Classifications

• • 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
  • C22C27/04—Alloys based on tungsten or molybdenum
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F9/00—Making metallic powder or suspensions thereof
  • B22F9/02—Making metallic powder or suspensions thereof using physical processes
  • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F9/00—Making metallic powder or suspensions thereof
  • B22F9/02—Making metallic powder or suspensions thereof using physical processes
  • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
  • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
  • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
• • 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
  • C22C1/045—Alloys based on refractory metals
• • 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
  • C22C1/05—Mixtures of metal powder with non-metallic powder
  • C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
• • 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
  • C22C1/10—Alloys containing non-metals
  • C22C1/1084—Alloys containing non-metals by mechanical alloying (blending, milling)
• • 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
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F9/00—Making metallic powder or suspensions thereof
  • B22F9/02—Making metallic powder or suspensions thereof using physical processes
  • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
  • B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F9/00—Making metallic powder or suspensions thereof
  • B22F9/02—Making metallic powder or suspensions thereof using physical processes
  • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
  • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
  • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
  • B22F2009/088—Fluid nozzles, e.g. angle, distance
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F2301/00—Metallic composition of the powder or its coating
  • B22F2301/20—Refractory metals
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B22—CASTING; POWDER METALLURGY
  • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
  • B22F2302/00—Metal Compound, non-Metallic compound or non-metal composition of the powder or its coating
  • B22F2302/20—Nitride

Definitions

• the present invention relates to a method of making a molybdenum alloy having a high titanium content which is suitable, for example, for the production of structural components, in particular of components, preferably vanes and blades, of turbomachines such as gas turbines and aircraft engines.
• Ternary molybdenum alloys which comprise molybdenum, silicon and boron as main alloying constituents.
• such alloys do not exhibit sufficient creep resistance.
• Attempts to increase the creep resistance with very finely dispersed particles of titanium, zirconium and carbon, as described, for example, in WO 85/03953 A1 have likewise not led to the desired results.
• US 2016/0060734 A1 discloses alloys which are suitable for the production of structural components such as vanes and blades of turbomachines and comprise molybdenum, silicon, boron and titanium as main components.
• structural components such as vanes and blades of turbomachines and comprise molybdenum, silicon, boron and titanium as main components.
• titanium metal due to the high reactivity of titanium metal with inter alia, oxygen, nitrogen, carbon and hydrogen and its propensity to form stable non-metallic compounds with these elements corresponding alloys are difficult and expensive to produce. If titanium is consumed by reacting with the above elements it is no longer available for the desired phase formation as Mo-Ti silicide and Mo-Ti mixed crystal. These phases are essential for achieving the properties which are required if the alloy is to be used for manufacturing turbine rotor blades and guide vanes.
• DE 10 2011 013 894 A1 discloses a process for the final shape production of components made of a (titanium-free) material comprising intermetallic phases of trimolybdenum silicide and molybdenum borosilicide homogeneously distributed in a molybdenum matrix, which process comprises subjecting a starting powder mixture that comprises at least molybdenum
• the problem underlying the present invention is to provide a method for the production of molybdenum alloys which contain high concentrations of titanium and are suitable for the production of structural components which are subjected to high temperatures and high stress in a simple and cost-efficient manner.
• the present invention provides a method for making a molybdenum alloy which has a high titanium content and further comprises at least silicon and/or boron.
• the method comprises subjecting to (pressureless) sintering under vacuum or sintering under pressure in an inert or reducing gas atmosphere (e.g., an Ar/H 2 atmosphere) a mixture of powders which comprise (i) one or more powders of an alloy of Mo and Ti and, optionally, one or more additional metals X and/or (i') powders of Mo and of titanium nitride (hereafter TiN) and at least one of (ii) one or more powders comprising one or more powders of silicides (and preferably also borides) of Mo and/or Ti and (iii) one or more powders of nitrides which comprise silicon nitride (hereafter Si 3 N 4) powder and/or boron nitride (hereafter BN) powder (in particular, at least silicon nitride
• X if present in the alloy of Mo and Ti, is selected from one or more (e.g., one, two, three or more) of Fe, Y, Hf, Nb, Zr and W.
