US3479157A - Welded articles and alloys containing hafnium and nickel - Google Patents

Welded articles and alloys containing hafnium and nickel Download PDF

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Publication number
US3479157A
US3479157A US559456A US3479157DA US3479157A US 3479157 A US3479157 A US 3479157A US 559456 A US559456 A US 559456A US 3479157D A US3479157D A US 3479157DA US 3479157 A US3479157 A US 3479157A
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Prior art keywords
hafnium
alloys
zirconium
alloy
boron
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US559456A
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Edward Gordon Richards
David Marshall Ward
Keith John Hales
Norman Stephenson
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Huntington Alloys Corp
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International Nickel Co Inc
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3033—Ni as the principal constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3033—Ni as the principal constituent
    • B23K35/304—Ni as the principal constituent with Cr as the next major constituent
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/06—Alloys based on chromium
    • 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
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12931—Co-, Fe-, or Ni-base components, alternative to each other

Definitions

  • This invention relates to nickel-base alloys and, more particularly, to hafnium-containing nickel-base alloys having improved weldability.
  • nickel-containing alloys are well known to have exceptional strength at high temperatures and are commonly used when creep resistance is essential. These alloys vary widely in composition, but all those with which this invention is concerned are age-hardened and have a face-centered cubic lattice structure and a base consisting, in addition to nickel, of one or more of iron, cobalt, and chromium, with or without one or more metals of high melting point such as tungsten, molybdenum, niobium and tantalum.
  • nickel may be the main constituent, and then normally amounts to 30% or more of the alloy, or only a minor constituent as, for example, in the age-hardenable stainless steels. In general, all the alloys in question contain at least 7.5% nickel.
  • the alloys with which this invention is concerned are of a composition such that a strengthening phase is precipitated upon heat treatment.
  • the strengthening phase is carbidic and in others, it contains titanium or aluminum or both.
  • alloys in which the highest strength at high temperature, say 650 C. and above, is required commonly contain both boron and zirconium in amounts up to 0.03% boron and 0.3% zirconium.
  • the surfaces being welded are displaced by thermal expansion to a greater extent than if it is low, thus increasing the stress to which the hot weld metal and the heat-affected zones are subjected during contraction when the welded structure cools. If there is complete restraint of relative movement, the deposited metal and the heat-affected zones are subjected to much more stress as a result of the contraction on cooling than if the welded surfaces can move towards one another. In either case cracking may occur.
  • the degree of restraint in a joint of a given configuration also depends on the section size of the component parts. Thicker sections are less able to yield on cooling and thereby relieve the stress on the joint. In a thick section, e.g. one greater than one-half inch, the effects of thermal expansion at right angles to the plate surface lead to additional stress in the joint, which increases as the thickness increases.
  • boron and zirconium on weldability depends both on the composition of the alloys as a whole and on the content of boron or zirconium or both. Some of the alloys are not weldable even when they are free from boron and zirconium. In other alloys the presence of either boron or zirconium inhibits weldability, even under the most favorable welding conditions. Still other alloys can be welded when the contents of boron and zirconium are very small, but lose weldability when the contents of boron and zirconium are increased to desirable values.
  • age-hardenable alloys containing boron and/or zirconium in amounts sufficient to substantially increase strength and ductility, can be made weldable without adversely affecting strength or ductility.
  • An object of the present invention is to provide high temperature alloys having high strength, ductility and weldability.
  • Another object of this invention is to provide high temperature, age-hardenable. alloys containing boron and/or zirconium which can be welded without cracking.
  • a further object of this invention is to provide a welded, high temperature alloy free from cracks and other weld defects.
  • FIGURES 1 to 3 show the permissible levels of boron and/or zirconium as a function of hafnium content in alloys of three different base compositions
  • FIGURE 4 shows the effect of hafnium on the multiplying factor.
  • the invention is based on the surprising discovery that the weldability of alloys of the kind in question containing boron or zirconium or both is much improved if the alloys contain a small amount of hafniums, and generally speaking, the present invention contemplates weldable, e.g., arc-weldable or otherwise, age-hardenable, nickel base alloys containing boron and/or zirconium with small additions of hafnium.
  • the improvement due to hafnium appears to be only a little affected by the base composi tion of the alloy, but to be dependent upon the boron and zirconium contents.
  • hafnium Extremely small additions of hafnium, that is to say as little as 0.005% or less, improve the weldability of the alloys, but the greatest improvement is obtained with amounts of hafnium in the range of 0.007% to 0.07%.
  • the way in which hafnium acts is not understood.
  • the hafnium increases the melting point of grain boundary constituents and thus reduces or eliminates liquid films around the grains which provide lines of Weakness in the alloy during cooling after welding.
