CN112725713A - High-strength and high-plasticity powder metallurgy titanium alloy and processing method thereof - Google Patents
High-strength and high-plasticity powder metallurgy titanium alloy and processing method thereof Download PDFInfo
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- 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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
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Abstract
The invention discloses a high-strength and high-plasticity powder metallurgy titanium alloy and a processing method thereof, belonging to the field of titanium alloys. According to the processing method, the oxygen content of the ingot blank prepared by the powder metallurgy method reaches 0.35 wt%, the high oxygen content in the ingot blank can not only influence the design of alloy forging temperature by improving the alloy phase transition point, but also obviously increase the content of alpha stable elements in the alloy so as to influence the mechanical property and the strengthening and toughening mechanism of the alloy; the high-oxygen ingot blank is subjected to three-upsetting three-pull-out forging, bar rolling and annealing heat treatment to obtain a heterogeneous layered multi-stage second-phase structure, so that the alloy has good high-strength and high-plasticity matching; the high-strength and high-plasticity powder metallurgy titanium alloy has the advantages that the inside of the high-strength and high-plasticity powder metallurgy titanium alloy is in a heterogeneous layered multi-stage second-phase structure, the structural strength of the alloy can be enhanced by the layered structure in the heterogeneous layered fine-grained structure, and the strain can be accommodated by the layered structure, so that the alloy keeps high toughness and high plasticity.
Description
Technical Field
The invention belongs to the field of titanium alloy, and particularly relates to a high-strength and high-plasticity powder metallurgy titanium alloy and a processing method thereof.
Background
The titanium alloy has the advantages of low density, high specific strength, good corrosion resistance, no magnetism and the like, and is widely applied to the industrial fields of aviation, aerospace, ocean engineering, automobiles and the like. The near-beta titanium alloy has high specific strength, can effectively reduce the structural weight, and is gradually emphasized in application.
The technical problems encountered in the development of the near-beta high-strength titanium alloy are that the strength is increased and the plasticity is reduced. To solve this technical problem, there are generally two approaches. Firstly, a novel titanium alloy is researched and developed, the content of impurity elements such as oxygen is strictly controlled, and the matching of the strength and the plasticity of the alloy is improved through a complex forging process and a high-temperature solid solution aging heat treatment process; and secondly, on the basis of the existing near-beta high-strength titanium alloy, the matching of the strength and the plasticity of the alloy is improved by changing the process path.
Disclosure of Invention
The invention aims to overcome the defects of high strength and poor plasticity of a near-beta high-strength titanium alloy and provides a high-strength and high-plasticity powder metallurgy titanium alloy and a processing method thereof.
In order to achieve the purpose, the invention adopts the following technical scheme to realize the purpose:
the processing method of the high-strength and high-plasticity powder metallurgy titanium alloy comprises the steps of performing three-upsetting three-drawing forging cogging on an ingot blank of the powder metallurgy Ti-5553 alloy at the temperature of 80-100 ℃ above a transformation point, performing three-upsetting three-drawing forging at the temperature of 50-80 ℃ below the transformation point to form a bar blank, and rolling the bar blank into a bar material by two times of heating at the temperature of 80-100 ℃ below the transformation point;
annealing the bar, keeping the temperature of 600-700 ℃ for 1h, and air-cooling to obtain a near-beta type titanium alloy;
wherein the oxygen content of the ingot blank of the powder metallurgy Ti-5553 alloy is 0.35 wt%;
the phase transition point is 975-985 ℃.
Further, the diameter of the bar blank is 30 mm.
Further, the diameter of the bar is 11 mm.
Further, the processing method of the Ti-5553 alloy ingot blank comprises the following steps:
using 325 mesh titanium powder and 250 mesh Al-30.4Mo-28.0V-16.7Cr quaternary intermediate alloy powder as raw materials, mixing to obtain Ti-5Al-5Mo-5V-3Cr, carrying out cold isostatic pressing at 250MPa for 1min, and then carrying out vacuum sintering at 1150 ℃ for 4.5h to obtain an ingot blank of the Ti-5553 alloy.
The powder metallurgy titanium alloy obtained by the processing method is a near-beta type titanium alloy.
Furthermore, the structure is in a heterogeneous layered multilevel second phase organization structure.
Furthermore, the tensile strength is 1354-1700 MPa, and the elongation is 7.2% -13%.
Compared with the prior art, the invention has the following beneficial effects:
according to the processing method of the high-strength and high-plasticity powder metallurgy titanium alloy, the oxygen content of the ingot blank prepared by the powder metallurgy method reaches 0.35 wt%, the high oxygen content in the ingot blank can not only influence the design of alloy forging temperature by improving the alloy phase transition point, but also obviously increase the content of alpha stable elements in the alloy so as to influence the mechanical property and the strengthening and toughening mechanism of the alloy; the high-oxygen ingot blank is subjected to three-upsetting three-pull-out forging, bar rolling and annealing heat treatment to obtain a heterogeneous layered multi-stage second-phase structure, so that the alloy has good high-strength and high-plasticity matching; cogging forging of three upsetting and three drawing ensures that crystal grains of the ingot blank are crushed in a large range; performing three-upsetting three-drawing forging to further refine alloy grains through recrystallization and separate out a primary second phase by combining dynamic phase change; the bar is rolled to enable the alloy to have the structure characteristic of lamellar distribution and generate a secondary second phase; finally, the third nanoscale second phase is precipitated through annealing heat treatment, and finally a heterogeneous layered multilevel second phase structure is formed in the alloy.
The high-strength and high-plasticity powder metallurgy titanium alloy has the advantages that the inside of the high-strength and high-plasticity powder metallurgy titanium alloy is in a heterogeneous layered multi-stage second-phase structure, the structural strength of the alloy can be enhanced by the layered structure in the heterogeneous layered fine-grained structure, and the strain can be accommodated by the layered structure, so that the alloy keeps high toughness and high plasticity; the multi-stage second phase (including primary, secondary and tertiary) can improve the strength of the alloy through multi-scale interface strengthening and high-oxygen solid solution strengthening effect, and simultaneously, the alloy keeps good plasticity and toughness through improving the coordinated deformation capacity and deformation accommodation capacity of the alloy.
Drawings
FIG. 1 is a view showing the microstructure of example 1;
FIG. 2 is a view showing the microstructure of example 2;
FIG. 3 is a view showing the microstructure of example 3.
Detailed Description
In order to make the technical solutions of the present invention better understood, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. 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.
It should be noted that the terms "first," "second," and the like in the description and claims of the present invention and in the drawings described above are used for distinguishing between similar elements and not necessarily for describing a particular sequential or chronological order. It is to be understood that the data so used is interchangeable under appropriate circumstances such that the embodiments of the invention described herein are capable of operation in sequences other than those illustrated or described herein. Furthermore, the terms "comprises," "comprising," and "having," and any variations thereof, are intended to cover a non-exclusive inclusion, such that a process, method, system, article, or apparatus that comprises a list of steps or elements is not necessarily limited to those steps or elements expressly listed, but may include other steps or elements not expressly listed or inherent to such process, method, article, or apparatus.
The invention is described in further detail below with reference to the accompanying drawings:
example 1
Using 325-mesh titanium powder and 250-mesh Al-30.4Mo-28.0V-16.7Cr quaternary intermediate alloy powder as raw materials, mixing to obtain Ti-5Al-5Mo-5V-3Cr (Ti-5553), performing cold isostatic pressing for 1min under 250MPa, and performing vacuum sintering for 4.5h at 1150 ℃ to obtain an ingot blank of the powder metallurgy Ti-5553 alloy;
three-upsetting three-drawing forging cogging at 1060 ℃ (80 ℃ above the transformation point), then three-upsetting three-drawing forging at 930 ℃ (50 ℃ below the transformation point) to form a bar blank with the diameter of 30mm, and then rolling the bar blank with the diameter of 11mm by two times of fire at 900 ℃ (80 ℃ below the transformation point), wherein the transformation point is 980 +/-5 ℃; annealing the bar, keeping the temperature at 600 ℃ for 1h, and air-cooling to obtain powder metallurgy near-beta type titanium alloy;
the tensile strength and elongation of the near-beta titanium alloy are 1700MPa and 7.2%, respectively.
Referring to fig. 1, fig. 1 is a microstructure diagram of a powder metallurgy near-beta titanium alloy after heat treatment of example 1, and as can be seen from fig. 1, the alloy after heat treatment is characterized by a layered heterogeneous multilevel second phase structure. Wherein the heterogeneous lamellar structure is clearly visible, and alpha phase delamination is initiated through a 'necklace shape' or a 'strip shape'. The multi-stage second phase mainly comprises a lamellar primary alpha phase, a strip-shaped grain boundary alpha phase, a fine needle-shaped secondary alpha phase and a tertiary alpha phase in a beta transition structure. Under the heat treatment condition of 600 ℃, the gaps of the layered structure are wider, the primary alpha phase presents a nearly equiaxial form, and the size of the fine needle-shaped secondary alpha phase is smaller.
Example 2
Using 325-mesh titanium powder and 250-mesh Al-30.4Mo-28.0V-16.7Cr quaternary intermediate alloy powder as raw materials, mixing to obtain Ti-5Al-5Mo-5V-3Cr (Ti-5553), performing cold isostatic pressing for 1min under 250MPa, and performing vacuum sintering for 4.5h at 1150 ℃ to obtain an ingot blank of the powder metallurgy Ti-5553 alloy;
three-upsetting three-drawing forging cogging at 1060 ℃ (80 ℃ above the transformation point), then three-upsetting three-drawing forging at 930 ℃ (50 ℃ below the transformation point) to form a bar blank with the diameter of 30mm, and then rolling the bar blank with the diameter of 11mm by two times of fire at 900 ℃ (80 ℃ below the transformation point), wherein the transformation point is 980 +/-5 ℃;
annealing the bar, keeping the temperature at 700 ℃ for 1h, and air-cooling to obtain a near-beta type titanium alloy;
the test shows that the tensile strength of the near-beta titanium alloy is 1354MPa, and the elongation is 13%.
Referring to fig. 2, fig. 2 is a microstructure diagram of the powder metallurgy near-beta titanium alloy of the example 2 after heat treatment, and as can be seen from fig. 2, the alloy after heat treatment has the characteristic of a layered heterogeneous multilevel second phase structure. Wherein the heterogeneous lamellar structure is clearly visible, and alpha phase delamination is initiated through a 'necklace shape' or a 'strip shape'. The multi-stage second phase mainly comprises a lamellar primary alpha phase, a strip-shaped grain boundary alpha phase, a fine needle-shaped secondary alpha phase and a tertiary alpha phase in a beta transition structure. Under the condition of 700 ℃ heat treatment, the proportion of the strip-shaped primary alpha phase is obviously improved, the fine needle-shaped secondary alpha phase is obviously coarsened, the fine needle-shaped secondary alpha phase is in a multidirectional growth mode, and the boundary of the primary alpha phase and the secondary alpha phase becomes fuzzy.
Example 3
Using 325-mesh titanium powder and 250-mesh Al-30.4Mo-28.0V-16.7Cr quaternary intermediate alloy powder as raw materials, mixing to obtain Ti-5Al-5Mo-5V-3Cr (Ti-5553), performing cold isostatic pressing for 1min under 250MPa, and performing vacuum sintering for 4.5h at 1150 ℃ to obtain an ingot blank of the powder metallurgy Ti-5553 alloy;
three-upsetting three-drawing forging cogging at 1060 ℃ (80 ℃ above the transformation point), then three-upsetting three-drawing forging at 930 ℃ (50 ℃ below the transformation point) to form a bar blank with the diameter of 30mm, and then rolling the bar blank with the diameter of 11mm by two times of fire at 900 ℃ (80 ℃ below the transformation point), wherein the transformation point is 980 +/-5 ℃;
annealing the bar, keeping the temperature at 660 ℃ for 1h, and air-cooling to obtain powder metallurgy near-beta type titanium alloy;
the tensile strength of the near-beta titanium alloy is 1486MPa, and the elongation is 9.0%.
Referring to fig. 3, fig. 3 is a microstructure diagram of the powder metallurgy near-beta titanium alloy of the example 3 after heat treatment, and as can be seen from fig. 3, the alloy after heat treatment has the characteristic of a layered heterogeneous multilevel second phase structure. Wherein the heterogeneous lamellar structure is clearly visible, and alpha phase delamination is initiated through a 'necklace shape' or a 'strip shape'. The multi-stage second phase mainly comprises a lamellar primary alpha phase, a strip-shaped grain boundary alpha phase, a fine needle-shaped secondary alpha phase and a tertiary alpha phase in a beta transition structure. Under the condition of 660 ℃ heat treatment, the gaps of the layered structure are obviously reduced, the proportion of the primary alpha phase is increased, the short strip shape at 600 ℃ is changed into a continuous strip shape, and the fine needle-shaped secondary alpha phase is obviously coarsened.
The above-mentioned contents are only for illustrating the technical idea of the present invention, and the protection scope of the present invention is not limited thereby, and any modification made on the basis of the technical idea of the present invention falls within the protection scope of the claims of the present invention.
Claims (7)
1. A processing method of a high-strength and high-plasticity powder metallurgy titanium alloy is characterized in that an ingot blank of the powder metallurgy Ti-5553 alloy is subjected to three-upsetting three-drawing forging cogging at a temperature of 80-100 ℃ above a transformation point, then is subjected to three-upsetting three-drawing forging at a temperature of 50-80 ℃ below the transformation point to form a bar blank, and then is subjected to two-fire-time rolling at a temperature of 80-100 ℃ below the transformation point to form a bar;
annealing the bar, keeping the temperature of 600-700 ℃ for 1h, and air-cooling to obtain a powder metallurgy near-beta titanium alloy;
wherein the oxygen content of the ingot blank of the powder metallurgy Ti-5553 alloy is 0.35 wt%;
the phase transition point is 975-985 ℃.
2. The method of claim 1, wherein the billet has a diameter of 30 mm.
3. The method of claim 1, wherein the diameter of the rod is 11 mm.
4. The method for processing the high-strength and high-plasticity powder metallurgy titanium alloy according to claim 1, wherein the method for processing the ingot blank of the Ti-5553 alloy comprises the following steps:
using 325 mesh titanium powder and 250 mesh Al-30.4Mo-28.0V-16.7Cr quaternary intermediate alloy powder as raw materials, mixing to obtain Ti-5Al-5Mo-5V-3Cr, carrying out cold isostatic pressing at 250MPa for 1min, and then carrying out vacuum sintering at 1150 ℃ for 4.5h to obtain an ingot blank of the Ti-5553 alloy.
5. A powder metallurgy titanium alloy obtainable by the process according to any one of claims 1 to 4, characterized by being a near- β titanium alloy.
6. The powder metallurgy titanium alloy of claim 5, having a heterogeneous layered multilevel second phase structure.
7. The powder metallurgy titanium alloy according to claim 5, wherein the tensile strength is 1354-1700 MPa, and the elongation is 7.2-13%.
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