US20160122850A1 - Method for producing a high temperature-resistant target alloy, a device, an alloy and a corresponding component - Google Patents
Method for producing a high temperature-resistant target alloy, a device, an alloy and a corresponding component Download PDFInfo
- Publication number
- US20160122850A1 US20160122850A1 US14/887,765 US201514887765A US2016122850A1 US 20160122850 A1 US20160122850 A1 US 20160122850A1 US 201514887765 A US201514887765 A US 201514887765A US 2016122850 A1 US2016122850 A1 US 2016122850A1
- Authority
- US
- United States
- Prior art keywords
- alloy
- powder
- base material
- attritor
- target alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Abandoned
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 98
- 239000000956 alloy Substances 0.000 title claims abstract description 98
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 239000000463 material Substances 0.000 claims abstract description 62
- 239000000843 powder Substances 0.000 claims abstract description 58
- 238000000034 method Methods 0.000 claims abstract description 38
- 238000000227 grinding Methods 0.000 claims abstract description 36
- 238000011049 filling Methods 0.000 claims abstract description 11
- 238000005275 alloying Methods 0.000 claims description 45
- 229910052750 molybdenum Inorganic materials 0.000 claims description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 13
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 12
- 229910052735 hafnium Inorganic materials 0.000 claims description 12
- 239000001301 oxygen Substances 0.000 claims description 12
- 229910052760 oxygen Inorganic materials 0.000 claims description 12
- 239000010936 titanium Substances 0.000 claims description 12
- 229910052727 yttrium Inorganic materials 0.000 claims description 12
- 229910052782 aluminium Inorganic materials 0.000 claims description 11
- 238000005551 mechanical alloying Methods 0.000 claims description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 11
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- 229910052726 zirconium Inorganic materials 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 229910052804 chromium Inorganic materials 0.000 claims description 9
- 239000007789 gas Substances 0.000 claims description 9
- 229910052691 Erbium Inorganic materials 0.000 claims description 8
- 229910052688 Gadolinium Inorganic materials 0.000 claims description 8
- 229910010038 TiAl Inorganic materials 0.000 claims description 8
- 229910052796 boron Inorganic materials 0.000 claims description 8
- 239000000470 constituent Substances 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 8
- 229910052758 niobium Inorganic materials 0.000 claims description 8
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 239000013078 crystal Substances 0.000 claims description 6
- 238000001513 hot isostatic pressing Methods 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 229910001182 Mo alloy Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 4
- 150000001875 compounds Chemical class 0.000 claims description 4
- 239000011733 molybdenum Substances 0.000 claims description 4
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 claims description 4
- 230000001681 protective effect Effects 0.000 claims description 4
- 229910001928 zirconium oxide Inorganic materials 0.000 claims description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- 238000010894 electron beam technology Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- MGRWKWACZDFZJT-UHFFFAOYSA-N molybdenum tungsten Chemical compound [Mo].[W] MGRWKWACZDFZJT-UHFFFAOYSA-N 0.000 claims description 3
- SIWVEOZUMHYXCS-UHFFFAOYSA-N oxo(oxoyttriooxy)yttrium Chemical compound O=[Y]O[Y]=O SIWVEOZUMHYXCS-UHFFFAOYSA-N 0.000 claims description 3
- 238000001465 metallisation Methods 0.000 claims description 2
- 239000002245 particle Substances 0.000 description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- 229910044991 metal oxide Inorganic materials 0.000 description 6
- 150000004706 metal oxides Chemical class 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 239000001307 helium Substances 0.000 description 4
- 229910052734 helium Inorganic materials 0.000 description 4
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 4
- 150000002739 metals Chemical class 0.000 description 4
- 238000000137 annealing Methods 0.000 description 3
- 229910052786 argon Inorganic materials 0.000 description 3
- 238000011109 contamination Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000013019 agitation Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical group [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- OQPDWFJSZHWILH-UHFFFAOYSA-N [Al].[Al].[Al].[Ti] Chemical class [Al].[Al].[Al].[Ti] OQPDWFJSZHWILH-UHFFFAOYSA-N 0.000 description 1
- SGTBFYDSKHPNLE-UHFFFAOYSA-N [Mo].[C].[Zr].[Hf] Chemical compound [Mo].[C].[Zr].[Hf] SGTBFYDSKHPNLE-UHFFFAOYSA-N 0.000 description 1
- CPTCUNLUKFTXKF-UHFFFAOYSA-N [Ti].[Zr].[Mo] Chemical compound [Ti].[Zr].[Mo] CPTCUNLUKFTXKF-UHFFFAOYSA-N 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000005684 electric field Effects 0.000 description 1
- UYAHIZSMUZPPFV-UHFFFAOYSA-N erbium Chemical compound [Er] UYAHIZSMUZPPFV-UHFFFAOYSA-N 0.000 description 1
- 230000005284 excitation Effects 0.000 description 1
- 238000005194 fractionation Methods 0.000 description 1
- UIWYJDYFSGRHKR-UHFFFAOYSA-N gadolinium atom Chemical compound [Gd] UIWYJDYFSGRHKR-UHFFFAOYSA-N 0.000 description 1
- 238000005247 gettering Methods 0.000 description 1
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000010310 metallurgical process Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 230000002000 scavenging effect Effects 0.000 description 1
- 238000012216 screening Methods 0.000 description 1
- 239000011343 solid material Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052723 transition metal Inorganic materials 0.000 description 1
- 150000003624 transition metals Chemical class 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- 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
-
- 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
-
- 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
-
- 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
- C22C1/047—Making non-ferrous alloys by powder metallurgy comprising intermetallic 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
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
-
- 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
- B22F2009/041—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by mechanical alloying, e.g. blending, 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
- B22F9/04—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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
Definitions
- the invention relates to a method for producing a high temperature-resistant target alloy, in particular a TiAl alloy.
