Brick made out of a titanium alloy and a method of its production

FIELD: non-ferrous metallurgy; methods of titanium alloy bricks production.

SUBSTANCE: the invention is pertaining to the field of non-ferrous metallurgy, in particular, to the brick made out of α+β titanium alloy and to a method of its manufacture. The offered brick consists of the following components (in mass %): aluminum - 4-5, vanadium - 2.5-3.5, iron - 1.5-2.5, molybdenum - 1.5-2.5, titanium - the rest. At that the alloy out of which the brick is manufactured, contains - 10-90 volumetric % of the primary α-phase. The average grain size of the primary α-phase makes 10 microns or less in a cross-section plain parallel to the brick rolling direction. Elongation of grain of the primary α -phase is the four-fold or less. The offered method of manufacture of the given brick includes a stage of a hot rolling. At that before the stage of the hot rolling conduct a stage of the alloy heating at the surfaces temperature (Tβ-150)- Tβ°C. During realization of the stage of the hot rolling the surface temperature is kept within the range of (Tβ-300)-( Tβ -50)°C, and the final surface temperature, that is a surface temperature directly after the last rolling, makes (Tβ-300)-( Tβ-100)°C, where Tβ is a temperature of α/β-transition. The technical result of the invention is formation of a brick out of the high-strength titanium alloy having a super pliability, excellent fatigue characteristics and moldability.

EFFECT: the invention ensures production of a brick out of the high-strength titanium alloy having a super pliability, excellent fatigue characteristics and moldability.

7 cl, 7 dwg, 21 tbl, 2 ex

 

The technical field

The present invention concerns a piece of titanium alloy, which has excellent ductility, fatigue resistance and the ability to molding, in particular, the invention concerns a piece of α+β-titanium alloy and method of its manufacture.

The level of technology

Due to high strength, light weight and excellent corrosion resistance of titanium alloys are used as structural material in areas such as chemical process plants, power generators, aircraft, and the like. Due to the high strength and fairly good ability to molding among all alloys are widely used titanium alloy type α+β.

Products made from titanium alloys, take various forms such as sheet, plate, bar and so on. The bar can be used by itself or it can forge or otherwise to give him a complex shape, such as some fastening element is threaded. Thus, it is required that the bar had a great ability to molding, as well as excellent ductility and characteristics of fatigue resistance.

Figure 1 shows a typical method of manufacture of the bar.

The ingot obtained by melting form in the workpiece, which is used in the AC is este base material for hot rolling. As shown in figa and FIGU, the material is subjected to hot rolling using a reversing rolling mill or tandem rolling mills, and it turns out the bar. Before rolling the bar is heated in the heating furnace. If necessary, the material is subjected to an intermediate re-heating for hot rolling for adjusting the temperature required for the subsequent hot rolling.

As for the piece of titanium alloy, especially of the bar of the α+β-titanium alloy, the temperature of the workpiece rises during hot rolling due to adiabatic heating, which creates interference stable hot rolling and fabrication of the bar from titanium alloy with excellent ductility and excellent fatigue resistance and suitability for use. For example, if the temperature of the workpiece rises to a temperature of α/β-transition or above, then the final block, the last hot rolling, has β microstructure consisting mainly of pointed and phases, thus not obtained excellent plasticity and characteristics of fatigue resistance. In addition, even for the alloy Ti-6Al-4V with high temperature α/β-transition, an increase in temperature during the hot rolling, due to adiabatic heating, enhances the growth of the Eren, despite the fact that the temperature during the hot rolling is hardly higher than the temperature of α/βtransition and, thus, fails excellent plasticity characteristics of fatigue resistance and the ability to molding.

To solve the increase in temperature due to adiabatic heating during hot rolling, the patent JP-A-59-82101 (referred to herein, the term "JP-A" means "untested publication of Japanese patent application") describes a method of rolling, in which the reduction ratio of the cross-sectional area of the workpiece is set at 40% or less for each rolling in α region or α+β area. Patent JP-A-58-25465 describes the way in which the workpiece during hot rolling is cooled by water that is being done to curb the increase in temperature due to adiabatic heating. Moreover, article 1 of the Hot rolling of the bar of Ti-6Al-4V in rolling mills continuous action (Titanium'92 Science and Technology)" describes what speed hot rolling to reduce the lower limit of the ability to work on the mill to keep the adiabatic warming up.

The methods described in JP-A-59-82101 and JP-A-58-25465, however, cannot be applied for the production of the bar from titanium alloy, which has excellent ductility, excellent Hara is the characteristics of fatigue resistance and the ability to molding.

Even if the reduction ratio of the cross-sectional area per rolling is 40% or less, according to the method of patent JP-A-59-82101, it is not enough to deter the adiabatic warming up for some types of titanium alloys. The method of the patent JP-A-58-25465 also causes deterioration of the characteristics due to hydrogen absorption, which occurs when the cooling water. There are also difficulties in precise temperature control due to deformation caused by rapid cooling.

The method described in article 1 refers to the alloy Ti-6Al-4V. As described below, this method is not necessarily applicable to alloys, which are characterized by a large adiabatic heating and, thus, should be assigned to hot rolling at low temperatures, resulting in poor ductility, poor characteristics of fatigue resistance and the ability to molding.

Figure 3 shows the relationship between temperature and time of hot rolling for the alloy Ti-6Al-4V and alloy Ti-4.5Al-3V-2Fe-2Mo.

The heating temperature was 950°for the alloy Ti-6Al-4V and 850°for the alloy Ti-4.5Al-3V-2Fe-2Mo. The alloy Ti-4.5Al-3V-2Fe-2Mo has a temperature of α/β-the transition to 100°C lower than the temperature of α/β-transition of the alloy Ti-6Al-4V, so that the temperature of heating was reduced by this difference, therefore, as temperature Razov the Eva was chosen value 850° C. Rolling was performed using a reversible rolling mill or tandem rolling mills, it was chosen the same conditions of speed rolling, the reduction ratio and the same schedule of rolling for both alloys. The rolling speed on reversing rolling mill was 2.7 m/s, and the rolling speed on the tandem rolling mills was 2.25 m/s for the final rolling when the rolling speed is maximum for both alloys. The rolling speed is lower than the rolling speed in Article 1 (6 m/s). The reduction ratio of the cross-sectional area per rolling was selected not more than 26% for both alloys.

