US20030223902A1 - Titanium alloy bar and method for manufacturing the same - Google Patents

Titanium alloy bar and method for manufacturing the same Download PDF

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Publication number
US20030223902A1
US20030223902A1 US10/418,252 US41825203A US2003223902A1 US 20030223902 A1 US20030223902 A1 US 20030223902A1 US 41825203 A US41825203 A US 41825203A US 2003223902 A1 US2003223902 A1 US 2003223902A1
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Prior art keywords
rolling
titanium alloy
type titanium
phase
sec
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US10/418,252
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English (en)
Inventor
Hideaki Fukai
Atsushi Ogawa
Kuninori Minakawa
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JFE Steel Corp
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JFE Steel Corp
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Assigned to JFE STEEL CORPORATION reassignment JFE STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: FUKAI, HIDEAKI, MINAKAWA, KUNINORI, OGAWA, ATSUSHI
Publication of US20030223902A1 publication Critical patent/US20030223902A1/en
Priority to US10/968,521 priority Critical patent/US20050051245A1/en
Abandoned legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals

Definitions

  • the present invention relates to a titanium alloy bar having excellent ductility, fatigue characteristics and formability, particularly to an ⁇ + ⁇ type titanium alloy bar, and to a method for manufacturing thereof.
  • titanium alloys are used as structural materials in the fields such as chemical plants, power generators, aircrafts and the like.
  • an ⁇ + ⁇ type titanium alloy occupies a large percentage of use because of its high strength and relatively good formability.
  • Products made of titanium alloys have various shapes such as sheet, plate, bar and so on.
  • the bar may be used as it is, or may be forged or formed in complex shapes such as a threaded fastener. Accordingly, the bar is requested to have excellent formability as well as superior ductility and fatigue characteristics.
  • FIG. 1 shows a typical manufacturing method of bar.
  • An ingot prepared by melting is forged to a billet as a base material for hot rolling.
  • the billet is hot rolled to a bar after reheated in a reheating furnace using a reverse rolling mill or tandem rolling mills. If necessary, the billet is intermediately reheated during hot rolling to compensate the temperature needed for subsequent hot rolling.
  • a titanium alloy bar particularly as for an ⁇ + ⁇ type titanium alloy bar
  • the temperature of billet increases during hot rolling owing to the adiabatic heat, which disturbs stable hot rolling and manufacturing of a titanium alloy bar having excellent ductility, fatigue characteristics and formability.
  • the finally hot rolled bar has ⁇ microstructure consisting mainly of acicular ⁇ phase, thus failing in attaining superior ductility and fatigue characteristics.
  • JP-A-59-82101 discloses a rolling method in which cross sectional area reduction rate of billet is specified to 40% or less per rolling pass in ⁇ region or in ⁇ + ⁇ region.
  • JP-A-58-25465 discloses a method in which billet is water cooled during hot rolling to suppress the temperature rise caused by the adiabatic heat.
  • Article 1 “Hot Bar Rolling of Ti-6Al-4V in a Continuous Mill (Titanium '92 Science and Technology)” describes that hot rolling speed is reduced to the lower limit of keeping performance of mill in order to suppress the adiabatic heat.
  • FIG. 3 shows a relationship between temperature and rolling time during hot rolling for Ti-6Al-4V alloy and Ti-4.5Al-3V-2Fe-2Mo alloy.
  • the heating temperature was 950° C. for the Ti-6Al-4V alloy, and 850° C. for the Ti-4.5Al-3V-2Fe-2Mo alloy.
  • the Ti-4.5Al-3V-2Fe-2Mo alloy has lower ⁇ transus than that of the Ti-6Al-4V alloy by 100° C. so that the heating temperature was reduced by the difference, thus selecting 850° C. as the heating temperature thereof.
  • the rolling was conducted using a reverse rolling mill and tandem rolling mills, while selecting the same conditions of rolling speed, reduction rate and pass schedule to both alloys.
  • the rolling speed of reverse rolling mill was 2.7 m/sec, and the rolling speed of tandem rolling mills was 2.25 m/sec at the final rolling pass where the rolling speed becomes the maximum for both alloys.
  • the rolling speeds are lower than the rolling speed of Article 1 (6 m/sec).
  • the cross sectional area reduction rate was selected to maximum 26% for both alloys.
  • the rolling was conducted at a sufficiently lower temperature than 1000° C. which is the ⁇ transus of the alloy, thus giving favorable structure.
  • the heating temperature was decreased by the magnitude of low ⁇ transus
  • the low temperature rolling resulted in increased deformation resistance and in increased adiabatic heat, so the temperature increased to a temperature region exceeding the ⁇ transus, thus failed to obtain favorable microstructure.
