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Process for the production of a titanium alloy based composite material reinforced with titanium carbide, and reinforced composite material obtained thereby

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Publication number
US20050008524A1
US20050008524A1 US10479881 US47988104A US2005008524A1 US 20050008524 A1 US20050008524 A1 US 20050008524A1 US 10479881 US10479881 US 10479881 US 47988104 A US47988104 A US 47988104A US 2005008524 A1 US2005008524 A1 US 2005008524A1
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Prior art keywords
titanium
material
alloy
composite
process
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Abandoned
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US10479881
Inventor
Claudio Testani
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Claudio Testani
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making alloys
    • C22C1/10Alloys containing non-metals
    • C22C1/1094Alloys containing non-metals comprising an after-treatment
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C32/00Non-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
    • C22C32/0047Non-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
    • C22C32/0052Non-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
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22FWORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER
    • B22F2998/00Supplementary information concerning processes or compositions relating to powder metallurgy
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22FWORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER
    • B22F2998/00Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10Processes characterised by the sequence of their steps
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22FWORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER
    • B22F2999/00Aspects linked to processes or compositions used in powder metallurgy

Abstract

Object of the present invention is a process for the production of a Titanium alloy based composite material with satisfactory mechanical features at high temperature, characterised in that Titanium alloy powders and Titanium carbide powders are blended, hot-pressed and hot-rolled or extruded. The invention also encompasses a composite material obtainable with said process.

