US3838981A - Wear-resistant power metallurgy nickel-base alloy - Google Patents

Wear-resistant power metallurgy nickel-base alloy Download PDF

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Publication number
US3838981A
US3838981A US00343845A US34384573A US3838981A US 3838981 A US3838981 A US 3838981A US 00343845 A US00343845 A US 00343845A US 34384573 A US34384573 A US 34384573A US 3838981 A US3838981 A US 3838981A
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percent
article
boron
alloys
alloy
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US00343845A
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E Foley
R Polk
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Stoody Co
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Cabot Corp
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Publication date
Application filed by Cabot Corp filed Critical Cabot Corp
Priority to US00343845A priority Critical patent/US3838981A/en
Priority to CA194,604A priority patent/CA1010266A/en
Priority to IN584/CAL/74A priority patent/IN142080B/en
Priority to JP3137574A priority patent/JPS5438971B2/ja
Priority to DE2413017A priority patent/DE2413017C2/de
Priority to BE142242A priority patent/BE812588A/xx
Priority to DD177303A priority patent/DD112469A5/xx
Priority to AU66886/74A priority patent/AU477193B2/en
Priority to CS7400002073A priority patent/CS185637B2/cs
Priority to NL7403850A priority patent/NL7403850A/xx
Priority to AT233774A priority patent/AT338537B/de
Priority to IT67901/74A priority patent/IT1011614B/it
Priority to SE7403839A priority patent/SE403914B/xx
Priority to CH394274A priority patent/CH589143A5/xx
Priority to BR742183A priority patent/BR7402183D0/pt
Priority to FR7409759A priority patent/FR2222447B1/fr
Priority to GB1255474A priority patent/GB1459873A/en
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Publication of US3838981A publication Critical patent/US3838981A/en
Assigned to STOODY COMPANY, A CORP. OF DE reassignment STOODY COMPANY, A CORP. OF DE ASSIGNMENT OF ASSIGNORS INTEREST. Assignors: CABOT CORPORATION, A CORP. OF DE
Assigned to WELLS FARGO BANK, N.A. reassignment WELLS FARGO BANK, N.A. SECURITY INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: STOODY DELORO STELLITE, INC.
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Expired - Lifetime 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
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0433—Nickel- or cobalt-based alloys
    • 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%
    • 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
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S75/00—Specialized metallurgical processes, compositions for use therein, consolidated metal powder compositions, and loose metal particulate mixtures
    • Y10S75/95—Consolidated metal powder compositions of >95% theoretical density, e.g. wrought

