Method of making thin sheets from pseudo-beta-titanium alloys

FIELD: metallurgy.

SUBSTANCE: proposed method comprises smelting of alloy, making slab, machining its surface, hot, warm, and cold rolling, sintering and ageing. Smelted is pseudo-beta-titanium alloy with aluminium content not higher than 5.0 wt % and molybdenum equivalent No eq. ≥ 12 wt %, calculated by the following formula: Mo eq. wt % = %Mo + %Ta/4 + %Nb/3.3 + %W/2 + %V/1.4 + %Cr/0.6 + +%Fe/0.5 + %Ni/0.8 + %Mn/0.6 + %Co/0.9. Semi-finished 8-2 mm-thick rolled stock produced in hot and cold rolling is subjected, prior to cold rolling, to quenching at Tpt+(20-50°C) for 0.1-0.5 h with cooling. Cold rolling is performed to sheet thickness of 6-1 mm in signal-phase beta-state in two and more steps in several passes with 1-6%-reduction in one pass and total reduction at every step of 30-50%. Note here that intermediate quenching is carried out between said steps in conditions identical to quenching of semi-finished rolled stock before cold rolling.

EFFECT: high-quality rolled thin sheets.

5 dwg, 2 tbl

 

The invention relates to the field of metal forming, and in particular to methods of manufacturing thin sheets by cold rolling of high strength pseudo-β-titanium alloys, which can be used in aerospace, chemical industry, mechanical engineering, medicine and other fields of national economy.

Cold rolling compared to hot has two big advantages. First, it allows the sheets and strips of a thickness of less than 1.0-0.8 mm up to several microns, which hot rolling unattainable. Secondly, it provides a higher quality production on all counts and dimensional accuracy, surface finish, physico-mechanical properties.

Titanium alloys are quite time-consuming when processing, so the cost of processing them is significantly higher in comparison with most other structural metals. In particular, most titanium alloys are difficult to deformation at room temperature, as a consequence, the industry's preference for hot deformation processing to produce semi-finished products, including sheet metal.

For example, a known method of manufacturing thin sheets of alloys mainly on the basis of titanium rolling in the package, including the preparation of the procurement, Assembly p is chum using steel case hot rolling package, heat package, the separation of the sheets, heat treatment, prokladku, editing and finishing the surface of the leaves, while the hot rolling of the package is carried out at thermal deformation parameters, implementing the scheme of deformation of a homogeneous compression of the material of the case and sheets thermoablative and ruled mostly in a vacuum furnace under conditions of creep (RF Patent No. 2179899, IPC B21B 1/38).

The process requires careful pre rigorous training, it is costly and inefficient compared to cold rolling. In addition, the implementation of technology in conditions of high temperatures in itself complicates the process and requires expensive heating equipment.

Known conditions under which it is possible to significantly improve the technological plasticity and reduce the deformation resistance of titanium alloys at room temperature to an acceptable level, allowing the cold rolling.

At almost the same content of impurities critical impact on the value of technological plasticity at room temperature have the following factors:

- high content of β-phase with the volume-centered cubic lattice, which is inherently more ductile than the hexagonal α-phase;

on gennoe aluminum content, because with the increase of its content in the alloy technological plasticity decreases, and when the content of more than 6% (by weight) Al technological plasticity of the alloys becomes insignificant.

These requirements under certain circumstances correspond to high-alloy pseudo-β-titanium alloys with low aluminum content and a high content of β-phase, which is fixed by quenching. These alloys in the hardened state have high plasticity and are capable of cold-formed.

However, in the final product to achieve high mechanical properties at high fracture toughness must be aging alloys. In the process of aging is dispersive decay of the β-phase with the formation at the grain boundaries of a thin layer of α-phase, which reduces the technological plasticity of the alloy and makes it impossible for the cold rolling of titanium alloys.

A known method of manufacturing sheets of the β-titanium alloy comprising machining the surface of the slab, hot, warm, cold rolling, annealing and aging (RF patent No. 2318913, IPC C22F 1/18, B21B 3/00).

The method does not provide receiving sheet of the pseudo-β-titanium alloys, as it does not guarantee the absence of α-phase in the cold rolling process and does not limit the critical content of aluminum in the titanium alloys, to the which can handle this method.

Task to be solved by the claimed invention is directed, is getting a quality sheet of semi-finished product made of high-strength pseudo-β-titanium alloys with thickness up to 1 mm or less with a high yield with minimal labor and energy costs.

Technical result achieved in the implementation of the invention is to obtain high-quality sheet metal, including sheet of high pseudo-β-titanium alloys by cold rolling, which is produced on the workpiece with the prepared single-phase β-alloy regulated when the content of aluminum.

The technical result is achieved in that in the method of manufacturing thin sheets of pseudo-β-titanium alloys, including alloy smelting, obtaining slab, mechanical surface treatment of the slab, hot, warm, cold rolling, annealing and aging, smelted pseudo-β-titanium alloy with an Al content in the alloy is not more than 5.0 wt.% and molybdenum equivalent Mo eq, % wt.≥12 wt.%, is calculated by the formula:

Mo eq, wt.% = %Mo+%Ta/4+%Nb/3.3+%W/2+%V/1,4+%Cr/0,6+%Fe/0,5+%Ni/0,8+%Mn/0,6+%Co/0,9,

when this is received after the hot and the heat-rolled steel thickness 8-2 mm before cold rolling is subjected to tempering at TPP+(20-50°C) for 0.1 to 0.5 hours, followed by cooling, the cooler the rolling is conducted respectively to the thickness of the sheet 6-1 mm single-phase β-able in two or more stages in several passes with the degree of deformation in a single pass 1-6% and the total strain at each stage of 30-50%, thus between stages perform intermediate quenching mode, identical to the hardening of the tackle before cold rolling.

The method is applicable when rolling pseudo-β-titanium alloys, the composition of which corresponds to the following conditions:

1. Molybdenum equivalent (Mo eq.) must be at least 12 wt.%. This allows the process of hardening in the air sheet thickness up to 8 mm fixed metastable β-phase, and thus in subsequent operations are guaranteed to improve the technology of plasticity to an acceptable level.

2. The Al content should not exceed 5.0 wt.%, because the excess of this value reduces technological plasticity pseudo-β-titanium alloys to the level of making sheet cold rolling problematic.

The entire process chain, from processing of the ingot to the manufacture of rolled stock, based on known methods of hot and warm treatment, as they are the most technologically and economically viable and meet the requirements of today.

Before cold rolling is quenched steel at a temperature TPP+(20-50°C), the shutter speed is within 0.1 to 0.5 hours and then cooled, the time and temperature intervals during hardening selected from the following considerations:

- modes of quenching below the lower bounds do not guarantee the education structure, ostoja entirely of β-phase;

- exceeds upper bounds leads to the excessive growth of β-grains, which is inherited by the metal to the final product and leads to a significant reduction of the values of the mechanical properties of the alloy, particularly in the aged condition.

Tempering allows in alloys with Mo eq. ≥12 wt.% transfer 100% of the alloy structure in the single-phase β-state.

The aluminum content in the alloy should not exceed 5%because this value is critical, and its excess reduces technological plasticity to the level that impedes the carrying out cold rolling.

The ability of pseudo-β-titanium alloys, hardened in the metastable β-phase, to decay upon heating with the formation of the second phase provides an opportunity to apply a hardening heat treatment to obtain the required level of mechanical properties in the final product. To do so, before annealing and aging to enter into the material energy stresses sufficient to recrystallization processes.

Cold rolling is performed with degrees:

- the overall degree of deformation is in the range of 30-50% in one step, which is carried out in several passages;

strain in a single pass - 1-6%.

To preserve the single-phase β-States in the cold rolling process between stages produce intermediate quenching mode, identical to the first hardening p is data.

Deformation within the above does not allow to create a sufficient hardening of the material, sufficient to process a refund upon annealing for recrystallization mechanism.

Strain this creates prerequisites for the mechanical disintegration of the β-phase formation at the grain boundaries of α-phase and, as a consequence, reduction of technological plasticity and cracking during the rolling process.

The proposed method is tested under production conditions sheet rolling shop in the manufacture of sheets of pseudo-β-titanium alloy VST3553 thickness H=1,6 mm

The panels are manufactured from hot rolled billets pseudo-β-titanium alloy VST3553 thickness Ho=20 mm Chemical composition shown in table 1.

Table 1
The chemical composition of the alloy
Mass fraction of elements, %
AlMoVCrZrFeSiCN
3.184.825.20 2.62<0.0030.3340.0490.0090.014

The temperature of polymorphic transformation TPPdetermined by the method of trial sakaluk, it amounted to 795°C.

Molybdenum equivalent was calculated by the formula

Mo eq.=%Mo++%V/1,4+%+Cr/0,6+%Fe/0,5=4,82+3,71+4,36+0,66=13,56 wt.%.

Manufacturing technology sheets with thickness of 1.6 mm

1. The heating of blanks in an electric furnace at a setpoint temperature of 750°C, duration : 30 minutes

2. Rolling of billets to a thickness of 5 mm: Hi=20→5 mm with intermediate heat treatment with a duration of 10 min at intermediate thicknesses of the strips 15 mm, 10 mm, the total degree of deformation ε=75%.

2. Hardening 820°C, 20 minutes, cooling in water.

3. The first stage of cold rolling Hi=5 mm→2.55 mm, ε=49%, for 10 passes.

4. The second stage of rolling Hi=2,55 mm→1.6 mm, ε=37%, for 7 passes.

5. Heat treatment: hardening+aging.

The invention is illustrated by photographs.

Figure 1 shows the microstructure of hot-rolled steel H=5 mm, the average transverse size of the β-grain is in the center of 180-230 μm, on the periphery of 150 μm, which demonstrates the heterogeneity of the deformation in the cross section of the sheet. The primary α-phase, mostly globular, size of 1-2 microns. It forms clusters of darker color that the army is there about the heterogeneity of strain.

Figure 2 shows the microstructure of hot-rolled steel H=5 mm after quenching, consisting of the equilibrium of recrystallized grains with an average size of 65±13 μm, consisting of β-phase.

Figure 3 shows the microstructure of cold-rolled sheet H=2,55 mm after the first stage of cold rolling of steel. There was a decrease in the average size of the β-grains to 45±3 μm with increasing degree of anisotropy to 2. In the body of the grains observed a large number of slip lines and doubles. In longitudinal section, viewed slip lines, passing through several grains.

Figure 4 shows the microstructure of the cold rolled sheet, H=1.6 mm after the second stage of cold rolling of steel. A decrease in the average transverse size of the original β-grain to the Dβ≈30-40 microns with anisotropy 3-4, as well as increasing the number and density of slip lines and clones.

Figure 5 shows the microstructure of cold-rolled sheet H=1.6 mm, quenching from a temperature of 815°C. after holding for 15 minutes and aging at 550°C, holding for 2 hours. Excerpt 15 minutes at a temperature of β-region provides a fine-grained recrystallized structure of β-phase with an average grain size of 55±3 μm. Subsequent aging leads to the decomposition of the supersaturated solid solution with the formation of melkopuzyrchatoy α-phase, leading to a considerable is rochani alloy.

The mechanical properties of the sheets h=1.6 mm alloy VST3553 after various modes of aging are shown in table 2.

753
Table 2
Mechanical properties of cold rolled sheets h=1.6 mm alloy VST3553 after various modes of aging
Alongacross
σof 0.2, MPaσin, MPaδ, %σof 0.2, MPaσin, MPaδ, %
sheet # 4 - h=1.6 mm742823147728188,6
815°C 15 min water75981311,481010,8
(source)cf750,581812,7762,58149,7
815°C 15 min water+530°C 6 hours air124313223,4138314381
815°C 15 min water+
550°C for 6 hours in the air
114912105,6118912464,4
113412286,812171306a 4.9
cf1141,512196,21203176 4,65
815°C 15 min water+
580°C 6 hours air
106711306,5114912055,6
106611588,4116712334,6
cf106611447,45115812195,1

This method allows to obtain the fine quality sheets of high-strength pseudo-β-titanium alloys with low anisotropy of mechanical properties on standard manufacturing equipment.

A method of manufacturing thin sheets of pseudo-β-titanium alloys, including alloy smelting, obtaining slab, mechanical surface treatment of the slab, hot, warm, cold rolling, annealing and aging, characterized in that smelted pseudo-β-titanium alloy with an Al content in the alloy is not more than 5.0 wt.% and molybdenum ek is Valenta Mo eq.≥12 wt.%, calculated by the formula:
Mo eq. wt.% = %Mo + %Ta/4 + %Nb/3.3 + %W/2 + %V/1,4 + %Cr/0,6 + + %Fe/0,5 + %Ni/0,8 + %Mn/0,6 + %Co/0,9,
when this is received after the hot and warm rolling the rolled thickness 8-2 mm before cold rolling is subjected to tempering at TPP+(20-50°C) for 0.1-0.5 h and then cooled, the cold rolling is conducted respectively to the thickness of the sheet 6-1 mm single-phase β-able in two or more stages in several passes with the degree of deformation in a single pass 1-6% and the total degree of deformation at each stage of 30-50%, while between stages perform intermediate quenching mode, identical to the hardening of the tackle before cold rolling.



 

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