Description

  • [0001]
    The present invention refers to the production of components obtained from Titanium alloy based components, to be used in the field of mechanics and of high temperature automotives in the presence of creep and of high specific stresses.
  • [0002]
    EP-0 215 941 (Dynamet) teaches the manufacturing, by blending and sintering, of Titanium-based composite materials including a dispersion of Titanium carbide (TiC) powder. The end product obtained is free of a significant reaction at the TiC-matrix interface or of dilution regions exhibiting a composition gradient.
  • [0003]
    The main restriction of this US process is that the product obtained has an interface exhibiting scarce chemical reaction, and therefore where the stresses are accordingly transferred by mechanical mechanisms. Moreover, exposure to high temperatures fosters grain growth, a phenomenon that worsens the mechanical properties, especially the fatigue strength.
  • [0004]
    Therefore, in the specific field there subsists the demand for a manufacturing process allowing to overcome the abovementioned drawbacks.
  • [0005]
    The process subject of the present invention surmounts all of the abovementioned drawbacks, further providing other advantages that will be mentioned hereinafter.
  • [0006]
    In fact, object of the present invention is a process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature, wherein a Titanium alloy powder and a Titanium carbide powder are blended, hot-compacted and hot-rolled or extruded.
  • [0007]
    The TiC content (concentration) can range from 0.5 to 30% b/w.
  • [0008]
    The granulometry of the Titanium alloy can be <250 μm, preferably <5 μm.
  • [0009]
    The blending of the two powders may be carried out in the presence of the 50% b/v acetone (or other anti-clumping agent), optionally added separately to each one of the powders to be blended, prior to blending.
  • [0010]
    The powder blending may be carried out under inert gas, e.g., Argon, atmosphere.
  • [0011]
    The blending may be obtained by revolving in a vessel, containing the two powder types, at a high rate of rpm for a time ranging from 5 minutes to 8 hours.
  • [0012]
    The hot compacting may be obtained by hot isostatic pressing (HIP) at temperatures ranging from 850 to 950° C., at pressures ranging from 80 to 130 MPa, for <4 h times.
  • [0013]
    The powders thus blended can be dried substantially under vacuum.
  • [0014]
    The material resulting from the hot pressing is preferably heated to a temperature of about 1000° C. and pressed to a thickness reduction of from 5 to 50%.
  • [0015]
    The yielded pressed product is rolled, at temperatures comprised in the range 800-1000° C., with <5% reduction passages, down to the desirable total thickness reduction, e.g. of about 80%.
  • [0016]
    The process according to the present invention allows an optimum distribution of the TiC particulate and the diffusion thereof at the interface with the Titanium alloy matrix.
  • [0017]
    The diffusion is measured from a Carbon (C) content of about 20% at 20 μm from a TiC particle.
  • [0018]
    The carbon diffusion obtained by TiC particles/Titanium alloy matrix interface reaction is controlled via the thermal treatment of hot compacting.
  • [0019]
    In particular, in order to obtain a C content of about 17% in atom percent, at a 20-μm distance from a TiC particle, a 960° C. temperature should be applied for 3 h with pressures of about 1100 MPa.
  • [0020]
    This significant dissolving of the TiC inside of the Titanium alloy matrix is accountable for the increase of the mechanical properties attained with the present invention.
  • [0021]
    With respect to the composite material disclosed in EP 0 215 941, for the composite material of the present invention the rolling step advantageously suffices to eliminate Titanium carbide agglomerates; these carbides, very uniformly dispersed, allow to overcome brittleness problems at room temperature, with breakaway of the bonds at the old particle edges in the unrolled material. The measured strength values are about 20-30% higher than those of the composite alloy of EP 0 215 941. This advantageous result could also be accounted for by the fact that inside of the matrix an evident dilution of the TiC has occurred, with a C concentration profile that drops from about the 50%, measured at the centre of a TiC particle, and stabilizes, after about 20 μm, to values of about 5%, measured also at about 60 μm from the edge of the TiC particle.
  • [0022]
    The Titanium alloys that yielded satisfactory results as matrices in the compounds according to the present invention are the following. Ti6Al4V, Ti6Al2Sn4Zr2Mo0.1Si, Ti15Al3V3Sn3Cr, and Ti6242S.
  • [0023]
    The present invention also refers to the composite material obtainable with the hereto-described process.
  • [0024]
    So far, a general description of the present invention was given. With the aid of the attached figures and of the following example, a more detailed description of specific embodiments of the invention, aimed at making better understood the objects, the features, the advantages and the operation modes thereof will be provided hereinafter.
  • [0025]
    FIG. 1 shows the microstructure of an embodiment of the homogeneous blend of Titanium alloy powder and TiC powder, prior to the hot compacting.
  • [0026]
    FIG. 2 shows the increase of the mechanical properties, at <600° C. temperatures, of a compound obtained with an embodiment of the process according to the invention with respect to the material obtained with the same powders by sintering and hot compacting.
  • EXAMPLE
  • [0027]
    The powders to be blended according to the invention are prepared by gas atomizing from 500 mm high, 45 mm Ø ingots. The end sizes of the particles obtained are <200 μm for the Ti6242S alloy, utilized in the example, and <10 μm for the Titanium carbide.
  • [0028]
    Table 1 shows the composition of the Titanium alloy powder with respect to that of the starting ingot. The Table also reports the average size (in μm) of the Ti6242S powder, the flow rate and the size (in μm) of the TiC particles.
    TABLE 1
    Al Sn Zn Mo O N H
    Ti6242S Alloy % % % % ppm ppm ppm
    Pre-atomizing samples 6.1 1.4 3.7 1.6 646 218 nd
    Powder samples 6.3 1.3 3.8 1.7 1096 496 90
    Average size (μm) Flow rate TiC particle size
    of Ti6242S particles (ASTMB213) (μm)
    44-200 28s 0.1-5
  • [0029]
    Ti6242S and TiC powders are blended in a rotary cylinder with movable blades, instead of resorting to a mechanical alloying that produces more superficial fractures and, therefore, more reaction sites with C, O, N. This procedure, as well as the mechanical alloying, provides optimum reinforcing material/matrix homogeneousness. FIG. 1 shows the 200×SEM (Scanning Electron Microscopy) microphotography of the homogenate blend.
  • [0030]
    Then, the blended powders are introduced in a steel cylinder that is sealed and welded to the lid by TIG (Tungsten Inert Gas) welding. The cylinder lid is provided with a port and a piping for carrying out the evacuation. The cylinder-shaped container was designed in order to resist fractures during the HIP process.
  • [0031]
    The evacuation takes place with a rotary pump, obtaining vacuums in the order of 10−5 mbar.
  • [0032]
    Post-evacuation, the powder is isostatically pressed, with ho prior consolidation, for 5 h at a 1000° C. temperature and with a pressure peak of 1500 Bar.
  • [0033]
    Then, tensile test samples of the yielded composite material are obtained, with their axes parallel to the cylinder generatrix.
  • [0034]
    After heating to 1100° C., the composite material is hot-rolled, with an 80% thickness reduction.
  • [0035]
    Samples of the rolled material thus obtained are subjected to tensile tests. The test results highlight an increase of the tensile strength of the material at <600° C. temperatures and a decrease of this parameter at >600° C. temperatures. FIG. 2 shows the increase of the mechanical properties of the rolled composite material of the invention with respect to that of the material merely sinterized and compacted by HIP.

