Method for isothermally forging nickel base super-alloys in air

FIELD: plastic working of metals, possibly forging blanks of nickel base super-alloy.

SUBSTANCE: method is realized with use of forging press with forging die sets of nickel base super-alloy having yield limit no less than stress of plastic yielding of super-alloy at forging for making forged pieces at temperature range approximately from 926.67°C till approximately 1010.00°C at nominal deformation rate. Blank for forging and die sets are heated till said forging temperature. Forging is realized at such temperature and at nominal deformation rate. Nickel base super-alloy selected from group of alloys may be used as material of forged blank. According to one variant of invention blank of compacted powder of nickel base super-alloy is used for forging. In such case die sets are made of nickel-base super-alloy containing, mass%: aluminum, approximately 5 - 7%; molybdenum, approximately 8 - 15%; tungsten, approximately 5 - 15%; magnesium, near 140 ppm; nickel and impurities, the balance.

EFFECT: lowered costs for producing forged pieces of super-alloy with desired properties.

15 cl, 3 dwg, 2 tbl

 

The invention relates to the forging of superalloys based on Nickel, in particular forging produced in the air.

The superalloys based on Nickel use in parts of aircraft gas turbine engines, to performance which has very high demands and which are exposed to very harsh environmental conditions. Casting superalloys based on Nickel use, such as blades and guide device turbines. Deformable superalloys based on Nickel use, such as disks and rotor shafts. The present invention relates to a deformable to superalloys based on Nickel.

Deformable superalloys based on Nickel initially supplied in the form of ingots, which were cast from metal or in the form of billets of compacted powder. Procurement of compacted powder was considered to be more preferable as a starting material in many applications, because they had a uniform, well-controlled initial microstructure and contained small grain sizes. In any case, the workpiece is reduced in size gradually, using the processes of metal working, such as forging or extrusion by extrusion, and then processing on machine tools. In one form of forging a workpiece placed between the two covoc the diversified dies in a forging press. Forging dies are pressed to each other forging pressure to reduce the thickness of the workpiece.

The choice of forging conditions depends on several factors, including the properties and metallurgical characteristics of supersplash Nickel-based and material properties of the forging dies. Forging dies must be strong enough to deform the material is subjected to forging, and deformable superslow must demonstrate the required properties after completion of the forging operation.

Currently, the superalloys based on Nickel, for example alloys Rene™ 88DT and M3, holding at a constant temperature (isothermal), amounting to about 1036,78° (1900°F) or above using TZM molybdenum stamps. This combination of supersplash subjected to forging, and the material of the stamp allows forging, and superslow has the required properties after forging. However, this combination of the temperature at which superslow is subjected to forging, and the material of the stamp you want the forging was carried out in vacuum or in an atmosphere of inert gas. The need for vacuum or inert gas atmosphere leads to considerable complication and increased cost of the forging process.

There is a need for an improved forging process superalloys based on Nickel, which was achieved would require the properties, and also would provide an opportunity to reduce the cost of the forging process. The present invention meets these requirements and, in addition, allows you to receive relevant benefits.

The present invention created a way of forging superalloys based on Nickel, for example alloys Rene™ 88DT and M3. The method allows isothermal forging in the air, resulting in significantly reduces the cost of the process. The final microstructure contains the desired structure of the grains that meets the requirements and allows additional processing, such as a final annealing to ensuring sorrysorrysorry.

The present invention created a way of forging supersplash that includes the following steps: providing a forging billet of forging supersplash Nickel-based; providing a forging press, equipped forging dies made of supersplash Nickel-base for stamping. It is desirable that superslow Nickel-based for stamps had a yield strength of not lower than the voltage plastic flow forging supersplash based on Nickel at a temperature of forging comprising from about 926,67°up to about 1010,00°With (from about 1700°F to about 1850°F), and the nominal rate of deformation during forging. The method further includes the steps of heating the forging C is cooking and forging dies to the forging temperature, component from about 926,67°up to about 1010,00°and forging the forging preform using the forging dies at a temperature of forging comprising from about 926,67°up to about 1010,00°and at a nominal strain rate in the forging process. Forging the workpiece is made from a forging supersplash on the basis of Nickel, preferably from an alloy Rene™ 88DT, having a nominal composition, wt.%: cobalt 13%, chromium 16%, mo 4%, titanium of 3.7%, aluminium 2.1%, tungsten, 4%, niobium 0,75%, boron 0,015%, zirconium 0,03%carbon 0.03%, iron up to about 0.5%, the rest is Nickel and the minimum number of impurities; or M3 alloy having a nominal composition, wt.%: cobalt, about 20.6%; chromium, about 13,0%; aluminum about 3.4%; titanium about 3,70%; tantalum, about 2.4%; niobium to about 0.90 percent; tungsten about 2,10%; molybdenum, about 3,80%; carbon, about 0.05%; Bor about 0,025%; zirconium, about 0.05%, iron 0.5%; the rest is Nickel and the minimum amount of impurities. These superalloys based on Nickel have superplasticity in an appropriate temperature range, corresponding to superplasticity at elevated temperatures. It is desirable to produce deformation during forging in the temperature range corresponding to the superplastic to avoid critical grain growth during subsequent annealing to ensuring sorrysorrysorry. The superalloys based on Nickel can be supplied in l the battle of the required form, for example in bars, packages or pieces of compacted powder. However, the superalloys based on Nickel, preferably delivered in the form of pressed blanks with a grain size not less than ASTM 12 (i.e., the grain size must comply with the ASTM standard 12 or less) (ASTM - American Society for testing and materials).

