CN102230097B - Preparation method of titanium alloy bars - Google Patents

Preparation method of titanium alloy bars Download PDF

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CN102230097B
CN102230097B CN2011100790251A CN201110079025A CN102230097B CN 102230097 B CN102230097 B CN 102230097B CN 2011100790251 A CN2011100790251 A CN 2011100790251A CN 201110079025 A CN201110079025 A CN 201110079025A CN 102230097 B CN102230097 B CN 102230097B
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forging
titanium alloy
temperature
less
rod bar
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CN2011100790251A
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CN102230097A (en
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赵永庆
陈军
杨海瑛
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西北有色金属研究院
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Abstract

The invention discloses a preparation method of titanium alloy bars. The finished titanium alloy bars are prepared through the following steps: heating prepared TC4-DT titanium alloy ingots to 1150 to 1200 DEG C; cogging and forging a beta phase zone of the ingots with a fast forging press; heating forging stocks to Tbeta-50 to Tbeta-20 DEG C through a resistance furnace; carrying out repeated upsetting and extension forging by the fast forging press; forging forged stocks to required dimensions at a forging temperature of Tbeta-70 to Tbeta-40 DEG C to obtain titanium alloy bars with uniform tissues; and carrying out duplex annealing on the obtained titanium alloy bars with the uniform tissues. The preparation method has the advantages of convenient operation, strong controllable technology, high stability of batches of prepared bars, and good repeatability. The titanium alloy bars prepared through the method of the present invention has the advantages of strong plasticity, qualified macrostructure, high strength and fracture toughness, and low fatigue crack growth rate.

Description

A kind of preparation method of titanium alloy rod bar

Technical field

The invention belongs to the alloy preparing technical field, be specifically related to a kind of preparation method of titanium alloy rod bar.

Background technology

For in for the strong high damage tolerance Type Titanium Alloy, what at present external consumption was maximum is Ti-6Al-4V ELI (ultralow gap) alloy.This alloy is sophisticated typical case (alpha+beta) diphasic titanium alloy; It is development and come on the basis of general T i-6Al-4V alloy; Surplus the history that various countries research and develop in succession existing 30 year and alloy designations separately arranged; Like UNS R56401, ASTM F468, Grade 23, AMS4930, the Ti-64ELI of the U.S., the IMI318ELI of Britain, the TA6VELI of France etc.Its performance characteristic is: fracture toughness property K ICCan reach 85MPam 1/2More than, fatigue crack growth rate is 8 * 10 -6~8 * 10 -5Between the mm/cycle, compare with general T C4 alloy phase, loss of strength 100MPa, the strength level of its Φ 100mm~Φ 180mm big stick-means of intimidation is about 825MPa~875MPa, the performance newspaper measured value of the above big stick-means of intimidation of Φ 180mm.It is used with the U.S. is main, like main rotor, the tail rotor rotatable parts of the tailplane rotating shaft of F-16 fighter, UH60A " blackhawk ", SH60B " Hai Ying ", CH53E vertiplanes such as " super kind of horses ".The application of the Ti-6Al-4V ELI titanium alloy of the U.S. the 4th generation opportunity of combat F22, third generation opportunity of combat F/A-18E/F etc. has got into adopts the more ripe application stage of large-scale integral stamp work; Last Ti-6Al-4V (the containing ELI) consumption of F-22 has accounted for 36% of aircraft structure weight.

For alpha and beta type titan alloy, microstructure morphology depends primarily on Chemical Composition, deformation technique and the heat treating regime of alloy, and the microtexture of diphasic titanium alloy roughly is divided into four types: equiaxed structure, bifurcation tissue, basket tissue, Widmannstatten structure.For general T C4 alloy, equiaxed structure has higher plasticity, and especially relative reduction in area is higher, has high plasticity and thermostability, but material antifatigue crack propagation ability and fracture toughness property are relatively poor.The bifurcation tissue has preferably strong plasticity and cooperates, and by the primary of proper ratio mutually and the bifurcation tissue of the secondary α phase composite of suitable long-width ratio, its antifatigue crack propagation ability and fracture toughness property are good.It is good that the basket tissue has fracture toughness property, and creep rupture strength is high, have high heat resistance and creep-resistant property, but plasticity, thermostability and fatigue property is lower.The method that obtains this tissue is that last fire heats blank in the β district, in the distortion of (alpha+beta) district or β end of extent.The fracture toughness property of Widmannstatten structure is better, but plasticity, fatigue property and tensile property are all lower.In actual production process, should avoid occurring Widmannstatten structure.

In order to improve the damage tolerance performance of material; Be the fracture toughness property and the fatigue crack growth rate of material; Developed alpha+beta phase region forging+β thermal treatment, perhaps β phase region forging+alpha+beta phase region thermal treatment, the thermal treatment of perhaps accurate β forging+alpha+beta phase region; Its purpose is in order to obtain all to have the lamellar structure or the basket tissue of high fracture toughness property and low fatigue crack growth rate; But β thermal treatment and β processing technology are more suitable in the final operation of the processing of forging, and changing forging and forging waste preparation of the waste base of forging generally is to carry out at the alpha+beta phase region, and purpose is in order to obtain uniform tissue.But material requires the stove temperature-controlled precision high in β phase region processing or β thermal treatment, and the control of soaking time is strict, prevents because stove runs temperature or the soaking time prolongation brings too growing up of material grains degree.But for suitability for industrialized production, same batch material is owing to the succession of forging, die forging, and soaking time unavoidably is not quite similar, and causes same batch forging tissue and the serious ununiformity of performance.Though β thermal treatment and β processing technology can obtain good fracture toughness property, fatigue crack growth rate, also can cause reduction of material plasticity and macrostructure defective simultaneously.

Summary of the invention

Technical problem to be solved by this invention is the deficiency to above-mentioned prior art, and a kind of preparation method of easy to operate, titanium alloy rod bar that process controllability is stronger is provided.Adopt the titanium alloy rod bar of this method preparation to have higher intensity and fracture toughness property, low fatigue crack growth rate.

For solving the problems of the technologies described above, the technical scheme that the present invention adopts is: a kind of preparation method of titanium alloy rod bar is characterized in that this method may further comprise the steps:

(1) ingot casting melting: Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium are packed into the alloy bag; Successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 420mm~Φ 720mm then; Or Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium is evenly mixed through mixer, successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 420mm~Φ 720mm then;

(2) gas furnace of employing resistance furnace or oxidizing atmosphere; TC4-DT titan alloy casting ingot described in the step (1) is heated to 1150 ℃~1200 ℃; Forge 2~3 fire with fast forging machine in the cogging of the β of titan alloy casting ingot phase region then and obtain forging stock; Every fire time forging ratio is not less than 1.3, and final forging temperature is not less than 850 ℃;

(3) adopt resistance furnace that forging stock described in the step (2) is heated to T β-50 ℃~T βAfter-20 ℃, with fast forging machine repeatedly jumping-up, pulling forge 3~6 fire, every fire time forging ratio is not less than 2.6, total forging ratio is not less than 10, final forging temperature is not less than 800 ℃, T βTransformation temperature for said forging stock;

(4) adopting the resistance furnace heating, is T with the forging stock after forging in the step (3) in forging temperature β-70 ℃~T βForge to desired size under-40 ℃ the condition, total forging ratio is not less than 3, and final forging temperature is not less than 750 ℃, obtains the titanium alloy rod bar of uniform formation;

(5) titanium alloy rod bar described in the step (4) is carried out double annealing and handle, obtain the finished product titanium alloy rod bar.

The system that double annealing described in the above-mentioned steps (5) is handled is: annealing for the first time is T in temperature β-50 ℃~T βBe incubated air cooling behind 0.3h~1.5h under-15 ℃ the condition, annealing for the second time is air cooling after being incubated 4h~8h under 540 ℃~600 ℃ the condition in temperature.

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

1, the present invention is easy to operate, process controllability is stronger, and the bar of preparation batch stability is high, good reproducibility.

2, adopt the TC4-DT bar plasticity of method preparation of the present invention strong, macrostructure is qualified, has higher intensity and fracture toughness property; And low fatigue crack growth rate; Its tensile strength surpasses 860MPa, and ys surpasses 750MPa, and unit elongation surpasses 8%; Relative reduction in area surpasses 15%, and fracture toughness property is greater than 90MPam 1/2, as stress ratio R=0.1, stress intensity factor Δ K=11MPam 1/2The time, the fatigue crack growth rate of titanium alloy rod bar is less than 8 * 10 -6Mm/cycle, each item index all meets the international advanced standard of like product.

Through embodiment, technical scheme of the present invention is done further detailed description below.

Embodiment

Embodiment 1

(1) ingot casting melting: 0 grade of Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium are packed into the alloy bag, and successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 570mm then; The weight percent of each composition of TC4-DT titan alloy casting ingot is Al:6.34%, V:4.21%, and O:0.09%, Fe:0.05%, C:0.02%, N:0.012%, H:0.007%, Ti are surplus;

(2) adopt resistance furnace, TC4-DT titan alloy casting ingot described in the step (1) is heated to 1200 ℃, forge machine soon with 1600T then and forge the inferior forging stock that obtains of 2 fire in the cogging of the β of titan alloy casting ingot phase region, every fire time forging ratio is not less than 1.3, and final forging temperature is not less than 850 ℃; The transformation temperature T of said forging stock βIt is 980 ℃;

(3) adopt resistance furnace that forging stock described in the step (2) is heated to T βAfter-20 ℃ (960 ℃), with fast forging machine repeatedly jumping-up, pulling forge 5 fire, every fire time forging ratio is not less than 2.6, total forging ratio is not less than 10, final forging temperature is not less than 800 ℃;

(4) adopting the resistance furnace heating, is T with the forging stock after forging in the step (3) in forging temperature βForge to desired size under the condition of-40 ℃ (940 ℃), total forging ratio is not less than 3, and final forging temperature is not less than 750 ℃, obtains the titanium alloy rod bar of uniform formation;

(5) titanium alloy rod bar described in the step (4) is carried out double annealing in resistance furnace and handle, obtain the finished product titanium alloy rod bar of Φ 90mm; The system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 0.3h under the condition of-15 ℃ (965 ℃), annealing for the second time are air cooling behind the insulation 6h under 570 ℃ the condition in temperature.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 2

Present embodiment is identical with the preparation method of embodiment 1, and wherein difference is: the specification of TC4-DT titan alloy casting ingot is Φ 650mm; Titan alloy casting ingot is heated to 1150 ℃, forges 3 fire with fast forging machine in the cogging of the β of titan alloy casting ingot phase region then and obtains forging stock; Forging stock is heated to T βAfter-35 ℃ (945 ℃), 6 fire are forged in jumping-up, pulling repeatedly with fast forging machine; The forging temperature of the forging stock after forging is T β-70 ℃ (910 ℃), the system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 1h under the condition of-25 ℃ (955 ℃), annealing for the second time are air cooling behind the insulation 8h under 540 ℃ the condition in temperature; The specification of the finished product titanium alloy rod bar of preparation is Φ 130mm.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 3

Present embodiment is identical with the preparation method of embodiment 1, and wherein difference is: the specification of TC4-DT titan alloy casting ingot is Φ 720mm; Titan alloy casting ingot is heated to 1175 ℃, forges machine soon with 4500T then and forges the inferior forging stock that obtains of 2 fire in the cogging of the β of titan alloy casting ingot phase region; Forging stock is heated to T βAfter-50 ℃ (930 ℃), 3 fire are forged in jumping-up, pulling repeatedly with fast forging machine; The forging temperature of the forging stock after forging is T β-50 ℃ (930 ℃), the system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 1.5h under the condition of-50 ℃ (930 ℃), annealing for the second time are air cooling behind the insulation 4h under 600 ℃ the condition in temperature; The specification of the finished product titanium alloy rod bar of preparation is Φ 300mm.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 4

(1) ingot casting melting: 0 grade of Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium is evenly mixed through mixer; Successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 420mm then; The weight percent of each composition of TC4-DT titan alloy casting ingot is Al:6.34%, V:4.21%, and O:0.08%, Fe:0.05%, C:0.02%, N:0.012%, H:0.007%, Ti are surplus;

(2) gas furnace of employing oxidizing atmosphere; TC4-DT titan alloy casting ingot described in the step (1) is heated to 1150 ℃; Forge machine soon with 1600T then and forge the inferior forging stock that obtains of 2 fire in the cogging of the β of titan alloy casting ingot phase region, every fire time forging ratio is not less than 1.3, and final forging temperature is not less than 850 ℃; The transformation temperature T of said forging stock βIt is 970 ℃;

(3) adopt resistance furnace that forging stock described in the step (2) is heated to (T β-50 ℃) after 920 ℃, with fast forging machine repeatedly jumping-up, pulling forge 6 fire, every fire time forging ratio is not less than 2.6, total forging ratio is not less than 10, final forging temperature is not less than 800 ℃;

(4) adopting the resistance furnace heating, is T with the forging stock after forging in the step (3) in forging temperature βForge to desired size under the condition of-70 ℃ (900 ℃), total forging ratio is not less than 3, and final forging temperature is not less than 750 ℃, obtains the titanium alloy rod bar of uniform formation;

(5) titanium alloy rod bar described in the step (4) is carried out double annealing and handle, obtain the finished product titanium alloy rod bar of Φ 90mm; The system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 0.3h under the condition of-20 ℃ (950 ℃), annealing for the second time are air cooling behind the insulation 8h under 540 ℃ the condition in temperature.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 5

Present embodiment is identical with the preparation method of embodiment 4, and wherein difference is: the specification of TC4-DT titan alloy casting ingot is Φ 650mm; Titan alloy casting ingot is heated to 1175 ℃, forges machine soon with 4500T then and forges the inferior forging stock that obtains of 3 fire in the cogging of the β of titan alloy casting ingot phase region; Forging stock is heated to T βAfter-20 ℃ (950 ℃), 5 fire are forged in jumping-up, pulling repeatedly with fast forging machine; The forging temperature of the forging stock after forging is T β-40 ℃ (930 ℃), the system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 1h under the condition of-15 ℃ (955 ℃), annealing for the second time are air cooling behind the insulation 4h under 600 ℃ the condition in temperature; The specification of the finished product titanium alloy rod bar of preparation is Φ 140mm.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 6

Present embodiment is identical with the preparation method of embodiment 4, and wherein difference is: the specification of TC4-DT titan alloy casting ingot is Φ 720mm; Titan alloy casting ingot is heated to 1200 ℃, forges 2 fire with fast forging machine in the cogging of the β of titan alloy casting ingot phase region then and obtains forging stock; Forging stock is heated to T βAfter-35 ℃ (935 ℃), 3 fire are forged in jumping-up, pulling repeatedly with fast forging machine; The forging temperature of the forging stock after forging is T β-60 ℃ (910 ℃), the system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 1.5h under the condition of-50 ℃ (920 ℃), annealing for the second time are air cooling behind the insulation 6h under 570 ℃ the condition in temperature; The specification of the finished product titanium alloy rod bar of preparation is Φ 300mm.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 7

(1) ingot casting melting: 0 grade of Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium are packed into the alloy bag, and successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 420mm then; The weight percent of each composition of TC4-DT titan alloy casting ingot is Al:6.23%, V:4.26%, and O:0.11%, Fe:0.04%, C:0.02%, N:0.012%, H:0.008%, Ti are surplus;

(2) gas furnace of employing oxidizing atmosphere; TC4-DT titan alloy casting ingot described in the step (1) is heated to 1150 ℃; Forge machine soon with 4200T then and forge the inferior forging stock that obtains of 3 fire in the cogging of the β of titan alloy casting ingot phase region, every fire time forging ratio is not less than 1.3, and final forging temperature is not less than 850 ℃; The transformation temperature T of said forging stock βIt is 985 ℃;

(3) adopt resistance furnace that forging stock described in the step (2) is heated to T βAfter-20 ℃ (965 ℃), with fast forging machine repeatedly jumping-up, pulling forge 6 fire, every fire time forging ratio is not less than 2.6, total forging ratio is not less than 10, final forging temperature is not less than 800 ℃;

(4) adopting the resistance furnace heating, is T with the forging stock after forging in the step (3) in forging temperature βForge to desired size under the condition of-70 ℃ (915 ℃), total forging ratio is not less than 3, and final forging temperature is not less than 750 ℃, obtains the titanium alloy rod bar of uniform formation;

(5) titanium alloy rod bar described in the step (4) is carried out double annealing and handle, obtain the finished product titanium alloy rod bar of Φ 90mm; The system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 0.3h under the condition of-15 ℃ (965 ℃), annealing for the second time are air cooling behind the insulation 8h under 540 ℃ the condition in temperature.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 8

Present embodiment is identical with the preparation method of embodiment 7, and wherein difference is: the specification of TC4-DT titan alloy casting ingot is Φ 650mm; Titan alloy casting ingot is heated to 1175 ℃, forges 3 fire with fast forging machine in the cogging of the β of titan alloy casting ingot phase region then and obtains forging stock; Forging stock is heated to T βAfter-35 ℃ (950 ℃), 4 fire are forged in jumping-up, pulling repeatedly with fast forging machine; The forging temperature of the forging stock after forging is T β-55 ℃ (930 ℃), the system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 1h under the condition of-30 ℃ (955 ℃), annealing for the second time are air cooling behind the insulation 6h under 560 ℃ the condition in temperature; The specification of the finished product titanium alloy rod bar of preparation is Φ 140mm.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

Embodiment 9

Present embodiment is identical with the preparation method of embodiment 7, and wherein difference is: the specification of TC4-DT titan alloy casting ingot is Φ 720mm; Titan alloy casting ingot is heated to 1200 ℃, forges 2 fire with fast forging machine in the cogging of the β of titan alloy casting ingot phase region then and obtains forging stock; Forging stock is heated to T βAfter-50 ℃ (935 ℃), 2 fire are forged in jumping-up, pulling repeatedly with fast forging machine; The forging temperature of the forging stock after forging is T β-70 ℃ (915 ℃), the system that double annealing is handled is: annealing for the first time is T in temperature βAir cooling behind the insulation 1.5h under the condition of-50 ℃ (935 ℃), annealing for the second time are air cooling behind the insulation 4h under 600 ℃ the condition in temperature; The specification of the finished product titanium alloy rod bar of preparation is Φ 300mm.

The titanium alloy rod bar of present embodiment preparation has good intensity, higher fracture toughness property and low fatigue crack growth rate.

The performance index of the titanium alloy rod bar for preparing in the embodiment of the invention are seen table 1, from table, can know, adopt the tensile strength Rm of the titanium alloy rod bar of method preparation of the present invention can reach more than the 915MPa ys Rp 0.2Can reach more than the 850MPa, unit elongation A is not less than 13.5%, and relative reduction in area Z is not less than 33.5%, fracture toughness property K ICGreater than 90MPam 1/2, as stress ratio R=0.1, stress intensity factor Δ K=11MPam 1/2The time, the fatigue crack growth rate da/dN of titanium alloy rod bar is less than 8 * 10 -6Mm/cycle.

The performance table of the titanium alloy rod bar of the above embodiment preparation of table 1

The above; It only is preferred embodiment of the present invention; Be not that the present invention is done any restriction, every according to inventing technical spirit to any simple modification, change and equivalent structure variation that above embodiment did, all still belong in the protection domain of technical scheme of the present invention.

Claims (1)

1. the preparation method of a titanium alloy rod bar is characterized in that, this method may further comprise the steps:
(1) ingot casting melting: Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium are packed into the alloy bag; Successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 420mm~Φ 720mm then; Or Titanium Sponge 40-60 mesh, Al-85V master alloy and commercial-purity aluminium is evenly mixed through mixer, successively through electrode compacting, plasma welding and the above vacuum consumable electrode arc furnace melting of secondary, obtaining specification is the TC4-DT titan alloy casting ingot of Φ 420mm~Φ 720mm then;
(2) gas furnace of employing resistance furnace or oxidizing atmosphere; TC4-DT titan alloy casting ingot described in the step (1) is heated to 1150 ℃~1200 ℃; Forge 2~3 fire with fast forging machine in the cogging of the β of titan alloy casting ingot phase region then and obtain forging stock; Every fire time forging ratio is not less than 1.3, and final forging temperature is not less than 850 ℃;
(3) adopt resistance furnace that forging stock described in the step (2) is heated to T β-50 ℃~T βAfter-20 ℃, with fast forging machine repeatedly jumping-up, pulling forge 3~6 fire, every fire time forging ratio is not less than 2.6, total forging ratio is not less than 10, final forging temperature is not less than 800 ℃, T βTransformation temperature for said forging stock;
(4) adopting the resistance furnace heating, is T with the forging stock after forging in the step (3) in forging temperature β-70 ℃~T βForge to desired size under-40 ℃ the condition, total forging ratio is not less than 3, and final forging temperature is not less than 750 ℃, obtains the titanium alloy rod bar of uniform formation;
(5) titanium alloy rod bar described in the step (4) is carried out double annealing and handle, obtain the finished product titanium alloy rod bar; The system that said double annealing is handled is: annealing for the first time is T in temperature β-50 ℃~T βBe incubated air cooling behind 0.3h~1.5h under-15 ℃ the condition, annealing for the second time is air cooling after being incubated 4h~8h under 540 ℃~600 ℃ the condition in temperature.
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