- the invention relates to a corresponding device for carrying out the method, the corresponding alloy and use of the device for producing the high temperature-resistant target alloy.
- Alloys based on intermetallic titanium aluminide compounds are used in the construction of continuous flow machines, such as stationary gas turbines or aircraft engines, for example as a material for rotor blades, since they have the mechanical properties necessary for the purpose and additionally have a low specific weight, such that the use of such alloys may increase the efficiency of stationary gas turbines and aircraft engines.
- TiAl alloys intermetallic titanium aluminide compounds
- components made from TiAl alloys may be manufactured both melt metallurgically and powder metallurgically.
- the manufacturing steps comprise, in addition or as an alternative to the individual steps of melt metallurgical production, the use of powder materials to produce a desired composition of the material for example by alloying.
- An example of the production of an article from a TiAl alloy using powder materials is described in U.S. Pat. No. 5,424,027, the entire disclosure of which is incorporated by reference herein.
- the powder may be produced for example from a molten bath, which is atomized by means of helium or argon at a very high cooling rate of up to 20,000 K/s. This results in a material with a microstructure which is intended to have a homogeneous and uniform grain structure. However, different particle sizes arise, which have to be separated out with effort by fractionation (for example by screening), such that to produce a component, powder may only be used which has powder particles of a specific minimum and a specific maximum diameter. Moreover, the powder must be subjected to multistage heat treatment, so as to optimize appropriately the micro-grain structure thereof This includes solution annealing, high temperature annealing and precipitation annealing. For this purpose, temperatures of over 1000° C. are needed for several hours. With these heat treatments care must be taken to ensure that no oxygen can reach the powder to be annealed.
- the alloy used for production of the component is provided in the form of a melt and the latter is cast in a mold.
- the cast material has conventionally to be subjected to suitable forming and/or heat treatment to destroy the cast structure and establish a desired microstructure for the material.
- the corresponding component may then be brought into the desired shape by suitable finishing, for example by machining or mechanical or electrochemical processing.
- Segregation problems and coarse oxide particle inclusions occur in melt metallurgical processes in the case of high-alloy TiAl, Fe and Mo alloys. Segregation is to be understood to mean demixing processes in a melt. This results in the concentration of certain elements in a mixed crystal increasing at one point and the concentration of these elements decreasing at another point. This reduces the creep strength of the alloy at elevated temperatures.
- the present invention provides a method for producing a high temperature-resistant target alloy, a device for mechanically alloying a high temperature-resistant target alloy, and a high temperature-resistant alloy as set forth in the appended claims.
- the invention provides a method for producing a high temperature-resistant target alloy, comprising:
- the powder is here alloyed by attrition of the attritor and/or attritor vessel and the grinding balls themselves.
- the components of the attritor include in particular an attritor vessel, a plurality of grinding balls and/or the agitator with a plurality of grinding arms.
- the grinding balls are hurled around in the attritor vessel and in the process strike the internal walls of said attritor vessel.
- Parts of the powder are then to be found between the surface of the grinding balls and the internal wall of the attritor.
- Components of the surface or the internal wall may then detach and in this way enter the atomic lattice structure of the base material.
- rotation proceeds at a rotational speed of from about 30 rpm to about 300 rpm for a period of about 1 h to about 10 h.
- the duration and rotational speed depend on the size of the attritor vessel, on the quantity of powder in the attritor vessel, on the initial size of the powder particles prior to mechanical alloying and on the desired final size of the powder particles after mechanical alloying.
- the final size is smaller than the initial size (here in terms of diameter), since the particles become ever smaller over time as a result of rubbing against the balls and against the other attritor components.
- the powder is heat-treated, in particular by laser or electron beam melting and/or by hot isostatic pressing, in such a way that fine oxides, with in particular a size of about 1 to about 500 nm, are eliminated and/or the residual oxygen is gettered out of the crystal lattice of the powder.
- metals are preferably introduced atomically into the crystal lattice as alloying components through the mechanical work.
- the metals include transition metals and lanthanoids (rare earth metals). These atomic metals have a high oxidation capacity, such that, in the presence of sufficient excitation energy, these atomic metals bind the residual oxygen in the crystal to themselves and thereby form corresponding metal oxides.
- Binding of the residual oxygen is known as gettering (from the verb “to get”).
- the ductility, high temperature resistance and creep strength of the target alloy are thereby increased significantly.
- the objective when forming metal oxide particles is in the process to keep these particles small in diameter and to distribute them uniformly in the material matrix, in order in this way to achieve fine distribution of the metal oxides.
- the oxide particles may thus be used purposefully as ODS elements (ODS—oxide particle strengthening).
- hot isostatic pressing takes place in a temperature range of from about 1000° C. to about 1500° C. for a period of about 1 h to about 10 h at a pressure of about 10 MPa to about 500 MPa.
- the duration, temperature and pressure depend on the desired degree of fine distribution and on the desired diameter of the metal oxides.
- the powder of the base material comprises powder grains with a diameter of less than or equal to about 500 ⁇ m.
- the diameter of the powder grains is preferably greater than or equal to about 45 ⁇ m. This has the advantage that the powder of the base material with a greater powder grain diameter is less sensitive to undesired oxygen take-up.
- the base material powder is plasma-cleaned prior to filling and/or at least one of the components of the attritor is plasma-cleaned prior to application of a vacuum.
- degassing of the attritor takes place at a vacuum of from about 0.01 Pa (10 ⁇ 4 mbar) to about 0.1 Pa (10 ⁇ 3 mbar) for a period of from about 0.5 h to about 5 h and at a temperature in a range less than or equal to about 400° C.
- This has the advantage that the oxygen contamination of the alloying components and/or of the base material may be reduced or eliminated.