• X may at least be Fe.
• one or more powders (i) are employed.
• the one or more powders (i) may be substantially spherical and may have a median particle size d50 (as determined by, e.g., laser diffraction) in the range from 0.001 ⁇ m to 50 ⁇ m, in particular from 0.001 ⁇ m to 40 ⁇ m, e.g., from 0.001 to 30 ⁇ m.
• one or more powders (i') (and preferably no powders (i)) are employed.
• the one or more powders (i') are substantially spherical and have a median particle size d50 (as determined by, e.g., laser diffraction) in the range from 0.01 ⁇ m to 100 ⁇ m, in particular from 0.1 ⁇ m to 50 ⁇ m, e.g., from 0.01 to 2 ⁇ m.
• one or more powders (ii) (and preferably no powders (iii)) are be employed.
• the one or more silicide powders (ii) may comprise powders of MoTi 5 Si 3 , Ti 5 Si 3 , MoTi 5 SiB 2 , Mo 3 Si or combinations of two or more thereof.
• one or more powders (iii) (and preferably no powders (ii)) are employed.
• the one or more powders (iii) may comprise one or more powders of silicon nitride and/or one or more powders of boron nitride.
• the powders (iii) may comprise at least one or more powders of silicon nitride.
• both silicon nitride powder(s) and boron nitride powder(s) are employed as powders (iii).
• the powders (i) and/or (i') and the powders (ii) and/or (iii) are combined in ratios which result in an alloy which comprises at least 35 at.% of molybdenum and/or not more than 66 at.% of molybdenum and/or at least 25 at.% of titanium and/or not more than 33 at.% of titanium and/or at least 9 at.% of silicon and/or not more than 15 at.% of silicon and/or at least 5 at.% of boron and/or not more than 9 at.% of boron.
• the alloy comprises at least 0.1 at.% of Fe and/or not more than 5 at.% of Fe.
• the present invention also provides an alloy which is obtainable by the method set forth above (including the various refinements thereof), as well as an article (e.g. a component of a turbine such as a rotor blade or guide vane) which is made of or comprises this alloy.
• the method according to the present invention comprises subjecting to pressureless sintering or sintering under pressure a mixture of powders which comprise (i) one or more powders of an alloy of Mo and Ti and, optionally, one or more additional metals X (e.g., one or more of Fe, Y, Hf, Nb, Zr, W and preferably at least Fe) and/or (i') powders of Mo and of TiN, and further comprise (ii) one or more powders comprising one or more powders of silicides (and preferably also borides) of Mo and/or Ti and/or (iii) one or more powders of nitrides which comprise Si 3 N 4 powder and/or BN powder.
• powders (iii) may not comprise Si 3 N 4 powder.
• the powders (i) may either be purchased (e.g. from H. C. Starck, Germany) or may be prepared, for example, by atomization in an inert gas atmosphere (preferably high purity argon) of a block or ingot of an alloy of Mo, Ti and, optionally, X to obtain a powder with particles which will usually be substantially spherical and will have a particle size (longest dimension and/or diameter) of less than 45 ⁇ m (particularly less than 10 ⁇ m, e.g., less than 1 ⁇ m).
• an inert gas atmosphere preferably high purity argon
• the alloy can be prepared, for example, by melting together (e.g., by plasma melting or arc melting) powders of metallic Mo, Ti and optionally one or more metals X and/or corresponding pre-alloys such as, e.g., Mo 80 Ti 20 , Mo 70 Ti 30 , Mo 60 Ti 40 , etc. (e.g., in powder form). Powders (i') may be prepared, for example, by reducing molybdenum oxides with e.g., hydrogen and by nitriding Ti powder, respectively.
• the phrase "less than z ⁇ m" as used herein is intended to mean that at least 95 % by weight, e.g., at least 98 % by weight, or at least 99 % by weight of the particles have a longest dimension or diameter of z ⁇ m.
• the particle size can be determined by methods well known to those of skill in the art, for example by sieve analysis or optical methods such as laser diffraction.