The forging dies can be made from any suitable for supersplash Nickel-based for stamps, but, preferably, the alloy must have a nominal composition, wt.%: aluminum is from about 5% to about 7%, molybdenum from about 8% to about 15%, tungsten from about 5% to about 15%, magnesium up to about 140 parts per million (preferably 140 parts per million), rare earth elements do not contain, the rest is Nickel and impurities.

The choice of the isothermal forging temperature and nominal strain rate during forging is based on consideration of the physical properties of the forging of supersplash Nickel-based and supersplash Nickel-based for stamps, as well as on the requirements for the temperature to reach the desired patterns forging supersplash Nickel-based on completion of the process. Superslow Nickel-based for stamps has sufficient yield stress to strain forging supersplash Nickel-based. With increasing temperature the tensile strength at catiii yield strength as forging supersplash Nickel-based, and supersplash on the basis of Nickel to die down, but with different speeds. In addition, the selected temperature for forging is preferred forging supersplash Nickel-base must be within the range of superplastic alloy to provide the desired final microstructure. In addition, to perform the preferred forging air temperature forging should not be so high as to forging superslow Nickel-based and superslow Nickel-based for stamps excessively oxidized.

With this in mind, the range of temperatures for isothermal forging was selected in the range from about 926,67°up to about 1010,00°With (from about 1700°F to about 1850°F). More preferably, the temperature range for isothermal forging is from about 954,44°up to about 9822,22°With (from about 1750°F to about 1800°F). The nominal rate of deformation during forging was chosen so that it does not exceed about 0,010-1. The tests showed that the bógreater strain rate within the temperature range of forging result in critical grain growth in the final resulting product.

The steps of heating and isothermal forging, preferably, performed in air at the specified temperature. Forging in the air allows more than forging in the atmosphere enertrag the gas or in vacuum, as is required when using TZM molybdenum dies, to reduce the cost of special equipment for heating and forging.

After the forging process according to the present solution, the product can be used in forgings (without additional processing), and further processed by any suitable processing means, such as Stripping, heat treatment, additional treatment, processing, cutting machines, etc. In one additional embodiment, the processing of interest, forgings heat treated by annealing at the annealing temperature higher than the temperature of dissolution of the primary gamma-phase, usually amounting to about 1148,89°With (about 2100° (F) for the alloy Rene™ 88DT and 1182,22°With (2160° (F) for alloy M3.

This decision created the technology of forging superalloys based on Nickel, which allows to obtain a finished product with quite acceptable from the point of view metallurgy, structure and properties, at the same time greatly reduce the cost of operation of forging capability of carrying out isothermal forging in the air. Other distinctive features and advantages of the present invention will become more clear when reading the subsequent detailed description of the preferred versions in combination with PR is proposed illustrations, which depicts, as an example, the principles of the present invention. Scope of the invention however, is not limited to this preferred embodiment.

Figure 1 shows the block diagram of the solutions to the practical use of the invention;

figure 2 - schematic view of the forging press and the product is subjected to forging;

figure 3 - schematic perspective view of forgings.