- this cleaning makes it possible to reduce or eliminate organic and/or inorganic impurities.
- At least one of the elements Si, Y, Hf, Er, Gd, B, C, Zr, Y, Hf, Nb, Mo, W, Co, Cr, V is contained as an alloying component.
- Atomic yttrium, atomic hafnium and/or atomic zirconium form with the (residual) oxygen high temperature-resistant oxides, which pin down the lattice dislocations in the metal matrix and in this way improve creep strength at elevated temperatures (even at above 780° C.).
- Atomic erbium and/or atomic gadolinium likewise form oxides which improve oxide resistance. This means improved corrosion resistance of the target alloy with regard to oxygen. All the metal oxides listed are finely distributed by mechanical alloying without forming coarse oxide particles in the process.
- At least one of the compounds from the group tungsten carbide, titanium-zirconium-molybdenum and hafnium-zirconium-carbon-molybdenum alloys and zirconium oxide, in particular stabilized with Y 2 O 3 is included as an alloying component.
- tungsten carbide is used to make the target alloy correspondingly harder.
- those alloying components to be mechanically alloyed are present in the base material powder which may also be present in a proportion of over 0.5 at % in the target alloy.
- the powder of the base material may also comprise alloying components which are present in the target alloy in a proportion equal to 0.5 at %. This is advantageous because the accuracy of large quantities of alloying components greater than or equal to 0.5 at % can be better established in the base material than by means of subsequent mechanical alloying.
- the alloying components present in small quantities of less than or equal to 0.5 at % are preferably added by the mechanical alloying.
- the powder of the base material preferably contains, in addition to the main constituents, in particular Ti and Al, the following elements in the stated proportions and is—apart from unavoidable impurities—formed from these: W: 0 to 8 at. %, C: 0 to 0.6 at. %, Zr: 0 to 6 at. %, B: 0 to 0.2 at. %, Nb: 4 to 25 at. %, Mo: 1 to 10 at. %, Co: 0.1 to 10 at. %, Cr: 0.5 to 3 at. % and/or V: 0.5 to 10 at. %.
- W 0 to 8 at. %
- C 0 to 0.6 at. %
- Zr 0 to 6 at. %
- B 0 to 0.2 at. %
- Nb 4 to 25 at. %
- Mo 1 to 10 at. %
- Co 0.1 to 10 at. %
- Cr 0.5 to 3 at. %
- V 0.5 to 10 at. %
- the target alloy preferably contains, in addition to the main constituents, in particular Ti and Al, the following elements in the stated proportions and is preferably—apart from unavoidable impurities—formed therefrom: W: 0 to 8 at. %, Si: 0.2 to 0.35 at. %, C: 0 to 0.6 at. %, Zr: 0 to 6 at. %, Y: 0 to 1.5 at. %, Hf: 0 to 1.5 at. %, Er: 0 to 0.5 at. %, Gd: 0 to 0.5 at. %, B: 0 to 0.2 at. %, Nb: 4 to 25 at. %, Mo: 1 to 10 at. %, Co: 0.1 to 10 at. %, Cr: 0.5 to 3 at. % and/or V: 0.5 to 10 at. %
- W 0 to 8 at. %
- Si 0.2 to 0.35 at. %
- C 0 to 0.6 at. %
- Zr 0 to
- the invention further relates to a device for mechanically alloying a high temperature-resistant target alloy, comprising an attritor vessel, an agitator and at least one grinding ball. At least one of the components of the attritor coming into contact with a base material powder contains or consists of the base material and/or at least one of the alloying components of the target alloy.
- the components of the attritor include in particular an attritor vessel, a plurality of grinding balls and/or the agitator with a plurality of grinding arms. This offers the advantage that the further alloying components do not have to be admixed in powder form. In particular, oxygen contamination is reduced thereby.
- the attritor vessel, the grinding balls and/or the grinding arms of the agitator are thus actively used as suppliers of alloying components.
- protective gas such as argon or helium, may preferably be used for scavenging purposes, to remove the residual oxygen. Filling of the attritor vessel with the base material powder preferably takes place under a vacuum.
- At least the surface of the grinding balls contains the base material and/or at least one of the alloying components of the target alloy.
- at least the internal walls of the attritor vessel may contain the base material and/or at least one of the alloying components which the target alloy comprises.
- at least the surface of the grinding arms of the agitator may contain the base material and/or at least one of the alloying components which the target alloy comprises.
- the components of the attritor (attritor vessel, grinding balls and/or agitator with the grinding arms) may be provided with a coating, which contains the base material and/or at least one of the alloying components.
- At least one component of the device for mechanical alloying may consist fully—apart from unavoidable impurities—of the base material and/or at least one of the alloying components. These are preferably the grinding balls and/or the grinding arms of the agitator.
- the attritor vessel may be lined internally with replaceable tiles, which constitute the internal walls of the attritor vessel. These tiles may in turn consist completely—apart from unavoidable impurities—of the base material and/or of at least one of the alloying components.
- a method for producing a high temperature-resistant target alloy comprising
- alloying component at least one compound having the following properties:
- the target alloy and/or of the powder of the base material at least one of the elements Fe, Ni, Ti, Al, Mo is present.
- a device for mechanically alloying a high temperature-resistant target alloy comprising at least the following components:
- all the components of the device which come into contact with the powder during mechanical alloying contain the base material and/or at least one of the alloying components of the target alloy.
- a high temperature-resistant alloy produced using a method according to any one of items 1 to 9.
- the base material powder for example of Ti and Al and for example Cr, V, W, Mo, Fe, Co, Zr, C and/or B, is likewise plasma cleaned under the same conditions and then loaded into the attritor vessel.
- the attritor accommodates around 5 kg of powder.