  • excellent ductility, fatigue characteristics and formability were not obtained.
  • rolling conditions such as rolling temperature, reduction rate and time between rolling passes shall be considered, as well as the rolling speed.
  • An object of the present invention is to provide a high strength titanium alloy bar having excellent ductility, fatigue characteristics and formability, and to provide a method of manufacturing thereof.
  • the object is attained by an ⁇ + ⁇ type titanium alloy bar consisting essentially of 4 to 5% Al, 2.5 to 3.5% V, 1.5 to 2.5% Fe, 1.5 to 2.5% Mo, by mass, and balance of Ti, and having 10 to 90% of volume fraction of primary ⁇ phase, 10 ⁇ m or less of average grain size of the primary ⁇ phase, and 4 or less of aspect ratio of the grain of the primary ⁇ phase on the cross sectional plane parallel in the rolling direction of the bar.
  • the ⁇ + ⁇ type titanium alloy bar can be manufactured by a method comprising the step of hot rolling an ⁇ + ⁇ type titanium alloy consisting essentially of 4 to 5% Al, 2.5 to 3.5% V, 1.5 to 2.5% Fe, 1.5 to 2.5% Mo, by mass, and balance of Ti, while keeping the surface temperature thereof to ⁇ transus or below.
  • FIG. 1 shows a typical method for manufacturing a bar.
  • FIG. 2 shows a process for hot rolling a bar.
  • FIG. 3 shows a relationship between temperature and rolling time during hot rolling for Ti-6Al-4V alloy and Ti-4.5Al-3V-2Fe-2Mo alloy.
  • FIG. 4 shows a relationship between average grain size of primary ⁇ phase and total elongation measured by high temperature tensile test.
  • FIG. 5 shows a relationship between average grain size of primary ⁇ phase and fatigue strength after 10 8 cycles observed in fatigue test.
  • FIG. 6 shows temperature changes with time at surface and center.
  • FIG. 7 shows a relationship between cross sectional area and temperature difference between surface and center.
  • the inventors of the present invention studied the microstructure of ⁇ + ⁇ type titanium alloy bar to provide excellent ductility, fatigue characteristics and formability, and found the followings.
  • the ⁇ + ⁇ type titanium alloy consists of primary ⁇ phase and transformed ⁇ phase. If, however, the alloy contains very large volume fraction of ⁇ phase that has HCP structure having little sliding system, or contains very large volume fraction of transformed ⁇ phase containing acicular ⁇ phase, formability and ductility deteriorate. Consequently, the volume fraction of primary ⁇ phase is specified to a range of from 10 to 90%. If the volume fraction of ⁇ phase and of ⁇ phase is equal or close to each other at reheating stage before hot rolling, the formability becomes better, so the volume fraction of primary ⁇ phase is preferably between 50 and 80%.
  • FIG. 4 shows a relationship between average grain size of primary ⁇ phase and total elongation measured by high temperature tensile test.
  • FIG. 5 shows a relationship between average grain size of primary ⁇ phase and fatigue strength after 10 8 cycles observed in fatigue test.
  • Forging a bar induces rough surface on a free deforming plane not contacting with a mold due to the shape of grains, or due to the aspect ratio of the grains.
  • the grains of bar tend to be elongated in the rolling direction.
  • elongated grains appear on a side face of the bar that becomes a free deforming plane. Therefore, it is necessary to avoid excessive increase in the aspect ratio during forging, more concretely to regulate the aspect ratio not exceeding 4 for the grains of the primary ⁇ phase on a cross section parallel in the rolling direction of the bar in order to prevent rough surface on the bar after forged.
  • a high strength titanium alloy bar having excellent ductility, fatigue characteristics and formability is obtained when the volume fraction of the primary ⁇ phase is between 10 and 90%, preferably between 50 and 80%, the average grain size in the primary ⁇ phase is 10 ⁇ m or less, preferably 6 ⁇ m or less, and further the aspect ratio of grains in the primary ⁇ phase is 4 or less.
  • the ⁇ + ⁇ type titanium alloy bar having above-described microstructure should consist essentially of 4 to 5% Al, 2.5 to 3.5% V, 1.5 to 2.5% Fe, 1.5 to 2.5% Mo, by mass, and balance of Ti. The reasons to limit the content of individual elements are described below.
  • Aluminum is an essential element to stabilize the ⁇ phase and to contribute to the strength increase. If the Al content is below 4%, high strength cannot fully be attained. If the Al content exceeds 5%, ductility degrades.
  • Vanadium is an element to stabilize the ⁇ phase and to contribute to the strength increase. If the V content is below 2.5%, high strength cannot fully be attained, and ⁇ phase becomes unstable. If the V content exceeds 3.5%, range of workable temperature becomes narrow caused by the lowered ⁇ transus, and cost increases.
  • Molybdenum is an element to stabilize the ⁇ phase and to contribute to the strength increase. If the Mo content is below 1.5%, high strength cannot fully be attained, and ⁇ phase becomes unstable. If the Mo content exceeds 2.5%, range of workable temperature becomes narrow-caused by the lowered ⁇ transus, and cost increases.
  • Iron is an element to stabilize the ⁇ phase and to contribute to the strength increase. Iron rapidly diffuses to improve formability. If, however, the Fe content is below 1.5%, high strength cannot fully be attained, and the ⁇ phase becomes unstable, which results in failing to attain excellent formability. If the Fe content exceeds 2.5%, range of workable temperature becomes narrow caused by the lowered ⁇ transus, and degradation in characteristics is induced by segregation.
  • the ⁇ + ⁇ type titanium alloy bar according to the present invention may be manufactured by hot rolling an ⁇ + ⁇ type titanium alloy having above-described composition while adjusting the conditions of heating temperature, rolling temperature range, reduction rate, rolling speed, time between passes, and other variables to suppress the temperature rise caused by the adiabatic g heat, namely to keep the surface temperature of the alloy not exceeding the ⁇ transus.
  • the method comprises the steps of: heating an ⁇ + ⁇ type titanium alloy having ⁇ transus of T ⁇ ° C.
  • the reason of heating the surface before hot rolling in the range of from (T ⁇ 150) to T ⁇ ° C. is the following. If the surface temperature before hot rolling is below (T ⁇ 150) ° C., the decrease in temperature during the final rolling stage becomes significant to increase crack susceptibility and deformation resistance. And, if the surface temperature before hot rolling exceeds T ⁇ ° C., the microstructure of the bar becomes ⁇ microstructure consisting mainly of acicular ⁇ phase, which deteriorates ductility and formability.
  • the reason of limiting the surface temperature during hot rolling to the range of from (T ⁇ 300) to (T ⁇ 50) ° C. is the following.
  • the hot formability deteriorates to induce problems such as cracking. And, if the surface temperature during hot rolling exceeds (T ⁇ 50) ° C., the temperature rise caused by the adiabatic heat induces coarse grains and formation of acicular phase.
  • the reason of limiting the finish surface temperature immediately after the final rolling pass to the range of from (T ⁇ 300) and (T ⁇ 100) ° C. is the following. If the finish temperature thereof is below (T ⁇ 300) ° C., the crack susceptibility and the deformation resistance increase. And, if the finish temperature thereof exceeds (T ⁇ 100) ° C., grains become coarse.
  • the hot rolling is conducted by plurality of rolling passes. To prevent temperature rise caused by the adiabatic heat, it is preferable to keep the reduction rate not more than 40% per rolling pass.
  • the hot rolling is conducted by a reverse rolling mill, it is preferable to limit the rolling speed not more than 6 m/sec to prevent the temperature rise caused by the adiabatic heat.
  • the hot rolling is conducted by tandem rolling mills, it is preferable to limit the rolling speed not more than 1.5 m/sec.
  • the surface of the alloy receives temperature drop to some extent before entering succeeding pass even if a temperature rise exists caused by the adiabatic heat.
  • the temperature drop at center section of the alloy is small so that a large temperature difference appears between the surface and the center of the alloy.
  • the alloy is subjected to succeeding rolling pass before lowering the temperature of the center, which further increases the temperature owing to the adiabatic heat. If the phenomenon sustains, the center is hot rolled at higher temperature than the initial temperature. Consequently, the center of alloy having large diameter is required to be cooled with sufficient time between rolling passes.
  • the inventors of the present invention made a detailed study on the temperature difference between the surface and the center, and derived the finding described below.
  • the temperature difference significantly increases at or above 3500 mm 2 of cross sectional area of alloy normal to the rolling direction thereof.
  • S mm 2 of the cross sectional area securing the time before entering succeeding rolling at 0.167 ⁇ S 1/2 sec or more can make the temperature difference small and is favorable in manufacturing a bar having homogeneous characteristics.
  • the hot rolling is carried out while keeping the surface temperature of the alloy to ⁇ transus or below, thus there is a possibility for the surface temperature to decrease to a lower than the required rolling temperature range during hot rolling depending on the time between rolling passes and on the diameter of alloy.
  • reheating the alloy may be given using a high frequency heating unit or the like.
  • Materials having 125 square mm size were prepared by cutting each of the base alloy A01 (having composition within the range of the present invention) and the base alloy A02 (having composition outside the range of the present invention), both of which are ⁇ + ⁇ type titanium alloy having respective chemical compositions given in Table 1.
  • the materials are hot rolled using a caliber rolling mill under respective conditions (B01 through B18) given in Table 2 to produce bars having 20 mm and 50 mm in diameter, respectively.
  • ⁇ denotes the time between rolling passes of 0.167 ⁇ S 1/2 or more for all the rolling passes under each rolling condition
  • X denotes the time between rolling passes of less than 0.167 ⁇ S 1/2 .
  • Table 3 through Table 20 give cross sectional area S of alloy, reduction rate, 0.167 ⁇ S 1/2 , time between rolling passes, surface temperature, and rolling speed on each rolling pass under each rolling condition.
  • R in the table signifies a reverse rolling mill, and T signifies tandem rolling mills.
  • optical microstructure examination was performed at the center of the bar and at the position of quarter of diameter (1 ⁇ 4 D) to determine grain size of primary ⁇ phase, volume fraction of the grains, and aspect ratio of the grains on a cross section parallel in the rolling direction.
  • bars produced using A02 having chemical composition outside the range of the present invention under the rolling conditions of B10 and B12 could not attain satisfactory ductility and fatigue characteristics because the grain size in the primary ⁇ phase exceeded 10 ⁇ m, though the adiabatic heat was suppressed because the rolling conditions were within the range of the present invention.
  • Cylindrical specimens having 8 mm in diameter and 12 mm in height were cut from the center section in radial direction of bars produced in Example 1 under the rolling conditions B01 through B18, respectively.
  • the specimens were heated to 800° C. and were compressed to 70%. After the compression, the occurrence of cracks and of rough surface on the surface of each specimen was inspected to give evaluation of hot forging property.
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US20070212251A1 (en) * 2004-04-09 2007-09-13 Hiroaki Otsuka High Strength AlphaType Titanuim Alloy
US20110179848A1 (en) * 2008-10-22 2011-07-28 Ruslan Zufarovich Valiev Nanostructured commercially pure titanium for biomedicine and a method for producing a rod therefrom
CN111545574A (zh) * 2020-05-20 2020-08-18 攀钢集团攀枝花钛材有限公司江油分公司 Ta15热轧板材组织控制的方法
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US7837812B2 (en) 2004-05-21 2010-11-23 Ati Properties, Inc. Metastable beta-titanium alloys and methods of processing the same by direct aging
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US10053758B2 (en) 2010-01-22 2018-08-21 Ati Properties Llc Production of high strength titanium
US9255316B2 (en) 2010-07-19 2016-02-09 Ati Properties, Inc. Processing of α+β titanium alloys
US8613818B2 (en) 2010-09-15 2013-12-24 Ati Properties, Inc. Processing routes for titanium and titanium alloys
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US20070212251A1 (en) * 2004-04-09 2007-09-13 Hiroaki Otsuka High Strength AlphaType Titanuim Alloy
US8562763B2 (en) * 2004-04-09 2013-10-22 Nippon Steel & Sumitomo Metal Corporation High strength α+β type titanuim alloy
EP1783235A1 (en) * 2004-07-30 2007-05-09 Public Stock Company "VSMPO-AVISMA Corporation" Titanium-based alloy
EP1783235A4 (en) * 2004-07-30 2008-02-13 Public Stock Company Vsmpo Avi ALLOY ON TITANIUM BASE
US20080181809A1 (en) * 2004-07-30 2008-07-31 Public Stock Company "Vsmpo-Avisma Corporation Titanium-Based Alloy
US20110179848A1 (en) * 2008-10-22 2011-07-28 Ruslan Zufarovich Valiev Nanostructured commercially pure titanium for biomedicine and a method for producing a rod therefrom
US8919168B2 (en) * 2008-10-22 2014-12-30 Ruslan Zufarovich Valiev Nanostructured commercially pure titanium for biomedicine and a method for producing a rod therefrom
CN111545574A (zh) * 2020-05-20 2020-08-18 攀钢集团攀枝花钛材有限公司江油分公司 Ta15热轧板材组织控制的方法
CN114535343A (zh) * 2022-04-26 2022-05-27 西部宝德科技股份有限公司 钛纤维制备方法

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TWI293987B (ru) 2008-03-01
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JP4013761B2 (ja) 2007-11-28
RU2003126234A (ru) 2005-03-10
EP1382695A4 (en) 2004-08-11
EP1382695A1 (en) 2004-01-21
RU2259413C2 (ru) 2005-08-27
WO2002070763A1 (fr) 2002-09-12

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