Figure 1 shows the block diagram of the preferred solutions for practical use of the invention. Provide forging the workpiece, the stage 20. Forging the workpiece is made from supersplash Nickel-based. According to this application, the alloy is an alloy based on Nickel, if it contains Nickel more than any other element, and, in addition, superbloom Nickel-based he is when he is strengthened by the precipitation of the primary gamma-phase or corresponding phases. Two supersplash Nickel-based, special interest, are the alloy Rene™ 88DT, having a nominal composition, wt.%: cobalt 13%, chromium 16%, mo 4%, titanium of 3.7%, aluminium 2.1%, tungsten, 4%, niobium 0,75%, boron 0,015%, zirconium 0,03%carbon 0.03%, iron up to about 5%, the rest is Nickel and the minimum number of impurities; and M3 alloy having a nominal composition, wt.%: cobalt, about 20.6%, chromium about 13,0%, aluminum around 3.4%titanium, about 3,70%, tantalum approximately the 2.4 percent, niobium is about 0.90 percent, tungsten, about 2,10%, molybdenum about 3,80%, carbon about 0.05%boron, about 0,025%, zirconium, about 0.05%, iron up to about 0.5%, the rest is Nickel and the minimum amount of impurities.

The superalloys based on Nickel can be placed in any desired form, but preferably are delivered in the form of billets of compacted powder. The workpiece compaction of powders selected superalloys by extrusion, and made them so that they contained a grain size corresponding to the ASTM standard 12 or more (i.e. meet the ASTM standard 12 or contain smaller grains as the grain size decreases with increasing number of grain size on the system ASTM). Procurement of compacted powder have an advantage in comparison with cast billets, which consists in a more uniform fine crystalline microstructure, and therefore it is preferable to achieve good chemical uniformity, good uniformity in strain and minimize the number of places for the initiation of cracks.

The size and shape of the forging billet chosen so that after forging, the product has the correct shape and size. The process of selecting the size and shape of the original forging billet thus, to obtain the desired final shape and size known in the art.

Provide for the adjustment of the press and forging dies, step 22. Can be used any suitable forging press, and figure 2 shows schematically the basic forging press 40. Forging press 40 includes a stationary lower table 42, a stationary upper plate 44 and the fixed guide 46, on which rests the top plate 44 relative to the bottom of the table 42. The upper slider 48 is moved along the guide rails 46 up and down by a motor 50 mounted on the upper plate 44. The lower forging the stamp 52 set motionless on the bottom of the table 42. Top forging the stamp 54 sets with the ability to move and attach to the upper slide 48 to move up and down together with the upper slide 48. The workpiece 56 fitted between the upper forging the stamp 54 and lower forging stamp 52. The heater 57 (shown here in the form of an induction heating coil) is placed around the forging dies 52 and 54 and the workpiece 56 in order to maintain the temperature of the forging dies and the workpiece in the selected approximately constant range of the forging temperature during displacement of the tool during the forging, thus supporting the isothermal forging process. During the progress of the tool during the forging may be some minimal temperature fluctuations, but in General, the temperature of the forging dies 52 and 54 and amrabat the excavated part 56 is maintained at approximately a constant level, providing an isothermal forging process.

The workpiece 56 in the initial state represents the forging of the workpiece from forging supersplash Nickel-based. The workpiece 56 fitted between the upper forging the stamp 54 and lower forging stamp 52 and are formed by pressing at a nominal strain rate by moving the top of the forging punch 54 down. Top forging the stamp 54 and lower forging the stamp 52 may be a flat plate or may be executed in relief so that the final forging had this relief, pressed on it. Figure 3 shows an exemplary view of forgings 58 with a relief surface 60, created through the use of relief forging dies.

The forging dies 52 and 54 are made of supersplash Nickel-based for stamps, and superslow Nickel-based for stamps has a yield strength of not lower than the voltage plastic flow forging superslow based on Nickel at a temperature of forging corresponding to the isothermal forging process constituting from about 926,67°up to about 1010,00°With (from about 1700°F to about 1850°F), and at a nominal strain rate in the forging process. The forging dies 52 and 54, preferably made from an alloy with a nominal composition, wt.%: aluminum is from about 5% to about 7%, molybd the n from about 8% to about 15%, tungsten from about 5% to about 15%, magnesium up to about 140 parts per million (preferably 140 parts per million), the rest is Nickel and impurities.

Choose the forging temperature and the rated speed of deformation during forging, the stage 24. Forging superalloys based on Nickel have superplasticity in the range of the corresponding temperature superplasticity and a certain range of strain rates at elevated temperatures. Deformation during forging is desirable to perform in the temperature range of superplasticity in order to avoid critical grain growth during subsequent annealing to ensuring surgestions.

The acceptable range of temperatures and strain rates can be determined by properties of plastic deformation forging supersplash Nickel-based. The following tables I and II, respectively, presents the results of laboratory tests of alloys Rene™ 88DT and M3 to determine the most appropriate to use temperatures to ensure isothermal forging process, and strain rates.