- the grinding arms, already located in the attritor vessel, of the agitator preferably consist only of Ti, Al and only of the corresponding alloying components, as do the grinding balls.
- the grinding balls have a diameter of around 2 cm.
- the grinding arms and the grinding balls are preferably formed from the solid material of an alloy similar or identical to the target alloy, such that not only does the surface of the grinding balls or of the grinding arms consist of the “target alloy” but also the material located under the surface.
- An alloy similar to the target alloy means that this similar alloy must not have any alloying components which are not present in the target alloy.
- the similar alloy may in this case comprise fewer alloying components than the target alloy, wherein the proportions of the alloying components in the similar alloy may be different from the target alloy.
- the attritor vessel is filled with grinding balls and then closed. Agitation is performed for 5 hours at a rotational speed of 100 rpm.
- the mechanically alloyed powder with the corresponding alloying components is then hot isostatically pressed at 1200° C. for 3 hours at 2000 bar (200 MPa) in a helium protective gas atmosphere.
- Hf, Y, Zr, Er and Gd oxides arise in the process, which are finely distributed in the matrix.
- LPT low pressure turbine
- LPT stators LPT stators
- LPT disks may consist of such an alloy.
- Hot gas baffles and/or further structural elements of a non-stationary or stationary gas turbine may also consist of such a target alloy.
- the above method may also be used for alloying other base materials.
- the base material of titanium and aluminum may be replaced for example by molybdenum, nickel or iron.
- the above-described alloying components and proportions may in this respect be identically selected for molybdenum, nickel or iron.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Optics & Photonics (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Physical Vapour Deposition (AREA)
Abstract
Description
- The present application claims priority under 35 U.S.C. §119 of German Patent Application No.
- 102014222347.4 filed Nov. 3, 2014, the entire disclosure of which is expressly incorporated by reference herein.
- 1. Field of the Invention
- The invention relates to a method for producing a high temperature-resistant target alloy, in particular a TiAl alloy. In addition, the invention relates to a corresponding device for carrying out the method, the corresponding alloy and use of the device for producing the high temperature-resistant target alloy.
- 2. Discussion of Background Information
- For operation of continuous flow machines, due to the conditions of use of the components used, which are exposed in part to high temperatures, aggressive environments and high forces, special materials are required for certain components which are optimally conformed to the intended purpose both by their chemical composition and by their microstructure.
- Alloys based on intermetallic titanium aluminide compounds (TiAl alloys) are used in the construction of continuous flow machines, such as stationary gas turbines or aircraft engines, for example as a material for rotor blades, since they have the mechanical properties necessary for the purpose and additionally have a low specific weight, such that the use of such alloys may increase the efficiency of stationary gas turbines and aircraft engines. There is accordingly already a plurality of TiAl alloys and methods for producing corresponding components therefrom.
- Like comparable components made from other high temperature alloys, for example based on Ni, Fe or Co, components made from TiAl alloys may be manufactured both melt metallurgically and powder metallurgically.
- In powder metallurgical production, the manufacturing steps comprise, in addition or as an alternative to the individual steps of melt metallurgical production, the use of powder materials to produce a desired composition of the material for example by alloying. An example of the production of an article from a TiAl alloy using powder materials is described in U.S. Pat. No. 5,424,027, the entire disclosure of which is incorporated by reference herein.
- The powder may be produced for example from a molten bath, which is atomized by means of helium or argon at a very high cooling rate of up to 20,000 K/s. This results in a material with a microstructure which is intended to have a homogeneous and uniform grain structure. However, different particle sizes arise, which have to be separated out with effort by fractionation (for example by screening), such that to produce a component, powder may only be used which has powder particles of a specific minimum and a specific maximum diameter. Moreover, the powder must be subjected to multistage heat treatment, so as to optimize appropriately the micro-grain structure thereof This includes solution annealing, high temperature annealing and precipitation annealing. For this purpose, temperatures of over 1000° C. are needed for several hours. With these heat treatments care must be taken to ensure that no oxygen can reach the powder to be annealed.
- In melt metallurgical production, the alloy used for production of the component is provided in the form of a melt and the latter is cast in a mold. The cast material has conventionally to be subjected to suitable forming and/or heat treatment to destroy the cast structure and establish a desired microstructure for the material. The corresponding component may then be brought into the desired shape by suitable finishing, for example by machining or mechanical or electrochemical processing. Segregation problems and coarse oxide particle inclusions occur in melt metallurgical processes in the case of high-alloy TiAl, Fe and Mo alloys. Segregation is to be understood to mean demixing processes in a melt. This results in the concentration of certain elements in a mixed crystal increasing at one point and the concentration of these elements decreasing at another point. This reduces the creep strength of the alloy at elevated temperatures.
- In view of the foregoing, it would be advantageous to have available a method and a corresponding device for producing a high temperature alloy which on the one hand improves the creep properties and high temperature resistance of the high temperature alloy and significantly reduces or prevents contamination of the high temperature alloy by undesired elements.
- The present invention provides a method for producing a high temperature-resistant target alloy, a device for mechanically alloying a high temperature-resistant target alloy, and a high temperature-resistant alloy as set forth in the appended claims.
- In particular, the invention provides a method for producing a high temperature-resistant target alloy, comprising:
-
- (a) applying a vacuum to an attritor vessel containing the base material of the target alloy,
- (b) filling the attritor vessel with a powder containing the base material of the target alloy with a reduced alloy element content,
- (c) filling the attritor vessel with grinding balls containing the base material of the target alloy,
- (d) rotating the agitator of the attritor and/or the attritor vessel.
- According to the invention, the powder is here alloyed by attrition of the attritor and/or attritor vessel and the grinding balls themselves.
