, columbium, and aluminum present in this alloy are restricted. More particularly, chromium is limited to not more than about 13%, better yet to not more than about 12.5%, and preferably to not more than about 12.0%. Nickel is limited to not more than about 11.6% and preferably to not more than about 11.25%. Too much cobalt adversely affects the strength and toughness provided by this alloy. Therefore, cobalt is restricted to not more than about 1.5%, better yet to not more than about 1.25%, and preferably to not more than about 1.1%. Molybdenum is restricted to not more than about 1.5%, better yet to not more than about 1.25%, and preferably to not more than about 1.1%.
  • Too much titanium adversely affects the toughness and notch toughness of the alloy. Therefore, titanium is restricted to not more than about 1.8% and preferably to not more than about 1.7% in this alloy. Too much aluminum can adversely affect the toughness and corrosion resistance provided by the alloy. Therefore, aluminum is restricted to not more than about 0.8%, better yet to not more than about 0.7%, and preferably to not more than about 0.65%. Too much columbium is likely to result in undesirable alloy segregation and the precipitation of unwanted secondary phases such as Laves phase. Therefore, columbium is restricted to not more than about 0.8%, better yet to not more than about 0.7%, and preferably to not more than about 0.6% in this alloy.
  • Additional elements such as manganese, silicon, and boron may be present in controlled amounts to benefit other desirable properties provided by this alloy. More specifically, up to about 1.0%, better yet up to about 0.5%, still better up to about 0.25%, and preferably up to about 0.10% manganese and/or up to about 0.75%, better yet up to about 0.5%, still better up to about 0.25%, and preferably up to about 0.10% silicon can be present in the alloy as residuals from scrap sources or deoxidizing additions. Such additions are beneficial when the alloy is not vacuum melted. Manganese and/or silicon are preferably kept at low levels because of their adverse effect on toughness, corrosion resistance, and the austenite-martensite phase balance in the matrix material.
  • Up to about 0.010% boron, better yet up to about 0.005% boron, and preferably up to about 0.0035% boron can be present in the alloy to benefit the hot workability of the alloy. In order to provide the desired effect, at least about 0.001% and preferably at least about 0.0015% boron is present in the alloy.
  • The balance of the alloy is essentially iron apart from the usual impurities inevitably found in commercial grades of alloys intended for similar service or use. The levels of such elements are controlled so as not to adversely affect the desired properties.
  • In particular, too much carbon and/or nitrogen impair the corrosion resistance and adversely affect the toughness provided by this alloy. Accordingly, not more than about 0.03%, better yet not more than about 0.02%, and preferably not more than about 0.015% carbon is present in the alloy. Also, not more than about 0.030%, better yet not more than about 0.015%, not more than about 0.010% nitrogen is present in the alloy. When carbon and/or nitrogen are present in larger amounts, the carbon and/or nitrogen bond with titanium, aluminum, and/or columbium to form undesirable non-metallic inclusions such as carbides or nitrides and/or carbonitrides. Those reactions inhibit the formation of the nickel-titanium/aluminum/columbium intermetallic phases which are a primary factor in the development of the high strength provided by this alloy.
  • Phosphorus is maintained at a low level because of its adverse effect on toughness and corrosion resistance. Accordingly, not more than about 0.040%, better yet not more than about 0.015%, and preferably not more than about 0.010% phosphorus is present in the alloy.
  • Not more than about 0.020%, better yet not more than about 0.010%, and preferably not more than about 0.005% sulfur is present in the alloy. Larger amounts of sulfur promote the formation of non-metallic sulfide inclusions which, like carbon and nitrogen, inhibit the desired strengthening effect provided by titanium, aluminum, and columbium. These sulfide inclusions impair the toughness of the alloy, especially in the transverse direction. Also, a greater amount of sulfur adversely affects the hot workability and corrosion resistance of this alloy.
