TW593706B - Method for processing beta titanium alloys - Google Patents

Abstract

An embodiment of the present invention comprises processing a beta titanium alloy by a method including the steps of cold working the alloy and then direct aging the alloy for a total aging time of less than 4 hours. Any beta titanium alloy may be used in the method, for example, Ti-38-644 alloy. The method may include fabricating the alloy into an article of manufacture such as, for example, a bar, wire, a coil spring. The method may be utilized to produce articles with high tensile strength while retain ductility. Another embodiment of the present invention is a method for producing a spring or other article of manufacture from a beta titanium alloy. The beta titanium alloy may be, for example, the alloy comprising, by weight, 3.0% to 4.0% aluminum, 7.5 to 8.5% vanadium, 5.5 to 6.5% chromium, 3.5 to 4.5% molybdenum, 3.5 to 4.5% zirconium, and titanium. The alloy may be hot worked, cold worked to provide a 5% to 60% reduction, and direct aged for a total time of less than 4 hours. Any cold working technique may be used in embodiments of the present invention. Useful cold working techniques include, but are not limited to, compression processes, drawing, wire drawing, tube drawing, deep drawing, rolling, contour forming, extruding, cold heading, swaging, coining, forging, tension processes, stretch forming, and spinning.

Description

593706 Field of the invention The present invention relates to titanium alloy processing methods, especially to Θ titanium alloy. The method of the present invention includes cold working / 9 titanium metal and direct aging of the alloy in less than 4 hours. 丨 Description of the invention | The unique properties of titanium alloys allow It is used in applications that require high corrosion resistance, high strength, and low material weight. Due to price, i

I. Applications Generally use low-strength un-doped titanium products. 0-doped titanium can be used for equipment such as chemical treatment, desalination, and power generation. In contrast, high-performance applications are usually highly selective. The method uses a high-strength titanium alloy, and the selection method depends on several design parameters, including weight, strength, ductility, and reliability requirements. In order to meet the requirements of its specific applications, alloys intended for high-performance applications generally undergo more stringent processing than titanium used for rotten uranium applications (additional costs are required). Nonetheless, they are used for a variety of temperatures to moderate temperatures. Titanium alloy j has inherently high strength and rigidity, favorable toughness, low density, and good i

The corrosion resistance of I, and the combination of these properties allow for significant weight savings in aerospace and other high temperature applications. This weight savings usually justifies the increase in costs associated with titanium alloy processing i. 1 I Tai alloy can be divided into Several types of metallurgy such as Alfa (α), near α, α! J-β or Θ ο Θ titanium alloys are particularly useful for aerospace structures 0 thermally processed / 5 titanium alloys can be cold worked into final or near final Form 〇 Cold-adding method causes high strength and / or favorable ductility / strength relationship of the alloy 〇 Some v, aviation material specifications " (AMS 49 57A and AMS 4958B) define the recommended Θ titanium alloy titanium-3 aluminum -8 vanadium-6 chromium _4 鲒 _4 molybdenum (referred to herein as Qin 2593706