"m"
Table I
The alloy Rene™ 88DT
Temperature, ° (°F)The rate of deformation, with-1Stress, kgf/cm2(kg psi)
982,22 (1800)0,00010,47 (3,03)0,512
982,22 (1800)0,00030,80 (5,15)0,459
982,22 (1800)0,0011,31 (8,44)0,406
982,22 (1800)0,0032,11 (13,62)0,352
982,22 (1800)0,013,05 (19,69)0,299
982,22 (1800)0,034,00 (25,79)0,249
954,44 (1750)0,00010,69 (4,43)0,497
954,44 (1750)0,00031,16 (of 7.48)0,440
954,44 (1750)0,0011,86 (a 12.03)0,385
954,44 (1750)0,0032,89 (18,65)0,329
954,44 (1750)0,014,01 (25,91)0,274
954,44 (1750)0,035,24 (33,83)0,220
926,67 (1700)0,00011,06 (6,85)0,453
926,67 (1700)0,00031,70 (10,95)0,400
926,67 (1700)0,0012,66 (17,14)0,348
926,67 (1700)0,003a 3.87 (24,97)0,295
926,67 (1700)0,015,26 (33,94)0,243
926,67 (1700)0,036,60 (42,56)0,192
Table II
Alloy M3
Temperature, ° (°F)The rate of deformation, with-1Stress, kgf/cm2(kg psi)"m"
982,22 (1800)0,00010,48 (3,07)0,738
982,22 (1800)0,00030,85 (5,49)0,677
982,22 (1800)0,0011,49 (9,59)0,612
982,22 (1800)0,0032,47 (15,94)0,538
982,22 (1800)0,013,66 (23,62)0,458
982,22 (1800)0,03br4.61 (29,76)0,371
954,44 (1750)0,00010,75 (4,87)0,747
954,44 (1750)0,00031,40 (9,02)0,669
954,44 (1750)0,0012,35 (15,14)0,582
954,44 (1750)0,0033,72 (24,00)0,481
954,44 (1750)0,014,96 (31,98)0,367
954,44 (1750)0,035,99 (38,67)0,240
926,67 (1700)0,00011,38 (8,92)0,672
926,67 (1700)0,00032,25 (14,54)0,594
926,67 (1700)0,0013,57 (23,02)0,508
926,67 (1700)0,0035,15 (33,2)0,408
926,67 (1700)0,016,65 (42,89)0,297
926,67 (1700)0,037,40 (47,77)0,174

From this information were selected process parameters to achieve the required value of "m", which would correspond to about 0.3 or more, where "m" is the exponent of superplastic deformation of the material. The forging temperature is, preferably, from about 926,67°up to about 1010,00°With (from about 1700°F to about 1850°F), and more preferably from about 954,44°up to about 9822,22° (okolo° F to about 1800° (F)to reduce the risk of excessive oxidation of the workpiece at higher temperatures. The nominal rate of deformation during forging is not more than about 0.01-1. Under "nominal" rate of deformation in this description to understand the speed defined by the General speed of movement of the upper slide 48, referred to the height of the workpiece 56, measured parallel to the direction of movement of the upper slide 48. Locally in the forging dies 52 and 54 of the real rate of strain may be greater or less than nominal.

Forging billet and forging dies are heated to a temperature corresponding to the isothermal forging process component and from about 926,67°up to about 1010,00°With (from about 1700°F to about 1850°F), step 26.

Forging billet forge, using the forging dies at a temperature corresponding to the isothermal forging process component and from about 926,67°up to about 1010,00°With (from about 1700°F to about 1850°F), and at a nominal strain rate during forging, step 28 using forging equipment, such as a forging press 40, depicted in figure 2.

Stage 26 and heating stage 28 forging, preferably, carried out on the air. Forging in the air can significantly reduce the cost of the forging operation in comparison with forging in the vacuum sludge is in the atmosphere of inert gas, as this was required previously known technology of forging superalloys based on Nickel. The definition of "forging in the air" is not arbitrary, and forging in the air can only be done if the material of the stamp is not excessively oxidized in air at a temperature of forging and resistant to significant loads when the forging temperature. The usual material for the manufacture of stamps, TZM-molybdenum cannot be used at these temperatures in the air because of its excessive oxidation.