Definitions

  • ABSTRACT A wearand abrasion-resistant article of sintered metal powder consists of chromium from about 23 percent to about 29 percent, tungsten from about 8 percent to about 15 percent, cobalt from about 8 percent to about 15 percent, molybdenum from about 8 percent to about 15 percent, carbon from about 1.65 percent to about 5 percent, boron up to about 1 percent, manganese up to about 1.3 percent, silicon up to about 1.3 percent, iron from about 10 percent to about 17.5 percent, and the balance nickel in amount at least about 20 percent and incidental impurities.
  • o zmsxoom 39 B QEm Eoom Carbon WEAR-RESISTANT POWER METALLURGY NICKEL-BASE ALLOY
  • This invention relates to articles of wear and abrasion-resistant alloys. It is more particularly concerned with such articles sintered from powder of a nickelbase alloy.
  • Numbers of abrasion and wear-resistant alloys have been developed for articles subject to those service conditions. They exhibit high tensile strength and great hardness at temperatures as high as I,200F. to l,400F., impact strength of the order of 3 to 5 foot pounds, and in general are difficult or impossible to work. Consequently, they have been used in the form of castings which are sometimes ground to dimensions, or hard-surfaced deposits produced by welding.
  • cobalt-base alloys containing substantial amounts of chromium, tungsten and sometimes molybdenum.
  • Cobalt is an expensive constituent and attempts have been made to substitute therefor, at least in part, other less expensive elements.
  • a nickel-base alloy which for many purposes is used in place of the cobalt-base alloys is disclosed in U.S. Pat. No. 3,068,096, issued to J. K. Elbaum et al., on Dec, 1 l, 1962. Its hardness, however, drops off somewhat below that of the best of the cobalt-base alloys at temperatures above about 1,200F. This would seem to be because of a deficiency of hard carbide constituents.
  • a number of the cobalt-base and other types of wearresistant alloys can be fabricated by the powder metallurgy technique summarized above.
  • the nickel-base alloy of the Elbaum et al., patent is very difficult to fabricate into articles in this way.
  • the compacts must be sintered at a temperature of 2,300F. or more, plus or minus a few degrees.
  • the width of the sintering range is influenced by the size of the powder particles and may be as narrow as plus or minus 10F, which renders the process scarcely more than a laboratory operation. Grinding of the particles to a smaller size, which is a tedious and expensive operation, widens the sintering range to plus or minus 20 or 25F. This is still quite narrow for commercial practice and requires rather elaborate furnace controls.
  • the sintering operation be carried out as a continuous operation. This is economically accomplished by loading the green compacts into metal trays and passing the trays one after another through a tunnel furnace in which the desired atmosphere is maintained and in which the articles remain at temperature for the time required for sintering to be completed.
  • a convenient way to effect this operation is to use the tray of green compacts being introduced into one end of the furnace to push out a tray of sintered compacts from the other end of the furnace.
  • the furnace length may be a multiple of the tray length. As it happens, however, the metal trays normally used for this purpose, when heated to temperatures of 2,300F.
  • composition of the articles of our invention is set out in the accompanying Table 1.
  • the alloy powder which we employ is preferably produced by the atomization of a melt of the desired composition.
  • This melt is heated to a temperature of 200F. or so above its fusion temperature in a crucible.
  • this melting is carried out in vacuum or under a blanket of inert gas such as argon.
  • the melt is then poured into a preheated refractory tundish which is fashioned with a small-diameter nozzle in the bottom through which the stream of metal flows into an atomizing chamber.
  • the stream emerging from the nozzle is broken up into fine particles by a high-pressure jet of inert gas, or of water, which makes contact with the molten stream just below the nozzle.
  • the particles or droplets are almost instantaneously quenched by the atomizing fluid and fall into a reservoir in the bottom of the atomizing chamber. Only the fraction is used which passes through a 30 mesh screen. These particles are approximately spherical in shape and about 25 percent to 35 percent of the particles are -325 mesh. When articles of high density are to be produced we use only the -325 mesh fraction.
  • the blending of the powder and binder particles is accomplished in any suitable mixing apparatus.
  • the amount of binder is not critical, and a few percent by weight is sufficient.
  • the plastic or putty-like blend of particles, binder and solvent is then consolidated into agglomerates, preferably by extrusion, but other methods, such as roll briquetting, may be employed.
  • the extrusions are dried, crushed in a roller crusher, hammer mill or the like, and screened.
  • the 100 mesh fraction of crushed extruded bindered powder is largely fines. From about 60 percent to 80 percent of the particles are 325 mesh with corresponding apparent densities of about 2.0 to 3.3 grams per cc. Both the percentage of fines and the apparent density of this material are, however, less than those of the milled powder.
  • the agglomerates of powder and binder are pressed in dies or molds of the desired shape under a pressure of about 50 tons per sq. inch.
  • the compacting pressure can be as low as tons per sq. inch or as high as 70 tons per sq. inch, the density of the green compacts being higher at higher compaction pressures.
