A vacuum arc remelting (VAR) system for forming an ingot from an electrode is disclosed. The system includes a crucible assembly configured to accommodate the electrode and the ingot. The system includes a primary electromagnetic energy source arranged about the crucible assembly. The primary electromagnetic energy source and the crucible assembly are configured to move relative to one another along a longitudinal axis of the crucible assembly. The system includes a secondary electromagnetic energy source arranged about an upper end portion of the crucible assembly. The secondary electromagnetic energy source is stationary and fixed to the upper end portion of the crucible assembly.
H05B 7/20 - Chauffage direct à arc, c.-à-d. au moins une extrémité de l'arc agissant directement sur le matériau à chauffer, y compris le chauffage par résistance additionnel produit par le courant d'arc traversant le matériau à chauffer
2.
TWIN COIL ARC SWEEP SYSTEM FOR VACUUM ARC REMELTING FURNACES
A vacuum arc remelting (VAR) system for forming an ingot from an electrode is disclosed. The system includes a crucible assembly configured to accommodate the electrode and the ingot. The system includes a primary electromagnetic energy source arranged about the crucible assembly. The primary electromagnetic energy source and the crucible assembly are configured to move relative to one another along a longitudinal axis of the crucible assembly. The system includes a secondary electromagnetic energy source arranged about an upper end portion of the crucible assembly. The secondary electromagnetic energy source is stationary and fixed to the upper end portion of the crucible assembly.
C22B 9/22 - Refusion des métaux en chauffant par énergie ondulatoire ou par rayonnement corpusculaire
F27D 11/06 - Chauffage par induction, c.-à-d. dans lequel le matériau à chauffer ou son contenant, ou bien les éléments incorporés dans celui-ci, constitue le secondaire d'un transformateur
F27D 11/12 - Aménagement des éléments pour le chauffage électrique dans ou sur les fours avec champs électromagnétiques agissant directement sur le matériau à chauffer
F27D 11/08 - Chauffage par décharge électrique, p. ex. décharge d'arc
F27D 99/00 - Matière non prévue dans les autres groupes de la présente sous-classe
3.
ALPHA-BETA TI ALLOY WITH IMPROVED HIGH TEMPERATURE PROPERTIES
An alpha-beta titanium alloy and method of manufacture includes forming an alpha-beta product from a titanium alloy with a composition in weight percent (wt. %) including 5.7-7.5 wt. % Al, 0.8-4.2 wt. % Mo, 0.0-3.0 wt. % Nb, 0.1-3.5 Sn, 0.1-3.0 wt. % Zr, 0.1-0.35 wt. % Si, 0.05-0.25 wt. % O, with the remainder being Ti and incidental impurities, and then heat treating the alpha-beta product with a first heat treatment step including a first temperature and a first time, a second heat treatment step including a second temperature and a second time, and a third heat treatment step including a third temperature less than the second temperature and a third time greater than the second time.
An alpha-beta titanium alloy and method of manufacture includes forming an alpha-beta product from a titanium alloy with a composition in weight percent (wt.%) including 5.7 - 7.5 wt.% Al, 0.8 - 4.2 wt.% Mo, 0.0 - 3.0 wt.% Nb, 0.1 - 3.5 Sn, 0.1 - 3.0 wt.% Zr, 0.1 - 0.35 wt.% Si, 0.05 - 0.25 wt.% O, with the remainder being Ti and incidental impurities, and then heat treating the alpha-beta product with a first heat treatment step including a first temperature and a first time, a second heat treatment step including a second temperature and a second time, and a third heat treatment step including a third temperature less than the second temperature and a third time greater than the second time.
An alpha-beta titanium alloy and method of manufacture includes forming an alpha-beta product from a titanium alloy with a composition in weight percent (wt.%) including 5.7 - 7.5 wt.% Al, 0.8 - 4.2 wt.% Mo, 0.0 - 3.0 wt.% Nb, 0.1 - 3.5 Sn, 0.1 - 3.0 wt.% Zr, 0.1 - 0.35 wt.% Si, 0.05 - 0.25 wt.% O, with the remainder being Ti and incidental impurities, and then heat treating the alpha-beta product with a first heat treatment step including a first temperature and a first time, a second heat treatment step including a second temperature and a second time, and a third heat treatment step including a third temperature less than the second temperature and a third time greater than the second time.
A method of vacuum arc remelting an ingot provided in a crucible assembly having an electrode includes generating a rotating magnetic field normal to a longitudinal axis of the ingot and localized to an arc region during remelting. The rotating magnetic field interacts with a melting current to produce a rotating arc directed radially outward.
C22B 9/22 - Refusion des métaux en chauffant par énergie ondulatoire ou par rayonnement corpusculaire
H05B 7/20 - Chauffage direct à arc, c.-à-d. au moins une extrémité de l'arc agissant directement sur le matériau à chauffer, y compris le chauffage par résistance additionnel produit par le courant d'arc traversant le matériau à chauffer
7.
VIDEO ANALYSIS-BASED ALGORITHM FOR TRIGGERING POWER CUTBACK IN VACUUM ARC REMELTING
A control system includes a vision system including an imaging device and a VAR monitoring system configured to determine a power adjustment phase of the VAR process based on the images from the vision system and a process parameter. The VAR monitoring system includes a vision analysis module configured to analyze the images from the vision system to detect a melt marker based on a remelt image process model, and a prediction module configured to predict an operational characteristic of the VAR process that is associated with the power adjustment relative to a melt marker location and a remelt prediction model. The VAR monitoring system is configured to initiate the power adjustment phase in response to the melt marker satisfying a predetermined melt marker condition, the operational characteristic of the VAR process satisfying a predetermined operational condition, or a combination thereof.
F27D 11/08 - Chauffage par décharge électrique, p. ex. décharge d'arc
F27D 19/00 - Aménagement des dispositifs de commande
F27D 21/02 - Dispositifs d'observation ou d'éclairage
H05B 7/144 - Sources de puissance spécialement adaptées pour le chauffage par décharge électriqueCommande automatique de la puissance, p. ex. en commandant la position des électrodes
8.
Video analysis-based algorithm for triggering power cutback in vacuum arc remelting
A control system includes a vision system including an imaging device and a VAR monitoring system configured to determine a power adjustment phase of the VAR process based on the images from the vision system and a process parameter. The VAR monitoring system includes a vision analysis module configured to analyze the images from the vision system to detect a melt marker based on a remelt image process model, and a prediction module configured to predict an operational characteristic of the VAR process that is associated with the power adjustment relative to a melt marker location and a remelt prediction model. The VAR monitoring system is configured to initiate the power adjustment phase in response to the melt marker satisfying a predetermined melt marker condition, the operational characteristic of the VAR process satisfying a predetermined operational condition, or a combination thereof.
