CN111455215A - Cavitation-corrosion-resistant titanium-aluminum-molybdenum alloy and preparation process thereof - Google Patents
Cavitation-corrosion-resistant titanium-aluminum-molybdenum alloy and preparation process thereof Download PDFInfo
- Publication number
- CN111455215A CN111455215A CN202010274933.5A CN202010274933A CN111455215A CN 111455215 A CN111455215 A CN 111455215A CN 202010274933 A CN202010274933 A CN 202010274933A CN 111455215 A CN111455215 A CN 111455215A
- Authority
- CN
- China
- Prior art keywords
- aluminum
- titanium
- weight
- parts
- molybdenum
- 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.)
- Granted
Links
Images
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
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention provides a cavitation erosion resistant titanium-aluminum-molybdenum alloy and a preparation process thereof. The reaction raw materials for forming the titanium-aluminum-molybdenum alloy comprise: 5.89 to 6 parts by weight of aluminum; 7.95 to 12.03 parts by weight of molybdenum; and 81.97 to 88 parts by weight of titanium sponge. The titanium-aluminum-molybdenum alloy has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and wide application prospect.
Description
Technical Field
The invention relates to the technical field of metallurgy, in particular to a cavitation erosion resistant titanium-aluminum-molybdenum alloy and a preparation process thereof.
Background
At present, titanium alloy has wide application in the fields of aerospace engineering, automation technology, marine chemical industry, petrochemical industry, nuclear industry, medical treatment and the like due to high thrust-weight ratio, excellent corrosion resistance, wide working temperature range, good corrosion resistance and good biocompatibility. Wherein, the TC4(Ti6Al4V) alloy accounts for more than half of the total amount of the titanium alloy. Particularly, in the petrochemical industry, the TC4 alloy is widely used for manufacturing flow-through equipment, but the flow-through equipment can cause serious damage to the equipment due to the ubiquitous cavitation phenomenon, and further the service life of the equipment is obviously shortened. Cavitation damage is caused by repeated impact of the microjets against the material surface due to collapse of bubbles on the solid wall surface. The microjets have been reported to have impact strengths of 1GPa to 5GPa, and velocities of up to about 700 m/s. Therefore, under these conditions, the titanium alloy surface is severely damaged, which limits the use of the TC4 alloy in flow components.
Therefore, the related art of the existing titanium alloy still needs to be improved.
Disclosure of Invention
The present invention is directed to solving, at least to some extent, one of the technical problems in the related art. Therefore, an object of the present invention is to provide a titanium-aluminum-molybdenum alloy with high elastic modulus, excellent cavitation erosion resistance, excellent electrochemical corrosion resistance, low noise level during cavitation erosion, or wide application prospects.
In one aspect of the invention, the invention provides a titanium aluminum molybdenum alloy. According to an embodiment of the invention, the reaction raw materials for forming the titanium-aluminum-molybdenum alloy comprise: 5.89 to 6 parts by weight of aluminum; 7.95 to 12.03 parts by weight of molybdenum; and 81.97 to 88 parts by weight of titanium sponge. The inventor finds that the titanium-aluminum-molybdenum alloy has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and wide application prospect.
According to an embodiment of the invention, the reaction feed comprises at least one of: 5.89 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.16 parts by weight of titanium sponge; 5.95 parts by weight of aluminum, 8.02 parts by weight of molybdenum and 86.03 parts by weight of titanium sponge; 5.93 parts by weight of aluminum, 7.98 parts by weight of molybdenum and 86.09 parts by weight of titanium sponge; 5.9 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.15 parts by weight of titanium sponge; 5.9 parts by weight of aluminum, 12.03 parts by weight of molybdenum and 82.07 parts by weight of titanium sponge; 5.95 parts by weight of aluminum, 11.9 parts by weight of molybdenum and 82.15 parts by weight of titanium sponge; 5.9 parts by weight of aluminum, 11.95 parts by weight of molybdenum and 82.15 parts by weight of titanium sponge; 5.98 parts by weight of aluminum, 11.96 parts by weight of molybdenum and 82.06 parts by weight of titanium sponge.
According to an embodiment of the invention, the titanium-aluminum-molybdenum alloy is formed by: mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block; under the vacuum condition, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block; carrying out second smelting treatment on the second prefabricated metal block under the vacuum condition to obtain a first prefabricated alloy ingot; carrying out first high-temperature treatment on the first prefabricated alloy ingot to obtain a second prefabricated alloy ingot; performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece; carrying out second high-temperature treatment on the first forging to obtain a third prefabricated alloy ingot; performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece; and annealing the second forging.
In another aspect of the invention, the invention provides a method of making the titanium aluminium molybdenum alloy described above. According to an embodiment of the invention, the method comprises: mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block; under the vacuum condition, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block; carrying out second smelting treatment on the second prefabricated metal block under the vacuum condition to obtain a first prefabricated alloy ingot; performing first high-temperature treatment on the first prefabricated alloy ingot for 1-3 hours at 1100-1200 ℃ to obtain a second prefabricated alloy ingot; performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece; performing second high-temperature treatment on the first forging for 0.5-1.5 h at the temperature of 900-930 ℃ to obtain a third prefabricated alloy ingot; performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece; and annealing the second forging to obtain the titanium-aluminum-molybdenum alloy. The inventor finds that the method is simple and convenient to operate, easy to implement and easy for industrial production, and the titanium-aluminum-molybdenum alloy can be effectively prepared.
According to an embodiment of the invention, the first smelting process satisfies at least one of the following conditions: the temperature is 1450-1750 ℃; the time is 3 to 4.5 hours; vacuum degree not greater than 10-2Pa。
According to an embodiment of the invention, the second smelting process satisfies at least one of the following conditions: the temperature is 1500 ℃ to 1800 ℃; the time is 3.5 to 5 hours; vacuum degree not greater than 10-2Pa。
According to the embodiment of the invention, the temperature of the annealing treatment is 650-750 ℃, and the time of the annealing treatment is 0.5-1.5 h.