-38-644 alloy) is used to produce round rods or wires that are mainly used as aviation wire 圏 springs. General aviation spring applications require high tensile strength, low density and corrosion resistance. Titanium-38-644 alloy includes (based on weight) 3.0 to 4.0% aluminum, 7.5 to 8.5% vanadium, 5.5 to 6.5% chromium, 3.5 to 4.5 hafnium molybdenum, 3.5 to 4.5% Zirconium, up to 0.14% oxygen, up to 0.05% carbon, up to 0.03% nitrogen, the rest is titanium. AMS 4957B requires additional restrictions on alloy composition, including up to 0.30% iron, up to 0.10% palladium, up to 300 ppm hydrogen, up to 50 ppm yttrium, and up to 0.4% of the entire remaining element. According to AMS specifications, alloys are aged by heating to a temperature in the range of 850 ° F to 1050 ° F (454 ° C to 566 ° C) and maintaining it at a selected temperature ± 10T (6 ° C) for 6 to 20 hours. The required minimum tensile properties that can be applied are determined according to ASTM E8 or ASTM E8M), depending on the nominal diameter of the round rod or wire finished product, but in any case not less than the minimum tensile strength of 180 ksi, the minimum 8% elongation percentage and Whether the minimum 20% reduction in section area 〇I Tai alloy is α, near 〇ί, α — / δ or Θ metallurgy is affected by the alloy's chemical composition, heat treatment and other factors. Metallurgical nomenclature refers to the main crystalline phase existing in the alloy microstructure at room temperature. Titanium has a closely packed hexagonal crystal structure at room temperature, called a α α. This structure can be transformed into a unitary cubic crystal structure at high temperature (/ 9 〃). The temperature at which the transformation occurs is called a / δ transformation temperature. 0 The commercial / 8 titanium alloy's / 8 transformation temperature is about 1 625T (885 1〇). 〇 Certain elements are added to pure titanium alloy to enhance one of the α and> 8 crystal structures. Elements that favor the α structure are called a α stable 〃, and elements that favor the / δ structure are called νν / 3 stable. For example, aluminum is an alpha stabilizer, so adding aluminum to a titanium alloy increases the > 8 transition temperature

Order-

593706; 10 chromium, iron, molybdenum, and vanadium are / 8 stabilizers, and adding them will reduce the / Θ transition temperature 丨

§ I; degree, which makes the / 9 structure stable at lower temperatures. 〇 The α and / δ stabilizers in the alloy 丨: The relative content and the heat treatment applied to the alloy determine whether the alloy's microstructure is mainly within a specific temperature range. It is a single α phase, a single phase, or a mixture of α and Nai. | The properties of titanium alloys are related to their microstructures. The two-phase α — / δ alloys are general; they show greater tensile strength than single-phase α alloys or single-phase θ alloys. In addition, I α — > Strengthening, because the microstructure can be manipulated by controlling the heating j, quenching and aging cycles. Many / 6 titanium alloys are mixed with more than one / β stabilizer. Use a sufficient amount; δ! Stabilizer and proper control of heat treatment and cold treatment, / δ phase is quite low ϊ! Temperature is sustainable; low temperature is lower than the normal > 5 transition temperature of the alloy. For example, the / δ phase can be rapidly cooled (such as quenched) from above and through the 々 transition temperature. T \ can be sustained in the titanium alloy. However, the titanium alloy must have a sufficient amount of / Θ It prevents the / 8 phase from being transformed into the α phase by the transformation of Asada. A / Θ stabilizer with a sufficient amount of I is sufficient to reduce the alloy's Asada dispersion transition temperature to below room temperature, and I but not enough to reduce the / Θ transition temperature to below room temperature is known to be metastable; Θ grained alloys are 0 metastable The Tie alloy can be maintained to a minimum of j / δ structure after heat treatment and cooling to a temperature of 0. The "/ 8 titanium alloy" referred to herein refers to the above-mentioned metastable / 3 Ϊ Tie alloy 0; j In addition, unless otherwise specified Statement that in this description and in the scope of the patent application | the numbers used to represent ingredients, time, temperature, etc. should be understood as in all | cases a means approximately 〃. Unless otherwise stated, the parameters in the figures described in Note I and the scope of the patent application are approximate, unless otherwise stated. Approximate conversion /-0¾.¾¾.¾: c.f ^; v · 3ίτ, Γ. 本 ί r