  • the hafnium addition may change the way in which the zirconium and boron are distributed in the alloy, and thus counteract their adverse effect on weldability.
  • hafnium enables us to produce welded articles in which at least one of the surfaces that are welded together is of an alloy of the kind in question that contains boron or zirconium or both and also hafnium in an amount such as to render the alloy or alloys Weldable despite the presence of the boron or zirconium or both.
  • Weldable alloys in accordance with the invention have a face-centered cubic lattice structure and comprise up to about 35% chromium, up to about 30% or even 45% cobalt, up to about 80% iron, up to about 1.5% carbon, up to about 10% manganese, up to about 2% copper, up to about 10% molybdenum, up to about 15% or 20% or even 27% tungsten, up to about 10% niobium, up to about 10% tantalum, up to about 8% silicon, up to about 8% titanium, up to about 8% aluminium, up to about 2% vanadium, at least one metal selected from the group consisting of boron and zirconium, an amount of hafnium effective to prevent cracking of the alloy on welding, and the balance essentially nickel in amounts of at least 7 .5%.
  • One group of such alloys in which the strengthening phase contains titanium and aluminium comprises about 12% to 22% chromium, up to about 23% cobalt, up to about 40% iron, up to about 0.2% carbon, up to about 1% manganese, up to about 0.5% copper, up to about 6% molybdenum, up to about 2% tungsten, up to about 2% niobium, up to about 2% tantalum, up to about 2% silicon, about 0.2% to 3.5% titanium, about 0.1% to aluminium, 0.005 to 0.2% hafnium, at least one metal selected from the group consisting of boron and Zirconium,
  • hafnium present in amounts of at least about 7.5%.
  • amount of hafnium present will be from 0.001% to 0.5%, e.g. about 0.005% to 0.2% hafnium.
  • the amount of hafnium required to provide weldability in an alloy of given base composition may readily be determined without the need to produce test plates of large numbers of alloys of different composition by a simple test in which weld deposits of the alloy under test is made between plates of an alloy of the base compositionfree from boron, zirconium and hafnium, the deposits being formed from cast filler rods containing varying amounts of these elements; such filler rods can be made quite easily.
  • a vertical and horizontal plate of an alloy of the base composition under test were arranged in the form of an inverted T, the vertical plate being held A3" away from the horizontal plate by a spacer.
  • the plates were joined and held in position by a' weld along one lower edge of the vertical plate and by metal supports welded to both plates and arranged at right angles to both of them, on the side on which the holding weld between the plates was made.
  • the plates forming the T were free from boron, zirconium and hafnium.
  • test weld was made between the other lower edge of the vertical plate and the adjacent surface of the horizontal plate, using the inert-gas-shielded tungsten-arc process, using a A" diameter filler rod of the alloy of which the weldability was being tested.
  • This had the same base composition as the plates of the T, but also contained one or more of boron, zirconium and hafnium.
  • a single pass was made, and the resulting weld deposit was inspected with the naked eye, the absence of any visible cracks being taken as the criterion of weldability of the alloy of the composition of the deposit.
  • FIGURES 1 to 3 of the accompanying drawings each of which is a graph in which the boron contents are plotted as abscissae and the zirconium contents as ordinates.
  • FIGURE 1 relates to alloys all nominally containing 20% chromium, 16% cobalt, 2.4% titanium and 1.2% aluminium, the balance being substantially all nickel, except for varying amounts of boron, zirconium and hafnium.
  • Each of the lines in FIGURE 1 indicates the approximate boundary zone for weldability in accordance with the hafnium content, those alloys with compositions such as to fall below the line being Weldable.
  • FIGURE 1 can be used to determine the amount of hafnium required in an alloy of any given boron and zirconium content.
  • an alloy containing 0.005% boron and 0.02% zirconium is indicated by the point X in FIGURE 1, which is just above the 0.005% hafnium line, and so should contain more than 0.005 hafnium to be Weldable. However, it is also above the 0.1% hafnium line, so 0.1% hafnium is too much.
  • FIGURE 1 also shows that the beneficial effect of hafnium decreases as the hafnium content increases above 0.03%, but the upper limit of the hafnium content that brings about improvement depends not only on the total content of boron and zirconium but also upon their relative contents.
  • the presence of 0.1% hafnium actually decreases the weldability, and the upper limit of the hafnium content in such an alloy is 0.08%.
  • hafnium contents of 0.2% or more improve the weldability.
  • FIGURE 2 relates to the welding of alloys nominally containing 42% nickel, 16% chromium, 3.3% molybdenum, 1.2% titanium and 1.2% aluminium, the balance being substantially all iron, except for varying quantities of boron, zirconium and hafnium. It will be seen that in an alloy (Y) containing 0.005% boron and 0.02% zirconium, 0.01% hafnium will confer weldability. Again 0.1% hafnium is too much.
  • FIGURE 3 relates to alloys all nominally containing 15% chromium, 20% cobalt, 5% molybdenum, 1.2% titanium and 4.6% aluminium, the balance being nickel except for varying quantities of boron, zirconium and hafnium. Alloys of this base composition are unweldable in the absence of boron and zirconium, as is shown by FIGURE 3. The invention enables these alloys to be welded even when they contain boron and zirconium. It will be seen, for example that in an alloy (Z) again containing 0.005% boron and 0.02% zirconium, 0.01% hafnium is not enough, but only a little more is required. On the other hand 0.1% hafnium is too much.