According to an embodiment of the invention, the method comprises: mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block; under vacuum degree of not more than 10-2Under the condition of Pa, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block, wherein the temperature of the first smelting treatment is 1450-1750 ℃, and the time is 3-4.5 h; under vacuum degree of not more than 10-2Carrying out second smelting treatment on the second prefabricated metal block under the condition of Pa to obtain a first prefabricated alloy ingot, wherein the temperature of the second smelting treatment is 1500-1800 ℃ and the time is 3.5-5 h; performing first high-temperature treatment on the first prefabricated alloy ingot for 1-3 hours at 1100-1200 ℃ to obtain a second prefabricated alloy ingot; performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece; performing second high-temperature treatment on the first forging for 0.5-1.5 h at the temperature of 900-930 ℃ to obtain a third prefabricated alloy ingot; performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece; and annealing the second forging for 0.5-1.5 h at 650-750 ℃ to obtain the titanium-aluminum-molybdenum alloy.
In yet another aspect of the invention, the invention provides a titanium aluminum molybdenum alloy. According to an embodiment of the invention, the titanium-aluminum-molybdenum alloy is prepared by the method described above. The inventor finds that the titanium-aluminum-molybdenum alloy has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and wide application prospect.
In yet another aspect of the invention, a workpiece is provided. According to an embodiment of the invention, at least a portion of the workpiece is formed from the titanium aluminum molybdenum alloy described above or is prepared by the method described above. The inventor finds that the workpiece has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and long service life, and has all the characteristics and advantages of the titanium-aluminum-molybdenum alloy, and redundant description is omitted.
Drawings
FIG. 1 shows a schematic flow diagram of a method for preparing a titanium aluminum molybdenum alloy according to one embodiment of the invention.
FIG. 2 shows a schematic structural diagram of an ASTM G32-10 standard cavitation test apparatus as described in examples 1 and 2 of the present invention.
FIG. 3a shows the amount of cavitation loss in the sulfuric acid solution of 0.1 mol/L (bar 1 is the amount of cavitation loss in example 1; bar 3 is the amount of cavitation loss in comparative example 1) for different periods of cavitation erosion of the titanium-aluminum-molybdenum alloy of example 1 and the titanium alloy of comparative example 1 according to the present invention.
FIG. 3b shows the cavitation erosion resistance of the titanium-aluminum-molybdenum alloy of example 1 of the present invention and the titanium alloy of comparative example 1 in a 0.1 mol/L sulfuric acid solution for different periods of cavitation erosion (bar 1 is the cavitation erosion resistance of example 1; bar 3 is the cavitation erosion resistance of comparative example 1).
FIG. 4 shows SEM micrographs of the surfaces of a titanium-aluminum-molybdenum alloy of example 1 of the present invention and a titanium alloy of comparative example 1 after cavitation etching in a 0.1 mol/L sulfuric acid solution for various periods of time (a, b, c, and d are 30min, 60min, 120min, and 180min, respectively, for the titanium alloy of comparative example 1; e, f, g, and h are 30min, 60min, 120min, and 180min, respectively, for the titanium-aluminum-molybdenum alloy of example 1, wherein the scale bar has a length of 20 μm).
FIG. 5 shows the three-dimensional optical micro-topography of the surface of the titanium-aluminum-molybdenum alloy of example 1 of the present invention and the titanium alloy of comparative example 1 after cavitation etching in a 0.1 mol/L sulfuric acid solution for different times (a, b, c, and d are 30min, 60min, 120min, and 180min respectively for the titanium alloy of comparative example 1; e, f, g, and h are 30min, 60min, 120min, and 180min respectively for the titanium-aluminum-molybdenum alloy of example 1).
FIG. 6a shows the amount of cavitation loss in the sulfuric acid solution of 0.1 mol/L (bar 2 is the amount of cavitation loss in example 2; bar 3 is the amount of cavitation loss in comparative example 1) for different periods of cavitation erosion of the titanium-aluminum-molybdenum alloy of example 2 of the present invention and the titanium alloy of comparative example 1.
FIG. 6b shows the cavitation erosion resistance of the titanium-aluminum-molybdenum alloy of example 2 of the present invention and the titanium alloy of comparative example 1 in a 0.1 mol/L sulfuric acid solution for different periods of cavitation erosion (bar 2 is the cavitation erosion resistance of example 2; bar 3 is the cavitation erosion resistance of comparative example 1).
FIG. 7 shows SEM micrographs of the surfaces of a titanium-aluminum-molybdenum alloy of example 2 of the present invention and a titanium alloy of comparative example 1 after cavitation etching in a 0.1 mol/L sulfuric acid solution for various periods of time (a, b, c, and d are 30min, 60min, 120min, and 180min, respectively, for the titanium alloy of comparative example 1; e, f, g, and h are 30min, 60min, 120min, and 180min, respectively, for the titanium-aluminum-molybdenum alloy of example 2, wherein the scale bar has a length of 20 μm).
FIG. 8 shows the three-dimensional optical micro-topography of the surface of the titanium-aluminum-molybdenum alloy of example 2 of the present invention and the titanium alloy of comparative example 1 after cavitation etching in a 0.1 mol/L sulfuric acid solution for different times (a, b, c, and d are 30min, 60min, 120min, and 180min respectively for the titanium alloy of comparative example 1; e, f, g, and h are 30min, 60min, 120min, and 180min respectively for the titanium-aluminum-molybdenum alloy of example 2).