After completion of the forging operation according to step 28 forgings 58 is removed from the forging press 40. Forged 58 may be used in the form in which it was forged, or it can then be further processed, step 30. In the preferred case of forgings of superalloys based on Nickel Rene™ 88DT and M3 annealed at the annealing temperature higher than the temperature of dissolution of the primary gamma-phase. The temperature of annealing, which is ultra-high solubility, preferably, is from about 1137,78°up to about 1148,89°With (from about 2080°F to about 2100° (F) for the alloy Rene™ 88DT and from about 1160,00°up to about 1182,22°With (from about 2120°F to about 2160° (F) for alloy M3, for from about 1 hour up to about 2 hours. Other types of subsequent processing stage 30 may include, for example, Stripping, heat treatment, updat the additional processing, processing cutting machines, etc.

Although there is described a specific embodiment of the invention for the purpose of illustration, various modifications and improvements may be made without departure from the essence and scope of the invention. Accordingly, the invention is not limited by anything except the attached claims.

1. Way of forging supersplash, characterized in that it comprises the following steps:

providing a forging billet from supersplash Nickel-based forging;

the provision of the forging press (40)containing the forging dies (52, 54), made of supersplash Nickel-based for stamps with yield strength is not lower than the voltage of the plastic flow supersplash Nickel-based forging when the forging temperature in the range from about 926,67°up to about 1010,00°and at a nominal strain rate in the forging process;

heating of the forging billet and forging dies (52, 54) to the forging temperature, component from about 926,67°up to about 1010,00°C;

forging the forging preform using the forging dies (52, 54) at a temperature of forging comprising from about 926,67°up to about 1010,00°and at a nominal strain rate in the forging process.

2. The method according to claim 1, characterized in that provide CuZn is know the workpiece, made from supersplash Rene™ 88DT, having a nominal composition, wt.%: cobalt 13%, chromium 16%, mo 4%, titanium of 3.7%, aluminium 2.1%, tungsten, 4%, niobium 0,75%, boron 0,015%, zirconium 0,03% carbon 0.03%, iron up to about 0.5%, the rest is Nickel and the minimum amount of impurities.

3. The method according to claim 1, characterized in that provide a forging billet, made of supersplash M3, having a nominal composition, wt.%: cobalt, about 20.6%, chromium about 13,0%aluminum to about 3.4%, titanium of about 3.7 percent, tantalum at about 2.4%, niobium, about 0.9%, tungsten, about 2.1%, molybdenum about 3.8%, carbon about 0.05%boron, about 0,025%, zirconium, about 0.05%, iron up to about 0.5%, the rest is Nickel and the minimum amount of impurities.

4. The method according to claim 1, characterized in that provide a forging billet of compacted powder.

5. The method according to claim 1, characterized in that the stage of the forging press (40) includes the step of providing the forging dies (52, 54) of supersplash, which has a nominal composition, in wt.%: aluminum is from about 5% to about 7%, molybdenum from about 8% to about 15%, tungsten from about 5% to about 15%, magnesium up to about 140 parts per million, the rest being Nickel and impurities.

6. The method according to claim 1, characterized in that the heating of the forging billet and forging dies (52, 54) being carried out in the air.

7. The method according to claim 1, characterized in that the forging forging is gotowke using the forging dies (52, 54) carried out on the air.

8. The method according to claim 1, characterized in that it includes an additional step of selecting a forging temperature, which is from about 954,44°up to about 982,22°C.

9. The method according to claim 1, characterized in that it includes an additional step of selecting a nominal strain rate during forging, the value of which is not higher than about 0.01-1.

10. Way of forging supersplash, characterized in that it comprises the following steps:

providing a forging billet from supersplash Nickel-based for forgings, which are selected from the group consisting of alloy Rene™ 88DT, having a nominal composition, wt.%: cobalt 13%, chromium 16%, mo 4%, titanium of 3.7%, aluminium 2.1%, tungsten, 4%, niobium 0,75%, boron 0,015%, zirconium 0,03% carbon 0.03%, iron up to about 0.5%, the rest is Nickel and the minimum amount of impurities, and M3 alloy having a nominal composition, in wt.%: cobalt, about 20.6%, chromium about 13,0%aluminum to about 3.4%, titanium of about 3.7 percent, tantalum at about 2.4%, niobium, about 0.9%, tungsten, about 2.1%, molybdenum about 3.8%, carbon about 0.05%boron, about 0,025%, zirconium, about 0.05%, iron up to about 0.5%, the rest is Nickel and the minimum number of impurities;

the provision of the forging press (40)containing the forging dies (52, 54), made of supersplash Nickel-based for stamps;

heating of the forging billet and kovochnoj (52, 54) to the forging temperature, component from about 926,67°up to about 1010,00°on the air; and

forging the forging preform using the forging dies (52, 54) at a temperature of forging comprising from about 926,67°up to about 1010,00°With, in the air.