  • FIGURE 4 of the accompanying drawings the multiplying factors for both boron and zircopium are plotted against hafnium content, the curves in full lines relating to the alloys of FIGURE 1, those in broken lines to the alloys of FIGURE 2, and those in chain lines to the alloys of FIGURE 3.
  • FIGURE 4 clearly shows the desirablity of working in the range of 0.007% to 0.07% hafnium.
  • a welded article according to the invention may consist of a single piece of an alloy having two surfaces Welded together to form, for example, a tube; of two components of the same alloy welded together; of two components of different alloys each of the kind in question welded together; or of a component of an alloy of the kind in question welded to a weldable metal or alloy.
  • the beneficial effect is to prevent cracking in the heat affected zone of the alloy of the kind in question.
  • the welding may be effected with or without a filler.
  • the filler may conveniently be of an alloy of the kind in question, which preferably but not necessarily also contains boron or zirconium or both. If it does contain boron or zirconium or both it should contain hafnium as well.
  • the most uniform properties throughout a welded structure are generally obtained when the surfaces that are welded together and the filler used in the welding are all of the same alloy.
  • a filler that is less susceptible to cracking may advantageously be used.
  • the parts to be welded are of dissimilar alloys, it is advantageous to use a filler different in composition from, but compatible with both the alloys.
  • the nickel base alloys which are weldable in accordance with this invention and the alloys for use as filler material may be prepared in the usual manner of preparing high temperature alloys. In this regard, preparation by vacuum melting is satisfactory but is not essential.
  • Hafnium and zirconium commonly occur together in nature, and it may be convenient to introduce the desired amounts of hafnium and zirconium by means of an addition agent containing both of these metals, e.g. a nickelzirconium-hafnium alloy.
  • EXAMPLE I An alloy, prepared in the usual manner, contained 20% chromium, 16% cobalt, 2.4% titanium, 1.2% aluminium, 0.003% boron, 0.02% zirconium, 0.08% hafnium, balance essentially nickel. A second alloy, prepared in the same manner, contained 0.11% hafnium, but otherwise had a composition identical to the first. A third alloy,
  • An alloy prepared in the usual manner, contained 42% nickel, 16% chromium, 3.3% molybdenum, 1.2%titaniurn, 1.2% aluminium, 0.004% boron, 0.02% zirconium, 0.1% hafnium, balance substantially iron.
  • Another alloy prepared in the same manner, had an identical composition to the first except that it did not contain hafnium. Butt welds were made between pairs of A3 inch thick plates of the alloys by the metal-inert gas short are proc ess under highly restrained conditions, using a filler of the same composition as the plates being welded. The heat affected zone of the hafnium free alloy showed cracks while the weld made with the hafnium containing alloy was sound.
  • EXAMPLE III This is an example of welding with a non-matching filler material.
  • An alloy prepared in the usual manner, contained 42% nickel, 16% chromium, 3.3% molybdenum, 1.2% titanium, 1.2% aluminium, 0.003% boron, 0.02% zirconium, 0.07% hafnium, balance essentially iron.
  • Another alloy prepared in the same manner, had an identical composition to the first except that it did not contain hafnium. Butt joints were made between pairs of inch thick plates of the alloys, under highly re strained conditions, using the metal-inert gas spray transfer welding process.
  • the filler material employed was a nickel-base alloy containing 16% chromium, 10% iron, 2% manganese and 3% titanium, the balance being nickel. The plates of hafnium-free alloy cracked in the heat-affected zone, but sound welds were obtained between those of the hafnium-containing alloy.
  • hafnium in the amounts required by the invention in alloys of the kind in question that contain boron or zirconium or both has not been found to impair the stress-rupture properties of the alloys.
  • the good welding characteristics displayed by the alloys of this invention greatly enhance their potential for high temperature applications such as, for example, use in aircraft gas turbines as jet pipes, flame tubes and jet silencers.
  • a crack-free welded article having at least one metal body with a fused joint therein with at least one of the surfaces at the fused joint being made of an age-hardenable nickel-containing alloy having a face-centered cubic lattice structure and being composed of at least one metal from the group consisting of iron, cobalt and chromium; iron, when present, being present in an amount up to cobalt, when present, being present in an amount up to 45%; chromium when present, being present in an amount up to 35%, up to about 1.5% carbon, up to about 10% manganese, up to about 2% copper, up to about 10% molybdenum, up to 27% tungsten, up to about 10% niobium, up to about 10% tantalum, up to about 8% silicon, up to about 8% titanium, up to about 8% aluminum, up to about 2% vanadium, at least one element selected from the group consisting of boron in an amount up to 0.03% and zirconium in an amount up to 0.3% to strengthen and
  • a welded article in accordance with claim 1 wherein the alloy is nickel-base and is composed of about 20% chromium, about 16% cobalt, about 2.4% titanium, about 1.2% aluminium, at least about 0.001% boron, at least about 0.02% zirconium and about 0.08% to 0.11% hafmum.
  • a weldable age-hardenable nickel-containing alloy composed of about 12% to 22% chromium, up to about 23% cobalt, up to about 40% iron, up to about 0.2% carbon, up to about 1% manganese, up to about 0.5% copper, up to about 6% molybdenum, up to about 2% tungsten, up to about 2% niobium, up to about 2% tantalum, up to about 2% silicon, about 0.2% to 3.5% titanium, about 0.1% to 5% aluminium, about 0.005% to 0.2% hafnium, at least one metal selected from the group consisting of boron in an amount up to 0.03% and zirconium in an amount up to 0.3% and the balance essentially nickel in an amount of at least 7.5%.