593706

I The desired properties attempted by the present invention can be changed. In the minimum case j I and without intention to limit the scope of the application of the doctrine of patents to the scope of patent application f !, the parameters on each digit should be interpreted at least according to the number of reported significant digits and 1 using the general rounding method. ! | Although the wide range of numbers and parameters of the present invention are stated as approximate, the numbers described in the specific examples are reported as accurately as possible. However, any number can essentially include measurements due to separate tests. The standard deviation must inevitably cause some errors. 0 A specific form of the present invention includes an aging time including cold working the alloy, and then directly aging the alloy for less than 4 hours as a whole. 0> The titanium alloy may be as titanium- 38-644 alloy. This method may include making an alloy into an article, such as a rod, wire, or coil spring. Another specific form of the present invention is the production of springs or other products using / 8 titanium alloy. The titanium alloy may include (by weight) 3.0 to 4.0% aluminum, 7.5 to 8.5% vanadium, 5.5 to 6.5% chromium, 3.5 to 4.5% molybdenum, 3.5 to 4.5% zirconium and titanium alloys. Alloys are hot-worked and cold-worked to provide 5 I to 60% shrinkage and aged directly for less than 4 hours. As used herein, cold-worked It is defined as various processing methods performed below the effective aging temperature of the alloy. Cold working of a titanium alloy can therefore be performed at a temperature lower than the alloy's I > 8 transition temperature. Cold working permanently deforms the machined part, which does not return to its original shape when the load causing deformation due to i I is removed. The degree of cold working! It is generally determined by the percentage reduction in the cross-sectional area of the workpiece. Therefore, the

I I The 5% reduction obtained by cold working refers to the 5% reduction in the cross-sectional area of the processed part during cold working. Any cold working technology can be used in the specific form of the invention. (Read the precautions on the back before filling this page.)

593706 # Ming means, in the Ming form. There are elongation, wire drawing forging, pressing, 0 cold-added strength and resistance to material elasticity change or cross-section closing to increase / 8 aging reaction. Cold working techniques for preparation according to the nature and the conventional method include (but not limited to) compression processing, drawing , Drawing, deep drawing, rolling, contour forming, cold forging nail heads, embossing, forging, tensile processing, stretch forming, and spinning forming can be used to improve the mechanical atoms of the alloy, including hardness, reduced tensile strength. However, ductility may be reduced during cold working. 0 Ductility is a measure of the ability of the material to not break. 0 Elongation and shrinkage during tensile tests are usually used as a measure of the ductility of the material. The method of the present invention can use the strength of a titanium alloy and maintain good ductility Significantly increase the alloy. The method of the present invention prepares and processes a / 8 titanium alloy, and then compares it with the same alloy composition but using a process including cold working and heat treatment steps. This test is detailed in the following titanium-38-644 alloy. The melt is cast into an ingot. The alloy's average temperature (% unit by weight) is shown in Table 10. The temperature is less than 170. Hot rolling, annealing, and air cooling-the first ingot. Table 1: Composition of the first ingot ϋ. Ming vanadium