11. The method according to claim 10, characterized in that provide a forging billet of compacted powder.

12. The method according to claim 10, characterized in that the stage of the forging press (40) includes the step of providing the forging dies (52, 54) of supersplash, having a nominal composition, wt.%: aluminum is from about 5% to about 7%, molybdenum from about 8% to about 15%, tungsten from about 5% to about 15%, magnesium up to about 140 parts per million, the rest being Nickel and impurities.

13. The method according to claim 10, characterized in that it includes an additional step of selecting a forging temperature, which is from about 954,44°up to about 982,22°C.

14. The method according to claim 10, characterized in that it includes an additional step of selecting a nominal strain rate during forging, the value of which is not higher than about 0.01-1and forging the forging preform is carried out at a nominal strain rate.

15. Way of forging supersplash, characterized in that it comprises the following steps:

providing a forging billet of compacted powder supersplash Nickel-base for p is cowok, which are selected from the group consisting of alloy Rene™ 88DT, having a nominal composition, wt.%: cobalt 13%, chromium 16%, mo 4%, titanium of 3.7%, aluminium 2.1%, tungsten, 4%, niobium 0,75%, boron 0,015%, zirconium 0,03% carbon 0.03%, iron up to about 0.5%, the rest is Nickel and the minimum amount of impurities, and M3 alloy having a nominal composition, in wt.%: cobalt, about 20.6%, chromium about 13,0%aluminum to about 3.4%, titanium of about 3.7 percent, tantalum at about 2.4%, niobium, about 0.9%, tungsten, about 2.1%, molybdenum about 3.8%, carbon about 0.05%boron, about 0,025%, zirconium, about 0.05%, iron up to about 0.5%, the rest is Nickel and the minimum number of impurities;

the provision of the forging press (40)containing the forging dies (52, 54), made of supersplash Nickel-base for stamping, having a nominal composition, in wt.%: aluminum is from about 5% to about 7%, molybdenum from about 8% to about 15%, tungsten from about 5% to about 15%, magnesium up to about 140 parts per million, the rest being Nickel and impurities;

heating of the forging billet and forging dies (52, 54) to the forging temperature, component from about 926,67°up to about 1010,00°C, air;

forging the forging preform using the forging dies (52, 54) at a temperature of forging comprising from about 926,67°up to about 982,22°S, at a nominal strain rate of no higher than about 0.01-1air.



 

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EFFECT: enhanced reliability of articles.

1 dwg, 1 tbl

FIELD: metallurgy; production of semi-finished products from high-temperature high-alloy wrought nickel-based alloys for manufacture of disks for gas-turbine engines working at temperatures higher than 600°C.

SUBSTANCE: proposed method includes preliminary deformation of blank by upsetting by two or more times, final deformation and heat treatment; first upsetting is performed in closed container; during next upsetting, technological metal ring at temperature of (0.02-0.5)Tdef. is placed on blank heated to deformation temperature Tdef. and free upsetting is performed in stamp tool heated to deformation temperature. Geometric parameters of ring are selected from given relationships. Preliminary deformation of blank is performed at intermediate annealing. Height-to-diameter ratio of starting blanks is no less than 3:1. Proposed method ensures forming of homogeneous fine-grain structure over entire volume of blank due to work in end zones.

EFFECT: simplified procedure; reduced labor consumption.

4 cl, 1 tbl, 5 ex

FIELD: manufacture of cylindrical articles, mainly of magnetic and electric screens, possibly in aircraft instrument making and machine engineering.

SUBSTANCE: method comprises steps of molding sheet blank and subjecting it to heat treatment. After molding blank assembling and welding processes are performed. Blank is subjected to heat treatment onto mandrel at simultaneously sizing product due to plastic deformation caused by interference between mandrel and article at heating process due to their different heat expansion coefficients. Preliminarily insulating layer of talc emulsion in fuel oil is applied on surface of mandrel. Said emulsion contains: talc, 1 mass p; fuel oil, 5 mass p. Finely divided talc fraction 1 - 15 micrometers is used for preparing such emulsion. Mandrel is subjected to heat treatment in vacuum furnace for 6 h at temperature 1150°C.

EFFECT: possibility for producing articles of predetermined size and desired magnetic properties.

1 ex

FIELD: medicine materials.

SUBSTANCE: invention relates to biocompatible seam and mesh materials having high adaptability to body tissues. Claimed method includes multiple drawing of heated drawpiece through sequence of nozzles, wherein the last drawing step is carried out without heating at deformation coefficient of 6-10 %.

