WO1998017836A1 - Procede de traitement d'alliages de titane et articles ainsi obtenus - Google Patents

Procede de traitement d'alliages de titane et articles ainsi obtenus Download PDF

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Publication number
WO1998017836A1
WO1998017836A1 PCT/US1997/018642 US9718642W WO9817836A1 WO 1998017836 A1 WO1998017836 A1 WO 1998017836A1 US 9718642 W US9718642 W US 9718642W WO 9817836 A1 WO9817836 A1 WO 9817836A1
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Prior art keywords
grain size
temperature
deforming
heat
stage
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PCT/US1997/018642
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English (en)
Inventor
Oskar Akramovich Kaibyshev
Gennady Alekseevich Salishchev
Rafael Mansurovich Galeyev
Ramil Yavatovich Lutfullin
Oleg Rayazovich Valiakhmetov
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General Electric Company
Institute Of Metals Superplasticity Problems Of Russian Academy Of Siences
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Application filed by General Electric Company, Institute Of Metals Superplasticity Problems Of Russian Academy Of Siences filed Critical General Electric Company
Publication of WO1998017836A1 publication Critical patent/WO1998017836A1/fr
Priority to US09/297,111 priority Critical patent/US6589371B1/en

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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 given invention is related to the field of metallurgy. More particularly, the invention relates to methods of preparing titanium alloys working with the lamellar structure. This invention is useful for making large semi-finished parts by working them with pressure to subsequently make finished products of different shapes.
  • the large section parts may be utilized in aerospace industries, for example, disks, jet-engine blades, and airframe structures.
  • Titanium alloys are hard to deform materials. Titanium alloys with microstructures of fine grains have better plasticity than those with coarse grains.
  • the need to increase the plasticity of titanium alloys results in the need to develop methods of making titanium alloy microstructures with grain sizes less than about 10 micrometers.
  • Such a microstructure can be obtained in small section semi-finished products, for example, in hot-rolled bars with diameters not exceeding 60 millimeters.
  • the microstructure of semi-finished products is coarser in large section sizes. Most semi-finished products have a coarse lamellar microstructure with crystallographic and metallographic texture having a grain size larger than 100 micrometers.
  • Grain coarsening in titanium alloys results in unsatisfactory mechanical properties.
  • a noteworthy feature of a coarse-grained lamellar microstructure is that it has a high degree of structural heterogeneity which results in combination of low tensile strength and lower plasticity, low fatigue properties, and significant scatter in mechanical properties. It is not possible to make the coarse-grain lamellar microstructure into a fine-grain microstructure by heat treatment. On the otherhand, it is possible to coarsen fine-grain microstructure of titanium alloys at the temperatures of single beta phase existence and at the temperatures in the two phase alpha and beta regions. Producing a homogeneous fine-grain microstructure in titanium alloys would improve the technological properties during the thermomechanical processing due to reduction of stresses required for plastic flow. Also, the superior mechanical properties of semi-finished products would be provided, as well as superior mechanical properties after heat treatment.
  • the conventional method of working titanium alloys such as gatorizing, is known. It includes initial working at temperatures about 56°C lower than the recrystallization temperature, with subsequent heating and working (pressing/forging) of the alloys at the recrystallization temperature.
  • the recrystallization temperature is the temperature that the metal starts to deform.
  • the formation of fine- grain microstructure is achieved by means of recrystallization of a work-hardened material during subsequent working.
  • the above- mentioned method of microstructure refinement can be applied mainly for semi-finished products which had been previously intensely hot- worked in the alpha and beta regions. An elongated microstructure and strong texture are formed in these worked titanium alloys, which lead to significant allotropy of the mechanical properties.
  • This invention satisfies the above-mentioned need by providing a method of manufacturing titanium alloys in large-section semi-finished product form with controlled microstructure in micrograin and subcrystalline states of aggregation, with reduced metallographic texture, to achieve the desired combination of mechanical properties in the titanium alloy product.
  • the final fine grain size is less than or equal to about 15 micrometers.
  • a fine grain size is defined as grains having less than or equal to about 15 micrometers diameter. More narrowly, a preferred fine grain is less than 5 micrometers diameter. Conversely, large grains are greater than 15 micrometers diameter.