Claims (11)

1. A process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature, in which a Titanium alloy powder and a Titanium carbide powder are blended, hot-compacted and hot-rolled, or extruded, characterised in that the hot compacting is obtained by isostatic hot pressing at a temperature ranging from 850 to 950° C., at a pressure ranging from 80 to 130 MPa, for a time less than four hours, and the resulting material is heated to a temperature of about 1000° C. and pressed to provide a thickness reduction of from 5 to 50%.
2. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 1, wherein the concentration of the Titanium carbide expressed in percent by weight ranges from 0.5 to 30%.
3. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 1, wherein the particle size of the Titanium alloy is less than 250 μm.
4. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 3, wherein the particle size of Titanium carbide is less than 5 μm.
5. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 1, wherein the blending of the said two powders is carried out in the presence of 50% by volume acetone or of an anti-clumping agent, optionally added separately to each of the powders to be blended.
6. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 1, wherein the blending of the two powders is carried out under inert gas, preferably Argon, atmosphere.
7. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 6, wherein the blending is obtained by revolving a vessel, containing the two powders, at a high rate for a time ranging from 5 minutes to 8 hours.
8. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 7, wherein the blended powders are dried under vacuum.
9. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to any of the preceding claims, wherein the resulting compound is hot-rolled in the range from 800 to 1000° C. with less than 5% reduction passages, until the desired total thickness is achieved.
10. The process for the production of a Titanium alloy based composite material having satisfactory mechanical features at high temperature according to claim 9, wherein the total thickness reduction is of about 80%.
11. A Titanium alloy based composite material reinforced with Titanium carbide, as obtained by the process of claim 1.
US10479881 2001-06-08 2002-06-03 Process for the production of a titanium alloy based composite material reinforced with titanium carbide, and reinforced composite material obtained thereby Abandoned US20050008524A1 (en)

Priority Applications (3)

Application Number Priority Date Filing Date Title
ITRM20010320 2001-06-08
ITRM2001A000320 2001-06-08
PCT/IT2002/000358 WO2002101104A1 (en) 2001-06-08 2002-06-03 Process for the production of a titanium alloy based composite material reinforced with titanium carbide, and reinforced composite material obtained thereby