Ml. Iron Carbon Nitrogen (Read the phonetic on the back? Matters and then fill out this page) 丨 Order --------- Line One M Wisdom. ¾ Financial% Money: · Η .η Balance 3.42 7.84 5.95 3.98 4.15 0.08 0.13 0.01 0.006 A part of the hot rolled, annealed and air-cooled ingot is processed by the method of the present invention. The other part of the hot rolled, annealed and air-cooled ingot is processed by conventional methods for comparison. The part processed by the conventional method is subjected to thermal processing, dissolution heat treatment, aging, and heat treatment parameters are changed to evaluate its impact on mechanical properties. As is known in the industry, dissolution heat treatment is a heat treatment step 593706. (6) step, in which the alloy is warmed to a * appropriate temperature and maintained at this temperature for a period of time long enough to allow one or more components of the alloy to enter a solid solution state. The alloy is rapidly cooled to maintain one or more of the components in the solution. 0 Dissolution heat treatment is usually performed on the alloy to improve ductility at a given strength. 0 Modifications of conventional heat treatment processes are compared with the process of the present invention. Table 2 includes The results of the room temperature tensile tests of the alloys in Table 1 are processed by conventional heat treatment methods under various conditions. All the tensile properties reported in Table 2 are measured in accordance with ASTM E8. The tensile test is used to determine the ultimate tensile strength, 0.2% drop strength, elongation, and cross-section shrinkage of the test piece. Sectional contraction and elongation are the measure of the ductility of the test piece. 0 Elongation is the amount of extension of the test piece under stress. 0 In a tensile test, elongation is the increment of the gauge length, and the gauge length is measured after the sample is broken. Usually expressed as the percentage of the original gauge on the test piece. Rolled state and heat treated room temperature tensile data Table 2: Properties of titanium-38-644 alloy processed by conventional methods Dissolution heat treatment temperature Dissolution aging temperature aging Time and cooling time and temperature (please read the precautions on the back before filling out this page) --------- 4 Member of the Intellectual Property Bureau of the Ministry of Economic Affairs II Consumption Du Printing Rolling status Rolling status Roll Rolling state 1 4 0 0 ° F / 1 hour water quenching Μ / \\\ 姐 / \\\ 1 4 0 0 ° F / 1 hour water quenching 9 0 0 ° F / 8 hours air cooling 1400 ° F / 20 minutes air-cooled 9 0 0 ° F / 8 hours air-cooled 1400 ° F / 20 minutes air-cooled 9 0 ° F / 16-hour air-cooled 1400 ° F / 20 minutes air-cooled 900T / 24-hour air-cooled 1400 ° F / 20 minutes air-cooled 9 50 0 T / 8 hours air-cooled 7-work paper ϋ I® for China National Standard (CNS) A4 specifications (: 210 X, 297 593706 A7 B7 V. Description of the invention (7) 1400 ° F / 20 minutes air-cooled 950T / 16 hours air-cooled (please read the precautions on the back before filling this page) l400 ° F / 20-minute air-cooled 950T / 24 hours air Cold (continued from the table above) Limit tensile strength (ks i) 〇 2% Drop yield (ksi) Elongation. (¾) Section shrinkage (%) Modulus 128 126 30 67 12.5 130 128 24 61 12.8 148 138 17 4 7 13.8 174 160 15 37 14.7 193 * 180 5 * 3 * 14.9 193 * 179 5 * 4 * 14.8 167 155 20 46 13.8 184 170 18 43 14.9 186 174 14 35 14.8 * = Rupture near Ministry of Economy wisdom The Consumer Cooperative of the Bureau of Property Bureau printed the test pieces listed in Table 2 from small tires with a diameter of 4 inches by hot rolling to a rod with a diameter of 0.569 inches, and they were dissolved and heat treated before aging. The data in Table 2 clearly shows that long aging is required. Time (more than 8 hours) to obtain high strength higher than 180 ksi in the alloy. Dissolution heat treatment processing for both of them (1400T (760 t :) 1 hour and 1400T (760 it) 20 minutes), conventional processing It takes 8 hours of aging to obtain the minimum tensile strength of titanium_38_644 rods and wires specified in AMS 4957A and AMS 4958B Degree 0 ^^ 3 4958B Specified / 9 titanium alloy must accept less than% f paper size after hot rolling and dissolution heat treatment Applicable to China National Standard (CNS) A4 specification (210 X 297 Intellectual Property Bureau of the Ministry of Economic Affairs Employee Consumer Cooperative) Printed 593706 A7 B7 5. Description of the invention (9), in the figure: Figure 1 depicts the effects of aging time on the ultimate tensile strength, 0.2% drop strength, elongation and section shrinkage of the titanium _38_644 alloy. The alloy is at 950 ° F. (510 ° C) subject to 13% or 15% cold work shrinkage or aging. Figure 2 depicts the effects of aging time and aging temperature on the ultimate tensile strength of titanium-38-644 alloy. The alloy is at 95 ° T (510 ° C), ιοοοτ (538 ° C) or 1 050 T (566 eC) subjected to 13% or 15% cold working shrinkage or aging. Figure 3 depicts the effect of aging time and aging temperature on the section shrinkage of titanium-38-644 alloy. T (510 eC), 1 000 T (538 eC), or 1050 ° F (566 ° C) subjected to 13% or 15% cold work shrinkage or aging. The alloy test pieces in Table 1 were processed according to the method of the present invention. -It will be understood that the method of the present invention can be applied to other components and is not limited to the methods described herein. Application 〇 By using the present invention, a relatively high strength / S