Reference numerals:
10: power supply 20: the thermostat device 30: test sample 40: the horn 50: test liquid
Detailed Description
In one aspect of the invention, the invention provides a titanium aluminum molybdenum alloy. According to an embodiment of the invention, the reaction raw materials for forming the titanium-aluminum-molybdenum alloy comprise: 5.89 to 6 parts by weight of aluminum; 7.95 to 12.03 parts by weight of molybdenum; and 81.97 to 88 parts by weight of titanium sponge. The inventor finds that the titanium-aluminum-molybdenum alloy has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and wide application prospect.
Specifically, in some specific embodiments of the present invention, the reaction raw materials may specifically include: 5.89 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.16 parts by weight of titanium sponge; 5.95 parts by weight of aluminum, 8.02 parts by weight of molybdenum and 86.03 parts by weight of titanium sponge; 5.93 parts by weight of aluminum, 7.98 parts by weight of molybdenum and 86.09 parts by weight of titanium sponge; 5.9 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.15 parts by weight of titanium sponge; 5.9 parts by weight of aluminum, 12.03 parts by weight of molybdenum and 82.07 parts by weight of titanium sponge; 5.95 parts by weight of aluminum, 11.9 parts by weight of molybdenum and 82.15 parts by weight of titanium sponge; 5.9 parts by weight of aluminum, 11.95 parts by weight of molybdenum and 82.15 parts by weight of titanium sponge or 5.98 parts by weight of aluminum, 11.96 parts by weight of molybdenum and 82.06 parts by weight of titanium sponge. After a great deal of thorough investigation and experimental verification, the inventor finds that when the reaction raw material for forming the titanium-aluminum-molybdenum alloy is any one of the above materials, the elastic modulus of the formed titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, the noise level in the cavitation erosion process is further reduced, and the application prospect is wider.
According to an embodiment of the present invention, further, the titanium aluminum molybdenum alloy is formed by: mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block; under the vacuum condition, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block; carrying out second smelting treatment on the second prefabricated metal block under the vacuum condition to obtain a first prefabricated alloy ingot; carrying out first high-temperature treatment on the first prefabricated alloy ingot to obtain a second prefabricated alloy ingot; performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece; carrying out second high-temperature treatment on the first forging to obtain a third prefabricated alloy ingot; performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece; and annealing the second forging. Therefore, the method for forming the titanium-aluminum-molybdenum alloy is simple and convenient to operate, easy to realize, easy for industrial production and capable of effectively preparing the titanium-aluminum-molybdenum alloy; meanwhile, the elastic modulus of the prepared titanium-aluminum-molybdenum alloy is further improved, the prepared titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, the noise level in the cavitation erosion process is further lowered, and the application prospect is wider.
In another aspect of the invention, the invention provides a method of making the titanium aluminium molybdenum alloy described above. According to an embodiment of the invention, referring to fig. 1, the method comprises the steps of:
s100: and mixing the reaction raw materials and then carrying out pressing treatment to obtain a first prefabricated metal block.
According to the embodiment of the present invention, the specific types, ratios, etc. of the reaction raw materials are the same as those described above, and therefore, redundant description is not repeated here.
According to the embodiment of the present invention, the specific manner of performing the pressing treatment after mixing the reaction raw materials is not particularly limited, and those skilled in the art can flexibly select the reaction raw materials according to actual needs, which is not described herein in detail.
According to the embodiments of the present invention, the specific shape of the obtained first prefabricated metal block is not particularly limited, for example, in some embodiments of the present invention, the first prefabricated metal block may be a cubic block or a circular block, and those skilled in the art can understand that the shape of the first prefabricated metal block may be flexibly selected according to the use requirement of the subsequent titanium-aluminum-molybdenum alloy, and therefore, redundant description is not repeated herein.
S200: and carrying out first smelting treatment on the first prefabricated metal block under the vacuum condition to obtain a second prefabricated metal block.
According to an embodiment of the present invention, further, the temperature of the first melting process may be 1450 ℃ to 1750 ℃. Specifically, in some embodiments of the present invention, the temperature of the first melting process may be specifically 1450 ℃, 1500 ℃, 1550 ℃, 1600 ℃, 1650 ℃, 1700 ℃, 1750 ℃ and the like. Therefore, the first smelting treatment temperature is proper, the first prefabricated metal block can be fully smelted to form a second prefabricated metal block, the formed second prefabricated metal block has a better micro-morphology and is matched with the reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of the components, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered.
According to the embodiment of the invention, the time of the first smelting treatment is 3-4.5 h. Specifically, in some embodiments of the present invention, the time of the first smelting process may be specifically 3h, 3.5h, 4h, 4.5h, and the like. Therefore, the first smelting treatment time is proper, the first prefabricated metal block can be fully smelted to form a second prefabricated metal block, the formed second prefabricated metal block has a better micro-morphology and is matched with the above reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of the components, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered; meanwhile, the first smelting treatment time is not too long, so that the production efficiency is high, and industrialization is easy to realize.
According to the embodiment of the invention, further, the vacuum degree of the reaction system is not more than 10 when the first smelting treatment is carried out-2Pa. Therefore, in the process of the first smelting treatment, the vacuum degree of the reaction system is low, so that other impurities are not easily introduced in the whole reaction process, the formed second prefabricated metal block has a better micro-morphology, the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered.
According to the embodiment of the present invention, further, the first melting treatment may be specifically performed in a vacuum consumable electrode furnace, and the specific model, manufacturer, and the like of the vacuum consumable electrode furnace are not particularly limited as long as the first melting treatment can be performed well, and the specific model thereof can be flexibly selected by a person skilled in the art as needed, and will not be described in detail herein. This makes it possible to provide the first melting treatment with a low degree of vacuum as described above.
S300: and carrying out second smelting treatment on the second prefabricated metal block under the vacuum condition to obtain a first prefabricated alloy ingot.