  • Although sulfur and phosphorus can be reduced to very low levels through the selection of high purity charge materials or by employing alloy refining techniques, their presence in the alloy cannot be entirely avoided under large scale production conditions. Therefore, a small amount of calcium may be added in controlled amounts to combine with phosphorus and/or sulfur to facilitate the removal and stabilization of those two elements in the alloy. Calcium is also used to deoxidize the alloy. When used, the retained amount of calcium is not more than about 0.010% and preferably to not more than about 0.005% in this alloy. As an alternative to the calcium treatment, one or more rare earth metals (REM), particularly cerium and lanthanum, can be added to the alloy. In this regard, the alloy may contain at least about 0.001% REM and better yet, at least about 0.002% REM. Too much REM recovery adversely affects the hot workability and the toughness of this alloy. Excessive REM content also results in the formation of undesirable oxide inclusions in the alloy. Therefore, the amount of REM present in this alloy is limited to not more than about 0.025%, better yet to not more than about 0.015%, and preferably to not more than about 0.010%, in this alloy. It is further contemplated that magnesium can be added as an alternative to calcium or REM for desulfurization and deoxidation.
  • Too much copper adversely affects the notch toughness, ductility, and strength of this alloy. Therefore, the alloy contains not more than about 0.75%, better yet not more than about 0.50%, and preferably not more than about 0.25% copper.
  • No special techniques are required for melting, casting, or working the alloy of the present invention. Vacuum induction melting (VIM) and vacuum induction melting followed by vacuum arc remelting (VAR) are the preferred methods of melting and refining this alloy, but other practices can be used. In addition, this alloy can be made using powder metallurgy techniques, if desired. Further, although the alloy of the present invention can be hot or cold worked, cold working enhances the mechanical strength of the alloy.
  • The preferred method of providing calcium in this alloy is through the addition of a nickel-calcium compound during VIM. The nickel-calcium compound, such as the Ni-Cal® alloy sold by Chemalloy Co. Inc., is added in an amount effective to combine with available phosphorus, sulfur, and oxygen. Other techniques for adding calcium may also be used. For example, capsules of elemental calcium or calcium master alloys can be added to the melt. It is believed that a slag containing calcium or a calcium compound may also be used. The chemical reactions result in the formation of secondary phase inclusions such as calcium sulfides, calcium oxides, and calcium oxysulfides that are readily removed during primary or secondary melting. When used, REM are added to the molten alloy in the form of mischmetal which is a mixture of rare earth elements, an example of which contains about 50% cerium, about 30% lanthanum, about 15% neodymium, and about 5% praseodymium.
  • The precipitation hardenable alloy of the present invention is processed in multiple steps to develop the desired combination of properties. In a first step, the alloy is solution annealed. The solution annealing temperature is selected to be high enough to dissolve essentially all of the undesired precipitates into the alloy matrix material and to ensure that the grain structure is fully recrystallized. Unrecrystallized grains can lead to increased anisotropy of the mechanical properties, particularly the ductility and toughness, of the alloy. However, if the solution annealing temperature is too high, it will impair the fracture toughness of the alloy by promoting excessive grain growth. Preferably, the alloy of the present invention is solution annealed at 1850° F.-1950° F. (1010° C.-1066° C.) for a time sufficient to substantially completely dissolve any precipitates in the alloy matrix and to fully recrystallize the grain structure. The time at the solution temperature depends on the thickness of the part. The alloy is then quenched, preferably in oil.
