CN114262852A - Ti2AlNb-based alloy bar and preparation method and application thereof - Google Patents
Ti2AlNb-based alloy bar and preparation method and application thereof Download PDFInfo
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Abstract
The invention relates to Ti2In particular to a Ti based alloy in the technical field of AlNb based alloy2An AlNb-based alloy bar and a preparation method and application thereof. The preparation method comprises the following steps: (A) mixing Ti2Carrying out homogenization heat treatment on the AlNb-based alloy ingot at 1160-1200 ℃ to obtain an ingot blank; (B) carrying out heat preservation treatment at 1130-1170 ℃, and then carrying out extrusion and drawing to obtain a primary bar blank; (C) carrying out heat preservation treatment on the primary bar blank at 1020-1060 ℃, then cooling the bar blank along with the furnace to below 500 ℃, and discharging the bar blank; (D) then carrying out heat preservation treatment at 960-980 ℃, and then carrying out extrusion and drawing to obtain a secondary bar blank; (E) carrying out solution heat treatment and aging heat treatment on the secondary bar billet to obtain Ti2AlNb-based alloy bars.The method improves Ti2Tensile strength, elongation and structural homogeneity of AlNb-based alloy rods.
Description
Technical Field
The invention relates to Ti2In particular to a Ti based alloy in the technical field of AlNb based alloy2An AlNb-based alloy bar and a preparation method and application thereof.
Background
Ti2The AlNb-based alloy belongs to a Ti-Al series intermetallic compound material and integrates Ti3The Al and TiAl have the advantages of good room temperature ductility and toughness, high specific strength, good creep resistance and oxidation resistance, and good high-temperature forming capability, are light high-temperature-resistant structural materials with great potential, are expected to replace the traditional nickel-based high-temperature alloy to become an important material for a hot-end part of an aerospace engine, and have important effects on improving the thrust-weight ratio of the engine and increasing the temperature-resistant grade. The blade forging for the aeronautic and astronautic engines is one of the main applications, however, the blade is mainly under the action of centrifugal force in the using process, and the requirement on the strong plasticity along the blade body direction is high. Therefore, how to prepare the rod material for the blade, which meets the working condition of the engine blade and has unidirectional high strength and high elongation matching, is the current technical difficulty.
The traditional bar preparation process adopts ingot casting cogging, multi-fire upsetting-drawing forging and final performance regulation heat treatment. Ti2The AlNb-based alloy is used as an intermetallic compound material, has large deformation resistance, insufficient process plasticity and high crack sensitivity, has large difficulty in controlling the uniformity of the structure in the upsetting-drawing forging process, and Ti2The AlNb alloy has stronger tissue inheritance and is influenced by the fluctuation of the tissue uniformity of the bar, the performance stability of the forge piece prepared by the traditional process can not be fully ensured all the time, and the service performance of the alloy and the service life of a product component are influenced.
In view of the above, the present invention is particularly proposed.
Disclosure of Invention
The first object of the present invention is to provide a Ti2The preparation method of the AlNb-based alloy bar improves Ti2The tensile strength and the elongation percentage of the AlNb-based alloy bar in a single direction are ensured, and other comprehensive mechanical properties can meet the use requirements.
The second object of the present invention is to provide a Ti2The AlNb-based alloy bar has good structure uniformity, the room-temperature tensile strength is more than or equal to 1250MPa, and the room-temperature elongation is more than or equal to 15%.
It is a third object of the present invention to provide the above Ti2The application of the AlNb-based alloy bar in aerospace equipment.
In order to achieve the above purpose of the present invention, the following technical solutions are adopted:
the invention provides a Ti2The preparation method of the AlNb-based alloy bar comprises the following steps:
(A) mixing Ti2Carrying out homogenization heat treatment on the AlNb-based alloy ingot at 1160-1200 ℃ to obtain an ingot blank;
(B) carrying out heat preservation treatment on the ingot casting blank at 1130-1170 ℃, and then carrying out extrusion and drawing to obtain a primary bar blank;
(C) carrying out heat preservation treatment on the primary bar blank at 1020-1060 ℃, then cooling the bar blank along with the furnace to below 500 ℃, and discharging the bar blank;
(D) carrying out heat preservation treatment on the primary bar blank treated in the step (C) at 960-980 ℃, and then carrying out extrusion and drawing to obtain a secondary bar blank;
(E) carrying out solution heat treatment on the secondary bar billet at 970-1000 ℃, and then carrying out aging heat treatment at 780-820 ℃ to obtain Ti2AlNb-based alloy bars.