In the case of alloy Ti-6Al-4V rolling was carried out at considerably lower temperatures than 1000°With equal temperature α/β-transition of the alloy, thus acquired a suitable structure. However, in the case of alloy Ti-4.5Al-3V-2Fe-2Mo, even if the temperature of heating was reduced to a value below the temperature α/β-transition, the low-temperature rolling would increase the deformation resistance and the increase in adiabatic heating, so the temperature would increase to a value higher than the temperature of α/βtransition and, thus, would not have achieved a suitable microstructure. The result is excellent ductility and excellent feature is the Tiki of fatigue resistance and the ability to molding will not be received. To achieve results you must take into account the conditions of rolling, such as temperature rolling, the shrinkage ratio and the time between prokatami, as it is necessary to consider the rolling speed.

Description of the invention

The present of the invention is to create a piece of high-strength titanium alloy having excellent ductility, excellent fatigue resistance and the ability to molding, and also to create a method of manufacturing the described bar.

The problem is solved in that the bar (α+β) titanium alloy consisting of the following components in wt.%: aluminum - 4-5, vanadium - 2,5-3 5 - iron 1.5 to 2.5, molybdenum and 1.5 - 2.5, titanium - rest, according to the invention the specified alloy contains 10-90 vol % primary α phase, the average grain size of primary α phase is 10 μm or less in a transverse plane parallel to the direction of rolling of the bar, the elongation of the primary grain α phase is four or less.

Preferably, when the volume fraction of primary α phase ranges from 50 to 80 volume %, and the average grain size of primary α phase equal to 6 μm or less. The problem is solved also by the fact that in the method of manufacturing bar (α+β) titanium alloy, comprising the step of hot rolling, while JV is AB contains the following components, in wt.%: aluminum - 4-5, vanadium - 2,5-3,5 - iron 1.5 to 2.5, molybdenum and 1.5 - 2.5, titanium - rest, according to the invention, before the step of hot rolling carry out the step of heating the alloy at the surface temperature (Tβ - 150) - Tβ°Since, during the step of hot rolling the surface temperature of the support in the range (Tβ - 300) - (Tβ - 50)°and the final surface temperature, that is, the surface temperature immediately after the last rolling, is Tβ - 300) - (Tβ - 100)°where Tβ temperature α/β-transition.

Recommended hot rolling with a shrinkage ratio of 40% or less per rolling.

Can hot rolling conducted using the reversing rolling mill, the rolling speed should be 6 m/s or less.

Alternatively, hot rolling conducted using a tandem rolling mill, the rolling speed should be 1.5 m/s or less.

Brief description of drawings

Figure 1 shows a typical method of manufacture of the bar.

Figure 2 shows the process of hot rolling of the bar.

Figure 3 shows the relationship between temperature and time for rolling hot-rolled alloy Ti-6Al-4V and alloy Ti-4.5Al-3V-2Fe-2Mo.

Figure 4 shows a graph of the relationship between the average grain size of primary α F. the gases and the total elongation this dependence is constructed by a tensile test at a high temperature.

Figure 5 shows the relationship between the average grain size of primary α phase and fatigue strength after 108cycles, this relationship was observed when tested on the fatigue resistance.

Figure 6 shows a graph of temperature change from time to time on the surface and in the Central part of the bar.

7 shows the relationship between the cross-sectional area and temperature difference on the surface and in the Central part.

Examples of carrying out the invention

The authors of the present invention studied the microstructure of the bar from titanium alloy α+β type in order to provide excellent flexibility, excellent fatigue resistance and the ability to molding, and found the following.

The titanium alloy α+β contains primary α phase and converted α phase. However, if the alloy contains a very large volume fraction α phase, which has a hexagonal closely Packed structure with a small system shift, or contains a very large volume fraction transformed β phase containing needle α phase, the ability to form and strength deteriorate. Therefore, the volume fraction of primary α phase set in INTA the shaft 10 to 90%. If at the stage of heating before hot rolling volume fraction α phase I β phase equal or close to each other, the ability to molding is increased, so that the volume fraction of primary α phase preferably set in the range 50-80%.

Figure 4 shows a graph of the relationship between the average grain size of primary α phase and total elongation, this dependence is constructed by a tensile test at a high temperature.

When the average grain size of primary α phase exceeds 10 μm, the total elongation measured during the tensile test at high temperature decreases rapidly and, consequently, the ability to molding is reduced.

Figure 5 shows the relationship between the average grain size of primary α phase and fatigue strength after 108cycles, this dependence was observed when tested on the fatigue resistance.

If the average grain size of primary α phase exceeds 10 μm, the fatigue strength decreases. If the average grain size of primary α phase becomes less than 6 μm, there is a higher fatigue strength.

In the forging of the bar is obtained a rough surface on the freely deformable surface, which is not in contact with the mold shape, roughness is obtained from C the form of grains or because of the relationship of the height of the grains to their width. Generally speaking, the grain of the bar tend to extend in the direction of rolling.

In particular, for the case of forming a draft of elongated grains appear on the side of the bar, which is freely deformable surface. Therefore, it is necessary to avoid excessive increase of the height of the grain to its width during forging and, more specifically, it is necessary to adjust the ratio of the height of the grain to its width so that it does not exceed the value of 4 for grains primary α phase in the transverse plane, parallel to the direction of rolling of the bar. The above is to ensure that after forging of the bar could not rough surfaces.

On the basis of the above data block of high-strength titanium alloy having excellent formability and excellent fatigue resistance and the ability to molding, is obtained when the volume fraction of primary α phase varies in the range of 10-90%, preferably 50-80%, average grain size in the primary α phase is 10 μm or less, better than 6 μm or less and, in addition, the ratio of the height of the grain to its width for primary α phase is 4 or less.

The bar from titanium alloy α+β type having the above-described microstructure should mainly consist of 4-5% Al, 2.5-3.5% V, 1.5 to 2.5% Fe, 1.5 to 2.5% Mo by weight, and the rest of the composition is yet Ti. Why are the limits of the content of each element is described below.

Al

Aluminum is an essential element for stabilization α phase and to increase strength. If the Al content is below 4%, it may not be fully achieved high strength. If the aluminum content exceeds 5%, reduced plasticity.