  • To further develop the high strength of the alloy, it is subjected to a refrigeration treatment after it is quenched. The refrigeration treatment cools the alloy to a temperature sufficiently below the martensite finish temperature to ensure the completion of the martensite transformation. Preferably, the refrigeration treatment comprises cooling the alloy to about −100° F. (−73° C.) or lower for a time sufficient to ensure that the alloy has substantially completely transformed to martensite. The need for a refrigeration treatment will be affected, at least in part, by the martensite finish temperature of the alloy. If the martensite finish temperature is sufficiently high, the transformation to a martensitic structure can proceed without the need for a refrigeration treatment. In addition, the need for a refrigeration treatment may also depend on the section size of the piece being manufactured. As the section size of the piece increases, segregation in the alloy becomes more significant and the use of a refrigeration treatment becomes more beneficial. Further, the length of time that the piece is chilled may need to be increased for large pieces in order to complete the transformation to martensite. For example, it has been found that a refrigeration treatment lasting a minimum of about 8 hours is preferred for developing the high strength that is characteristic of this alloy.
  • The alloy of the present invention is age hardened in accordance with techniques used for the known precipitation hardening, stainless steel alloys, which treatments are known to those skilled in the art. For example, the alloys are preferably aged at about 950-975° F. (510-524° C.) for a time sufficient to ensure that the alloy is substantially uniformly heated to the aging temperature depending on the thickness of the part and typically for an additional 4 to 8 hours to complete the aging reaction and to reach the desired combination of strength and toughness. The specific aging temperature used is selected by considering that: (1) the ultimate tensile strength of the alloy decreases as the aging temperature increases; and (2) the time required to age harden the alloy to a desired strength level increases as the aging temperature decreases.
  • The alloy of the present invention can be formed into a variety of product shapes for a wide variety of uses and lends itself to the formation of billets, bars, rod, wire, strip, plate, or sheet using conventional practices. The alloy of the present invention is useful in a wide range of practical applications which require an alloy having a good combination of corrosion resistance, strength, and toughness. In particular, the alloy of the present invention can be used to produce structural members for aircraft, including but not limited to landing gear components and fasteners. The alloy is also well suited for use in medical and dental applications such as dental tools and medical scrapers, cutters, and suture needles.
    • WORKING EXAMPLES
  • In order to demonstrate the novel combination of strength, toughness, and corrosion resistance provided by the alloy according to this invention, a comparative testing program was carried out. Seven 35 lb. heats having the weight percent compositions set forth in Table I below were produced by VIM.
  • TABLE I
    Elmt. Ex. 1 Ex. 2 Ex. A Ex. B. Ex. C Ex. D. Ex. E
    C 0.002 0.003 0.005 0.002 0.002 0.002 0.003
    Mn <0.01 <0.01 <0.01 <0.01 <0.01 <0.01 <0.01
    Si <0.01 <0.01 0.04 <0.01 <0.01 <0.01 <0.01
    P <0.005 <0.005 0.005 <0.005 <0.005 <0.005 <0.005
    S 0.0006 0.0005 0.0009 0.0005 0.0005 0.0005 0.0005
    Cr 11.42 11.49 11.35 11.48 11.47 11.47 11.47
    Ni 11.04 10.66 10.86 11.01 11.04 10.41 10.00
    Mo 0.95 0.95 0.94 0.95 0.95 0.95 0.95
    Co 0.98 0.98 (Note) 1.96 2.94 1.96 2.94
    Ti 1.63 1.62 1.54 1.63 1.65 1.63 1.63
    Al 0.55 0.57 0.07 0.53 0.50 0.54 0.54
    Cb 0.50 0.51 <0.01 0.51 0.54 0.50 0.51
    B 0.0021 0.0019 0.0023 0.0019 0.0021 0.0021 0.0022
    N 0.0015 0.0014 0.0013 0.0011 0.0014 0.0015 0.0015
    Ca 0.0019 0.0021 0.0006 0.0021 0.0019 0.0019 0.0021
    (Note):
    No positive addition.

    The balance of each heat is iron and usual impurities. Examples 1 and 2 are representative of the alloy according to the present invention. Examples A to E are comparative alloys. In particular, Example A is within the scope of the alloy described in U.S. Pat. No. 5,681,526.