  • compact density is about 56 to 58 percent of cast density, and at tons per sq. inch it is 70 to 72 percent of cast density.
  • a finished article of the desired density is obtained by sintering the compact in vacuum or reducing atmosphere at a temperature between the solidus and liquidus temperatures of the alloy. Sintering can be completed in about an hour but if the time is extended to two or at most three hours the temperature can be reduced somewhat without impairing the properties of the article.
  • Compacts properly sintered have densities of 98 percent or better of cast density,
  • Our process also contemplates grinding, when necessary, of part or all of the powder particles resulting from the atomization of a melt as above described, so as to convert a larger fraction of the powder to 325 mesh.
  • our alloy here described with a carbon content of 2.4 percent, for example, can be sintered at temperatures between 2,190F. and 2,270F.
  • Our alloy with a carbon content of 4.2 percent can be sintered at temperatures as low as 2,110F. and as high as 2,210F.
  • FIG. 2 shows graphically how the Rockwell C scale room temperature hardness of our alloy increases with an increase in its carbon content.
  • this curve also is extended into the composition range of the Elbaum et al., patent.
  • the hardness is seen to increase almost linearly until the carbon content of the alloy reaches about 3.3 percent, beyond which the graph begins to bend over and reaches its peak at about 4 percent carbon content.
  • the room temperature hardness of our alloy with this carbon content is about 57 Rockwell C scale.
  • the maximum carbon content of our alloy is effectively limited by another consideration.
  • the boron content of our alloys is not critical. As we have pointed out, boron additions do not increase the allowable range of sintering temperatures of the alloys here concerned, but do lower the absolute value of those temperatures. The higher carbon contents of our alloys, on the other hand, bring about both broadening of the range of sintering temperatures and a lowering of the minimum sintering temperature. Thus, as the carbon content of our alloys is increased, their boron contents becomes less significant. We prefer to include boron in amounts of about 0.5 percent in our alloys, but as little as about 0.05 percent is effective, and there seems to be no advantage in using boron contents above about 1 percent. Our alloys may be made with no boron addition if the apparatus used for sintering can withstand the necessary sintering temperatures.
  • the nickel content of our alloy should be at least 20 percent by weight and the amounts of the other elements listed should be adjusted accordingly within the ranges specified for each element. Contrary to the teaching of the Elbaum et al., patent, cobalt cannot be replaced by any other element but must be present within the ranges indicated.
  • the elements other than carbon which are specified by Elbaum et al. act in the same way as they have described.
  • the modifying elements mentioned in Table 1 consist of zirconium, lanthanum, yttrium, vanadium, beryllium, magnesium and rare-earth metals. The presence of one or more of these elements in the amounts tabulated improves the working characteristics such as ductility and oxidation resistance of the alloy.
  • the optional elements mentioned in that Table consist of tantalum, columbium, titanium, aluminum, hafnium, and copper. The presence of these elements in the amounts tabulated is not detrimental to the hardness, impact resistance or sinterability of the alloy.
  • the alloys from which the data of FIGS. 1 and 2 were derived had approximately nominal compositions as set out in the Table, except for carbon content, and contained no modifying or optional elements.
  • the curve of room temperature hardness against sintering temperature and the curve of article density against sintering temperature peak together at a temperature below the liquidus temperature of the alloy, and the sintering temperature limits are chosen to bracket those peaks reasonably symmetrically.
  • the upper limit must, of course, be below the temperature at which the green compact begins to slump or lose its shape, and the lower limit is set at a temperature which produces an article density of at least of cast density in the desired sintering time.
  • An article of sintered metal powder consisting of chromium from about 23 percent to about 29 percent, tungsten from about 8 percent to about 15 percent, cobalt from about 8 percent to about 15 percent, molybdenum from about 8% to about 15 percent, carbon from about 1.65 percent to about 5 percent, boron up to about 1 percent, manganese up to about 1.3 percent, silicon up to about 1.3 percent, iron from about 10 percent to about 17.5 percent, and the balance nickel in amount at least about 20 percent and incidental impurities.
  • the article of claim 1 including boron from about 0.05 percent to about 1 percent.
  • the article of claim 1 containing chromium from about 25 percent to 27 percent, tungsten from about 9 percent to 11 percent, carbon from about 1.65 percent to about 4.2 percent, silicon up to about 1 percent, manganese up to about 1 percent, boron up to about 1 percent, cobalt from about 9 percent to about 11 percent, molybdenum from about 9 percent to about 11 percent and iron from about 11.5 percent to about 13.5 percent.
  • the article of claim 3 including boron from about 0.05 percent to about 1 percent.
  • the article of claim 1 containing chromium about 26 percent, tungsten about 10 percent, carbon about 1.65 percent to 4.2 percent, silicon about 1 percent, manganese about 0.75 percent, boron about 0.5 percent, cobalt about 10%, molybdenum about 10% and iron about 12.5%.
  • the article of claim 1 including one or more of the elements zirconium, lanthanum, yttrium, vanadium,