According to an embodiment of the present invention, further, the temperature of the second melting process may be 1500 to 1800 ℃. Specifically, in some embodiments of the present invention, the temperature of the second melting process may be specifically 1500 ℃, 1550 ℃, 1600 ℃, 1650 ℃, 1700 ℃, 1750 ℃, 1800 ℃ and the like. Therefore, the second smelting treatment temperature is proper, the second prefabricated metal block can be fully smelted to form the first prefabricated alloy ingot, the formed first prefabricated alloy ingot has a better micro-morphology and is matched with the above reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of the components, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered.
According to the embodiment of the invention, the time of the second smelting treatment is 3.5-5 h. Specifically, in some embodiments of the present invention, the time of the second melting process may be specifically 3.5h, 4h, 4.5h, 5h, and the like. Therefore, the second smelting treatment time is proper, the second prefabricated metal block can be fully smelted to form a first prefabricated alloy ingot, the formed first prefabricated alloy ingot has a better micro-morphology and is matched with the above reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of the components, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered; meanwhile, the first smelting treatment time is not too long, so that the production efficiency is high, and industrialization is easy to realize.
According to the embodiment of the invention, further, the vacuum degree of the reaction system is not more than 10 when the second smelting treatment is carried out-2Pa. Therefore, in the process of the second smelting treatment, the vacuum degree of the reaction system is low, so that other impurities are not easily introduced in the whole reaction process, the formed first prefabricated alloy ingot has a better micro-morphology, the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered.
According to the embodiment of the present invention, further, the second melting treatment may be specifically performed in a vacuum consumable electrode furnace, and the specific model, manufacturer, and the like of the vacuum consumable electrode furnace are not particularly limited as long as the second melting treatment can be performed well, and the specific model thereof can be flexibly selected by a person skilled in the art as needed, and will not be described in detail herein. This makes it possible to provide the second melting process with a low degree of vacuum as described above.
According to embodiments of the present invention, the size of the first pre-alloy ingot is not particularly limited, and in some embodiments of the present invention, the diameter of the first pre-alloy ingot may be 100mm to 140mm, and specifically, may be 100mm, 110mm, 120mm, 130mm, 140mm, or the like. Therefore, the first prefabricated alloy ingot is proper in size, the titanium-aluminum-molybdenum alloy is favorably prepared in the subsequent steps, and the subsequent application is favorably realized.
S400: and carrying out first high-temperature treatment on the first prefabricated alloy ingot for 1-3 h at the temperature of 1100-1200 ℃ to obtain a second prefabricated alloy ingot.
According to an embodiment of the present invention, further, the temperature of the first high temperature treatment may be 1100 ℃, 1120 ℃, 1140 ℃, 1160 ℃, 1180 ℃, 1200 ℃, or the like. Therefore, the first high-temperature treatment temperature is proper, the first pre-cast alloy ingot can be fully subjected to high-temperature treatment to form a second pre-cast alloy ingot, the formed second pre-cast alloy ingot has a better micro-morphology and is matched with the reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of the components, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered.
According to the embodiment of the present invention, further, the time of the first high temperature treatment may be specifically 1h, 2h, 3h, or the like. Therefore, the first high-temperature treatment time is proper, the first prefabricated alloy ingot can be sufficiently subjected to high-temperature treatment to form a second prefabricated alloy ingot, the formed second prefabricated alloy ingot has a better micro-morphology and is matched with the reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of each component, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered; meanwhile, the time of the first high-temperature treatment is not too long, so that the production efficiency is high, and the industrialization is easy to realize.
S500: and carrying out first forging treatment on the second prefabricated alloy ingot to obtain a first forging.
According to an embodiment of the present invention, specifically, the first forging process may be performed using a 1-3 ton air hammer, and specifically, the air hammer may be 1 ton, 2 ton, 3 ton, or the like. Thus, the first forged part can be obtained more effectively and easily.
According to an embodiment of the present invention, specifically, the size of the first forging is not particularly limited, and in some embodiments of the present invention, the diameter of the first forging may be 80mm to 120mm, specifically, 80mm, 90mm, 100mm, 110mm, or 120mm, and the like. Therefore, the first forging piece is proper in size, the titanium-aluminum-molybdenum alloy is favorably prepared in the subsequent steps, and the subsequent application is favorably realized.
According to the embodiment of the invention, after the first forging treatment is carried out to obtain the first forging, the method can further comprise the steps of carrying out air cooling treatment on the first forging, then checking whether cracks exist on the surface of the first forging, and if cracks exist on the surface of the first forging, polishing the surface of the first forging. Therefore, the obtained first forging piece has a good microstructure, and is beneficial to subsequent preparation of titanium-aluminum-molybdenum alloy and subsequent application.
S600: and carrying out second high-temperature treatment on the first forging for 0.5-1.5 h at the temperature of 900-930 ℃ to obtain a third prefabricated alloy ingot.
According to an embodiment of the present invention, further, the temperature of the second high temperature treatment may be 900 ℃, 910 ℃, 920 ℃, 930 ℃, or the like. Therefore, the temperature of the second high-temperature treatment is proper, the first forging piece can be fully subjected to the high-temperature treatment to form a third prefabricated alloy ingot, the formed third prefabricated alloy ingot has a better micro-appearance and is matched with the reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of the components, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered.
According to the embodiment of the present invention, further, the time of the second high temperature treatment may be specifically 0.5h, 1h, 1.5h, or the like. Therefore, the second high-temperature treatment time is proper, the first forging piece can be fully subjected to high-temperature treatment to form a third prefabricated alloy ingot, the formed third prefabricated alloy ingot has a better micro-morphology and is matched with the reaction raw materials for forming the titanium-aluminum-molybdenum alloy, namely the proportion of each component, so that the elastic modulus of the finally prepared titanium-aluminum-molybdenum alloy is further improved, the titanium-aluminum-molybdenum alloy has more excellent cavitation erosion resistance and more excellent electrochemical corrosion resistance, and the noise level in the cavitation erosion process is further lowered; meanwhile, the time of the first high-temperature treatment is not too long, so that the production efficiency is high, and the industrialization is easy to realize.
