CN104931315A - Method for testing nonuniformity of titanium alloy low power tissue - Google Patents
Method for testing nonuniformity of titanium alloy low power tissue Download PDFInfo
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Abstract
The invention relates to a method for testing nonuniformity of titanium alloy low power tissue. The method comprises the following steps: a sample cut from a bar material or forging stock which is forged and deformed in a two-phase region is heated at the temperature range near the phase transformation point of (T beta-10 DEG C)-(T beta+15 DEG C) to generate oriented variant preferential selection of alpha-beta-alpha phase change, nonuniform phenomenon of an original tissue utilizes the 'tissue heredity' effect of crystallology orientation, the grain orientation difference of interfaces of normal tissue and abnormal tissue is enlarged, and meanwhile the tissue nonuniformity caused by component segregation is displayed through the sensitivity character of component segregation to alpha-beta-alpha phase change near the phase transformation point, so that the nonuniformity of the low power tissue after the corrosion can be smoothly observed. Through the method, the tissue defects, that the agglomeration of the original low power tissue is nonuniform, the large block dispersion is nonuniform and small block dispersion is nonuniform, of semi-finished products of titanium alloy bar material, forging stock and the like caused by component segregation or nonuniform deformation can be straightforwardly observed.
Description
Technical field
The present invention relates to a kind of method checking titanium alloy macrostructure unevenness.
Background technology
The industrial application such as Aeronautics and Astronautics, weapons and naval vessel constantly expand half-finished demands such as super large standard titanium alloy large-sized casting ingot and bar, forging stock and slabs, Chinese large-sized quick forging machine and pressing machine also come into operation in succession for this reason, particularly in order to improve the damage tolerance performance of titanium alloy further, improve serviceable life and the safe reliability of large-scale load-carrying member, the titanium alloy forging stock after the forging deformation of two-phase region or forging generally also all will carry out final β forging or β thermal treatment.Under above-mentioned requirement background and fabrication process condition, the macrostructure non-uniform phenomenon caused at forging process central part and edge deformation unevenness because of large-sized casting ingot uneven components and titanium alloy semi-manufacture also comes out gradually, thus causes the uneven microstructure defect of forging stock in the process such as follow-up β forging or β thermal treatment.In uneven microstructure rejected region titanium alloy strength ratio normal region, intensity generally will reduce more than 100MPa, also can cause simultaneously forging or part fatigue lifetime and plasticity etc. performance significantly reduction, have impact on serviceable life and the safe reliability of titanium alloy load-carrying member.The uneven defect of macrostructure of the type, if adopt the common discrepancy factory method of inspection to be difficult to be found when semi-manufacture bar or forging stock state, thus often cause the economic loss that is difficult to retrieve in follow-up β process and quality accident, work out also to titanium alloy Manufacture Technology of Semi-finished Products and bring misleading.
Summary of the invention
The object of the invention is the method for inspection proposing a kind of semi-manufacture macrostructure unevenness such as bar and forging stock checking two-phase region to forge, thus better can ensure half-finished quality such as bar and forging stock, guarantee structural homogenity, to reduce or to avoid the unnecessary loss that follow-up forging and part processing produce.
The technical solution adopted for the present invention to solve the technical problems is:
(1) from bar or forging stock intercepting one section of sample that virgin state is two-phase region forging;
(2) sample described in step (1) is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, temperature uniformity requires ± 10 DEG C, and holding temperature T is bar or forging stock β phase transition point temperature T
β10 DEG C to beta transformation point temperature T below
βabove 15 DEG C, i.e. T
β-10 DEG C≤T≤T
β+ 15 DEG C, after stove arrives holding temperature again, start to calculate temperature retention time, temperature retention time t=η × δ
max, the unit of temperature retention time t is min, δ
maxfor the maximum gauge of sample, unit is mm, η is heating coefficient, and the value of heating coefficient η is 0.15 ~ 0.5, and the shortest temperature retention time is 20min, then air cooling;
(3) sample described in step (2) is observed macrostructure after machining surface is processed and corroded.
The advantage that the present invention has and beneficial effect
The present invention can according to the requirement of product, is that the bar of two-phase region forging or any part of forging stock and arbitrary section intercept any thickness and shape sample in virgin state.By carrying out T to sample
β-10 DEG C ~ T
βnear+15 DEG C of transformation temperatures temperature heating and produce the orientation variant optimum selecting of α → β → α phase transformation, the non-uniform phenomenon of original structure is made to utilize " Structure Inheritance " effect of crystalline orientation, expand the grain orientation difference at normal structure and abnormal structure interface, near passing through transformation temperature, α → β → α phase transformation is to the susceptibility feature of component segregation simultaneously, also clearly can show the structural heterogenity that composition segregated zone comes, thus be conducive to the unevenness observing macrostructure after corrosion smoothly.The semi-manufacture such as titanium alloy rod bar and forging stock can be observed out intuitively because of component segregation or be out of shape the tissue defects such as uneven, the tiny piece decentralized of uneven, the relatively large decentralized of reunion shape of the uneven original macrostructure caused is uneven, as shown in Figure 1,2,3, 4 by the method.The method is simple to operate, and it is convenient to implement, and checkability is high.
Accompanying drawing explanation
Fig. 1 is the reunion shape heterogeneous structure macrostructure photo observed after adopting first heating post-etching method of the present invention;
Fig. 2 is the uneven macrostructure photo of relatively large decentralized observed after adopting first heating post-etching method of the present invention;
Fig. 3 is the uneven macrostructure photo of tiny piece of decentralized observed after adopting first heating post-etching method of the present invention;
Fig. 4 is the heart portion observed after adopting first heating post-etching method of the present invention is the uneven macrostructure photo of reunion shape, and in figure, black ellipsoid shape is the heterogeneous structure that component segregation causes.
Fig. 5 is the TC21 bar macrostructure photo of the embodiment of the present invention 1, and wherein, (a) adopts traditional caustic solution; B () adopts first heating post-etching method of the present invention.
Fig. 6 is the TC4-DT bar macrostructure photo of the embodiment of the present invention 2, and wherein, (a) adopts traditional caustic solution; B () adopts first heating post-etching method of the present invention.
Fig. 7 is the macrostructure photo after the TC18 forging stock of the embodiment of the present invention 3 adopts first heating post-etching method of the present invention.
Fig. 8 is the macrostructure photo after the TB6 titanium alloy rod bar of the embodiment of the present invention 4 adopts first heating post-etching method of the present invention.
Fig. 9 is the macrostructure photo after the TC18 titanium alloy forging of the embodiment of the present invention 5 adopts first heating post-etching method of the present invention.
Embodiment
Technique comprises the following steps:
(1) from bar or forging stock intercepting one section of sample that virgin state is two-phase region forging;
(2) sample described in step (1) is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, temperature uniformity requires ± 10 DEG C, and holding temperature T is bar or forging stock β phase transition point temperature T
β10 DEG C to beta transformation point temperature T below
βabove 15 DEG C, i.e. T
β-10 DEG C≤T≤T
β+ 15 DEG C, after stove arrives holding temperature again, start to calculate temperature retention time, temperature retention time t=η × δ
max, the unit of temperature retention time t is min, δ
maxfor the maximum gauge of sample, unit is mm, η is heating coefficient, and the value of heating coefficient η is 0.15 ~ 0.5, and when temperature retention time calculated value is less than 20min, temperature retention time is 20min, then air cooling;
(3) sample described in step (2) is observed macrostructure after machining surface is processed and corroded.
Embodiment 1
From TC21 titanium alloy rod bar (the phase point temperature T forged through two-phase region
βbe 960 DEG C) the thick xsect sheet metal specimens of head intercepting 15mm two pieces.Wherein one piece of sheet metal specimens is processed through machining surface and uses proportioning for 10HF-20HNO
3-70H
2the macrostructure observed after the corrosive liquid corrosion of O (Vol.%) is as shown in Fig. 5 (a).
Another block sheet metal specimens is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, and temperature uniformity requires ± 10 DEG C, and holding temperature T is beta transformation point temperature T
βabove 15 DEG C, namely 975 DEG C, stove starts to calculate temperature retention time after again arriving holding temperature, temperature retention time t=0.5 × 15=7.5min<20min, determines that temperature retention time is 20min, air cooling; Then the sheet metal specimens after heating processed through machining surface and use proportioning for 10HF-20HNO
3-70H
2the macrostructure observed after the corrosive liquid corrosion of O (Vol.%) is as shown in Fig. 5 (b).As can be seen from the figure, adopt the method for directly etching to be difficult to observe out heterogeneous structure (see Fig. 5 (a)), and adopt the method first heating post-etching to observe out macrostructure to there is reunion shape heterogeneous structure (see Fig. 5 (b)).
Embodiment 2
From TC4-DT titanium alloy rod bar (the phase point temperature T forged through two-phase region
βbe 985 DEG C) two pieces, the thick xsect sample of afterbody intercepting 50mm, wherein one piece of sample is processed through machining surface and uses proportioning for 10HF-20HNO
3-70H
2the macrostructure observed after the corrosive liquid corrosion of O (Vol.%) is as shown in Fig. 6 (a).
Another block sample is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, and temperature uniformity requires ± 10 DEG C, and holding temperature T is beta transformation point temperature T
βabove 5 DEG C, namely 990 DEG C, stove starts to calculate temperature retention time after again arriving holding temperature, temperature retention time t=0.5 × 50=25min, air cooling; Then the sample after heating processed through machining surface and use proportioning for 10HF-20HNO
3-70H
2the macrostructure observed after the corrosive liquid corrosion of O (Vol.%) is as shown in Fig. 6 (b).As can be seen from the figure, adopt the method for directly etching to be difficult to observe out heterogeneous structure (see Fig. 6 (a)), and adopt the method first heating post-etching to observe out macrostructure to there is relatively large decentralized heterogeneous structure (see Fig. 6 (b)).
Embodiment 3
From TC18 titanium alloy forging stock (the phase point temperature T forged through two-phase region
βbeing 870 DEG C) middle part intercepts one piece of 100mm thick longitudinal section sample.Sample is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, temperature uniformity requires ± 10 DEG C, and holding temperature T is beta transformation point temperature T
β10 DEG C below, namely 860 DEG C, stove starts to calculate temperature retention time after again arriving holding temperature, temperature retention time t=0.4 × 100=40min, air cooling; Then after machining surface processing, use proportioning for 10HF-20HNO to sample
3-70H
2the corrosive liquid corrosion of O (Vol.%), the macrostructure observed as shown in Figure 7.As can be seen from the figure, there is obvious reunion shape heterogeneous structure in macrostructure.
Embodiment 4
200mm thick longitudinal section sample is intercepted from the TB6 titanium alloy rod bar forged through two-phase region.Sample is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, temperature uniformity requires ± 10 DEG C, and holding temperature T is beta transformation point temperature T
β5 DEG C below, namely 810 DEG C, stove starts to calculate temperature retention time after again arriving holding temperature, temperature retention time t=0.25 × 200=50min, air cooling; Then after machining surface processing, use proportioning for 10HF-20HNO to sample
3-70H
2the corrosive liquid corrosion of O (Vol.%), the uneven macrostructure observed as shown in Figure 8, this is because the beta transformation point fluctuation that the component segregations such as Fe cause, is repeatedly heating and is exacerbating structural heterogenity further after forging deformation.
Embodiment 5
400mm thick longitudinal section sample is intercepted from the TC18 titanium alloy forging forged through two-phase region.Sample is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, temperature uniformity requires ± 10 DEG C, and holding temperature T is beta transformation point temperature T
β10 DEG C below, namely 860 DEG C, stove starts to calculate temperature retention time after again arriving holding temperature, temperature retention time t=0.15 × 400=60min, air cooling; Then after machining surface processing, use proportioning for 10HF-20HNO to sample
3-70H
2the corrosive liquid corrosion of O (Vol.%), the uneven macrostructure observed as shown in Figure 9, this is because the beta transformation point fluctuation that the component segregations such as Fe cause, is repeatedly heating and is exacerbating structural heterogenity further after forging deformation.
Claims (1)
1. check a method for titanium alloy macrostructure unevenness, it is characterized in that, specifically comprise the following steps:
(1) from bar or forging stock intercepting one section of sample that virgin state is two-phase region forging;
(2) sample described in step (1) is placed on the resistance furnace effective workspace inside holding after arriving holding temperature, temperature uniformity requires ± 10 DEG C, and holding temperature T is bar or forging stock β phase transition point temperature T
β10 DEG C to beta transformation point temperature T below
βabove 15 DEG C, i.e. T
β-10 DEG C≤T≤T
β+ 15 DEG C, after stove arrives holding temperature again, start to calculate temperature retention time, temperature retention time t=η × δ
max, the unit of temperature retention time t is min, δ
maxfor the maximum gauge of sample, unit is mm, η is heating coefficient, and the value of heating coefficient η is 0.15 ~ 0.5, and the shortest temperature retention time is 20min, then air cooling;
(3) sample described in step (2) is observed macrostructure after machining surface is processed and corroded.
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Cited By (4)
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| CN106680059A (en) * | 2016-12-27 | 2017-05-17 | 北京有色金属研究总院 | Method for inspecting macrostructures and defects of beta titanium alloy |
| CN106694770A (en) * | 2016-12-15 | 2017-05-24 | 陕西宏远航空锻造有限责任公司 | Forging method of TC21 titanium alloy |
| CN114283900A (en) * | 2021-12-14 | 2022-04-05 | 燕山大学 | Prediction and regulation method for near-beta titanium alloy low-magnification coarse grain structure distribution |
| CN114908306A (en) * | 2022-05-10 | 2022-08-16 | 湖南金天钛业科技有限公司 | Method for evaluating microcosmic component uniformity of easily segregated titanium alloy ingot |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN114283900A (en) * | 2021-12-14 | 2022-04-05 | 燕山大学 | Prediction and regulation method for near-beta titanium alloy low-magnification coarse grain structure distribution |
| CN114908306A (en) * | 2022-05-10 | 2022-08-16 | 湖南金天钛业科技有限公司 | Method for evaluating microcosmic component uniformity of easily segregated titanium alloy ingot |
| CN114908306B (en) * | 2022-05-10 | 2023-08-08 | 湖南湘投金天钛业科技股份有限公司 | Method for evaluating micro-component uniformity of easily segregated titanium alloy ingot |
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Application publication date: 20150923 |