G05B 13/02 - Systèmes de commande adaptatifs, c.-à-d. systèmes se réglant eux-mêmes automatiquement pour obtenir un rendement optimal suivant un critère prédéterminé électriques
A control system includes a vision system including an imaging device and a VAR monitoring system configured to determine a power adjustment phase of the VAR process based on the images from the vision system and a process parameter. The VAR monitoring system includes a vision analysis module configured to analyze the images from the vision system to detect a melt marker based on a remelt image process model, and a prediction module configured to predict an operational characteristic of the VAR process that is associated with the power adjustment relative to a melt marker location and a remelt prediction model. The VAR monitoring system is configured to initiate the power adjustment phase in response to the melt marker satisfying a predetermined melt marker condition, the operational characteristic of the VAR process satisfying a predetermined operational condition, or a combination thereof.
F27D 11/08 - Chauffage par décharge électrique, p. ex. décharge d'arc
F27D 19/00 - Aménagement des dispositifs de commande
F27D 21/02 - Dispositifs d'observation ou d'éclairage
H05B 7/144 - Sources de puissance spécialement adaptées pour le chauffage par décharge électriqueCommande automatique de la puissance, p. ex. en commandant la position des électrodes
An electron beam (EB) gun assembly for an EB furnace is provided. The EB gun assembly includes an EB gun-frame assembly including a skeleton frame (100) and at least one EB gun (22) mounted to the skeleton frame, and the EB gun-frame assembly is configured to rigidly mount onto a first EB chamber lid (40a) and melt material in a first EB chamber and be removed and rigidly mount onto a second EB chamber lid (40b) and melt material in a second EB chamber. In some forms, the EB gun assembly includes at least one mounting frame (120) and the at least one EB gun is mounted to the at least one mounting frame and the at least one mounting frame is mounted to the skeleton frame.
An electron beam (EB) gun assembly for an EB furnace is provided. The EB gun assembly includes an EB gun-frame assembly including a skeleton frame (100) and at least one EB gun (22) mounted to the skeleton frame, and the EB gun-frame assembly is configured to rigidly mount onto a first EB chamber lid (40a) and melt material in a first EB chamber and be removed and rigidly mount onto a second EB chamber lid (40b) and melt material in a second EB chamber. In some forms, the EB gun assembly includes at least one mounting frame (120) and the at least one EB gun is mounted to the at least one mounting frame and the at least one mounting frame is mounted to the skeleton frame.
An electron beam (EB) gun assembly for an EB furnace is provided. The EB gun assembly includes an EB gun-frame assembly including a skeleton frame and at least one EB gun mounted to the skeleton frame, and the EB gun-frame assembly is configured to rigidly mount onto a first EB chamber lid and melt material in a first EB chamber and be removed and rigidly mount onto a second EB chamber lid and melt material in a second EB chamber. In some forms, the EB gun assembly includes at least one mounting frame and the at least one EB gun is mounted to the at least one mounting frame and the at least one mounting frame is mounted to the skeleton frame.
F27B 5/14 - Aménagement des dispositifs de chauffage
C22B 9/22 - Refusion des métaux en chauffant par énergie ondulatoire ou par rayonnement corpusculaire
F27B 5/04 - Fours à mouflesFours à cornuesAutres fours où la charge est complètement isolée adaptés pour le traitement de la charge sous vide ou sous atmosphère contrôlée
13.
TITANIUM ALLOYS HAVING IMPROVED CORROSION RESISTANCE, STRENGTH, DUCTILITY, AND TOUGHNESS
Titanium alloys with an improved and unexpected combination of corrosion resistance, strength, ductility and toughness are provided. The titanium alloys contain molybdenum, nickel, zirconium, iron, and oxygen as alloying agents. Also the titanium alloys may be subjected to thermal treatments. The titanium alloys can include molybdenum between 3.0 to 4.5 wt.%, nickel between 0.1 to 1.0 wt.%, zirconium between 0.1 to 1.5 wt.%, iron between 0.05 to 0.3 wt.%, oxygen between 0.05 to 0.25 wt.%, and a balance of titanium and unavoidable impurities. The titanium alloys can have a yield strength between 550 to 750 MPa, a tensile strength between 700 to 900 MPa, an elongation to failure between 25 to 35%, a reduction in area between 55 to 70%, and a corrosion rate between 0.5 to 2.5 mils per year when exposed to 1 wt.% boiling hydrochloric acid per the ASTM G-31 test method.
Titanium alloys with an improved and unexpected combination of corrosion resistance, strength, ductility and toughness are provided. The titanium alloys contain molybdenum, nickel, zirconium, iron, and oxygen as alloying agents. Also the titanium alloys may be subjected to thermal treatments. The titanium alloys can include molybdenum between 3.0 to 4.5 wt.%, nickel between 0.1 to 1.0 wt.%, zirconium between 0.1 to 1.5 wt.%, iron between 0.05 to 0.3 wt.%, oxygen between 0.05 to 0.25 wt.%, and a balance of titanium and unavoidable impurities. The titanium alloys can have a yield strength between 550 to 750 MPa, a tensile strength between 700 to 900 MPa, an elongation to failure between 25 to 35%, a reduction in area between 55 to 70%, and a corrosion rate between 0.5 to 2.5 mils per year when exposed to 1 wt.% boiling hydrochloric acid per the ASTM G-31 test method.
Titanium alloys with an improved and unexpected combination of corrosion resistance, strength, ductility and toughness are provided. The titanium alloys contain molybdenum, nickel, zirconium, iron, and oxygen as alloying agents. Also the titanium alloys may be subjected to thermal treatments. The titanium alloys can include molybdenum between 3.0 to 4.5 wt. %, nickel between 0.1 to 1.0 wt. %, zirconium between 0.1 to 1.5 wt. %, iron between 0.05 to 0.3 wt. %, oxygen between 0.05 to 0.25 wt. %, and a balance of titanium and unavoidable impurities. The titanium alloys can have a yield strength between 550 to 750 MPa, a tensile strength between 700 to 900 MPa, an elongation to failure between 25 to 35%, a reduction in area between 55 to 70%, and a corrosion rate between 0.5 to 2.5 mils per year when exposed to 1 wt. % boiling hydrochloric acid per the ASTM G-31 test method.
