CN102943228A - 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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CN102943228A
CN102943228A CN201210540484XA CN201210540484A CN102943228A CN 102943228 A CN102943228 A CN 102943228A CN 201210540484X A CN201210540484X A CN 201210540484XA CN 201210540484 A CN201210540484 A CN 201210540484A CN 102943228 A CN102943228 A CN 102943228A
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time
titanium alloy
fire
forged
heat treated
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CN201210540484XA
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CN102943228B (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 the 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 becomes the key structure material of Aeronautics and Astronautics aircraft owing to have the excellent specific properties such as specific tenacity height, good corrosion resistance.Along with the raising of aeroplane performance, housing construction be increase trend with the titanium amount, at present the most representative F-22 opportunity of combat reach 41% of structural weight with the titanium amount, also reached 15% of structural weight with the titanium amount in the up-to-date large-scale Boeing 787.Since the sixties in 20th century, high reliability and long lifetime become aviation with structural part selection and the developing direction that manufactures and designs, design concept changes the 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 the good obdurability coupling of forging at positive optimization heat processing technique and development damage tolerance type alloy.

The mechanical property of diphasic titanium alloy is strong depends on its microstructure parameter.According to the difference of heat processing technique, usually 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 contain certain phase such as α such as axle such as grade in the tissue, it has preferably intensity and plasticity.And Widmannstatten structure has best damage tolerance performance.This is because the extensions path of crackle is comparatively tortuous in the Widmannstatten structure, has increased the length of crackle, thereby has absorbed more energy, reduces crack growth rate, has improved fracture toughness property.Yet, because original grain existence thick and the grain boundary α phase causes the plasticity of Widmannstatten structure lower, so usually be not used.For the aerospace structural part, what mostly adopt is equiaxed structure or bifurcation tissue, but the damage tolerance performance of this tissue that the traditional hot complete processing obtains is lower.Therefore, how to obtain desirable microstructure by optimizing heat processing technique, when 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.Adopt the diphasic titanium alloy large scale rod bar of the method preparation to have 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, improved the flaw detection rank of large scale rod bar; Adopt the diphasic titanium alloy large scale rod bar of the present invention's preparation to have 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 is characterized in that the method may further comprise the steps:

Step 1, the diphasic titanium alloy ingot casting is carried out cogging forge, obtain the cross section after the water-cooled and be 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 minute two fire and is finished, the deflection that time cogging of every fire is forged is 80%~90%, and before forging, time cogging of every fire all the diphasic titanium alloy ingot casting is carried out the fs heat treated, the temperature of carrying out the fs heat treated before wherein the first fire time cogging is forged is above 150 ℃~180 ℃ of beta transformation point, and the temperature of carrying out the fs heat treated before the second fire time cogging is forged is above 100 ℃~120 ℃ of beta transformation point;

Step 2, the first forging stock described in the step 1 is carried out the first upsetting pull forge, obtain the cross section after the water-cooled and be 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 minute 4~5 fire are finished, and all the first forging stock are carried out the subordinate phase heat treated before time the first upsetting pull forging of every fire, and the temperature of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is following 40~50 ℃ of beta transformation point;

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

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

Step 5, the 3rd forging stock described in the step 4 is carried out finished products process, obtaining diameter of section behind the naturally cooling 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 the 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 fs described in the step 1 is: the time t that carries out the fs heat treated before the first fire time cogging is forged 1Satisfy: 0.8 δ 1≤ t 1≤ 1.0 δ 1, δ wherein 1Be the diameter value of described diphasic titanium alloy ingot casting, δ 1Unit be mm, t 1Unit be min; When the temperature of diphasic titanium alloy ingot casting is lower than 930 ℃ after the first fire time cogging is forged, before forging, the second fire time cogging carries out the time t of fs heat treated 1' satisfy: 0.8 δ 1≤ t 1'≤1.0 δ 1, otherwise, before forging, the second fire time cogging carries out the time t of fs heat treated 1' satisfy: 0.5 δ 1≤ t 1'≤0.7 δ 1, δ wherein 1Be 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 the step 2 is: the time t that carries out the subordinate phase heat treated before time the first upsetting pull of every fire is forged 2All satisfy: 0.8 δ 2≤ t 2≤ 1.0 δ 2, δ wherein 2Be 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, the final forging temperature that time the first upsetting pull of every fire is forged in the step 2 all is not less than 830 ℃.

Above-mentioned a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability is characterized in that, the temperature that homogenizing described in the step 3 is processed is above 30 ℃~300 ℃ of beta transformation point, the time t that described homogenizing is processed 3Satisfy: t 3=0.6 δ 3, δ wherein 3Be 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 the step 4 is: the time t of heating before time the second upsetting pull of every fire is forged 4All satisfy: 0.6 δ 4≤ t 4≤ 1.0 δ 4, described δ 4Be 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, the final forging temperature that time the second upsetting pull of every fire is forged in the step 4 all is not less than 830 ℃.

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

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

1, the present invention to the diphasic titanium alloy large scale rod bar two-phase region first forge that i.e. the first upsetting pull is forged and again two-phase region forge i.e. the second upsetting pull and add the quick cooling process of mode that adopts water-cooled after a high temperature β district homogenizing is processed and forged between forging, and the two-phase region Heating temperature of forging is higher than the Heating temperature of first two-phase region forging again; Wherein high-temperature homogenization is processed, and can make alloying constituent more even, and the size of Original β grain, form, distribution etc. are more even in the tissue simultaneously; Adopt the mode of water-cooled to cool off fast after forging, can increase the crystallization nuclei in the process of cooling, thinning microstructure, the secondary α bar of separating out in the simultaneously β transformation tissue is 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 two-phase region heat of forging again, has effectively controlled the axle α phase content scope 30%~40% that waits; Carry out finished products after the forging and process, can not make the microstructure of alloy that large variation occurs, but in heating with at a slow speed in the process of cooling, secondary α bar can be grown up, chap, obtains size evenly and the chaotic secondary α bar that distributes, long-width ratio is about 10 ︰ 1; Simultaneously, owing to wait the 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, adopt the diphasic titanium alloy large scale rod bar of the present invention's preparation to have 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, improved the flaw detection rank of large scale rod bar; Adopt the diphasic titanium alloy large scale rod bar of the present invention's preparation to have good obdurability.

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

Description of drawings

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

Embodiment

Embodiment 1

The working method that present embodiment improves diphasic titanium alloy large scale rod bar obdurability may further comprise the steps:

Step 1, TC4 diphasic titanium alloy ingot casting is carried out cogging forge, obtain the first forging stock after the water-cooled; 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 the upsetting pull mode to divide two fire to finish, the deflection that time cogging of every fire is forged is 80%, and before forging, time cogging of every fire all the diphasic titanium alloy ingot casting is carried out the fs heat treated, the temperature of carrying out the fs heat treated before wherein the first fire time cogging is forged is above 150 ℃ of beta transformation point, the time of carrying out the fs heat treated before the first fire time cogging is forged is 368min, and the final forging temperature that the first fire time cogging is forged is 950 ℃; The temperature of carrying out the fs heat treated before the second fire time cogging is forged is above 100 ℃ of beta transformation point, and the time of carrying out the fs heat treated before the second fire time cogging is forged is 230min;

Step 2, the first forging stock described in the step 1 is carried out the first upsetting pull forge, obtain the second forging stock after the water-cooled; 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 the upsetting pull mode to divide 5 fire to finish, and before forging, time the first upsetting pull of every fire all the first forging stock is carried out the subordinate phase heat treated, the temperature of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is following 50 ℃ of beta transformation point, the time of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is 256min, and the final forging temperature that time the first upsetting pull of every fire is forged is 850 ℃;

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

Step 4, the second forging stock after homogenizing in the step 3 processed carry out the second upsetting pull and forge, and obtain the 3rd forging stock after the water-cooled; 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 minute 3 fire and is finished, and before forging, time the second upsetting pull of every fire all the second forging stock is carried out the phase III heat treated, the temperature of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is following 30 ℃ of beta transformation point, the time of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is 192min, and the final forging temperature that time the second upsetting pull of every fire is forged is 850 ℃;

Step 5, the 3rd forging stock described in the step 4 is carried out finished products process, the temperature that finished products is processed is 650 ℃, and the time that finished products is processed is 2h, and obtaining diameter of section behind the naturally cooling is the diphasic titanium alloy large scale rod bar of 250mm.

The mirco structure SEM photo of the TC4 diphasic titanium alloy large scale rod bar of employing present embodiment preparation as shown in Figure 1; As shown in Figure 1, adopt the homogeneous microstructure of the TC4 diphasic titanium alloy large scale rod bar of present embodiment preparation, wait 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.

Adopt the TC4 diphasic titanium alloy large scale rod bar of present embodiment preparation and the performance comparison data of the TC4 diphasic titanium alloy large scale rod bar that conventional forging process prepares to see Table 1.

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

As shown in Table 1, vertical performance and the lateral performance difference of the TC4 diphasic titanium alloy large scale rod bar of employing present embodiment preparation are less, have effectively reduced the anisotropy of TC4 diphasic titanium alloy large scale rod bar.Compare with traditional two-phase region forging process, present embodiment is by the working method of the processing of β district high-temperature homogenization, quick water-cooled and control forging deformation amount, effectively improved TC4 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, make flaw detection end wave attenuation level reduce by 20%, the clutter the level rise of single reflected signal 50%~100%.Adopt the TC4 diphasic titanium alloy large scale rod bar of present embodiment preparation in intensity and plasticity raising, with fracture toughness property K ICImproved 96%, illustrated and adopt the TC4 diphasic titanium alloy large scale rod bar of present embodiment preparation to have good obdurability.

Embodiment 2

The working method that present embodiment improves diphasic titanium alloy large scale rod bar obdurability may further comprise the steps:

Step 1, TC6 diphasic titanium alloy ingot casting is carried out cogging forge, obtain the first forging stock after the water-cooled; 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 the upsetting pull mode to divide two fire to finish, the deflection that time cogging of every fire is forged is 85%, and before forging, time cogging of every fire all the diphasic titanium alloy ingot casting is carried out the fs heat treated, the temperature of carrying out the fs heat treated before wherein the first fire time cogging is forged is above 160 ℃ of beta transformation point, carry out the time 600min of fs heat treated before the first fire time cogging is forged, the final forging temperature that the first fire time cogging is forged is 860 ℃; The temperature of carrying out the fs heat treated before the second fire time cogging is forged is above 110 ℃ of beta transformation point, and the time of carrying out the fs heat treated before the second fire time cogging is forged is 600min;

Step 2, the first forging stock described in the step 1 is carried out the first upsetting pull forge, obtain the second forging stock after the water-cooled; 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 minute 4 fire and is finished, and before forging, time the first upsetting pull of every fire all the first forging stock is carried out the subordinate phase heat treated, the temperature of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is following 40 ℃ of beta transformation point, the time of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is 480min, and the final forging temperature that time the first upsetting pull of every fire is forged is 830 ℃;

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

Step 4, the second forging stock after homogenizing in the step 3 processed carry out the second upsetting pull and forge, and obtain the 3rd forging stock after the water-cooled; 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 minute 4 fire and is finished, and before forging, time the second upsetting pull of every fire all the second forging stock is carried out the phase III heat treated, the temperature of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is following 20 ℃ of beta transformation point, the time of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is 480min, and the final forging temperature that time the second upsetting pull of every fire is forged is 830 ℃;

Step 5, the 3rd forging stock described in the step 4 is carried out finished products process, the temperature that finished products is processed is 650 ℃, and the time that described finished products is processed is 2h, and obtaining diameter of section behind the naturally cooling is the diphasic titanium alloy large scale rod bar of 360mm.

The vertical and horizontal performance difference of the TC6 diphasic titanium alloy large scale rod bar of employing present embodiment preparation is less, has effectively reduced the anisotropy of TC6 diphasic titanium alloy large scale rod bar.Compare with traditional two-phase region forging process, present embodiment is by the working method of the processing of β district high-temperature homogenization, quick water-cooled and control forging deformation amount, effectively improved TC6 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, make flaw detection end wave attenuation level reduce by 20%, the clutter the level rise of single reflected signal 50%~100%.Adopt the TC6 diphasic titanium alloy large scale rod bar of present embodiment preparation in intensity and plasticity raising, fracture toughness property has been improved 92%, illustrate and adopt the TC6 diphasic titanium alloy large scale rod bar of present embodiment preparation to have good obdurability.

Embodiment 3

The working method that present embodiment improves diphasic titanium alloy large scale rod bar obdurability may further comprise the steps:

Step 1, TC11 diphasic titanium alloy ingot casting is carried out cogging forge, obtain the first forging stock after the water-cooled; 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 the upsetting pull mode to divide two fire to finish, the deflection that time cogging of every fire is forged is 90%, and before forging, time cogging of every fire all the diphasic titanium alloy ingot casting is carried out the fs heat treated, the temperature of carrying out the fs heat treated before wherein the first fire time cogging is forged is above 180 ℃ of beta transformation point, the time of carrying out the fs heat treated before the first fire time cogging is forged is 800min, and the final forging temperature that the first fire time cogging is forged is 930 ℃; The temperature of carrying out the fs heat treated before the second fire time cogging is forged is above 120 ℃ of beta transformation point, and the time of carrying out the fs heat treated before the second fire time cogging is forged is 560min;

Step 2, the first forging stock described in the step 1 is carried out the first upsetting pull forge, obtain the second forging stock after the water-cooled; 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 minute 5 fire and is finished, and before forging, time the first upsetting pull of every fire all the first forging stock is carried out the subordinate phase heat treated, the temperature of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is following 50 ℃ of beta transformation point, the time of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is 558min, and the final forging temperature that time the second upsetting pull of every fire is forged is 870 ℃;

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

Step 4, the second forging stock after homogenizing in the step 3 processed carry out the second upsetting pull and forge, and obtain the 3rd forging stock after the water-cooled; 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 minute 3 fire and is finished, and before forging, time the second upsetting pull of every fire all the second forging stock is carried out the phase III heat treated, the temperature of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is following 30 ℃ of beta transformation point, the time of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is 558min, and the final forging temperature that time the second upsetting pull of every fire is forged is 870 ℃;

Step 5, the 3rd forging stock described in the step 4 is carried out finished products process, the temperature that finished products is processed is 650 ℃, and the time that described finished products is processed is 2h, and obtaining diameter of section behind the naturally cooling is the diphasic titanium alloy large scale rod bar of 450mm.

The vertical and horizontal performance difference of the TC11 diphasic titanium alloy large scale rod bar of employing present embodiment preparation is less, has effectively reduced the anisotropy of TC11 diphasic titanium alloy large scale rod bar.Compare with traditional two-phase region forging process, present embodiment is by the working method of the processing of β district high-temperature homogenization, quick water-cooled and control forging deformation amount, effectively improved TC11 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, make flaw detection end wave attenuation level reduce by 20%, the clutter the level rise of single reflected signal 50%~100%.Adopt the TC11 diphasic titanium alloy large scale rod bar of present embodiment preparation in intensity and plasticity raising, fracture toughness property has been improved 93%, illustrate and adopt the TC11 diphasic titanium alloy large scale rod bar of present embodiment preparation to have good obdurability.

Embodiment 4

The working method that present embodiment improves diphasic titanium alloy large scale rod bar obdurability may further comprise the steps:

Step 1, TC6 diphasic titanium alloy ingot casting is carried out cogging forge, obtain the first forging stock after the water-cooled; 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 the upsetting pull mode to divide two fire to finish, the deflection that time cogging of every fire is forged is 80%, and before forging, time cogging of every fire all the diphasic titanium alloy ingot casting is carried out the fs heat treated, the temperature of carrying out the fs heat treated before wherein the first fire time cogging is forged is above 150 ℃ of beta transformation point, carry out the time 560min of fs heat treated before the first fire time cogging is forged, the final forging temperature that the first fire time cogging is forged is 860 ℃; The temperature of carrying out the fs heat treated before the second fire time cogging is forged is above 110 ℃ of beta transformation point, and the time of carrying out the fs heat treated before the second fire time cogging is forged is 448min;

Step 2, the first forging stock described in the step 1 is carried out the first upsetting pull forge, obtain the second forging stock after the water-cooled; 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 minute 4 fire and is finished, and before forging, time the first upsetting pull of every fire all the first forging stock is carried out the subordinate phase heat treated, the temperature of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is following 45 ℃ of beta transformation point, the time of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is 460min, and the final forging temperature that time the first upsetting pull of every fire is forged is 830 ℃;

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

Step 4, the second forging stock after homogenizing in the step 3 processed carry out the second upsetting pull and forge, and obtain the 3rd forging stock after the water-cooled; 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 minute 4 fire and is finished, and before forging, time the second upsetting pull of every fire all the second forging stock is carried out the phase III heat treated, the temperature of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is following 25 ℃ of beta transformation point, the time of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is 414min, and the final forging temperature that time the second upsetting pull of every fire is forged is 830 ℃;

Step 5, the 3rd forging stock described in the step 4 is carried out finished products process, the temperature that finished products is processed is 650 ℃, and the time that described finished products is processed is 2h, and obtaining diameter of section behind the naturally cooling is the diphasic titanium alloy large scale rod bar of 300mm.

The vertical and horizontal performance difference of the TC6 diphasic titanium alloy large scale rod bar of employing present embodiment preparation is less, has effectively reduced the anisotropy of TC6 diphasic titanium alloy large scale rod bar.Compare with traditional two-phase region forging process, present embodiment is by the working method of the processing of β district high-temperature homogenization, quick water-cooled and control forging deformation amount, effectively improved TC6 diphasic titanium alloy large scale rod bar homogeneity of structure, refinement tissue, make flaw detection end wave attenuation level reduce by 20%, the clutter the level rise of single reflected signal 50%~100%.Adopt the TC6 diphasic titanium alloy large scale rod bar of present embodiment preparation in intensity and plasticity raising, fracture toughness property has been improved 98%, illustrate and adopt the TC6 diphasic titanium alloy large scale rod bar of present embodiment preparation to have good obdurability.

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

Claims (9)

1. working method that improves diphasic titanium alloy large scale rod bar obdurability is characterized in that the method may further comprise the steps:
Step 1, the diphasic titanium alloy ingot casting is carried out cogging forge, obtain the cross section after the water-cooled and be 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 minute two fire and is finished, the deflection that time cogging of every fire is forged is 80%~90%, and before forging, time cogging of every fire all the diphasic titanium alloy ingot casting is carried out the fs heat treated, the temperature of carrying out the fs heat treated before wherein the first fire time cogging is forged is above 150 ℃~180 ℃ of beta transformation point, and the temperature of carrying out the fs heat treated before the second fire time cogging is forged is above 100 ℃~120 ℃ of beta transformation point;
Step 2, the first forging stock described in the step 1 is carried out the first upsetting pull forge, obtain the cross section after the water-cooled and be 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 minute 4~5 fire are finished, and all the first forging stock are carried out the subordinate phase heat treated before time the first upsetting pull forging of every fire, and the temperature of carrying out the subordinate phase heat treated before time the first upsetting pull of every fire is forged is following 40~50 ℃ of beta transformation point;
Step 3, the second forging stock described in the step 2 is carried out homogenizing process, then water-cooled to 25 ℃ room temperature;
Step 4, the second forging stock after homogenizing is processed in the step 3 is carried out the second upsetting pull forge, obtain the cross section after the water-cooled and be the 3rd circular forging stock; The accumulative total deflection that described the second upsetting pull is forged is 80%~90%; Described the second upsetting pull is forged minute 3~4 fire and is finished, and all the second forging stock is carried out the phase III heat treated before time the second upsetting pull of every fire is forged, the temperature of carrying out the phase III heat treated before time the second upsetting pull of every fire is forged is following 20 ℃~30 ℃ of beta transformation point;
Step 5, the 3rd forging stock described in the step 4 is carried out finished products process, obtaining diameter of section behind the naturally cooling 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 the 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, it is characterized in that the concrete system of the heat treated of fs described in the step 1 is: the time t that carries out the fs heat treated before the first fire time cogging is forged 1Satisfy: 0.8 δ 1≤ t 1≤ 1.0 δ 1, δ wherein 1Be the diameter value of described diphasic titanium alloy ingot casting, δ 1Unit be mm, t 1Unit be min; When the temperature of diphasic titanium alloy ingot casting is lower than 930 ℃ after the first fire time cogging is forged, before forging, the second fire time cogging carries out the time t of fs heat treated 1' satisfy: 0.8 δ 1≤ t 1'≤1.0 δ 1, otherwise, before forging, the second fire time cogging carries out the time t of fs heat treated 1' satisfy: 0.5 δ 1≤ t 1'≤0.7 δ 1, δ wherein 1Be the diameter value of described diphasic titanium alloy ingot casting, δ 1Unit be mm, t 1' unit be min.
4. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1, it is characterized in that the concrete system of the heat treated of subordinate phase described in the step 2 is: the time t that carries out the subordinate phase heat treated before time the first upsetting pull of every fire is forged 2All satisfy: 0.8 δ 2≤ t 2≤ 1.0 δ 2, δ wherein 2Be the diameter value of described the first forging stock, δ 2Unit be mm, t 2Unit be min.
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 final forging temperature that time the first upsetting pull of every fire is forged in the step 2 all is not less than 830 ℃.
6. 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 that homogenizing described in the step 3 is processed is above 30 ℃~300 ℃ of beta transformation point, the time t that described homogenizing is processed 3Satisfy: t 3=0.6 δ 3, δ wherein 3Be the diameter value of described the second forging stock, δ 3Unit be mm, t 3Unit be min.
7. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1 is characterized in that, the concrete system of the heat treated of phase III described in the step 4 is: the time t of heating before time the second upsetting pull of every fire is forged 4All satisfy: 0.6 δ 4≤ t 4≤ 1.0 δ 4, described δ 4Be the diameter value of described the second forging stock, δ 4Unit be mm, t 4Unit be min.
8. a kind of working method that improves diphasic titanium alloy large scale rod bar obdurability according to claim 1 is characterized in that, the final forging temperature that time the second upsetting pull of every fire is forged in the step 4 all is not less than 830 ℃.
9. 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 that finished products described in the step 5 is processed is 650 ℃~750 ℃, and the time that described finished products is processed 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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CN103361586A (en) * 2013-07-31 2013-10-23 西北有色金属研究院 Processing method for raising strength and toughness of TC4-DT titanium alloy sheet materials
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CN107858618A (en) * 2017-11-10 2018-03-30 攀钢集团成都钛材有限公司江油分公司 A kind of preparation method of TC11 titanium alloy large sizes bar
CN108034911A (en) * 2017-12-05 2018-05-15 西部超导材料科技股份有限公司 The preparation method of the high uniformly TC11 alloy bar materials of blade
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CN108396270A (en) * 2018-05-29 2018-08-14 陕西华西钛业有限公司 A method of producing α, nearly α or alpha+beta titanium alloys bar
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