- The components of the attritor include in particular an attritor vessel, a plurality of grinding balls and/or the agitator with a plurality of grinding arms. Through agitation, the grinding balls are hurled around in the attritor vessel and in the process strike the internal walls of said attritor vessel. Parts of the powder are then to be found between the surface of the grinding balls and the internal wall of the attritor. Components of the surface or the internal wall may then detach and in this way enter the atomic lattice structure of the base material. This has the advantage that the alloying components do not have to be present in powder form, which would enlarge the surface area of the alloying components. The alloying components would then form metal oxides to a greater and uncontrolled extent.
- In one advantageous embodiment of the invention, rotation proceeds at a rotational speed of from about 30 rpm to about 300 rpm for a period of about 1 h to about 10 h. The duration and rotational speed depend on the size of the attritor vessel, on the quantity of powder in the attritor vessel, on the initial size of the powder particles prior to mechanical alloying and on the desired final size of the powder particles after mechanical alloying. In this respect, the final size is smaller than the initial size (here in terms of diameter), since the particles become ever smaller over time as a result of rubbing against the balls and against the other attritor components.
- In a further advantageous embodiment of the invention, the powder is heat-treated, in particular by laser or electron beam melting and/or by hot isostatic pressing, in such a way that fine oxides, with in particular a size of about 1 to about 500 nm, are eliminated and/or the residual oxygen is gettered out of the crystal lattice of the powder. To this end, metals are preferably introduced atomically into the crystal lattice as alloying components through the mechanical work. The metals include transition metals and lanthanoids (rare earth metals). These atomic metals have a high oxidation capacity, such that, in the presence of sufficient excitation energy, these atomic metals bind the residual oxygen in the crystal to themselves and thereby form corresponding metal oxides. Binding of the residual oxygen is known as gettering (from the verb “to get”). The ductility, high temperature resistance and creep strength of the target alloy are thereby increased significantly. The objective when forming metal oxide particles is in the process to keep these particles small in diameter and to distribute them uniformly in the material matrix, in order in this way to achieve fine distribution of the metal oxides. The oxide particles may thus be used purposefully as ODS elements (ODS—oxide particle strengthening).
- In a further advantageous embodiment of the invention, hot isostatic pressing takes place in a temperature range of from about 1000° C. to about 1500° C. for a period of about 1 h to about 10 h at a pressure of about 10 MPa to about 500 MPa. The duration, temperature and pressure depend on the desired degree of fine distribution and on the desired diameter of the metal oxides.
- In a further advantageous embodiment of the invention, the powder of the base material comprises powder grains with a diameter of less than or equal to about 500 μm. The diameter of the powder grains is preferably greater than or equal to about 45 μm. This has the advantage that the powder of the base material with a greater powder grain diameter is less sensitive to undesired oxygen take-up.
- In a further advantageous embodiment of the invention, the base material powder is plasma-cleaned prior to filling and/or at least one of the components of the attritor is plasma-cleaned prior to application of a vacuum. Preferably, degassing of the attritor takes place at a vacuum of from about 0.01 Pa (10−4 mbar) to about 0.1 Pa (10−3 mbar) for a period of from about 0.5 h to about 5 h and at a temperature in a range less than or equal to about 400° C. This has the advantage that the oxygen contamination of the alloying components and/or of the base material may be reduced or eliminated. In addition, this cleaning makes it possible to reduce or eliminate organic and/or inorganic impurities.
- In a further advantageous embodiment of the invention, at least one of the elements Si, Y, Hf, Er, Gd, B, C, Zr, Y, Hf, Nb, Mo, W, Co, Cr, V is contained as an alloying component. Atomic yttrium, atomic hafnium and/or atomic zirconium form with the (residual) oxygen high temperature-resistant oxides, which pin down the lattice dislocations in the metal matrix and in this way improve creep strength at elevated temperatures (even at above 780° C.). Atomic erbium and/or atomic gadolinium likewise form oxides which improve oxide resistance. This means improved corrosion resistance of the target alloy with regard to oxygen. All the metal oxides listed are finely distributed by mechanical alloying without forming coarse oxide particles in the process.
- In a further advantageous embodiment of the invention, at least one of the compounds from the group tungsten carbide, titanium-zirconium-molybdenum and hafnium-zirconium-carbon-molybdenum alloys and zirconium oxide, in particular stabilized with Y2O3, is included as an alloying component. For example, tungsten carbide is used to make the target alloy correspondingly harder.
- In a further advantageous embodiment of the invention, those alloying components to be mechanically alloyed are present in the base material powder which may also be present in a proportion of over 0.5 at % in the target alloy. Alternatively or in combination, the powder of the base material may also comprise alloying components which are present in the target alloy in a proportion equal to 0.5 at %. This is advantageous because the accuracy of large quantities of alloying components greater than or equal to 0.5 at % can be better established in the base material than by means of subsequent mechanical alloying. The alloying components present in small quantities of less than or equal to 0.5 at % are preferably added by the mechanical alloying.
- The powder of the base material preferably contains, in addition to the main constituents, in particular Ti and Al, the following elements in the stated proportions and is—apart from unavoidable impurities—formed from these: W: 0 to 8 at. %, C: 0 to 0.6 at. %, Zr: 0 to 6 at. %, B: 0 to 0.2 at. %, Nb: 4 to 25 at. %, Mo: 1 to 10 at. %, Co: 0.1 to 10 at. %, Cr: 0.5 to 3 at. % and/or V: 0.5 to 10 at. %. The values and numbers therebetween and not explicitly stated are also included.