  • Another embodiment of the invention is a method of making a substantially controlled homogeneous fine grain microstructure in a titanium alloy article, comprising the steps of: heating and deforming at a predetermined heat and deforming stage temperature at or below a temperature of complete polymorphous transformation where the titanium alloy article has sufficient ductility and a starting grain size, said heat and deforming stage contains at least one heat and deforming step and at least one cooling step, and where said heat and deforming stage is for a sufficient amount of time to reduce the grain size from the starting grain size at the beginning of the heat and deforming stage to a reduced grain size at the end of the heat and deforming stage, where deforming the titanium alloy is in a controlled manner at a rate of strain to achieve the desired grain size of the heat and deforming stage, where the true strain during the deformation is greater than or equal to 0.6 for each heat and deforming stage and where the cooling step is performed after the heat and deforming step at a temperature below the heat and deforming stage temperature, in a controlled manner at a cooling rate to substantially maintain the reduced grain size
  • Still another embodiment of the invention provides methods of making large section semi-finished products without any limits in size and shape.
  • semi-finished product is defined as a material form, such as a bar, plate or billet, that is supplied for further processing.
  • a bar is a semi-finished product from which bolts, pins, etc., are manufactured.
  • a billet is a semi-finished product from which aircraft disk forgings are made.
  • the term large section is relative to the part being semi-finished. For instance, a titanium alloy billet greater than about 4 inches could be termed large, disk forgings greater than about 30 inches diameter or 6 inches thickness are large.
  • Lamellar structure refers to alpha phase (hexagonal crystal structure) titanium arranged in plates. Often, plates share a common crystallographic orientation and are termed a "colony”.
  • FIG. 3- Microstructure of titanium alloy BT8 after working at 950°C.
  • Fig. 4- Microstructure of titanium alloy BT8 after working at 650°C.
  • Fig. 5- Relation of recrystallized grain size to strain temperature for titanium alloy BT1-00.) at strain rate of 3 10 "4 sec '1 and at e 0.6 strain.
  • the d * and T * areas (at d 0 200 mm) are shaded.
  • Fig. 6- Microstructure of titanium alloy BT1-00 in initial state.
  • Fig. 10- Microstructure of titanium alloy BT30 in initial state.
  • the invention is achieved by methods of working titanium alloys which include heating of the starting stock or ingot and its deformation inside preheated forging tools.
  • a distinguishing feature of the method is that the temperature range for thermomechanical processing is extended to the range of about 400°C to T cp petition where T cpt is the temperature of the complete polymorphous transformation, also called the beta transus.
  • the temperature of complete polymorphous transformation (beta transus) is the temperature at which all alpha phase in the titanium alloy has transformed to beta phase.
  • the specified temperature range (400°C to T cpt ) is then divided into two zones.
  • the boundary between those zones is set at the temperature T* at which the grain size is d * .
  • the grain size d * can be determined from the ratio Ig (d o /d*) equals about 2.4 to about 2.6 for the alloys with the beta stabilization coefficient K B ⁇ about 1.4 and Ig (d ⁇ d*) equals about 1.8 to about 2 for the alloys with K B > 1.4, where d 0 is the grain size of the initial stock or ingot.
  • the deformation can be done in one or several stages.
  • the number of stages and the temperature of each stage shall be defined by subsequent adding to the T ⁇ temperature the difference in the temperatures a the nearest stages until the strain temperature exceeds or is getting equal to the T * temperature.
  • the deformation at each heating and deforming stage is processed by strain e not less than 0.6.
  • the heating of the stock or ingot at each following stage is provided to the temperature which does not exceed the strain temperature at the previous stage.
  • the deformation at each stage is provided at the stage temperature in several steps.
  • the deformation axis may rotate or turn the stock and change the deflection angle of between about 45 - 90°.
  • the deformation is performed in the preferred strain rate range of about 10 ⁇ * - 10 " sec "1 .
  • the deformation temperature should be corrected by multiplying a coefficient dependent on a semi-finished product volume. This coefficient is 0.98 for the volume up to 1 dm 3 , 0.97 for the volume from 1 to 10 dm 3 , and 0.95 for the volume greater than 10 dm 3 . It should be noted that as the strain rate increases, the coefficient becomes a more important factor in the processing of the titanium alloys.
  • the stock with the original beta-transformed grain size greater than 2000 micrometers must be worked (deformed) before the first heat and deforming stage at a temperature higher than the polymorphous transformation temperature, such that T cpt + 10-50°C.
  • the obtained grain size should be considered " as the original grain size during the selection of the region of the main working.
  • the stock with original beta-transformed grain size greater than 2000 micrometers must be deformed with a reduction of 0.3 and strain rate in the range of 10 " 2 - 10 3 sec '1 at the temperature higher than T cpt - 30-50°C and with subsequent heating up to T cpt + 20-70°C and cooled down to room temperature at the rate of about 5 - 100°C/sec.