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US20050211475A1 (en) * 2004-04-28 2005-09-29 Mirchandani Prakash K Earth-boring bits
US20060024140A1 (en) * 2004-07-30 2006-02-02 Wolff Edward C Removable tap chasers and tap systems including the same
US20060131081A1 (en) * 2004-12-16 2006-06-22 Tdy Industries, Inc. Cemented carbide inserts for earth-boring bits
US20070102202A1 (en) * 2005-11-10 2007-05-10 Baker Hughes Incorporated Earth-boring rotary drill bits including bit bodies comprising reinforced titanium or titanium-based alloy matrix materials, and methods for forming such bits
US20070102198A1 (en) * 2005-11-10 2007-05-10 Oxford James A Earth-boring rotary drill bits and methods of forming earth-boring rotary drill bits
US20070251732A1 (en) * 2006-04-27 2007-11-01 Tdy Industries, Inc. Modular Fixed Cutter Earth-Boring Bits, Modular Fixed Cutter Earth-Boring Bit Bodies, and Related Methods
US20080029310A1 (en) * 2005-09-09 2008-02-07 Stevens John H Particle-matrix composite drill bits with hardfacing and methods of manufacturing and repairing such drill bits using hardfacing materials
US20080101977A1 (en) * 2005-04-28 2008-05-01 Eason Jimmy W Sintered bodies for earth-boring rotary drill bits and methods of forming the same
US20080145686A1 (en) * 2006-10-25 2008-06-19 Mirchandani Prakash K Articles Having Improved Resistance to Thermal Cracking
US20090041612A1 (en) * 2005-08-18 2009-02-12 Tdy Industries, Inc. Composite cutting inserts and methods of making the same
US20090113811A1 (en) * 2005-09-09 2009-05-07 Baker Hughes Incorporated Abrasive wear-resistant materials, methods for applying such materials to earth-boring tools, and methods for securing cutting elements to earth-boring tools
US20090293672A1 (en) * 2008-06-02 2009-12-03 Tdy Industries, Inc. Cemented carbide - metallic alloy composites
US20090301789A1 (en) * 2008-06-10 2009-12-10 Smith Redd H Methods of forming earth-boring tools including sinterbonded components and tools formed by such methods
US7703555B2 (en) 2005-09-09 2010-04-27 Baker Hughes Incorporated Drilling tools having hardfacing with nickel-based matrix materials and hard particles
US7776256B2 (en) 2005-11-10 2010-08-17 Baker Huges Incorporated Earth-boring rotary drill bits and methods of manufacturing earth-boring rotary drill bits having particle-matrix composite bit bodies
US20100290849A1 (en) * 2009-05-12 2010-11-18 Tdy Industries, Inc. Composite cemented carbide rotary cutting tools and rotary cutting tool blanks
US7846551B2 (en) 2007-03-16 2010-12-07 Tdy Industries, Inc. Composite articles
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US8074750B2 (en) 2005-11-10 2011-12-13 Baker Hughes Incorporated Earth-boring tools comprising silicon carbide composite materials, and methods of forming same
US8104550B2 (en) 2006-08-30 2012-01-31 Baker Hughes Incorporated Methods for applying wear-resistant material to exterior surfaces of earth-boring tools and resulting structures
US8201610B2 (en) 2009-06-05 2012-06-19 Baker Hughes Incorporated Methods for manufacturing downhole tools and downhole tool parts
US8261632B2 (en) 2008-07-09 2012-09-11 Baker Hughes Incorporated Methods of forming earth-boring drill bits
US8308096B2 (en) 2009-07-14 2012-11-13 TDY Industries, LLC Reinforced roll and method of making same
US8318063B2 (en) 2005-06-27 2012-11-27 TDY Industries, LLC Injection molding fabrication method
US8322465B2 (en) 2008-08-22 2012-12-04 TDY Industries, LLC Earth-boring bit parts including hybrid cemented carbides and methods of making the same
US8490674B2 (en) 2010-05-20 2013-07-23 Baker Hughes Incorporated Methods of forming at least a portion of earth-boring tools
RU2492256C1 (en) * 2012-05-16 2013-09-10 Валерий Иванович Панин Pure titanium-based nanostructured composite and method of its production
US20130260166A1 (en) * 2012-04-02 2013-10-03 Kennametal Inc. Coated Titanium Alloy Surfaces
US8790439B2 (en) 2008-06-02 2014-07-29 Kennametal Inc. Composite sintered powder metal articles
US8800848B2 (en) 2011-08-31 2014-08-12 Kennametal Inc. Methods of forming wear resistant layers on metallic surfaces
US8905117B2 (en) 2010-05-20 2014-12-09 Baker Hughes Incoporated Methods of forming at least a portion of earth-boring tools, and articles formed by such methods
US8978734B2 (en) 2010-05-20 2015-03-17 Baker Hughes Incorporated Methods of forming at least a portion of earth-boring tools, and articles formed by such methods
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US9428822B2 (en) 2004-04-28 2016-08-30 Baker Hughes Incorporated Earth-boring tools and components thereof including material having hard phase in a metallic binder, and metallic binder compositions for use in forming such tools and components
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US7703555B2 (en) 2005-09-09 2010-04-27 Baker Hughes Incorporated Drilling tools having hardfacing with nickel-based matrix materials and hard particles
US9200485B2 (en) 2005-09-09 2015-12-01 Baker Hughes Incorporated Methods for applying abrasive wear-resistant materials to a surface of a drill bit
US20090113811A1 (en) * 2005-09-09 2009-05-07 Baker Hughes Incorporated Abrasive wear-resistant materials, methods for applying such materials to earth-boring tools, and methods for securing cutting elements to earth-boring tools
US20080029310A1 (en) * 2005-09-09 2008-02-07 Stevens John H Particle-matrix composite drill bits with hardfacing and methods of manufacturing and repairing such drill bits using hardfacing materials
US8388723B2 (en) 2005-09-09 2013-03-05 Baker Hughes Incorporated Abrasive wear-resistant materials, methods for applying such materials to earth-boring tools, and methods of securing a cutting element to an earth-boring tool using such materials
US7997359B2 (en) 2005-09-09 2011-08-16 Baker Hughes Incorporated Abrasive wear-resistant hardfacing materials, drill bits and drilling tools including abrasive wear-resistant hardfacing materials
US8002052B2 (en) 2005-09-09 2011-08-23 Baker Hughes Incorporated Particle-matrix composite drill bits with hardfacing
US8758462B2 (en) 2005-09-09 2014-06-24 Baker Hughes Incorporated Methods for applying abrasive wear-resistant materials to earth-boring tools and methods for securing cutting elements to earth-boring tools
US7776256B2 (en) 2005-11-10 2010-08-17 Baker Huges Incorporated Earth-boring rotary drill bits and methods of manufacturing earth-boring rotary drill bits having particle-matrix composite bit bodies
US9192989B2 (en) 2005-11-10 2015-11-24 Baker Hughes Incorporated Methods of forming earth-boring tools including sinterbonded components
US8074750B2 (en) 2005-11-10 2011-12-13 Baker Hughes Incorporated Earth-boring tools comprising silicon carbide composite materials, and methods of forming same
US7802495B2 (en) 2005-11-10 2010-09-28 Baker Hughes Incorporated Methods of forming earth-boring rotary drill bits
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US9700991B2 (en) 2005-11-10 2017-07-11 Baker Hughes Incorporated Methods of forming earth-boring tools including sinterbonded components
US20070102198A1 (en) * 2005-11-10 2007-05-10 Oxford James A Earth-boring rotary drill bits and methods of forming earth-boring rotary drill bits
US20070102202A1 (en) * 2005-11-10 2007-05-10 Baker Hughes Incorporated Earth-boring rotary drill bits including bit bodies comprising reinforced titanium or titanium-based alloy matrix materials, and methods for forming such bits
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