US20060062685A1 - Beta type titanium alloy and manufacturing method thereof - Google Patents

Beta type titanium alloy and manufacturing method thereof Download PDF

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US20060062685A1
US20060062685A1 US11/006,766 US676604A US2006062685A1 US 20060062685 A1 US20060062685 A1 US 20060062685A1 US 676604 A US676604 A US 676604A US 2006062685 A1 US2006062685 A1 US 2006062685A1
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alloy
mass
pickling
titanium alloy
type titanium
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Wataru Takahashi
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Nippon Steel Corp
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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
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/10—Other heavy metals
    • C23G1/106—Other heavy metals refractory metals
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/12—Light metals

Definitions

  • the present invention relates to a ⁇ type titanium alloy that has excellent deformability, in a solution-treated state, with a low deformation resistance during cold working, and also has a high strength after aging, and a method of manufacturing the alloy.
  • Titanium alloys generally have high strength at low density with the higher specific strength (strength/density) among the practical metallic materials and are excellent in corrosion resistance. Therefore, titanium alloys are used for aircraft and automobile parts, medical equipments, glass frames, golf clubs and tableware. With this extension, further improvement in property and reduction in cost are strongly demanded for the titanium alloys.
  • the titanium alloys are roughly classified to ⁇ type, ⁇ type and ⁇ + ⁇ type: ⁇ type has a hexagonal close packed (hcp) microstructure, ⁇ type has a body centered cubic (bcc) microstructure, and ⁇ + ⁇ type has both of hcp and bcc microstructures.
  • ⁇ type has a hexagonal close packed (hcp) microstructure
  • ⁇ type has a body centered cubic (bcc) microstructure
  • ⁇ + ⁇ type has both of hcp and bcc microstructures.
  • a pure titanium metal and a titanium alloy with a small amount of other elements such as Al correspond to ⁇ type.
  • a Ti-6Al-4V alloy which is well known as a high strength alloy and used in aircrafts parts, corresponds to ⁇ + ⁇ type.
  • a ⁇ type alloy includes elements that stabilize a ⁇ phase more than an ⁇ + ⁇ type alloy.
  • titanium alloys are generally poor in cold workability, their manufacturing cost is high.
  • a pure titanium metal with a low oxygen content which is relatively satisfactory in cold workability, is hardly applicable to parts requiring high specific strength, because of the insufficient strength of its molded product.
  • a Ti-6Al-4V alloy with high strength that is most representative of a titanium alloy has extremely poor deformability at room temperature. Therefore, it can only be formed to an intended shape by hot working or by cutting, which causes an increased manufacturing cost.
  • ⁇ type titanium alloy having a body centered cubic crystalline structure.
  • the ⁇ type titanium alloy include a Ti-3Al-8V-6Cr-4Mo-4Zr alloy and a Ti-15V-3Cr-3Al-3Sn alloy. These ⁇ type alloys have preferable characteristics, which can be used for precision parts. Because ⁇ type alloys are highly deformable in cold working when laid in a single ⁇ phase by solution treatment, they can be enhanced in strength by precipitating an ⁇ -phase by aging treatment after working.
  • conventional ⁇ type titanium alloys have satisfactory deformability but high deformation resistance. Accordingly, in cold forging, for example, a metal mold such as a die or punch is frequently cracked or chipped even when infrequently used. Further, abrasive wear of a roll is serious in cold rolling for manufacturing a work piece, and seizure is apt to occur in case of cold wire drawing.
  • Ti-20V-4Al-1Sn alloy As an invention which solves such problems, an alloy consisting of V: 15 to 25%, Al: 2.5 to 5%, Sn:0.5 to 4%, oxygen: not more than 0.12%, and the balance of Ti and impurities (hereinafter referred to as “Ti-20V-4Al-1Sn alloy” for short) are disclosed in Japanese Patent No. 2669004.
  • This alloy has not only a low deformation resistance with low strength in a solution-treated state, but also has high strength after the aging treatment, although its deformability is substantially equal to those of the conventional ⁇ type titanium alloys.