  • the stock at least after the first strain stage should be cooled down to room temperature at the rate of about 5 - 100°C/sec.
  • the thermocycle treating should be carried out in the temperature range from about 500 °C to T cpt with the number of cycles from 1 to 5 before deforming. This may not be needed and depends on the grain size of the titanium alloy stock.
  • the stock may be deformed in tools preheated to the temperature of about 10 - 50°C higher than the heating temperature of the worked alloy. This is an optional step.
  • the amount of steps of deforming may be chosen to be four or more at the final heat and deforming stage in additional to that the turning of the axis of deformation must be provided in a single plane.
  • the forming of semi-finished products of different shapes from the stocks with prepared microsructures can be accomplished by forming them at a temperature not lower than the strain temperature of the stock at the final heat and deforming stage of the stock material. In addition to this, the following is also recommended: forming (shaping) must be done under superplasticity conditions. Local deformation must be used.
  • the problem of making semi-finished products of unlimited sizes with micro- ( ⁇ 15 micrometers) and submicro-crystalline ( ⁇ 1 micrometer) structures can be achieved by tightly setting a block of stocks or semi-finished products, and carrying out the block upsetting at the strain rate of about 10 " " - 10 '2 sec "1 and the true-strain not less than 0.2 within the temperature range from 400°C to T CPT where the upsetting temperature at the finishing stage is chosen to be not less than the strain temperature of the stock or semi-finished product with the coarsest grain size.
  • the upsetting temperature must be not lower than the highest one of any of them.
  • Another aspect is to set up a block of at least two stocks or semi-finished products, and place between them the layer from the same material with grain size (d) by an order of magnitude less than what is in the stocks or semi-products.
  • the layer thickness should be not less than 10 d.
  • the upsetting of the block must be carried out at the strain rate of 10 5 - 10 "1 sec 1 , at 0.2 the true strain, in the temperature range from 400°C to T CPT , and where, the upsetting temperature is chosen to be not lower than the temperature at the final stage of working at which the grain size of the layer was obtained.
  • the essence of the invention is based on the fact that the uniform fine-grained microstructure with required grain size up to submicro-crystalline grains is formed as the result of the process of dynamic recrystallization over the wide temperature range of 400°C - T CPT .
  • the dynamic recrystallization of titanium and its alloys is difficult due to low diffusion mobility of atoms.
  • the dynamic recrystallization at those lower temperatures can not be carried out practically by the use of conventional equipment.
  • the T* temperature can be considered in a range of temperatures, and T* depends on the initial grain size (d 0 ) and increases with the initial grain size to about the temperature of the complete polymorphous transformation.
  • the T * temperature divides the specified temperature range (400°C- T cpt ) into two zones: T cpt - T * and T- 400°C.
  • first zone including the T* temperature
  • second zone the stock is worked for more than one heat and deforming stage, with lowering of the temperature. This is caused by the fact that the technological plasticity of titanium alloys significantly depends on the microstructure, which is why at each previous heat and deforming stage it is necessary to obtain the microstructure with the proper grain size that achieves the necessary level of technological plasticity at the subsequent stage.
  • the one or more stages of working must be determined depending on which temperature zone of the curve the T ⁇ is located.
  • the amount of those stages and the stage temperatures is chosen as follows: by adding step-by-step (sequentially) to the T ⁇ the regulated difference between stage temperatures until the strain temperature does not exceed (or is equal) to the T ⁇ .
  • true strain "e” Values of true strain "e" are used, because the true strain is an equivalent for different loading, and it allows calculations of the required strain for processes like upsetting, drawing, extrusion, rolling, or torsion.
  • a strain not less than 0.6 at each heat and deforming stage provides a dynamic recrystallization over the volume of the stock, and, therefore, results in an uniform fine grained microstructure.
  • the heating at each stage must be done until the temperature does not exceed the strain temperature at the previous stage, otherwise the grain size coarsing will take place during heating.
  • the invention essence can be additionally developed and made precise by the usage of the following procedures.
  • Decreasing of a strain rate is one of the ways to improve the technological plasticity (hot ductility), and in consequence of that, of strain uniformity. It is recommended to carry out the working or deforming at strain rates in the range of about 10 " - 10 2 sec 1 . Dynamic recrystallization in that range can result in superplastic metal flowing, depending on the initial state of material, and additionally to increase or improve the microstructure uniformity of the processed article.