  • The VIM heats were melted and cast into 4″ square ingots. The ingots were charged into a furnace operating at 1500° F. and the furnace temperature was ramped up to 2300° F. Ingots were held at 2300° F. for 16 hours after which the furnace temperature was lowered to 2000° F. The ingots were held at 2000° F. until they were substantially fully equalized in temperature. The ingots were then double-end forged to 2¾″ square billet from starting temperature of 2000° F. and then hot cut into 3 pieces each. Pieces were re-heated at 2000° F., and double-end forged to 1¼″ square. The bars were again hot cut into 3 pieces and reheated at 2000° F. The bars were then single-end forged to 11/16″ square with no reheats. The bars were cooled in air, overage annealed at 1250° F. for 8 hours, and then air cooled.
  • Longitudinal smooth and notched (Kt=3) tensile samples, longitudinal Charpy V-notch (CVN) samples, and longitudinal rising step load (RSL) fracture toughness samples were machined from the bars of each heat. The samples from Examples 1, 2, B, C, D, and E were solution treated at 1900° F. for 1 hour and oil quenched. The samples from Example A were solution treated at 1800° F. in accordance with the usual practice for that alloy. After solution treatment, all samples were refrigerated at −100° F. for 24 hours then warmed in air to room temperature. The samples were then age-hardened at various temperatures ranging from 900° F. to 1000° F. Aging was conducted by holding the samples at temperature for 4 hours in air and then quenching the samples in water.
  • The results of room temperature tensile testing on the samples of each heat are shown in Tables IIA and IIB below including the 0.2% offset yield strength (Y.S.) and the ultimate tensile strength (U.T.S) in ksi, the percent elongation (% El.), the percent reduction in area (% R.A.), and the notch tensile strength (N.T.S.) in ksi.
  • TABLE IIA
    Heat Solution Age Y.S. U.T.S. % EI. % R.A. N.T.S.
    Ex. 1 1900° F. 900° F. —  —  —  — 
    257 280 7.1 29.5
    257 283 6.6 28.8
    925° F. 255 280 9.1 36.6
    263 286 8.0 31.8
    263 286 8.2 35.1
    950° F. 268 286 9.8 45.8 282
    261 284 10.0 44.0 320
    258 283 8.9 40.9 282
    975° F. 260 280 10.1 43.8
    263 280 10.8 49.8
    258 280 9.7 47.0
    Ex. 2 1900° F. 900° F. —* —* —* —*
    259 285 —* —*
    252 284 —* —*
    925° F. 270 292 7.6 34.4
    271 294 7.6 35.4
    267 289 9.0 41.0
    950° F. 272 292 8.9 37.8
    274 290 11.0 47.0
    262 283 9.5 46.6
    975° F. 264 283 10.2 46.6 227
    259 279 11.5 50.3 239
    267 285 10.6 47.6 233
    Ex. A 1800° F. 925° F. 250 265 11.3 56.7 —
    248 262 11.4 58.2 —
    250 265 12.5 58.9 —
    950° F. 245 258 10.9 56.1 384
    247 261 13.5 60.4 396
    247 261 11.6 55.8 402
    975° F. 237 249 12.6 63.4 —
    230 241 11.7 55.3 —
    231 241 11.9 60.7 —
    Ex. B 1900° F. 900° F. 241 273 7.6 24.6
    248 274 7.7 29.9
    246 274 7.8 30.7
    925° F. 251 275 9.2 38.8
    254 277 10.4 39.5
    247 273 9.2 41.1
    950° F. 252 277 9.6 42.6
    259 281 8.5 35.2
    244 277 9.1 39.6
    975° F. 241 270 9.0 42.7
    244 266 11.3 53.3
    249 272 10.8 50.4
    *Samples fractured in a manner such that valid results could not be obtained.
  • TABLE IIB
    Heat Solution Age Y.S. U.T.S. % EI. % R.A. N.T.S.
