CN1603427A - Beta-phase transformation point thermal treatment process for titanium alloy - Google Patents
Beta-phase transformation point thermal treatment process for titanium alloy Download PDFInfo
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Abstract
The invention involves a kind to obtain the high plastic laminated organization titanium alloy accurate b (delta v) the heat treatment craft, is the materials science area of technology. The craft has solved the laminated organization plasticity low technology key. (Arab League sends) +b after a (delta v) the area forging forging (delta v) to change in b (Tb (delta v)) below 20deg.C~~40deg.C, namely Tb (delta v) - (20~~40) deg.C preheating, then along with stove elevation of temperature to After Tb (delta v) -10deg.C~~Tb (delta v) +40deg.C short-time heats up the rapid water cooling or air cooled, and presses needs the performance requirement (Arab League to send) +b in a (delta v) the area essential to carry on annealing, double annealing and so on the supplement heat treatment. The craft is suitable to a (Arab League sends) and a (Arab League sends) -b (delta v) the titanium alloy, obtains laminated organization newborn a (Arab League sends) the content not to be bigger than 15%, its plastic and the net basket organization is same, break toughness, fatigue cracking expansion resisting force, slow change resisting force and so on then remarkably is higher than a pair of condition organization, may make half-finished product and the components and so on titanium alloy structure.
Description
The present invention relates to a kind of beta-phase transformation point thermal treatment process for titanium alloy that obtains the high-ductility lamellar structure, belong to materials science field.
Nearly α type and alpha-beta Type Titanium Alloy are because of the different microstructures that can obtain four types of thermal distortion (thermal treatment) technology, and wherein the maximum forging of practical application is a bifurcation tissue, and promptly nascent alpha+beta changes to be organized.
Along with the progress of structure design thought, a kind of advanced person's damage tolerance design has obtained practical application, and it is had higher requirement to the mechanical property of material, mainly be need be higher fracture toughness property and lower crack growth rate.Expectation is satisfied the microstructure of this requirement and is had only basket tissue and lamellar structure.Can obtain uniform tissue more through the heat treated lamellar structure of β than the forged basket tissue of process, and lamellar structure has higher K
ICThe value and lower da/dN, so lamellar structure more the Designers favor.
Lamellar structure is made up of equiaxial β crystal grain, and crystal boundary is continuously straight α phase, and intracrystalline then is the boundling sheet α phase of braiding, makes crack propagation form the zigzag path, thereby obtains very high K
ICValue and very low da/dN.But the existence of straight grain boundary phase causes the remarkable reduction of material plasticity again continuously, has influence on the reliability of fatigue property and member, becomes the heat treated a great problem of titanium alloy beta so solve the plasticity problem of lamellar structure always.According to traditional concept, through being not contain the primary phase in the β heat treated lamellar structure, for example β thermal treatment adopted in T β+(20～30) ℃ of Ti-6Al-2Sn-2Zr-2Mo-2Cr-0.2Si titanium alloy.This idea makes the heat treated Heating temperature of β all be higher than T β+20 ℃.In addition, because the thermal conductivity of titanium alloy is lower, be 1/3 of steel.So the predetermined heating time is long.Even in the heating of β district, heating coefficient η, i.e. t heat-up time (min) and forging maximum cross-section thickness δ
Max(mm) ratio is generally also more than 0.7.
Studies show that having material to β grain growth kinetics is Heating temperature.Heating temperature is high more, and grain growth is strong with regard to Shaoxing opera.Except that Heating temperature, heat-up time, length also can be impelled the β grain growth.β thermal treatment in the past just causes producing thick β grain structure just because of and soaking time length high in β district Heating temperature, and forms straight α phase network continuously, the common low basic reason of lamellar structure plasticity that Here it is at crystal boundary.
As everyone knows, β crystal grain constantly forms in the dissolved process mutually gradually at primary, it is contemplated that, if can design a kind of technology, can obtain had not both had the primary phase, do not have β grain boundary phase yet, have only the lamellar structure of the boundling sheet α phase of braiding, a kind of ideal lamellar structure that Here it is.Just will control a kind of state, primary has just dissolved mutually, and β crystal grain is inchoate moment still again.This perfect condition may exist in some little zones, is impossible but will make whole forging all have this state.Yet use as engineering, can find a zone of transition, be about to primary and be limited in mutually in certain ratio, as 15%, the β grain boundary is again the zone that part produces mutually, and near the zone Here it is the beta transformation point is just at T
β-10 ℃ to T
β+ 10 ℃ of these zone of transition that do not have the people to study.When heat in this zone, may leave a spot of primary phase, β crystal grain does not form or the tiny β crystal grain that has just formed as yet.In process of cooling, have the β crystal boundary of part to separate out the α phase, but this grain boundary phase network is smaller, the overwhelming majority is for forming the boundling sheet α phase of braiding.
What β thermal treatment was in the past adopted is the method that workpiece is directly heated in the β district, so require heating coefficient η generally more than 0.7, if adopt the heat treated zone heating method of accurate β, promptly earlier in the upper temp preheating of alpha+beta district, be warming up to the heating of β district with stove fast then, then can shorten heat-up time greatly in the β district.Studies show that, the time that is warmed up to the β district from the alpha+beta district is approximately 8min～10min, in this temperature-rise period, primary is constantly dissolving mutually, as long as the blank that 100mm is thick is just can be so that blank center and outside homogeneous microstructure at β district insulation 20min～25min (η=0.2～0.25), and high more in the Heating temperature in β district, the soaking time that needs is also short more.
Technical solution of the present invention is utilized the heating of beta transformation point near zone just, and adopts the zone heating method of control primary phased soln, designs beta-phase transformation point thermal treatment process.And purpose of the present invention is also designed a kind of β thermal treatment process that obtains the high-ductility lamellar structure just, and promptly this lamellar structure has with basket and organizes the same good plasticity, simultaneously lamellar structure inherent good characteristic is arranged again, can satisfy the damage tolerance designing requirement.
Technical scheme of the present invention realizes by following technical measures:
Employing is at forged nearly α type and alpha-beta Type Titanium Alloy forging through the alpha+beta district, and at III class stove, promptly effectively workspace maximum temperature deviation is not more than ± heats in 10 ℃ the resistance furnace.The general factory of this condition all possesses, and adopts the silicon controlled rectifier temperature control, temperature fluctuation ± 2 ℃.The shove charge after furnace temperature arrives preheating temperature of forging or member is placed in effective workspace.At first at T
β-(20～40) ℃ preheating, stove calculates soaking time, soaking time t (min)=η * δ after arriving preheating temperature
Max, δ
Max(mm) be the maximum cross-section thickness of forging or member, η is a heating coefficient, and the value of the preheating heating coefficient η of forging or member is 0.4～0.7; Be warming up to T with stove fast then
β-10 ℃～T
βCalculate soaking time after+40 ℃, the calculation formula of soaking time t (min) is with above-mentioned unanimity, but the value of heating coefficient η is 0.1～0.5; In addition, forging or member also can be without above-mentioned preheating insulation steps, but with it directly at T
β-10 ℃～T
β+ 40 ℃ of heating equally in shove charge after temperature, and are calculated soaking time after furnace temperature arrives said temperature, the calculation formula of soaking time t (min) is with above-mentioned unanimity, but the value of heating coefficient η is 0.3～0.8; Above-mentioned two kinds of methods are all rapid water-cooled or air cooling after heating and insulation, thickens mutually to stop grain boundary; Carry out the thermal treatment of subordinate phase again according to technical requirements through forging or member after the above-mentioned thermal treatment.
The present invention relatively has following advantage with the β thermal treatment of routine: the Heating temperature in the β district is low, and soaking time is short; The macrostructure that obtains is thin, the plasticity height, and fatigue property is good; K
IC, da/dN is suitable with creep property; Has improved comprehensive mechanical performance.Following example is respectively the half-finished performance comparison such as forging, slab and bar after beta-phase transformation point thermal treatment process is handled.
The drawing of accompanying drawing is described as follows:
Fig. 1 adopts the da/dN curve that obtains behind the beta-phase transformation point thermal treatment process for the high-strength and high ductility TC21 titanium alloy forging stock of embodiment three
Fig. 2 is the da/dN curve after the medium tenacity TC4-DT titanium alloy thick plate of embodiment four adopts beta-phase transformation point thermal treatment process
Below with reference to embodiment technical solution of the present invention is further described:
The concrete processing step of technical solution of the present invention is:
This kind beta-phase transformation point thermal treatment process for titanium alloy, the titanium alloy type that it was suitable for is nearly alpha titanium alloy and alpha-beta Type Titanium Alloy, it is characterized in that: this technology may further comprise the steps:
(1). the preheating insulation of titanium alloy forging (or workpiece), titanium alloy forging (or workpiece) is placed on preheating in the resistance furnace, preheating temperature is beta transformation point (T
β) following 20 ℃～40 ℃, i.e. T
β-(20～40) ℃, stove calculates soaking time, soaking time t (min)=η * δ after arriving preheating temperature
Max, δ
Max(mm) be the maximum cross-section thickness of forging, η is a heating coefficient, and the value of the preheating heating coefficient η of forging (or workpiece) is 0.4～0.7;
(2). the forging (or workpiece) behind step (1) preheating insulation is warming up to T with stove
β-10 ℃～T
βCalculate soaking time after+40 ℃, the unanimity of the same step of calculation formula (1) of soaking time t (min), but the value of heating coefficient η is 0.1～0.5;
(3). with above-mentioned in preset temperature heating and the forging (or workpiece) after reaching predetermined soaking time come out of the stove rapid water-cooled or air cooling.
In addition, forging (or workpiece) also can be without above-mentioned steps (1) preheating insulation, but its direct heating is calculated soaking time to T β-10 ℃～T β+40 ℃, the calculation formula of soaking time t (min) and aforesaid right require consistent in 1 the step (1), but the value of heating coefficient η is 0.3～0.8; Afterwards, with above-mentioned in preset temperature heating and the forging (or workpiece) after reaching predetermined soaking time come out of the stove rapid water-cooled or air cooling.
In the resistance furnace effectively the maximum temperature deviation of workspace be not more than ± 10 ℃, forging (or workpiece) shove charge after furnace temperature arrives preheating temperature is placed in effective workspace.And the Heating temperature in the above-mentioned steps can be controlled at T more accurately
β～T
βIn+10 ℃ the scope.The titanium alloy type that is applicable to this kind thermal treatment process is that nearly alpha titanium alloy and alpha-beta Type Titanium Alloy are the forging with bifurcation tissue signature (or workpiece) through forging of alpha+beta district or moulding.
Embodiment one:
TC21 titanium alloy die forging spare adopt performance after above-mentioned novel beta-phase transformation point thermal treatment process is handled from table one as can be seen, stamp work can obtain the basket tissue, has further improved intensity, simultaneously, has obtained high K
ICDamage tolerance performance (see figure 1) with low da/dN value.
The application of table 1 beta-phase transformation point thermal treatment process on the tough titanium alloy die forging spare of height
Embodiment two:
The performance comparison of novel beta-phase transformation point thermal treatment process and conventional β thermal treatment process, conventional alpha+beta thermal treatment process (common annealing) the results are shown in Table shown in 2.As known from Table 2, can obtain the matched well of intensity-plasticity by novel beta-phase transformation point thermal treatment process, wherein, novel beta-phase transformation point thermal treatment process can obtain than the better plasticity of conventional β thermal treatment process, and KIC is suitable with it, KIC than conventional alpha+beta thermal treatment process is higher simultaneously, and plasticity is suitable with it.
The novel β thermal treatment process of table 2 is in the application (40mm slab) of TC4 alloy
Embodiment three:
Bar performance situation after the accurate β art breading is shown in Table 3.
The mechanical property of table 3 TC21 titanium alloy φ 90mm bar after accurate β thermal treatment
| Accurate β thermal treatment | σ bMPa | σ 0.2Mpa | δ 5％ | ψ ％ |
| 967℃/15min | 1190 | 1073 | 10.5 | 23.7 |
| 967℃/30min | 1153 | 1047 | 8.0 | 15.3 |
| 967℃/45min | 1137 | 1040 | 12.3 | 12.3 |
Embodiment four:
Mechanical property was shown in Table 4 after medium tenacity titanium alloy TC 4-DT adopted accurate β art breading, and the da/dN curve is seen shown in Figure 2, as can be seen, through obtaining best intensity-plasticity-toughness and minimum da/dN value after the accurate β art breading, wherein, KIC is up to more than 95, and da/dN works as
The time be lower than 8～9 * 10-9m/ week (R=0.1).
Table 4 TC4-DT alloy 30mm slab room temperature typical case tensile property
Technical solution of the present invention is compared with present technology can obtain the high-ductility lamellar structure, has solved the low key problem in technology of lamellar structure plasticity.Its plasticity is the same with the basket tissue, and fracture toughness property, fatigue crack growth resistance, creep resistance etc. then are significantly higher than the bifurcation tissue, can make work in-process and parts such as titanium alloy structure spare.
Claims (8)
1. beta-phase transformation point thermal treatment process for titanium alloy, the titanium alloy type that it was suitable for is nearly alpha titanium alloy and alpha-beta Type Titanium Alloy, it is characterized in that: this technology may further comprise the steps:
(1). the preheating insulation of titanium alloy forging (or workpiece), titanium alloy forging (or workpiece) is placed on preheating in the resistance furnace, preheating temperature is beta transformation point (T
β) following 20 ℃～40 ℃, i.e. T
β-(20 °～40) ℃, stove calculates soaking time, soaking time t (min)=η * δ after arriving preheating temperature
Max, δ
Max(mm) be the maximum cross-section thickness of forging, η is a heating coefficient, and the value of the preheating heating coefficient η of forging (or workpiece) is 0.4～0.7;
(2). the forging (or workpiece) behind step (1) preheating insulation is warming up to T with stove
β-10 ℃～T
βCalculate soaking time after+40 ℃, the unanimity of the same step of calculation formula (1) of soaking time t (min), but the value of heating coefficient η is 0.1～0.5;
(3). with above-mentioned in preset temperature heating and the forging (or workpiece) after reaching predetermined soaking time come out of the stove rapid water-cooled or air cooling.
2. beta-phase transformation point thermal treatment process for titanium alloy according to claim 1 is characterized in that: in the resistance furnace effectively the maximum temperature deviation of workspace be not more than ± 10 ℃, forging (or workpiece) shove charge after furnace temperature arrives preheating temperature is placed in effective workspace.
3. beta-phase transformation point thermal treatment process for titanium alloy according to claim 1 is characterized in that: the heating and temperature control in the above-mentioned steps (2) is at T
β～T
βIn+10 ℃ of scopes.
4. beta-phase transformation point thermal treatment process for titanium alloy according to claim 1 is characterized in that: the titanium alloy type that is applicable to this kind thermal treatment process is that nearly alpha titanium alloy and alpha-beta Type Titanium Alloy are the forging with bifurcation tissue signature (or workpiece) through forging of alpha+beta district or moulding.
5. beta-phase transformation point thermal treatment process for titanium alloy, the titanium alloy type that it was suitable for is nearly alpha titanium alloy and alpha-beta Type Titanium Alloy, it is characterized in that: this technology may further comprise the steps:
(1). forging (or workpiece) is without preheating insulation, direct heating calculates soaking time to T β-10 ℃～T β+40 ℃, the calculation formula of soaking time t (min) and aforesaid right require consistent in 1 the step (1), but the value of heating coefficient η is 0.3～0.8;
(2). with above-mentioned in preset temperature heating and the forging (or workpiece) after reaching predetermined soaking time come out of the stove rapid water-cooled or air cooling.
6. beta-phase transformation point thermal treatment process for titanium alloy according to claim 5 is characterized in that: in the resistance furnace effectively the maximum temperature deviation of workspace be not more than ± 10 ℃, forging (or workpiece) shove charge after furnace temperature arrives preheating temperature is placed in effective workspace.
7. beta-phase transformation point thermal treatment process for titanium alloy according to claim 5 is characterized in that: the heating and temperature control in the above-mentioned steps (1) is at T
β～T
βIn+10 ℃ of scopes.
8. beta-phase transformation point thermal treatment process for titanium alloy according to claim 5 is characterized in that: the titanium alloy type that is applicable to this kind thermal treatment process is that nearly alpha titanium alloy and alpha-beta Type Titanium Alloy are the forging with bifurcation tissue signature (or workpiece) through forging of alpha+beta district or moulding.
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| CN102851627A (en) * | 2012-09-21 | 2013-01-02 | 中国航空工业集团公司北京航空材料研究院 | Novel titanium alloy partitioned beta heat treatment process |
| CN103616268A (en) * | 2013-11-15 | 2014-03-05 | 中国第二重型机械集团德阳万航模锻有限责任公司 | Method for inspecting macrostructure defects of titanium alloy raw material |
| CN103668026A (en) * | 2013-12-13 | 2014-03-26 | 无锡透平叶片有限公司 | Quasi beta thermal treatment technology of TC4-DT titanium alloy structural component |
| CN103852360A (en) * | 2014-03-05 | 2014-06-11 | 中国航空工业集团公司北京航空材料研究院 | Method for inspecting nonuniformity of low power structure of titanium alloy |
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| CN106694770A (en) * | 2016-12-15 | 2017-05-24 | 陕西宏远航空锻造有限责任公司 | Forging method of TC21 titanium alloy |
| CN109234656A (en) * | 2018-11-08 | 2019-01-18 | 江苏理工学院 | A kind of predeformation heat treatment process improving metastable β Titanium-alloy intensity |
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| JPS61177361A (en) * | 1985-01-30 | 1986-08-09 | Sumitomo Metal Ind Ltd | Isometric crystallization method of (alpha+beta) type titanium alloy |
| CN1032962A (en) * | 1987-11-01 | 1989-05-17 | 西北工业大学 | Technology of equiaxial miniaturization of crystal microstructure of alpha+beta titanium alloys |
| JP3041277B2 (en) * | 1998-10-29 | 2000-05-15 | トヨタ自動車株式会社 | Method for producing particle-reinforced titanium alloy |
| JP4302265B2 (en) * | 1999-11-11 | 2009-07-22 | 大同特殊鋼株式会社 | Method for improving ductility of titanium alloy castings |
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| CN102851627B (en) * | 2012-09-21 | 2014-02-26 | 中国航空工业集团公司北京航空材料研究院 | Novel titanium alloy partitioned beta heat treatment process |
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| CN109234656A (en) * | 2018-11-08 | 2019-01-18 | 江苏理工学院 | A kind of predeformation heat treatment process improving metastable β Titanium-alloy intensity |
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