CN112410698B - Three-phase Ti2AlNb alloy multilayer structure uniformity control method - Google Patents
Three-phase Ti2AlNb alloy multilayer structure uniformity control method Download PDFInfo
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Abstract
The invention relates to a three-phase Ti2The AlNb alloy multilayer structure uniformity control method comprises the step of mixing Ti2The AlNb alloy ingot is extruded and cogging to obtain fully crushed B2 phaseA bar blank; carrying out B2 phase recrystallization heat treatment on the bar blank to obtain a bar blank with a uniformly refined metastable B2 phase structure; then the bar blank is processed by heat preservation, and is heated to 950 ℃ to 1000 ℃ for heat preservation, and finally the bar blank is quenched to obtain alpha2The phases are uniformly dispersed in the bar blank of the B2 phase matrix structure; will be alpha2The bar blank with the phase evenly dispersed and distributed in the B2 phase matrix structure is subjected to heat preservation treatment at 550-650 ℃, then is heated to 700-850 ℃ for heat preservation treatment, and finally is cooled to obtain the bar blank with O phase and alpha phase2The alloy material is uniformly dispersed and distributed in a B2 phase matrix structure. The invention comprehensively solves the problems of matrix B2 phase and high-temperature precipitated phase alpha in the alloy structure2The distribution uniformity of three organization composition phases of the phase and the low-temperature precipitated phase O phase.
Description
Technical Field
The invention belongs to the field of titanium alloy structure control, and relates to three-phase Ti2A method for controlling the homogeneity of an AlNb alloy multi-layer structure.
Background
Ti2The AlNb alloy is a light high-temperature-resistant structural material with excellent comprehensive performance, has high strength, good heat-resistant performance, fatigue resistance, ignition resistance and certain process plasticity, is expected to replace nickel-based high-temperature alloy to realize great weight reduction of weapons, and is a key material for promoting upgrading of aeroengines and aerospace flight.
Ti2The AlNb alloy has the characteristics of high alloying degree, difficult control of component uniformity, narrow phase zone temperature, complex phase change, multiple structural layers, large deformation resistance, narrow window and the like, so that the structural uniformity of the AlNb alloy needs to be effectively controlled in a layered and targeted manner. For the uniformity control of the matrix B2 phase, the current technical means is to perform upset-draw forging on an alloy ingot for multiple times above the B2 transformation point, and gradually refine and homogenize a coarse B2 phase structure by utilizing the principle of deformation dynamic recrystallization. But is limited by the high deformation resistance and narrow process window of the alloy, has limited deformation amount of free upsetting and is easy to crack, resulting in uniform refinement of the B2 phaseThe effect is not ideal. For high temperature precipitated phase alpha2At present, no special targeted technical means exist for controlling the uniformity of the phase and the O phase of the low-temperature precipitated phase, and researchers generally think that the uniformity of the distribution of the two phases during precipitation is mainly influenced by the uniformity of the compositions of alloy micro-regions, so the problem is solved by improving the uniformity of the compositions of the alloy. But Ti2The characteristics of high alloying and narrow phase zone of the AlNb alloy are more prominent in the technical problem of controlling the uniformity of the compositions of the micro-zone, and for the high alloying alloy with the alloy element content of nearly 50 percent, the competition of precipitated phase nucleation and growth is extremely strong, and even if the uniformity of the compositions of the micro-zone is further improved, the distribution of the precipitated phase is difficult to be uniform. Thus, for three phases of Ti2AlNb alloy, either as a matrix B2 phase or as a high-temperature precipitated phase alpha2The phase is also a low-temperature precipitated phase O phase, and the prior art means can not completely realize homogenization control.
Disclosure of Invention
In view of the above-mentioned circumstances of the prior art, it is an object of the present invention to provide a three-phase Ti2A method for controlling the uniformity of a multi-layer structure of an AlNb alloy, which aims to comprehensively solve the problems of a matrix B2 phase and a high-temperature precipitated phase alpha in an alloy structure2The distribution uniformity of three organization composition phases of the phase and the low-temperature precipitated phase O phase.