EFFECT: nickelide-titanium filament with improved implantability.

5 dwg, 1 ex

FIELD: metallurgy; production of reticular nickel structures from metallized foamed plastics used as bases in manufacture of storage batteries, filtering materials or catalyst carriers.

SUBSTANCE: proposed method includes heating of starting nickel-plated polymer for removal of polymer substrate and decarbonization of nickel for obtaining nickel structure followed by annealing of nickel structure. Thermochemical treatment of nickel-plated polymer structures is performed in two zones at different atmospheres. Heating of starting nickel-plated polymer in first zone is performed for removal of polymer substrate and decarbonization of nickel at obtaining nickel structure in oxidizing/reducing atmosphere at temperature of 900-1300°C for at least 3 s. In second zone, nickel structure is subjected to annealing in reducing atmosphere at temperature of 800-1100°C.

EFFECT: possibility of production of foamed nickel of preset chemical composition and mechanical properties.

3 cl, 3 dwg, 3 tbl, 10 ex

FIELD: nonferrous metallurgy; production of the sheet semi-products made out of the hardly-deformed nickel alloys.

SUBSTANCE: the invention is pertaining to the field of nonferrous metallurgy, in particular, to production of the sheet semiproducts made out of the hardly-deformed alloy based on nickel of Inconel 718 type, which may be used at manufacture of hollow products by molding and a diffusion welding in conditions of superplasticity. The invention offers the method of production of such sheet semiproducts. The method includes: production of a casting after a smelt, deformation working of the casting by rolling with production of a blank part and its final rolling with production of the sheet semiproduct. The deformation working of the casting is exercised by rolling in the single-phase field of the alloy, and the final rolling is conducted within the temperature range of 975-825°C with the deformation speed of 10-4 - 101 s-1, with a total degree of the deformation of no less than 50 % at least for two runs to provide the process of a dynamic recrystallization. The technical result of the invention is expansion of production capabilities at manufacture of the sheet semiproducts made out of the hardly-deformed alloy based on nickel of Inconel 718 type at simultaneous improvement in quality due to production of the homogeneous fine-grain structure with the grains sizes of up to 1 micron and less providing expansion of the temperature-speed interval of superplasticity for the subsequent manufacture from it a product, as well as the products of responsible designation, which need the superplastic formation.

EFFECT: the invention ensures expansion of production capabilities at manufacture of the sheet semiproducts made out of hardly-deformed alloy based on nickel of Inconel 718 type, improvement of their quality, expansion of the temperature-speed range of superplasticity to produce the products and special purpose products requiring the superplastic formation.

15 cl, 3 dwg, 2 tbl, 6 ex

FIELD: plastic working of metals, possibly manufacture of internal combustion connecting rod by closed forming.

SUBSTANCE: method comprises steps of preparing blank with two thickened end portions and one thickened portion in mean zone; deforming prepared blank in cavity of die set while making openings in thickened end portions at displacing blank metal; shaping mean portion of connecting rod and after-forming its heads. Volume of thickened portion in mean zone of blank exceeds volume of mean portion of article by value equal to half of total metal volume of blank displaced at making said openings. Gravity center of thickened portion of mean zone is spaced from axes of openings by distance inversely proportional to metal volumes displaced at forming respective openings.

EFFECT: improved quality of article.

2 dwg, 1 ex

FIELD: plastic working of metals, possibly manufacture of axles of rolling stock by forming and forging.

SUBSTANCE: method comprises steps of deforming initial square cross section blank by forging till intermediate designed size by knocking off faces in order to form semi-finished cylindrical product of forged piece; then feeding semi-finished product of forged piece to hammer die set. Die set is detachable one, it includes two parts with cavities restricting open finish impression without flash grooves. Profile of finish impression of die set corresponds to final size of forged piece. Two compensation openings are arranged in ends of impression. In die set hot die forging of semi-finished product driven to rotation by means of manipulator is realized. Then excess metal on ends is trimmed, forged piece is straightened and cooled.

EFFECT: enhanced quality of forged piece due to providing optimal deforming schedule, lowered power and metal consumption.

4 cl, 5 dwg

FIELD: plastic working of metals, namely forging production, manufacture of forged pieces of ring-like cone gear wheels with diameter 638 mm and with wide massive rim.