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US559456A 1965-06-25 1966-06-22 Welded articles and alloys containing hafnium and nickel Expired - Lifetime US3479157A (en)

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GB27074/65A GB1070099A (en) 1965-06-25 1965-06-25 Welding high-temperature alloys

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AT (1) AT270245B (de)
BE (1) BE683097A (de)
CH (1) CH462598A (de)
DE (1) DE1533285A1 (de)
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Cited By (20)

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US3753697A (en) * 1971-01-18 1973-08-21 Martin Marietta Corp Tungsten free alloy
US3765879A (en) * 1970-12-17 1973-10-16 Martin Marietta Corp Nickel base alloy
US3804680A (en) * 1970-06-06 1974-04-16 Atomic Energy Commission Method for inducing resistance to embrittlement by neutron irradiation and products formed thereby
US3865581A (en) * 1972-01-27 1975-02-11 Nippon Steel Corp Heat resistant alloy having excellent hot workabilities
US3898109A (en) * 1973-09-06 1975-08-05 Int Nickel Co Heat treatment of nickel-chromium-cobalt base alloys
US4039330A (en) * 1971-04-07 1977-08-02 The International Nickel Company, Inc. Nickel-chromium-cobalt alloys
US4530727A (en) * 1982-02-24 1985-07-23 The United States Of America As Represented By The Department Of Energy Method for fabricating wrought components for high-temperature gas-cooled reactors and product
US4774149A (en) * 1987-03-17 1988-09-27 General Electric Company Oxidation-and hot corrosion-resistant nickel-base alloy coatings and claddings for industrial and marine gas turbine hot section components and resulting composite articles
US5783318A (en) * 1994-06-22 1998-07-21 United Technologies Corporation Repaired nickel based superalloy
US6258317B1 (en) 1998-06-19 2001-07-10 Inco Alloys International, Inc. Advanced ultra-supercritical boiler tubing alloy
US6761854B1 (en) 1998-09-04 2004-07-13 Huntington Alloys Corporation Advanced high temperature corrosion resistant alloy
US20060051234A1 (en) * 2004-09-03 2006-03-09 Pike Lee M Jr Ni-Cr-Co alloy for advanced gas turbine engines
US20060222557A1 (en) * 2004-09-03 2006-10-05 Pike Lee M Jr Ni-Cr-Co alloy for advanced gas turbine engines
US20130048700A1 (en) * 2011-08-29 2013-02-28 General Electric Company Filler metal chemistry for improved weldability of super alloys
US20130323533A1 (en) * 2012-06-05 2013-12-05 General Electric Company Repaired superalloy components and methods for repairing superalloy components
US20150306710A1 (en) * 2014-04-04 2015-10-29 Special Metals Corporation High Strength Ni-Cr-Mo-W-Nb-Ti Welding Product and Method of Welding and Weld Deposit Using the Same
US9346132B2 (en) 2011-08-29 2016-05-24 General Electric Company Metal chemistry for improved weldability of super alloys
US20190241995A1 (en) * 2018-02-07 2019-08-08 General Electric Company Nickel Based Alloy with High Fatigue Resistance and Methods of Forming the Same
US10610982B2 (en) 2015-11-12 2020-04-07 General Electric Company Weld filler metal for superalloys and methods of making
US11187082B2 (en) 2015-10-07 2021-11-30 Siemens Energy Global GmbH & Co. KG Method for making steel or titanium products containing a precipitation-hardening nickel-base alloy, and part