    Ex. C 1900° F. 900° F. 241 272 8.4 30.2
    237 272 8.0 30.4
    243 272 8.1 29.6
    925° F. 244 273 9.5 36.8
    239 274 9.8 37.4
    244 276 8.4 36.2
    950° F. 253 275 10.4 43.3
    250 274 9.9 38.7
    247 271 —* 39.3
    975° F. 243 264 11.9 52.6
    243 267 10.8 50.9
    241 264 11.3 49.8
    Ex. D 1900° F. 925° F. 269 275 —* —*
    274 293 6.0 27.5
    —* —* —* —*
    950° F. 264 291 9.9 43.7
    260 291 9.9 36.4
    268 295 9.4 42.3
    975° F. 263 281 9.3 48.5 271
    276 289 8.9 47.4 283
    273 290 9.4 44.2 240
    1000° F.  251 269 11.6 59.0
    252 270 11.5 54.6
    250 275 11.4 54.5
    Ex. E 1900° F. 925° F. 270 295 3.6  9.4
    274 295 4.5 10.6
    271 293 8.7 34.6
    950° F. 276 296 8.0 42.1
    270 290 8.7 40.8
    280 295 7.4 34.4
    975° F. —* —* —* —*
    268 291 8.5 43.5
    269 287 8.7 43.5
    1000° F.  257 272 10.6 49.9
    263 277 10.4 49.3
    259 278 9.1 45.1
  • The results of Charpy V-notch (CVN) impact testing of Examples 1, 2, and D are shown in Table III below including the aging temperature, the Rockwell C-scale hardness (HRC), and the impact toughness (CVN) in foot-pounds. CVN testing was performed in accordance with ASTM Standard Test Procedure E23.
  • TABLE III
    Example Age HRC CVN Avg.
    Ex. 1 950° F. 54.0 4.4, 4.3, 3.8 4
    Ex. 2 975° F. 53.5 4.3, 4.4, 4.0 4
    Ex. D 975° F. 54.0 4.1, 4.6, 3.7 4
  • Rising Step Load (RSL) samples for plane-strain fracture toughness testing and stress corrosion cracking resistance (SCC) were finish machined from the age-hardened bars of Examples 1, 2, A, and D. Two samples from each heat were tested in air to provide a fracture toughness value (KO. Additional samples were tested in 3.5% NaCl solution, natural pH, at room temperature, to provide a threshold stress intensity value (KISCC). Testing was performed on a test machine that meets the requirements of ASTM Standard Test Procedure E1290. The results of room temperature fracture toughness testing (KIc) and stress corrosion cracking testing for Examples 1, 2, A, and D are presented in Table IV below including the plane-strain fracture toughness (KIc) in ksi√in and the threshold stress intensity to produce stress corrosion cracking (KISCC) in ksi√in. KISCC is reported for each step interval and as a final value. The lowest of the measured values for each example is designated as the final value of KISCC in accordance with the standard test procedure. The tensile strength values for each example are also reported in Table IV to show that the fracture toughness and stress corrosion cracking resistance were measured on alloys having similar levels of strength.
  • TABLE IV
    Avg. KISCC
    Example Solution Age U.T.S. 1 hour steps 2 hour steps 4 hour steps Final KISCC KIC
    Ex. 1 1900° F. 950° F. 284 26.3 26.0 28.8 26 47.3, 46.0
    Ex. 2 1900° F. 975° F. 282 29.0 22.0 34.8 22 45.5, 49.0
    Ex. A 1800° F. 950° F. 260 71.6 32.3 36.0 32 90.5
    Ex. D 1900° F. 975° F. 287 31.4 23.6 27.3 24 43.5, 42.1
  • Duplicate salt spray corrosion test cones were finish machined from the bars of Examples 1, 2, A, D after age-hardening. The cone samples were prepared by turning and hand polishing to a 600 grit finish. Prior to testing, all salt spray cones were passivated using 20% Nitric acid+3 oz./gallon Sodium Dichromate at 120/140° F. for 30 minutes. Samples were tested in accordance with ASTM B117, using a 5% NaCl concentration, natural pH, at 95° F. for 200 hour test duration. Time to first rust was noted for all samples, as well as a final rating after the completion of 200 hours test duration. The results of the salt-spray testing are shown in Table V below including the time to first appearance of rust and a final rating after the completion of the test duration. The ratings are defined as follows: 1=no rust, 2=1-3 rust spots, 3=<5% rust, 4=5-10%, 5=10-20%, 6=20-40%, 7=40-60%, 8=60-80%, 9=>80%.