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
US00343845A 1973-03-22 1973-03-22 Wear-resistant power metallurgy nickel-base alloy Expired - Lifetime US3838981A (en)

Priority Applications (17)

Application Number Priority Date Filing Date Title
US00343845A US3838981A (en) 1973-03-22 1973-03-22 Wear-resistant power metallurgy nickel-base alloy
CA194,604A CA1010266A (en) 1973-03-22 1974-03-11 Wear-resistant powder metallurgy nickel-base alloy
IN584/CAL/74A IN142080B (xx) 1973-03-22 1974-03-18
JP3137574A JPS5438971B2 (xx) 1973-03-22 1974-03-19
DE2413017A DE2413017C2 (de) 1973-03-22 1974-03-19 Verschleißfeste Sinterkörper aus einer Nickel-Chrom-Legierung
DD177303A DD112469A5 (xx) 1973-03-22 1974-03-20
AU66886/74A AU477193B2 (en) 1973-03-22 1974-03-20 Wear-resistant powder metallurgy nickel-base alloy
BE142242A BE812588A (fr) 1973-03-22 1974-03-20 Alliage a base de nickel resistant a l'usure fabrique par metallurgie des poudres
FR7409759A FR2222447B1 (xx) 1973-03-22 1974-03-21
AT233774A AT338537B (de) 1973-03-22 1974-03-21 Gegenstand aus gesintertem metallpulver
CS7400002073A CS185637B2 (en) 1973-03-22 1974-03-21 Piece product with wear and abrasion resistance
SE7403839A SE403914B (sv) 1973-03-22 1974-03-21 Sintrat, nothallfast foremal av pulver av nickellegering
CH394274A CH589143A5 (xx) 1973-03-22 1974-03-21
BR742183A BR7402183D0 (pt) 1973-03-22 1974-03-21 Artigo de po metalico sinterizado
NL7403850A NL7403850A (xx) 1973-03-22 1974-03-21
GB1255474A GB1459873A (en) 1973-03-22 1974-03-21 Nickel-base alloy and articles
IT67901/74A IT1011614B (it) 1973-03-22 1974-03-21 Lega per la fabbricazione di arti coli sinterizzati resistenti al l usura

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US00343845A US3838981A (en) 1973-03-22 1973-03-22 Wear-resistant power metallurgy nickel-base alloy

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US (1) US3838981A (xx)
JP (1) JPS5438971B2 (xx)
AT (1) AT338537B (xx)
AU (1) AU477193B2 (xx)
BE (1) BE812588A (xx)
BR (1) BR7402183D0 (xx)
CA (1) CA1010266A (xx)
CH (1) CH589143A5 (xx)
CS (1) CS185637B2 (xx)
DD (1) DD112469A5 (xx)
DE (1) DE2413017C2 (xx)
FR (1) FR2222447B1 (xx)
GB (1) GB1459873A (xx)
IN (1) IN142080B (xx)
IT (1) IT1011614B (xx)
NL (1) NL7403850A (xx)
SE (1) SE403914B (xx)