S700: and carrying out second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece.
According to an embodiment of the present invention, specifically, a specific manner of the second forging process is the same as that of the first forging process, and will not be described in detail herein.
According to embodiments of the present invention, the specific shape, size, etc. of the second forging is not particularly limited, and in some embodiments of the present invention, the diameter of the second forging may be 20mm to 40mm, specifically, 20mm, 30mm, 40mm, etc. Therefore, the size of the second forging piece is proper, the titanium-aluminum-molybdenum alloy is favorably prepared in the subsequent steps, and the subsequent application is favorably realized.
S800: and annealing the second forging to obtain the titanium-aluminum-molybdenum alloy.
Further, according to an embodiment of the present invention, the temperature of the annealing treatment may be 650 ℃ to 750 ℃. Specifically, in some embodiments of the present invention, the temperature of the annealing treatment may be specifically 650 ℃, 700 ℃, or 750 ℃, and the like. Thus, the internal stress generated by the first forging and the second forging can be eliminated, and the titanium-aluminum-molybdenum alloy with more excellent performance can be obtained.
According to the embodiment of the invention, the time of the annealing treatment is 0.5 h-1.5 h. Specifically, in some embodiments of the present invention, the time of the annealing treatment may be specifically 0.5h, 1h, 1.5h, or the like. Thus, the internal stress generated by the first forging and the second forging can be eliminated, and the titanium-aluminum-molybdenum alloy with more excellent performance can be obtained.
In yet another aspect of the invention, the invention provides a titanium aluminum molybdenum alloy. According to an embodiment of the invention, the titanium-aluminum-molybdenum alloy is prepared by the method described above. The inventor finds that the titanium-aluminum-molybdenum alloy has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and wide application prospect.
In yet another aspect of the invention, a workpiece is provided. According to an embodiment of the invention, at least a portion of the workpiece is formed from the titanium aluminum molybdenum alloy described above or is prepared by the method described above. The inventor finds that the workpiece has high elastic modulus, excellent cavitation erosion resistance and electrochemical corrosion resistance, low noise level in the cavitation erosion process and long service life, and has all the characteristics and advantages of the titanium-aluminum-molybdenum alloy, and redundant description is omitted.
According to embodiments of the present invention, the specific type of the workpiece is not particularly limited, for example, in some embodiments of the present invention, the workpiece may be a workpiece on an overcurrent device, which has excellent cavitation erosion resistance, such that the service life of the workpiece is significantly increased and the service performance of the workpiece is better.
The following describes embodiments of the present invention in detail. The following examples are illustrative only and are not to be construed as limiting the invention. The examples, where specific techniques or conditions are not indicated, are to be construed according to the techniques or conditions described in the literature in the art or according to the product specifications. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products commercially available.
Example 1
Method for preparing titanium-aluminum-molybdenum alloy
Firstly, 5.89 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.16 parts by weight of sponge titanium are mixed and pressed into round blocks with the diameter of 80mm, then the pressed round blocks are smelted in a vacuum consumable furnace for 2 times (the first smelting temperature is 1600 ℃, the time is 4 hours, the second smelting temperature is 1650 ℃, the time is 4.25 hours), and the vacuum degree is kept at 10 during smelting-2Pa or less, and finally obtaining a first pre-alloy ingot with the diameter of 120 mm. Heating the obtained first precast alloy ingot to 1150 ℃ in an electric furnace, preserving heat for 2 hours, then carrying out first cogging forging treatment, forging the first precast alloy ingot into a blank with the diameter of about 100mm square, air-cooling, then checking the surface quality of the square blank, and if cracks exist, polishing treatment is needed, so that the forging cracks are completely eliminated. Then the forging is atHeating to 915 deg.C in electric furnace, keeping the temperature for 1 hr, forging into round bar with diameter of about 30mm, and air cooling. And finally, placing the round rod with the diameter of 30mm in an electric furnace, and annealing for 1 hour at 700 ℃ to finally obtain the titanium-aluminum-molybdenum alloy with excellent cavitation erosion resistance.
The cavitation erosion resistance of the titanium-aluminum-molybdenum alloy prepared according to the present example in a 0.1 mol/L sulfuric acid solution is verified according to a standard cavitation erosion test (standard ultrasonic cavitation test) of ASTM G32-10, and the results are shown below, fig. 2 shows a schematic diagram of a standard cavitation erosion test apparatus of ASTM G32-10, wherein the distance d between a horn 40 and a test sample 30 is 0.5mm, a column 1 in fig. 3a shows the cavitation erosion weight loss of the titanium-aluminum-molybdenum alloy prepared according to the present example in a 0.1 mol/L sulfuric acid solution at different times, and fig. 3b shows the corresponding cavitation erosion resistance in fig. 3a, it can be seen that the cavitation erosion weight loss amount corresponding to each cavitation erosion time is much less than that of a column 3 (experimental data of comparative example 1), which shows that the titanium-aluminum-molybdenum-aluminum-alloy cavitation erosion resistance of the titanium-aluminum-molybdenum-aluminum-molybdenum alloy of example 1 is much better than that of the titanium-aluminum-molybdenum-aluminum-molybdenum-alloy-aluminum-molybdenum-aluminum-molybdenum-alloy-aluminum-molybdenum-titanium-aluminum-molybdenum-titanium-molybdenum-titanium-aluminum-molybdenum-alloy-titanium-molybdenum alloy-titanium-aluminum-molybdenum alloy-titanium-aluminum-titanium-molybdenum alloy-titanium-molybdenum alloy-titanium-molybdenum alloy-titanium-aluminum-titanium-molybdenum alloy, and-molybdenum-titanium-molybdenum-titanium-molybdenum-titanium-aluminum-titanium-aluminum-molybdenum alloy-titanium-molybdenum alloy-molybdenum.