V

Vanadium is an element that stabilizes β phase and contribute to an increase in strength. If the vanadium content is below 2.5%, may not be fully achieved high strength and β phase becomes unstable. If the vanadium content exceeds 3.5%, the range of working temperatures become lower, which is due to temperature reduction α/β-transition, and increase costs.

Mo

Molybdenum is an element that stabilizes β phase and contribute to an increase in strength. If the molybdenum content is below 1.5%, may not be fully achieved high strength and β phase becomes unstable. If the molybdenum content exceeds 2.5%, the range of working temperatures become lower, which is due to temperature reduction α/β-transition, and increase costs.

Fe

Iron is an element that stabilizes β phase and contribute to an increase in strength. Iron rapidly diffuses that appreciation is no ability to molding. However, if the iron content is less than 1.5%, may not be fully achieved high strength and β phase becomes unstable, resulting in failure in obtaining an excellent ability to molding. If the iron content exceeds 2.5%, the range of working temperatures become lower, which is due to temperature reduction α/βtransition and separation causes deterioration of the characteristics.

The bar from titanium alloy α+β type according to the present invention can be produced by hot rolling of titanium alloy α+β type, the composition of which is described above, while governed by the following conditions: temperature of heating, the temperature range of the rolling coefficient of elongation, the rolling speed, the time between prokatami and other parameters. These terms regulate with the aim of controlling the growth temperature due to adiabatic heating, namely, prevent the surface temperature of the alloy was higher than the temperature α/β-transition. For example, the method comprises the following steps: heating the titanium alloy α+β type having a temperature of α/βtransition equal to Tβ °so that the surface temperature varies in the interval (Tβ - 150) - Tβ°C; and hot rolling the heated α+β-titanium alloy such that the surface is I temperature in the time of hot rolling ranges in the interval (Tβ - 300 and Tβ - 50)°S, and such that the final surface temperature above varies in the interval (Tβ - 300) - (Tβ-100)°C.

The reason why the surface prior to hot rolling is heated to a temperature in the range of (Tβ - 150) to Tβ°C, is the following. If the surface temperature prior to hot rolling below (Tβ - 150)°s, the temperature decrease during the final stage of the rolling becomes sufficient to increase susceptibility to cracking and increase the resistance to deformation. And if the surface temperature prior to hot rolling exceeds Tβ°C, the microstructure of the bar becomes β microstructure consisting mainly of needle α phases, which degrades the ductility and the ability to molding. The reason why the surface temperature during the hot rolling should be in the range of from (Tβ - 300) to (Tβ - 50)°C, is the following. If the surface temperature during the hot rolling below (Tβ - 300)°With the ability to hot molding deteriorates, which causes problems such as cracking. And if the surface temperature during the hot rolling exceeds (Tβ - 50)°With the increase of temperature resulting from adiabatic heating, causes the formation to the total grain and needle-like phase. The reason that the final surface temperature immediately after the last rolling should be in the range (Tβ - 300) - (Tβ - 100)°C, is the following. If the final temperature of the surface below (Tβ-300)°With, it increases the tendency to cracking and increased resistance to deformation. And if the final surface temperature exceeds (Tβ - 100)°then increase the grain size.

Hot rolling is carried out by several pochatok. To prevent temperature increase that occurs due to adiabatic heating, it is preferable that the shrinkage ratio was not more than 40% per rolling.

When hot rolling is carried out by reversing rolling mill, it is preferable to limit the rolling speed value not more than 6 m/C. This is done to prevent the temperature increase that occurs due to adiabatic heating. When hot rolling is performed on a tandem rolling mills, it is preferable to limit the rolling speed value not more than 1.5 m/s

Since the surface of the workpiece alloy is cooled after each rolling, before carrying out the subsequent rolling there has been some drop in temperature on the surface of the alloy, even if the temperature rises due to adiabatic, rathre is at. However, as shown in Fig.6, when the workpiece diameter of the alloy makes a significant value (in this case, 106 mm in diameter), then drop the temperature in the Central part of the billet of the alloy is small, so that there is a big temperature difference between the surface and the Central part of the billet of the alloy. When the temperature drop in the center slightly, the alloy is subjected to further rolling to a larger temperature drop in the Central part, which further increases the temperature due to adiabatic heating. If this phenomenon persists, the Central portion is subjected to hot rolling at a temperature higher than the original temperature. Therefore, the Central part of the workpiece with a large diameter is necessary between prokatami to cool a sufficient amount of time.

By the way, the authors of the present invention conducted a detailed study of the temperature difference between the surface and the Central part and got the results described below. As shown in Fig.7, the temperature difference increases significantly when the cross-sectional area of the billet of the alloy from 3500 mm2and above, which shows the cross-section plane perpendicular to the direction of rolling. When the workpiece is composed of an alloy having a large sectional area, experience the tsya hot rolling, after which the cross-sectional area is equal to S mm2after temporary interruption in 0,167·S1/2seconds or more before carrying out the subsequent rolling will be a small temperature difference, and this will be useful for the production of bar, having homogeneous characteristics.

According to the method of manufacture in accordance with the present invention when carrying out hot rolling, the surface temperature of the alloy is maintained equal to the temperature α/β-transition or below and, thus, there is a possibility of reducing the surface temperature to a value that is outside the desired temperature range of the hot rolling time-dependent between prokatami and the diameter of the billet of the alloy. In this case, you can heat the alloy using a device with a high-frequency heating element or the like.

Example 1

Materials, the cross-sectional area which is 125 mm2manufactured by cutting the main billet alloy A01 (which corresponds to the present invention) and the main billet alloy A02 (the composition of which is not in conformity with this invention). Both alloy are α+β-titanium alloys and have the appropriate chemical composition, shown in Table 1. The materials are subjected to the hot rolling using template rolling mill under appropriate conditions (V to 18), which are presented in table 2. After rolling out the bars, the diameter of which is respectively 20 mm and 50 mm intervals between prokatami presented in Table 2, mean time between prokatami in 0,167·S1/2or more seconds for all pochatok for any conditions of rolling and X represents the time between prokatami less than 0,167·S1/2. Table with numbers from 3 to 20 contain: area S of the cross section of the alloy, the reduction ratio, 0,167·S1/2the time between prokatami, surface temperature and rolling speed of each rolling for each condition rolling. R in the tables indicates a reversible rolling mill, and T means a tandem rolling mills.