  • the alloy disclosed above is prepared and molded to various parts, the deformability in the ⁇ type alloy is not always stable, and the deformation resistance is unstable. Further, the strength after aging is largely fluctuated.
  • the first objective of the present invention is to provide a titanium alloy capable of easily and stably realizing the characteristics of excellent cold workability in a solution-treated state and high strength after an aging treatment.
  • the present invention also has a second objective, which is to provide a pickling method for reducing the H (hydrogen) content during manufacturing of the titanium alloy.
  • the ⁇ type titanium alloy has a metastable ⁇ phase that is a high temperature phase of titanium, which is quenched and kept at room temperature.
  • the stabilizing elements for ⁇ phase are V, Mo, Nb, Ta, Cr, Fe, Mn, and the like.
  • V and Mo are particularly given as relatively inexpensive elements, which are capable of minimizing the hardening, by solution treatment with a minimized bad effect on workability, while providing high strength by aging.
  • Mo is easy to segregate because of its high melting point, and the addition of Mo leads to an increase in deformation resistance during hot or cold working. Therefore, the Ti-20V-4Al-1Sn alloy, in addition to selecting not Mo but V, is proposed to add Al in order to increase the strength in aging treatment, and also add Sn in order to suppress solid solution hardening.
  • this alloy has the problem with cold workability and age strengthen ability which cannot be always stably obtained.
  • the present inventor made various examinations to determine and respond to the cause of this problem. With respect to V, Al and Sn that are the main elements of this alloy, the cold workability and the age strengthability were examined while varying the ranges of their content. However, no remarkable influence was observed on a characteristic change by the variation of the main elements of this alloy, although its effect appears close to the limit of the content ranges.
  • O Oxygen
  • H Hydrogen
  • Fe which is a ⁇ phase stabilizing element, enhances the strength of the solution-treated alloy and results in increasing the deformation resistance. It is not preferable to include a large amount of Fe.
  • C forms a carbide precipitate and results in significantly reducing the deformation resistance and deformability.
  • N which is dissolved in ⁇ phase in an amount of about 1%, causes a significant reduction in ductility, which reduces the deformability.
  • a ⁇ type Ti-20V-4Al-1Sn alloy includes elements that cannot be easily reduced within the ranges defined in JIS even if the impurities are restricted within these ranges; and that it includes elements whose contents have a significant influence on the characteristics of this alloy even if they are restricted within the standard. This may be because the Ti-20V-4Al-1Sn alloy is a ⁇ type, in contrast with a type titanium alloys and ⁇ + ⁇ type titanium alloys, defined in the JIS.
  • a ⁇ type alloy absorbs hydrogen much more easily than a type or ⁇ + ⁇ type alloys.
  • descaling must be carried out after hot rolling in order to obtain a satisfactory surface.
  • the method of mechanically grinding the surface could be adopted for the descaling, the speed and the yield are low. Accordingly, it is general to carry out a pickling with fluoric acid or nitric fluoric acid.
  • a Ti-20V-4Al-1Sn alloy which is made of ⁇ type by a solution treatment for cold rolling, hydrogen is absorbed in an amount largely exceeding the upper limit of the amount defined by the JIS during the pickling. The variation of the pickling condition does not result in an effective reduction of hydrogen content. Since the above alloy includes elements that increase the oxidized scales, the absorption of hydrogen is apt to increase when the pickling time is prolonged.
  • a ⁇ type alloy can be improved in strength by performing an aging treatment after working into a desired shape.
  • the hydrogen included in the alloy remarkably disturbs the age hardening and results in prolonging the aging treatment time or failing to produce the intended strength.
  • the hydrogen reduces the ductility of the alloy, which deteriorates the workability and seriously deteriorates the toughness as well.
  • heating at a high temperature in a vacuum can perform dehydrogenation, this method is not practical because it requires an excessive time for treatment, which causes aging.
  • the inventor conceived that, even if the alloy plate after pickling might inevitably include hydrogen absorbed during pickling, the deterioration in aging speed and the reduction in workability and toughness, caused by the absorbed hydrogen during pickling, can be recovered by suppressing the amounts of other impurity elements such as O, Fe, N and C.
  • the inventor could stably obtain an excellent Ti-20V-4Al-1Sn alloy by limiting the respective contents of the elements O, Fe, N and C as well as H.
  • the gist of the present invention is to provide with titanium alloys described in the following (1) to (3), and to provide with methods of manufacturing titanium alloys described in the following (4) and (5).
  • a ⁇ type titanium alloy characterized by consisting of, by mass %, V: 15 to 25%, Al: 2.5 to 5%, Sn: 0.5 to 4%, O (Oxygen): not more than 0.20%, H: not more than 0.03%, Fe: not more than 0.40%, C: not more than 0.05% and N: not more than 0.02%, and the balance Ti and impurities.
  • a ⁇ type titanium alloy characterized by consisting of, by mass %, V: 15 to 25%, Al: 2.5 to 5%, Sn: 0.5 to 4%, O (Oxygen): not more than 0.12%, H: not more than 0.03%, Fe: not more than 0.15%, C: not more than 0.05% and N: not more than 0.02%, and the balance Ti and impurities.
  • a ⁇ type titanium alloy characterized by consisting of, by mass %, V: 15 to 25%, Al: 2.5 to 5%, Sn: 0.5 to 4%, O (Oxygen): not more than 0.20%, H: not more than 0.03%, Fe: not more than 0.40%, C: not more than 0.05% and N: not more than 0.02%, and less than 3% of at least one element selected from Zr, Mo, Nb, Ta, Cr, Mn, Ni, Pd and Si, and the balance Ti and impurities.
  • a method of manufacturing a ⁇ type titanium alloy characterized by comprising the following steps (a) to (c):
  • FIG. 1 is a view showing the influence of hydrogen content on the change in hardness of a titanium alloy by aging.
  • the reason of limiting the content of elements of a ⁇ type titanium alloy, according to the present invention, is as follows.
  • the content of each component is represented by mass %.
  • V is an important element for stabilizing ⁇ phase and also making the alloy to a single ⁇ phase structure at room temperature.
  • a martensitic structure is generated during the solution treatment by quenching, such as water-cooling from a high temperature where ⁇ phase exists, and significantly deteriorates the cold workability.
  • quenching such as water-cooling from a high temperature where ⁇ phase exists
  • significantly deteriorates the cold workability When it exceeds 25%, the age hardenability of a ⁇ type alloy is deteriorated and this results in extending the time required for the aging treatment. An insufficient strength could sometimes be obtained even after the aging treatment.
  • the deformation resistance in cold working of the alloy is increased.
  • a ⁇ type alloy is finally reinforced by the aging treatment.
  • Al is included therein in order to attain a sufficient increase in strength.
  • Al also effects the suppressing precipitation of ⁇ phase that makes the alloy brittle and promotes the precipitation of ⁇ phase during the aging treatment. Such effects are insufficient with less than 2.5%, of Al. When it exceeds 5%, the hardness in ⁇ state is increased, and, consequently reduces the cold workability. Accordingly, the content of Al is set 2.5 to 5%.
  • Sn has the same effect as the above Al. Sn does not increase hardness in ⁇ state more than Al. Sn that can suppress the increase in deformation resistance can also substitute a part of Al. Since such an effect of Sn is reduced as the content of Sn is smaller, the content is set to 0.5% or more. On the other hand, since the hardness of a ⁇ type alloy is increased as the content of Sn becomes larger, the content is set up to 4%.
  • O deteriorates the deformability of the alloy causing cracking during the cold working with a strong rolling reduction and increases the deformation resistance.
  • the content of Oxygen limited to not more than 0.20%, thereby making undesirable effects inconspicuous. It is more desirably set to not more than 0.12%.
  • H not only retards the precipitation of ⁇ phase during aging treatment but also reduces the age strengthening. It also deteriorates the ductility and toughness. Therefore, a smaller amount of H is preferred.
  • the ⁇ type Ti-20V-4Al-1Sn alloy easily absorbs hydrogen not only during the pickling process but also outside of pickling process. Particularly when producing a thin plate of the alloy, it is difficult to reduce the content of H to an amount below 0.005%, because of descaling by pickling. Accordingly, the upper value is limited to 0.03%, which does not make a serious impact. A content of not more than 0.01% is desirable. The lower limit value is not particularly determined.
  • a hot rolled plate 5 mm thick of an alloy having a chemical composition consisting of V: 20.0%, Al: 3.2%, Sn: 1.0%, O: 0.11%, H: 0.015%, Fe: 0.10%, C: 0.01%, N: 0.01%, and the balance Ti and impurities was solution-treated, followed by steel shot blasting. Thereafter, the aging treatment was carried out at 450° C., where the hydrogen content varied by varying the pickling time.
  • the solution treatment comprises heating at 850° C. for 5 minutes in the atmosphere followed by cooling with water.
  • the alloy When the hydrogen content is 0.015% or 0.025%, as is apparent from FIG. 1 , the alloy is saturated with an intended hardness by a 12-hour aging treatment. In contrast, when the hydrogen content is 0.040% or 0.065%, the alloy does not reach a sufficient hardness even if it is treated for 20 hours. These alloys require an extended aging treatment, exceeding 20 hours, if they reach the same hardness as obtained in the alloy with a hydrogen content of 0.015% or 0.025%. When the hydrogen content is 0.100%, the alloy can be scarcely hardened as shown in FIG. 1 .
  • the content of H in the alloy is desirably suppressed to 0.03% or less.
  • Fe stabilizes the ⁇ phase and retards the age hardening as well as hydrogen and further increases the deformation resistance, the smaller amount is better. Since hydrogen is inevitable included as described above, the upper limit of the content of Fe is set up to 0.40%, which never causes a remarkable increase in deformation resistance. The further desirable Fe content is not more than 0.15%.
  • the upper limit of the content is set up to 0.05%, which never causes a remarkable reduction in deformability.
  • the content of further desirably is not more than 0.03%.
  • the impure elements O, Fe, C and N are derived from a sponge titanium which is a raw material, and increased in the following melting or high temperature heating processes of the alloy. Therefore, the contents of the impure elements in the alloy are never reduced to less than the level of the contents in the raw material. Accordingly, it is necessary to select a sponge titanium with smaller contents of impurities and reduce the contamination in the manufacturing process as much as possible.
  • the alloy may contain, in addition to V, Al and Sn, less than 3% of at least one element selected from a group consisting of Zr, Mo, Nb, Ta, Cr, Mn, Ni, Pd and Si within a range that never impairs the working effect of the present invention.
  • These elements contribute to an improvement in the strength of the alloy after aging treatment without impairing the deformability and other characteristics of the alloy of the present invention.
  • the desirable content of each element is 0.1-1%.
  • the average grain size in the alloy made to ⁇ type by solution treatment is desirably 20-130 ⁇ m. With less than 20 ⁇ m, the deformation resistance is increased which makes a working difficult. With larger than 130 ⁇ m, the alloy tends to crack during working because the deformability is reduced, and this causes a lack of strength even after aging.
  • the aging treatment is usually carried out at a temperature of 400 to 500° C. By setting the grain size of ⁇ phase to the above range, the ⁇ phase precipitated by aging can have a grain size in a preferable range of 0.02 to 0.2 ⁇ m, which provides excellent strength and toughness.
  • the desirable average grain size can be obtained by using the manufacturing condition described below.
  • the alloy plate of the present invention is manufactured by forging an alloy having a required chemical composition, hot rolling it followed by cold rolling, and then performing a solution treatment.
  • the manufacturing condition is desirably set as follows.
  • the heating temperature in the hot rolling is preferably set from 900 to 1050° C. If the temperature is lower than 900° C., the deformation resistance during hot working is too large a load on the working facility, and also if the temperature exceeds 1050° C., the oxidation during heating causes not only a reduction in yield but also a roughing of the crystal grains, which affects the alloy characteristics after working.
  • the temperature during hot working is desirably within the range of 750 to 1050° C. persisting the temperature of not less than ⁇ transits, although there might be a drop in the temperature during the non-heating time between deformation works, and an increase in temperature caused by working heat.
  • a quenching such as water cooling at an average cooling rate of not less than 30° C./min is preferably performed, because a slow cooling causes precipitation and hardening of ⁇ phase and makes it impossible to uncoil the coiled plate of the alloy.
  • the alloy is solution-treated for descaling through a continuous pickling and annealing device.
  • the solution treatment that is ⁇ treatment, desirably comprises heating to 750-950° C. followed by water-cooling, because a temperature lower than 750° C. might be insufficient to form the single ⁇ phase, and a temperature exceeding 950° C. might cause roughing of the crystal grains.
  • the heating time of the solution treatment is preferably 1 to 30 minutes in order to sufficiently solution-treat the alloy and avoid useless heating.
  • the average grain size becomes smaller than 20 ⁇ m, therefore, it is desirable to avoid such a temperature.
  • the average grain size could be smaller than 20 ⁇ m, which is obtained by setting the hot working temperature to the ⁇ transits or lower and the temperature in the continuous pickling and annealing device close to 750° C.
  • the average grain size of 10 ⁇ m might be available.
  • the ⁇ case means a hard and brittle oxygen rich layer formed by intrusion of oxygen to the surface of the ⁇ -titanium alloy.
  • a preferred example of a pickling condition is mentioned in the following of (1) to (3):
  • the shot blasting of item (1) above is not always necessary. However, if a light shot blasting is performed, the picking time might be shortened because the oxidized scales are thereby cracked.
  • the aqueous solution of item (2) above may include, in addition to 3 to 40 mass % of HF, a reducing agent such as nitric acid and hydrogen peroxide, which suppresses absorption of hydrogen.
  • a waste solution which is produced in a semiconductor manufacturing process is also available, which includes a reducing agent such as acetic acid in addition to fluoric acid.
  • the aqueous solution of item (3) above could include a reducing agent such as hydrogen peroxide and acetic acid in addition to 3 to 6 mass % of HF and 5 to 20 mass % of HNO 3 .
  • a reducing agent such as hydrogen peroxide and acetic acid in addition to 3 to 6 mass % of HF and 5 to 20 mass % of HNO 3 .
  • the pickling of item (2) above is carried out first in an aqueous solution that contains mainly fluoric acid.
  • the pickling by fluoric acid is effective to remove the oxidized scales, but the absorption of hydrogen is excessive especially during the removal of the ⁇ case by pickling. Accordingly, the pickling of item (2) above is should be limited within 10 minutes in order to leave the a case, and then the pickling of item (3) above is successively carried out.
  • the oxygen rich layer formed under the oxidized scales, that is the ⁇ case can be efficiently removed by the nitric fluoric acid solution.
  • the pickling by the nitric fluoric acid solution has an advantage of little absorption of hydrogen due to the reducing effect of nitric acid, the time required for the removal is extended when the amount of oxidized scales is excessive, whereby local corrosion might progress and lead to a rough surface. Therefore, after the pickling of item (2) above by the aqueous solution mainly containing fluoric acid, the pickling of item (3) above by the nitric fluoric acid solution is carried out. However, since the absorption of hydrogen is also increased, even with the nitric fluoric acid, if the treatment is extended over a long time, the pickling is preferably carried out within 20 minutes.
  • the temperature is set from 20 to 70° C., because, at a temperature lower than 20° C., the removal of the scales or oxygen rich layer requires too much time, and because, at a temperature exceeding 70° C., the surface is remarkably roughed and evaporation of the acid is also increased.
  • a concentration of HF of less than 3 mass %, the reaction speed is too slow in both the solutions of the pickling of items (2) and (3) above.
  • it exceeds 40 mass % the reaction becomes too severe in the solution of the pickling of item (2) above, which may cause a danger, and also it is difficult to make an adjustment of corrosion quantity.
  • the cold working is desirably carried out at a reduction rate of 30% or more to produce a grain size of 130 ⁇ m or less by ⁇ treatment after working.
  • the rolling reduction rate is 30% or more
  • the reduction rate of area is 30% or more.
  • this alloy has its own upper limit of reduction rate that is caused by its own work hardenability of the alloy.
  • the ⁇ phase treatment after cold rolling is preferably performed by the solution treatment of heating in a temperature of 750 to 900° C. and then cooling at the cooling rate of air cooling or a more rapid cooling rate, which simultaneously performs annealing.
  • the reason why the heating temperature of 750-900° C. is desirable is that the ⁇ phase treatment is insufficient when the temperature is too low, and the grain size becomes rough when the temperature is too high, similarly to the case of the heating temperature range in the above-mentioned solution treatment before cold working. Since an excessively short or long heating time similarly causes an insufficient ⁇ phase treatment or roughing of the grain size, the heating time is preferably set from 1 to 30 minutes.
  • the heating in the solution treatment after cold rolling is desirably carried out in vacuum or in inert gas such as highly pure Ar or He.
  • a heating in a condition causing oxidation of the surface requires removal of the oxidized film, or a pickling by nitric fluoric acid for descaling.
  • the hydrogen content in the alloy exceeds the upper limit by intrusion of hydrogen to the alloy.
  • the solution treatment is usually carried out prior to cold rolling.
  • the alloy could be worked into the required shape in a cold rolled state and then aged. In this case, a highly strong part with minute crystal grains can be formed.
  • the aging treatment for reinforcing the ⁇ type alloy of the present invention is preferably carried out at 400-500° C. Although the aging precipitates a minute ⁇ phase, the age hardening requires an excessive time at a temperature lower than 400° C., and therefore, the ductility after age hardening is extremely reduced. As a result, the toughness deteriorates and the ⁇ phase becomes rough at a temperature higher than 500° C. which reduces the strength.
  • Titanium alloys which have compositions shown in Tables 1 and 2 were melted in a vacuum arc melting furnace with a water-cooled copper crucible consumable-electrode, and produced ingots which are 140 mm in diameter.
  • the ingots were heated to 1000° C. followed by hot forging to form hot rolled materials 50 mm in thickness and 150 mm in width. These materials were heated to 950° C. followed by hot rolling, and the rolling ended at 800° C. They were immediately cooled to 300° C. at an average cooling rate of 200° C./min by a water spray cooling method, and allowed to stand cool.
  • the resulting hot rolled plates were subjected to a solution treatment of “heating at 880° C. for 10 minutes followed by water cooling”.
  • the hydrogen amounts shown in the tables are values obtained by analyzing samples after the cold rolling.
  • the deformability of the solution treated ⁇ type alloy was determined from the state of edge cracking caused by cold rolling.
  • Test Nos. 20, 21 and 30 were dipped for 15 minute, instead of 4 minutes, in an aqueous solution of 30° C. of fluoric acid including 4 mass % of HF in order to increase the hydrogen amount.
  • Test Nos. 1 to 24 has the same main composition as that of the Ti-20V-4Al-1Sn alloy. Compared with Test Nos. 20 to 33, Test Nos. 1 to 19 are excellent in cold workability and also in strength and elongation after aging. This is the effect caused by limiting the contents of H, Fe, C and N which were not controlled in the past, showing the importance of minimizing the contents of these elements.
  • the titanium alloy according to the present invention can be suitably used as not only a material for industrial equipment, such as an automotive valve gear member or aerospace plane parts, but also as a material for daily commodities, such as a glass frame, or athlete equipment such as a golf club head.
  • a cold rolled product of a titanium alloy having a stable quality, can be manufactured.
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