CN118006966A - Metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and preparation method thereof - Google Patents
Metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and preparation method thereof Download PDFInfo
- Publication number
- CN118006966A CN118006966A CN202410245984.3A CN202410245984A CN118006966A CN 118006966 A CN118006966 A CN 118006966A CN 202410245984 A CN202410245984 A CN 202410245984A CN 118006966 A CN118006966 A CN 118006966A
- Authority
- CN
- China
- Prior art keywords
- titanium alloy
- induced
- solid solution
- solution strengthening
- interstitial oxygen
- 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.)
- Pending
Links
- 239000000956 alloy Substances 0.000 title claims abstract description 59
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 58
- 229910001040 Beta-titanium Inorganic materials 0.000 title claims abstract description 32
- 229910052760 oxygen Inorganic materials 0.000 title claims abstract description 32
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 title claims abstract description 29
- 239000001301 oxygen Substances 0.000 title claims abstract description 29
- 238000005728 strengthening Methods 0.000 title claims abstract description 29
- 239000006104 solid solution Substances 0.000 title claims abstract description 27
- 230000007704 transition Effects 0.000 title claims abstract description 15
- 238000002360 preparation method Methods 0.000 title claims abstract description 13
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 46
- 238000002844 melting Methods 0.000 claims abstract description 27
- 230000008018 melting Effects 0.000 claims abstract description 27
- 238000005098 hot rolling Methods 0.000 claims abstract description 15
- 239000010936 titanium Substances 0.000 claims abstract description 14
- 239000012535 impurity Substances 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 10
- 239000000243 solution Substances 0.000 claims abstract description 9
- 238000005097 cold rolling Methods 0.000 claims abstract description 7
- 238000000137 annealing Methods 0.000 claims abstract description 3
- 230000009466 transformation Effects 0.000 claims description 22
- 238000001816 cooling Methods 0.000 claims description 20
- 238000010791 quenching Methods 0.000 claims description 16
- 230000000171 quenching effect Effects 0.000 claims description 16
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 12
- 238000000034 method Methods 0.000 claims description 8
- 239000002994 raw material Substances 0.000 claims description 7
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 6
- 238000004321 preservation Methods 0.000 claims description 6
- 238000003825 pressing Methods 0.000 claims description 6
- 238000005096 rolling process Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims 4
- 230000035515 penetration Effects 0.000 claims 1
- 238000005482 strain hardening Methods 0.000 abstract description 17
- 230000000694 effects Effects 0.000 abstract description 16
- 230000000052 comparative effect Effects 0.000 description 11
- 230000015572 biosynthetic process Effects 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000007769 metal material Substances 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 238000010998 test method Methods 0.000 description 4
- 238000005275 alloying Methods 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 230000004075 alteration Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
- C22B9/20—Arc remelting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
-
- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- 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)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Plasma & Fusion (AREA)
- Manufacturing & Machinery (AREA)
- Composite Materials (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention provides a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and a preparation method thereof. The titanium alloy comprises the following elements in percentage by mass: 18-20% of V, 0.15-0.4% of O, and the balance of Ti and trace impurity elements; the preparation method of the titanium alloy comprises the steps of vacuum arc melting, vacuum homogenizing annealing, hot rolling, cold rolling, vacuum solution heat treatment and the like. The titanium alloy provided by the invention improves the solid solution strengthening effect by introducing interstitial oxygen element on one hand, and simultaneously obtains high yield strength and high work hardening capacity by adjusting and controlling a deformation mechanism and utilizing stress-induced omega phase transition to excite the phase transition to induce the plasticity effect on the other hand. The yield strength of the titanium alloy exceeds 500MPa, the tensile strength exceeds 784MPa, and meanwhile, the titanium alloy still has excellent plasticity and work hardening capacity, and can be potentially applied to novel aeroengine gear boxes, landing gears and hydraulic system components.
Description
Technical Field
The invention belongs to the technical field of titanium alloy materials, and particularly relates to a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress-induced omega phase transformation induced plasticity and a preparation method thereof.
Background
The titanium alloy has the advantages of high specific strength, good corrosion resistance and the like, and the application of the titanium alloy on an aviation structural member can realize remarkable structural weight reduction, thereby being beneficial to improving the maneuverability and the fuel efficiency of an airplane. In recent years, there has been a great deal of attention to metastable beta titanium alloys having the transformation-induced plasticity (transformation-induced plasticity) effect and/or the twinning-induced plasticity (TWIP) effect. A great number of researches show that the TRIP and/or TWIP effect is introduced into metastable beta titanium alloy by regulating and controlling the stability of the beta matrix, so that the work hardening capacity and plasticity of the alloy can be greatly improved. Notably, however, the TRIP effect in most metastable beta titanium alloys is stimulated by stress induced beta- > alpha' -martensitic transformation. Because of the low critical cutting stress of beta- & gtalpha '' -martensitic transformation, the alloy starts to generate nonlinear deformation at a very low strength level (generally lower than 400 MPa), and the engineering application of the alloy is severely limited.
Obviously, if the stress-induced beta- & gtomega phase transition which can excite the TRIP effect can be introduced into metastable beta titanium alloy, and meanwhile, interstitial oxygen with obvious solid solution strengthening effect is added to further improve the critical slitting stress, the defect that the nonlinear deformation critical stress of the traditional TRIP titanium alloy is low can be overcome, and therefore, the TRIP titanium alloy is expected to have higher strength on the basis of keeping excellent plasticity and work hardening capacity of the TRIP titanium alloy.
Disclosure of Invention
Considering that most TRIP titanium alloys begin to deform nonlinearly at very low strength levels (generally lower than 400 MPa), engineering application of the alloys is severely limited, so that research and development of a metastable beta titanium alloy which remarkably improves solid solution strengthening effect by utilizing interstitial oxygen elements and has stress-induced beta- & omega phase transition induced plasticity effect is a key way for solving the problem. The titanium alloy can be potentially applied to novel aeroengine gear boxes, landing gears and hydraulic system components.
In the composition design of metastable beta titanium alloys, including but not limited to, controlling the content of the main alloying element V and the remaining alloying elements within a specific interval, atoms on the {112} plane of the beta matrix portion may be subject to dislocation along the <111> direction during deformation, thereby causing stress-induced beta- > omega phase transformation of the alloy. The formation of stress-induced omega phase can inhibit stress-induced beta- & gtalpha '' martensitic transformation with lower critical splitting stress, and can effectively block dislocation slip and excite TRIP effect, so that the strength and work hardening capacity of the corresponding alloy can be obviously improved. In addition, adding an appropriate amount of oxygen element to the metastable beta titanium alloy does not completely inhibit the TRIP/TWIP effect of the alloy while improving the strength level of the alloy, and therefore, does not greatly reduce the plasticity and work hardening capacity of the alloy.
Based on the above consideration, the invention provides a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transformation induced plasticity and a preparation method thereof, aiming at the problem that the nonlinear deformation critical stress of the existing TRIP titanium alloy is low.
Specifically, the first aspect of the invention provides a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transformation induced plasticity, wherein the titanium alloy comprises the following elements in percentage by mass: 18-20% of V, 0.15-0.4% of O, and the balance of Ti and trace impurity elements.
As a further explanation of the invention, the sum of 0.67 times of the mass percent value of the V element and 2.9 times of the mass percent value of the substitution impurity Fe element in the titanium alloy is within the range of 10-13, so that the titanium alloy can obtain a beta phase with lower 100% stability after solution quenching within the temperature range of the beta phase region.
As a further explanation of the present invention, the mass percentages of the interstitial impurity elements H, N, C in the titanium alloy are respectively lower than 0.01%, 0.055% and 0.05% to ensure that the dislocation of atoms on the {112} plane of the portion involved in the stress-induced beta- > omega phase transition of the titanium alloy along the <111> direction is not completely blocked by the interstitial impurity atoms.
As a further illustration of the invention, the titanium alloy consists of 100% beta phase and produces a stress induced omega phase in the plastic deformation phase {332} <113> deforming twinning.
The second aspect of the present invention provides a method for preparing the metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced ω phase transformation induced plasticity, comprising the steps of:
S1, taking pure Ti, pure V and pure TiO 2 as raw materials, and obtaining a finished product ingot through vacuum arc melting;
s2, carrying out vacuum homogenizing annealing treatment on the finished cast ingot;
s3, hot rolling the cast ingot processed in the step S2, water-cooling and quenching to room temperature after the hot rolling is finished, and then carrying out multi-pass cold rolling on the hot rolled plate;
S4, performing vacuum solution heat treatment on the obtained cold-rolled sheet, and performing water-cooling quenching to room temperature after the solution treatment is completed, so as to complete the preparation of the alloy.
As a further explanation of the present invention, in S1, high purity Ti, high purity V and high purity TiO 2 having a purity of not less than 99.95% are used as raw materials, and the ingredients are formulated according to the mass percentages of the respective elements; the vacuum arc melting is carried out in a vacuum arc melting furnace, and the vacuum state is kept in the furnace all the time in the melting process; the vacuum arc melting is repeated for 3-5 times, and after each melting is completed, the alloy ingot is turned over to perform the next melting.
As a further explanation of the present invention, in S2, the obtained finished ingot is placed in an atmosphere having a vacuum degree of more than 3.5X10 - 4 Pa, kept at 1050℃for 12 hours or more, and then cooled to room temperature with a furnace.
As a further explanation of the invention, in S3, firstly, the cast ingot processed in S2 is placed in an environment with the vacuum degree higher than 3.5 multiplied by 10 -4 Pa, the temperature is raised along with the furnace, the heat is preserved for more than 30 minutes at 900 ℃, then, a double-roller plate and strip mill is adopted for one-time rolling, the deformation is 40% -60%, and after the hot rolling is finished, the cast ingot is quenched to the room temperature through water cooling; and then, carrying out multi-pass rolling on the hot rolled plate by using a double-roller plate and strip mill at room temperature, wherein the roll pressing amount of each pass is not more than 0.3mm, and the total deformation amount is 60% -70%.
As a further explanation of the invention, in S4, the cold-rolled sheet obtained in S3 is subjected to heat preservation at 830-900 ℃ for 30min in an environment with a vacuum degree higher than 1X 10 -3 Pa, and then is subjected to water cooling quenching to room temperature.
As a further explanation of the present invention, in S4, the solution heat treatment is performed at a temperature at which an equiaxed beta grain structure having an average grain size in the range of 50 μm to 150 μm is obtained.
Compared with the prior art, the invention has the following beneficial technical effects:
The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transformation induced plasticity prepared by the method disclosed by the invention introduces stress induced omega phase transformation with higher critical slitting stress into the metastable beta titanium alloy through reasonable regulation and control of beta stable element V and interstitial oxygen element content, so that the alloy has improved strength while exhibiting TRIP effect. The alloy has yield strength exceeding 500MPa and tensile strength exceeding 784MPa, the elongation at break still reaches more than 35%, the yield ratio is not more than 0.654, the maximum work hardening rate in the plastic deformation stage exceeds 1700MPa, good strength plastic matching and excellent work hardening capacity are shown, and the alloy can be potentially applied to novel aeroengine gear boxes, landing gears and hydraulic system components.
Drawings
FIG. 1 is a back-scattered electron image of the initial structure of the titanium alloy prepared in examples 1 to 3 and comparative example 4 according to the present invention.
Fig. 2 is a graph showing an example of room temperature tensile engineering stress-engineering strain curve of the titanium alloy prepared in examples 1 to 3 and comparative example 4 according to the present invention.
FIG. 3 is a graph showing an example of room temperature tensile work hardening rate-true strain curve of the titanium alloy prepared in examples 1 to 3 and comparative example 4 according to the present invention.
Fig. 4 is an electron back scattering diffraction pattern of deformed structure of the titanium alloy prepared in examples 1 to 3 and comparative example 4 according to the present invention.
Detailed Description
The following description of the embodiments of the present invention will be made clearly and completely with reference to the accompanying drawings, in which it is apparent that the embodiments described are only some embodiments of the present invention, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
Example 1
The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity comprises the following main elements in percentage by mass: 19.26% V,0.16% O,0.002% H,0.019% N,0.014% C,0.012% Fe, the balance being Ti and unavoidable impurity elements.
The preparation method of the metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transformation induced plasticity comprises the following steps:
s1, taking high-purity Ti with the purity of 99.995%, high-purity V with the purity of 99.95% and high-purity TiO 2 with the purity of 99.99% as raw materials, obtaining a finished product ingot through vacuum arc melting, repeating the melting for 5 times, and turning over the alloy ingot for the next melting after each melting is completed;
S2, placing the obtained finished cast ingot in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, homogenizing for 12 hours at 1050 ℃, and then cooling to room temperature along with a furnace;
S3, placing the cast ingot processed in the S2 in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, heating along with a furnace, preserving heat at 900 ℃ for 30min, performing primary hot rolling by adopting a double-roller plate and strip mill, wherein the total deformation is 40.93%, and performing water cooling quenching to room temperature after the hot rolling is finished. Then a double-roller plate and strip mill is used for carrying out multi-pass cold rolling on the hot rolled plate, the roll pressing amount of each pass is 0.3mm, and the total deformation amount is 67.86%;
And S4, carrying out heat preservation on the cold-rolled sheet obtained in the step S3 for 30min at 830 ℃ in an environment with the vacuum degree of 1X 10 -3 Pa, and then carrying out water cooling quenching to room temperature.
The initial structure of the titanium alloy prepared in this example was characterized using a scanning electron microscope, as shown in fig. 1. As can be seen from the figure, the initial structure of the titanium alloy prepared in this example is mainly characterized by equiaxed β -phase grains, no other structural phase formation is observed at the micrometer scale, and the average grain size is 104.2±2.2 μm.
According to GB/T228.1-2010 section 1 Metal Material tensile test: the room temperature test method measures the mechanical properties of the titanium alloy prepared in the embodiment, the engineering stress-engineering strain curve is shown in figure 2, the work hardening rate curve is shown in figure 3, and the result shows that the yield strength is 535MPa, the tensile strength is 784MPa, the elongation at break is 43%, the yield ratio is 0.638, and the maximum work hardening rate in the plastic deformation stage reaches 1890MPa.
The deformation structure of the titanium alloy prepared in this example was characterized by electron back-scattering diffraction using a scanning electron microscope, as shown in fig. 4, and it can be seen from the figure that stress-induced ω -phase and {332} <113> deformation twins were generated during the alloy deformation.
Example 2
The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity comprises the following main elements in percentage by mass: 19.10% V,0.28% O,0.002% H,0.003% N,0.013% C,0.009% Fe, the balance being Ti and unavoidable impurity elements.
The preparation method of the metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transformation induced plasticity comprises the following steps:
s1, taking high-purity Ti with the purity of 99.995%, high-purity V with the purity of 99.95% and high-purity TiO 2 with the purity of 99.99% as raw materials, obtaining a finished product ingot through vacuum arc melting, repeating the melting for 5 times, and turning over the alloy ingot for the next melting after each melting is completed;
S2, placing the obtained finished cast ingot in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, homogenizing for 12 hours at 1050 ℃, and then cooling to room temperature along with a furnace;
S3, placing the cast ingot processed in the S2 in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, heating along with a furnace, preserving heat at 900 ℃ for 30min, performing primary hot rolling by adopting a double-roller plate and strip mill, wherein the total deformation is 55.14%, and performing water cooling quenching to room temperature after the hot rolling is finished. And then carrying out multi-pass cold rolling on the hot rolled plate by using a double-roller plate and strip rolling mill, wherein the roll pressing amount of each pass is 0.3mm, and the total deformation amount is 63.86%. ;
And S4, carrying out heat preservation for 30min at 875 ℃ on the cold-rolled sheet obtained in the step S3 in an environment with the vacuum degree of 1X 10 -3 Pa, and then carrying out water cooling quenching to room temperature.
The initial structure of the titanium alloy prepared in this example was characterized using a scanning electron microscope, as shown in fig. 1. As can be seen from the figure, the initial structure of the titanium alloy prepared in this example is mainly characterized by equiaxed β -phase grains, no other structural phase formation is observed at the micrometer scale, and the average grain size is 104.6±1.6 μm.
According to GB/T228.1-2010 section 1 Metal Material tensile test: the room temperature test method measures the mechanical properties of the titanium alloy prepared in the embodiment, the engineering stress-engineering strain curve is shown in figure 2, the work hardening rate curve is shown in figure 3, the result shows that the yield strength is 526MPa, the tensile strength is 797MPa, the elongation after fracture is 41%, the yield ratio is 0.654, and the maximum work hardening rate in the plastic deformation stage reaches 2109MPa.
The deformation structure of the titanium alloy prepared in this example was characterized by electron back-scattering diffraction using a scanning electron microscope, as shown in fig. 4, and it can be seen from the figure that stress-induced ω -phase and {332} <113> deformation twins were generated during the alloy deformation.
Example 3
The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity comprises the following main elements in percentage by mass: 19.07% v,0.37% o,0.002% h,0.051% n,0.018% c,0.009% fe, the balance being Ti and unavoidable impurity elements.
The preparation method of the metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transformation induced plasticity comprises the following steps:
s1, taking high-purity Ti with the purity of 99.995%, high-purity V with the purity of 99.95% and high-purity TiO 2 with the purity of 99.99% as raw materials, obtaining a finished product ingot through vacuum arc melting, repeating the melting for 5 times, and turning over the alloy ingot for the next melting after each melting is completed;
S2, placing the obtained finished cast ingot in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, homogenizing for 12 hours at 1050 ℃, and then cooling to room temperature along with a furnace;
s3, placing the cast ingot processed in the S2 in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, heating along with a furnace, preserving heat at 900 ℃ for 30min, performing primary hot rolling by adopting a double-roller plate and strip mill, wherein the total deformation amount is 40.60%, and performing water cooling quenching to room temperature after the hot rolling is finished. And then carrying out multi-pass cold rolling on the hot rolled plate by using a double-roller plate and strip mill, wherein the roll pressing amount of each pass is 0.3mm, and the total deformation amount is 67.63%. ;
And S4, carrying out heat preservation for 30min at 860 ℃ on the cold-rolled sheet obtained in the step S3 in an environment with the vacuum degree of 1X 10 -3 Pa, and then carrying out water cooling quenching to room temperature.
The initial structure of the titanium alloy prepared in this example was characterized using a scanning electron microscope, as shown in fig. 1. As can be seen from the figure, the initial structure of the titanium alloy prepared in this example is mainly characterized by equiaxed β -phase grains, no other structural phase formation is observed on the micrometer scale, and the average grain size is 103.8±1.3 μm.
According to GB/T228.1-2010 section 1 Metal Material tensile test: the room temperature test method measures the mechanical properties of the titanium alloy prepared in the embodiment, the engineering stress-engineering strain curve is shown in figure 2, the work hardening rate curve is shown in figure 3, the result shows that the yield strength is 596MPa, the tensile strength is 839MPa, the elongation after fracture is 36%, the yield ratio is 0.635, and the maximum work hardening rate in the plastic deformation stage reaches 1720MPa.
The deformation structure of the titanium alloy prepared in this example was characterized by electron back-scattering diffraction using a scanning electron microscope, as shown in fig. 4, and it can be seen from the figure that stress-induced ω -phase and {332} <113> deformation twins were generated during the alloy deformation.
Comparative example 4
The titanium alloy provided by the comparative example comprises the following main elements in percentage by mass: 12.14% Mo,0.042% O,0.0008% H,0.003% N,0.021% Fe, the balance being Ti and unavoidable impurity elements.
The preparation method of the alloy comprises the following steps:
S1, taking high-purity Ti with the purity of 99.99% and high-purity TiMo 32 intermediate alloy with the purity of 99.95% as raw materials, obtaining a finished product ingot through vacuum arc melting, repeating the melting for 5 times, and turning over the alloy ingot for the next melting after each melting is completed;
S2, placing the obtained finished cast ingot in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, homogenizing for 12 hours at 1050 ℃, and then cooling to room temperature along with a furnace;
S3, placing the cast ingot processed in the S2 in an environment with the vacuum degree of 3.5 multiplied by 10 -4 Pa, heating along with a furnace, preserving heat at 900 ℃ for 30min, performing primary hot rolling by adopting a double-roller plate and strip mill, wherein the total deformation amount is 50%, and performing water cooling quenching to room temperature after the hot rolling is finished. And then carrying out multi-pass cold rolling on the hot rolled plate by using a double-roller plate and strip rolling mill, wherein the roll pressing amount of each pass is 0.3mm, and the total deformation amount is 35%. ;
And S4, carrying out heat preservation on the cold-rolled sheet obtained in the step S3 for 30min at 905 ℃ in an environment with the vacuum degree of 1X 10 -3 Pa, and then carrying out water cooling quenching to room temperature.
The initial structure of the titanium alloy prepared in this comparative example was characterized by using a scanning electron microscope, as shown in fig. 1. As can be seen from the figure, the initial structure of the titanium alloy prepared in this comparative example is mainly characterized by equiaxed β -phase grains, no other structural phase formation is observed at the micrometer scale, and the average grain size is about 100 μm.
According to GB/T228.1-2010 section 1 Metal Material tensile test: the room temperature test method measures the mechanical properties of the titanium alloy prepared in the comparative example, the engineering stress-engineering strain curve is shown in figure 2, the work hardening rate curve is shown in figure 3, and the result shows that the yield strength is 480MPa, the tensile strength is 682MPa, the elongation at break is 53%, the yield ratio is 0.704, and the maximum work hardening rate in the plastic deformation stage reaches 2128MPa.
The deformation structure of the titanium alloy prepared in this comparative example was characterized by electron back-scattering diffraction using a scanning electron microscope, as shown in fig. 4, and it can be seen from the figure that {332} <113> deformation twins and stress-induced α martensite were generated during the alloy deformation.
Compared with examples 1-3, although the same preparation process was adopted, the composition of the titanium alloy described in comparative example 4 was not within the scope of the present application, which resulted in significantly weaker solution strengthening effect and failure to produce stress-induced ω transformation induced plasticity effect during deformation, so that the nonlinear deformation critical stress was lower and exhibited lower strength level.
It should be noted that in this document, terms such as "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
Although embodiments of the present invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made therein without departing from the principles and spirit of the invention, the scope of which is defined in the appended claims and their equivalents.
Claims (10)
1. A metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity is characterized in that the element composition and mass percent of the titanium alloy are as follows: 18-20% of V, 0.15-0.4% of O, and the balance of Ti and trace impurity elements.
2. The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced ω transformation induced plasticity according to claim 1, wherein the sum of 0.67 times the mass percent value of the V element and 2.9 times the mass percent value of the substitutional impurity Fe element in the titanium alloy is in the range of 10-13.
3. The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced ω transformation induced plasticity according to claim 1, wherein the mass percent of interstitial impurity elements H, N, C in the titanium alloy is less than 0.01%, 0.055%, 0.05%, respectively.
4. The metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced ω phase transformation induced plasticity of claim 1, wherein the titanium alloy consists of 100% β phase and generates a stress induced ω phase {332} <113> deformed twinning during plastic deformation phase.
5. A method of preparing a metastable beta titanium alloy in combination with interstitial oxygen solid solution strengthening and stress induced ω transformation induced plasticity as defined in any one of claims 1-4, comprising the steps of:
S1, taking pure Ti, pure V and pure TiO 2 as raw materials, and obtaining a finished product ingot through vacuum arc melting;
s2, carrying out vacuum homogenizing annealing treatment on the finished cast ingot;
s3, hot rolling the cast ingot processed in the step S2, water-cooling and quenching to room temperature after the hot rolling is finished, and then carrying out multi-pass cold rolling on the hot rolled plate;
S4, performing vacuum solution heat treatment on the obtained cold-rolled sheet, and performing water-cooling quenching to room temperature after the solution treatment is completed, so as to complete the preparation of the alloy.
6. The method for producing a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced ω transformation induced plasticity according to claim 5, wherein in S1, vacuum arc melting is repeated 3 to 5 times, and after each melting, the alloy ingot is turned over to perform the next melting.
7. The method for producing a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity according to claim 5, wherein in S2, the obtained finished ingot is placed in an environment with a vacuum degree higher than 3.5 x 10 -4 Pa, kept at 1050 ℃ for more than 12 hours, and then cooled to room temperature with a furnace.
8. The method for preparing metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity according to claim 5, wherein in S3, firstly placing the cast ingot treated in S2 in an environment with vacuum degree higher than 3.5 multiplied by 10 -4 Pa, heating along with a furnace, preserving heat at 900 ℃ for more than 30min for heat penetration, then adopting a double-roller plate and strip mill to perform one-pass rolling, wherein the deformation is 40% -60%, and performing water cooling quenching to room temperature after the completion of hot rolling; and then, carrying out multi-pass rolling on the hot rolled plate by using a double-roller plate and strip mill at room temperature, wherein the roll pressing amount of each pass is not more than 0.3mm, and the total deformation amount is 60% -70%.
9. The method for producing a metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity according to claim 5, wherein in S4, the cold-rolled sheet obtained by the treatment in S3 is subjected to heat preservation at 830 ℃ to 900 ℃ for 30min in an environment with a vacuum degree higher than 1 x 10 -3 Pa, and then is subjected to water cooling quenching to room temperature.
10. The method for producing a metastable beta titanium alloy in combination with interstitial oxygen solid solution strengthening and stress induced ω phase transformation induced plasticity according to claim 5, wherein in S4, the temperature of the solution heat treatment is maintained at a temperature to obtain a structure characterized by equiaxed beta grains having an average grain size in the range of 50 μm to 150 μm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410245984.3A CN118006966A (en) | 2024-03-05 | 2024-03-05 | Metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410245984.3A CN118006966A (en) | 2024-03-05 | 2024-03-05 | Metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN118006966A true CN118006966A (en) | 2024-05-10 |
Family
ID=90947007
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202410245984.3A Pending CN118006966A (en) | 2024-03-05 | 2024-03-05 | Metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN118006966A (en) |
-
2024
- 2024-03-05 CN CN202410245984.3A patent/CN118006966A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP0683242B1 (en) | Method for making titanium alloy products | |
| WO2023093464A1 (en) | High-entropy austenitic stainless steel, and preparation method therefor | |
| WO2012032610A1 (en) | Titanium material | |
| JPS6289855A (en) | High strength ti alloy material having superior workability and its manufacture | |
| CN109154051A (en) | TWIP steel plate with austenitic matrix | |
| US4108687A (en) | Process for improving the heat resistance of zirconium and its alloys | |
| CN113862512B (en) | Processing and manufacturing method of novel high-strength and high-toughness high-temperature titanium alloy with two-state structure | |
| CN114990382B (en) | Ultra-low-gap phase transition induced plasticity metastable beta titanium alloy and preparation method thereof | |
| US8137488B2 (en) | Method of producing a flat zirconium alloy product, flat product thus obtained and a nuclear plant reactor grid which is made from said flat product | |
| JPH01252747A (en) | High strength titanium material having excellent ductility and its manufacture | |
| KR101630403B1 (en) | Manufacture method of nuclear fuel component made of zirconium applied multi-stage cold rolling | |
| US5092940A (en) | Process for production of titanium and titanium alloy material having fine equiaxial microstructure | |
| KR101265261B1 (en) | Zirconium alloy manufacturing method having excellent corrosion resistance and high strength | |
| US5417779A (en) | High ductility processing for alpha-two titanium materials | |
| CN114480811B (en) | High-strength-plastic product medium manganese steel with gradient structure and preparation method thereof | |
| CN118006966A (en) | Metastable beta titanium alloy combining interstitial oxygen solid solution strengthening and stress induced omega phase transition induced plasticity and preparation method thereof | |
| CN112853230B (en) | Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof | |
| CN112662932B (en) | TWIP steel and preparation method thereof | |
| CN114086086A (en) | Nano-phase carbon-nitrogen composite particle enhanced invar alloy wire and preparation method thereof | |
| CN107723510B (en) | High-strength and high-plasticity β titanium alloy with TRIP/TWIP effect and preparation method thereof | |
| CN116397131A (en) | High-strength high-plasticity metastable beta titanium alloy reinforced by oxygen element and preparation method thereof | |
| US2319538A (en) | Heat treatment of copper-chromium alloy steels | |
| CN115786832B (en) | Method for improving high Jiang Yawen beta titanium alloy strong plasticity matching and titanium alloy | |
| JP2016509628A (en) | Zirconium alloy processing method, zirconium alloy obtained by the method, and nuclear reactor component comprising the alloy | |
| CN117248130A (en) | Preparation method of quick strain hardening double-yield metastable beta titanium alloy |
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 |