  • Titanium alloys have low thermal conductivity. Therefore, during the working process, the temperature of the central area of a massive stock always is higher compared with that of peripheral areas, because of strain heating and insufficient transmission of heat in the stock central area. As a result, a coarse grain size can be formed in the center area of a massive stock. That is why in this invention the heating temperature is adjusted (depending on the stock size): multiplying the experimentally determined coefficients. In this case the difference in grain sizes over the stock volume is eliminated by heating during which the grains in the peripheral areas of the stock are getting coarser.
  • Titanium alloys with the size of beta-transformed grains more than 2000 micrometers have low hot ductility (low technological plasticity) at temperatures below T cpt .
  • the total strain must be increased by usage of multi-passes working at a stage.
  • those titanium alloys have the T * near the T cpt , therefore, it is expedient to provide a pre-working procedure of the titanium alloys with the size of beta- transformed grains more than 2000 micrometers before the main working process.
  • This preliminary working can be carried out at about 30-50°C below T cpt , a strain not less than 0.3, and a strain rate in the range of about 10 "2 - 10 1 sec "1 with subsequent annealing at temperature of T cpt + 20-70°C.
  • the method includes selections of sequences of the stock turns during multi-pass strain at the finish stage. For example, to make a bar at the finishing stage of working, the turn of deformation axis between passes is carried out at one plane, and the number of passes should not be less than four.
  • the shaping of the semi-finished product from the stock with specified microstructure should be done at a temperature not below the strain temperature of the stock at the finishing stage.
  • the article should be treated to about T ⁇ or a little higher to increase the ductility of the material.
  • the temperature should be at a temperature sufficient to increase the ductility without substantially changing the final grain size.
  • strain rate for shaping can be chosen in such a way to ensure superplastic conditions of deformation. This additionally improves the microstructure uniformity, and achieves a high level of mechanical properties after a final heat-treatment.
  • the technological conditions of achieving a homogeneous fine grain microstructure in unlimited size or large semi- finished products can be simplified by building up (gathering) a block in a prearranged size (specified size) from small stocks, and subsequently applying controlled strain of that block (for example, by upsetting) within the temperature range of 400°C-T cpt , at strain rates of about 10 '5 - 10 1 sec "1 , at not less than 0.2 strain.
  • the specific block strain temperature must not be chosen below the strain temperature of stocks at the final stage.
  • the described above working parameters insure superplastic flow conditions during the deformation of the block.
  • the fundamental mechanism of superplastic deformation is grain boundary slipping (GBS), e.g., turn and slipping displacement of adjoining grains relatively to each other.
  • GBS development during the block deformation allows to get a solid state joining of small stocks, moreover, at 0.2 and greater strain, the block becomes monolithic, and the boundary lines between the stocks that formed the block, disappear completely. This is achieved due to elimination of all possible pores in the joining area of the stocks by grain motion resulting from GBS. No less than 0.2 strain is required for stable superplastic deformation with maximum development of the GBT mechanism. Under such conditions the formation of high-grade solid state joining can be guaranteed.
  • the semi-finished stocks worked by described above method can be used further as initial stocks to make larger semi-finished products.
  • the requirements in physical, mechanical or service characteristics for different areas of the same large section products, for example, turbine disks for aircraft engines, can vary significantly.
  • the assembly and subsequent deformation of stocks from alloys with different chemical composition, consequently, with different strain temperatures at the final working heat and deforming stage, may be considered like the method of making large section part.
  • the assembled block has to be deformed at the temperature not less than the highest strain temperature among joined stocks.
  • the invention is illustrated by the following examples. Three alloys the chemical composition of which is shown in the table were worked.
  • the stock volume (0 150-300 mm) does not exceed of 10 dm 3 , thus, taking into account the correction factor of 0.97, the heating temperature will be of 925°C.
  • the stock is placed into KS-500 resistor furnace.
  • the heating time determined under condition that mm of diameter should be heated per minute will be minimum 150 minutes.
  • the stock is placed into an isothermal press tool, which open dies from superalloy KC6-Y, are heated in low-frequency inductor up to 950°C.
  • the strain of the stock at the stage is carried out at the average rate of 710 "4 sec 1 .
  • thermocyclic treating which includes five repeated heatings up to 1000°C and cooling to 500°C should be carried out before the working of the alloy.
  • the stock strain at each stage should be done at several passes (similar to example 1).
  • the stock can be formed into a rod, the cross section of which is equilateral triangle, or square, or equilateral hexagon.
  • the microstructure of the worked alloy is shown in Fig.4.