The above object of the present invention is achieved by the following technical solutions:
three-phase Ti2The AlNb alloy multilayer structure uniformity control method comprises the following steps:
step 1: mixing Ti2Extruding and cogging the AlNb alloy cast ingot to obtain a B2 phase fully-crushed bar blank;
step 2: carrying out B2 phase recrystallization heat treatment on the obtained B2 phase fully-crushed bar blank at 1050-1080 ℃ for a predetermined time, and then quenching to obtain a bar blank with a uniformly refined metastable B2 phase structure;
and step 3: alpha is alpha2Performing two-step heat treatment with homogeneous phase distribution, namely performing heat preservation treatment on the bar blank with the uniformly refined metastable B2 phase structure obtained in the step 2 at 600-700 ℃, and then heating the bar blank to 950 ℃ along with a furnaceHeat preservation treatment is carried out at the temperature of 1000 ℃ below zero, and finally quenching is carried out to obtain the product with alpha2The phases are uniformly dispersed and distributed in the bar blank of the B2 phase matrix structure, thus, the phase alpha is separated out by regulating and controlling the high temperature2Competition relationship between nucleation and growth, making alpha2The phases are uniformly dispersed in the refined B2 phase matrix.
Step 4, the alpha of the product obtained in step 32The bar blank with phases uniformly dispersed in the B2 phase matrix structure is subjected to heat preservation treatment at 550-650 ℃, then is heated to 700-850 ℃ along with a furnace for heat preservation treatment, and is finally cooled, so that the low-temperature precipitated phase is uniformly dispersed and distributed in the refined B2 phase matrix by regulating and controlling the competitive relationship between the nucleation and the growth of the O phase of the low-temperature precipitated phase, and the bar blank with the O phase and the alpha phase is obtained2The alloy material is uniformly dispersed and distributed in the B2 phase matrix structure, and the multilevel structure uniformity control of the alloy is completed.
Wherein the extrusion cogging process conditions are that the extrusion temperature is 950-1150 ℃ and the extrusion ratio is 4-10.
The time of the B2 phase recrystallization heat treatment is 0.5 h-1 h, thereby ensuring that the B2 phase is fully recrystallized and the B2 is not excessively grown.
Wherein in the step 3, the heat preservation treatment time at 600-700 ℃ is 1-4 h, and the heat preservation time at 950-1000 ℃ is 0.5-2 h.
Wherein in the step 4, the heat preservation treatment at the temperature of 550-650 ℃ is 1-4 h, and the heat preservation treatment at the temperature of 700-850 ℃ is 6-24 h.
Wherein the quenching in the steps 2 and 3 adopts an oil cooling or water cooling mode.
Wherein the cooling in step 4 comprises air cooling, oil cooling or water cooling.
The method of the invention utilizes the thermomechanical principle to uniformly refine the original B2 phase, and on the basis, controls the precipitation behavior of the supersaturated B2 phase, sequentially regulates and controls the competition relationship between nucleation and growth of the high-temperature and low-temperature precipitated phases, so that the high-temperature and low-temperature precipitated phases are uniformly and dispersedly distributed in the refined B2 phase matrix, thereby comprehensively solving the problems of the matrix B2 phase and the high-temperature precipitated phase alpha in the alloy structure2Distribution uniformity of three organization composition phases of phase and low-temperature precipitated phase O phaseAnd (5) problems are solved. Thereby increasing Ti2The stability of the performance of the AlNb alloy ensures the safety and reliability of the service of the alloy component.
Drawings
FIG. 1 is a three-phase Ti treated by the method of the present invention2Microstructure diagram of AlNb alloy.
Detailed Description
For a clearer understanding of the objects, technical solutions and advantages of the present invention, the present invention will be described in further detail below with reference to the accompanying drawings and embodiments.
Example one
1. Mixing Ti2Extruding and cogging AlNb alloy cast ingot at 1100 ℃ with the extrusion ratio of 6 to obtain a B2 phase fully-crushed bar billet;
2. carrying out B2 phase recrystallization heat treatment on the fully crushed B2 phase bar obtained in the step 1 at 1050 ℃ for 0.5h, and then cooling in an oil cooling mode to obtain a bar with a uniformly refined metastable B2 phase structure;
3、α2performing two-step heat treatment with homogeneous phase distribution, namely performing heat preservation treatment on the bar blank with the uniformly refined metastable B2 phase structure obtained in the step 2 at 650 ℃ for 2h, heating the bar blank to 950 ℃ along with a furnace, performing heat preservation treatment for 1h, and finally cooling the bar blank in an oil cooling mode to obtain the bar blank with alpha2The phases are uniformly dispersed in the bar blank of the B2 phase matrix structure;
4. the obtained product in step 3 has alpha2Carrying out heat preservation treatment on the bar blank with the phase uniformly dispersed and distributed in the B2 phase matrix structure at 600 ℃ for 2h, then heating to 750 ℃ along with a furnace for 12h, and finally cooling in an air cooling mode to obtain the bar blank with O phase and alpha phase2The alloy material is uniformly dispersed and distributed in the B2 phase matrix structure, and the multilevel structure uniformity control of the alloy is completed.
Example two
1. Mixing Ti2Extruding and cogging the AlNb alloy cast ingot at 1000 ℃ with the extrusion ratio of 5 to obtain a B2 phase fully-crushed bar billet;
2. carrying out B2 phase recrystallization heat treatment on the fully crushed B2 phase bar obtained in the step 1 at 1060 ℃ for 0.5h, and then cooling the bar in a water cooling mode to obtain a bar with a uniformly refined metastable B2 phase structure;
3. carrying out heat preservation treatment on the bar blank with the uniformly refined metastable B2 phase structure obtained in the step 2 at 600 ℃ for 4h, then heating to 960 ℃ along with a furnace to carry out heat preservation treatment for 1.5h, and finally cooling in a water cooling mode to obtain the bar blank with alpha2The phases are uniformly dispersed in the bar blank of the B2 phase matrix structure;
4. the obtained product in step 3 has alpha2Carrying out heat preservation treatment on the bar blank with the phase uniformly dispersed and distributed in the B2 phase matrix structure at 650 ℃ for 3h, then heating to 800 ℃ along with a furnace to carry out heat preservation treatment for 8h, and finally cooling in an air cooling mode to obtain the bar blank with O phase and alpha phase2The alloy material is uniformly dispersed and distributed in the B2 phase matrix structure, and the multilevel structure uniformity control of the alloy is completed.
EXAMPLE III
1. Mixing Ti2Extruding and cogging AlNb alloy cast ingot at 950 ℃ with the extrusion ratio of 4 to obtain a B2 phase fully-crushed bar billet;
2. carrying out B2 phase recrystallization heat treatment on the fully crushed B2 phase bar obtained in the step 1 at 1050 ℃ for 1h, and then cooling the bar in a water cooling mode to obtain a bar with a uniformly refined metastable B2 phase structure;
3. carrying out heat preservation treatment on the bar blank with the uniformly refined metastable B2 phase structure obtained in the step 2 at 700 ℃ for 1h, then heating the bar blank to 980 ℃ along with a furnace for 2h, and finally cooling the bar blank in an oil cooling mode to obtain the bar blank with alpha2The phases are uniformly dispersed in the bar blank of the B2 phase matrix structure;
4. the obtained product in step 3 has alpha2Carrying out heat preservation treatment on the bar blank with the phase uniformly dispersed and distributed in the B2 phase matrix structure at 550 ℃ for 4h, then heating to 720 ℃ along with a furnace to carry out heat preservation treatment for 15h, and finally cooling in an air cooling mode to obtain the bar blank with the O phase and the alpha phase2The alloy material is uniformly dispersed and distributed in the B2 phase matrix structure, and the multilevel structure uniformity control of the alloy is completed.
Example four
1. Mixing Ti2Extruding and cogging AlNb alloy cast ingot at 1080 ℃ with the extrusion ratio of 7 to obtain B2-phase fully crushed bar blank;
2. carrying out B2 phase recrystallization heat treatment on the fully crushed B2 phase bar obtained in the step 1 at 1080 ℃ for 0.5h, and then cooling in an oil cooling mode to obtain a bar with a uniformly refined metastable B2 phase structure;
3. carrying out heat preservation treatment on the bar blank with the uniformly refined metastable B2 phase structure obtained in the step 2 at 600 ℃ for 2h, then heating the bar blank to 1000 ℃ along with a furnace to carry out heat preservation treatment for 2h, and finally cooling the bar blank in an oil cooling mode to obtain the bar blank with alpha2The phases are uniformly dispersed in the bar blank of the B2 phase matrix structure;
4. the obtained product in step 3 has alpha2Carrying out heat preservation treatment on the bar blank with the phase uniformly dispersed and distributed in the B2 phase matrix structure at 650 ℃ for 3h, then heating to 830 ℃ along with a furnace to carry out heat preservation treatment for 8h, and finally cooling in an air cooling mode to obtain the bar blank with O phase and alpha phase2The alloy material is uniformly dispersed and distributed in the B2 phase matrix structure, and the multilevel structure uniformity control of the alloy is completed.
FIG. 1 is a three-phase Ti treated by the method of the present invention2Microstructure diagram of AlNb alloy. As can be seen from FIG. 1, the O phases and α2Uniformly dispersed and distributed in a B2 phase matrix, and completely solves the problems of the matrix B2 phase and the high-temperature precipitated phase alpha in the alloy structure2The distribution uniformity of three organization composition phases of the phase and the low-temperature precipitated phase O phase.
Claims (5)
1. Three-phase Ti2The AlNb alloy multilayer structure uniformity control method comprises the following steps:
step 1: mixing Ti2Extruding and cogging the AlNb alloy cast ingot to obtain a B2 phase fully-crushed bar blank;
step 2: carrying out B2 phase recrystallization heat treatment on the obtained B2 phase fully-crushed bar blank at 1050-1080 ℃ for 0.5-1 h, and then quenching to obtain a bar blank with a uniformly refined metastable B2 phase structure;
and step 3: alpha is alpha2Phase distribution homogeneity two-step heat treatment, namely performing the bar billet with the uniformly refined metastable B2 phase structure obtained in the step 2 at 600-700 ℃ for 1h E4h of heat preservation treatment, then the temperature is raised to 950 ℃ to 1000 ℃ along with the furnace, the heat preservation treatment is carried out for 0.5h to 2h, and finally the temperature is quenched, thus obtaining the alpha2The phases are uniformly dispersed in the bar blank of the B2 phase matrix structure;
step 4, the alpha of the product obtained in step 32The bar blank with the phase evenly dispersed and distributed in the B2 phase matrix structure is subjected to heat preservation treatment for 1 to 4 hours at the temperature of 550 to 650 ℃, then is heated to the temperature of 700 to 850 ℃ along with a furnace to be subjected to heat preservation treatment for 6 to 24 hours, and finally is cooled to obtain the bar blank with the O phase and the alpha phase2The alloy material is uniformly dispersed and distributed in a B2 phase matrix structure.
2. The method according to claim 1, wherein the extrusion cogging process conditions are an extrusion temperature of 950 ℃ to 1150 ℃ and an extrusion ratio of 4 to 10.
3. The method of claim 1, wherein the quenching of step 2 is oil-cooled or water-cooled.
4. The process of claim 1, wherein the quenching in step 3 is oil or water cooled.
5. The method of claim 1, wherein said cooling in step 4 comprises air cooling, oil cooling, or water cooling.
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| FR2772790B1 (en) * | 1997-12-18 | 2000-02-04 | Snecma | TITANIUM-BASED INTERMETALLIC ALLOYS OF THE Ti2AlNb TYPE WITH HIGH ELASTICITY LIMIT AND HIGH RESISTANCE TO CREEP |
| DE102007051499A1 (en) * | 2007-10-27 | 2009-04-30 | Mtu Aero Engines Gmbh | Material for a gas turbine component, method for producing a gas turbine component and gas turbine component |
| CN101525733B (en) * | 2009-01-21 | 2011-04-20 | 中国钢研科技集团公司 | Heat treatment technology for improving intercrystalline corrosion resistant performance of austenitic nickel-based corrosion resistant alloy |
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| CN109332693A (en) * | 2018-11-08 | 2019-02-15 | 有研工程技术研究院有限公司 | A kind of three-phase Ti of laser gain material manufacture2The heat treatment process of AlNb based alloy |
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| CN104148562A (en) * | 2014-06-30 | 2014-11-19 | 贵州安大航空锻造有限责任公司 | Cogging method for Ti2AlNb-based alloy ingot |
| CN107217221A (en) * | 2017-05-22 | 2017-09-29 | 西部超导材料科技股份有限公司 | A kind of preparation method of high uniform Ti 15Mo titanium alloy bar stocks |
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