Made the bars are subjected to annealing at a temperature in the range of 700-720°C. To determine the yield strength (0.2% PT), ultimate tensile strength (PR), elongation (UD) and reduction of area (UE) was carried out tensile test. In addition, a test was conducted on the fatigue strength without notch (assuming Kt=1) and test the fatigue strength with notch (assuming Kt=3), which was conducted to determine the fatigue strength.

In addition, a study of the microstructure in the center of the bar and in place, separated by a quarter in diameter (1/4 L), with the aim to define what elite the grain size of primary α phase volume fraction of the grains and the ratio of the height of the grains to their width in the transverse plane, parallel to the direction of rolling.

The results are presented in Table 21. The columns of the microstructure in the table that do not bear grain size, mean that there is only β microstructure consisting mainly of needle α phases and that equiaxial primary α phase are not observed.

When the temperature of the heating surface was less (Tβ - 150)°C, the surface temperature of the alloy was extremely low and the pressure rolling becomes too large for rolling. When the heating temperature exceeded Tβ°C, the surface temperature of the alloy becomes too high, even if the time between prokatami were within the limits set forth in the present invention, which can be seen for rolling W and B11, thus the surface temperature exceeded Tβ°that was due to adiabatic heating, the formed β microstructure consisting mainly of needle α phase in the center of the bar, therefore, deteriorated ductility and characteristics fatigue resistance.

When the end-surface temperature was lower (Tβ - 300)°C, the temperature of the alloy becomes too low, which would worsen the ability of the Sabbath. ü for forming and could cause cracks during hot rolling. When the end surface temperature is exceeded (Tβ - 100)°With, you could not get a good microstructure, which would worsen the plasticity and characteristics of fatigue resistance, as in the cases when the conditions V, W and W.

When the surface temperature during hot rolling was lower (Tβ - 300)°With surface temperature was too low and formed cracks. When the surface temperature is exceeded (Tβ - 50)°after hot rolling in the centre and at the point1/4diameter was observed β microstructure consisting mainly of needle α phase, which degrades the ductility and characteristics of fatigue resistance.

When the reduction ratio for each rolling exceeded 40%, increased adiabatic heating, and the temperature of the alloy was higher than Tβ°and it was impossible to get a good microstructure.

In the case of rolling 14, which was used reversible rolling mill and rolled the rolling speed above 6 m/s, or in the case of rolling a 15, which was used tandem rolling mills and was chosen the rolling speed is above 1.5 m/s, adiabatic warming has become so large that the surface temperature exceeded Tβ°thus was not a good microstructure.

When the time between prokatami o who came for the range, characteristic of the present invention, the increase in surface temperature caused by adiabatic heating, exceeded the decrease in temperature caused by air cooling, thus the surface temperature exceeded Tβ°and it was impossible to get a good microstructure.

For bars of alloy A01, which have a chemical composition according to the present invention and manufactured under conditions of rolling V, W, B08, B09, B16, B17 and B18, there is a homogeneous microstructure, the grain size of primary α phase is 10 μm or less, for these bars characterized by excellent flexibility and resistance to fatigue. That is an additional excellent formability and excellent fatigue resistance can be obtained, giving 15% and greater elongation of 40% or greater reduction in the area of 500 MPa or greater fatigue strength without notch and 200 MPa fatigue strength (Kt=3) with a cut. Moreover, for a piece of α+β-titanium alloy, whose volume fraction of primary α phase is 50-80% and the average grain size of primary α phase is 6 μm or less and manufactured under conditions of rolling V, W, B08 and B09, can be obtained even better plasticity and characteristics of fatigue resistance at 20% or more elongation, 50% or more of umensheniya, 550 MPa or greater fatigue strength without notch and 200 MPa fatigue voltage (Kt=3) with the cut.

On the one hand, for bars made of A02 and having a chemical composition that does not match described in the present invention, under conditions of rolling B10 and B12, were not achieved satisfactory plasticity and characteristics of fatigue resistance, as the grain size of primary α phase exceeded 10 μm, although the adiabatic heating restrained (due to the fact that conditions of rolling corresponded to the range of the present invention).

Example 2

Cylindrical specimens with 8 mm diameter and 12 mm height were cut from the Central part (in the radial direction) of the bars produced in example 1 under the conditions of rolling from V to B18, respectively. The samples were heated up to 800°and were compressed up to 70%. After compression, each sample was inspected for cracks or unevenness on its surface. This was done to assess the hot ductility.

The results are shown in Table 21.

As for bars, made under conditions of rolling V, W, B08, B09, B16 and B18, which are in the framework of the present invention showed no cracks or rough edges and was achieved a good hot ductility.

On the other hand, bars, made under conditions of hire and B10 and B12, in which the grain size of primary α phase exceeds 10 μm, appeared roughness on the surface, although cracks were not formed. As for bars, having only α the phase in the center and the point1/4diameter, made under conditions of rolling V, W, V, W, V, B14, B15, it appeared as cracks and roughness. Moreover, the roughness of the surface also appears to bars, made under the condition of rolling B14, in which grains in a transverse plane parallel to the direction of rolling, the ratio of the height of the grain to its width exceeds 4, and the grain size of primary α phase and its volume fraction is in the range specified in the present invention, the rough surface was also observed.

