SU1135798A1 - Method for treating billets of titanium alloys - Google Patents

Method for treating billets of titanium alloys

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Publication number
SU1135798A1
SU1135798A1 SU833626071A SU3626071A SU1135798A1 SU 1135798 A1 SU1135798 A1 SU 1135798A1 SU 833626071 A SU833626071 A SU 833626071A SU 3626071 A SU3626071 A SU 3626071A SU 1135798 A1 SU1135798 A1 SU 1135798A1
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SU
USSR - Soviet Union
Prior art keywords
deformation
temperature
phase
carried out
degree
Prior art date
Application number
SU833626071A
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Russian (ru)
Inventor
Игорь Алексеевич Акмулин
Алевтина Яковлевна Вишнякова
Андрей Николаевич Ершов
Виктор Семенович Левченко
Владимир Кимович Портной
Илья Изриэлович Новиков
Олег Михайлович Смирнов
Игорь Леонидович Федотов
Михаил Анатольевич Цепин
Original Assignee
Московский Ордена Октябрьской Революции И Ордена Трудового Красного Знамени Институт Стали И Сплавов
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Priority to SU833626071A priority Critical patent/SU1135798A1/en
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Publication of SU1135798A1 publication Critical patent/SU1135798A1/en

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Abstract

A METHOD FOR PROCESSING PREPARATIONS FROM TITANIUM ALLOYS, mainly large-sized, including the first deformation at temperature / region, cooling, the second deformation at temperature (() - regions, heating, the third deformation at temperature exceeding the temperature of the second deformation, and the final cooling, characterized by that, in order to improve plasticity, endurance limit, as well as to obtain a fine equilibrium structure, the first deformation is carried out with a degree of 40-60%, the second deformation is carried out in the direction Pendent direction of the first deformation (L with a degree of 30-40% at a temperature corresponding to the content of the about-phase in the amount of 601-75%; the third deformation is carried out in (oi + /) - areas with a degree of 30-40% in the range of temperature corresponding to the content of o (-phase in the amount of 15-55%, a. the final cooling is carried out with the speed of a cae of 0.01-0.05 deg / s: l with eo

Description

I the invention relates to metallurgy, in particular to the processing of titanium-free alloys, mainly two-phase ones, and can be used when processing large-sized blanks, mainly ingots to prepare the structure and the last deformation in the state of superplasticity. The method of processing, including heating and deformation at temperature | - area, subsequent quenching, heating and deformation at temperature (o14p} -region l J. The disadvantage of this method is the impossibility of obtaining large-sized blanks with a uniform fine-grained structure throughout the cross section due to the low thermal conductivity of titanium alloys. The closest in technical essence and the achieved result to The proposed method is a treatment, which includes the first deformation of the 1T under the temperature of the region, cooling, the second deformation at the temperature of the (ot 4 | i) region, heating, the third deformation at a temperature of ft-region 2. The disadvantage of this method is that providing a homogeneous, fine-grained macrostructure throughout the cross section of the workpiece, the microstructure is plate-like, which lowers the ductility characteristics, the fatigue limit, increases the notch sensitivity and also makes it impossible subsequent deformation in a state of extra plasticity. The purpose of the invention is to increase plasticity, fatigue strength, as well as to obtain a fine equilibrium structure. The goal is achieved by the fact that according to the method including the first deformation at a temperature and the field, cooling, the second deformation at a temperature (about (+ | 3) -the region, heating, the third deformation at a temperature exceeding the second deformation temperature and the final cooling, Deformation of the wire, dt with a degree of deformation of 40-60%, the second deformation is carried out in the direction perpendicular to the direction of the first deformation with a degree of 30-40% at a temperature corresponding to the content of the C-phase in the amount of 60-75%, the third deformation lead in (about (- |) -region with a degree of 30-40% in the range of temperature, corresponding to the content of c-phase in the amount of 15-55%, and; final cooling is carried out at a rate of 0.01-0.05 deg / s When processing in the I-region by unidirectional deformation, the σ-grains are pulled in the direction of the metal flow. In order for most grains to undergo such a deformation, its degree should be 40-60%, due to the unevenness of the actual processes of metal forming . A further increase in the degree of deformation does not lead to a noticeable increase in the mechanical properties and refinement of the microstructure, but is accompanied by an increase in processing strength and in some cases by cracking of the alloy. The second deformation in the () -region in the perpendicular direction provides an effective work hardening of 04-points, which stand out along the boundaries of the fl-grains and therefore also have a preferential orientation, and, moreover, the intragrain o are applied to the work hardening (, - plates less coarse than The degree of deformation should be 30-40%. The limit of the oi-phase in 60-75% is due to the fact that at a lower content of hlep intragranular Ci-ppastin is insufficient, which ultimately leads to the presence of plate-like -phase in the structure of the workpiece. Exceeding the content of the Ь-phase in the alloy of more than 75% leads to a decrease in the ductility of the alloy.When heated to temperatures of the third deformation, the about-phase dissolves, which, due to preliminary cold work and polygonization, leads to its fragmentation. The i-phase is in the range, the lower value of which is 15%, and the upper value is 20% lower than the content of the c-phase during the second deformation. The lower value is due to the fact that when heated to higher temperatures, the subsequent cooling leads to the formation of α-plates along the boundaries of the recrystallized / 3-phase, which impairs plastic properties and prevents the flow of superplastic deformation during subsequent processing. The upper value of the content of the Ob-phase is due to the fact that when heated from temperatures, the second deformation to the third deformation temperature should undergo at least 20% of the circulating phase to ensure its subsequent fragmentation. In addition, the value of the third strain should be 30–40% to obtain the 06-phase in the form of round particles. An increase in the deformation value during the third and second deformations of more than 40%, as in the case of the first deformation, does not lead to a noticeable increase in the mechanical properties of the alloy, but contributes to an increase in the strain force and leads to cracking of the workpiece. The final cooling is a wire with a speed of 0.01-0.05 cf / s, t-tie, not exceeding the critical one, below which the phase transformation passes through the growth of the about-phase particles, and the nature of the structure does not change. It represents a mixture of o1 particles. - and / 3-phases are rounded, not more than 5-7 microns in size, which provides high values of plasticity, fatigue strength and lower sensitivity to notch compared to a lamellar structure. In this case, subsequent processing in a superplastic state becomes possible, for which it is necessary that the grains are rounded, not larger than 10 µm. When cooled at a speed higher than 0.05 deg / s, the structure is a mixture of round particles. 7984 and particles with a / - transformed structure (with lamellar oi-phase), which significantly impairs the characteristics of superplastic deformation. Cooling at a rate of less than 0.01 deg / s leads to particle-phase coarsening and their growth to 7-8 microns, which degrades the characteristics of superplasticity. Example. Cast samples of the VTZ-1 alloy with a polymorphic transformation temperature of 980 ° C are treated by the proposed and known methods. The processing modes and properties of the obtained semi-finished products are given in the table. As can be seen from the data presented in the table, the proposed method allows to increase the ductility and endurance of titanium alloys in comparison with alloys processed in a known manner. In addition, the proposed method allows to obtain, without the introduction of an additional amount of heating, large-sized preforms with fine-grained macro- and microstructure, suitable for further processing in the state of superplasticity. At the same time, the structure obtained in this way provides a 15-20% increase in the fatigue limit, an elongation of 30-50%, and a transverse narrowing of 30-50%. The speed sensitivity coefficient varies from 0.25-0.35 to 0.750, 8. The economic efficiency of the proposed method is due to the fact that, compared with the known method, it is possible with subsequent stamping to reduce the deformation force and bring the forging size closer to the dimensions of the part.