- The target alloy preferably contains, in addition to the main constituents, in particular Ti and Al, the following elements in the stated proportions and is preferably—apart from unavoidable impurities—formed therefrom: W: 0 to 8 at. %, Si: 0.2 to 0.35 at. %, C: 0 to 0.6 at. %, Zr: 0 to 6 at. %, Y: 0 to 1.5 at. %, Hf: 0 to 1.5 at. %, Er: 0 to 0.5 at. %, Gd: 0 to 0.5 at. %, B: 0 to 0.2 at. %, Nb: 4 to 25 at. %, Mo: 1 to 10 at. %, Co: 0.1 to 10 at. %, Cr: 0.5 to 3 at. % and/or V: 0.5 to 10 at. % The values and numbers therebetween and not explicitly stated are also included.
- The invention further relates to a device for mechanically alloying a high temperature-resistant target alloy, comprising an attritor vessel, an agitator and at least one grinding ball. At least one of the components of the attritor coming into contact with a base material powder contains or consists of the base material and/or at least one of the alloying components of the target alloy.
- The regions of the components which come into contact with the base material powder—apart from unavoidable impurities—preferably contain just one of the alloying components of the target alloy in addition to the base material. This prevents other undesired elements from the alloy composition of the components from being alloyed into the base material powder at an atomic level and thus contaminating the target alloy. The components of the attritor include in particular an attritor vessel, a plurality of grinding balls and/or the agitator with a plurality of grinding arms. This offers the advantage that the further alloying components do not have to be admixed in powder form. In particular, oxygen contamination is reduced thereby. The attritor vessel, the grinding balls and/or the grinding arms of the agitator are thus actively used as suppliers of alloying components. When a vacuum is applied to the attritor vessel, protective gas, such as argon or helium, may preferably be used for scavenging purposes, to remove the residual oxygen. Filling of the attritor vessel with the base material powder preferably takes place under a vacuum.
- In a further advantageous embodiment of the invention, at least the surface of the grinding balls contains the base material and/or at least one of the alloying components of the target alloy. Alternatively or in combination, at least the internal walls of the attritor vessel may contain the base material and/or at least one of the alloying components which the target alloy comprises. Alternatively or in combination, at least the surface of the grinding arms of the agitator may contain the base material and/or at least one of the alloying components which the target alloy comprises. The components of the attritor (attritor vessel, grinding balls and/or agitator with the grinding arms) may be provided with a coating, which contains the base material and/or at least one of the alloying components. Alternatively or in combination, at least one component of the device for mechanical alloying may consist fully—apart from unavoidable impurities—of the base material and/or at least one of the alloying components. These are preferably the grinding balls and/or the grinding arms of the agitator. The attritor vessel may be lined internally with replaceable tiles, which constitute the internal walls of the attritor vessel. These tiles may in turn consist completely—apart from unavoidable impurities—of the base material and/or of at least one of the alloying components.
- In particular the following aspects and combinations thereof are encompassed by the invention:
- 1. A method for producing a high temperature-resistant target alloy, comprising
-
- (a) applying a vacuum to an attritor vessel containing the base material of the target alloy,
- (b) filling the attritor vessel with a powder containing the base material of the target alloy with a reduced alloy element content,
- (c) filling the attritor vessel with grinding balls containing the base material of the target alloy,
- (d) rotating the agitator of the attritor and/or of the attritor vessel, wherein the powder is alloyed by attrition of the attritor and/or attritor vessel and the grinding balls themselves.
- 2. The method according to item 1, wherein the target alloy contains TiAl.
- 3. The method according to items 1 or 2, wherein the base material powder is plasma-cleaned prior to filling and/or the attritor vessel is plasma-cleaned prior to application of a vacuum.
- 4. The method according to any one of the preceding items, wherein mechanical alloying takes place under a vacuum of from about 1×10−6 to about 1×10−4 mbar or under an inert protective gas atmosphere, in particular helium or argon, at from about 1×10−3 mbar to about 2000 mbar for a period of from about 0.5 h to about 10 h and at a temperature of less than or equal to about 400° C.
- 5. The method according to any one of the preceding items, wherein
-
- the powder of the base material in (b) comprises powder grains with a diameter of less than or equal to about 500 μm and in particular, with a diameter of at least about 15 μm and/or
- (d) proceeds at a rotational speed of from about 30 to about 2000 rpm for a period of from about 1 to about 10 hours.
- 6. The method according to any one of the preceding items, wherein the mechanically alloyed powder of the target alloy is heat-treated in a subsequent step in such a way that fine oxides are eliminated and/or the residual oxygen is gettered out of the crystal lattice of the powder.
- 7. The method according to item 6, wherein the powder of the target alloy is heat-treated by laser or electron beam melting, laser metal deposition and/or by hot isostatic pressing and the fine oxides with a size of from about 1 nm to about 500 nm are eliminated.
- 8. The method according to item 7, wherein the hot isostatic pressing proceeds in a temperature range of from about 1000 ° C. to about 1500 ° C. for a period of from about 1 h to about 10 h at a pressure of from about 10 to about 500 MPa.
- 9. The method according to any one of the preceding items, wherein
- as alloying component at least
-
- one of the elements Si, Y, Hf, Er, Gd, B, C, Zr, Y, Hf, Nb, Mo, W, Co, Cr, V is present and/or
- at least one compound from the group tungsten carbide, tungsten molybdenum alloys, zirconium oxide and yttrium oxide is present
- and/or
- as main constituent of the target alloy and/or of the powder of the base material at least one of the elements Fe, Ni, Ti, Al, Mo is present.
- 10. A device for mechanically alloying a high temperature-resistant target alloy, comprising at least the following components:
-
- an attritor vessel with internal walls,
- an agitator and
- at least one grinding ball,
- wherein all the components of the device which come into contact with the powder during mechanical alloying contain the base material and/or at least one of the alloying components of the target alloy.
- 11. The device according to item 10, wherein at least the internal walls of the attritor vessel comprise the base material and/or at least one of the alloying components of the target alloy.
