Method of producing plates from two-phase titanium alloys

FIELD: metallurgy.

SUBSTANCE: proposed method comprises hot forming of slab, hot rolling and teat treatment of plate, whereat hot forming if carried out in one step. Immediately after reaching required thickness in slab forming it is quickly cooled to the depth of 20-30 mm at the rate of at least 50°C/min. Subsequent hot lengthwise rolling at performed at first step in α+β-area by partial reduction with deformation degree εi varying from 3% to 5% to total deformation ε=25…30% with breaks between passes of 8 to 12 s. At second step, it is performed in β-area from heating temperature determined by definite formula. At the next step rolling is performed in α+β-are with breaks and heating in lengthwise or transverse directions with total degree of deformation e after every break to 60%.

EFFECT: homogeneous fine-grain microstructure, high and stable mechanical properties, high precision, no surface defects.

 

The invention relates to a pressure treatment of metals, in particular thermo-mechanical processing of two-phase titanium alloys in the process of obtaining thick sheets and plates

It is known that the structure and homogeneity have a decisive influence on the level and stability of mechanical properties of thick sheets and plates (the plates). Therefore, the development of technological process of manufacturing plates critical is the selection of conditions of structure formation during hot deformation pseudo α, (α+β)-titanium alloys.

Known typical diagram of the technology for production of hot-rolled plates, including heating of the slab, hot rolling, cutting-to-length length, annealing and finishing operations (Titanium alloys. Semi-finished products from titanium alloys. Assumed. editors: NF Anoshkin, MS of Ermenek. M, jist VILS, 1996, s-210).

There is a method of fabrication of titanium alloys (RF Patent No. 2169791, IPC C22F 1/18), comprising heating the slab to a temperature rolling, pre-rolling in two stages, the heating of the roll to a temperature rolling and final rolling, the rolling is performed with regulated temperature and deformation modes

The use of a patent (No. 2169791, IPC C22F 1/18) in the production of plates from the α+β alloys type VT23, VT with a higher ratio of β-phase alloys of the so-called "to imicheskogo), than that of alloy VT6, results in uneven patterns, attacks on property, increased scrapping metal.

In these schemes the manufacture of hot-rolled plates are not regulated temporal factors of the process, the influence of chemical composition of titanium alloys, which leads to heterogeneity of structure, instability and anisotropy of mechanical properties.

The prototype of the chosen method of fabrication of two-phase titanium alloys (RF Patent No. 2378410, IPC C22F 1/18), including hot deformation of the ingot into a slab in three stages, hot rolling slabs in several stages with intermediate cooling between stages to room temperature and subsequent heat treatment of the plates. The duration of the deformation process of the ingot in the slab due to the need at this stage to give the necessary structural metal and plastic properties for subsequent rolling. The resulting plates are characterized by a homogeneous fine-grained structure, high level and stability of mechanical properties.

The disadvantages of the prototype is that the deformation of the ingot in the slab is carried out in three stages, which is associated with significant time and material costs for the heating, the main and auxiliary production operations, as well as large losses of metal, is knitted with intoxication and the resulting surface defects.

Attempts to reduce the complexity of the deformation of the ingot, namely limited pressing slab in a single step, while maintaining the quality of the plates, have not yielded positive results due to the inhomogeneous structure of the alloy according to the section, as it leads to the fact that:

when the deformation of the ingot in one stage on the border of the large β-grains, which are stored in the surface layers, there is an intensive development of the rim of the α-phase, which may exceed the critical size and cause intense development of cracks during the subsequent rolling;

- if there is insufficient study of the structure of the alloy (low plasticity) when the first operation rolling unregulated rhythm rolling leads to unacceptable soolaimon the slab surface in contact with the cold rolls (due to the low thermal conductivity of titanium alloys the temperature of the surface layers do not have time to recover due to the heat coming from the Central regions) and there is a shortage of their plasticity.