SU833626071A 1983-07-27 1983-07-27 Method for treating billets of titanium alloys SU1135798A1 (en)

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SU833626071A SU1135798A1 (en) 1983-07-27 1983-07-27 Method for treating billets of titanium alloys

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Application Number Priority Date Filing Date Title
SU833626071A SU1135798A1 (en) 1983-07-27 1983-07-27 Method for treating billets of titanium alloys

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SU1135798A1 true SU1135798A1 (en) 1985-01-23

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10053758B2 (en) 2010-01-22 2018-08-21 Ati Properties Llc Production of high strength titanium
US10094003B2 (en) 2015-01-12 2018-10-09 Ati Properties Llc Titanium alloy
US10144999B2 (en) 2010-07-19 2018-12-04 Ati Properties Llc Processing of alpha/beta titanium alloys
RU2675886C2 (en) * 2013-03-15 2018-12-25 ЭйТиАй ПРОПЕРТИЗ ЭлЭлСи Thermomechanical processing of two-phase alpha-beta titanium alloys
US10287655B2 (en) 2011-06-01 2019-05-14 Ati Properties Llc Nickel-base alloy and articles
US10337093B2 (en) 2013-03-11 2019-07-02 Ati Properties Llc Non-magnetic alloy forgings
US10422027B2 (en) 2004-05-21 2019-09-24 Ati Properties Llc Metastable beta-titanium alloys and methods of processing the same by direct aging

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
I.Портной В.К. и др. Термомеханическа обработка дл улучшени сверхпластичности двухфазных титановых сплавов. - Технологи легких сплавов. 1980, № 3, с.41-46. 2. Евменов О.П. Исследование тер- момеханических параметров ковки титановых сплавов и разработка технологии получени заготовок с однородной мелкозернистой структурой. Дне. на соиск. учен, степени канд. техн. наук. М., 1978, с.84-90. *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10422027B2 (en) 2004-05-21 2019-09-24 Ati Properties Llc Metastable beta-titanium alloys and methods of processing the same by direct aging
US10053758B2 (en) 2010-01-22 2018-08-21 Ati Properties Llc Production of high strength titanium
US10144999B2 (en) 2010-07-19 2018-12-04 Ati Properties Llc Processing of alpha/beta titanium alloys
US10287655B2 (en) 2011-06-01 2019-05-14 Ati Properties Llc Nickel-base alloy and articles
US10337093B2 (en) 2013-03-11 2019-07-02 Ati Properties Llc Non-magnetic alloy forgings
RU2675886C2 (en) * 2013-03-15 2018-12-25 ЭйТиАй ПРОПЕРТИЗ ЭлЭлСи Thermomechanical processing of two-phase alpha-beta titanium alloys
US10370751B2 (en) 2013-03-15 2019-08-06 Ati Properties Llc Thermomechanical processing of alpha-beta titanium alloys
US10094003B2 (en) 2015-01-12 2018-10-09 Ati Properties Llc Titanium alloy

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