Cited By (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4216015A (en) * 1979-04-09 1980-08-05 Cabot Corporation Wear-resistant iron-nickel-cobalt alloys
US4299629A (en) * 1979-06-01 1981-11-10 Goetze Ag Metal powder mixtures, sintered article produced therefrom and process for producing same
DE3116185A1 (de) * 1980-04-25 1982-03-11 Cabot Corp., 02110 Boston, Mass. "metallbinder fuer das verpressen von metallpulvern"
US4331741A (en) * 1979-05-21 1982-05-25 The International Nickel Co., Inc. Nickel-base hard facing alloy
US4842953A (en) * 1986-11-28 1989-06-27 General Electric Company Abradable article, and powder and method for making
US5298052A (en) * 1991-07-12 1994-03-29 Daido Metal Company, Ltd. High temperature bearing alloy and method of producing the same
US5498276A (en) * 1994-09-14 1996-03-12 Hoeganaes Corporation Iron-based powder compositions containing green strengh enhancing lubricants
US6039784A (en) * 1997-03-12 2000-03-21 Hoeganaes Corporation Iron-based powder compositions containing green strength enhancing lubricants
US6338747B1 (en) 2000-08-09 2002-01-15 Keystone Investment Corporation Method for producing powder metal materials
US6485540B1 (en) 2000-08-09 2002-11-26 Keystone Investment Corporation Method for producing powder metal materials
US20040115084A1 (en) * 2002-12-12 2004-06-17 Borgwarner Inc. Method of producing powder metal parts
US20080038148A1 (en) * 2006-08-09 2008-02-14 Paul Crook Hybrid corrosion-resistant nickel alloys
US20100272597A1 (en) * 2009-04-24 2010-10-28 L. E. Jones Company Nickel based alloy useful for valve seat inserts
US20100276209A1 (en) * 2009-05-04 2010-11-04 Smith International, Inc. Roller Cones, Methods of Manufacturing Such Roller Cones, and Drill Bits Incorporating Such Roller Cones
US20110042145A1 (en) * 2009-05-04 2011-02-24 Smith International, Inc. Methods for enhancing a surface of a downhole tool and downhole tools having an enhanced surface
CN105624551A (zh) * 2016-02-26 2016-06-01 铜陵安东铸钢有限责任公司 一种高硼耐磨铸钢及其制备方法
US9638075B2 (en) 2013-12-02 2017-05-02 L.E. Jones Company High performance nickel-based alloy
US9828658B2 (en) 2013-08-13 2017-11-28 Rolls-Royce Corporation Composite niobium-bearing superalloys
US9938610B2 (en) 2013-09-20 2018-04-10 Rolls-Royce Corporation High temperature niobium-bearing superalloys
CN114107715A (zh) * 2021-11-30 2022-03-01 中国科学院兰州化学物理研究所 一种FeCoCrNiMo基高熵合金复合材料及其制备方法和应用

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2050424B (en) * 1979-05-09 1983-06-15 Special Metals Corp Nickel-cobalt-chromium base alloy
EP0035043A1 (en) * 1980-02-28 1981-09-09 Scm Corporation Spray-and-fuse self-fluxing alloy powders, a process for preparing the powders and articles coated therewith
JPH0772315B2 (ja) * 1987-09-30 1995-08-02 株式会社神戸製鋼所 ハロゲンガスに対する耐食性に優れた高耐摩耗合金とその製造方法
JP3340614B2 (ja) * 1996-03-28 2002-11-05 山陽特殊製鋼株式会社 高温強度に優れたＦｅまたはＮｉ基耐熱固化成形体
EP3601625B1 (en) * 2017-03-21 2021-05-19 Brother Group (Hong Kong) Limited Process for preparing iron- and chrome-containing particles
CN112795815B (zh) * 2020-12-31 2021-12-14 广州湘龙高新材料科技股份有限公司 一种钴铬钼钨硅合金粉末