- 12. The device according to at least one of items 10 and 11, wherein at least the surface of the grinding balls comprises the base material and/or at least one of the alloying components of the target alloy.
- 13. A high temperature-resistant alloy, produced using a method according to any one of items 1 to 9.
- 14. The alloy according to item 13, wherein the alloy contains at least one of the elements iron, nickel, titanium, aluminum, molybdenum.
- 15. Use of a device according to any one of items 10 to 13 in a method according to any one of items 1 to 9 for producing a high temperature-resistant target alloy.
- The particulars shown herein are by way of example and for purposes of illustrative discussion of the embodiments of the present invention only and are presented in the cause of providing what is believed to be the most useful and readily understood description of the principles and conceptual aspects of the present invention. In this regard, no attempt is made to show details of the present invention in more detail than is necessary for the fundamental understanding of the present invention, the description making apparent to those of skill in the art how the several forms of the present invention may be embodied in practice.
- First of all, an attritor vessel, whose internal walls consist of the base material, for example Ti and/or Al, and of some or all of the alloying components of the target alloy is plasma cleaned at a low pressure of from 0.05 to 200 Pa in an alternating electrical field by ionization of the real gas atoms. Then the attritor vessel is degassed at 10−3 mbar at a temperature of T=400° C. for 2 hours.
- The base material powder, for example of Ti and Al and for example Cr, V, W, Mo, Fe, Co, Zr, C and/or B, is likewise plasma cleaned under the same conditions and then loaded into the attritor vessel. The attritor accommodates around 5 kg of powder.
- The grinding arms, already located in the attritor vessel, of the agitator preferably consist only of Ti, Al and only of the corresponding alloying components, as do the grinding balls. The grinding balls have a diameter of around 2 cm. The grinding arms and the grinding balls are preferably formed from the solid material of an alloy similar or identical to the target alloy, such that not only does the surface of the grinding balls or of the grinding arms consist of the “target alloy” but also the material located under the surface.
- An alloy similar to the target alloy means that this similar alloy must not have any alloying components which are not present in the target alloy. The similar alloy may in this case comprise fewer alloying components than the target alloy, wherein the proportions of the alloying components in the similar alloy may be different from the target alloy.
- The attritor vessel is filled with grinding balls and then closed. Agitation is performed for 5 hours at a rotational speed of 100 rpm.
- To form the oxides, the mechanically alloyed powder with the corresponding alloying components is then hot isostatically pressed at 1200° C. for 3 hours at 2000 bar (200 MPa) in a helium protective gas atmosphere. Hf, Y, Zr, Er and Gd oxides arise in the process, which are finely distributed in the matrix.
- For example low pressure turbine (LPT) blades, LPT stators and/or LPT disks may consist of such an alloy. Hot gas baffles and/or further structural elements of a non-stationary or stationary gas turbine may also consist of such a target alloy.
- The above method may also be used for alloying other base materials. To this end, the base material of titanium and aluminum may be replaced for example by molybdenum, nickel or iron. The above-described alloying components and proportions may in this respect be identically selected for molybdenum, nickel or iron.
- Although the present invention has been described herein with reference to particular means, materials and embodiments, the present invention is not intended to be limited to the particulars disclosed herein; rather, the present invention extends to all functionally equivalent structures, methods and uses, such as are within the scope of the appended claims.
Claims (20)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102014222347.4 | 2014-11-03 | ||
DE102014222347.4A DE102014222347A1 (en) | 2014-11-03 | 2014-11-03 | Method for producing a high-temperature-resistant target alloy, a device, an alloy and a corresponding component |
Publications (1)
Publication Number | Publication Date |
---|---|
US20160122850A1 true US20160122850A1 (en) | 2016-05-05 |
Family
ID=54359709
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US14/887,765 Abandoned US20160122850A1 (en) | 2014-11-03 | 2015-10-20 | Method for producing a high temperature-resistant target alloy, a device, an alloy and a corresponding component |
Country Status (3)
Country | Link |
---|---|
US (1) | US20160122850A1 (en) |
EP (1) | EP3015199A3 (en) |
DE (1) | DE102014222347A1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111455329A (en) * | 2020-05-12 | 2020-07-28 | 长沙迅洋新材料科技有限公司 | Aluminum-titanium-boron target material and powder solid-phase alloying sintering method thereof |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107971491B (en) * | 2017-11-28 | 2020-01-07 | 北京航空航天大学 | Method for eliminating microcracks of nickel-based superalloy parts manufactured by selective electron beam melting and material increase |
CN108213440B (en) * | 2017-12-25 | 2019-12-31 | 安泰天龙钨钼科技有限公司 | Preparation method of molybdenum-rhenium alloy pipe |
CN111299669B (en) * | 2020-03-26 | 2021-09-14 | 宁波江丰电子材料股份有限公司 | Processing technology of target material |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3637930C1 (en) * | 1985-11-07 | 1992-04-09 | Fraunhofer Ges Forschung | Mfg. composite material for armour piercing ammunition - using alloy powder contg. tungsten@, nickel@, iron@, copper@, titanium@, aluminium@ and/or molybdenum@ |
US20070215463A1 (en) * | 2006-03-14 | 2007-09-20 | Applied Materials, Inc. | Pre-conditioning a sputtering target prior to sputtering |