titanium alloy can be produced in a relatively short period of time while still maintaining its ductility. The specific forms of the present invention are shown in Tables 3 to 9. In each case, After the cold working step, the test piece is directly aged for a total aging time of less than 4 hours. Direct alloy aging includes aging the alloy after processing without intermediate heat treatment steps, such as dissolution heat treatment. Direct aging does not exclude cold working alloys. Other processing steps are performed after and before the alloy is aged. These steps may be, for example, mechanical processing (such as scraping) or chemical processing (such as dipping). The processing steps used in the table and those obtained from room temperature tensile tests are listed. Mechanical properties of processed alloy samples. ^ The paper size applies the Chinese National Standard (CNS) A4 specification (210 X 2973) ^ -------------------- Order --------- line ( Please read the notes on the back before filling this page) 593706 A7 B7 V. Description of the invention (10) Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs, Tables 3 to 9 list the application of the present invention with: 8 The specific form of titanium alloy 〇 The amount of cold working can be any process! 芰, but in the specific form of the method of the present invention> 9 1 Tai alloy is preferably subjected to at least! Cold working from 5% reduction to 60% reduction. Cold-worked β titanium alloys even preferably include at least less than 35% reduction, and more preferably the specific form of the method of the present invention includes cold working titanium alloys to between 15% and 35%. With respect to Table 3, the test piece was hot rolled and cold drawn to provide 8% shrinkage and then directly aged at the temperature and time shown in the table. The test piece described in Table 3 was cold; also before extension Pre-annealing and 4ttC JliL · y \\\ Heart grinding. The specific forms listed in Table 3 produce TO strength by direct aging in less than 4 hours (the ultimate tensile strength is greater than 170 ksi) and maintain ductility (elongation greater than 8% and cross-sectional shrinkage greater than 20%) Q is listed In the specific form, it can reach the ultimate tensile strength greater than 18 0 ksi and the quotient to 190 ksi. The highest ultimate tensile strength reaches 9 50 ° F (510 β C). The aging temperature reaches 9 at this temperature, the limit of 199 ksi. Tensile strength is achieved in a total aging time of only 166 minutes. 0 Elongation and section shrinkage are achieved! The highest ductility is achieved at a higher aging temperature of 1 050 ° F (566 T). Table 3: 8% reduction in cold working Tensile test results of specific forms of the invention Aging temperature Aging time limit Tensile limit Tensile strength 0.2% Drop (° F) [° C] (minutes) Strength (k si) Strength (MPa) Strength (ksi) 0 140 • 5 969 132 • 5 950 [510] 166 199 • 0 1372 182 Λ 950 [510] 170 197 • 5 1362 180 .6 1000 [5 38] 125 1 86 • 7 1287 168 • 7 1000 [538] 200 186 • 0 1282 167 .5 (Please read the notes on the back before filling this page) Paper size is applicable to China National Standard (CNS) A4 (210 X 297 593706 A7) B7 、 Explanation of the invention (u) 1050 [565] 133 175.1 1207 156.9 1050 [565] 182 172.8 1191 155.3 (continued from the table above) 0.2% Elongation at 1% (MPa) (%) Section shrinkage (%) Modulus 913 19 61 12.0 1256 14 41 14.4 1245 14 35 13.4 1163 18 42 14.2 1155 18 41 14.9 1082 20 49 14.4 1071 21 52 14.5 (Please read the notes on the back before filling out this page) Table 4 lists the specific forms of the present invention, in which the test piece is hot rolled, cold stretched to 13% shrinkage, and directly aged. In addition, the specific forms described in Table 4 are subjected to heat rolling and before cold extension. Annealing and centerless honing. The specific form of the method of the present invention in Table 4 shows a significantly increased intensity after only 20 minutes of total aging time. Further aging at 950 T (510 t!) And 1 000 ° F (538 C) aging temperature, the strength increased to a level greater than required by AMS 4958A and 4957B specifications. However, the test pieces aged at 1050T (565 ° C) did not obtain the same strength as the test pieces aged at lower aging temperatures. The test piece aged at 1050T (565 eC) does maintain greater ductility as measured by elongation and cross-sectional shrinkage. 0 Table 4: Tensile test of the present invention in the form of 13% cold shrinkage reduction + paper size applies Chinese national standards (CNS) A4 specifications (210 X 297 Canghua 5) _ 593706 A7 B7 V. Description of the invention (12) Aging temperature (T) [° C] printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs, aging time limit tensile (minutes) ) Strength (ksi) Ultimate tensile strength (MPa) 0.2% drop strength (ksi) Extension state Extension state 145.3 1002 137.5 950 [510] 20 172.8 1191 163.1 950 [510] 166 2 03.5 1403 187.1 950 [510] 170 20 2.9 1399 185.8 1000 [538] 20 168.7 1163 156.8 1000 [538] 125 189.9 1309 172.1 1000L538] 200 189.8 1308 173.3 1050 [565] 20 164.4 1133 151.3 1050L565] 133 178.7 1232 161.7 1050 [565] 182 176.6 1217 159.3 (connected (Above table) 0.2% drop strength (MPa) elongation (%) section. Shrinkage (%) modulus 948 17 5 5 11.0 1124 21 50 13.7 1290 14 32 15.0 1281 15 36 15.1 1081 24 51 14.4 1186 18 44 14.7 1195 16 41 15.0 1043 26 51 14.4 1115 20 47 14.4 1098 20 52 14.0 Paper size is applicable to China National Standard (CNS) A4 (210 X 297 warehouse 6) _ (Please read the precautions on the back before filling this page)

