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WO2002101110A2 - Procede de traitement des alliages hypereutectiques a base d'aluminures de titane $g(g)-tial et ?$g(a)2-ti3 al - Google Patents

Procede de traitement des alliages hypereutectiques a base d'aluminures de titane $g(g)-tial et ?$g(a)2-ti3 al Download PDF

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Publication number
WO2002101110A2
WO2002101110A2 PCT/RU2002/000284 RU0200284W WO02101110A2 WO 2002101110 A2 WO2002101110 A2 WO 2002101110A2 RU 0200284 W RU0200284 W RU 0200284W WO 02101110 A2 WO02101110 A2 WO 02101110A2
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deφορmatsii
οbρabοτκi
processing
πρi
stage
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Russian (ru)
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WO2002101110A3 (fr
Inventor
Valery Mazitovich Imaev
Renat Mazitovich Imaev
Andrey Vitaljevich Kuznetsov
Marat Rafaeljevich Shagiev
Gennady Alekseevich Salishchev
Oskar Akramovich Kaibyshev
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INSTITUT PROBLEM SVERKHPLASTICHNOSTI METALOV RAN
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INSTITUT PROBLEM SVERKHPLASTICHNOSTI METALOV RAN
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Publication of WO2002101110A2 publication Critical patent/WO2002101110A2/fr
Publication of WO2002101110A3 publication Critical patent/WO2002101110A3/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon

Definitions

  • the alloys developed at the present time with ⁇ + ⁇ 2 have, in the ordinary course of life, a customary construction structure.
  • the disease is complicated by an enlarged, severous area of the obstructive crystals, and for the microcystic, there is a strong dendritic disease.
  • the alloys are characterized by a strong plastic anisotropy observed in a wide range of tempera- tures.
  • ⁇ ⁇ ezul ⁇ a ⁇ e ⁇ a ⁇ y ⁇ b ⁇ ab ⁇ i in s ⁇ lava ⁇ ⁇ -48 ⁇ 1-2 ⁇ -2cT ⁇ dve ⁇ gnu ⁇ m ⁇ edva ⁇ i ⁇ eln ⁇ y g ⁇ m ⁇ genizatsii in ⁇ ⁇ az ⁇ v ⁇ y ⁇ blas ⁇ i and ⁇ -46 ⁇ 1-2 ⁇ -2cT-1 ⁇ a
  • ⁇ dve ⁇ gnu ⁇ m ⁇ edva ⁇ i ⁇ eln ⁇ y e ⁇ s ⁇ uzii in ⁇ ⁇ blas ⁇ i was ⁇ luchena ⁇ dn ⁇ dnaya mel ⁇ ze ⁇ nis ⁇ aya mi ⁇ s ⁇ u ⁇ u ⁇ a with submi ⁇ is ⁇ alliches ⁇ im ⁇ azme ⁇ m ze ⁇ en / particles.
  • P ⁇ ch ⁇ i ⁇ ln ⁇ s ⁇ yu gl ⁇ bulya ⁇ iz ⁇ vannaya s ⁇ u ⁇ u ⁇ a was ⁇ luchena in ⁇ ezul ⁇ a ⁇ e iz ⁇ e ⁇ miches ⁇ y de ⁇ matsii in ⁇ + ⁇ ⁇ az ⁇ v ⁇ y ⁇ blas ⁇ i, ⁇ gda s ⁇ edshes ⁇ v ⁇ val ⁇ bys ⁇ e ⁇ lazhdenie in e ⁇ y same ⁇ az ⁇ v ⁇ y ⁇ blas ⁇ i, ⁇ bes ⁇ echivshee v ⁇ zni ⁇ n ⁇ venie me ⁇ as ⁇ abiln ⁇ y ⁇ ⁇ azy [2].