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US3562024A (en) * 1967-12-04 1971-02-09 Standard Pressed Steel Co Cobalt-nickel base alloys containing chromium and molybdenum
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Cited By (25)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4216015A (en) * 1979-04-09 1980-08-05 Cabot Corporation Wear-resistant iron-nickel-cobalt alloys
US4331741A (en) * 1979-05-21 1982-05-25 The International Nickel Co., Inc. Nickel-base hard facing alloy
US4299629A (en) * 1979-06-01 1981-11-10 Goetze Ag Metal powder mixtures, sintered article produced therefrom and process for producing same
DE3116185A1 (de) * 1980-04-25 1982-03-11 Cabot Corp., 02110 Boston, Mass. "metallbinder fuer das verpressen von metallpulvern"
US4842953A (en) * 1986-11-28 1989-06-27 General Electric Company Abradable article, and powder and method for making
US5298052A (en) * 1991-07-12 1994-03-29 Daido Metal Company, Ltd. High temperature bearing alloy and method of producing the same
US5498276A (en) * 1994-09-14 1996-03-12 Hoeganaes Corporation Iron-based powder compositions containing green strengh enhancing lubricants
WO1996008329A1 (en) * 1994-09-14 1996-03-21 Hoeganaes Corporation Improved iron-based powder compositions containing green strength enhancing lubricants
US5624631A (en) * 1994-09-14 1997-04-29 Hoeganaes Corporation Iron-based powder compositions containing green strength enhancing lubricants
US6039784A (en) * 1997-03-12 2000-03-21 Hoeganaes Corporation Iron-based powder compositions containing green strength enhancing lubricants
US6338747B1 (en) 2000-08-09 2002-01-15 Keystone Investment Corporation Method for producing powder metal materials
US6485540B1 (en) 2000-08-09 2002-11-26 Keystone Investment Corporation Method for producing powder metal materials
US20040115084A1 (en) * 2002-12-12 2004-06-17 Borgwarner Inc. Method of producing powder metal parts
US20050123432A1 (en) * 2002-12-12 2005-06-09 Borgwarner Inc. Method of producing powder metal parts
US20080038148A1 (en) * 2006-08-09 2008-02-14 Paul Crook Hybrid corrosion-resistant nickel alloys
US7785532B2 (en) 2006-08-09 2010-08-31 Haynes International, Inc. Hybrid corrosion-resistant nickel alloys
US20100272597A1 (en) * 2009-04-24 2010-10-28 L. E. Jones Company Nickel based alloy useful for valve seat inserts
US20100276209A1 (en) * 2009-05-04 2010-11-04 Smith International, Inc. Roller Cones, Methods of Manufacturing Such Roller Cones, and Drill Bits Incorporating Such Roller Cones
US20110042145A1 (en) * 2009-05-04 2011-02-24 Smith International, Inc. Methods for enhancing a surface of a downhole tool and downhole tools having an enhanced surface
US9828658B2 (en) 2013-08-13 2017-11-28 Rolls-Royce Corporation Composite niobium-bearing superalloys
US9938610B2 (en) 2013-09-20 2018-04-10 Rolls-Royce Corporation High temperature niobium-bearing superalloys
US9638075B2 (en) 2013-12-02 2017-05-02 L.E. Jones Company High performance nickel-based alloy
CN105624551A (zh) * 2016-02-26 2016-06-01 铜陵安东铸钢有限责任公司 一种高硼耐磨铸钢及其制备方法
CN114107715A (zh) * 2021-11-30 2022-03-01 中国科学院兰州化学物理研究所 一种FeCoCrNiMo基高熵合金复合材料及其制备方法和应用
CN114107715B (zh) * 2021-11-30 2022-05-13 中国科学院兰州化学物理研究所 一种FeCoCrNiMo基高熵合金复合材料及其制备方法和应用

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CA1010266A (en) 1977-05-17
NL7403850A (xx) 1974-09-24
CS185637B2 (en) 1978-10-31
IN142080B (xx) 1977-05-28
FR2222447B1 (xx) 1977-06-17
AU6688674A (en) 1975-09-25
JPS5438971B2 (xx) 1979-11-24
ATA233774A (de) 1976-12-15
AU477193B2 (en) 1976-10-14
BE812588A (fr) 1974-07-15
DE2413017A1 (de) 1974-10-03
JPS5041704A (xx) 1975-04-16
BR7402183D0 (pt) 1974-10-29
FR2222447A1 (xx) 1974-10-18
GB1459873A (en) 1976-12-31
DD112469A5 (xx) 1975-04-12
DE2413017C2 (de) 1982-04-29
IT1011614B (it) 1977-02-10
SE403914B (sv) 1978-09-11
CH589143A5 (xx) 1977-06-30
AT338537B (de) 1977-08-25

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