A titanium alloy composition is provided. In weight percent (wt.%), the alloy includes 5.7 to 8.0% vanadium, 0.5 to 1.75% aluminum, 0.25 to 1.5% iron, 0.1 to 0.2% oxygen, up to 0.15% silicon, up to 0.1% carbon and less than 0.03% nitrogen is provided. In one form, the titanium alloy has a 0.2% yield strength between 600 to 850 MPa, an ultimate tensile strength between 700 to 950 MPa, a percent elongation to failure between 20 to 30%, a percent reduction in area between 40 to 80%, a Charpy U-notch impact energy between 30 to 70 J, and/or a Charpy V-notch impact energy between 40 to 150 J.
A titanium alloy composition is provided. In weight percent (wt.%), the alloy includes 5.7 to 8.0% vanadium, 0.5 to 1.75% aluminum, 0.25 to 1.5% iron, 0.1 to 0.2% oxygen, up to 0.15% silicon, up to 0.1% carbon and less than 0.03% nitrogen is provided. In one form, the titanium alloy has a 0.2% yield strength between 600 to 850 MPa, an ultimate tensile strength between 700 to 950 MPa, a percent elongation to failure between 20 to 30%, a percent reduction in area between 40 to 80%, a Charpy U-notch impact energy between 30 to 70 J, and/or a Charpy V-notch impact energy between 40 to 150 J.
A titanium alloy composition is provided. In weight percent (wt. %), the alloy includes 5.7 to 8.0% vanadium, 0.5 to 1.75% aluminum, 0.25 to 1.5% iron, 0.1 to 0.2% oxygen, up to 0.15% silicon, up to 0.1% carbon and less than 0.03% nitrogen is provided. In one form, the titanium alloy has a 0.2% yield strength between 600 to 850 MPa, an ultimate tensile strength between 700 to 950 MPa, a percent elongation to failure between 20 to 30%, a percent reduction in area between 40 to 80%, a Charpy U-notch impact energy between 30 to 70 J, and/or a Charpy V-notch impact energy between 40 to 150 J.
A vacuum arc remelting system for forming an ingot from an electrode is provided that includes a crucible assembly configured to accommodate the electrode and the ingot, an electromagnetic energy source arranged about the crucible assembly, and a lift mechanism operable to move the electromagnetic energy source along a longitudinal axis of the crucible assembly. A magnetic field generated by the electromagnetic energy source is localized to an arc region during remelting, and in one form, the electromagnetic energy source is a coil assembly having a magnetic core and a plurality of coil pairs wrapped around the core, wherein the coil assembly is operable to generate a magnetic field from the coil based on electric current flowing in the plurality of coil pairs.
F27B 3/08 - Fours à sole, p. ex. fours à réverbérationFours à arc électrique à chauffage électrique, p. ex. fours à arc électrique, avec ou sans une autre source de chaleur
F27D 11/06 - Chauffage par induction, c.-à-d. dans lequel le matériau à chauffer ou son contenant, ou bien les éléments incorporés dans celui-ci, constitue le secondaire d'un transformateur
F27D 11/08 - Chauffage par décharge électrique, p. ex. décharge d'arc
H05B 6/34 - Dispositions pour la circulation du métal fondu
H05B 7/07 - Électrodes prévues pour fondre à l'usage
H05B 7/20 - Chauffage direct à arc, c.-à-d. au moins une extrémité de l'arc agissant directement sur le matériau à chauffer, y compris le chauffage par résistance additionnel produit par le courant d'arc traversant le matériau à chauffer
20.
COMPACT COIL ASSEMBLY FOR A VACUUM ARC REMELTING SYSTEM
A vacuum arc remelting system for forming an ingot from an electrode is provided that includes a crucible assembly configured to accommodate the electrode and the ingot, an electromagnetic energy source arranged about the crucible assembly, and a lift mechanism operable to move the electromagnetic energy source along a longitudinal axis of the crucible assembly. A magnetic field generated by the electromagnetic energy source is localized to an arc region during remelting, and in one form, the electromagnetic energy source is a coil assembly having a magnetic core and a plurality of coil pairs wrapped around the core, wherein the coil assembly is operable to generate a magnetic field from the coil based on electric current flowing in the plurality of coil pairs.
F27B 3/08 - Fours à sole, p. ex. fours à réverbérationFours à arc électrique à chauffage électrique, p. ex. fours à arc électrique, avec ou sans une autre source de chaleur
F27D 11/06 - Chauffage par induction, c.-à-d. dans lequel le matériau à chauffer ou son contenant, ou bien les éléments incorporés dans celui-ci, constitue le secondaire d'un transformateur
F27D 11/08 - Chauffage par décharge électrique, p. ex. décharge d'arc
H05B 6/34 - Dispositions pour la circulation du métal fondu
H05B 7/07 - Électrodes prévues pour fondre à l'usage
H05B 7/20 - Chauffage direct à arc, c.-à-d. au moins une extrémité de l'arc agissant directement sur le matériau à chauffer, y compris le chauffage par résistance additionnel produit par le courant d'arc traversant le matériau à chauffer
21.
Compact coil assembly for a vacuum arc remelting system
A vacuum arc remelting system for forming an ingot from an electrode is provided that includes a crucible assembly configured to accommodate the electrode and the ingot, an electromagnetic energy source arranged about the crucible assembly, and a lift mechanism operable to move the electromagnetic energy source along a longitudinal axis of the crucible assembly. A magnetic field generated by the electromagnetic energy source is localized to an arc region during remelting, and in one form, the electromagnetic energy source is a coil assembly having a magnetic core and a plurality of coil pairs wrapped around the core, wherein the coil assembly is operable to generate a magnetic field from the coil based on electric current flowing in the plurality of coil pairs.
C22B 9/22 - Refusion des métaux en chauffant par énergie ondulatoire ou par rayonnement corpusculaire
H05B 7/20 - Chauffage direct à arc, c.-à-d. au moins une extrémité de l'arc agissant directement sur le matériau à chauffer, y compris le chauffage par résistance additionnel produit par le courant d'arc traversant le matériau à chauffer
22.
PLANETARY REFORM ROLLER AND METHOD OF REFORMING A VESSEL CAVITY
A device for reforming a vessel cavity is provided that includes a central shaft, a central gear coupled to the central shaft, and a plurality of roller gears coupled to the central gear, with each of the plurality of roller gears having a central portion. A proximal support member couples the plurality of roller gears and at least one of the central gear and the central shaft. A plurality of rollers is also provided, each of the plurality of rollers connected to the central portion of each of the plurality of roller gears. In one form, at least one idler member is disposed between the plurality of rollers. A distal support member couples the plurality of rollers and at least one of the central gear and a translation member. Also, a stationary member is secured to a distal portion of the vessel cavity.