The invention also provides a method for preparing the Ti2Ti prepared by preparation method of AlNb-based alloy bar2AlNb-based alloy bars.
The invention also provides the Ti2The application of the AlNb-based alloy bar in aerospace equipment.
Compared with the prior art, the invention has the beneficial effects that:
the invention provides a Ti2The preparation method of the AlNb-based alloy bar adopts small-size ingot casting, and improves Ti content by the steps of homogenization heat treatment, high-temperature extrusion cogging, tissue homogenization treatment, low-temperature extrusion forming and bar performance regulation heat treatment2The structural uniformity, the unidirectional room temperature tensile strength and the room temperature elongation of the AlNb-based alloy bar can simultaneously meet the requirements of other comprehensive mechanical properties; the method has the advantages of simple operation, short production period, high stability, and suitability for industrial production.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are required to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
FIG. 1 shows Ti prepared in example 1 of the present invention2SEM image of AlNb-based alloy rods magnified 500 times.
FIG. 2 shows Ti prepared in example 1 of the present invention2SEM image of AlNb-based alloy rods magnified 2000 times.
FIG. 3 shows Ti prepared in comparative example 1 of the present invention2SEM image of AlNb-based alloy rods magnified 500 times.
FIG. 4 shows Ti prepared in comparative example 2 of the present invention2SEM image of AlNb-based alloy rods magnified 500 times.
FIG. 5 shows Ti prepared in example 1 of the present invention2EBSD pole figures for AlNb-based alloy rods.
FIG. 6 shows Ti prepared in example 1 of the present invention2EBSD antipole of AlNb-based alloy bars.
Detailed Description
The technical solutions of the present invention will be described clearly and completely with reference to the following detailed description, but those skilled in the art will understand that the following described examples are some, not all, of the examples of the present invention, and are only used for illustrating the present invention, and should not be construed as limiting the scope of the present invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The following is a Ti2The AlNb-based alloy bar and the preparation method and the application thereof are specifically explained.
Some embodiments of the present invention provide a Ti2The preparation method of the AlNb-based alloy bar comprises the following steps:
(A) mixing Ti2Carrying out homogenization heat treatment on the AlNb-based alloy ingot at 1160-1200 ℃ to obtain an ingot blank;
(B) carrying out heat preservation treatment on the ingot blank at 1130-1170 ℃, and then carrying out extrusion and drawing to obtain a primary bar blank;
(C) carrying out heat preservation treatment on the primary bar blank at 1020-1060 ℃, then cooling the bar blank along with the furnace to below 500 ℃, and discharging the bar blank;
(D) carrying out heat preservation treatment on the primary bar blank treated in the step (C) at 960-980 ℃, and then carrying out extrusion and drawing to obtain a secondary bar blank;
(E) carrying out solution heat treatment on the secondary bar billet at 970-1000 ℃, and then carrying out aging heat treatment at 780-820 ℃ to obtain Ti2AlNb-based alloy bars.
In some embodiments of the present invention, in step (a), the temperature of the homogenization heat treatment may be, for example, 1160 ℃, 1165 ℃, 1170 ℃, 1175 ℃, 1180 ℃, 1185 ℃, 1190 ℃, 1195 ℃ or 1200 ℃, and the like, typically but not limitedly.
In some embodiments of the present invention, the temperature of the incubation process in step (B) may be, for example, typically but not limited to 1130 ℃, 1135 ℃, 1140 ℃, 1145 ℃, 1150 ℃, 1155 ℃, 1160 ℃, 1165 ℃, 1170 ℃, and the like.
In some embodiments of the present invention, in step (C), the temperature of the incubation treatment may be, for example, 1020 ℃, 1025 ℃, 1030 ℃, 1035 ℃, 1040 ℃, 1045 ℃, 1050 ℃, 1055 ℃ or 1060 ℃ and the like, typically but not limitatively.
In some embodiments of the present invention, in step (D), the temperature of the incubation treatment, typically but not limited to, may be 960 ℃, 965 ℃, 970 ℃, 975 ℃, 980 ℃, and the like, for example.
In some embodiments of the present invention, in step (E), the temperature of the solution heat treatment may be, for example, 970 ℃, 975 ℃, 980 ℃, 985 ℃, 990 ℃, 995 ℃, or 1000 ℃, and the like, typically but not limitedly.
In some embodiments of the present invention, in step (E), the temperature of the aging heat treatment may be, for example, 780 ℃, 785 ℃, 790 ℃, 795 ℃, 800 ℃, 805 ℃, 810 ℃, 815 ℃, 820 ℃ or the like, typically but not by way of limitation.
The invention is through the reaction of Ti2Carrying out homogenization heat treatment, high-temperature extrusion cogging, structure homogenization heat treatment, low-temperature extrusion forming and bar material performance regulation heat treatment on the AlNb-based alloy cast ingot so as to prepare a homogeneous fine-grained bar material with high strength and high elongation along the extrusion direction, and improving the Ti content2The unidirectional tensile strength and elongation of the AlNb-based alloy bar ensure the use requirements of other comprehensive mechanical properties.
In some embodiments of the invention, in step (A), Ti2The diameter of the AlNb-based alloy ingot is 160-280 mm; typically but not limitatively, e.g. Ti2The AlNb-based alloy ingot has a diameter of 160mm, 170mm, 180mm, 190mm, 200mm, 210mm, 220mm, 230mm, 240mm, 250mm, 260mm, 270mm, or 280mm, or the like; preferably, Ti2The diameter of the AlNb-based alloy ingot is 280 mm.
The invention adopts small-sized cast ingots, and the cast structure of the cast ingots is fine, thereby being beneficial to improving the structure uniformity of the bars. Compared with the traditional process, the production process of small cast ingots and extrusion is adopted, so that the steps of forging and the like are reduced, the production period is shortened, the production efficiency is improved, and the structure uniformity of the bar is further improved.
In some embodiments of the invention, in step (a), Ti is prepared by a method comprising one-time vacuum consumable melting, two-time vacuum skull melting and three-time vacuum consumable melting2And (4) casting an AlNb-based alloy ingot.
In some embodiments of the invention, Ti2The alloy composition of the AlNb-based alloy ingot includes, but is not limited to, Ti-22Al-25Nb, and the remainder is Ti2AlNb-based alloys are acceptable.
In some embodiments of the present invention, in the step (A), the holding time of the homogenization heat treatment is 35-45 h; typical but non-limiting holding times for the homogenization heat treatment are 35h, 36h, 37h, 38h, 39h, 40h, 41h, 42h, 43h, 44h, 45h, and the like, for example.
In some embodiments of the invention, in step (A), Ti is added2And (3) carrying out heat preservation treatment on the AlNb-based alloy ingot at 1180 ℃ for 38 hours.
In some embodiments of the present invention, step (a) further comprises homogenizing the heat-treated Ti2And (4) carrying out surface peeling, dead head cutting and bottom cutting on the AlNb-based alloy cast ingot.
In some embodiments of the invention, in the step (B), the time of the heat preservation treatment is 2-4 h; typical but non-limiting examples of the incubation time are 2h, 2.5h, 3h, 3.5h and 4h, etc.
In some embodiments of the invention, in step (B), the ingot is held at 1150 ℃ for 3 hours.
In some embodiments of the present invention, the ratio of step (B) is 3 to 5.5: 1; typically, but not by way of limitation, for example, the extrusion ratio of extrusion to elongation is 3: 1. 3.2: 1. 3.5: 1. 3.8: 1. 4: 1. 4.2: 1. 4.5: 1. 4.8: 1. 5: 1. 5.2: 1 or 5.5: 1, etc.; preferably, in step (B), the extrusion ratio of the extrusion elongation is 4.5: 1.
in some embodiments of the invention, step (B) further comprises applying an antioxidant coating and a glass lubricant on the surface of the ingot blank in sequence before the heat preservation treatment, wherein the antioxidant coating comprises an antioxidant coating resistant to 1200 ℃, and the glass lubricant comprises glass powder. Preferably, the coating thickness of the anti-oxidation coating is 0.2-0.4 mm, the coating thickness of the glass lubricant is 0.4-0.6 mm, and more preferably, the coating thickness of the anti-oxidation coating is 0.3mm, and the coating thickness of the glass lubricant is 0.5 mm.
In some embodiments of the invention, in the step (C), the time of the heat preservation treatment is 1-3 h; typically, but not by way of limitation, the incubation time is, for example, 1h, 1.5h, 2h, 2.5h, 3h, and the like.
In some embodiments of the invention, in step (C), the primary rod blank is incubated at 1040 ℃ for 2 h.
In some embodiments of the present invention, in the step (C), the product is discharged from the furnace after cooling to 300-500 ℃.
In some embodiments of the invention, in the step (D), the time of the heat preservation treatment is 1-2 h; typically, but not by way of limitation, the incubation period is, for example, 1h, 1.5h, 2h, and the like.
In some embodiments of the invention, in step (D), the primary rod blank treated in step (C) is subjected to heat preservation treatment at 970 ℃ for 1.5 h.
In some embodiments of the invention, in the step (D), the extrusion ratio of the extrusion elongation is 3 to 5.5: 1; typically, but not by way of limitation, for example, the extrusion ratio of extrusion to elongation is 3: 1. 3.2: 1. 3.5: 1. 3.8: 1. 4: 1. 4.2: 1. 4.5: 1. 4.8: 1. 5: 1. 5.2: 1 or 5.5: 1, etc.; preferably, in step (D), the extrusion ratio of the extrusion elongation is 4.0: 1.
in some embodiments of the present invention, step (D) further comprises applying an antioxidant coating and a glass lubricant on the surface of the ingot blank in sequence before the heat preservation treatment, wherein the antioxidant coating comprises an antioxidant coating resistant to 1200 ℃, and the glass lubricant comprises glass powder. Preferably, the coating thickness of the antioxidant coating is 0.2-0.4 mm, and the coating thickness of the glass lubricant is named as 0.4-0.6.
In some embodiments of the invention, in the step (E), the time of the solution heat treatment is 2.5 to 4 hours; typically, but not by way of limitation, the solution heat treatment may be for a time of, for example, 2.5 hours, 3 hours, 3.5 hours, 4 hours, and the like.
In some embodiments of the invention, in step (E), the time of the aging heat treatment is more than or equal to 16 h; preferably, the time of aging heat treatment is 16-32 h; typical but non-limiting times for the aging heat treatment are, for example, 16h, 18h, 20h, 22h, 24h, 26h, 28h, 30h, 32h, and the like.
In some embodiments of the invention, in step (E), solution heat treatment is performed at 980 ℃ for 3 h.
In some embodiments of the invention, in step (E), the aging heat treatment is carried out at 800 ℃ for 24 h.
Some embodiments of the present invention also provide for using the above-described Ti2Ti prepared by preparation method of AlNb-based alloy bar2AlNb-based alloy bars.
In some embodiments of the invention, Ti2The room-temperature tensile strength of the AlNb-based alloy bar is more than or equal to 1250 MPa; ti2The room temperature elongation of the AlNb-based alloy bar is more than or equal to 15 percent.
Some embodiments of the invention also provide Ti2The application of the AlNb-based alloy bar in aerospace equipment; preferably, the aerospace device comprises an aerospace engine.
Ti prepared by the invention2The AlNb-based alloy bar can meet the material selection requirement of the aerospace engine blade forging, and the use reliability of the blade forging is improved.
The features and properties of the present invention are described in further detail below with reference to examples. Ti used in the embodiment of the present invention2The alloy composition of the AlNb-based alloy ingot will be described by taking Ti-22Al-25Nb as an example.
Example 1
This example provides Ti2The preparation method of the AlNb-based alloy bar comprises the following steps:
(A) will be provided with
Ti of (A)2The AlNb-based alloy ingot is subjected to heat preservation treatment 38 at 1180 DEG CAfter h, the mixture is sequentially subjected to surface peeling, dead head cutting and bottom removing treatment to obtain the product
Ingot casting blank;
(B) coating anti-1200 ℃ antioxidant coating (TB1200-16) with the thickness of 0.3mm on the surface of an ingot blank in sequence, spraying glass powder with the thickness of 0.5mm, carrying out heat preservation treatment at 1150 ℃ for 3h, then placing the ingot blank in an extruder for extrusion and drawing to obtain a primary bar blank, wherein the extrusion ratio is 4.5: 1;
(C) carrying out heat preservation treatment on the primary bar blank at 1040 ℃ for 2h, then cooling the bar blank along with the furnace to 500 ℃, and discharging the bar blank;
(D) peeling the primary bar blank treated in the step (C) to
Sequentially coating 1200 deg.C-resistant antioxidant coating (TB1200-16) with thickness of 0.3mm on the surface, spraying 0.5mm glass powder, maintaining the temperature at 970 deg.C for 1.5 hr, and extruding and drawing in extruder to obtain the final product
A secondary bar stock, wherein the extrusion ratio is 4: 1;
(E) carrying out solution heat treatment on the secondary bar billet for 3h at 980 ℃, and then carrying out aging heat treatment for 24h at 800 ℃ to obtain Ti2AlNb-based alloy bars.
Among them, Ti used in the present example2The preparation method of the AlNb-based alloy ingot comprises the following steps: firstly, calculating the required ingredient weight of each electrode according to nominal ingredient components, then carrying out raw material mixing and electrode pressing to prepare a primary consumable electrode, and carrying out primary consumable and secondary skull melting to obtain a skull cast ingot with uniform and consistent components. Then, assembling and welding the skull cast ingot into a self-consuming electrode in a furnace welding mode, and finally obtaining the self-consuming electrode through vacuum self-consuming smelting
Ti of (A)2And (4) casting an AlNb-based alloy ingot.
Example 2
This example provides Ti2The preparation method of the AlNb-based alloy bar comprises the following steps:
(A) mixing Ti2AlNb-based alloy
After the cast ingot is subjected to heat preservation treatment for 35 hours at 1200 ℃, the cast ingot is obtained by sequentially carrying out surface peeling, dead head cutting and bottom treatment
Ingot casting blank;
(B) sequentially coating 1200 ℃ resistant antioxidant coating (TB1200-16) with the thickness of 0.3mm on the surface of the ingot blank, spraying glass powder with the thickness of 0.5mm, carrying out heat preservation treatment at 1170 ℃ for 2h, and then placing the ingot blank in an extruder for extrusion and drawing to obtain the alloy
Primary billet, wherein the extrusion ratio is 4.5: 1;
(C) carrying out heat preservation treatment on the primary bar blank at 1060 ℃ for 1h, then cooling the bar blank along with the furnace to 400 ℃, and discharging the bar blank;
(D) peeling the primary bar blank treated in the step (C) to
Sequentially coating 1200 deg.C-resistant antioxidant coating (TB1200-16) with thickness of 0.3mm on the surface, spraying 0.5mm glass powder, maintaining the temperature at 980 deg.C for 1 hr, and extruding and drawing in extruder to obtain the final product
The secondary billet of (2), wherein the extrusion ratio is 4: 1;
(E) carrying out solution heat treatment on the secondary bar billet at 1000 ℃ for 2.5h, and carrying out aging heat treatment at 820 ℃ for 16h to obtain Ti2AlNb-based alloy bars.
Ti used in this example2The AlNb-based alloy ingot was the same as in example 1.
Example 3
This example provides Ti2The preparation method of the AlNb-based alloy bar comprises the following steps:
(A) mixing Ti2AlNb-based alloy
After the cast ingot is subjected to heat preservation treatment at 1160 ℃ for 45 hours, the cast ingot is obtained by sequentially carrying out surface peeling, dead head cutting and bottom treatment
Ingot casting blank;
(B) sequentially coating 1200 ℃ resistant antioxidant coating (TB1200-16) with the thickness of 0.3mm on the surface of the ingot blank, spraying glass powder with the thickness of 0.5mm, carrying out heat preservation treatment at 1130 ℃ for 4h, and then placing the ingot blank into an extruder for extrusion and drawing to obtain the alloy
Primary billet, wherein the extrusion ratio is 4.5: 1;
(C) carrying out heat preservation treatment on the primary bar blank at 1020 ℃ for 3h, then cooling the bar blank along with the furnace to 300 ℃, and discharging the bar blank;
(D) peeling the primary bar blank treated in the step (C) to
Sequentially coating 1200 deg.C-resistant antioxidant coating (TB1200-16) with thickness of 0.3mm on the surface, spraying 0.5mm glass powder, maintaining the temperature at 960 deg.C for 2 hr, and extruding and drawing in extruder to obtain the final product
The secondary billet of (2), wherein the extrusion ratio is 4: 1;
(E) carrying out solution heat treatment on the secondary bar billet for 4h at 970 ℃, and then carrying out aging heat treatment for 30h at 780 ℃ to obtain Ti2AlNb-based alloy bars.
Ti used in this example2The AlNb-based alloy ingot was the same as in example 1.
Comparative example 1
Ti of this comparative example2The method for producing AlNb-based alloy rods is as described in example 1, except that: (A) mixing Ti2Homogenizing the AlNb-based alloy ingot at 1100 ℃ for 50h, and sequentially carrying out surface peeling, riser head cutting and bottom removing treatment to obtain the AlNb-based alloy ingot
And (5) ingot casting blank.
Comparative example 2
Ti of this comparative example2The AlNb-based alloy rod was produced by the method according to example 1, except that step (D) was directly performed after step (B), and step (C) was not performed.
Test example 1
For Ti prepared in example 12The AlNb-based alloy rods were subjected to scanning electron microscope tests in the extrusion direction, and the results are shown in fig. 1 and 2.
Ti prepared in comparative example 1 and comparative example 22The AlNb-based alloy rods were subjected to scanning electron microscope tests in the extrusion direction, and the results are shown in fig. 3 and 4.
As can be seen from FIGS. 1, 2, 3 and 4, Ti produced in example 1 of the present invention2The AlNb-based alloy bar has uniform and fine microstructure, good structure uniformity and better structure uniformity than the Ti prepared in comparative examples 1 and 22AlNb-based alloy bars.
For Ti of example 12EBSD testing of the AlNb-based alloy rods resulted in pole and counter pole patterns along the extrusion line, the results of which are shown in fig. 5 and 6.
The grain size and the slab size of examples 1 to 3 were measured using a grain size measuring tool in image pro plus software, and the results are shown in table 1.
TABLE 1
| Average size of particles (. mu.m) | Average length of lath (μm) | |
| Example 1 | 2.63 | 0.55 |
| Example 2 | 2.67 | 0.53 |
| Example 3 | 2.65 | 0.57 |
The final structure of the extruded bar is alpha after observation of the structure2+B2+ O three-phase, in which the particles of examples 1-3 are uniformly distributed and fine, the particle size is about 2.65 μm, and the lath length is about 0.55 μm. While comparative examples 1 and 2 are also made of2+B2The + O three-phase structure is a two-state structure, but the particles are not uniformly distributed, and the structure has a serious delamination phenomenon. Comparative example 1 mainly because the homogenization temperature of the ingot was low, the elements in the original extruded billet still had severe segregation, so that the recrystallization degree in the subsequent extrusion and heat treatment processes was different, thereby causing the delamination phenomenon. Comparative example 2 is mainly due to the fact that recrystallization of the original B2 grains was incomplete after the primary extrusion, and no structure homogenization was performed before the secondary extrusion, resulting in that the non-uniformity of the primary extrusion was maintained, thereby making the final particle distribution non-uniform.
Research shows that the bar after two times of extrusion has the original as-cast crystal grains fully crushed and a great deal of deformation energy accumulated and stored under two times of extrusion is in the subsequent heat treatment processThe recrystallization occurs, so that the original cast-state crystal grains are fully refined, and the refined B2The crystal grains are only about 200 μm, and the strength and plasticity of the alloy are improved due to the effect of fine-grained strengthening. Meanwhile, through pole figure analysis of EBSD (see fig. 5 and 6), it can be seen that after two times of extrusion, a large amount of force is generated along the extrusion direction<101>And (4) silk texture. Since the most easily actuated slip system in BCC structures is (101)<111>Thereby giving the alloy better plasticity when a large number of (101) planes are parallel to the extrusion direction. This is the main reason for making it have better strength and plasticity along the extrusion direction.
Test example 2
The room temperature tensile strength and the room temperature elongation of examples 1 to 3 and comparative examples 1 to 3 were measured in accordance with the GB/T228.1-2010 room temperature tensile test standards, and the results are shown in Table 1.
TABLE 1
As can be seen from Table 1, Ti produced by the present invention2The room-temperature tensile strength of the AlNb-based alloy bar can reach more than 1250MPa, and the room-temperature elongation can reach more than 15%.
The durability of example 1 was tested according to the GB/T-2039 standard, and the results of three measurements are shown in Table 2.
The high temperature tensile properties of example 1 were tested according to GB/T-228.2, and the results of three measurements are shown in Table 3.
TABLE 2
TABLE 3
As can be seen from tables 2 and 3, the present inventionApplication of Ti obtained in example 12The AlNb-based alloy bar improves the room-temperature tensile strength and room-temperature elongation in one direction, and can meet the requirements of other comprehensive mechanical properties.
Finally, it should be noted that: the above embodiments are only used to illustrate the technical solution of the present invention, and not to limit the same; while the invention has been described in detail and with reference to the foregoing embodiments, it will be understood by those skilled in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some or all of the technical features may be equivalently replaced; and the modifications or the substitutions do not make the essence of the corresponding technical solutions depart from the scope of the technical solutions of the embodiments of the present invention.
Claims (10)
1. Ti2The preparation method of the AlNb-based alloy bar is characterized by comprising the following steps:
(A) mixing Ti2Carrying out homogenization heat treatment on the AlNb-based alloy ingot at 1160-1200 ℃ to obtain an ingot blank;
(B) carrying out heat preservation treatment on the ingot casting blank at 1130-1170 ℃, and then carrying out extrusion and drawing to obtain a primary bar blank;
(C) carrying out heat preservation treatment on the primary bar blank at 1020-1060 ℃, then cooling the bar blank along with the furnace to below 500 ℃, and discharging the bar blank;
(D) carrying out heat preservation treatment on the primary bar blank treated in the step (C) at 960-980 ℃, and then carrying out extrusion and drawing to obtain a secondary bar blank;
(E) carrying out solution heat treatment on the secondary bar billet at 970-1000 ℃, and then carrying out aging heat treatment at 780-820 ℃ to obtain Ti2AlNb-based alloy bars.
2. The Ti of claim 12The preparation method of the AlNb-based alloy bar is characterized in that in the step (A), the Ti2The diameter of the AlNb-based alloy ingot is 160-280 mm;
preferably, in the step (A), the method for preparing the alloy is realized by adopting a method of primary vacuum consumable melting, secondary vacuum skull melting and tertiary vacuum consumable meltingThe above Ti2And (4) casting an AlNb-based alloy ingot.
3. The Ti of claim 12The preparation method of the AlNb-based alloy bar is characterized in that in the step (A), the heat preservation time of the homogenization heat treatment is 35-45 h;
preferably, in the step (A), the Ti is added2And (3) carrying out heat preservation treatment on the AlNb-based alloy ingot at 1180 ℃ for 38 hours.
4. The Ti of claim 12The preparation method of the AlNb-based alloy bar is characterized in that in the step (B), the heat preservation treatment time is 2-4 h;
preferably, in the step (B), the ingot casting blank is subjected to heat preservation treatment at 1150 ℃ for 3 h;
preferably, in the step (B), the extrusion ratio of the extrusion drawing is 3-5.5: 1;
preferably, in step (B), the extrusion ratio of the extrusion elongation is 4.5: 1.
5. the Ti of claim 12The preparation method of the AlNb-based alloy bar is characterized in that in the step (C), the heat preservation treatment time is 1-3 h;
preferably, in step (C), the primary rod blank is heat-preserved at 1040 ℃ for 2 h.
6. The Ti of claim 12The preparation method of the AlNb-based alloy bar is characterized in that in the step (D), the heat preservation treatment time is 1-2 h;
preferably, in the step (D), the primary bar blank treated in the step (C) is subjected to heat preservation treatment at 970 ℃ for 1.5 h;
preferably, in the step (D), the extrusion ratio of the extrusion elongation is 3-5.5: 1;
preferably, in the step (D), the extrusion ratio of the extrusion elongation is 4: 1.
7. the Ti of claim 12AlNb radicalThe preparation method of the alloy bar is characterized in that in the step (E), the time of the solution heat treatment is 2.5-4 hours;
and/or in the step (E), the time of the aging heat treatment is more than or equal to 16 h;
preferably, in step (E), the solution heat treatment is carried out at 980 ℃ for 3 h;
and/or, in step (E), the ageing heat treatment is carried out at 800 ℃ for 24 h.
8. Use of Ti as described in any of claims 1 to 72Ti prepared by preparation method of AlNb-based alloy bar2AlNb-based alloy bars.
9. The Ti of claim 82An AlNb-based alloy bar characterized in that the Ti2The room-temperature tensile strength of the AlNb-based alloy bar is more than or equal to 1250 MPa; the Ti2The room temperature elongation of the AlNb-based alloy bar is more than or equal to 15 percent.
10. The Ti of claim 8 or 92The application of the AlNb-based alloy bar in aerospace equipment;
preferably, the aerospace device comprises an aerospace engine.
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