Example 2
Method for preparing titanium-aluminum-molybdenum alloy
Firstly, 5.9 parts by weight of aluminum, 12.03 parts by weight of molybdenum and 82.07 parts by weight of sponge titanium are mixed and pressed into a round rod with the diameter of 80mm, then the pressed round rod is smelted in a vacuum consumable electrode furnace for 2 times (the first smelting temperature is 1600 ℃ for 4 hours, the second smelting temperature is 1650 ℃ for 4.25 hours), and finally a first prefabricated alloy ingot with the diameter of 120mm is obtained. Heating the obtained first precast alloy ingot to 1150 ℃ in an electric furnace, preserving heat for 2 hours, then carrying out first cogging forging treatment, forging the first precast alloy ingot into a blank with the diameter of about 100mm square, air-cooling, then checking the surface quality of the square blank, and if cracks exist, polishing treatment is needed, so that the forging cracks are completely eliminated. And then heating the forge piece to 915 ℃ in an electric furnace, preserving heat for 1 hour, then forging for the second time to obtain a round rod with the diameter of about 30mm, and cooling in air. And finally, placing the round rod with the diameter of 30mm in an electric furnace, and annealing for 1 hour at 700 ℃ to finally obtain the titanium-aluminum-molybdenum alloy with excellent cavitation erosion resistance.
The cavitation erosion resistance of the titanium-aluminum-molybdenum alloy prepared according to the present example in a 0.1 mol/L sulfuric acid solution is verified according to a standard cavitation erosion test (standard ultrasonic cavitation test) of ASTM G32-10, and the results are shown below, fig. 2 shows a schematic diagram of a standard cavitation erosion test apparatus of ASTM G32-10, wherein the distance d between a horn 40 and a test sample 30 is 0.5mm, a column 2 in fig. 6a shows the cavitation erosion weight loss of the titanium-aluminum-molybdenum alloy prepared according to the present example in a 0.1 mol/L sulfuric acid solution at different times, and fig. 6b shows the corresponding cavitation erosion resistance in fig. 6a, it can be seen that the cavitation erosion weight loss amount corresponding to each cavitation erosion time is much less than that of a column 3 (experimental data of comparative example 1), which shows that the titanium-aluminum-molybdenum-aluminum-alloy cavitation erosion resistance of the titanium-aluminum-molybdenum-aluminum-molybdenum alloy of example 2 is much better than that of the titanium-aluminum-molybdenum-alloy-aluminum-alloy-molybdenum-aluminum-molybdenum-alloy-aluminum-molybdenum-aluminum-molybdenum-alloy-aluminum-molybdenum-aluminum-molybdenum-titanium-molybdenum-aluminum-molybdenum-titanium-molybdenum-titanium-alloy-titanium-aluminum-molybdenum alloy-titanium-molybdenum alloy-titanium-molybdenum alloy-aluminum-titanium-molybdenum alloy-titanium-molybdenum alloy-titanium-molybdenum alloy-titanium-aluminum-molybdenum alloy-titanium-molybdenum alloy-titanium-aluminum-titanium-molybdenum alloy, and-titanium-molybdenum alloy.
Table 1 roughness test results in X, Y, Z three directions for alloys in example 1, example 2 and comparative example 1
Therefore, the titanium-aluminum-molybdenum alloy disclosed by the invention is high in elastic modulus, excellent in cavitation erosion resistance and electrochemical corrosion resistance, low in noise level in the cavitation erosion process and wide in application prospect.
Example 3
The only difference from example 1 is: the reaction raw materials for forming the titanium-aluminum-molybdenum alloy include 5.95 parts by weight of aluminum, 8.02 parts by weight of molybdenum, and 86.03 parts by weight of titanium sponge.
The titanium-aluminum-molybdenum alloy obtained in example 3 was subjected to a cavitation erosion resistance test, and the test results were similar to those in example 1.
Example 4
The only difference from example 1 is: the reaction raw materials for forming the titanium-aluminum-molybdenum alloy include 5.93 parts by weight of aluminum, 7.98 parts by weight of molybdenum, and 86.09 parts by weight of titanium sponge.
The titanium-aluminum-molybdenum alloy obtained in example 4 was subjected to a cavitation erosion resistance test, and the test results were similar to those in example 1.
Example 5
The only difference from example 1 is: the reaction raw materials for forming the titanium-aluminum-molybdenum alloy include 5.9 parts by weight of aluminum, 7.95 parts by weight of molybdenum, and 86.15 parts by weight of titanium sponge.
The titanium-aluminum-molybdenum alloy obtained in example 5 was subjected to a cavitation erosion resistance test, and the test results were similar to those in example 1.
Example 6
The only difference from example 2 is: the reaction raw materials for forming the titanium-aluminum-molybdenum alloy include 5.95 parts by weight of aluminum, 11.9 parts by weight of molybdenum, and 82.15 parts by weight of titanium sponge.
The titanium-aluminum-molybdenum alloy obtained in example 6 was subjected to a cavitation erosion resistance test, and the test results were similar to those in example 2.
Example 7
The only difference from example 2 is: the reaction raw materials for forming the titanium-aluminum-molybdenum alloy include 5.9 parts by weight of aluminum, 11.95 parts by weight of molybdenum, and 82.15 parts by weight of titanium sponge.
The titanium-aluminum-molybdenum alloy obtained in example 7 was subjected to a cavitation erosion resistance test, and the test results were similar to those in example 2.
Example 8
The only difference from example 2 is: the reaction raw materials for forming the titanium-aluminum-molybdenum alloy include 5.98 parts by weight of aluminum, 11.96 parts by weight of molybdenum, and 82.06 parts by weight of titanium sponge.
The titanium-aluminum-molybdenum alloy obtained in example 8 was subjected to a cavitation erosion resistance test, and the test results were similar to those in example 2.
Comparative example 1
TC4 alloy in the related art.
The TC4 alloy of comparative example 1 was tested for cavitation erosion resistance, as previously described.
In the description of the present invention, it is to be understood that the terms "first", "second" and the like are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implying any number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of the present invention, "a plurality" means two or more unless specifically defined otherwise.
In the description herein, references to the description of the term "one embodiment," "some embodiments," "an example," "a specific example," or "some examples," etc., mean that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the invention. In this specification, the schematic representations of the terms used above are not necessarily intended to refer to the same embodiment or example. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples. Furthermore, various embodiments or examples and features of different embodiments or examples described in this specification can be combined and combined by one skilled in the art without contradiction.
Although embodiments of the present invention have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present invention, and that variations, modifications, substitutions and alterations can be made to the above embodiments by those of ordinary skill in the art within the scope of the present invention.
Claims (10)
1. A titanium aluminum molybdenum alloy, wherein the reaction feed materials for forming the titanium aluminum molybdenum alloy comprise:
5.89 to 6 parts by weight of aluminum;
7.95 to 12.03 parts by weight of molybdenum; and
81.97 to 88 parts by weight of titanium sponge.
2. The titanium aluminum molybdenum alloy of claim 1, wherein the reaction feed material comprises at least one of:
5.89 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.16 parts by weight of titanium sponge;
5.95 parts by weight of aluminum, 8.02 parts by weight of molybdenum and 86.03 parts by weight of titanium sponge;
5.93 parts by weight of aluminum, 7.98 parts by weight of molybdenum and 86.09 parts by weight of titanium sponge;
5.9 parts by weight of aluminum, 7.95 parts by weight of molybdenum and 86.15 parts by weight of titanium sponge;
5.9 parts by weight of aluminum, 12.03 parts by weight of molybdenum and 82.07 parts by weight of titanium sponge;
5.95 parts by weight of aluminum, 11.9 parts by weight of molybdenum and 82.15 parts by weight of titanium sponge;
5.9 parts by weight of aluminum, 11.95 parts by weight of molybdenum and 82.15 parts by weight of titanium sponge;
5.98 parts by weight of aluminum, 11.96 parts by weight of molybdenum and 82.06 parts by weight of titanium sponge.
3. The titanium aluminum molybdenum alloy of claim 1, wherein the titanium aluminum molybdenum alloy is formed by:
mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block;
under the vacuum condition, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block;
carrying out second smelting treatment on the second prefabricated metal block under the vacuum condition to obtain a first prefabricated alloy ingot;
carrying out first high-temperature treatment on the first prefabricated alloy ingot to obtain a second prefabricated alloy ingot;
performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece;
carrying out second high-temperature treatment on the first forging to obtain a third prefabricated alloy ingot;
performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece;
and annealing the second forging.
4. A method of making the titanium aluminium molybdenum alloy of any one of claims 1 to 3, comprising:
mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block;
under the vacuum condition, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block;
carrying out second smelting treatment on the second prefabricated metal block under the vacuum condition to obtain a first prefabricated alloy ingot;
performing first high-temperature treatment on the first prefabricated alloy ingot for 1-3 hours at 1100-1200 ℃ to obtain a second prefabricated alloy ingot;
performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece;
performing second high-temperature treatment on the first forging for 0.5-1.5 h at the temperature of 900-930 ℃ to obtain a third prefabricated alloy ingot;
performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece;
and annealing the second forging to obtain the titanium-aluminum-molybdenum alloy.
5. The method of claim 4, wherein the first smelting process satisfies at least one of the following conditions:
the temperature is 1450-1750 ℃;
the time is 3 to 4.5 hours;
vacuum degree not greater than 10-2Pa。
6. The method defined in claim 4 or claim 5 wherein the second smelting process meets at least one of the following conditions:
the temperature is 1500-1800 ℃;
the time is 3.5 to 5 hours;
vacuum degree not greater than 10-2Pa。
7. The method according to claim 4, wherein the temperature of the annealing treatment is 650 ℃ to 750 ℃, and the time of the annealing treatment is 0.5h to 1.5 h.
8. The method of claim 4, comprising:
mixing the reaction raw materials and then performing pressing treatment to obtain a first prefabricated metal block;
under vacuum degree of not more than 10-2Under the condition of Pa, carrying out first smelting treatment on the first prefabricated metal block to obtain a second prefabricated metal block, wherein the temperature of the first smelting treatment is 1450-1750 ℃, and the time is 3-4.5 h;
under vacuum degree of not more than 10-2Carrying out second smelting treatment on the second prefabricated metal block under the condition of Pa to obtain a first prefabricated alloy ingot, wherein the temperature of the second smelting treatment is 1500-1800 ℃ and the time is 3.5-5 h;
performing first high-temperature treatment on the first prefabricated alloy ingot for 1-3 hours at 1100-1200 ℃ to obtain a second prefabricated alloy ingot;
performing first forging treatment on the second prefabricated alloy ingot to obtain a first forging piece;
performing second high-temperature treatment on the first forging for 0.5-1.5 h at the temperature of 900-930 ℃ to obtain a third prefabricated alloy ingot;
performing second forging treatment on the third prefabricated alloy ingot to obtain a second forging piece;
and annealing the second forging for 0.5-1.5 h at 650-750 ℃ to obtain the titanium-aluminum-molybdenum alloy.