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Publication number Priority date Publication date Assignee Title
CA1109297A (en) * 1976-10-12 1981-09-22 David S. Duvall Age hardenable nickel superalloy welding wires containing manganese

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US3024109A (en) * 1957-12-24 1962-03-06 Gen Electric Elevated temperature, nickel-base brazing alloys
GB912814A (en) * 1959-01-21 1962-12-12 Allegheny Ludlum Steel Improvements in or relating to an austenitic nickel-chrome iron-base alloy
US3184577A (en) * 1963-01-18 1965-05-18 Int Nickel Co Welding material for producing welds with low coefficient of expansion
US3201233A (en) * 1962-06-13 1965-08-17 Westinghouse Electric Corp Crack resistant stainless steel alloys
US3262777A (en) * 1964-07-13 1966-07-26 Int Nickel Co Ultra tough maraging steel
US3303023A (en) * 1963-08-26 1967-02-07 Crucible Steel Co America Use of cold-formable austenitic stainless steel for valves for internal-combustion engines
US3342974A (en) * 1961-11-18 1967-09-19 Wallner Werner Arc welding electrode providing welds having high yield and rupture value

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Publication number Priority date Publication date Assignee Title
US2428033A (en) * 1941-11-24 1947-09-30 John S Nachtman Manufacture of rustproof electrolytic coatings for metal stock
US3024109A (en) * 1957-12-24 1962-03-06 Gen Electric Elevated temperature, nickel-base brazing alloys
GB912814A (en) * 1959-01-21 1962-12-12 Allegheny Ludlum Steel Improvements in or relating to an austenitic nickel-chrome iron-base alloy
US3342974A (en) * 1961-11-18 1967-09-19 Wallner Werner Arc welding electrode providing welds having high yield and rupture value
US3201233A (en) * 1962-06-13 1965-08-17 Westinghouse Electric Corp Crack resistant stainless steel alloys
US3184577A (en) * 1963-01-18 1965-05-18 Int Nickel Co Welding material for producing welds with low coefficient of expansion
US3303023A (en) * 1963-08-26 1967-02-07 Crucible Steel Co America Use of cold-formable austenitic stainless steel for valves for internal-combustion engines
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Cited By (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3804680A (en) * 1970-06-06 1974-04-16 Atomic Energy Commission Method for inducing resistance to embrittlement by neutron irradiation and products formed thereby
US3765879A (en) * 1970-12-17 1973-10-16 Martin Marietta Corp Nickel base alloy
US3753697A (en) * 1971-01-18 1973-08-21 Martin Marietta Corp Tungsten free alloy
US4039330A (en) * 1971-04-07 1977-08-02 The International Nickel Company, Inc. Nickel-chromium-cobalt alloys
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Also Published As

Publication number Publication date
CH462598A (fr) 1968-09-15
BE683097A (de) 1966-12-27
SE327614B (de) 1970-08-24
ES328348A1 (es) 1967-08-16
AT270245B (de) 1969-04-25
DE1533285A1 (de) 1969-12-18
GB1070099A (en) 1967-05-24

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