CN105483585A - Preparation method for titanium-aluminum alloy with excellent room-temperature ductility - Google Patents
Preparation method for titanium-aluminum alloy with excellent room-temperature ductility Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
The invention discloses a preparation method for a titanium-aluminum alloy with excellent room-temperature ductility. The preparation method comprises the following steps: firstly, carrying out uniform thermal treatment on a TiAl-based alloy, and carrying out multi-direction isothermal forging deformation treatment on the TiAl-based alloy subjected to the uniform thermal treatment, wherein a deformation temperature is 700-1000 DEG C, a deformation rate is 0.1-0.001s<-1>, single-step deformation amount is 5-20%, and deformation pass number is 1-3; and carrying out annealing treatment on the materials after forging, preserving the heat for 3-60 minutes at a temperature of 1150-1350 DEG C, and then, carrying out air-cooling, thereby realizing control on grain size and grain boundary structure of the TiAl-based alloy. The preparation method adopts the deformation thermal treatment steps to repeatedly treat materials, has better grain boundary structure control effect, and can improve mechanical performances such as breaking strength, room-temperature ductility and the like of the TiAl-based alloy.
Description
Technical field
The present invention relates to a kind of superalloy art, particularly a kind of titanium aluminium base alloy preparation method of temperature-room type plasticity excellence.
Background technology
The lightweight TiAl-base alloy of the hot strength had, high creep resistance and good high temperature oxidation resistance is considered to the important high-temperature structural material of following aviation field.But TiAl-base alloy is brittleness at room temperature (less than 700 DEG C plasticity is very poor, elongation 2%-3%), and the pyroplastic deformation working ability difference caused thus becomes the major obstacle of its application.
In recent years, in order to improve the temperature-room type plasticity of TiAl-base alloy, domestic and international investigator has carried out a large amount of research work, obtains abundant achievement, but temperature-room type plasticity index does not still reach practical requirement.At present, crystal grain thinning is considered to the effective means that uniquely can improve TiAl-base alloy intensity simultaneously, improve plasticity.There are some researches show: when the grain-size of TiAl-base alloy is 50nm, its temperature-room type plasticity reaches 50%, considerably beyond the plasticity of conventional die size, and has superplasticity at normal temperatures.Therefore, how in TiAl-base alloy sample, obtaining tiny, uniform microstructure, is very significant work to improving its temperature-room type plasticity.
Sever Plastic Deformation is the effective means of refining alloy crystal grain, concentrates on canned forging and unidirectional isothermal compression technique at present to the viscous deformation research of TiAl-base alloy.Canned forging is that TiAl-base alloy utilizes the triaxial pressure effect of stainless steel sheath material to carry out viscous deformation, reduce the tendency of TiAl-base alloy cracking, major part canned forging is warmed up to after certain temperature through heat treatment furnace, take out from heat treatment furnace and carry out rapid forge, although sheath material can reduce the calorific loss of alloy in forging process, but still can not reach constant-temperature deformation condition, and rate of deformation is very fast, has tearing tendency; Unidirectional isothermal compression carries out unidirectional compression under the high temperature conditions, at constant temperature or be similar to the next direction of constant temperature and can be out of shape 90% at most, but material becomes pie after deforming more than 60%, there is larger change in shape, shape more shape changeable cannot be entered, and the more difficult part being processed into certain size, and there is cracking phenomena.Although so canned forging and unidirectional isothermal compression technique can carry out the viscous deformation of certain deflection to TiAl-base alloy, be subject to texturing temperature, rate of deformation and distortion quantitative limitation, constant temperature large plastometric set cannot be accomplished.
But in fact, due to the existence of TiAl-base alloy intrinsic fragility, the temperature-room type plasticity of the nanocrystalline and ultrafine grain metal material obtained by grain refining is merely all very low.There are some researches show: polycrystalline TiAl-base alloy shows any plasticity hardly before disrumpent feelings, always intergranular flwrittle fracture occurs.Therefore, start with from intrinsic reason, by changing material internal microtexture state, under the prerequisite ensureing high strength, improving its plasticity is an effective approach.This patent utilizes bounding engineering means to improve TiAl-base alloy temperature-room type plasticity further, control and optimize the Grain Boundary Character distribution of TiAl-base alloy material, particularly produce a large amount of twins (distortion and annealing twin) at material internal, also be obtain the high tough effective way waiting comprehensive mechanical property alloy material, on the basis of crystal grain thinning, the temperature-room type plasticity of TiAl-base alloy can be improved further.
The TiAl-base alloy grain refining means had been reported are unidirectional compression set under comparatively high temps, make material occurrence dynamics recrystallization softening crystal grain, there is not yet and adopt multidirectional compared with low temperature isothermal forging in conjunction with subsequent anneal thermal treatment, make material generation Static Recrystallization to control the report of material grains size.The improvement TiAl-base alloy temperature-room type plasticity had been reported mostly is started with from alloying and crystal grain thinning aspect, there is not yet the concept of TiAl-base alloy based on bounding engineering, adopt the distortion of multidirectional isothermal forging in conjunction with subsequent anneal thermal treatment to control and to optimize the GBCD of TiAl-base alloy, improve the report of the interaction mechanism of its temperature-room type plasticity and fracture crack and crystal boundary.
Summary of the invention
The object of the present invention is to provide a kind of titanium aluminium base alloy preparation method of temperature-room type plasticity excellence.
Realizing the object of the invention technical solution is: a kind of titanium aluminium base alloy preparation method of temperature-room type plasticity excellence, comprises the following steps:
The first step, first carries out homogenizing thermal treatment to TiAl-base alloy;
Second step, carries out multidirectional isothermal forging deformation process to the TiAl-base alloy after homogenizing thermal treatment, and texturing temperature is 700-1000 DEG C, and rate of deformation is 0.1-0.001s
-1, single work step deflection is 5-20%, and rolling pass is 1-3 passage;
3rd step, the alloy finally deformation process crossed carries out anneal, air cooling after insulation.
In the first step, after TiAl-base alloy is incubated 45-50h at 1150 ± 20 DEG C, furnace cooling carries out homogenizing thermal treatment.
In 3rd step, annealing temperature is 1150-1350 DEG C, and soaking time is 3-90min.
Compared with prior art, the present invention has following remarkable advantage:
(1) block materials with excellent temperature-room type plasticity can be prepared by the present invention, and isothermal multiway forging is that mould and blank heating are maintained this temperature to forging temperature and carry out the plastic working technique of the large plastometric set of low strain rate distortion, there is no tearing tendency, the forging precision of little surplus or Near net shape can be obtained, be particularly suitable for the difficult-to-deformation material that those forging warm areas are narrow.As compared to the severe plastic deformation method such as ECAP with HPT, the advantage that multidirectional isothermal forging method is outstanding is that specimen size is unrestricted, equipment is simple and efficiency is high.
(2) material through process of the present invention is made standard metallographic specimen, the Grain Boundary Character of back scattering diffraction technical testing material is utilized to distribute after polishing, polishing, electropolishing, in tissue, the ratio of special grain boundary reaches more than 45%, and grain-size is reduced to about 20 μm; Sample after multidirectional isothermal forging and subsequent heat treatment and homogenizing heat treatment material are contrasted, under identical compression verification condition, the ultimate compression strength of material improves about 80%, and limited compression rate improves about 20%, and TiAl-base alloy temperature-room type plasticity and mechanical property are all improved.
Below in conjunction with accompanying drawing, the present invention is described in further detail.
Accompanying drawing explanation
Fig. 1 is γ of the present invention-TiAl-base alloy Grain Boundary Character distribution schematic diagram (before a process, after b process).
Embodiment
Principle of the present invention: based on the principle of refined crystalline strengthening and bounding engineering, by multidirectional isothermal forging in conjunction with subsequent anneal thermal treatment, TiAl-base alloy crystal grain thinning and optimize grain boundary structure simultaneously, thus improve TiAl-base alloy temperature-room type plasticity performance.
Sever Plastic Deformation of the present invention is that multidirectional isothermal forging combines annealing heat treating method, alloy carries out axially different repeated deformation, by accumulating deflection each time, reach the object of large plastometric set, and then carry out annealing thermal treatment, the effect of crystal grain thinning and the distribution of optimization Grain Boundary Character can be reached simultaneously.The advantage that this deformation method is given prominence to is that specimen size is unrestricted, equipment simple and efficiently, can carries out large plastometric set at relatively high temperatures, and does not have the risk of cracking.
Aluminum base alloy preparation method of the present invention comprises following concrete steps:
1. first carry out homogenizing thermal treatment to γ-TiAl-base alloy, homogenizing heat treatment mode is furnace cooling after 1150 ± 20 DEG C of insulation 45-50h;
2. by adjustment 700-1000 DEG C of forging temperature, 0.1-0.001s
-1the combination that the deformation parameters such as forging speed, 5-20% mono-work step deflection and 1-3 rolling pass etc. are different, alloy carries out multidirectional isothermal forging deformation process (every a time alloy forging deformation 3 faces);
3. the material finally conducting forging processing crossed is placed in heat treatment furnace, and holding temperature is 1150-1350 DEG C, and soaking time is 3-60min, air cooling after insulation.
In the following Examples and Comparative Examples, represent the thinning effect of material internal crystal grain with average grain size (μm), it is better to be worth more novel classification effect.Represent the effect of optimization of grain boundaries structure with special grain boundary percentage ratio (%), it is better to be worth higher explanation crystal boundary effect of optimization.
Embodiment 1
The test result of the different forging temperature of table 1
Utilize isothermal multiway forging equipment Gleeble-3500 γ-TiAl-base alloy to be carried out to the deformation process of different forging temperature, forging temperature is respectively 1000,900,850,800,700 DEG C, forging speed 0.01s
-1, single pass is out of shape, and single work step deflection is 20%, and concrete technology is see table 1.γ-TiAl-base alloy after thermomechanical treatment is carried out to the annealing thermal treatment of 90min subsequently at 1100 DEG C, air cooling after anneal.The ratio of the inner average grain size of the sample after thermomechanical treatment and low energy CSL (coincidence site lattice) special grain boundary changes with the change of forging temperature, and concrete technology parameter and test result are in table 1.
Embodiment 2
The test result of the different forging deformation speed of table 2
Utilize isothermal multiway forging equipment Gleeble-3500 to carry out the deformation process of different forging speed to γ-TiAl-base alloy, forging temperature comprises 900 and 800 DEG C, forging speed is 0.001,0.01,0.1s
-1, single pass is out of shape, and single work step deflection is 20%, the γ-TiAl-base alloy after thermomechanical treatment is carried out to the annealing thermal treatment of 90min subsequently at 1100 DEG C, air cooling after anneal.The ratio of the inner average grain size of the sample after thermomechanical treatment and low energy CSL (coincidence site lattice) special grain boundary changes with the change of forging temperature, and concrete technology parameter and test result are in table 2.
Embodiment 3
The test result of the different forging deformation passage of table 3
Utilize isothermal multiway forging equipment Gleeble-3500 γ-TiAl-base alloy to be carried out to the deformation process of different distortion passage, forging temperature comprises 900 and 800 DEG C, forging speed is 0.001,0.01,0.1s
-1, rolling pass comprises a time and three passages, and single work step deflection is 20%, the γ-TiAl-base alloy after thermomechanical treatment is carried out to the annealing thermal treatment of 90min subsequently at 1100 DEG C, air cooling after anneal.The ratio of the inner average grain size of the sample after thermomechanical treatment and low energy CSL (coincidence site lattice) special grain boundary changes with the change of forging temperature, and concrete technology parameter and test result are in table 3.
Embodiment 4
The test result of the different forging deformation step of table 4 and deflection
Utilize isothermal multiway forging equipment Gleeble-3500 γ-TiAl-base alloy to be carried out to the deformation process of different distortion step, have the deformation technique that five kinds are different, wherein predeformation thermal treatment process has three kinds first time, be respectively without pre-treatment, 1200 DEG C/0.001s
-1single work step 20% single pass distortion is without annealing thermal treatment and 800 DEG C/0.01s
-1single work step 20% single pass distortion+1300 DEG C of-5min annealing thermal treatments.Carry out the deformation process of single pass multiway forging compression extruding or Uniaxial Compression after predeformation thermal treatment, the γ-TiAl-base alloy after thermomechanical treatment is carried out to the annealing thermal treatment of 5min subsequently at 1300 DEG C, air cooling after anneal.The ratio of the inner average grain size of the sample after thermomechanical treatment and low energy CSL (coincidence site lattice) special grain boundary changes with the change of forging temperature, and concrete technology parameter and test result are in table 4.
Embodiment 5
The test result of the different subsequent anneal thermal treatment process of table 5
Isothermal multiway forging equipment Gleeble-3500 is utilized first to carry out 800 DEG C of 0.01s to γ-TiAl-base alloy
-1single work step 20% single pass distortion+1300 DEG C of-5min annealing thermal treatment pre-treatment, the deformation process of unidirectional isothermal compression is carried out after predeformation thermal treatment, subsequently γ-the TiAl-base alloy after thermomechanical treatment is carried out to the annealing thermal treatment of different annealing heat treatment process, air cooling after anneal.The ratio of the inner average grain size of the sample after thermomechanical treatment and low energy CSL (coincidence site lattice) special grain boundary changes with the change of forging temperature, and concrete technology parameter and test result are in table 5.
Comparative example
Table 6 processes the test result of material and mother metal
In order to compare the difference on process material and starting materials structure and properties, get starting material and carry out the thermal treatment of 1150 DEG C of-48h homogenizing annealings, carry out the test of room temperature compression performance with the material of thermomechanical treatment, reduced size is the cylinder of Φ 4 × 6mm, and compression speed is 0.001s
-1, getting breaking tenacity is ultimate compression strength, and rate of compression during fracture is limited compression rate, and be respectively intensity index and the temperature-room type plasticity index of material, test result is in table 6.
Material through process of the present invention is made standard metallographic specimen, the grain boundary structure of EBSD technical testing material is utilized after polishing, polishing, electrolytic corrosion, in tissue, the ratio of special grain boundary can up to more than 45%, average grain size is reduced to less than about 20 μm, can find under identical compression verification condition, the room temperature strength of thermomechanical treatment material and temperature-room type plasticity all be improved significantly.
Fig. 1 (a) is depicted as Grain Boundary Character distribution situation in starting material tissue, wherein the ratio of special grain boundary (Σ≤29) is 36.3%, Fig. 1 (b) is depicted as Grain Boundary Character distribution situation in the material structure of aforesaid method process, wherein the ratio of special grain boundary is 41.4%, in figure, black lines represents the free crystal boundary of high energy, and grey lines represent low energy Σ CSL crystal boundary.
Claims (3)
1. a titanium aluminium base alloy preparation method for temperature-room type plasticity excellence, is characterized in that, comprise the following steps:
The first step, first carries out homogenizing thermal treatment to TiAl-base alloy;
Second step, carries out multidirectional isothermal forging deformation process to the TiAl-base alloy after homogenizing thermal treatment, and texturing temperature is 700-1000 DEG C, and rate of deformation is 0.1-0.001s
-1, single work step deflection is 5-20%, and rolling pass is 1-3 passage;
3rd step, the alloy finally deformation process crossed carries out anneal, air cooling after insulation.
2. the titanium aluminium base alloy preparation method of temperature-room type plasticity excellence as claimed in claim 1, it is characterized in that, in the first step, after TiAl-base alloy is incubated 45-50h at 1150 ± 20 DEG C, furnace cooling carries out homogenizing thermal treatment.
3. the titanium aluminium base alloy preparation method of temperature-room type plasticity excellence as claimed in claim 1, it is characterized in that, in the 3rd step, annealing temperature is 1150-1350 DEG C, and soaking time is 3-90min.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111411210A (en) * | 2020-04-26 | 2020-07-14 | 陕西理工大学 | Multi-angle grain boundary pure iron material and preparation method thereof |
| CN113774300A (en) * | 2021-09-15 | 2021-12-10 | 西北工业大学 | Thermomechanical treatment method for weakening titanium alloy deformation texture and reducing abrasion |
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| JPS63171862A (en) * | 1987-01-08 | 1988-07-15 | Nkk Corp | Manufacture of heat resistant ti-al alloy |
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| CN102312181A (en) * | 2011-09-07 | 2012-01-11 | 上海交通大学 | Isothermal forging method of TiAl alloy |
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| JPS63171862A (en) * | 1987-01-08 | 1988-07-15 | Nkk Corp | Manufacture of heat resistant ti-al alloy |
| US5442847A (en) * | 1994-05-31 | 1995-08-22 | Rockwell International Corporation | Method for thermomechanical processing of ingot metallurgy near gamma titanium aluminides to refine grain size and optimize mechanical properties |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111411210A (en) * | 2020-04-26 | 2020-07-14 | 陕西理工大学 | Multi-angle grain boundary pure iron material and preparation method thereof |
| CN113774300A (en) * | 2021-09-15 | 2021-12-10 | 西北工业大学 | Thermomechanical treatment method for weakening titanium alloy deformation texture and reducing abrasion |
| CN113774300B (en) * | 2021-09-15 | 2022-04-22 | 西北工业大学 | Thermomechanical treatment method for weakening titanium alloy deformation texture and reducing abrasion |
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