  • ⁇ bschim susches ⁇ vennym ned ⁇ s ⁇ a ⁇ m iz ⁇ e ⁇ miches ⁇ y de ⁇ matsii in ⁇ + ⁇ ⁇ az ⁇ v ⁇ y ⁇ blas ⁇ i yavlyae ⁇ sya ne ⁇ b ⁇ dim ⁇ s ⁇ is ⁇ lz ⁇ vaniya d ⁇ g ⁇ s ⁇ yascheg ⁇ sh ⁇ am ⁇ v ⁇ g ⁇ ins ⁇ umen ⁇ a and zaschi ⁇ n ⁇ y a ⁇ m ⁇ s ⁇ e ⁇ y protecting ⁇ ⁇ isleniya ⁇ i s ⁇ l vys ⁇ i ⁇ ⁇ em ⁇ e ⁇ a ⁇ u ⁇ a ⁇ , ch ⁇ siln ⁇ ⁇ vyshae ⁇ s ⁇ im ⁇ s ⁇ ⁇ b ⁇ ab ⁇ i.
  • ⁇ a ⁇ sn ⁇ ve e ⁇ g ⁇ was made vyv ⁇ d ⁇ v ⁇ zm ⁇ zhn ⁇ s ⁇ i ⁇ hostname u ⁇ azanny ⁇ me ⁇ d ⁇ v in ⁇ myshlenny ⁇ massh ⁇ aba ⁇ .
  • Decommissioning at the first stage of processing is carried out in the process in quasi-isothermal conditions with a true degree of deformation of at least 0.7
  • ⁇ a ⁇ e ⁇ v ⁇ y s ⁇ adii de ⁇ matsi ⁇ nnuyu ⁇ b ⁇ ab ⁇ u ⁇ + ⁇ 2 ssh ⁇ av ⁇ v ⁇ v ⁇ dya ⁇ in ⁇ + ⁇ ⁇ az ⁇ v ⁇ y ⁇ blas ⁇ i (see. Diag ⁇ ammu, ⁇ ig. 1) wherein blag ⁇ da ⁇ ya ⁇ las ⁇ ichn ⁇ y, ⁇ azu ⁇ yad ⁇ chenn ⁇ y ⁇ ⁇ aze e ⁇ i s ⁇ lavy ⁇ sh ⁇ ⁇ ddayu ⁇ sya ⁇ b ⁇ ab ⁇ e.
  • the second stage treatment at the second stage is subject to thermal conditions and relatively low rates of deformation. Another goal is to grind the crop in the harvesting volume and to reach the required size of ⁇ grain and ⁇ 2 particles.
  • P ⁇ edlagae maya ⁇ b ⁇ ab ⁇ a two s ⁇ adii m ⁇ zhe ⁇ by ⁇ is ⁇ lz ⁇ vana ⁇ ⁇ n ⁇ sheniyu li ⁇ ym zaev ⁇ e ⁇ idnym ⁇ ⁇ + ⁇ 2 s ⁇ lavam ( ⁇ ig.1) in ⁇ myshlenny ⁇ usl ⁇ viya ⁇ , ⁇ bes ⁇ echivaya e ⁇ e ⁇ ivn ⁇ e grinding ⁇ azme ⁇ a ze ⁇ en ⁇ and ⁇ 2 in chas ⁇ its ⁇ beme zag ⁇ v ⁇ i d ⁇ m ⁇ m 1 and 0.1 m ⁇ m, s ⁇ ve ⁇ s ⁇ venn ⁇ .
  • the size of the recovered crystallized ⁇ grains decreases, approaching the size of the globular ⁇ 2 particles.
  • the size of ⁇ grain and ⁇ 2 particles in the preparation are found to be substantially less than after the usual conventional free process. This substantially reduces the temperature-viscous transition and the lower temperature boundary of the superplasticity.
  • ⁇ Profile ⁇ Result from overload in superplastic or 10 close conditions ensure high quality of processing, which is important for the following treatment.
  • the ability to process depends on the size of the grains and even more so on the size of the particles of the alloy. It is known that the formation of the product is conveniently 1 / N, where ⁇ is the size of the grain, ⁇ is the size of the particles.
  • the size of the part and the size of the particles is reduced after two-stage processing, as compared to the obtained process, it is possible to change the ⁇ me ⁇ g ⁇ , ⁇ avn ⁇ snaya ⁇ ma ⁇ 2 chas ⁇ its ⁇ sle dvus ⁇ adiyn ⁇ y ⁇ b ⁇ ab ⁇ i in ⁇ lichie ⁇ ne ⁇ avn ⁇ sn ⁇ y ⁇ my, ⁇ luchaem ⁇ y ⁇ sle ⁇ dn ⁇ s ⁇ adiyn ⁇ y ⁇ b ⁇ ab ⁇ i [2] ve ⁇ ya ⁇ nee vseg ⁇ ⁇ a ⁇ lse s ⁇ s ⁇ bs ⁇ vue ⁇ ⁇ vysheniyu s ⁇ ivleniya ⁇ b ⁇ az ⁇ vaniyu ⁇ i de ⁇ matsii.
  • Homogenizing firing substantially improves the chemical, phase, and rapid single casting of ⁇ + ⁇ 2 alloys. Thanks to this, it is possible that both the GUI and the GUI will increase the speed of operation at the first stage of processing and accelerate the process of normalization.
  • the firing temperature of the fired furnace was only slightly higher than ⁇ ⁇ , and the firing time was not too good.
  • ⁇ -hardening helps to achieve the highest high-performance properties in fusion in the case of small-scale accidents.
  • P ⁇ isu ⁇ s ⁇ vie chas ⁇ its Fer ⁇ ⁇ izmelcheschi ⁇ s ⁇ u ⁇ u ⁇ y sli ⁇ a, s ⁇ s ⁇ bs ⁇ vue ⁇ ⁇ azvi ⁇ iyu ⁇ tsess ⁇ v ⁇ e ⁇ is ⁇ allizatsii / gl ⁇ bulya ⁇ izatsii and e ⁇ e ⁇ ivn ⁇ mu grinding s ⁇ u ⁇ u ⁇ y sli ⁇ a in ⁇ tsesse de ⁇ matsi ⁇ nn ⁇ y ⁇ b ⁇ ab ⁇ i, ⁇ bes ⁇ echivae ⁇ d ⁇ s ⁇ izhenie naib ⁇ lee s ⁇ abilny ⁇ mi ⁇ s ⁇ u ⁇ u ⁇ ny ⁇ s ⁇ s ⁇ yany and me ⁇ aniches ⁇ i ⁇ sv ⁇ ys ⁇ v.
  • Boron was selected as a modifying element that facilitates the grinding of the ingot structure and the particle / particle size in the process.
  • boron is an effective modifier for ⁇ -hardening alloys. Modification of the material significantly increases the uniformity of the equipment and the volume of the ingot, the size of the large varieties is increased 12 approx. 50 to 1000 ⁇ m or less, depending on the alloy’s compaction. In the case of larger quantities, it is more likely to cause processing and defective treatment, while the quantity of the medium has lesser quantity of disease. This alloy possesses good mechanical properties in the cast iron and is well-maintained.
  • P ⁇ vedenie ⁇ a ⁇ y ⁇ edva ⁇ i ⁇ eln ⁇ y ⁇ b ⁇ ab ⁇ i ⁇ zv ⁇ lyae ⁇ is ⁇ lz ⁇ va ⁇ naib ⁇ lee vys ⁇ ie s ⁇ s ⁇ i de ⁇ matsii on ⁇ e ⁇ v ⁇ y s ⁇ adii ⁇ b ⁇ ab ⁇ i and ⁇ a ⁇ lse ⁇ a ⁇ and ⁇ edyduschem case ⁇ vyshae ⁇ e ⁇ e ⁇ ivn ⁇ s ⁇ dvus ⁇ adiyn ⁇ y ⁇ b ⁇ ab ⁇ i in tsel ⁇ m.
  • Decommissioning at the first stage is the most convenient way to deal with quasi-industrial conditions in case of an increase in the rate of increase. This avoids the use of the best-in-class tool, for example, from a small alloy. In this case, it is possible that there is a slight decrease in the amount of baking in the processing process, and in the process of industrialization / expansion of the process it is overwhelming.
  • various schemes of deformation can be used: case, exclusion and other.
  • the calculation of the component shall be calculated on the basis of the condition of the processing which is carried out above the account of the test ⁇ b ⁇ l ⁇ ch ⁇ a ⁇ ed ⁇ anyae ⁇ zag ⁇ v ⁇ u ⁇ siln ⁇ g ⁇ ⁇ isleniya and ⁇ a ⁇ zhe umeny ⁇ ae ⁇ force ⁇ eniya between ins ⁇ umen ⁇ m and zag ⁇ v ⁇ y, ⁇ vyshaya ⁇ dn ⁇ dn ⁇ s ⁇ de ⁇ matsii ⁇ ⁇ bemu zag ⁇ v ⁇ i and s ⁇ s ⁇ bs ⁇ vuya ⁇ em most b ⁇ lee ⁇ ln ⁇ mu grinding s ⁇ u ⁇ u ⁇ y in ⁇ beme sli ⁇ a.
  • the true degree of degradation at the first stage of processing should be at least 0.7, otherwise the structure will not 14 will be shredded to a sufficient degree and the temperature of the bulk-viscous process will not be reduced to the point that this is not the goal, that is the aim
  • the speed of the selection is selected in the range of 10 " -10 s " .
  • the front end of the process is at the first stage of the process. Most of all, the speed of the deformation was not less than 10 "2 s " 1 , in the case of a negative process, I will neglect the processes of process normalization / globalization.
  • the degree of performance of the process depends on the subsequent processing and the required end-user process.
  • Decommissioning at the second stage of the processing process is subject to ⁇ 2 + ⁇ thermal processing due to or near physical disruption.
  • the mode of processing is low - the temperature, the speed and the degree of adaptation, are selected on the basis of the test of the property for the test and the dependence on the property.
  • the relatively low temperature of the unit at the second stage of processing makes it possible to use grease and, in particular, grease.
  • Glass grease protects the sludge from acidification and reduces the level of contact between the zagotovka and the tool, increasing the cost of the business.
  • Burning contributes to an increase in the volume of the globular structure.
  • the company prepares a batch in ⁇ • phased area for receiving the most free-of-charge plastic.
  • the temperature of the process is reduced to the temperature of the cooler, so that there is no loss of The final aging process is for the improvement of basic and plastic properties.
  • ⁇ a ⁇ ig. 2 are indicated: a - the original preparation of the alloy ⁇ -42.7 ⁇ 1-1.9 ⁇ -1.9Sg-0.37 ⁇ ; b - preparation after placing it in a block from Steel 3; c - preparation in the factory after the first stage of processing; d - batch after extracting it from the bulk; e - batch after the first stage of processing and burning at 1000 ° C for 5 hours.
  • ⁇ a ⁇ ig. 3 shows the structure of the fusion after the GUI and the homogenized burning: a - ⁇ -42.7 ⁇ 1-1.9 ⁇ -1.9Sg-0.37 ⁇ ; b - ⁇ -45,2 ⁇ 1-1 5 7 ⁇ -1,5 ⁇ -0,46 ⁇ .
  • ⁇ a ⁇ ig. 4 shows the microstructure of the Tin-42.7 ⁇ 1-1.9 ⁇ ⁇ -1.9Sg-0.37 ⁇ alloy: a - after the GUIP and the homogenized burning, after the second stage of the operation there was a 1000 kiln burn-out
  • ⁇ a ⁇ ig. 6 are indicated: a - a sheet of alloy ⁇ -45,2 ⁇ 1-1,7 ⁇ -1,5Sg-0,46 ⁇ ; b - the leaflet path along the direction of the path.
  • ⁇ a ⁇ ig. 7 are shown: a - the original preparation for the stamping of the blades and the punched blades from the alloy ⁇ -45,2 ⁇ 1-1,7 ⁇ -1,5 ⁇ -0,46 ⁇ ; b - the microscope of the blade after the process in the ⁇ phase area. 18
  • ⁇ a ⁇ ig. 10 is shown near the zone of destruction for the alloy ⁇ -46,5 ⁇ 1- ⁇ - with "1 : a - state 1, 6 - state 2.
  • over-alloyed ⁇ + ⁇ 2 alloys were taken alloys on the basis ⁇ - 42.7%> ⁇ 1, 44-44.2 ⁇ 1%, ⁇ -45.2 ⁇ 1%> and ⁇ -48 ⁇ 1, which are missing from aluminum alloys (see diagram, Fig. 1).
  • EXAMPLE 1 A cast billet (Fig. 2a) with an alloy of 42-42.7 ⁇ 1-1.9 ⁇ -1.9Sg-0.37 ⁇ with dimensions of 070x120 mm was heated at a constant pressure of 175 ° C and was subjected to a pressure of 175 ° C. Ignition at 1300 ° C for 60 minutes. The ingot is shown in FIG. Behind. The size of the large plate is about 50 microns (fig. 4a).
  • a stamp was obtained with a thickness of about 15 mm and a diameter of 195 mm (Fig. 2e). After finishing the damping process, we burned it at a temperature of 1000 ° C for 5 hours. After the described processing of the machine, the unit is equipped with a single section.
  • a cast billet of ⁇ -45 5 2 ⁇ 1-1,7 ⁇ -1,5Sg-0,46 ⁇ alloy with sizes of 0 70x120 mm was heated at a static pressure of 1200 ° C and a pressure of 175 Canal Pa. ⁇ a ⁇ ig. 36 the ingot is shown. It seems that it has an extended fixed area. The length of the small ones is a few millimeters, and the width is a few microns.
  • the batch was opened with a glass grease EH-24, heated to 1000 ⁇ 5 ° C in the furnace type ⁇ -520/14, it was quicker (not more than 6-7 seconds later). 10 "-5x10" to "on ⁇ ?
  • the preparation was placed in a cask from Steel 3, heated in a furnace of type ⁇ -520/14 to a temperature of 1200 + 10 ° ⁇ , and kept at this temperature for 1 hour.
  • the performance was carried out under quasi-thermal conditions.
  • ⁇ ⁇ ezul ⁇ a ⁇ e was ⁇ luchena sh ⁇ am ⁇ v ⁇ a ⁇ lschin ⁇ y 15 mm and diame ⁇ m 195 mm.
  • P ⁇ sle ⁇ isann ⁇ y ⁇ b ⁇ ab ⁇ i ma ⁇ s ⁇ u ⁇ u ⁇ a a single section for cross-section, and a microstructure - for industrialization a and gl ⁇ bulya ⁇ iz ⁇ vana in "80% ⁇ bema zag ⁇ v ⁇ i, s ⁇ edny ⁇ azme ⁇ ⁇ e ⁇ is ⁇ alliz ⁇ vanny ⁇ ze ⁇ en ⁇ and ⁇ 2 gl ⁇ bulya ⁇ iz ⁇ vanny ⁇ chas ⁇ its s ⁇ s ⁇ avlyae ⁇ ⁇ l ⁇ m ⁇ m 1-2 and 0.1-1 m ⁇ m s ⁇ ve ⁇ s ⁇ venn ⁇ ( ⁇ ig. 5c).
  • a - plates For the implementation of the package from the stamped out: a - plates; b - samples for tension. The test results of the samples were used to select the operating mode of the process. The plates were placed in a box and wrapped in quasi-thermal conditions. ⁇ a ⁇ ig. 6 The sheet and its microstructure are shown along the direction of the treatment.
  • EXAMPLE 3 A cast billet of ⁇ -45.2-11-1.7 ⁇ -1.5Sg-0.46 ⁇ alloy with sizes of 0 70x120 mm was heated at a temperature of 1200 ° C and a pressure of 175 ° C was used. C for 60 minutes.
  • the preparation was opened with a glass-lubricant ⁇ -24, heated in a furnace of type ⁇ -520/14 to a temperature of 1200 ⁇ 10 ° ⁇ , and it was heated at a temperature of 1 hour.
  • the deformation was carried out under thermal conditions at a temperature of 1150 ° ⁇ .
  • ⁇ ⁇ ezul ⁇ a ⁇ e was ⁇ luchena sh ⁇ am ⁇ v ⁇ a ⁇ lschin ⁇ y ⁇ l ⁇ 30 mm and diame ⁇ m 140 mm.
  • P ⁇ sle ⁇ isann ⁇ y ⁇ b ⁇ ab ⁇ i ma ⁇ s ⁇ u ⁇ u ⁇ a sh ⁇ am ⁇ v ⁇ ⁇ dn ⁇ dna ⁇ section.
  • EXAMPLE 4 Pour ingot from alloy ⁇ -48 ⁇ 1-2 ⁇ -2 ⁇ with sizes 0160x220 mm was doubled to a hot pressure of 1260 ° ⁇ and a pressure of 175 ⁇ Pa for 2 hours. Next, the preparation was placed in a container from the titanium alloy Albany6, heated in the furnace of the type “Kaegegt” to a temperature of 1390 ⁇ 5 ° ⁇ and separated from it.
  • ⁇ ⁇ ezul ⁇ a ⁇ e was ⁇ luchena sh ⁇ am ⁇ v ⁇ a ⁇ lschin ⁇ y 15 mm and diame ⁇ m 195 mm.
  • P follows de ⁇ matsii sh ⁇ am ⁇ v ⁇ u ⁇ dve ⁇ gali s ⁇ a ⁇ eniyu ⁇ i ⁇ em ⁇ e ⁇ a ⁇ u ⁇ e 900 ° C ⁇ echenie 10 chas ⁇ v.
  • EXAMPLE 5 A cast ingot from alloy ⁇ -44 5 2 ⁇ 1-0.67 ⁇ -1 5 85 Cg-0.44 ⁇ , which is directly doubled at a constant pressure of 1200 ° C and has a pressure of 160 mm; In the process, the boiler was ignited and humidified at 1320 ° C for 60 minutes in the atmosphere. Then, baking for 10-15 seconds was transferred to the furnace of type ⁇ -520/14, heated to a temperature of 1200 ⁇ 10 ° ⁇ and was kept at this temperature for 5 minutes.
  • ⁇ a ⁇ ig. 8 ⁇ eds ⁇ avlena mi ⁇ s ⁇ u ⁇ u ⁇ a s ⁇ lava ⁇ sle ⁇ b ⁇ ab ⁇ i ⁇ ⁇ i ⁇ u - s ⁇ s ⁇ yanie 1 and ⁇ ⁇ edlagaem ⁇ mu ⁇ esheniyu - s ⁇ s ⁇ yanie 2. ⁇ idn ⁇ , ch ⁇ ⁇ sle ⁇ b ⁇ ab ⁇ i ⁇ ⁇ i ⁇ u mi ⁇ s ⁇ u ⁇ u ⁇ a s ⁇ lava d ⁇ v ⁇ ln ⁇ ne ⁇ dn ⁇ dna ( ⁇ ig 8a.).
  • ⁇ grain Around 90% of the ⁇ grain has a size of 3 to 20 ⁇ m, the rest - over 20 ⁇ m. The size of some of them reaches 50 microns.
  • the particle size of ⁇ 2 phases varies from 1 to 7 ⁇ m (Fig. 86). Significantly finer and more uniform microstructure is obtained in the process of processing by the proposed solution (Fig. 8c).
  • the size of the ⁇ grain does not exceed 5–6 ⁇ m, but the average size is 2 ⁇ m.
  • Particles of ⁇ 2 phase are located both in borders and in the interior of ⁇ grains.
  • the size of ⁇ 2 particles varies in the range of 0.1–0.6 ⁇ m (Fig. 8g).

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Abstract

L'invention appartient au domaine du traitement par pression des métaux et alliages et notamment au traitement par pression des alliages hypereutectiques à base d'aluminures de titane η-TiAl (superstructure Ll0- phase η) et Ti3Al (superstructure DO19- phase α2) obtenus par coulage. L'invention peut s'utiliser pour obtenir ces matériaux sous forme de blancs à l'échelle industrielle, de produits semi-finis et d'articles à structure réglementée. L'invention vise à développer un procédé de traitement de blancs coulés à partir d'alliages hypereutectiques η+α2 qui peut être mis en oeuvre à l'échelle industrielle pour conférer à ces blancs, par déformation à chaud, d'une structure homogène à faible granularité, avec une taille de grains η inférieure à 5 micromètres et une taille de particules α inférieure à 1 micromètre. Le procédé de l'invention consiste à traiter des alliages hypereutectiques à base d'aluminures de titane η-TiAl (superstructure Ll0- phase η) et Ti3Al en chauffant et en déformant les alliages, le réchauffement et la déformation se faisant en deux stades. Au premier stade, la déformation du blanc se fait dans l'intervalle Te Te + ΔT °C, dans laquelle Te est la température de la transformation eutectique, ?ΔT étant sélectionnée de manière à préserver la structure la composante globulaire de la structure, obtenue par la déformation, pendant le refroidissement après déformation. La vitesse de déformation ε1 est sélectionnée dans l'intervalle ε'1min -¿ε'¿1max? dont la limite supérieure est limitée par la déformabilité de l'alliage, et la limite inférieure par la condition de prédominance des processus de recristallisation / globularisation sur ceux de retour. Le degré de déformation ε1 est choisi de manière à assurer la diminution de la taille moyenne des grains / colonies dans le blanc jusqu'aux valeurs assurant l'abaissement de la température de transition cassant - ductile du matériau T* du blanc jusqu'à T*<Te si la température et la vitesse de déformation restent dans les intervalles indiqués. Au deuxième stade, la déformation du blanc est effectuée dans des conditions isothermiques, dans une gamme de températures Tmin Te °C, dans laquelle Tmin est une température maximale assurant la déformation non destructive avec un taux de déformation ε2 et une vitesse de déformation ε'2 sélectionnés de manière à assurer la diminution de la taille des grains η et des particules α2 grâce à des procédés de recristallisation / globularisation.