Table 1
AlloyAlVFeMoAboutNNthe pace. α/β-transition
A014.73.12.11.90.10.0010.0050.0017900°
A026.14.10.2-0.20.010.006 0.00161000°

The numbers are in percent by weight

Table 3
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7790R
21100015.417.5252.7796R
3950013.616.3252.7801R
4800015.814.9252.7803R
5650018.813.525 2.7811R
6520020.012.0252.7801R
7415020.210.8252.7779R
8330020.59.6252.7761R
9245025.88.3252.7738R
10185024.57.2252.7719R
11145021.66.450.350721T
12115020.75.750.466732T
1390021.75.050.581739T
1470022.24.450.733745T
1555021.43.95 0.871741T
1642023.63.450.982730T
1732023.81.125714T

Table 4
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7929R
21100015.417.5252.7925R
3950013.616.3252.7919R
4/td> 800015.814.9252.7913R
5650018.813.5252.7911R
6520020.012.0252.7900R
7415020.210.8252.7891R
8330020.59.6252,7880R
9245025.88.3252.7868R
10185024.57.2252.7860R
11145021.66.450.350852T
12115020.75.750.466839T
1390021.75.050.581829T
1470022.24.450.733822T
1555021.43.950.871803T
1642023.63.450.982785T
1732023.81.125765T

Table 5
Conditions of rolling: who
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7890R
21100015.417.5 252.7894R
3950013.616.3252.7899R
4800015.814.9252.7906R
5650018.813.5252.7911R
6520020.012.0252.7902R
7415020.210.8252.7889R
8330020.59.6252.7881R
9245025.88.3252.7867R
10185024.57.2252.7860R
11145021.66.450.350852T
12115020.75.7 50.466829T
1390021.75.050.581830T
1470022.24.450.733820T
1555021.43.950.871803T
1642023.63.450.982784T
1732023.81.125764T

Table 6
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
1930040.519.0252.7849R
2550040.917.5252.7865R
3330040.016.3252.7879R
4190042.414.9252.7896R
5110042.113.5252.7912R
666040.0to 12.0252.7921R
740039.410.8252.7930R
832020.02.7919R

Table 7
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)The ratio at which Eisenia (%) 0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0102.7791R
21100015.417.5102.7805R
3950013.616.3102.7819R
4800015.814.9102.7836R
5650018.813.5102.7850R
6520020.012.0102.7865R
7415020.210.8102.7871R
8330020.59.6 102.7875R
9245025.88.3102,7879R
10185024.57.2102.7884R
11145021,66.450.350901T
12115020.75.750.466899T
1390021.75.050.581895T
1470022.24.450.733895T
1555021.43.950.871883T
1642023.63.450.982875T
1732023.81.125860T

Table 8
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7791R
21100015.417.5252.7796R
3950013.616.3252.7801R
4800015.814.9252.7804R
5670016.313.7252.7806R
6600010.512.9252.7784R
7520013.312.0252.7764R
8465010.611.4252.7746R
9380018.310.3252.7733R
10310018.49.350.622733T
11260016.18.550.837734T
12221015.01.125731T

Table 9
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625ÈA;
11300016.819.0102.7819R
21100015.417.5102.7836R
3950013.616.3102.7849R
4800015.814.9102.7873R
5670016.313.7102.7879R
6600010.512.9102.7896R
7520013.312.0102.7901R
8465010.611.4102.7904R
9380018.310.352.7909R
10310018.49.3 50.622902T
11260016.18.550.837883T
12221015.01.125874T

Table 10
Conditions of rolling: B08
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7790R
21100015.417.5252.7795R
3950013.616.3252.7799 R
4800015.814.9252.7804R
5650018.813.5252.7812R
6520020.012.0252.7800R
7415020.210.8252.7780R
8330020.59.6252.7759R
9245025.88.3252.7741R
10185024.57.2252.7720R
11145021.66.4100.350719T
12115020.75.7100.466724T
1390021.75.0100.581730 T
1470022.24.4100.733729T
1555021.43.9100.871721T
1642023.63.4100.982705T
1732023.81.125690T

Table 11
Conditions of rolling: V
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7810R
211000 17.5252.7816R
3950013.616.3252.7821R
4800015.814.9252.7824R
5650018.813.5252.7829R
6520020.012.0252.7821R
7415020.210.8252.7800R
8330020.59.6252.7779R
9245025.88.3252.7761R
10185024.57.2252.7749R
11145021.66.450.350741T
121150 5.750.466751T
1390021.75.050.581760T
1470022.24.450.733766T
1555021.43.950.871761T
1642023.63.450.982751T
1732023.81.125726T

Table 12
Conditions of rolling: 10
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625ÈA;
11300016.819.0252.7886R
21100015.417.5252.7884R
3950013.616.3252.7884R
4800015.814.9252.7887R
5650018.813.5252.7885R
6520020.012.0252.7859R
7415020.210.8252.7841R
8330020.59.6252.7820R
9245025.88.3252.7800R
10185024.57.2252.7 791R
11145021.66.450.350801T
12115020.75.750.466810T
1390021.75.050.581830T
1470022.24.450.733836T
1555021.43.950.871829T
1642023.63.450.982821T
1732023.81.125806T

Table 13
Conditions of rolling: B11
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (0The time between prokatami (C)/ Min net is ü rolling(m/s) Temperature (°)Rolling mill
15625
11300016.819.0252.71024R
21100015.417.5252.71015R
3950013.616.3252.71003R
4800015.814.9252.7996R
5650018.813.5252.7985R
6520020.012.0252.7969R
7415020.210.8252.7961R
8330020.59.6252.7949R
92450 25.88.3252.7930R
10185024.57.2252.7921R
11145021.66.450.350911T
12115020.75.750.466901T
1390021.75.050.581891T
1470022.24.450.733881T
1555021.43.950.871864T
1642023.63.450.982845T
1732023.81.125825T

Table 14
Conditions of rolling: 12
The cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7891R
21100015.417.5252.7895R
3950013.616.3252.7899R
4800015.814.9252.7905R
5670016.313,7252.7906R
6600010.512.9252.7886R
7520013.312.0252.7865 R
8465010.611.4252.7845R
9380018.310.3252.7836R
10310018,49.350.622835T
11260016.18.550.837834T
12221015.01.125830T

td align="center"> 16.8
Table 15
Conditions of rolling: B13
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300019.0252.7929R
21100015.417.5252.7925R
3950013.616.3252.7919R
4800015.814.9252.7913R
5650018.813.5252.7911R
6520020.012.0252.7900R
7415020.210.8252.7891R
8330020.59.6252.7880R
9245025.88.3252.7868R
10185024.57.2252.7850R
111450 21.66.4100.350832T
12115020.75.7100.466804T
1390021.75.0100.581777T
1470022.24.4100.733749T
1555021.43.9100.871728T
1642023.63.4100.982713T
1732023.81.125698T

Table 16
Conditions of rolling: 14
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)raketnyy mill
15625
11300016.819.02510.8810R
21100015.417.52510.8836R
3950013.616.32510.8861R
4800015.814.92510.8883R
5650018.813.52510.8911R
6520020.012.02510.8901R
7415020.210.82510.8869R
8330020.59.6251.8841R
9245025.88.32510.8 808R
10185024.57.22510.8779R
11145021.66.4100.350781T
12115020.75.7100.466792T
1390021.75.0100.581799T
1470022,24.4100.733805T
1555021.43.9100.871801T
1642023.63.4100.982790T
1732023.81.125774T

Table 17
Conditions of rolling: 15
Room rollingThe cross-sectional area (the m 2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016,819.0252.7790R
21100015.417.5252.7796R
3950013.616.3252.7801R
4800015.814.9252.7803R
5650018.813.5252.7811R
6520020.012.0252.7801R
7415020.210.8252.7779R
8 330020.59.6252.7761R
9245025.88.3252.7738R
10185024.57.2252.7719R
11145021.66.450.700751T
12115020.75.750.932782T
1390021.75.051,162 notices829T
1470022.24.451.466865T
1555021.43.951.742891T
1642023.63.451.964910T
1732023.82.500864T

Table 18
Conditions of rolling: B16
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7821R
21100015.417.5252.7817R
3950013.616.3252.7834R
4800015.814.9252.7838R
5670016.313.7252.7845R
6600010.512.9252.7824 R
7520013.312.0252.7794R
8465010.611.4252.7776R
9380018.310.3252.7767R
10310018.49.350.622764R
11260016.18.550.837769T
12221015.01.125766T

Table 19
Conditions of rolling: B17
Room rollingThe cross-sectional area (mm2)Reduction ratio (%)0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7822R
21100015.417.5252.7825R
3950013.616.3252.7833R
4800015.814.9252.7834R
5650018.813.5252.7842R
6520020.012.0252.7830R
7415020.210.8252.7809R
8330020.59.6252.7790R
9245025.88.3252.7765R
101850 24.57.2252.7757R
11145021.66.450.350759T
12115020.75.750.466772T
1390021.75.050.581771T
1470022.24.450.733774T
1555021.43.950.871771T
1642023.63.450.982779T
1732023.81.125777T

2.7
Table 20
Conditions of rolling: 18
Room rollingThe cross-sectional area (mm2)Reduction ratio (%) 0.167√ S (C)The time between prokatami (C)The rolling speed (m/s)Temperature (°)Rolling mill
15625
11300016.819.0252.7850R
21100015.417.5252.7847R
3950013.616.3252.7847R
4800015.814.9252.7845R
5650018.813.5252.7844R
6520020.012.0252.7845R
7415020.210.8252.7843R
8330020.59.625834R
9245025.88.3252.7830R
10185024.57.2252.7829R
11145021.66.450.350821T
12115020.75.750.466814T
1390021.75.050.581803T
1470022.24.450.733794T
1555021.43.950.871790T
1642023.63.450.982782T
1732023.81.125772T

1. Rouge (α+β) iconologia alloy, consisting of the following components, wt.%: aluminum 4-5, vanadium 2,5-3,5, iron 1.5 to 2.5, molybdenum, 1.5 to 2.5, titanium else, characterized in that the alloy from which it is made, contains 10-90 vol.% primary α-phase, the average grain size of primary α-phase is 10 μm or less in a transverse plane parallel to the direction of rolling of the bar, the elongation of the primary grain α-phase is four or less.

2. The bar according to claim 1, characterized in that the volume fraction of primary α-phase ranges from 50 to 80 vol.%, and the average grain size of primary α-phase is equal to 6 μm or less.

3. The method of manufacture of the bar of (α+β) titanium alloy, comprising the step of hot rolling, the alloy contains the following components, wt.%: aluminum 4-5, vanadium 2,5-3,5, iron 1.5 to 2.5, molybdenum, 1.5 to 2.5, titanium else, characterized in that before the step of hot rolling carry out the step of heating the alloy at the surface temperature (T β-150) - T β°Since, during the step of hot rolling the surface temperature of the support in the range (T β-300) - (T β-50)°and the final temperature of the surface, i.e. the surface temperature directly after the last rolling is (T β-300) - (T β-100)°where T βtemperature α/β - transition.

4. The method according to claim 3, characterized in that Provo is it hot rolling with a shrinkage ratio of 40% or less per rolling.

5. The method according to claim 3, wherein the hot rolling is carried out with the use of a reversing rolling mill, the rolling speed is 6 m/s or less.

6. The method according to claim 3, wherein the hot rolling is carried out with use of a tandem rolling mill, the rolling speed is 1.5 m/s or less.

7. The method according to claim 3, characterized in that the alloy is re-heated during hot rolling.



 

Same patents:

FIELD: metallurgy, namely processes for forging titanium alloys and blank of such alloy suitable for forging.

SUBSTANCE: method comprises steps of preparing blank and forging it. Forging is realized at providing mechanical hardening factor equal to 1.2 or less and at difference of hardness values between central (along width) zone and near-surface zone equal to 60 or less by Vickers. Factor of mechanical hardening is determined as HV(def)/HV(ini), where HV(ini) - hardness of titanium alloy blank before forging; HV(def) -hardness of titanium alloy blank after forging at forging reduction 20%. Forging may be realized at deformation rate from 2 x 10 -4 s -1 to 1s-1 while keeping relations (T β - 400)°C ≤ Tm ≤ 900°C and 400°C ≤ Td ≤ 700°C, where Tβ (°C) -temperature of β-phase transition of titanium alloy, T m(°C) - temperature of worked blank; Td(°C) - temperature of die set. Blank has factor of mechanical hardening 1.2 or less and difference of hardness values between central (along width) zone and near-surface zone equal to 60 or less by Vickers.

EFFECT: possibility for forging titanium alloy blanks at minimum difference of material properties along depth, simplified finishing of blank surface after forging, reduced cracking of blank material, good workability of blank with favorable ductility and fatigue properties.

8 cl, 5 tbl, 6 dwg, 4 ex

FIELD: non-ferrous metallurgy; methods of thermal treatment of items or blanks made out of the two-phase titanium alloys titanium alloys.

SUBSTANCE: the invention is pertaining to the field of metallurgy, in particular, to the method of thermal treatment of an item or blanks made out of the two-phase titanium alloys titanium alloys. The offered method of thermal treatment of an item or a blanks made out of the two-phase titanium alloys provides for their heating, seasoning and chilling. At that the item or the blank is heated up to the temperature of (0.5-0.8)tag , where tag is the temperature of the alloy aging, and chilling is conducted from -10 up to -20°С at simultaneous action of a gas current and an acoustic field of an acoustical range frequency with a level of the sound pressure of 140-160 dB. The technical result is the invention ensures an increased strength of items or blanks at keeping the satisfactory plastic properties.

EFFECT: the invention ensures an increased strength of items or blanks at keeping the satisfactory plastic properties.

7 cl, 1 dwg, 1 tbl, 1 ex

FIELD: aircraft industry; mechanical engineering; methods of metals plastic working.

SUBSTANCE: the invention is pertaining to the methods of metals plastic working, in particular, to production of blanks for units of a gas turbine engine and may be used in production of aircraft engines and in mechanical engineering. The method includes heating of a high-temperature resistant alloy bar and its straining during several runs. For obtaining a homogeneity of the blank chemical composition and structure in the whole volume of the blank and for increasing the alloy mechanical properties during the blank subsequent machining at least one run is conducted at the temperature exceeding the temperature of the beginning of the alloy hardening inter-metallic phase dissolution. Then, they conduct a press forming in the interval of the temperatures from the temperature of a recrystallization process start to the temperature of the recrystallization process end for production of the uniform fine grained structure, that ensures a high level of general physical-mechanical properties of the blank and the item as a whole.

EFFECT: the invention ensures production of the uniform fine-grained structure and a high level of general physical-mechanical properties of the blank and the item as a whole.

2 ex

FIELD: deformation-heat treatment of metal with change of its physical and mechanical properties, possibly in machine engineering, manufacture of air craft engines and in medicine for making semi-finished products of titanium.

SUBSTANCE: method comprises steps of intensive plastic deformation in mutually crossing ducts and further mechanical working of blank. Mechanical working is realized by multiple rolling or extrusion at 20°C at reduction degree in one pass causing no main cracking and material destruction. Number of passes of rolling or extrusion provides final deformation degree 80- 90 %.

EFFECT: manufacture of ultra-fine grain titanium sheet blanks with improved fatigue limit value at the same strength and working ductility.

1 dwg, 1 ex

FIELD: metallurgy, in particular feed from titanium-based alloy for aircraft industry and engineering.

SUBSTANCE: claimed method includes feed heating, deformation thereof in die, heated to temperature of total titanium-based alloy polymorphous conversion or above: isothermal holding at die temperature for time effective to total titanium-based alloy recrystallization; and quench. Feed is heated up to temperature by 10-30oC lower than the same of total polymorphous conversion; deformation is carried out in two steps: in the first one deformation rate is sufficient to feed heating up to die temperature, and deformation degree is 30-60 %, and in the second one rate is 10-2-10-4 s-1, and deformation degree is 10-30 %; isothermal holding is carried out under pressure of 10-150 MPa.

EFFECT: strained feed with homogenous recrystallized structure and β-grain size of 10-30 mum; with high strength and improved coefficient of metal utilization.

5 cl, 2 tbl, 1 ex

FIELD: manufacture of metallic articles, particularly of hard-to-form intermetallic alloys, possibly electric resistive heating members.

SUBSTANCE: article is made of aluminides of iron, nickel and titanium. Method comprises steps of subjecting article being cold worked to cold hardening; performing rapid annealing at seasoning less than 1 min; repeating operations of cold working and rapid annealing for receiving article with desired size. It is possible to make article by casting, powder metallurgy process or plasma deposition.

EFFECT: enhanced strength of article.

26 cl, 4 dwg

FIELD: mechanical engineering; piston internal combustion engines.

SUBSTANCE: invention relates to valve of internal combustion engine, method of its manufacture and heat-resistant titanium alloy used for manufacture of valve consisting of following components, mass %: aluminum 7.5-12.5; molybdenum 1.6-2.6; zirconium 1.4-2.4; silicon 0.1-0.2' yttrium 0.005-0.1; titanium - the rest. It has α+α2+β phase composition with intermetallide α2 phase on Ti3Al base dispersed in α phase. Proposed method includes forming of valve from cylindrical blank by deformation machining with preliminary heating and subsequent heat treatment. Preliminary heating of part of blank related to rod done to temperature 5-20oC lower than temperature of complete polymorphic transformation of alloy, and its deformation machining is carrying out by wedge cross rolling. Deformation machining of part of blank related to head is done by forging with preliminary heating to temperature 5-50oC higher than temperature of complete polymorphic transformation of alloy corresponding to beginning of forging, and forging is finished at temperature lower than complete polymorphic transformation of alloy to form plate head of valve and transition section provided smooth changing of head into rod. Invention provides designing of valve, method of its manufacture and heat-resistant alloy used in manufacture of valve making it possible to operate valve within operating temperature range owing to increased long-term strength and creep resistant of valve head material and increased strength, modulus of elasticity and hardness of valve rod material.

EFFECT: improved quality of valve and increased reliability in operation.

16 cl, 3 tbl, 1 ex, 15 dwg

-titanium alloys" target="_blank">

The invention relates to ferrous metallurgy, in particular to the processing of titanium alloys

The invention relates to a pressure treatment of metals to improve the physico-mechanical properties, in particular in the manufacture of semi-finished titanium or other metals

FIELD: metallurgy.

SUBSTANCE: invention proposes titanium-base alloy and article made of thereof. Alloy comprising aluminum, molybdenum, vanadium, chrome, iron, zirconium, oxygen, carbon, hydrogen, nitrogen, copper and nickel comprises additionally silicon and tungsten in the following ratio of components, wt.-%: aluminum, 2.0-6.8; molybdenum, 1.0-3.5; vanadium, 3.0-6.0; chrome, 0.4-1.6; iron, 0.2-1.2; zirconium, 0.01-0.3; oxygen, 0.04-0.14; carbon, 0.02-0.1; hydrogen, 0.003-0.02; nitrogen, 0.005-0.05; copper, 0.001-0.1; nickel, 0.001-0.01; silicon, 0.02-0.15; tungsten, 0.001-0.03, and titanium, the balance. Invention provides the development of titanium alloys designated for making plane stringers, ribs, frames, fuselage, wings and engines and for applying as material for welding. Invention provides enhancing strength and crack-resistance of the basic alloy and welding joints and reducing article mass.

EFFECT: improved properties and quality of alloy.

3 cl, 2 tbl, 3 ex

FIELD: metallurgy, namely processes for forging titanium alloys and blank of such alloy suitable for forging.

SUBSTANCE: method comprises steps of preparing blank and forging it. Forging is realized at providing mechanical hardening factor equal to 1.2 or less and at difference of hardness values between central (along width) zone and near-surface zone equal to 60 or less by Vickers. Factor of mechanical hardening is determined as HV(def)/HV(ini), where HV(ini) - hardness of titanium alloy blank before forging; HV(def) -hardness of titanium alloy blank after forging at forging reduction 20%. Forging may be realized at deformation rate from 2 x 10 -4 s -1 to 1s-1 while keeping relations (T β - 400)°C ≤ Tm ≤ 900°C and 400°C ≤ Td ≤ 700°C, where Tβ (°C) -temperature of β-phase transition of titanium alloy, T m(°C) - temperature of worked blank; Td(°C) - temperature of die set. Blank has factor of mechanical hardening 1.2 or less and difference of hardness values between central (along width) zone and near-surface zone equal to 60 or less by Vickers.

EFFECT: possibility for forging titanium alloy blanks at minimum difference of material properties along depth, simplified finishing of blank surface after forging, reduced cracking of blank material, good workability of blank with favorable ductility and fatigue properties.

8 cl, 5 tbl, 6 dwg, 4 ex

FIELD: powder metallurgy, namely sintered titanium base alloys used as constructional materials.

SUBSTANCE: sintered titanium base alloy contains, mass. %: aluminum, 5.5 - 7.0; zirconium, 1.4 -2.5; molybdenum,, 0.5 - 1.8; vanadium,, 0.8 -2.3; titanium, the balance. Alloy is prepared of powder of said content with particle size in range 0.5 - 3.0 micrometers. Structure of particles includes martensite α - phase and ω-phase with coherent dissipation range 300 - 600 Å. Percentage density of alloy - 99.6%. In structure of alloy there is no α2 - phase. Alloy is prepared by compacting under pressure 1200 Mpa, sintering at 1523 K for 3 hours in vacuum 0.0133 Mpa, annealing at 723 - 823 K for 1.5 hours and cooling together with furnace until room temperature.

EFFECT: enhanced mechanical properties of alloy.

FIELD: metallurgy, in particular alloy with shape memory effect useful as implants in medicine, as temperature sensors, thermosensitive elements in equipment engineering, radio engineering, etc.

SUBSTANCE: claimed alloys contain a) (at. %) titanium 48-52; cobalt 20-30; and balance: gold; and b) titanium 48-52; iron 13,1-16; and balance: gold. Materials of present invention are free from nickel and have shape memory effect and superelasticity at human body temperatures that provides high biomechanical compatibility of implant made from the same in contacting region with various tissues of living organism.

EFFECT: alloys with excellent shape memory effect and superelasticity.

2 cl, 1 tbl, 1 ex

FIELD: mechanical engineering; piston internal combustion engines.

SUBSTANCE: invention relates to valve of internal combustion engine, method of its manufacture and heat-resistant titanium alloy used for manufacture of valve consisting of following components, mass %: aluminum 7.5-12.5; molybdenum 1.6-2.6; zirconium 1.4-2.4; silicon 0.1-0.2' yttrium 0.005-0.1; titanium - the rest. It has α+α2+β phase composition with intermetallide α2 phase on Ti3Al base dispersed in α phase. Proposed method includes forming of valve from cylindrical blank by deformation machining with preliminary heating and subsequent heat treatment. Preliminary heating of part of blank related to rod done to temperature 5-20oC lower than temperature of complete polymorphic transformation of alloy, and its deformation machining is carrying out by wedge cross rolling. Deformation machining of part of blank related to head is done by forging with preliminary heating to temperature 5-50oC higher than temperature of complete polymorphic transformation of alloy corresponding to beginning of forging, and forging is finished at temperature lower than complete polymorphic transformation of alloy to form plate head of valve and transition section provided smooth changing of head into rod. Invention provides designing of valve, method of its manufacture and heat-resistant alloy used in manufacture of valve making it possible to operate valve within operating temperature range owing to increased long-term strength and creep resistant of valve head material and increased strength, modulus of elasticity and hardness of valve rod material.

EFFECT: improved quality of valve and increased reliability in operation.

16 cl, 3 tbl, 1 ex, 15 dwg

The invention relates to the field of metallurgy, namely the creation of a modern titanium alloys used for manufacturing high-strength and high-tech products, including large, i.e

The invention relates to a method of manufacturing a rotor in the piece with the blades, which use the stub portion of the rotor is made in the preferred embodiment, titanium alloy, and are welded to her shoulder, in the preferred embodiment, also made of titanium alloy

The invention relates to the field of metallurgy, namely the creation of alloys based on titanium, intended for use as a structural material in the manufacture of medical devices and in the construction of chemical and petrochemical engineering

The invention relates to metallurgy and alloys based on titanium, designed for the production of structural parts, components and assemblies in the aerospace industry, shipbuilding, automotive, energy and chemical engineering

-titanium alloy" target="_blank">

The invention relates to the field of non-ferrous metallurgy, in particular to the creation of new alloys based on titanium

FIELD: rolling; sheet rolling processes.

SUBSTANCE: proposed method is based on measuring distribution of relative elongations of band longitudinal sections of strips detected by measuring device. According to invention, longitudinal band sections of strip chosen by measuring device adjoin each other without gaps and overlaps covering entire width of strip and strip tension is measured additionally. Relative overspeeding of metal in direction of strip movement in band longitudinal sections of strip singled out by measuring device relative to metal speed in one of band longitudinal sections of strip singled out by measuring device at minimum speed of metal are calculated using mathematical dependence. Relative overspeeds of metal in direction of strip movement in band longitudinal sections of strip singled out by measuring device, as compared with minimum speed of metal in one of band longitudinal sections of strip singled out using measuring device can be used to adjust profile of roll gap for producing strip of high planeness.

EFFECT: improved planeness of rolled strips owing to increased accuracy of measurement of nonuniformity of metal flow in process of rolling.

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