  • TABLE V
    Example Solution Age First Rust Final Rating
    Ex. 1 1900° F. 950° F. None, None 1, 1
    Ex. 2 1900° F. 975° F. None, None 1, 1
    Ex. A 1800° F. 950° F. None, None 1, 1
    Ex. D 1900° F. 975° F. None, None 1, 1
  • Cyclic polarization (pitting) test samples were finish machined from the aged bars of Examples 1, 2, A, and D. Scans to measure pitting resistance were run on duplicate samples from each of those examples. The samples were tested in 3.5% NaCl solution, natural pH, at room temperature and were cleaned but not passivated prior to testing. Testing was performed with a modified ASTM Standard Test procedure G61 as described below. Voltage values at the knee of the curve and protection potentials were measured for all samples. The results of the potentiodynamic pitting tests are shown in Table VI below including the pitting potential and the protection potential in millivolts (mV).
  • TABLE VI
    Example Solution Age mV @ knee Protection Potential
    Ex. 1 1900° F. 950° F. 62.7, 66.7 11.1, 34.9
    Ex. 2 1900° F. 975° F.  76.2, 126.2 −12.7, −60.3
    Ex. A 1800° F. 950° F.  76.2, 118.0 19.5, −8.7
    Ex. D 1900° F. 975° F. 110.0, 126.2 −52.4, none 
  • A steel article made from the alloy described above and processed in accordance with the foregoing processing steps provides a combination of properties that make it particularly useful for aircraft landing gear and other aircraft structural components, including but not limited to flap tracks and slat tracks, and for other applications where both high strength and corrosion resistance are required. In particular, a steel article fabricated from the alloy that is solution heat treated and age hardened as described above provides a tensile strength of at least 280 ksi and a fracture toughness (KIc) of at least 45 ksi√in when tested with a test machine that meets the requirements of ASTM Standard Test Procedure E1290. A steel article in accordance with this invention is also characterized by a Charpy V-notch impact energy of at least about 4 ft-lbs when tested in accordance with ASTM Standard Test Procedure E23. Further, a steel article in accordance with this invention is characterized by general corrosion resistance such that the article does not rust when tested in accordance with ASTM Standard Test procedure B 117 and by sufficient pitting corrosion resistance such that the article has a pitting potential of at least 62 mV when tested in accordance with a modified ASTM Standard Test procedure G61. The ASTM G61 test procedure was modified by using round bar rather than flat samples. The use of round bar samples exposes the end grains and can be considered to be a more severe test than the standard G61 procedure.
  • The terms and expressions which are employed in this specification 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.

Claims (26)

1. A precipitation hardenable, martensitic stainless steel alloy having a unique combination of strength, toughness, and corrosion resistance comprising in weight percent, about
C  0.03 max Mn  1.0 max Si  0.75 max P 0.040 max S 0.020 max Cr 10-13 Ni 10.5-11.6 Mo 0.25-1.5  Cu  0.75 max Co 0.5-1.5 Ti 1.5-1.8 Al 0.3-0.8 Cb 0.3-0.8 B 0.010 max N 0.030 max
and the balance is iron and usual impurities.