  • the described above treatment will result in the beta- transformed grain size of 1000 ⁇ m, and that grain size is used for definition of the T* temperature (required for achievement of the grain size 3 ⁇ m ) and can be defined from the curves in Figure 1.
  • the heating temperature and required strain of the stock can be defined similar to Example 1.
  • the die tools shall be heated up to the temperature 900°C.
  • the stock is first formed into the disk stock 350 mm in diameter.
  • the final semi-finished disk product will be obtained by flattening under superplastisity conditions.
  • Example 4 It is required to work a stock (100 x 100 x 200 mm) from alloy A with the initial beta-transformed grain size of 5000 ⁇ m into the stock of the same size and grain size of 2 ⁇ m. In order to reach that goal, it is expedient preliminarily to refine the initial grain structure.
  • the described treatment will result in the beta-transformed grain size of 500 ⁇ m , and the last is used for defining of the T* temperature (in that case, it will be 780-830°C ).
  • the T ⁇ temperature required for achieving the grain size of 3 ⁇ m can be defined from the curves in Figure 1. That is the temperature 830°C, e.g., within the range of T * - T cpt , therefore, the stock will be preliminary worked at one stage.
  • the heating temperature and required strain of the stock can be defined similar to Example 1.
  • the strain should be carried out at rate of 10 ⁇ 3 sec at six passes with turn of the stock through 90° after each pass in such way that upsetting (load direction) will coincide with the largest stock size.
  • the stock can be under superplastic conditions at 830°C into a rod, the cross section of which is equilateral triangle, or square, or equilateral hexagon.
  • Example 5 It is require to work a stock (100 x 100 x 200 mm) from alloy A with the initial beta-transformed grain size of 5000 ⁇ m into the stock of the same size and grain size of 1.2 ⁇ m. In order to reach that goal , it is expedient preliminarily to fine the initial grain structure.
  • the described above treatment will result in the beta-transformed grain size of 500 ⁇ m, and the last is used for defining of the T* temperature (in that case, it will be 780-830°C ).
  • the heating temperature and required strain of the stock can be defined similar to Example 1.
  • the strain should be carried out at rate of 10 sec. " at six passes with turn of the stock through 90° after each pass in such way that upsetting (load direction) will coincide with the largest stock size.
  • the final shape of the semi-finished product will be the square section parallelopiped 55 ⁇ m in side size.
  • the microstructure of the worked stock after treating is shown in Fig. 7.
  • Example 7 It is necessary in the alloy B stock (0 50 x 100 mm )with the initial grain size of 200 ⁇ m (Fig.6) to obtain the microstructure with the average grain size of 0.1 ⁇ m.
  • Determined values of the T ⁇ and T* temperatures are 400°C and 520-550°C, respectively.
  • the stock will be worked at several stages, the number of which can be determined as follows.
  • the grain size before the final stage is chosen twice larger (coarser) (e.g., 0.2um).
  • the grain size of 0.2um correlates to the temperature 450°C (see the curve in Fig.5) which does not exceed T * , thus, one more stage is required.
  • the stock should be worked at four stages, and the temperature at each stage are 670, 500, 450 and 700°C.
  • the strain at each stage can be determined taking into account the strain temperature at the stage and the initial grain size before working at each stage.
  • the stock at each stage is deformed at several passes similar to that in example 1.
  • the stock can be formed into a rod, the cross section of which is equilateral triangle, or square, or equilateral hexagon.
  • the microstructure of the worked alloy is shown in Fig. 8.
  • That grain size (3 ⁇ m) correlates to the temperature of 730°C, which is between T*- T cpt , therefore, that stage will be the first one during working.
  • the choice of the strain, heating temperature, and strain chart at each stage is carried out in the way illustrated in example 1.
  • the stock should be water cooled to room temperature.
  • the microstructure of the worked stock is shown in Fig 12.
  • Example 10 It is necessary in the alloy C stock (0 50 x 100 mm ) with the initial grain size of 40 ⁇ m to obtain the microstructure with the average grain size of 0.5 ⁇ m. Determined values of the Tk and T * temperatures are of 625°C and 600-645°C, respectively. As the T k is within the range T * -T cpt , the stock will be worked at one stage. Before the main treatment, the stock is heated to the temperature of 760°C and water cooled then to room temperature. The choice of the strain, heating temperature, and strain chart at each stage is carried out in the way illustrated in example 1.
  • Example 11 It is necessary to obtain a semi-finished product with the average grain size of 5 ⁇ m from the alloy A stock (0200 x 400 mm ) with the beta-transformed grain size of 2000 ⁇ m.