Both factors reduce the resource of plasticity and lead to deep surface cracks, which may be classified as correctable, and under adverse circumstances, and fatal marriage. Plate with correctable marriage require additional machining surface the plates to remove cracks. This operation is time-consuming, leading to huge losses of metal, as well as additional time and material costs.

The invention aims to improve the competitiveness of thick sheets and plates by reducing cost while maintaining a high level and stability of mechanical properties and surface quality.

The technical result in the implementation of this invention is to reduce the complexity of the process, increasing the yield and prevent the appearance of surface cracks during thermal deformation processing of plates, and the guaranteed provision of a homogeneous macro - and microstructure.

This technical result is ensured by the fact that in the method of manufacture of plates of two-phase titanium alloys, including hot deformation of the ingot into a slab, hot rolling and subsequent heat treatment plates, hot deformation of the ingot into a slab produced in one step and immediately after reaching the final thickness during deformation of the slab, it is rapidly cooled at a depth from the surface is 20 to 30 mm at a speed of not less than 50°C/min, subsequent longitudinal hot rolling are the first stage in the α+β region from the heating temperature TN=(TPP-20...40°C small private reductions with the degree of deformation εithe t 3% to 5%, to the total degree of deformation ε=25...30%, while bear pause between cuts lasting from 8 to 12, and the second stage longitudinal rolling is carried out in the β-region of the heating temperature, which is determined by the formula:

TN(TPP+(10×MoEK+80))C,(1)

where TN- heating temperature of the slab, °C;

TPPthe temperature of polymorphic transformation, °C;

MoECmolybdenum equivalent, which is calculated by the formula:

MoEK=[Mo]+[V]/1,5+[Cr]*1,25+[Fe]*2,5+[Ni]/0,8,mandwith awith a.%,(2 )

the next stage of rolling produced in the α+β region with interrupt and heatings in the longitudinal or transverse directions with a total degree of deformation after each interrupt ε up to 60%.

In the process of cooling the deformed during one stage of the slabs on the border of the β-grains, there is a development of the rim of the α-phase, which reduces the service life of plasticity and leads to the formation of surface cracks during the subsequent rolling in the α+β region. This becomes a critical factor for the proposed invention, since the ingot is deformed in the slab at one stage and the structure of the slab is still largely inherits enough plastic cast structure of the ingot, particularly in the surface layers. To stop this process, namely the formation of an acceptable thickness of the rim of the α-phase at the grain boundary, it is possible to ensure the cooling rate of the ingot after the final stage of deformation of the ingot in the slab, while the cooling rate should be not less than 50°C/min and spread to a depth of from 20 to 30 mm As shown for this purpose in many cases is sufficient to maintain contact between the surfaces of the slab and tools after deformation or cooling the slab in water, the contact time, finding the slab in water are determined empirically.

At the first stage of rolling due to the fact that the structure of the slab, deformed at one stage, is not yet sufficiently developed and its ductility resource is limited, therefore unregulated rhythm rolling leads to critical soolaimon the slab surface in contact with the cold rolls. This is because, with the aim of increasing the productivity of the rolling process, operators of rolling mills, traditionally oriented to the reduction in the duration of pauses between passages 3-5 SiS of the low thermal conductivity of titanium alloys the temperature of the surface layers do not have time to recover due to the heat coming from the Central regions, which leads to the cooled surface of the slab cracks, emerging at the triple junctions of β-grains. The interval between passages duration from 8 to 12 enables the alignment of the temperature field in the cross section of the slab to an acceptable level, not provoking the formation of surface cracks.

When selecting the first temperature α+β-rolling assumed that a sufficient degree of Polygonaceae work hardening" reported the metal only in the presence of and the corresponding stability of the interphase boundaries. To prevent in the first stage of rolling in the α+β-development processes dynamic and spontaneous recrystallization, rolling was carried out by small private compression and ε i=3...5% to the total degree of deformation ε from 20% to 30% at a temperature TPP-20...40°C, while the metal is reported sufficient degree Polygonaceae work hardening", which provides a metal higher energy level to ensure the effect of recrystallization β-grain structure in the subsequent second stage rolling in the β-region. The temperature of the subsequent second stage rolling in the β-region is defined by the formula (1), which is obtained on the basis of experimental data.

The heating temperature of the slab at the second stage of rolling, providing the desired effect recrystallization of β-phase, depends on the chemical composition of the alloy, namely from its molybdenum equivalent MoECthe formula (2).

To provide a given level of mechanical properties subsequent stage rolling produced in the α+β region with interrupt and heatings in the longitudinal or transverse directions with a total degree of deformation after each interrupt 8 to 60%. The metal at this stage and given the modes has a reserve of plasticity, which does not require strict regulation of the rhythm rolling.

In the following examples of specific performance, the heating temperature before the second rolling was determined in accordance with formulas 1 and 2.

Example 1

The proposed method was tested in the manufacture of slabs the size of the AMI 16×900×2000 mm of two-phase titanium alloy Ti-6Al4V. The temperature of polymorphic transformation alloy CCI=980°C. the Production of slab produced from an ingot with a diameter of 740 mm, the Ingot was heated to a temperature of 1180°C (210°C higher CCI), extruded in a vicious stamp on the size 276×1080×1600 mm and withstand the resulting slab in the stamp, without lifting the top prints for 3 min, which provided the cooling rate of the surface layer to a depth of 20 mm is not less than 50°C/min, Further cooling of the slab was carried out on the adjustage separately without contact with other hot slabs. Machined to the dimensions of 266×1080×1700 mm slab was heated to a temperature of 940°C (40°C below CCI) and rolled on the mill quarto-2000 small reductions εi=3-4%, and the interval between passages duration from 8 to 12 C to the total degree of deformation ε=25% and then cooled to the temperature of the shop. Visual inspection of surface cracks are not detected. Next, the roll was heated to a temperature of 1090°C, rolled with the degree of deformation ε=55% and cooled to the temperature of the shop. Then the roll was heated to a temperature of 940°C (40°C below CCI) and were rolling with the degree of deformation ε=50%. After cooling, the strip was cut into cards and final rolling with a degree of deformation ε=50% spent in the transverse direction.

The resulting plate was subjected to heat treatment processing, as well as PEFC is blowing tests of mechanical properties and control patterns.

The test results met the requirements of the Russian TU-1-805-391-79 and international standards A, AMS4911H.

Example 2

The proposed method was tested in the manufacture of plates with dimensions 50×1000×2000 mm of two-phase titanium alloy W 23. The temperature of polymorphic transformation alloy CCI=890°C. the Production of slab produced from an ingot with a diameter of 740 mm weight 3200 kg Ingot was heated to a temperature of 1150°C (260°C higher CCI)was subjected to forging one stage to the size of 300×1100×1700 mm and cooled the resulting slab in the tank with water for 3 min to ensure that the cooling rate of the surface layer to a depth of 20 mm is not less than 50°C /min, Further cooling of the slab was carried out on adjustage separately without contact with other hot slabs. Machined to the dimensions 280×1080×1730 mm slab was heated to a temperature of 860°C rolled on the mill quarto small reductions εi=3-4%, and the interval between passages duration from 8 to 12 C to the total degree of deformation 8=25% and then cooled to the temperature of the shop. Visual inspection of surface cracks are not detected. Next, the roll was heated to a temperature of 1050°C, rolled with the degree of deformation ε=65% and cooled to the temperature of the shop. Then the roll was heated to a temperature of 860°C (30°C below TPPand spent the final about ATCO with the degree of deformation ε=50%.

The resulting plate was subjected to heat treatment processing, and subsequent testing of mechanical properties and control patterns.

The test results met the requirements of the domestic TY1-805-103-8L

Mechanical properties are shown in table 1.

Table 1
Mechanical properties
The way the
foster plates
The condition of the test sampletemporary resistance □kg/mm2relative elongation δ, %the relative narrowing of Ψ, %impact strength KCU, MJ/m2
Aged1329,628,00,35
OfferHardened and aged130,510,631,00,33
Sostar the TES 124,37,813,90,34
KnownHardened and aged128,48,418,40,31
TL1-805-103-81Heat-treated110-1308,011,00,30

Example 3

The proposed method was applied in the manufacture of plates with dimensions of 45×1000×2000 mm of two-phase titanium alloy W 22. The temperature of polymorphic transformation alloy TPP=870°C. the Production of slab produced from an ingot with a diameter of 740 mm, the Ingot was heated to a temperature of 1200°C (330°C above TPPand made forging one stage to the size of 300×1100×1700 mm and cooled the resulting slab in the tank with water for 3 min to ensure that the cooling rate of the surface layer to a depth of 20 mm is not less than 50°C/min, Further cooling of the slab was carried out on adjustage separately without contact with other hot slabs. Machined to the dimensions 280×1080×1700 mm slab was heated to a temperature of 840°C (30°C below TPP) and were rolling the and mill quarto 2000 small reductions ε i=3-4% to the total degree of deformation ε=25%, with intervals between passages duration 8-12 C and then cooled to the temperature of the shop. Visual inspection of surface cracks are not detected. Next, the roll was heated to a temperature of 1075°C, rolled with the degree of deformation ε=58% and cooled to the temperature of the shop. Then the roll was heated to a temperature of 900°C (30°C below TPPand spent the final rolling with a degree of deformation ε=50%.

The resulting plate was subjected to heat treatment and subsequent testing of mechanical properties and control patterns. The test results of mechanical properties are given in table 2.

The macrostructure of the plates 5-6 points, sections 7 points allowed in THE 1-92-31-74 and I-76 for serial plates are missing.

The microstructure of plates 1-3 type, sections 4 types permitted in THE 1-92-31-74 and I-76 for serial plates are missing.

Table 2
The method of manufacture
of plates
The condition of the test sampleMechanical properties
temporary resistance □kg/mm2relative elongation δ, % the relative narrowing of Ψ, %impact strength KCU, MJ/m2
Discov
text
annealed120,112,830,90,30
annealed122,812,529,10,32
Knownannealed124,37,212,40,34
annealed118,48,018,40,31
TL1-92-31-74annealed110-130616,00,25

The resulting plates are characterized by a homogeneous fine-grained structure, high level and stability of mechanical properties and high dimensional accuracy and the absence of surface defects.

A method of manufacturing plates of duhf the testing of titanium alloys including hot deformation of the ingot into a slab, hot rolling and subsequent heat treatment of the plates, characterized in that to produce one-stage hot deformation of the ingot into a slab and once in the deformation process of finite thickness slab carry out rapid cooling on the depth of the slab from the surface is 20 mm to 30 mm at a speed of not less than 50°C/min, then conduct subsequent longitudinal hot rolling, and the first stage is in the α+β region from the heating temperature TN=(TPP-20...40°C)private reductions with the degree of deformation εifrom 3% to 5% to the total degree of deformation ε=25...30% and with pauses between cuts lasting from 8 to 12, and the second stage is in the β-region of the heating temperature, which is determined by the formula:
TN≥(TPP+(10×MoEC+80)°C,
where TN- heating temperature of the slab, °C;
TPPthe temperature of polymorphic transformation, °C;
MoECmolybdenum equivalent, calculated according to the formula:
MoEC=[Mo]+[V]/1,5+[Cr]·1,25+[Fe]·2,5+[Ni]/0.8, wt.%
at the subsequent stages are rolling in the α+β region with interrupt and heatings in the longitudinal or transverse directions with a total degree of deformation ε after each interrupt to 60%.



 

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2 cl, 2 tbl

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