• the atomization of an ingot or block may, for example, be carried out by an EIGA (Electrode Induction melting Gas Atomization) process or by gas atomization using a Laval nozzle (preferably using high purity argon).
• the atomization may optionally be preceded by subjecting the alloy obtained by, e.g., arc melting or plasma melting to hot isostatic pressing (HIP), e.g., at a temperature of from 1,300°C to 1,500°C and at a pressure of from 100 to 300 MPa for 5 to 10 hours.
• HIP hot isostatic pressing
• a heat treatment may be carried out, e.g., at a temperature of from 1,300°C to 1,600°C for 5 to 50 hours.
• Non-limiting examples of commercially available powders (i) for use in the instant method have a median particle size d50 in the range from 0.01 ⁇ m to 50 ⁇ m (at a purity of, e.g., from 95 % to 99.9 % by weight) or a d50 of from 0.01 ⁇ m to 30 ⁇ m (at a purity of, e.g., from 98 % to 99.9 % by weight).
• the alloy of Mo, Ti and, optionally, X for making the one or more powders (i) may, for example, comprise (in % by weight based on the total weight of the alloy):
• Fe, Nb, Zr, W, Hf and Y may be present in the alloy.
• the alloy for making the one or more powders (i) preferably does not contain any (or at most only trace amounts) of Si and B because the presence of these elements will cause the alloy to become brittle. The same applies to the one or more powders (i').
• Non-limiting examples of commercially available Mo powders (i') for use in the instant method have a median particle size d50 in the range from 0.1 ⁇ m to 50 ⁇ m (at a purity of, e.g., from 95 % to 99.9 % by weight) or a d50 of 0.5 ⁇ m to 2 ⁇ m (at a purity of, e.g., from 98 % to 99.9 % by weight).
• d50 in the range from 0.1 ⁇ m to 50 ⁇ m (at a purity of, e.g., from 95 % to 99.9 % by weight) or a d50 of 0.5 ⁇ m to 2 ⁇ m (at a purity of, e.g., from 98 % to 99.9 % by weight).
• the one or more powders (ii) for use in the instant method may comprise powders of one or more of Mo(Ti) 5 Si 3 , Ti 5 Si 3 , Mo(Ti) 5 SiB 2 , Mo 3 Si.
• the one or more powders (ii) may either be purchased (e.g., from H. C. Starck, Germany) or may be prepared by, for example, arc melting (usually in an argon atmosphere) from elemental Mo, Ti and Si (and preferably B), usually in the form of powders of the elements and/or corresponding pre-alloys.
• the powders (ii) will usually comprise one or more phases of formula MoTi 5 Si 3 , Ti 5 Si 3 , MoTi, and MoTi 5 SiB 2 and/or corresponding substoichiometric or hyperstoichometric phases.
• these phases may contain more or less Si and/or B than indicated, or may contain Mo and/or Ti, which can activate the sintering process and can result in high sinter densities (e.g., > 95 %).
• the powders (ii) for use in the instant method will usually have a median particle size d50 (as determined by, e.g., laser diffraction) in the range from 0.001 ⁇ m to 50 ⁇ m, in particular from 0.001 ⁇ m to 40 ⁇ m, e.g., 0.001 to 30 ⁇ m.
• d50 median particle size
• Non-limiting examples of commercially available powders (ii) for use in the instant method may have a median particle size d50 as follows:
• the powders (iii) for use in the instant method will usually have a median particle size d50 (as determined by, e.g., laser diffraction) in the range from 0.001 ⁇ m to 50 ⁇ m, e.g., from 0.001 ⁇ m to 40 ⁇ m, or from 0.001 to 30 ⁇ m.
• d50 median particle size
• Non-limiting examples of commercially available powders (iii) for use in the instant method may have a median particle size d50 as follows:
• the powders (i) and/or (i') and the powders (ii) and/or (iii) are mixed and optionally milled, and then subjected to a sintering process (either pressureless or under pressure in a reducing or inert gas atmosphere, e.g., an atmosphere consisting essentially of Ar/H 2 or helium).
• a sintering process either pressureless or under pressure in a reducing or inert gas atmosphere, e.g., an atmosphere consisting essentially of Ar/H 2 or helium.