B24B 39/02 - Machines ou dispositifs à brunir, c.-à-d. utilisant des organes de pression pour durcir les surfacesAccessoires à cet effet pour travailler intérieurement des surfaces de révolution
23.
PLANETARY REFORM ROLLER AND METHOD OF REFORMING A VESSEL CAVITY
A device for reforming a vessel cavity is provided that includes a central shaft, a central gear coupled to the central shaft, and a plurality of roller gears coupled to the central gear, with each of the plurality of roller gears having a central portion. A proximal support member couples the plurality of roller gears and at least one of the central gear and the central shaft. A plurality of rollers is also provided, each of the plurality of rollers connected to the central portion of each of the plurality of roller gears. In one form, at least one idler member is disposed between the plurality of rollers. A distal support member couples the plurality of rollers and at least one of the central gear and a translation member. Also, a stationary member is secured to a distal portion of the vessel cavity.
B24B 39/02 - Machines ou dispositifs à brunir, c.-à-d. utilisant des organes de pression pour durcir les surfacesAccessoires à cet effet pour travailler intérieurement des surfaces de révolution
24.
Planetary reform roller and method of reforming a vessel cavity
A device for reforming a vessel cavity is provided that includes a central shaft, a central gear coupled to the central shaft, and a plurality of roller gears coupled to the central gear, with each of the plurality of roller gears having a central portion. A proximal support member couples the plurality of roller gears and at least one of the central gear and the central shaft. A plurality of rollers is also provided, each of the plurality of rollers connected to the central portion of each of the plurality of roller gears. In one form, at least one idler member is disposed between the plurality of rollers. A distal support member couples the plurality of rollers and at least one of the central gear and a translation member. Also, a stationary member is secured to a distal portion of the vessel cavity.
B21B 13/20 - Cages de laminoirs, c.-à-d. ensembles composés d'un châssis, de cylindres et d’accessoires pour laminage progressif intermittent ou par train planétaire pour laminage par train planétaire
B21B 1/42 - Méthodes de laminage ou laminoirs pour la fabrication des produits semi-finis de section pleine ou de profilésSéquence des opérations dans les trains de laminoirsInstallation d'une usine de laminage, p. ex. groupement de cagesSuccession des passes ou des alternances de passes pour laminage progressif intermittent ou par train planétaire
B24B 39/02 - Machines ou dispositifs à brunir, c.-à-d. utilisant des organes de pression pour durcir les surfacesAccessoires à cet effet pour travailler intérieurement des surfaces de révolution
An alpha-beta titanium alloy is provided. The alpha-beta titanium alloy composition includes concentrations of Al from about 4.7 wt. % to about 6.0 wt. %; V from about 6.5 wt. % to about 8.0 wt. %; Si from about 0.15 wt. % to about 0.6 wt. %; Fe up to about 0.3 wt. %; O from about 0.15 wt. % to about 0.23 wt. %; Ti and incidental impurities as a balance. The alpha-beta titanium alloy may have a solution treated and aged microstructure and an elongation of at least about 10% at room temperature. Also, the alpha-beta titanium alloy may have an Al/V ratio from about 0.65 to about 0.8, the Al/V ratio being equal to the concentration of the Al divided by the concentration of the V in weight percent.
B22D 21/00 - Coulée de métaux non ferreux ou de composés métalliques, dans la mesure où leurs propriétés métallurgiques affectent le procédé de couléeUtilisation de compositions appropriées
A method of making an alpha-beta titanium alloy is provided. The method includes forming a melt and solidifying the melt to form an ingot. The melt composition includes concentrations of Al from about 4.7 wt. % to about 6.0 wt. %; V from about 6.5 wt. % to about 8.0 wt. %; Si at less than 1 wt. %; Fe at up to about 0.3 wt. %; 0 at less than 1 wt. %; and a balance of Ti and incidental impurities. Furthermore, the Al/V ratio in the melt is equal to the concentration of the Al divided by the concentration of the V in weight percent is from about 0.65 to about 0.8.
C22C 1/02 - Fabrication des alliages non ferreux par fusion
B22D 21/00 - Coulée de métaux non ferreux ou de composés métalliques, dans la mesure où leurs propriétés métallurgiques affectent le procédé de couléeUtilisation de compositions appropriées
27.
Beta titanium alloy sheet for elevated temperature applications
Titanium alloys formed into a part or component used in applications where a key design criterion is the energy absorbed during deformation of the part when exposed to impact, explosive blast, and/or other forms of shock loading is described. The titanium alloys generally comprise a titanium base with added amounts of aluminum, an isomorphous beta stabilizing element such as vanadium, a eutectoid beta stabilizing element such as silicon and iron, and incidental impurities. The titanium alloys exhibit up to 70% or more improvement in ductility and up to a 16% improvement in ballistic impact resistance over a Ti-6Al-4V alloy, as well as absorbing up to 50% more energy than the Ti-6Al-4V alloy in Charpy impact tests. A method of forming a part that incorporates the titanium alloys and uses a combination of recycled materials and new materials is also described.
A high strength alpha-beta titanium alloy is provided that has improved high temperature oxidation resistance, high temperature strength and creep resistance, and improved superplasticity. In one form, the alloy comprises about 4.5 wt% to about 5.5 wt% aluminum, about 3.0 wt% to about 5.0 wt% vanadium, about 0.3 wt% to about 1.8 wt% molybdenum, about 0.2 wt% to about 1.2 wt% iron, about 0.12 wt% to about 0.25 wt% oxygen, about 0.10 wt% to about 0.40 wt% silicon, with the balance titanium and incidental impurities, with each incidental impurity being less than about 0.1 wt% and about 0.5 wt%, respectively, in total.
A high strength alpha-beta alloy is provided that has improved high temperature oxidation resistance, high temperature strength and creep resistance, and improved superplasticity. In one form, the alloy comprises about 4.5 wt % to about 5.5 wt % aluminum, about 3.0 wt % to about 5.0 wt % vanadium, about 0.3 wt % to about 1.8 wt % molybdenum, about 0.2 wt % to about 1.2 wt % iron, about 0.12 wt % to about 0.25 wt % oxygen, about 0.10 wt % to about 0.40 wt % silicon, with the balance titanium and incidental impurities, with each being less than about 0.1 wt % and about 0.5 wt %, respectively, in total.
A high strength alpha-beta titanium alloy is provided that has improved high temperature oxidation resistance, high temperature strength and creep resistance, and improved superplasticity. In one form, the alloy comprises about 4.5 wt% to about 5.5 wt% aluminum, about 3.0 wt% to about 5.0 wt% vanadium, about 0.3 wt% to about 1.8 wt% molybdenum, about 0.2 wt% to about 1.2 wt% iron, about 0.12 wt% to about 0.25 wt% oxygen, about 0.10 wt% to about 0.40 wt% silicon, with the balance titanium and incidental impurities, with each incidental impurity being less than about 0.1 wt% and about 0.5 wt%, respectively, in total.