  • the values of the T ⁇ and T* temperatures determined from the curve in Figure 1 are of 950°C and 950-990°C, respectively.
  • the stock will be worked at one stage. It can be defined that the required strain e should be not less than 2.7.
  • next strain chart should be used: stock heating up to the temperature of 95 °C, stock deformation through the stock height at 0.25 strain, subsequent water cooling to room temperature; stock heating up to the temperature of 950°C, stock deformation through the stock at five passes at 0.25 strain at each pass, and with the stock turn through 90° between the passes, and subsequent water cooling to room temperature; repeat two previous paragraphs.
  • the rod 100 ⁇ m in diameter will be obtained after the final formation.
  • Cylindrical stocks 40 mm in height are cut from a rod (0 20 mm) from alloy B with submicrocrystalline structure with the average grain size of 0.1 ⁇ m.
  • the stocks are heated in an electrical furnace in Argon inert atmosphere up to the temperature of 400°C and upset at the average strain rate of 5 10 "4 sec "1 up to 10 mm in height in a large (100 tonne power) hydraulic press between plain dies preheated by an inductor up to 400°C.
  • the stocks of a disk shape 40 mm in diameter will be produced.
  • the grain size in the disk stocks retain of 0.1 ⁇ m.
  • the disk stocks are machined to 38 mm in diameter. The upper and bottom surfaces of the disk stocks are being polished ( from each surface the layer not less than 0.5 mm has been deleted).
  • the heating of the surface of the worked disk stock must not exceed 50°C.
  • the polished surfaces are washed, dried and degreased. Then the block in the form of a cylinder 38 mm in diameter and 81 mm in height is set up from nine stocks 38 mm in diameter and 9 mm in height placed one over another coaxially.
  • a disk stock with submicrocrystalline microstructure and practically of any size can be manufactured making use of industry heating and forging equipment.
  • Example 13 Cylindrical stocks 60 mm in height are cut from a rod (0 30 mm) from alloy A with submicrocrystalline structure with the average grain size of 0.4 ⁇ m. The stocks are heated in an electrical furnace in Argon-inert atmosphere up to the temperature of 700°C and upset at the average strain rate of 5 10 4 sec 1 up to 10 mm in height in a large (100 tonne power) hydraulic press between simple dies preheated by an inductor up to 700°C. The stocks of a disk shape about 74 mm in diameter and 10 mm in height will be produced .
  • the grain size in the disk stocks remains of 0.4 ⁇ m.
  • the disk stocks are machined to 72 mm in diameter.
  • the upper and bottom surfaces of the disk stocks are polished (from each surface the layer not less than 0.5 mm has been removed) and made parallel. During the mechanical treatments, the heating of the surface of the worked disk stock must not exceed 50°C.
  • the polished surfaces are washed, dried and degreased. Then the block in the form of a cylinder 72 mm in diameter and 144 mm in height is set up from 16 stocks, 72 mm in diameter and 9 mm in height placed one over another coaxially.
  • laser welding must be performed to the depth not more than 0.3 mm along the ring line of the stock joint.
  • the stocks block is heated in an electrical furnace in Argon-inert atmosphere up to the temperature of 700°C and upset at the average strain rate of 510 "4 sec "1 up to 20 mm in height in a large (100 tonne power) hydraulic press between simple dies preheated by an inductor up to 700°C.
  • the semifinished product 192 mm in diameter and 20 mm in height will be produced.
  • the grain size in the disk stocks remains of 0.4 um over the whole volume. Porosity in the zone of solid-phase joining is not revealed by metallography.
  • a disk stock with submicrocrystalline microstructure and practically of any size required for development can be manufactured using industry heating and forging equipment.
  • Cylindrical stocks 100 mm in height are cut from a rod (0 50 mm) from alloy C with submicrocrystalline structure with the average grain size of 2.0 ⁇ m.
  • the stocks are heated in an electrical furnace in Argon inert atmosphere up to the temperature of 700°C and upset at the average strain rate of 5 10 "4 sec "1 up to 10 mm in height in a large (100 tonne power) hydraulic press between simple dies preheated by an inductor up to 700°C.
  • the stocks of a disk shape about 158 mm in diameter and 10 mm in height will be produced .
  • the grain size in the disk stocks remains of 2 ⁇ m.
  • the disk stocks are machined to 156 mm in diameter.