PCT/RU2002/000284 2001-06-13 2002-06-06 Procede de traitement des alliages hypereutectiques a base d'aluminures de titane $g(g)-tial et ?$g(a)2-ti3 al Ceased WO2002101110A2 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
RU2001116535 2001-06-13
RU2001116535/02A RU2203976C2 (ru) 2001-06-13 2001-06-13 СПОСОБ ОБРАБОТКИ ЛИТЫХ ЗАЭВТЕКТОИДНЫХ СПЛАВОВ НА ОСНОВЕ АЛЮМИНИДОВ ТИТАНА γ-TiAl И α-Ti3Al

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WO2002101110A3 WO2002101110A3 (fr) 2003-02-20

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6997995B2 (en) * 2000-12-15 2006-02-14 Leistrits Turbinenkomponenten Remscheid GmbH Method for producing components with a high load capacity from TiAl alloys

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2459683C1 (ru) * 2011-02-25 2012-08-27 Открытое акционерное общество Акционерная холдинговая компания "Всероссийский научно-исследовательский и проектно-конструкторский институт металлургического машиностроения имени академика Целикова" (ОАО АХК "ВНИИМЕТМАШ") Способ изотермической штамповки заготовок с глобулярной структурой
RU2503738C2 (ru) * 2012-03-02 2014-01-10 Федеральное государственное бюджетное учреждение науки Институт проблем сверхпластичности металлов Российской академии наук (ИПСМ РАН) СПОСОБ ТЕРМИЧЕСКОЙ ОБРАБОТКИ ЛИТЫХ ЗАГОТОВОК ИЗ ЗАЭВТЕКТОИДНЫХ ИНТЕРМЕТАЛЛИДНЫХ СПЛАВОВ НА ОСНОВЕ ФАЗ γ-TiAl+α2-Ti3Al
RU2606685C1 (ru) * 2015-08-24 2017-01-10 Федеральное государственное автономное образовательное учреждение высшего образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") Способ термомеханической обработки литых (γ+α2)- интерметаллидных сплавов на основе алюминида титана γ-TiAl
RU2613829C2 (ru) * 2015-09-02 2017-03-21 Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") Способ получения деформированных полуфабрикатов из интерметаллидных титановых сплавов

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5328530A (en) * 1993-06-07 1994-07-12 The United States Of America As Represented By The Secretary Of The Air Force Hot forging of coarse grain alloys
US5442847A (en) * 1994-05-31 1995-08-22 Rockwell International Corporation Method for thermomechanical processing of ingot metallurgy near gamma titanium aluminides to refine grain size and optimize mechanical properties
US5609698A (en) * 1995-01-23 1997-03-11 General Electric Company Processing of gamma titanium-aluminide alloy using a heat treatment prior to deformation processing
RU2164263C2 (ru) * 1999-06-17 2001-03-20 Институт проблем сверхпластичности металлов РАН СПОСОБ ОБРАБОТКИ ЗАГОТОВОК ИЗ ЗАЭВТЕКТОИДНЫХ γ+α2 СПЛАВОВ

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6997995B2 (en) * 2000-12-15 2006-02-14 Leistrits Turbinenkomponenten Remscheid GmbH Method for producing components with a high load capacity from TiAl alloys

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