Titanium alloys formed into a part or component used in applications where a key design criterion is the energy absorbed during deformation of the part when exposed to impact, explosive blast, and/or other forms of shock loading is described. The titanium alloys generally comprise a titanium base with added amounts of aluminum, an isomorphous beta stabilizing element such as vanadium, a eutectoid beta stabilizing element such as silicon and iron, and incidental impurities. The titanium alloys exhibit up to 70% or more improvement in ductility and up to a 16% improvement in ballistic impact resistance over a Ti-6Al-4V alloy, as well as absorbing up to 50% more energy than the Ti-6Al-4V alloy in Charpy impact tests. A method of forming a part that incorporates the titanium alloys and uses a combination of recycled materials and new materials is also described.
A cold rollable beta titanium alloy is provided by the present disclosure that exhibits excellent tensile strength, and creep and oxidation resistance at elevated temperatures. In one form, the beta titanium alloy includes molybdenum in an amount ranging between 13.0 wt.% to 20.0 wt.%, niobium between 2.0 wt.% to 4.0 wt.%, silicon between 0.1 wt.% to 0.4 wt.%, aluminum between 3.0 wt.% to 5.0 wt.%, at least one of: zirconium up to 3.0 wt.% and tin up to 5.0 wt.%, oxygen up to 0.25 wt.%, and a balance of titanium and incidental impurities. Additionally, the ranges for each element satisfies the conditions of: (i) 6.0 wt.% < X wt.% < 7.5 wt.%; and (ii) 3.5 wt.% < Y wt.% < 5.15 wt.%, where X wt.% = aluminum + tin/3 + zirconium/6 + 10*(oxygen + nitrogen+carbon), and Y wt.% = aluminum + silicon*(zirconium + tin).
A cold rollable beta titanium alloy is provided by the present disclosure that exhibits excellent tensile strength, and creep and oxidation resistance at elevated temperatures. In one form, the beta titanium alloy includes molybdenum in an amount ranging between 13.0 wt.% to 20.0 wt.%, niobium between 2.0 wt.% to 4.0 wt.%, silicon between 0.1 wt.% to 0.4 wt.%, aluminum between 3.0 wt.% to 5.0 wt.%, at least one of: zirconium up to 3.0 wt.% and tin up to 5.0 wt.%, oxygen up to 0.25 wt.%, and a balance of titanium and incidental impurities. Additionally, the ranges for each element satisfies the conditions of: (i) 6.0 wt.% < X wt.% < 7.5 wt.%; and (ii) 3.5 wt.% < Y wt.% < 5.15 wt.%, where X wt.% = aluminum + tin/3 + zirconium/6 + 10*(oxygen + nitrogen+carbon), and Y wt.% = aluminum + silicon*(zirconium + tin).
An alpha-beta titanium alloy comprises Al at a concentration of from about 4.7 wt. % to about 6.0 wt. %; V at a concentration of from about 6.5 wt. % to about 8.0 wt. %; Si at a concentration of from about 0.15 wt. % to about 0.6 wt. %; Fe at a concentration of up to about 0.3 wt. %; O at a concentration of from about 0.15 wt. % to about 0.23 wt. %; and Ti and incidental impurities as a balance. The alpha-beta titanium alloy has an Al/V ratio of from about 0.65 to about 0.8, where the Al/V ratio is defined as the ratio of the concentration of Al to the concentration of V in the alloy, with each concentration being in weight percent (wt %).
B22D 21/00 - Coulée de métaux non ferreux ou de composés métalliques, dans la mesure où leurs propriétés métallurgiques affectent le procédé de couléeUtilisation de compositions appropriées
An alpha-beta titanium alloy comprises Al at a concentration of from about 4.7 wt.% to about 6.0 wt.%; V at a concentration of from about 6.5 wt.% to about 8.0 wt.%; Si at a concentration of from about 0.1 5 wt.% to about 0.6 wt.%; Fe at a concentration of up to about 0.3 wt.%; O at a concentration of from about 0.15 wt.% to about 0.23 wt.%; and Ti and incidental impurities as a balance. The alpha-beta titanium alloy has an Al/V ratio of from about 0.65 to about 0.8, where the Al/V ratio is defined as the ratio of the concentration of Al to the concentration of V in the alloy, with each concentration being in weight percent (wt.%).
An alpha-beta titanium alloy comprises Al at a concentration of from about 4.7 wt.% to about 6.0 wt.%; V at a concentration of from about 6.5 wt.% to about 8.0 wt.%; Si at a concentration of from about 0.1 5 wt.% to about 0.6 wt.%; Fe at a concentration of up to about 0.3 wt.%; O at a concentration of from about 0.15 wt.% to about 0.23 wt.%; and Ti and incidental impurities as a balance. The alpha-beta titanium alloy has an Al/V ratio of from about 0.65 to about 0.8, where the Al/V ratio is defined as the ratio of the concentration of Al to the concentration of V in the alloy, with each concentration being in weight percent (wt.%).
Titanium alloys formed into a part or component used in applications where a key design criterion is the energy absorbed during deformation of the part when exposed to impact, explosive blast, and/or other forms of shock loading is described. The titanium alloys generally comprise a titanium base with added amounts of aluminum, an isomorphous beta stabilizing element such as vanadium, a eutectoid beta stabilizing element such as silicon and iron, and incidental impurities. The titanium alloys exhibit up to 70% or more improvement in ductility and up to a 16% improvement in ballistic impact resistance over a Ti-6AI-4V alloy, as well as absorbing up to 50% more energy than the Ti-6AI-4V alloy in Charpy impact tests. A method of forming a part that incorporates the titanium alloys and uses a combination of recycled materials and new materials is also described.
Titanium alloys formed into a part or component used in applications where a key design criterion is the energy absorbed during deformation of the part when exposed to impact, explosive blast, and/or other forms of shock loading is described. The titanium alloys generally comprise a titanium base with added amounts of aluminum, an isomorphous beta stabilizing element such as vanadium, a eutectoid beta stabilizing element such as silicon and iron, and incidental impurities. The titanium alloys exhibit up to 70% or more improvement in ductility and up to a 16% improvement in ballistic impact resistance over a Ti-6AI-4V alloy, as well as absorbing up to 50% more energy than the Ti-6AI-4V alloy in Charpy impact tests. A method of forming a part that incorporates the titanium alloys and uses a combination of recycled materials and new materials is also described.