9. A titanium aluminium molybdenum alloy, characterized in that it is prepared by a process according to any one of claims 4 to 8.
10. A workpiece, wherein at least a portion of the workpiece is formed from the titanium aluminium molybdenum alloy of any one of claims 1 to 3 or 9, or is prepared by the process of any one of claims 4 to 8.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010274933.5A CN111455215B (en) | 2020-04-09 | 2020-04-09 | Cavitation-corrosion-resistant titanium-aluminum-molybdenum alloy and preparation process thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010274933.5A CN111455215B (en) | 2020-04-09 | 2020-04-09 | Cavitation-corrosion-resistant titanium-aluminum-molybdenum alloy and preparation process thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111455215A true CN111455215A (en) | 2020-07-28 |
| CN111455215B CN111455215B (en) | 2021-06-22 |
Family
ID=71678463
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010274933.5A Active CN111455215B (en) | 2020-04-09 | 2020-04-09 | Cavitation-corrosion-resistant titanium-aluminum-molybdenum alloy and preparation process thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111455215B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111321318A (en) * | 2018-12-14 | 2020-06-23 | 上海纳微涂层有限公司 | Cavitation-resistant titanium alloy and preparation process thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1665948A (en) * | 2002-06-27 | 2005-09-07 | 梅莫瑞公司 | Beta titanium compositions and methods of manufacture thereof |
| CN201634746U (en) * | 2009-10-30 | 2010-11-17 | 大连海事大学 | Titanium alloy member with cavitation erosion resistant surface |
| CN103498072A (en) * | 2013-09-03 | 2014-01-08 | 中国船舶重工集团公司第七二五研究所 | High-strength high-impact-toughness titanium alloy used for oil well and gas well, and preparation method thereof |
| CN107746990A (en) * | 2017-09-27 | 2018-03-02 | 西安交通大学 | A kind of High-strength high-plasticity Ti Al Zr Mo V system's beta-titanium alloys and its Technology for Heating Processing |
| EP2971200B1 (en) * | 2013-03-15 | 2018-04-11 | ATI Properties LLC | Thermomechanical processing of alpha-beta titanium alloys |
-
2020
- 2020-04-09 CN CN202010274933.5A patent/CN111455215B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1665948A (en) * | 2002-06-27 | 2005-09-07 | 梅莫瑞公司 | Beta titanium compositions and methods of manufacture thereof |
| CN201634746U (en) * | 2009-10-30 | 2010-11-17 | 大连海事大学 | Titanium alloy member with cavitation erosion resistant surface |
| EP2971200B1 (en) * | 2013-03-15 | 2018-04-11 | ATI Properties LLC | Thermomechanical processing of alpha-beta titanium alloys |
| CN103498072A (en) * | 2013-09-03 | 2014-01-08 | 中国船舶重工集团公司第七二五研究所 | High-strength high-impact-toughness titanium alloy used for oil well and gas well, and preparation method thereof |
| CN107746990A (en) * | 2017-09-27 | 2018-03-02 | 西安交通大学 | A kind of High-strength high-plasticity Ti Al Zr Mo V system's beta-titanium alloys and its Technology for Heating Processing |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111321318A (en) * | 2018-12-14 | 2020-06-23 | 上海纳微涂层有限公司 | Cavitation-resistant titanium alloy and preparation process thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111455215B (en) | 2021-06-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101927312B (en) | Method for processing TC4 titanium alloy into forged rings | |
| US3356542A (en) | Cobalt-nickel base alloys containing chromium and molybdenum | |
| CN104498849B (en) | A kind of preparation technology of Ti662 titanium alloy pipe | |
| CN101886232B (en) | Amorphous alloy-based composite material and preparation method thereof | |
| US9994946B2 (en) | High strength, homogeneous copper-nickel-tin alloy and production process | |
| CN111455215B (en) | Cavitation-corrosion-resistant titanium-aluminum-molybdenum alloy and preparation process thereof | |
| JP2017503086A (en) | Aluminum casting alloy with improved high temperature performance | |
| JP5385038B2 (en) | Titanium plate with high yield strength and excellent press formability | |
| CN102560268A (en) | Ultra-low carbon high strength stainless steel thin pipe and manufacturing method thereof | |
| CN101503771B (en) | High strength and high full hardening titanium alloy | |
| CN105202275A (en) | Titanium alloy TC4 hot-rolled pipe and preparation method thereof | |
| CN112359302B (en) | Method for homogenizing nickel-based superalloy flat steel structure | |
| CN111961919A (en) | Nickel-copper alloy bar for ship and processing method thereof | |
| CN105765092A (en) | Method for processing dispersion-hardened platinum composition | |
| CN111394613B (en) | Anti-cavitation titanium-aluminum-zirconium alloy and preparation process thereof | |
| CN112626431B (en) | Preparation method of prestressed bolt for medical ultrasonic transducer | |
| CN114934246A (en) | Entropy-regulated CoCrFeNi-series flexible micron fiber and preparation method thereof | |
| CN113106273A (en) | Production process of TA7 wire for special purpose | |
| CN111155021B (en) | High-temperature alloy ingot blank, preparation method thereof and high-temperature alloy part | |
| CN110116211A (en) | A kind of heat treatment method of selective laser melting AlSi10Mg alloy product | |
| US20070169856A1 (en) | Method for making a hybrid casting and forging stainless steel product | |
| CN117862388A (en) | Forging process of deep-sea thin-wall sealing ring Inconel 718 nickel-based alloy forging | |
| CN114434102B (en) | Double titanium metal ring and preparation method thereof | |
| CN109371283B (en) | High-strength high-toughness Ti5Mo5V5Cr3Al titanium alloy and preparation method thereof | |
| Dong et al. | High-temperature deformation resistance and creep resistance of a TiAl-based alloy fabricated by cold crucible directional solidification technology |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |