CN117107112B - Short-medium-time high-temperature titanium alloy and preparation method thereof - Google Patents
Short-medium-time high-temperature titanium alloy and preparation method thereof Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 101
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 238000005266 casting Methods 0.000 claims abstract description 27
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 17
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 15
- 239000011733 molybdenum Substances 0.000 claims abstract description 15
- 230000032683 aging Effects 0.000 claims abstract description 12
- 239000010936 titanium Substances 0.000 claims abstract description 12
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 12
- 238000002844 melting Methods 0.000 claims abstract description 11
- 230000008018 melting Effects 0.000 claims abstract description 11
- 239000006104 solid solution Substances 0.000 claims abstract description 10
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 10
- 239000010937 tungsten Substances 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 10
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 9
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 6
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 239000010703 silicon Substances 0.000 claims abstract description 6
- 238000000034 method Methods 0.000 claims description 26
- 238000003723 Smelting Methods 0.000 claims description 25
- 239000002994 raw material Substances 0.000 claims description 18
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 238000010438 heat treatment Methods 0.000 claims description 14
- 239000000956 alloy Substances 0.000 claims description 13
- 229910045601 alloy Inorganic materials 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 9
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 239000010949 copper Substances 0.000 claims description 5
- 238000005516 engineering process Methods 0.000 claims description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 4
- 239000012467 final product Substances 0.000 claims description 3
- 239000000243 solution Substances 0.000 claims description 3
- 238000005303 weighing Methods 0.000 claims description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 2
- 238000004364 calculation method Methods 0.000 claims description 2
- 239000001257 hydrogen Substances 0.000 claims description 2
- 229910052739 hydrogen Inorganic materials 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 239000001301 oxygen Substances 0.000 claims description 2
- 229910052760 oxygen Inorganic materials 0.000 claims description 2
- 239000003054 catalyst Substances 0.000 claims 1
- 230000005672 electromagnetic field Effects 0.000 claims 1
- 239000007789 gas Substances 0.000 claims 1
- 238000003756 stirring Methods 0.000 claims 1
- 238000005728 strengthening Methods 0.000 abstract description 7
- 238000001513 hot isostatic pressing Methods 0.000 abstract description 4
- 239000000463 material Substances 0.000 abstract description 4
- 230000000087 stabilizing effect Effects 0.000 abstract description 3
- 229910018540 Si C Inorganic materials 0.000 abstract 1
- 229910010271 silicon carbide Inorganic materials 0.000 abstract 1
- 239000012856 weighed raw material Substances 0.000 abstract 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 6
- 238000005242 forging Methods 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 241001062472 Stokellia anisodon Species 0.000 description 2
- 239000012300 argon atmosphere Substances 0.000 description 2
- 239000012298 atmosphere Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000010955 niobium Substances 0.000 description 2
- 230000002411 adverse Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 238000005495 investment casting Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000007935 neutral effect Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 230000001502 supplementing effect Effects 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- 230000003245 working effect Effects 0.000 description 1
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- 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
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- 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
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- 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)
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Abstract
The invention provides a high-temperature titanium alloy for short and medium time and a preparation method thereof, wherein the high-temperature titanium alloy comprises 6.6-7.2% of aluminum by weight percent; tin is 2.6% -3%; zirconium is 4% -5%; molybdenum is not less than 4%; tungsten is 1% -1.6%; silicon is 0.1-0.3%; carbon is 0.1% -0.15%; the balance being titanium; greatly improves the content of molybdenum and tungsten, and further improves the high-temperature strength by utilizing the two beta stabilizing elements with higher melting points. The weighed raw materials are subjected to vacuum casting to prepare Ti-Al-Sn-Zr-Mo-W-Si-C cast ingots/pieces, and the tensile properties of the cast high-temperature titanium alloy at the room temperature and the high temperature of 650-700 ℃ after hot isostatic pressing are exceeded only through multi-element solid solution strengthening and aging treatment. The preparation method can meet the requirements of short-medium-high-temperature use of hot-end materials in the fields of aerospace and military industry and the like, and effectively shortens the preparation flow of components.
Description
Technical Field
The invention relates to the technical field of alloy materials, in particular to a high-temperature titanium alloy for short and medium time and a preparation method thereof.
Background
The titanium alloy has the advantages of low density, high specific strength, corrosion resistance and the like, and has been widely applied in the fields of aerospace and the like. However, as the flight speed of aircraft continues to increase, higher demands are placed on the operating temperature and service performance of titanium alloys. The high-temperature titanium alloy needs to be further broken through, and particularly the service temperature and the high-temperature performance of the high-temperature titanium alloy are improved. At present, the maximum use temperature of the mature high-temperature titanium alloy is about 600 ℃, and the maximum use temperature is typically represented by Ti-1100 in the United states, IMI834 in the United kingdom, BT36 in Russian, ti600 in China and the like. However, the high temperature titanium alloy system above 600 ℃ still has the defects. In developed countries, the development of novel high-temperature titanium alloys has been put in a very important place in recent years. The high-temperature titanium alloy in China is started later, the early stage is mainly referred to as a reference, and the high-temperature titanium alloy in China gradually goes on an independent research and development road at present.
Aiming at the special fields of aerospace, military industry and the like, based on the working property of an aircraft, the high-temperature titanium alloy can meet the service requirement only by ensuring the structural performance of the high-temperature titanium alloy in a middle-short service time. In order to improve the heat treatment capability and the mechanical property at room temperature, the traditional superalloy generally only contains a small amount of beta stabilizing elements, and the main reason is that under long-time service conditions, excessive beta phases can reduce the heat stability and high-temperature creep property of a structure. Thus, conventional high temperature titanium alloys such as Ti-1100 and IMI834 alloys, the total content of beta elements generally does not exceed 2wt.%. However, for the short-medium use high temperature titanium alloy, since the instantaneous high temperature strength of the alloy can be improved by appropriately sacrificing the heat stability of the structure, it is permissible to add higher contents of β -stabilizing elements such as Mo, W, nb and other high melting point elements to the presently common short-medium use high temperature titanium alloy. Meanwhile, when designing the alloy components, the aluminum equivalent [ Al ] eq and the molybdenum equivalent [ Mo ] eq of the alloy are comprehensively considered, and the [ Al ] eq or the [ Mo ] eq value is taken as an important criterion for designing the titanium alloy.
Because the titanium alloy forging has higher cost, the casting is a near net forming method, and has great cost advantage compared with other metallurgical methods such as forging and the like. Meanwhile, casting is also an important forming means of hollow complex precision components. In recent years, the production and application of titanium alloy castings has remained a strong development. Practice proves that titanium alloy parts with complex shapes can be directly manufactured by casting, a large number of machining procedures are omitted, and the utilization rate of materials is improved. The material utilization rate of the common forging is only 10% -15%, the utilization rate of the common casting is 45%, and the precision casting can reach 75% -90%, which is particularly important for expensive titanium alloy. The microstructure and mechanical properties of the titanium alloy are very sensitive to the heat treatment process, and the microstructure morphology can be changed by carrying out the heat treatment processes such as solid solution, aging and the like so as to achieve the aim of improving the mechanical properties.
The invention CN109763026A proposes a Ti-A1-Sn-Zr-Mo-Cr-Nb-Fe system titanium alloy for high strength casting, which has a room temperature tensile strength of about 1100MPa and an elongation of 8%, but is not suitable for high temperatures of 600 ℃ or higher.
The invention CN111020290A proposes a titanium alloy casting material suitable for high temperature of 650-750 ℃, but the tensile strength of the cast alloy at room temperature is only 925MPa at most even though the cast alloy is subjected to hot isostatic pressing treatment.
The invention CN107058801a proposes a cast titanium alloy suitable for 560-650 ℃ which, after hot isostatic pressing and solution aging treatment, but only shows tensile properties of 600 ℃ and room temperature elongation of less than 6%.
The invention CN106636746A provides a high-strength high-elongation high-temperature titanium alloy, the invention CN106801164A and the invention CN102978440A provide a short-time high-temperature titanium alloy, but the alloy is subjected to complex multi-firing forging and solid solution aging treatment.
In general, high temperature titanium alloys used at 650 ℃ and above in China are still in the research stage. Aiming at the problems, a casting titanium alloy component meeting the requirements of short, medium and high temperatures is developed, and a proper casting preparation process and a heat treatment strengthening means are designed, so that the room temperature and high temperature mechanical properties of the alloy meet the use requirements, and the method is very necessary.
Disclosure of Invention
In view of this, the present invention proposes a high temperature titanium alloy for short-medium time and a method for producing the same, for providing a cast titanium alloy composition satisfying the high temperature performance at short-medium time of 650-700 ℃ and a suitable production process.
The technical scheme of the invention is realized as follows: the invention provides a high-temperature titanium alloy for short and medium time, which comprises the following components in percentage by weight,
6.6 To 7.2 percent of aluminum;
Molybdenum is not less than 4%;
zirconium is 4% -5%;
Tin is 2.6% -3%;
tungsten is 1% -2%;
Silicon is 0.1-0.3%;
carbon is 0.1% -0.15%;
the balance being titanium.
Based on the technical scheme, preferably, the weight percentage of the molybdenum is 4% -6%, and the sum of the weight percentages of the molybdenum and the tungsten is 5% -8%.
On the basis of the technical scheme, the method preferably further comprises impurities, wherein the impurities comprise at least one of nitrogen, hydrogen and oxygen, and the weight percentage of the impurities is not more than 0.2%.
On the other hand, the invention also provides a preparation method of the high-temperature titanium alloy for the short and medium time, which comprises the following steps,
Weighing the raw materials of each component of the titanium alloy by adopting a thousandth electronic balance with the precision of 0.001g to ensure that the error is controllable, and then placing the raw materials into a water-cooled copper crucible of a smelting furnace;
Step two, after closing the vacuum chamber of the smelting furnace, vacuumizing the vacuum chamber, then backfilling high-purity argon into the vacuum chamber, and smelting raw materials until a titanium alloy melt with uniform components is obtained;
And thirdly, pouring the titanium alloy melt into a casting mold, and cooling to obtain the cast ingot or casting with the required shape and size.
On the basis of the technical scheme, the method preferably further comprises a step four of carrying out heat treatment on the obtained cast ingot or casting to obtain a final product, wherein the heat treatment process is 950 ℃ for 2h of solid solution, and then air cooling is carried out after ageing for 4h at 700 ℃.
On the basis of the technical scheme, in the first step, preferably, according to the principle that the melting point is low to high, the low-melting-point raw materials are placed at the bottom, the high-melting-point raw materials are placed at the top, and the raw materials are sequentially placed in a water-cooled copper crucible of a smelting furnace.
On the basis of the technical scheme, in the second step, preferably, before smelting the titanium alloy, the titanium ingot or the zirconium ingot is smelted, and residual air is absorbed to provide a pure atmosphere for the subsequent smelting and casting operation.
On the basis of the technical scheme, in the second step, preferably, after the vacuum chamber of the smelting furnace is closed, the vacuum chamber is vacuumized to be less than 0.01Pa, then high-purity argon is backfilled to be about 5 multiplied by 10 4 Pa, the operations of vacuumization and backfilling the argon are repeated for 2 times, and then the titanium alloy is smelted.
On the basis of the technical scheme, in the third step, preferably, the titanium alloy melt is poured into a casting mould in an argon atmosphere to obtain a required cast ingot or casting.
On the basis of the technical scheme, in the second step, preferably, a vacuum smelting technology is adopted to smelt the titanium alloy.
Compared with the prior art, the high-temperature titanium alloy for short and medium time and the preparation method thereof have the following beneficial effects:
(1) The invention adopts a multi-element solid solution strengthening and aging strengthening mode, and the beta stabilizing elements such as Mo, W and the like are obviously improved when high Al is added, so that the high-temperature strength is improved; neutral elements such as Zr, sn and the like are added in proportion so as to play a role in supplementing and strengthening; si is added to avoid reducing the plasticity of the titanium alloy; c is added to increase the temperature range of a two-phase region in the titanium alloy, the high-temperature processing temperature window of the titanium alloy is increased, and the comprehensive mechanical properties of the titanium alloy can be effectively improved through heat treatment; the contents of molybdenum and tungsten are remarkably improved, and the high-temperature strength of the titanium alloy can be effectively improved by utilizing the characteristics of beta element, so that the purpose of short-medium-time high-temperature application is achieved; meanwhile, rare earth elements and various other metal elements with larger density are avoided/reduced, and complex precipitated phases are avoided; finally, the brittleness of the titanium alloy is avoided while the high-temperature strength and creep resistance of the titanium alloy are ensured, the processing performance of the titanium alloy is improved, and the titanium alloy is matched with good strength and plasticity.
(2) The invention adopts the design concept of multi-element composite reinforcement, so that the Mo equivalent related to the beta stable element is 4.4-6.8, and the mechanical property of the existing cast high-temperature titanium alloy after hot isostatic pressing and even forging can be similar to the mechanical property of the existing cast high-temperature titanium alloy by only adopting the casting combined with solid solution aging heat treatment process, and the purpose of greenness and high efficiency is achieved.
(3) The invention adopts the vacuum smelting technology to smelt and prepare the titanium alloy, and the preparation technology has the advantages of wide applicability, convenient operation and high efficiency.
Drawings
In order to more clearly illustrate the embodiments of the invention or the technical solutions in the prior art, the drawings that are required in the embodiments or the description of the prior art will be briefly described, it being obvious that the drawings in the following description are only some embodiments of the invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a microstructure of a high temperature titanium alloy at room temperature according to an embodiment of the present invention;
FIG. 2 is a microscopic view of a tensile fracture of a high temperature titanium alloy according to an embodiment of the present invention, wherein (a) is a room temperature tensile fracture; (b) stretch break at 650 ℃; (c) a tensile break at 700 ℃;
FIG. 3 is a microstructure of a second high temperature titanium alloy of the present invention at room temperature;
FIG. 4 is a microscopic view of tensile fracture of a second high temperature titanium alloy according to an embodiment of the present invention, wherein (a) is a room temperature tensile fracture; (b) stretch break at 650 ℃; (c) a tensile break at 700 ℃;
FIG. 5 is a microstructure of a titanium alloy at room temperature according to an embodiment of the present invention;
FIG. 6 is a microscopic view of tensile fracture of a titanium alloy at elevated temperature according to an embodiment of the present invention, wherein (a) is a tensile fracture at room temperature; (b) stretch break at 650 ℃; (c) tensile fracture at 700 ℃.
Detailed Description
The following description of the embodiments of the present invention will clearly and fully describe the technical aspects of the embodiments of the present invention, and it is apparent that the described embodiments are only some embodiments of the present invention, not all embodiments. All other embodiments, based on the embodiments of the invention, which a person of ordinary skill in the art would achieve without inventive faculty, are within the scope of the invention.
Example 1
The high-temperature titanium alloy for short and medium time comprises, by weight, 6.6% of aluminum Al; molybdenum Mo 4%; zirconium Zr is 4%; tin Sn 2.6%; tungsten W is 1%; silicon Si is 0.1%; carbon C is 0.1%; the impurity is 0.08%, and the balance is titanium Ti.
Compared with the conventional common titanium alloy composition ratio, the embodiment has three differences:
Firstly, the content of molybdenum Mo is greatly improved. The melting point of molybdenum is high, and the high-temperature strength of the titanium alloy can be effectively improved by improving the content ratio of molybdenum in the titanium alloy. The calculation formula of Mo equivalent in the alloy system is as follows: [ Mo ] eq=Mo+W/1.5.
Secondly, the rare earth elements which are usually adopted and have high cost are not added into the alloy. The purpose of adding rare earth elements to titanium alloys is to improve the heat stability, but for high temperature titanium alloys used in short-medium time applications, the high temperature strength is more of a concern than the heat stability. The addition of rare earth elements has small contribution to strengthening effect, and the titanium alloy of the embodiment is mainly used for improving the high-temperature performance of the titanium alloy and has strong pertinence, so that the addition of the rare earth elements in the components is not necessary. Meanwhile, the rare earth elements are added into the components of the titanium alloy, so that the casting difficulty is increased, and the alloy components are difficult to control accurately.
Thirdly, compared with the domestic and foreign high-temperature titanium alloy mentioned in the background art, the elements such as niobium Nb, tantalum Ta and the like are removed from the components, and the density of the elements is large, so that the specific strength of the titanium alloy is adversely affected.
The invention relates to a preparation method of a high-temperature titanium alloy for short and medium time, which comprises the following steps,
Firstly, weighing the raw materials of each component of the titanium alloy by adopting an electronic balance with the accuracy of 0.001g to ensure that the error is controllable, then placing the raw materials with low melting point at the lowest and the raw materials with high melting point at the uppermost according to the principle that the melting point is low to high, and sequentially placing the raw materials into a water-cooled copper crucible of a smelting furnace to ensure that the raw materials are fully melted.
Step two, after closing the vacuum chamber of the smelting furnace, vacuumizing the vacuum chamber to less than 0.01Pa, then backfilling high-purity argon to about 5X 10 4 Pa, and repeating vacuumizing and backfilling argon for 2 times; before smelting titanium alloy, firstly smelting titanium ingot or zirconium ingot to absorb residual air to provide pure atmosphere for subsequent smelting and casting operation; and smelting the titanium alloy by adopting a vacuum smelting technology, and smelting the raw materials until a titanium alloy ingot with uniform components is obtained.
And thirdly, pouring the titanium alloy ingot into a casting mold under the argon atmosphere, and cooling to obtain the ingot or casting with the required size. In this example, for convenience, a cylindrical metal ingot was obtained.
And step four, carrying out solid solution aging strengthening heat treatment on the obtained cast ingot or casting to obtain a final product, wherein the heat treatment process is carried out after 950 ℃ solid solution for 2 hours, and then carrying out air cooling after aging for 4 hours at 700 ℃.
Example two
The titanium alloy comprises, by weight, 6.9% of aluminum Al; molybdenum Mo 5%; zirconium Zr 4.5%; tin Sn 2.8%; tungsten W is 1.5%; silicon Si 0.15%; carbon C is 0.12%; the impurity is 0.08%, and the balance is titanium Ti.
Example III
The titanium alloy comprises, by weight, 7.2% of aluminum Al; molybdenum Mo 6%; zirconium Zr is 5%; tin Sn 3%; tungsten W is 2%; silicon Si is 0.3%; carbon C is 0.15%; the impurity is 0.08%, and the balance is titanium Ti.
The preparation method of the first embodiment is adopted to detect the final products obtained in the three embodiments according to the component proportions of the first to third embodiments, and the room temperature stretching and the high temperature stretching are carried out according to the methods of national standards GB/T228-2002 and GB/T4338-2006 to obtain a comparison table of the room temperature and the high temperature stretching performances of the titanium alloy in the following table 1.
TABLE 1
It can be found that the room temperature tensile strength R m is more than or equal to 1100MPa, the yield strength R p0.2 is more than or equal to 990MPa and the elongation A is more than or equal to 7% after solid solution aging heat treatment; the tensile strength R m is more than or equal to 560MPa at 650 ℃, the yield strength R p0.2 is more than or equal to 460MPa, and the elongation A is more than or equal to 10%; the tensile strength R m is more than or equal to 460MPa at 700 ℃, the yield strength R p0.2 is more than or equal to 370MPa, and the elongation A is more than or equal to 10.5%. Therefore, the high-temperature titanium alloy component has excellent strong plasticity for the strength and plasticity of the high-temperature titanium alloy which are critical for the subsequent processing service.
The foregoing description of the preferred embodiments of the invention is not intended to be limiting, but rather is intended to cover all modifications, equivalents, alternatives, and improvements that fall within the spirit and scope of the invention.
Claims (7)
1. A preparation method of a high-temperature titanium alloy for short and medium time is characterized by comprising the following steps: the high-temperature titanium alloy for short and medium time comprises the following components in percentage by weight,
6.6 To 7.2 percent of aluminum;
Molybdenum is 4% -6%;
zirconium is 4% -5%;
Tin is 2.6% -3%;
tungsten is 1% -2%;
Silicon is 0.1-0.3%;
carbon is 0.1% -0.15%;
And the balance being titanium, wherein the sum of the molybdenum and the tungsten is 5-8% by weight percent; wherein, the Mo equivalent in the alloy system is 4.4-6.8, and the calculation formula of the Mo equivalent is [ Mo ] eq=Mo+W/1.5;
Wherein, the room temperature tensile strength R m is more than or equal to 1100MPa, the yield strength R p0.2 is more than or equal to 990MPa and the elongation A is more than or equal to 7% after the solution aging heat treatment of the high-temperature titanium alloy during the short period; the tensile strength R m is more than or equal to 560MPa at 650 ℃, the yield strength R p0.2 is more than or equal to 460MPa, and the elongation A is more than or equal to 10%; the tensile strength R m is more than or equal to 460MPa at 700 ℃, the yield strength R p0.2 is more than or equal to 370MPa, and the elongation A is more than or equal to 10.5%;
Comprises the steps of,
Firstly, weighing the raw materials of each component of the titanium alloy by adopting an electronic balance with the accuracy of 0.001g to ensure that the error is controllable, and then placing the raw materials into a water-cooled copper crucible of a smelting furnace according to the sequence from low melting point to high melting point;
step two, after closing the vacuum chamber of the smelting furnace, vacuumizing the vacuum chamber, then backfilling high-purity argon into the vacuum chamber, and then carrying out vacuum smelting on raw materials, wherein the whole smelting process is completed under the condition of electromagnetic field stirring until a titanium alloy melt with uniform components is obtained;
pouring the titanium alloy melt into a casting mold in a vacuum environment, and cooling to obtain an ingot or casting with a required size;
And step four, carrying out vacuum heat treatment on the obtained cast ingot or casting to obtain a final product, wherein the heat treatment process is carried out after 950 ℃ solid solution for 2 hours and then air cooling after ageing for 4 hours at 700 ℃.
2. The method for preparing the high-temperature titanium alloy for short and medium time according to claim 1, wherein the method comprises the following steps: the catalyst further comprises an impurity, wherein the impurity comprises at least one of nitrogen, hydrogen and oxygen, and the impurity is not more than 0.2% by weight percent.
3. The method for preparing the high-temperature titanium alloy for short and medium time according to claim 1, wherein the method comprises the following steps: in the first step, according to the principle that the melting point is low to high, the low-melting-point raw materials are placed at the bottom, the high-melting-point raw materials are placed at the top, and the raw materials are sequentially placed in a water-cooled copper crucible of a smelting furnace.
4. The method for preparing the high-temperature titanium alloy for short and medium time according to claim 1, wherein the method comprises the following steps: in the second step, before smelting the titanium alloy, residual air in a titanium ingot or zirconium ingot absorbing furnace is smelted.
5. The method for preparing the high-temperature titanium alloy for short and medium time according to claim 1, wherein the method comprises the following steps: in the second step, after the vacuum chamber of the smelting furnace is closed, vacuumizing the vacuum chamber to less than 0.01Pa, then backfilling high-purity argon to about 5X 10 4 Pa, repeating the vacuumizing and backfilling operations for 2 times, and then smelting the titanium alloy.
6. The method for preparing the high-temperature titanium alloy for short and medium time according to claim 1, wherein the method comprises the following steps: in the second step, a vacuum melting technology is adopted to melt the titanium alloy.
7. The method for preparing the high-temperature titanium alloy for short and medium time according to claim 1, wherein the method comprises the following steps: in the third step, the titanium alloy ingot is poured into a casting mould in argon gas, so that a required cast ingot or casting is obtained.
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| FR1170630A (en) * | 1956-04-04 | 1959-01-16 | Ici Ltd | Titanium based alloys |
| GB1049624A (en) * | 1964-11-13 | 1966-11-30 | Birmingham Small Arms Co Ltd | Improvements in or relating to titanium alloys |
| CN108456806A (en) * | 2018-04-30 | 2018-08-28 | 西北有色金属研究院 | A kind of high-silicon high plasticity beta titanium alloy and preparation method thereof |
| CN108893628A (en) * | 2018-08-03 | 2018-11-27 | 中鼎特金秦皇岛科技股份有限公司 | A kind of low elastic modulus erosion resistant titanium alloy and preparation method thereof |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR1170630A (en) * | 1956-04-04 | 1959-01-16 | Ici Ltd | Titanium based alloys |
| GB1049624A (en) * | 1964-11-13 | 1966-11-30 | Birmingham Small Arms Co Ltd | Improvements in or relating to titanium alloys |
| CN108456806A (en) * | 2018-04-30 | 2018-08-28 | 西北有色金属研究院 | A kind of high-silicon high plasticity beta titanium alloy and preparation method thereof |
| CN108893628A (en) * | 2018-08-03 | 2018-11-27 | 中鼎特金秦皇岛科技股份有限公司 | A kind of low elastic modulus erosion resistant titanium alloy and preparation method thereof |
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