A titanium alloy having high strength, fine grain size, and low cost and a method of manufacturing the same is disclosed. In particular, the inventive alloy offers a strength increase of about 100 MPa over Ti 6-4, with a comparable density and near equivalent ductility. The inventive alloy is particularly useful for a multitude of applications including components of aircraft engines. The Ti alloy comprises, in weight percent, about 6.0 to about 6.7 % aluminum, about 1.4 to about 2.0 % vanadium, about 1.4 to about 2.0 % molybdenum, about 0.20 to about 0.42 % silicon, about 0.17 to about 0.23 % oxygen, maximum about 0.24 % iron, maximum about 0.08 % carbon and balance titanium with incidental impurities.
A titanium alloy having high strength, fine grain size, and low cost and a method of manufacturing the same is disclosed. In particular, the inventive alloy offers a strength increase of about 100 MPa over Ti 6-4, with a comparable density and near equivalent ductility. The inventive alloy is particularly useful for a multitude of applications including components of aircraft engines. The Ti alloy comprises, in weight percent, about 6.0 to about 6.7 % aluminum, about 1.4 to about 2.0 % vanadium, about 1.4 to about 2.0 % molybdenum, about 0.20 to about 0.42 % silicon, about 0.17 to about 0.23 % oxygen, maximum about 0.24 % iron, maximum about 0.08 % carbon and balance titanium with incidental impurities.
A method of manufacturing fine grain titanium alloy sheets that is suitable for superplastic forming (SPF) is disclosed. In one embodiment, a high strength titanium alloy comprising: Al: about 4.5% to about 5.5%, V: about 3.0% to about 5.0%, Mo: about 0.3% to about 1.8%, Fe: about 0.2% to about 0.8%, O: about 0.12% to about 0.25% with balance titanium is forged and hot rolled to sheet bar, which is then fast-cooled from a temperature higher than beta transus. According to this embodiment, the sheet bar is heated between about 1400° F. to about 1550° F. and rolled to intermediate gage. After reheating to a temperature from about 1400° F. to about 1550° F., hot rolling is performed in a direction perpendicular to the previous rolling direction to minimize anisotropy of mechanical properties. The sheets are then annealed at a temperature between about 1300° F. to about 1550° F. followed by grinding and pickling.
A method of manufacturing fine grain titanium alloy sheets that is suitable for superplastic forming (SPF) is disclosed. In one embodiment, a high strength titanium alloy comprising: A1: about 4.5% to about 5.5%, V: about 3.0% to about 5.0%, Mo: about 0.3% to about 1.8%, Fe: about 0.2% to about 0.8%, O: about 0.12% to about 0.25% with balance titanium is forged and hot rolled to sheet bar, which is then fast-cooled from a temperature higher than beta transus. According to this embodiment, the sheet bar is heated between about 1400°F to about 1550°F and rolled to intermediate gage. After reheating to a temperature from about 1400°F to about 1550°F, hot rolling is performed in a direction perpendicular to the previous rolling direction to minimize anisotropy of mechanical properties. The sheets are then annealed at a temperature between about 1300°F to about 1550°F followed by grinding and pickling.
C22F 1/18 - Métaux réfractaires ou à point de fusion élevé ou leurs alliages
C23F 17/00 - Procédés à étapes multiples pour le traitement de surface de matériaux métalliques utilisant au moins un procédé couvert par la classe et au moins un procédé couvert soit par la sous-classe , soit par la sous-classe , soit par la classe
C23G 1/00 - Nettoyage ou décapage de matériaux métalliques au moyen de solutions ou de sels fondus
45.
METHOD FOR THE MANUFACTURE OF ALPHA-BETA TI-AL-V-MO-FE ALLOY SHEETS
A method of manufacturing fine grain titanium alloy sheets that is suitable for superplastic forming (SPF) is disclosed. In one embodiment, a high strength titanium alloy comprising: A1: about 4.5% to about 5.5%, V: about 3.0% to about 5.0%, Mo: about 0.3% to about 1.8%, Fe: about 0.2% to about 0.8%, O: about 0.12% to about 0.25% with balance titanium is forged and hot rolled to sheet bar, which is then fast-cooled from a temperature higher than beta transus. According to this embodiment, the sheet bar is heated between about 1400°F to about 1550°F and rolled to intermediate gage. After reheating to a temperature from about 1400°F to about 1550°F, hot rolling is performed in a direction perpendicular to the previous rolling direction to minimize anisotropy of mechanical properties. The sheets are then annealed at a temperature between about 1300°F to about 1550°F followed by grinding and pickling.
50 ballistic limit of about 1936 fps. The Ti alloy may be manufactured using a combination of recycled and/or virgin materials, thereby providing a low-cost route to the formation of high-quality armor plate for use in military systems.
A high strength near-beta titanium alloy including, in weight %, 5.3 to 5.7% aluminum, 4.8 to 5.2% vanadium, 0.7 to 0.9% iron, 4.6 to 5.3% molybdenum, 2.0 to 2.5% chromium, and 0.12 to 0.16% oxygen with balance titanium and incidental impurities is provided. An aviation system component comprising the high strength near-beta titanium alloy, and a method for the manufacture of a titanium alloy for use in high strength, deep hardenability, and excellent ductility applications are also provided.
A method for qualifying an automated process for inspecting and sorting particles through the production and use of seed particles is disclosed. In one embodiment, seed particles are produced by forming a conformal surface layer on a plurality of particles, thereby imparting them with at least one property whose value or range of values is the same as or about the same as a value or range of values of a corresponding property of undesirable particles. By introducing a predetermined quantity of seed particles, their detection and removal by the automated sorting system can be used to periodically calibrate and qualify the sorting system without interrupting the manufacturing operations or introducing actual undesirable particles into the process stream. The production and use of seed particles to qualify an automated sorting system is particularly well-suited for use with Ti sponge sorting operations.
G06F 7/00 - Procédés ou dispositions pour le traitement de données en agissant sur l'ordre ou le contenu des données maniées
G01B 5/28 - Dispositions pour la mesure caractérisées par l'utilisation de techniques mécaniques pour mesurer la rugosité ou l'irrégularité des surfaces
49.
SYSTEM AND METHOD FOR INSPECTING AND SORTING PARTICLES AND PROCESS FOR QUALIFYING THE SAME WITH SEED PARTICLES
A method for qualifying an automated process for inspecting and sorting particles through the production and use of seed particles is disclosed. In one embodiment, seed particles are produced by forming a conformal surface layer on a plurality of particles, thereby imparting them with at least one property whose value or range of values is the same as or about the same as a value or range of values of a corresponding property of undesirable particles. By introducing a predetermined quality of seed particles, their detection and removal by the automated sorting system can be used to periodically calibrate and qualify the sorting system without interrupting the manufacturing operations or introducing actual undesirable particles into the process stream. The production and use of seed particles to qualify an automated sorting system is particularly well-suited for use with Ti sponge sorting operations.