  • the upper and bottom surfaces of the disk stocks are being polished (from each surface the layer not less than 0.5 mm has been removed) and made parallel. During the mechanical treatments, the heating of the surface of the worked disk stock must not exceed 50°C. The polished surfaces are washed, dried and degreased. Then the block in the form of a cylinder 72 mm in diameter and 144 mm in height is set up from 16 stocks, 72 mm in diameter and 9 mm in height placed one over another coaxially. In order to fix the assembled block and to protect the inner contact surfaces of the stocks from oxidation, laser welding must be performed to the depth not more than 0.3 mm along the ring line of the stock joint.
  • the block unit in the form of a cylinder 156 mm in diameter and 306 mm in height is assembled from 34 stocks of 156 mm in diameter and 9 mm in height placed one over another coaxially.
  • the block assembly is carried out directly on the lower flat die installed in a 1600 tonne power hydraulic press. After the end of the assembly the block is tightened by lowering of the upper flat die. The compression stress does not exceed 10 tonne.
  • the dies together with the stocks block are heated in an inductor in argon atmosphere up to the temperature of 700°C and then upset to 30 mm in height at the average rate of 5 10 "4 sec 1 .
  • the working surfaces of the dies from alloy KC6-Y ( Russian Spec.) are preliminary coated with a thin layer of boron nitride in order to reduce friction coefficient and prevent sticking to the stock.
  • the semi-finished product of about 498 mm in diameter and 30 mm in height will be produced.
  • the grain size in the disk stocks remains of 2 ⁇ m over the whole volume. Porosity in the zone of solid-phase joining is not revealed by metallography.
  • Example 15 In the way similar to described in the above examples the cylindrical disk-type stock 300 mm in diameter and 50 mm in height is made of the 0 20 mm rod from alloy A with microcrystalline microstructure. The strain temperature is 650°C. The ring stock 300 mm in outer diameter and 100 mm in inner diameter is made from that disk stock by cutting off its central area by a mechanical, or anode- mechanical, or arc cutting by fusion method.
  • the cylindrical stock 0 100 "0 15 mm and 50 mm in height are made of the 0 20 mm rod from alloy C accordingly to described in previous examples manner. Moreover, the strain temperature is 650°C. Then the disk stock 300 mm in diameter and 50 mm in height is assembled from the alloy A ring stock and the alloy C stock by installing the alloy C stock into the center of the alloy A ring stock. Before assembling the contact flat surfaces of the block stock have to be polished (the heating of the surfaces must not exceed 50°C during polishing). The polished surfaces are washed, dried and degreased. Then the block in the form of a cylinder 38 mm in diameter and 81 mm in height is set up from nine stocks 38 mm in diameter and 9 mm in height placed one over another coaxially. In order to fix the assembled block and to protect the inner contact surfaces of the stocks from oxidation, laser welding must be performed to the depth not more than 0.5 mm along the ring line of the stock joint.
  • the assembled block stock is installed on the bottom die in a 1600 tonne power hydraulic press and tightened by lowering of the upper flat die.
  • the compression stress does not exceed 10 tonne.
  • the dies together with the block stock are heated in an inductor in argon atmosphere up to the 650°C and upset to of 25 mm in height at the average rate of 510 "4 sec "1 .
  • the working surfaces of the dies are preliminary coated with a thin layer of boron nitride.
  • the central area of that disk stock is mad from alloy C with the grain size of 0.5 ⁇ m, and the rim - from alloy A with grain size of 0.2 ⁇ m.
  • Example 16 the cylindrical disks 350 mm in diameter and 70 mm in the height with grain size of 3 ⁇ m are made from alloy A under superplastic deformation conditions at the temperature of 900°C.
  • the sheet stocks 350 mm in diameter and one mm in the height are made of the 0 20 mm rod from the same alloy with grain size of 0.2 ⁇ m are made by superplastic strain, and subsequent upsetting, rolling, and machining.
  • the sheet-stock is placed between each couple of the disk stock (placed coaxially on each other) between each couple of the disk stock (placed coaxially on each other) between each couple of the disk stock (placed coaxially on each other) the sheet-stock is placed. In that manner the cylindrical block stock 350 mm in diameter and 354 mm in height will be set up (assembled). Before assembling the contact flat surfaces of the stocks have to be polished (the heating of the surfaces must not exceed 50°C during polishing). The polished surfaces are washed, dried and degreased. The block stock assembly is carried out directly on the lower flat die installed in a 1600 tonne power hydraulic press. After the end of the assembly the block is tightened by lowering of the upper flat die. The compression stress does not exceed 10 tonne.
  • the dies together with the block stock are heated in an inductor in argon atmosphere up to the 650°C and upset to of 351 mm in height at the average rate of 5 10 "4 sec "1 .
  • the working surfaces of the dies are preliminary coated with a thin layer of boron nitride.
  • the monolithic semi-finished disk stock 350 mm in diameter and 351 mm in height will be made.
  • the obtained block-stock is annealed at the temperature of 900°C. After that heat treatment the made rod stock 350 mm in diameter will have the uniform microstructure with the grain size of 3 ⁇ m.

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Abstract

Cette invention concerne un procédé de fabrication d'alliages de titane, sous la forme d'un produit semi-fini de grandes sections présentant une microstructure contrôlée en états d'agrégation micrograinés ou subcristallins, et une texture métallographique réduite. Ledit procédé permet de conférer au produit en alliage de titane la combinaison de propriétés mécaniques voulues.
PCT/US1997/018642 1996-10-18 1997-10-17 Procede de traitement d'alliages de titane et articles ainsi obtenus WO1998017836A1 (fr)

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RU96120958 1996-10-18
RU96120958A RU2134308C1 (ru) 1996-10-18 1996-10-18 Способ обработки титановых сплавов

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WO2002072906A1 (fr) * 2001-03-11 2002-09-19 Institut Problem Sverkhplastichnosti Metallov Ran Procede de traitement des ebauches, principalement de grandes dimensions, en alliages de titane ($g(a)+$g(b))
WO2003035130A1 (fr) * 2001-10-25 2003-05-01 Advanced Cardiovascular Systems, Inc. Fabrication de materiau a grains fins pour dispositifs medicaux
US7008491B2 (en) 2002-11-12 2006-03-07 General Electric Company Method for fabricating an article of an alpha-beta titanium alloy by forging
EP1872882A2 (fr) * 2005-03-23 2008-01-02 Institut Problem Sverkhplastichnosti Metallov Ran Procede de fabrication d'un article au moyen du formage superplastique et de soudage par diffusion
EP2048260A4 (fr) * 2006-07-06 2009-04-15 Inst Sverkhplastichnosti Metal Procédé de fabrication d'un blanc en feuille à partir d'un alliage de titane
WO2012036841A1 (fr) * 2010-09-15 2012-03-22 Ati Properties, Inc. Trains de traitement de titane et d'alliages de titane
WO2014093009A1 (fr) * 2012-12-14 2014-06-19 Ati Properties, Inc. Procédés de traitement d'alliages de titane
US9050647B2 (en) 2013-03-15 2015-06-09 Ati Properties, Inc. Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys
US9192981B2 (en) 2013-03-11 2015-11-24 Ati Properties, Inc. Thermomechanical processing of high strength non-magnetic corrosion resistant material
US9206497B2 (en) 2010-09-15 2015-12-08 Ati Properties, Inc. Methods for processing titanium alloys
US9255316B2 (en) 2010-07-19 2016-02-09 Ati Properties, Inc. Processing of α+β titanium alloys
US9523137B2 (en) 2004-05-21 2016-12-20 Ati Properties Llc Metastable β-titanium alloys and methods of processing the same by direct aging
US9616480B2 (en) 2011-06-01 2017-04-11 Ati Properties Llc Thermo-mechanical processing of nickel-base alloys
US9777361B2 (en) 2013-03-15 2017-10-03 Ati Properties Llc Thermomechanical processing of alpha-beta titanium alloys
US9796005B2 (en) 2003-05-09 2017-10-24 Ati Properties Llc Processing of titanium-aluminum-vanadium alloys and products made thereby
US9869003B2 (en) 2013-02-26 2018-01-16 Ati Properties Llc Methods for processing alloys
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
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US10502252B2 (en) 2015-11-23 2019-12-10 Ati Properties Llc Processing of alpha-beta titanium alloys
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RU2586188C1 (ru) * 2014-12-04 2016-06-10 Федеральное государственное бюджетное образовательное учреждение высшего образования "Санкт-Петербургский государственный университет" (СПбГУ) Способ интенсивной пластической деформации кручением под высоким давлением при ступенчатом нагреве заготовок
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US8562664B2 (en) 2001-10-25 2013-10-22 Advanced Cardiovascular Systems, Inc. Manufacture of fine-grained material for use in medical devices
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US8579960B2 (en) 2001-10-25 2013-11-12 Abbott Cardiovascular Systems Inc. Manufacture of fine-grained material for use in medical devices
US8211164B2 (en) 2001-10-25 2012-07-03 Abbott Cardiovascular Systems, Inc. Manufacture of fine-grained material for use in medical devices
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