Order --------- line J 593706 A7 _B7_ V. Description of the invention (13) Table 5 lists the specific form of the invention, in which the test piece is hot rolled, cold drawn to 13% reduction and direct The method of aging is similar to the specific form shown in Table 4. However, the test pieces listed in Table 5 are not annealed and centerlessly honed before cold working. However, the specific forms of the invention listed in Table 5 have the following characteristics: High strength and ductility test piece. The specific form of Table 5 produces extremely high strength (ultimate tensile strength exceeding 190 ksi) in the titanium alloy when aged for as short as 69 to 72 minutes. This result shows that when the present invention is applied to the / Θ titanium alloy of Table 1 At this time, the annealing step of the specific form of the present invention can be removed without significantly affecting the mechanical properties. Table 5: The results of the Hangzhou-Ningbo test of the specific form of the present invention with 13% cold processing shrinkage without annealing (Fill in this page) Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs Aging temperature (° F) [° C] Aging time (minutes-) Ultimate tensile strength (ksi) Ultimate tensile strength (MPa) 0 · 2% Reduced strength (Ks extended state extended state 147.2 1015 141,0 950 [510] 69 199.3 1374 181.0 950 [510] 94 199.7 1377 181.7 1000L538] 72 194.7 1342 176.8 1000L538] 89 190.2 1311 173.3 1000L538] 125 190.8 1315 172.8 1000L538] 200 191.8 1322 173.3 1050 [565] 81 179.0 1234 162.2 1050 [565] 88 178.9 1233 161.6 (continued from the table above) 0.2% reduced elongation strength (MPa) (%) The cross-section close-shrink (%) modulus is appropriate for the paper size China National Standard (CNS) A4 specification (210 X 297 full generation j {* ^ 'i I / 593706 A7 B7 V. Description of invention (14) 972 18 67 12.4 1248 18 37 14.6 1253 17 42 15.1 1219 20 43 14.5 1195 20 37 14.6 1191 16 45 14.5 1198 16 46 15.1 1116 24 57 15.0 1114 24 57 14.6 (Please read the notes on the back before filling out this page) Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs, Table 6 lists the specific form of the invention Among them, the test pieces are hot rolled, cold drawn to 15% shrinkage and directly aged. In addition, the test pieces in Table 6 are not annealed and heartlessly honed before cold drawing. Some of the methods of the present invention in Table 6 are specific The form includes an aging time of less than 60 minutes. The specific form including cold working to 15% reduction shows a higher strength than the cold forming to 8% reduction of the specific form without loss of ductility. The specific form of cold processing to 15% reduction is in the total Aging time is only 45 minutes, 900 T (482. 〇) and 950 ° F (510 ° C) temperature after aging to obtain ultimate tensile strength greater than 190 ksi, at the same temperature, the total aging time of only 60 minutes after the ultimate tensile strength greater than 200 ksi was obtained Table 6 : 15% cold gun shrinkage of the hairpin test results of the specific form of the hairpin I aging temperature (° F) rc] aging time (minutes) ultimate tensile strength (ksi) 〇 2% drop_JM (ksi) elongation (% ) Section shrinkage (magic 0 148.4 146.3 19.3 65.9 900 [482] 45 192.5 177.2 15.8 45.2 900 [482] 60 206.1 190.4 11.4 40.6 j Paper size applies to China National Standard (CNS) A4 specifications (210 X 297 public shame ^^^ 593706 A7 _B7 V. Description of the invention (15) Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs

900 [482] 60 200.5 189.3 13.4 40.0 900 [482] 120 212.2 192.9 16.3 35.7 950 [510] 30 179.4 164.5 17.2 50.5 950 [510] 45 190.3 172.2 16.9 45.7 950 [510] 60 195.2 174.7 15.8 40.6 950 [510] 60 197.5 186.4 13.7 37.8 950 [510] 60 195.2 183.5 13.5 37.6 950 [510] 156 207.6 187.0 14.8 37.0 1000 [538] 45 187.8 167.7 18.2 45.6 1000 [538] 60 188.4 175.8 15.8 44.0 1000 [538] 60 188.3 175.7 16.8 44.6 Table 7 lists the specific forms of the present invention, in which the test piece is hot rolled, cold drawn to 19% shrinkage and direct aging. In addition, the specific forms described in Table 7 are annealed and centerlessly honed before cold extension. Table 7: 19% cold working shrinkage of the specific form of the invention results of the tensile test aging temperature (T) [° C] aging time limit tensile limit tensile strength (minutes) strength (ksi) strength (MPa) 0.2% drop strength (ksi J extended state 0 153.3 1057 141.0 950 [510] 166 210.2 1449 193.3 950 [510] 170 209.4 1444 191.6 1000 [538] 72 191.7 1322 173.8 1000 [538] 89 196.9 1357 179.3 1000L538] 125 196.5 1355 179.1 1000L538] 200 196. 0 1351 178.6 1050 [565] 81 183.8 1267 166.6 The scale of the scale is applicable to the Chinese National Standard (CNS) A4 specification (210 X 297 Xi (please read the precautions on the back before filling this page) Order ------ --- Line 593706 A7 B7, Description of the invention (16) 1050 [565] 88 186.3 1284 169.0 1050 [565] 133 183.1 1262 165.4 1050 [565] 182 161.7 12 5 3 164.5 (MPa) Elongation (%) Section shrinkage modulus 972 13 57 13.3 1336 12 27 14.2 1321 14 31 14.7 1198 22 47 15.4 1236 19 32 15.3 1235 14 33 14.1 1231 15 40 14.4 1149 22 5 4 14.1 1165 23 52 15.1 1140 20 54 13.6 1134 20 50 15.1 Table 8 shows the specific form of the present invention, in which the test piece is hot rolled, cold drawn to 20% shrinkage and directly aged. In addition, the test piece in Table 8 is not tested before cold extension. After annealing and centerless honing. The specific form of the invention in Table 8 uses a 15% reduction in cold working to produce a limit tensile strength increase of about 5% and a 0.2% drop strength increase of about 6%. Cold working to 20% Reduction makes ductility about ▲ -III I --- order ---- I ---- line ' (Please read the notes on the back before filling this page) Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs% (measured by elongation) or 9% (measured by cross-section shrinkage).