• the mixed (and optionally milled) powders Prior to sintering the mixed (and optionally milled) powders will usually be combined with a preferably organic binder (e.g., an organic wax) and then subjected to cold isostatic pressing (CIP) at room temperature, e.g., at a pressure of from 100 to 300 MPa for, e.g., 5 to 60 minutes, to form a green body.
• a preferably organic binder e.g., an organic wax
• CIP cold isostatic pressing
• the one or more powders (i) or (i') are usually mixed with the one or more powders (ii) and/or (iii) in ratios which result in a weight percentage of the one or more powders (i) and/or the one or more powders (i') of at least 85 %, e.g., at least 88 %, at least 90 %, at least 92 %, or at least 94 % by weight, but usually not higher than 97 %, e.g., not higher than 96 % by weight, based on the total weight of the powder mixture (i.e., without optional binder).
• weight percentages of powders (i) and (iii) in a corresponding mixture may be as follows:
• the sintering (or reaction sintering if nitrides are present) is usually carried out in several (e.g., two, three or four) steps at different temperatures.
• the sintering may be carried out, in each case with a holding time of from 1 to 3 hours, (1) at a temperature of from 350°C to 450°C (e.g., at about 400°C) to decompose the optionally present organic binder, (2) at a temperature of from 650°C to 750°C (e.g., at about 700°C) to decompose nitrides, if present, (3) at a temperature of from 1,150°C to 1,250°C (e.g., at about 1,200°C) and (4) at a temperature of from 1,650°C to 1,750°C (e.g., at about 1,700°C).
• the sintered body thus obtained may optionally be subjected to hot isostatic pressing (HIP), e.g., at a temperature of from 1,300°C to 1,500°C and at a pressure of from 100 to 300 MPa for 5 to 10 hours.
• HIP hot isostatic pressing
• a heat treatment may be carried out, e.g., at a temperature of from 1,300°C to 1,600°C for 5 to 50 hours.
• the sintered body may also be subjected to forming (optionally preceded by HIP and/or heat treatment(s) as set forth above) such as, e.g., rolling, extrusion, forging (e.g., isothermal or "hot die”), optionally followed by a heat treatment as set forth above.
• HIP and/or heat treatment(s) such as, e.g., rolling, extrusion, forging (e.g., isothermal or "hot die"), optionally followed by a heat treatment as set forth above.
• the sintering (and the CIP) can be replaced by a generative production method, e.g. by using a laser with which a desired structure is built up layer by layer, the laser being used to sinter each deposited layer of powder material before the next layer of powder material is deposited.
• a powder (i) was prepared by arc melting of a powder mixture of elemental Mo (81 % by weight), Ti (18 % by weight) and Fe (1 % by weight) to form an ingot, followed by atomization of the ingot by means of a Laval nozzle.
• the resultant product showed the following (approximate) concentrations (in at.%): Mo 57 Ti 25 Fe 1 Si 9 B 8
• a powder (i) is prepared by plasma melting of a powder mixture of elemental Mo, Ti, Fe and Hf to form an ingot, followed by atomization of the ingot by means of a Laval nozzle.
• the powder (i) is then mixed with powders (iii) of Si 3 N 4 and BN and an organic binder and the resultant mixture is subjected to CIP and thereafter to reaction sintering at temperatures of about 400°C, about 700°C, about 1,200°C and about 1,700°C, each for about 1-3 hours in a reducing atmosphere or in vacuum, followed by a heat treatment at about 1,400°C for about 10 hours and HIP for about 5 hours at about 1,400°C and about 150 MPa.
• a powder (i) is prepared by arc melting or plasma melting of a powder mixture of elemental Mo, Ti, Fe, Y, Hf, Nb, Zr and W to form an ingot, followed by an optional heat treatment, optional HIP and atomization of the ingot by means of a Laval nozzle or by means of an EIGA method.
• the powder (i) is then mixed with powders (iii) of Si 3 N 4 and BN and an organic binder and the resultant mixture is subjected to CIP and thereafter to reaction sintering at temperatures of about 400°C, about 700°C, about 1,200°C and about 1,700°C, each for about 1-3 hours in a reducing atmosphere or in vacuum, followed by optional HIP for about 5 to about 10 hours at a temperature of from about 1,300°C to about 1,500°C and a pressure of from about 100 to about 300 MPa, forming by rolling, extrusion or forging at a temperature of higher than 1,600°C and a subsequent heat treatment for about 5 to about 50 hours at a temperature of from about 1,300°C to about 1,600°C.
• a powder (i) is prepared by plasma melting of a powder mixture of elemental Mo, Ti and Fe to form an ingot, followed by atomization of the ingot by means of a Laval nozzle.
• the powder (i) is then mixed with powders (ii) of Mo(Ti) 5 Si 3 and Mo(Ti) 5 SiB 2 and an organic binder and the resultant mixture is subjected to CIP and thereafter to sintering at temperatures of about 400°C, about 1,200°C and about 1,700°C, each for about 1-3 hours in a reducing atmosphere or in vacuum, followed by a heat treatment at about 1,400°C for about 10 hours and HIP for about 5 hours at about 1,400°C and about 150 MPa.
• a powder mixture (i') of elemental Mo and of TiN is mixed with powders (iii) of Si 3 N 4 and BN and an organic binder and the resultant mixture is subjected to CIP and thereafter to reaction sintering at temperatures of about 400°C, about 700°C, about 1,200°C and about 1,700°C, each for about 1-3 hours in a reducing atmosphere or in vacuum, followed by a heat treatment at about 1,400°C for about 10 hours and HIP for about 5 hours at about 1,400°C and about 150 MPa.
• the method of the present invention is suitable for making molybdenum alloys which have a high titanium content.
• the term "molybdenum alloy” as used herein and in the appended claims refers to an alloy in which the element molybdenum makes up the greatest alloying fraction in at.%. In other words, in a molybdenum alloy, there is no other element which has a greater alloying fraction in at.% than Mo.
• the molybdenum content of the alloy in at.% will usually be at least 30 at.%, preferably at least 35 at.%, and in particular at least 40 at.%, e.g., at least 45 at.% (based on all elements present in the alloy, as in the following).
• High titanium content refers to a titanium content of at least 15 at.%, preferably at least 20 at.% and particularly at least 25 at.%, e.g., at least 30 at. %.
• the alloy made by the instant method may further comprise iron and/or yttrium, each in a concentration of from 0.1 to 5 at.%, in particular in a concentration of from 0.3 to 3 at.%.
• iron may be present in a concentration of from 0.5 to 3 at.%, in particular from 0.8 to 2 at.%
• yttrium may be present in a concentration of from 0.3 to 3 at.%, in particular from 0.5 to 2 at.%.
• the alloy produced by the method of the present invention may further comprise one or more of zirconium, niobium, hafnium, and tungsten.
• zirconium may be present in a concentration of not more than 5 at.%, in particular in a concentration of from 0.3 to 3 at.%
• niobium may be present in a concentration of not more than 20 at.%, in particular in a concentration of from 0.3 to 10 at.%
• tungsten may be present in a concentration of not more than 8 at.%, in particular in a concentration of from 0.3 to 5 at.%
• hafnium may be present in a concentration of not more than 5 at.%, in particular in a concentration of from 0.3 to 3 at.%.
• the alloy of the present invention may comprise silicon in a concentration of from 9 to 15 at.%, in particular in a concentration of from 12 to 14 at.%, and/or boron in a concentration of from 5 to 9 at.%, in particular in a concentration of from 5 to 6 at.%, and/or titanium in a concentration of from 25 to 33 at.%, in particular in a concentration of from 26 to 29 at.%.
• the alloy may, for example, be formed exclusively of molybdenum, silicon, boron, titanium, iron, yttrium, niobium, tungsten, zirconium, hafnium (and unavoidable impurities), or may be formed exclusively of molybdenum, silicon, boron, titanium, iron, yttrium (or hafnium).
• molybdenum may be present in a concentration of from 35 to 66 at.%, in particular in a concentration of from 40 to 60 at.%, e.g., from 45 to 57 at.%, or in a concentration such that the alloy comprises 100 at.% together with the remaining alloying constituents mentioned.
• the true density of the produced alloy may be less than or equal to 9 g/cm 3 , in particular less than or equal to 8.5 g/cm 3 , or less than or equal to 8 g/cm 3 .
• the structure of the alloy may comprise a matrix of a molybdenum mixed crystal and silicide phases, the silicide phases being formed in particular by Mo(Ti) 5 Si 3 and/or Mo(Ti) 5 SiB 2 .
• the alloy may comprise from 15 to 35 vol.%, in particular from 25 to 35 vol.% Mo(Ti) 5 Si 3 and from 15 to 35 vol.%, in particular from 15 to 25 vol.% Mo(Ti) 5 SiB 2 and from 1 to 20 vol.% minor phases.
• the alloy may comprise from 45 to 55 vol.%, in particular from 48 to 55 vol.%, molybdenum mixed crystal or a fraction of molybdenum mixed crystal such that the alloy together with the remaining phase constituents comprises 100 vol.%.
• niobium and tungsten may additionally be present in the alloy.
• the addition of niobium improves the fracture toughness and therefore the deformability or ductility, whereas tungsten improves the oxidation resistance of the alloy.
• the alloy is formed exclusively of the elements molybdenum, silicon, boron, titanium, iron, yttrium, niobium, tungsten, hafnium and zirconium, wherein the fraction of niobium, tungsten, hafnium and zirconium may be 0 at.%.
• an alloy can comprise further elements as unavoidable impurities, wherein, however, none of these further elements should make up more than 1 at.%, preferably more than 0.1 at.%, in the alloy.
• alloys can be produced by the method of the present invention which, in addition to unavoidable impurities, exclusively comprise Mo, Si, B, Ti, Fe, Y, Zr, Nb, Hf and/or W.
• Mo-Si-B-Ti-Fe-, Mo-Si-B-Ti-Fe-Zr-, Mo-Si-B-Ti-Fe-Y-, Mo-Si-B-Ti-Fe-Y-Nb- and Mo-Si-B-Ti-Fe-Y-Nb-W alloys can be produced, likewise a Mo-Si-B-Ti-Y alloy which does not comprise iron, although an alloy containing iron is preferred in principle.
• the alloy composition can in particular also be selected in such a manner that the true density, that is to say the density without any pores or cavities, is adjusted to be less than or equal to 9 g/cm 3 , in particular less than or equal to 8.5 g/cm 3 , preferably less than or equal to 8 g/cm 3 .
• the corresponding structure of the alloy can be adjusted in such a manner that the structure has a matrix of molybdenum mixed crystal (e.g., molybdenum-titanium mixed crystal), into which the silicide phases are incorporated, wherein the silicide phases can be formed by Mo(Ti) 5 Si 3 and/or Mo(Ti) 5 SiB 2 .
• molybdenum can be replaced by titanium and vice versa.
• the molybdenum alloy made by the method of the present invention may comprise from 15 to 35 vol.%, e.g., from 25 to 35 vol.% Mo(Ti) 5 Si 3 and from 15 to 35 vol.%, e.g., from 15 to 25 vol.% Mo(Ti) 5 SiB 2 and from 1 to 20 vol.%, e.g., from 1 to 5 vol.%, minor phases.
• Minor phases can comprise various phases, in particular various mixed phases or mixed crystals of the alloying elements present in the alloy.
• the molybdenum alloy may additionally comprise from 45 to 55 vol.%, in particular from 48 to 55 vol.%, molybdenum mixed crystal or a fraction of molybdenum mixed crystal such that the alloy together with the remaining phase constituents comprises 100 vol.%.
• components of turbomachines preferably of gas turbines or aero engines can be manufactured, wherein the components can be, in particular, rotor blades or guide vanes of the turbomachine, and in particular guide vanes or rotor vanes of rapidly running uncooled low-pressure turbines.

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• 2016
  • 2016-10-13 EP EP16193634.9A patent/EP3309266A1/fr not_active Withdrawn
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