A method for qualifying an automated process for inspecting and sorting particles through the production and use of seed particles is disclosed. In one embodiment, seed particles are produced by forming a conformal surface layer on a plurality of particles, thereby imparting them with at least one property whose value or range of values is the same as or about the same as a value or range of values of a corresponding property of undesirable particles. By introducing a predetermined quality of seed particles, their detection and removal by the automated sorting system can be used to periodically calibrate and qualify the sorting system without interrupting the manufacturing operations or introducing actual undesirable particles into the process stream. The production and use of seed particles to qualify an automated sorting system is particularly well-suited for use with Ti sponge sorting operations.
A titanium alloy having high strength, fine grain size, and low cost and a method of manufacturing the same is disclosed. In particular, the inventive alloy offers a strength increase of about 100 MPa over Ti 6-4, with a comparable density and near equivalent ductility. The inventive alloy is particularly useful for a multitude of applications including components of aircraft engines. The Ti alloy comprises, in weight percent, about 6.0 to about 6.7% aluminum, about 1.4 to about 2.0% vanadium, about 1.4 to about 2.0% molybdenum, about 0.20 to about 0.42% silicon, about 0.17 to about 0.23% oxygen, maximum about 0.24% iron, maximum about 0.08% carbon and balance titanium with incidental impurities.
An alpha-beta Ti alloy having improved mechanical and ballistic properties formed using a low-cost composition is disclosed. In one embodiment, the Ti alloy composition, in weight percent, is 4.2 to 5.4 % aluminum, 2.5 to 3.5 % vanadium, 0.5 to 0.7 % iron, 0.15 to 0.19 % oxygen and balance titanium. The exemplary Ti alloy exhibits a tensile yield strength of at least about 120,000 psi and an ultimate tensile strength of at least about 128,000 psi in both longitudinal and transverse directions, a reduction in area of at least about 43 %, an elongation of at least about 12 % and about a 0.430-inch-thick plate has a V50 ballistic limit of about 1936 fps. The Ti alloy may be manufactured using a combination of recycled and/or virgin materials, thereby providing a low-cost route to the formation of high-quality armor plate for use in military systems.
An alpha-beta Ti alloy having improved mechanical and ballistic properties formed using a low-cost composition is disclosed. In one embodiment, the Ti alloy composition, in weight percent, is 4.2 to 5.4 % aluminum, 2.5 to 3.5 % vanadium, 0.5 to 0.7 % iron, 0.15 to 0.19 % oxygen and balance titanium. The exemplary Ti alloy exhibits a tensile yield strength of at least about 120,000 psi and an ultimate tensile strength of at least about 128,000 psi in both longitudinal and transverse directions, a reduction in area of at least about 43 %, an elongation of at least about 12 % and about a 0.430-inch-thick plate has a V50 ballistic limit of about 1936 fps. The Ti alloy may be manufactured using a combination of recycled and/or virgin materials, thereby providing a low-cost route to the formation of high-quality armor plate for use in military systems.
According to one embodiment of the invention, a method for preventing the failure of a system, which includes one or more pipes, or one or more cooling jackets, or one or more fluid cooled system components carrying a fluid, involves detecting one or more pressure levels of the fluid in the one or more pipes at one or more points, then comparing the detected pressure levels to a corresponding one or more predetermined limitation values. If the detected pressure levels exceed the corresponding limitation values, a shut-down signal is generated. The shut-down signal triggers the adjusting of one or more systems responsible for causing thermal variations of the fluid, preventing the system from failing while allowing the system to continue operation shortly thereafter.
A high strength near-beta titanium alloy including, in weight %, 5.3 to 5.7% aluminum, 4.8 to 5.2% vanadium, 0.7 to 0.9% iron, 4.6 to 5.3% molybdenum, 2.0 to 2.5% chromium, and 0.12 to 0.16% oxygen with balance titanium and incidental impurities is provided. An aviation system component comprising the high strength near-beta titanium alloy, and a method for the manufacture of a titanium alloy for use in high strength, deep hardenability, and excellent ductility applications are also provided.
A titanium alloy containing carbon with and without addition of silicon exhibiting improved corrosion resistance and mechanical strength as compared to commercially pure ASTM grade 2 titanium or PGM-alloyed ASTM grade 7 titanium.
A high strength near-beta titanium alloy including, in weight %, 5.3 to 5.7 % aluminum, 4.8 to 5.2 % vanadium, 0.7 to 0.9 % iron, 4.6 to 5.3 % molybdenum, 2.0 to 2.5 % chromium, and 0.12 to 0.16 % oxygen with balance titanium and inci-dental impurities is provided. An aviation system component comprising the high strength near-beta titanium alloy, and a method for the manufacture of a titanium alloy for use in high strength, deep hardenability, and excellent ductility applications are also provided.
A high strength near-beta titanium alloy including, in weight %, 5.3 to 5.7 % aluminum, 4.8 to 5.2 % vanadium, 0.7 to 0.9 % iron, 4.6 to 5.3 % molybdenum, 2.0 to 2.5 % chromium, and 0.12 to 0.16 % oxygen with balance titanium and incidental impurities is provided. An aviation system component comprising the high strength near-beta titanium alloy, and a method for the manufacture of a titanium alloy for use in high strength, deep hardenability, and excellent ductility applications are also provided.
Methods and associated apparatus for semi-continuous casting of hollow ingots are described. In one embodiment a method for the semi-continuous casting of a metallic hollow ingot is provided. The method includes providing a mold comprising a mold center having an inner pipe and an outer pipe arranged to form an annular space for a cooling media and an outer mold, circulating a cooling media in the annular space, feeding a source material to the mold, heating the source material to produce a molten material, moving the mold center progressively downward relative to the outer mold, and solidifying the molten material to form a hollow ingot. Embodiments relating to an apparatus for semi-continuous casting of hollow ingots, and products resulting from the semi-continuous casting of hollow ingots are also described.
Methods and associated apparatus for semi-continuous casting of hollow ingots are described. In one embodiment a method for the semi-continuous casting of a metallic hollow ingot is provided. The method includes providing a mold comprising a mold center having an inner pipe and an outer pipe arranged to form an annular space for a cooling media and an outer mold, circulating a cooling media in the annular space, feeding a source material to the mold, heating the source material to produce a molten material, moving the mold center progressively downward relative to the outer mold, and solidifying the molten material to form a hollow ingot. Embodiments relating to an apparatus for semi-continuous casting of hollow ingots, and products resulting from the semi-continuous casting of hollow ingots are also described.