2. The alloy recited in claim 1 which contains no more than about 0.50% copper.
3. The alloy recited in claim 1 which contains at least about 0.75% cobalt.
4. The alloy recited in claim 1 which contains at least about 0.4% columbium.
5. The alloy recited in claim 1 which contains at least about 10.75% nickel.
6. The alloy recited in claim 1 which contains at least about 0.4% aluminum.
7. The alloy recited in claim 1 which contains at least about 10.5% chromium.
8. The alloy recited in claim 1 which contains not more than about 12.5% chromium.
9. The alloy recited in claim 1 which contains not more than about 1.7% titanium.
10. The alloy recited in claim 1 which contains not more than about 1.25% molybdenum.
11. The alloy recited in claim 1 which contains at least about 0.75 weight percent molybdenum.
12. The alloy recited in claim 1 which contains up to about 0.003% calcium.
13. The alloy recited in claim 1 which contains up to about 0.025% cerium.
14. A precipitation hardenable, martensitic stainless steel alloy having a good combination of corrosion resistance, strength, and toughness comprising in weight percent, about
C 0.02 max Mn 0.25 max Si 0.25 max P 0.015 max  S 0.010 max  Cr 10.5-12.5 Ni 10.75-11.25 Mo 0.75-1.25 Cu 0.50 max Co 0.75-1.25 Ti 1.5-1.7 Al 0.4-0.7 Cb 0.4-0.7 B 0.001-0.005 N 0.015 max 
and the balance is iron and usual impurities.
15. The alloy recited in claim 14 which contains not more than about 1.1% cobalt.
16. The alloy recited in claim 14 which contains at least about 0.9% cobalt.
17. The alloy recited in claim 14 which contains at least about 10.85% nickel.
18. The alloy recited in claim 14 which contains not more than about 0.6% columbium.
19. The alloy recited in claim 14 which contains at least about 0.45% aluminum.
20. The alloy recited in claim 14 which contains not more than about 0.65% aluminum.
21. The alloy recited in claim 14 which contains at least about 0.9% molybdenum.
22. The alloy recited in claim 14 which contains up to about 0.003% calcium.
23. The alloy recited in claim 14 which contains up to about 0.025% cerium.
24. A precipitation hardenable, martensitic stainless steel alloy having a good combination of corrosion resistance, strength, and toughness consisting essentially of, in weight percent, about
C 0.015 max Mn  0.10 max Si  0.10 max P 0.010 max S 0.005 max Cr 11.0-12.0 Ni 10.85-11.25 Mo 0.9-1.1 Co 0.9-1.1 Cu  0.25 max Ti 1.5-1.7 Al 0.45-0.65 Cb 0.4-0.6 B 0.0015-0.0035 N 0.010 max
and the balance is iron and usual impurities.
25. The alloy recited in claim 24 which contains up to about 0.003% calcium.
26. The alloy recited in claim 24 which contains up to about 0.025% cerium.
US13/706,800 2012-12-06 2012-12-06 High Strength Precipitation Hardenable Stainless Steel Abandoned US20140161658A1 (en)

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EP13814314.4A EP2929062A1 (en) 2012-12-06 2013-12-06 High streng preciptation hardenable stainless steel
PCT/US2013/073542 WO2014089418A1 (en) 2012-12-06 2013-12-06 High streng preciptation hardenable stainless steel
KR1020157015534A KR101780875B1 (en) 2012-12-06 2013-12-06 High strength precipitation hardenable stainless steel
CA2893272A CA2893272C (en) 2012-12-06 2013-12-06 High strength precipitation hardenable stainless steel
BR112015013006A BR112015013006A2 (en) 2012-12-06 2013-12-06 precipitation hardened martensitic stainless steel alloy
CN201380072413.4A CN105102649A (en) 2012-12-06 2013-12-06 High streng preciptation hardenable stainless steel
JP2015545869A JP6117372B2 (en) 2012-12-06 2013-12-06 High strength precipitation hardening stainless steel
US15/210,107 US20160319406A1 (en) 2012-12-06 2016-07-14 High Strength Precipitation Hardenable Stainless Steel
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