WO2008010733A1 (en) * | 2006-07-20 | 2008-01-24 | Titanox Development Limited | Metal alloy powders production |
US8507085B2 (en) * | 2011-04-28 | 2013-08-13 | Hong Fu Jin Precision Industry (Shenzhen) Co., Ltd. | Anti-corrosion treatment process for aluminum or aluminum alloy and aluminum or aluminum alloy article thereof |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3617489A1 (en) * | 1986-05-24 | 1987-11-26 | Bayer Ag | SINTERABLE SI (DOWN ARROW) 3 (DOWN ARROW) N (DOWN ARROW) 4 (DOWN ARROW) POWDER AND ITS PRODUCTION METHOD |
US5424027A (en) | 1993-12-06 | 1995-06-13 | The United States Of America As Represented By The Secretary Of The Air Force | Method to produce hot-worked gamma titanium aluminide articles |
DE102011008809A1 (en) * | 2011-01-19 | 2012-07-19 | Mtu Aero Engines Gmbh | Generatively produced turbine blade and apparatus and method for their production |
-
2014
- 2014-11-03 DE DE102014222347.4A patent/DE102014222347A1/en not_active Withdrawn
-
2015
- 2015-09-23 EP EP15186417.0A patent/EP3015199A3/en not_active Withdrawn
- 2015-10-20 US US14/887,765 patent/US20160122850A1/en not_active Abandoned
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3637930C1 (en) * | 1985-11-07 | 1992-04-09 | Fraunhofer Ges Forschung | Mfg. composite material for armour piercing ammunition - using alloy powder contg. tungsten@, nickel@, iron@, copper@, titanium@, aluminium@ and/or molybdenum@ |
US20070215463A1 (en) * | 2006-03-14 | 2007-09-20 | Applied Materials, Inc. | Pre-conditioning a sputtering target prior to sputtering |
WO2008010733A1 (en) * | 2006-07-20 | 2008-01-24 | Titanox Development Limited | Metal alloy powders production |
US8507085B2 (en) * | 2011-04-28 | 2013-08-13 | Hong Fu Jin Precision Industry (Shenzhen) Co., Ltd. | Anti-corrosion treatment process for aluminum or aluminum alloy and aluminum or aluminum alloy article thereof |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111455329A (en) * | 2020-05-12 | 2020-07-28 | 长沙迅洋新材料科技有限公司 | Aluminum-titanium-boron target material and powder solid-phase alloying sintering method thereof |
Also Published As
Publication number | Publication date |
---|---|
DE102014222347A1 (en) | 2016-05-19 |
EP3015199A2 (en) | 2016-05-04 |
EP3015199A3 (en) | 2016-05-18 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
Zhou et al. | Microstructure, precipitates and mechanical properties of powder bed fused inconel 718 before and after heat treatment | |
Salvan et al. | CuCrZr alloy produced by laser powder bed fusion: Microstructure, nanoscale strengthening mechanisms, electrical and mechanical properties | |
JP5524257B2 (en) | Method for producing metal articles without melting | |
US11718897B2 (en) | Precipitation hardenable cobalt-nickel base superalloy and article made therefrom | |
US10029309B2 (en) | Production process for TiAl components | |
JP2007131949A (en) | AS-CAST GAMMA-TiAl ALLOY PREFORM AND PROCESS FOR PRODUCING SHEET OF GAMMA-TiAl | |
US20160122850A1 (en) | Method for producing a high temperature-resistant target alloy, a device, an alloy and a corresponding component | |
Liu et al. | Effects of Tantalum on the microstructure and properties of Ti-48Al-2Cr-2Nb alloy fabricated via laser additive manufacturing | |
Guo et al. | Microstructure of rapidly solidified Nb-based pre-alloyed powders for additive manufacturing | |
CN113073274B (en) | Novel method for preparing double-phase ultra-fine grain high-entropy alloy | |
Tan et al. | The evolution history of superalloy powders during hot consolidation and plastic deformation | |
Lazurenko et al. | Influence of the Ti/Al/Nb ratio on the structure and properties on intermetallic layers obtained on titanium by non-vacuum electron beam cladding | |
Kamyshnykova et al. | Grain refinement of cast peritectic TiAl-based alloy by solid-state phase transformations | |
JP6552137B2 (en) | Oxide particle dispersion strengthened Ni base super alloy | |
Zhu et al. | Effect of solution and aging treatments on the microstructure and mechanical properties of dual-phase high-entropy alloy prepared by laser-powder bed fusion using AlSi10Mg and FeCoCrNi powders | |
EP2913419B1 (en) | Ni superalloy component production method | |
JP6753838B2 (en) | Corrosion resistant article and manufacturing method | |
Klimová et al. | The effect of heat treatment on microstructure and hardness of in-situ Ti-38Al-7.5 Nb-5C-0.9 Mo composite. | |
JP2021502476A (en) | Alloy turbine parts containing MAX phase | |
Sun et al. | A Nb521 alloy processed by selective laser melting: Microstructure and tensile properties | |
CN110193597B (en) | Method for producing crystalline aluminum-iron-silicon alloy | |
EP3060366B1 (en) | Ferritic alloys and methods for preparing the same | |
Çelik et al. | The effect of the amount of Y2O3 doped to the MA6000 alloy produced by mechanical alloying method on wear behavior | |
Kardos | The influence of 2 at.% to 4 at.% zirconium on phase equilibria in γ-based Ti–Al alloys | |
Şelik et al. | The effect on wear behavior of the amount of Y2O3 doped to the MA6000 alloy produced by mechanical alloying method |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: MTU AERO ENGINES AG, GERMANY Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:SCHLOFFER, MARTIN, DR.;REEL/FRAME:037010/0440 Effective date: 20151109 |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: FINAL REJECTION MAILED |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: RESPONSE AFTER FINAL ACTION FORWARDED TO EXAMINER |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: ADVISORY ACTION MAILED |
|
STCV | Information on status: appeal procedure |
Free format text: NOTICE OF APPEAL FILED |
|
STCV | Information on status: appeal procedure |
Free format text: APPEAL BRIEF (OR SUPPLEMENTAL BRIEF) ENTERED AND FORWARDED TO EXAMINER |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: NON FINAL ACTION MAILED |
|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |