CN102943228B - Machining method for improving obdurability of two-phase titanium alloy large-size bar - Google Patents

Machining method for improving obdurability of two-phase titanium alloy large-size bar Download PDF

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CN102943228B
CN102943228B CN201210540484.XA CN201210540484A CN102943228B CN 102943228 B CN102943228 B CN 102943228B CN 201210540484 A CN201210540484 A CN 201210540484A CN 102943228 B CN102943228 B CN 102943228B
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forging
time
fire
titanium alloy
carried
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CN201210540484.XA
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CN102943228A (en
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韩栋
赵永庆
毛小南
洪权
郭萍
贾蔚菊
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西北有色金属研究院
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Abstract

The invention provides a machining method capable of improving the obdurability of a two-phase titanium alloy large-size bar, comprising the following steps of: 1, performing cogging forging on a two-phase titanium alloy cast ingot; 2, performing primary upsetting-drawing forging; 3, performing homogenization treatment; 4, performing secondary upsetting-drawing forging; and 5, performing annealing treatment on a finished product to obtain the two-phase titanium alloy large-size bar having a diameter of 250-450 mm. The two-phase titanium alloy large-size bar prepared by the machining method disclosed by the invention has a certain equiaxial alpha-phase content, original beta-crystalline grains are uniform and fine, and secondary alpha-strips are of a duplex organization structure with a certain length-width ratio, so that the flaw detection level of the large-size bar is raised while the strength and the fracture toughness of alloy is improved; and the two-phase titanium alloy large-size bar prepared by the machining method disclosed by the invention is good in obdurability.

Description

A kind of working method that improves diphasic titanium alloy large scale rod bar obdurability

Technical field

The invention belongs to titanium alloy processing technique field, be specifically related to a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability.

Background technology

Titanium alloy is the excellent specific property such as specific tenacity is high, good corrosion resistance owing to having, and becomes the key structure material of Aeronautics and Astronautics aircraft.Along with the raising of aeroplane performance, housing construction be increase trend by titanium amount, at present the most representative F-22 opportunity of combat reach 41% of structural weight by titanium amount, in up-to-date large-scale Boeing 787, also reached 15% of structural weight by titanium amount.Since the sixties in 20th century, the developing direction that high reliability and long lifetime become aviation structural part selection and manufacture and design, design concept changes damage tolerance design concept into by simple Static Strength Design of past, and selection criterion correspondingly also changes thereupon.Based on the needs of damage tolerance design concept, various countries all obtain at positive optimization heat processing technique and development damage tolerance type alloy the obdurability coupling that forging is good.

What the mechanical property of diphasic titanium alloy was strong depends on its microstructure parameter.According to the difference of heat processing technique, conventionally can obtain four kinds of typical microtextures, i.e. equiaxed structure, bifurcation tissue, basket tissue and Widmannstatten structure.Wherein, equiaxed structure and bifurcation tissue, owing to containing certain phase such as α such as axle such as grade in tissue, it has good intensity and plasticity.And Widmannstatten structure has best damage tolerance performance.This is because the extensions path of crackle is comparatively tortuous in Widmannstatten structure, has increased the length of crackle, thereby has absorbed more energy, reduces crack growth rate, has improved fracture toughness property.But, because original grain is thick and the existence of grain boundary α phase causes the plasticity of Widmannstatten structure lower, so be not conventionally used.For structural part for aerospace, what mostly adopt is equiaxed structure or bifurcation tissue, but the damage tolerance performance of this tissue that traditional heat processing technique obtains is lower.Therefore, how to obtain desirable microstructure by optimizing heat processing technique, in improving alloy strength, significantly improve the fracture toughness property of alloy, become the key of excavating traditional diphasic titanium alloy performance potential.

Summary of the invention

Technical problem to be solved by this invention is for above-mentioned the deficiencies in the prior art, and a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability is provided.The diphasic titanium alloy large scale rod bar that adopts the method to prepare has certain phase content such as the axle α of grade, even, the tiny and secondary α bar of Original β grain has the bifurcation weave construction of certain long-width ratio, when alloy strength and fracture toughness property are improved, improve the flaw detection rank of large scale rod bar; The diphasic titanium alloy large scale rod bar that adopts the present invention to prepare has good obdurability.

For solving the problems of the technologies described above, the technical solution used in the present invention is: a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, it is characterized in that, and the method comprises the following steps:

Step 1, diphasic titanium alloy ingot casting is carried out to cogging forging, after water-cooled, obtaining cross section is the first circular forging stock; The cross section of described diphasic titanium alloy ingot casting is that diameter is the circle of 460mm~800mm; Described cogging is forged point two fire and is completed, the deflection that time cogging of every fire is forged is 80%~90%, and time cogging of every fire is all carried out first stage heat treated to diphasic titanium alloy ingot casting before forging, wherein before forging, to carry out the temperature of first stage heat treated be above 150 DEG C~180 DEG C of beta transformation point in the first fire time cogging, and first stage heat treated is carried out in the second fire time cogging temperature before forging is above 100 DEG C~120 DEG C of beta transformation point;

Step 2, the first forging stock described in step 1 is carried out to the first upsetting pull forging, after water-cooled, obtaining cross section is the second circular forging stock; The accumulative total deflection that described the first upsetting pull is forged is 70%~80%; Described the first upsetting pull forging point 4~5 fire complete, and all the first forging stock are carried out to subordinate phase heat treated before time the first upsetting pull forging of every fire, and subordinate phase heat treated is carried out in time the first upsetting pull of every fire temperature before forging is following 40~50 DEG C of beta transformation point;

Step 3, the second forging stock described in step 2 is carried out to homogenizing processing, then water-cooled to 25 DEG C room temperature;

Step 4, be the 3rd circular forging stock by carrying out the second upsetting pull forging through homogenizing the second forging stock after treatment in step 3, obtaining cross section after water-cooled; The accumulative total deflection that described the second upsetting pull is forged is 80%~90%; Described the second upsetting pull is forged point 3~4 fire and is completed, and time the second upsetting pull of every fire is all carried out phase III heat treated to the second forging stock before forging, phase III heat treated is carried out in time the second upsetting pull of every fire temperature before forging is following 20 DEG C~30 DEG C of beta transformation point;

Step 5, the 3rd forging stock described in step 4 is carried out to finished products processing, after naturally cooling, obtaining diameter of section is the diphasic titanium alloy large scale rod bar of 250mm~450mm.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the ingot casting of diphasic titanium alloy described in step 1 is TC4 titan alloy casting ingot, TC6 titan alloy casting ingot or TC11 titan alloy casting ingot.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the concrete system of the heat treated of first stage described in step 1 is: the time t of first stage heat treated is carried out in the first fire time cogging before forging 1meet: 0.8 δ 1≤ t 1≤ 1.0 δ 1, wherein δ 1for the diameter value of described diphasic titanium alloy ingot casting, δ 1unit be mm, t 1unit be min; When after the first fire time cogging is forged, the temperature of diphasic titanium alloy ingot casting is lower than 930 DEG C, the time t of first stage heat treated is carried out in the second fire time cogging before forging 1' meet: 0.8 δ 1≤ t 1'≤1.0 δ 1, otherwise the time t of first stage heat treated is carried out in the second fire time cogging before forging 1' meet: 0.5 δ 1≤ t 1'≤0.7 δ 1, wherein δ 1for the diameter value of described diphasic titanium alloy ingot casting, δ 1unit be mm, t 1' unit be min.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the concrete system of the heat treated of subordinate phase described in step 2 is: the time t of subordinate phase heat treated is carried out in time the first upsetting pull of every fire before forging 2all meet: 0.8 δ 2≤ t 2≤ 1.0 δ 2, wherein δ 2for the diameter value of described the first forging stock, δ 2unit be mm, t 2unit be min.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, in step 2, the final forging temperature of every fire time the first upsetting pull forging is all not less than 830 DEG C.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the temperature of the processing of homogenizing described in step 3 is above 30 DEG C~300 DEG C of beta transformation point, the time t of described homogenizing processing 3meet: t 3=0.6 δ 3, wherein δ 3for the diameter value of described the second forging stock, δ 3unit be mm, t 3unit be min.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the concrete system of the heat treated of phase III described in step 4 is: the time t that time the second upsetting pull of every fire is heated before forging 4all meet: 0.6 δ 4≤ t 4≤ 1.0 δ 4, described δ 4for the diameter value of described the second forging stock, δ 4unit be mm, t 4unit be min.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, in step 4, the final forging temperature of every fire time the second upsetting pull forging is all not less than 830 DEG C.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the temperature of the processing of finished products described in step 5 is 650 DEG C~750 DEG C, and the time of described finished products processing is 1h~2h.

The present invention compared with prior art has the following advantages:

1, the present invention diphasic titanium alloy large scale rod bar is forged in two-phase region first to i.e. the first upsetting pull is forged and again two-phase region forge the quick cooling process of mode that adopts water-cooled i.e. the second upsetting pull adds a high temperature β district homogenizing to process and forge between forging after, and the Heating temperature that forge two-phase region is again higher than the Heating temperature that forges two-phase region first; Wherein high-temperature homogenization processing, can make alloying constituent more even, and in tissue, the size of Original β grain, form, distribution etc. are more even simultaneously; After forging, adopt the mode of water-cooled cooling fast, can increase the crystallization nuclei in process of cooling, thinning microstructure, the secondary α bar of separating out in the tissue of β transformation is simultaneously tiny, chaotic; In two-phase region forging process again, fine second α bar is broken, nodularization, thereby obtains the tiny axle shape α phase that waits, and the heat that forge two-phase region again, has effectively controlled the axle α phase content scope 30%~40% that waits; After forging, carry out finished products processing, can not make the microstructure of alloy that large variation occurs, but in heating with at a slow speed in process of cooling, secondary α bar can be grown up, chap, obtains size evenly and the secondary α bar that distributes chaotic, long-width ratio is about 10 ︰ 1; Meanwhile, owing to waiting existence of axle α phase, limited growing up of β crystal grain, can obtain tiny Original β grain, grain-size is 10 μ m~20 μ m.

2, the diphasic titanium alloy large scale rod bar that adopts the present invention to prepare has the axle α phase contents such as certain, even, the tiny and secondary α bar of Original β grain has the bifurcation weave construction of certain long-width ratio, when alloy strength and fracture toughness property are improved, improve the flaw detection rank of large scale rod bar; The diphasic titanium alloy large scale rod bar that adopts the present invention to prepare has good obdurability.

Below in conjunction with drawings and Examples, the present invention is described in further detail.

Brief description of the drawings

Fig. 1 is the mirco structure SEM photo of the diphasic titanium alloy large scale rod bar prepared of the embodiment of the present invention 1.

Embodiment

Embodiment 1

The working method that the present embodiment improves diphasic titanium alloy large scale rod bar obdurability comprises the following steps:

Step 1, TC4 diphasic titanium alloy ingot casting is carried out to cogging forging, after water-cooled, obtain the first forging stock; The cross section of described diphasic titanium alloy ingot casting is that diameter is the circle of 460mm; The cross section of described the first forging stock is that diameter is the circle of 320mm; Described cogging is forged and is adopted upsetting pull mode to divide two fire to complete, the deflection that time cogging of every fire is forged is 80%, and time cogging of every fire is all carried out first stage heat treated to diphasic titanium alloy ingot casting before forging, the temperature of wherein carrying out first stage heat treated before time cogging forging of the first fire is above 150 DEG C of beta transformation point, first stage heat treated is carried out in the first fire time cogging time before forging is 368min, and the final forging temperature that the first fire time cogging is forged is 950 DEG C; First stage heat treated is carried out in the second fire time cogging temperature before forging is above 100 DEG C of beta transformation point, and first stage heat treated is carried out in the second fire time cogging time before forging is 230min;

Step 2, the first forging stock described in step 1 is carried out to the first upsetting pull forging, after water-cooled, obtain the second forging stock; The cross section of described the second forging stock is that diameter is the circle of 320mm; The accumulative total deflection that described the first upsetting pull is forged is 70%; Described the first upsetting pull is forged and is adopted upsetting pull mode to divide 5 fire to complete, and time the first upsetting pull of every fire is all carried out subordinate phase heat treated to the first forging stock before forging, subordinate phase heat treated is carried out in time the first upsetting pull of every fire temperature before forging is following 50 DEG C of beta transformation point, subordinate phase heat treated is carried out in time the first upsetting pull of every fire time before forging is 256min, and the final forging temperature of every fire time the first upsetting pull forging is 850 DEG C;

Step 3, the second forging stock described in step 2 is carried out to homogenizing processing, then water-cooled to 25 DEG C room temperature; The temperature of described homogenizing processing is above 30 DEG C of beta transformation point, and the time of described homogenizing processing is 192min;

Step 4, the second forging stock after treatment homogenizing in step 3 is carried out to the second upsetting pull forging, after water-cooled, obtain the 3rd forging stock; The cross section of described the 3rd forging stock is that diameter is the circle of 250mm; The accumulative total deflection that described the second upsetting pull is forged is 80%; Described the second upsetting pull is forged point 3 fire and is completed, and time the second upsetting pull of every fire is all carried out phase III heat treated to the second forging stock before forging, phase III heat treated is carried out in time the second upsetting pull of every fire temperature before forging is following 30 DEG C of beta transformation point, phase III heat treated is carried out in time the second upsetting pull of every fire time before forging is 192min, and the final forging temperature of every fire time the second upsetting pull forging is 850 DEG C;

Step 5, the 3rd forging stock described in step 4 is carried out to finished products processing, the temperature of finished products processing is 650 DEG C, and the time of finished products processing is 2h, and after naturally cooling, obtaining diameter of section is the diphasic titanium alloy large scale rod bar of 250mm.

The mirco structure SEM photo of TC4 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment as shown in Figure 1; As shown in Figure 1, the homogeneous microstructure of TC4 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment, waits axle α phase content 30%~40%, its distribution and size are evenly, secondary precipitation α bar size is short and small, and long-width ratio is about 10:1, and Original β grain is even, tiny.

The performance comparison data of TC4 diphasic titanium alloy large scale rod bar prepared by TC4 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment and conventional forging process are in table 1.

TC4 large scale rod bar prepared by table 1 embodiment of the present invention 1 and existing TC4 large scale rod bar performance comparison data sheet

As shown in Table 1, longitudinal performance and the lateral performance difference of TC4 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment are less, have effectively reduced the anisotropy of TC4 diphasic titanium alloy large scale rod bar.Compared with traditional two-phase region forging process, the present embodiment is by the working method of the high-temperature homogenization processing of β district, fast water-cooled and control forging deformation amount, effectively improve TC4 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, the end wave attenuation level that makes to detect a flaw has reduced by 20%, and the clutter level of single reflected signal has improved 50%~100%.TC4 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment is in intensity and plasticity raising, by fracture toughness property K iCimprove 96%, illustrated that the TC4 diphasic titanium alloy large scale rod bar that adopts the present embodiment to prepare has good obdurability.

Embodiment 2

The working method that the present embodiment improves diphasic titanium alloy large scale rod bar obdurability comprises the following steps:

Step 1, TC6 diphasic titanium alloy ingot casting is carried out to cogging forging, after water-cooled, obtain the first forging stock; The cross section of described diphasic titanium alloy ingot casting is that diameter is the circle of 600mm; The cross section of described the first forging stock is that diameter is the circle of 480mm; Described cogging is forged and is adopted upsetting pull mode to divide two fire to complete, the deflection that time cogging of every fire is forged is 85%, and time cogging of every fire is all carried out first stage heat treated to diphasic titanium alloy ingot casting before forging, the temperature of wherein carrying out first stage heat treated before time cogging forging of the first fire is above 160 DEG C of beta transformation point, the time 600min of first stage heat treated is carried out in the first fire time cogging before forging, the final forging temperature that the first fire time cogging is forged is 860 DEG C; First stage heat treated is carried out in the second fire time cogging temperature before forging is above 110 DEG C of beta transformation point, and first stage heat treated is carried out in the second fire time cogging time before forging is 600min;

Step 2, the first forging stock described in step 1 is carried out to the first upsetting pull forging, after water-cooled, obtain the second forging stock; The cross section of described the second forging stock is that diameter is the circle of 480mm; The accumulative total deflection that described the first upsetting pull is forged is 75%; Described the first upsetting pull is forged point 4 fire and is completed, and time the first upsetting pull of every fire is all carried out subordinate phase heat treated to the first forging stock before forging, subordinate phase heat treated is carried out in time the first upsetting pull of every fire temperature before forging is following 40 DEG C of beta transformation point, subordinate phase heat treated is carried out in time the first upsetting pull of every fire time before forging is 480min, and the final forging temperature of every fire time the first upsetting pull forging is 830 DEG C;

Step 3, the second forging stock described in step 2 is carried out to homogenizing processing, then water-cooled to 25 DEG C room temperature; The temperature of described homogenizing processing is above 100 DEG C of beta transformation point, and the time of described homogenizing processing is 288min;

Step 4, the second forging stock after treatment homogenizing in step 3 is carried out to the second upsetting pull forging, after water-cooled, obtain the 3rd forging stock; The cross section of described the 3rd forging stock is that diameter is the circle of 360mm; The accumulative total deflection that described the second upsetting pull is forged is 85%; Described the second upsetting pull is forged point 4 fire and is completed, and time the second upsetting pull of every fire is all carried out phase III heat treated to the second forging stock before forging, phase III heat treated is carried out in time the second upsetting pull of every fire temperature before forging is following 20 DEG C of beta transformation point, phase III heat treated is carried out in time the second upsetting pull of every fire time before forging is 480min, and the final forging temperature of every fire time the second upsetting pull forging is 830 DEG C;

Step 5, the 3rd forging stock described in step 4 is carried out to finished products processing, the temperature of finished products processing is 650 DEG C, and the time of described finished products processing is 2h, and after naturally cooling, obtaining diameter of section is the diphasic titanium alloy large scale rod bar of 360mm.

The vertical and horizontal performance difference of TC6 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment is less, has effectively reduced the anisotropy of TC6 diphasic titanium alloy large scale rod bar.Compared with traditional two-phase region forging process, the present embodiment is by the working method of the high-temperature homogenization processing of β district, fast water-cooled and control forging deformation amount, effectively improve TC6 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, the end wave attenuation level that makes to detect a flaw has reduced by 20%, and the clutter level of single reflected signal has improved 50%~100%.TC6 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment, in intensity and plasticity raising, has improved 92% by fracture toughness property, illustrates that the TC6 diphasic titanium alloy large scale rod bar that adopts the present embodiment to prepare has good obdurability.

Embodiment 3

The working method that the present embodiment improves diphasic titanium alloy large scale rod bar obdurability comprises the following steps:

Step 1, TC11 diphasic titanium alloy ingot casting is carried out to cogging forging, after water-cooled, obtain the first forging stock; The cross section of described diphasic titanium alloy ingot casting is that diameter is the circle of 800mm; The cross section of described the first forging stock is that diameter is the circle of 620mm; Described cogging is forged and is adopted upsetting pull mode to divide two fire to complete, the deflection that time cogging of every fire is forged is 90%, and time cogging of every fire is all carried out first stage heat treated to diphasic titanium alloy ingot casting before forging, the temperature of wherein carrying out first stage heat treated before time cogging forging of the first fire is above 180 DEG C of beta transformation point, first stage heat treated is carried out in the first fire time cogging time before forging is 800min, and the final forging temperature that the first fire time cogging is forged is 930 DEG C; First stage heat treated is carried out in the second fire time cogging temperature before forging is above 120 DEG C of beta transformation point, and first stage heat treated is carried out in the second fire time cogging time before forging is 560min;

Step 2, the first forging stock described in step 1 is carried out to the first upsetting pull forging, after water-cooled, obtain the second forging stock; The cross section of described the second forging stock is that diameter is the circle of 620mm; The accumulative total deflection that described the first upsetting pull is forged is 80%; Described the first upsetting pull is forged point 5 fire and is completed, and time the first upsetting pull of every fire is all carried out subordinate phase heat treated to the first forging stock before forging, subordinate phase heat treated is carried out in time the first upsetting pull of every fire temperature before forging is following 50 DEG C of beta transformation point, phase III heat treated is carried out in time the second upsetting pull of every fire time before forging is 558min, and the final forging temperature of every fire time the second upsetting pull forging is 870 DEG C;

Step 3, the second forging stock described in step 2 is carried out to homogenizing processing, then water-cooled to 25 DEG C room temperature; The temperature of described homogenizing processing is above 300 DEG C of beta transformation point, and the time of described homogenizing processing is 372min;

Step 4, the second forging stock after treatment homogenizing in step 3 is carried out to the second upsetting pull forging, after water-cooled, obtain the 3rd forging stock; The cross section of described the 3rd forging stock is that diameter is the circle of 450mm; The accumulative total deflection that described the second upsetting pull is forged is 90%; Described the second upsetting pull is forged point 3 fire and is completed, and time the second upsetting pull of every fire is all carried out phase III heat treated to the second forging stock before forging, phase III heat treated is carried out in time the second upsetting pull of every fire temperature before forging is following 30 DEG C of beta transformation point, phase III heat treated is carried out in time the second upsetting pull of every fire time before forging is 558min, and the final forging temperature of every fire time the second upsetting pull forging is 870 DEG C; ;

Step 5, the 3rd forging stock described in step 4 is carried out to finished products processing, the temperature of finished products processing is 650 DEG C, and the time of described finished products processing is 2h, and after naturally cooling, obtaining diameter of section is the diphasic titanium alloy large scale rod bar of 450mm.

The vertical and horizontal performance difference of TC11 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment is less, has effectively reduced the anisotropy of TC11 diphasic titanium alloy large scale rod bar.Compared with traditional two-phase region forging process, the present embodiment is by the working method of the high-temperature homogenization processing of β district, fast water-cooled and control forging deformation amount, effectively improve TC11 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, the end wave attenuation level that makes to detect a flaw has reduced by 20%, and the clutter level of single reflected signal has improved 50%~100%.TC11 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment, in intensity and plasticity raising, has improved 93% by fracture toughness property, illustrates that the TC11 diphasic titanium alloy large scale rod bar that adopts the present embodiment to prepare has good obdurability.

Embodiment 4

The working method that the present embodiment improves diphasic titanium alloy large scale rod bar obdurability comprises the following steps:

Step 1, TC6 diphasic titanium alloy ingot casting is carried out to cogging forging, after water-cooled, obtain the first forging stock; The cross section of described diphasic titanium alloy ingot casting is that diameter is the circle of 560mm; The cross section of described the first forging stock is that diameter is the circle of 460mm; Described cogging is forged and is adopted upsetting pull mode to divide two fire to complete, the deflection that time cogging of every fire is forged is 80%, and time cogging of every fire is all carried out first stage heat treated to diphasic titanium alloy ingot casting before forging, the temperature of wherein carrying out first stage heat treated before time cogging forging of the first fire is above 150 DEG C of beta transformation point, the time 560min of first stage heat treated is carried out in the first fire time cogging before forging, the final forging temperature that the first fire time cogging is forged is 860 DEG C; First stage heat treated is carried out in the second fire time cogging temperature before forging is above 110 DEG C of beta transformation point, and first stage heat treated is carried out in the second fire time cogging time before forging is 448min;

Step 2, the first forging stock described in step 1 is carried out to the first upsetting pull forging, after water-cooled, obtain the second forging stock; The cross section of described the second forging stock is that diameter is the circle of 460mm; The accumulative total deflection that described the first upsetting pull is forged is 72%; Described the first upsetting pull is forged point 4 fire and is completed, and time the first upsetting pull of every fire is all carried out subordinate phase heat treated to the first forging stock before forging, subordinate phase heat treated is carried out in time the first upsetting pull of every fire temperature before forging is following 45 DEG C of beta transformation point, subordinate phase heat treated is carried out in time the first upsetting pull of every fire time before forging is 460min, and the final forging temperature of every fire time the first upsetting pull forging is 830 DEG C;

Step 3, the second forging stock described in step 2 is carried out to homogenizing processing, then water-cooled to 25 DEG C room temperature; The temperature of described homogenizing processing is above 100 DEG C of beta transformation point, and the time of described homogenizing processing is 276min;

Step 4, the second forging stock after treatment homogenizing in step 3 is carried out to the second upsetting pull forging, after water-cooled, obtain the 3rd forging stock; The cross section of described the 3rd forging stock is that diameter is the circle of 300mm; The accumulative total deflection that described the second upsetting pull is forged is 88%; Described the second upsetting pull is forged point 4 fire and is completed, and time the second upsetting pull of every fire is all carried out phase III heat treated to the second forging stock before forging, phase III heat treated is carried out in time the second upsetting pull of every fire temperature before forging is following 25 DEG C of beta transformation point, phase III heat treated is carried out in time the second upsetting pull of every fire time before forging is 414min, and the final forging temperature of every fire time the second upsetting pull forging is 830 DEG C;

Step 5, the 3rd forging stock described in step 4 is carried out to finished products processing, the temperature of finished products processing is 650 DEG C, and the time of described finished products processing is 2h, and after naturally cooling, obtaining diameter of section is the diphasic titanium alloy large scale rod bar of 300mm.

The vertical and horizontal performance difference of TC6 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment is less, has effectively reduced the anisotropy of TC6 diphasic titanium alloy large scale rod bar.Compared with traditional two-phase region forging process, the present embodiment is by the working method of the high-temperature homogenization processing of β district, fast water-cooled and control forging deformation amount, effectively improve TC6 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, the end wave attenuation level that makes to detect a flaw has reduced by 20%, and the clutter level of single reflected signal has improved 50%~100%.TC6 diphasic titanium alloy large scale rod bar prepared by employing the present embodiment, in intensity and plasticity raising, has improved 98% by fracture toughness property, illustrates that the TC6 diphasic titanium alloy large scale rod bar that adopts the present embodiment to prepare has good obdurability.

The above, be only preferred embodiment of the present invention, not the present invention imposed any restrictions.Every any simple modification of above embodiment being done according to invention technical spirit, change and equivalence change, and all still belong in the protection domain of technical solution of the present invention.

Claims (5)

1. a working method that improves diphasic titanium alloy large scale rod bar obdurability, is characterized in that, the method comprises the following steps:
Step 1, diphasic titanium alloy ingot casting is carried out to cogging forging, after water-cooled, obtaining cross section is the first circular forging stock; The cross section of described diphasic titanium alloy ingot casting is that diameter is the circle of 460mm~800mm; Described cogging is forged point two fire and is completed, the deflection that time cogging of every fire is forged is 80%~90%, and time cogging of every fire is all carried out first stage heat treated to diphasic titanium alloy ingot casting before forging, wherein before forging, to carry out the temperature of first stage heat treated be above 150 DEG C~180 DEG C of beta transformation point in the first fire time cogging, and first stage heat treated is carried out in the second fire time cogging temperature before forging is above 100 DEG C~120 DEG C of beta transformation point; The concrete system of described first stage heat treated is: the time t of first stage heat treated is carried out in the first fire time cogging before forging 1meet: 0.8 δ 1≤ t 1≤ 1.0 δ 1, wherein δ 1for the diameter value of described diphasic titanium alloy ingot casting, δ 1unit be mm, t 1unit be min; When after the first fire time cogging is forged, the temperature of diphasic titanium alloy ingot casting is lower than 930 DEG C, the time t of first stage heat treated is carried out in the second fire time cogging before forging 1' meet: 0.8 δ 1≤ t 1'≤1.0 δ 1, otherwise the time t of first stage heat treated is carried out in the second fire time cogging before forging 1' meet: 0.5 δ 1≤ t 1'≤0.7 δ 1, wherein δ 1for the diameter value of described diphasic titanium alloy ingot casting, δ 1unit be mm, t 1' unit be min;
Step 2, the first forging stock described in step 1 is carried out to the first upsetting pull forging, after water-cooled, obtaining cross section is the second circular forging stock; The accumulative total deflection that described the first upsetting pull is forged is 70%~80%; Described the first upsetting pull forging point 4~5 fire complete, and all the first forging stock are carried out to subordinate phase heat treated before time the first upsetting pull forging of every fire, and subordinate phase heat treated is carried out in time the first upsetting pull of every fire temperature before forging is following 40~50 DEG C of beta transformation point; The concrete system of described subordinate phase heat treated is: the time t of subordinate phase heat treated is carried out in time the first upsetting pull of every fire before forging 2all meet: 0.8 δ 2≤ t 2≤ 1.0 δ 2, wherein δ 2for the diameter value of described the first forging stock, δ 2unit be mm, t 2unit be min;
Step 3, the second forging stock described in step 2 is carried out to homogenizing processing, then water-cooled to 25 DEG C room temperature; The temperature of described homogenizing processing is above 30 DEG C~300 DEG C of beta transformation point, the time t of described homogenizing processing 3meet: t 3=0.6 δ 3, wherein δ 3for the diameter value of described the second forging stock, δ 3unit be mm, t 3unit be min;
Step 4, be the 3rd circular forging stock by carrying out the second upsetting pull forging through homogenizing the second forging stock after treatment in step 3, obtaining cross section after water-cooled; The accumulative total deflection that described the second upsetting pull is forged is 80%~90%; Described the second upsetting pull is forged point 3~4 fire and is completed, and time the second upsetting pull of every fire is all carried out phase III heat treated to the second forging stock before forging, phase III heat treated is carried out in time the second upsetting pull of every fire temperature before forging is following 20 DEG C~30 DEG C of beta transformation point; The concrete system of described phase III heat treated is: the time t that time the second upsetting pull of every fire is heated before forging 4all meet: 0.6 δ 4≤ t 4≤ 1.0 δ 4, described δ 4for the diameter value of described the second forging stock, δ 4unit be mm, t 4unit be min;
Step 5, the 3rd forging stock described in step 4 is carried out to finished products processing, after naturally cooling, obtaining diameter of section is the diphasic titanium alloy large scale rod bar of 250mm~450mm.
2. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1, is characterized in that, the ingot casting of diphasic titanium alloy described in step 1 is TC4 titan alloy casting ingot, TC6 titan alloy casting ingot or TC11 titan alloy casting ingot.
3. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1, is characterized in that, in step 2, the final forging temperature of every fire time the first upsetting pull forging is all not less than 830 DEG C.
4. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1, is characterized in that, in step 4, the final forging temperature of every fire time the second upsetting pull forging is all not less than 830 DEG C.
5. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1, is characterized in that, the temperature of the processing of finished products described in step 5 is 650 DEG C~750 DEG C, and the time of described finished products processing is 1h~2h.
CN201210540484.XA 2012-12-14 2012-12-14 Machining method for improving obdurability of two-phase titanium alloy large-size bar CN102943228B (en)

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