Techniques for manufacturing sheet product of varying surface profile and products thus manufactured are disclosed herein. In some embodiments, the disclosed invention provides a method for profiling a surface of a sheet product (200) having a first profile on first surface. In one embodiment, the method includes creating a profiling template (220) or contoured support surface. A profiled surface may be formed by arranging the profiling template(220) and the sheet product (200) such that the profiling template is located between the sheet product and a support surface, conforming the arrangement of the sheet product and the profiling template to the support surface such that conformance causes the sheet product to have a second surface profile on the first surface, and processing the sheet product to form a third surface profile on the first surface.
B21D 31/00 - Autres procédés de travail des tôles, tubes ou profilés métalliques
B23P 25/00 - Traitement auxiliaire des pièces, avant ou pendant les opérations d'usinage, afin de faciliter l'action de l'outil ou d'obtenir pour les pièces l'état final désiré, p. ex. la réduction des contraintes internes
B23Q 3/08 - Moyens de fixation de la pièce autres que les moyens actionnés mécaniquement
B24B 13/00 - Machines ou dispositifs conçus pour meuler ou polir les surfaces optiques des lentilles ou les surfaces de forme similaire d'autres piècesAccessoires à cet effet
B25B 11/00 - Porte-pièces ou dispositifs de mise en position non couverts par l'un des groupes , p. ex. porte-pièces magnétiques, porte-pièces utilisant le vide
Techniques for manufacturing sheet product of varying surface profile and products thus manufactured are disclosed herein. In some embodiments, the disclosed invention provides a method for profiling a surface of a sheet product having a first profile on first surface. In one embodiment, the method includes creating a profiling template or contoured support surface. A profiled surface may be formed by arranging the profiling template and the sheet product such that the profiling template is located between the sheet product and a support surface, conforming the arrangement of the sheet product and the profiling template to the support surface such that conformance causes the sheet product to have a second surface profile on the first surface, and processing the sheet product to form a third surface profile on the first surface.
B24B 7/02 - Machines ou dispositifs pour meuler les surfaces planes des pièces, y compris ceux pour le polissage des surfaces planes en verreAccessoires à cet effet comportant une table porte-pièce se déplaçant suivant un mouvement de va-et-vient
According to one embodiment of the invention, a method for preventing the failure of a system, which includes one or more pipes, or one or more cooling jackets, or one or more fluid cooled system components carrying a fluid, involves detecting one or more pressure levels of the fluid in the one or more pipes at one or more points, then comparing the detected pressure levels to a corresponding one or more predetermined limitation values. If the detected pressure levels exceed the corresponding limitation values, a shut-down signal is generated. The shut-down signal triggers the adjusting of one or more systems responsible for causing thermal variations of the fluid, preventing the system from failing while allowing the system to continue operation shortly thereafter.
Methods for the manufacture of the above-mentioned titanium alloy for use in combustion engine exhaust systems are disclosed herein. An exemplary method of the disclosed subject matter for the manufacture of titanium alloy for use in a high temperature and high stress environment includes performing a first heat treatment of the titanium alloy at a first temperature, rolling the titanium alloy to a desired thickness, performing a second heat treatment of the titanium alloy at a second temperature, and performing a third heat treatment of the titanium alloy at a third temperature. In some embodiments, the first temperature is selected such that recrystallization and softening of the titanium alloy is optimized without substantial coarsening of second phase particles and can be approximately 1500-1600.degree. F. In some embodiments, the rolling of the titanium alloy reduces the thickness of the titanium alloy by at least than 65%.
Methods for the manufacture of the above-mentioned titanium alloy for use in combustion engine exhaust systems are disclosed herein. An exemplary method of the disclosed subject matter for the manufacture of titanium alloy for use in a high temperature and high stress environment includes performing a first heat treatment of the titanium alloy at a first temperature, rolling the titanium alloy to a desired thickness, performing a second heat treatment of the titanium alloy at a second temperature, and performing a third heat treatment of the titanium alloy at a third temperature. In some embodiments, the first temperature is selected such that recrystallization and softening of the titanium alloy is optimized without substantial coarsening of second phase particles and can be approximately 1500-1600° F. In some embodiments, the rolling of the titanium alloy reduces the thickness of the titanium alloy by at least than 65%.
Methods for the manufacture of the above-mentioned titanium alloy for use in combustion engine exhaust systems are disclosed herein. An exemplary method of the disclosed subject matter for the manufacture of titanium alloy for use in a high temperature and high stress environment includes performing a first heat treatment of the titanium alloy at a first temperature, rolling the titanium alloy to a desired thickness, performing a second heat treatment of the titanium alloy at a second temperature, and performing a third heat treatment of the titanium alloy at a third temperature. In some embodiments, the first temperature is selected such that recrystallization and softening of the titanium alloy is optimized without substantial coarsening of second phase particles and can be approximately 1500-1600° F. In some embodiments, the rolling of the titanium alloy reduces the thickness of the titanium alloy by at least than 65%.
A titanium alloy containing carbon with and without addition of silicon exhibiting improved corrosion resistance and mechanical strength as compared to commercially pure ASTM grade 2 titanium or PGM-alloyed ASTM grade 7 titanium.
According to one embodiment of the invention, a method for preventing the failure of a system, which includes one or more pipes, or one or more cooling jackets, or one or more fluid cooled system components carrying a fluid, involves detecting one or more pressure levels of the fluid in the one or more pipes at one or more points, then comparing the detected pressure levels to a corresponding one or more predetermined limitation values. If the detected pressure levels exceed the corresponding limitation values, a shut-down signal is generated. The shut-down signal triggers the adjusting of one or more systems responsible for causing thermal variations of the fluid, preventing the system from failing while allowing the system to continue operation shortly thereafter.
A titanium alloy containing carbon with and without addition of silicon exhibiting improved corrosion resistance and mechanical strength as compared to commercially pure ASTM grade 2 titanium or PGM-alloyed ASTM grade 7 titanium.
A titanium alloy containing carbon with and without addition of silicon exhibiting improved corrosion resistance and mechanical strength as compared to commercially pure ASTM grade 2 titanium or PGM-alloyed ASTM grade 7 titanium.
A titanium article having improved corrosion resistance resulting from a direct or indirect attachment of a platinum group metal or alloy thereof or incorporation of this metal or alloy thereof into a minor surface portion of the article.