SUBSTANCE: method comprises steps of preliminarily upsetting initial blank with diameter 250 mm and length 335 mm; then subjecting upset blank to non-complete open broaching and its further die forging. All operations are realized in the same die set. Preliminary upsetting is performed on flat striker with diameter 350 mm till achieving diameter of upset blank equal to said value. Striker is arranged in central portion of die set impression before broaching and after broaching it is removed. Non-complete open broaching of upset blank is realized by means of detachable cone broach with mounting land having diameter 270 mm.

EFFECT: improved quality of produced forged pieces.

8 dwg, 1 ex

FIELD: plastic working of metals, possibly manufacture of hollow parts such as sleeve type parts with central protrusion on inner surface of bottom, namely artillery shell cases.

SUBSTANCE: method comprises steps of backward pressing out of initial blank and shaping bottom portion having protrusion on inner surface during several transitions. After backward pressing out transition, blank is drawn at several transitions. Bottom portion with central protrusion is formed during two transitions, namely: at transition for preliminarily shaping central protrusion and at transition for finally forming bottom portion. Preliminary forming is realized during transition of backward pressing out of initial blank by means of inner punch with recess. Final forming is realized by means of inner punch with recess and outer punch with protrusion.

EFFECT: improved quality of articles.

5 dwg

FIELD: plastic metal working, namely processes of die forging, possibly for manufacturing stepped hollow shafts.

SUBSTANCE: method comprises steps of calibrating blank prepared by chopping; forming in blank upper and lower cavities, bottom portion with cylindrical near-bottom part and local outer bulged zone. Upper cavity is formed at first pressing out stage. At second stage of pressing out lower cavity, bottom portion and local outer bulged zone are formed simultaneously while blank is centered by punch along it upper cavity and in die along cylindrical near-bottom part.

EFFECT: enlarged manufacturing possibilities of method.

6 dwg

FIELD: plastic working of metals, possibly manufacture of forged pieces with central opening.

SUBSTANCE: method comprises steps of upsetting heated initial blank; forming semi-finished product having bridge in zone of one end of its inner portion in die set without forming burr; remaining part of end surface having no contact with tool; then performing final forming, mainly in one half of open die set at displacing outer burr and with possibility of displacing inner burr; removing bridge and trimming burrs.

EFFECT: lowered metal and energy consumption at process.

20 cl, 6 dwg, 1 ex

FIELD: plastic working of metals, possibly forming forged pieces, for example rings, gear wheels, flanges.

SUBSTANCE: initial blank is heated, preliminarily shaped, finally formed and trimmed. At final forming open die set is used; said die set has gap between its upper and lower halves. Said gap is arranged in zone of forging that is formed last. Dimensions of die set are no more than respective dimensions of forging in order to prevent deforming of displaced excess of metal.

EFFECT: lowered deforming efforts, decreased metal consumption.

11 cl, 2 dwg, 1 ex

FIELD: metal working, possibly manufacture of flanged articles and articles without flanges of different alloys.

SUBSTANCE: method comprises steps of heating blank and deforming it in die set; sustaining relation of blank temperature to that of die set in range 0.7 - 7.4. Blank is heated in predetermined temperature range depending upon blank material. Said temperature range may be found from ductility diagram and(or) yield curves and(or) from blank material recrystallization diagrams.

EFFECT: enhanced factor of using metal, improved quality of articles, lowered labor consumption of forging and subsequent working of blank.

6 cl, 2 dwg, 2 ex

FIELD: plastic working of metals, possibly operations for finish working of forgings of double-end box nut wrenches.

SUBSTANCE: die set includes upper and lower plates with guiding columns, punch for punching operation mounted on upper plate, stripper, lower die for punching, half-open trimming lower die and trimming punch. Trimming lower die is mounted on upper plate; it has cutting edge and cavity arranged behind collar of cutting edge and designed for freely placing forging of nut wrench. Trimming punch is mounted on lower plate and it has embracing supporting surface for fixing forging at trimming and straightening operations.

EFFECT: enhanced quality of forging.

9 dwg, 1 ex

The invention relates to the processing of metals by pressure and can be used to obtain the forging of ingots and pre deformirovannykh billets for forging complexes

FIELD: plastic working of metals, possibly operations for finish working of forgings of double-end box nut wrenches.

SUBSTANCE: die set includes upper and lower plates with guiding columns, punch for punching operation mounted on upper plate, stripper, lower die for punching, half-open trimming lower die and trimming punch. Trimming lower die is mounted on upper plate; it has cutting edge and cavity arranged behind collar of cutting edge and designed for freely placing forging of nut wrench. Trimming punch is mounted on lower plate and it has embracing supporting surface for fixing forging at trimming and straightening operations.

EFFECT: enhanced quality of forging.

9 dwg, 1 ex

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