_The paper size is applicable to China National Standard (CNS) A4 specifications (210 X 297 male H 593706 A7 B7 V. Description of the invention (17 Table 8: 20% cold processing shrinkage reduction of the specific form of the present invention specific anti-MMM fruit-fruit aging temperature (° F ) [t!] Aging time (minutes) Ultimate tensile strength (ksi) 0.2% Drop strength (ksi) Elongation (%) Section shrinkage (magic 0 156.2 152.0 16.4 63.5 900 [482] 45 201.1 185.9 15.3 40.6 900 [482 ] 120 216.0 199.4 9.3 36.4 950 [510] 30 188.1 173.9 17.3 50.3 950 [510] 45 200.8 184.0 17.4 43.8 950 [510] 60 205.0 187.2 13.2 36.9 950 [510] 156 214.8 196.3 14.5 32.5 1000 [538] 45 194.2 174.7 17.2 40.4 1000 [538] 60 196.5 176.9 18.0 40.0 Table 9 shows the specific forms of the invention, in which the test piece is hot rolled, cold drawn to 25% shrinkage and direct aging. In addition, the specific forms described in Table 9 are cold It does not undergo annealing and centerless honing before extension. The specific forms of the invention listed in Table 9 increase the ultimate tensile strength by about 7% and about 0.2% by reducing the average yield strength by about 15% compared to those using cold working to 15% shrinkage. Up to 25% reduction and utilization of cold work The specific form of reduction to 15% reduces the ductility by about 11% (measured by elongation) or 2% (measured by cross-section shrinkage). Table 9: Test results of specific forms of the present invention with 25% cold processing reduction Time limit tensile 0.2% fall-off extension, temporary (° F) [° C] (minutes) strength (kG) strength (ksi) 0 162.5 159.4 16.9 64.0 900 [482] 45 207.2 193.0 13.7 43.8 900 [482] 120 220.9 204.6 15.2 34.9 950 [510] 30 194.2 180.8 16.9 48.7 950 [510] 45 205.1 189.9 15.4 43.2 This paper size is applicable to China National Standard (CNS) A4 (210 X 297 cm) (Please read the precautions on the back before (Fill in this page) -I! II 1 Order! I I ---- line i Printed by the employee's consumer cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs Printed by the employee's consumer cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs Printed 5933706 [510] 60 207.6 189.3 14.0 39.4 950 [510] 156 212.7 193.7 16.4 33.8 1000 [538] 45 199.3 181.7 16.0 46.5 The tensile properties of the specific form of the invention including cold working to 13% to 15% reduction steps are shown in Figure 1 To 3 〇 The drawing in Figure 1 illustrates the aging time. It has the effect of the titanium-38-644 0 titanium alloy sample with the composition shown in Table 1. The method includes the cold working step of cold working to 13% reduction. The ultimate tensile strength and 0.2% drop strength are all the aging time of at least the first 60 minutes. The specific tensile strength of the test pieces in this specific form reaches 180 ksi within a total aging time of 30 minutes. The test pieces are aged in a conventional laboratory test furnace. It may be more efficient to heat articles in a production aging furnace, so in the production aging furnace, we expect that the total aging time achieved by the method of the present invention to achieve high strength (such as 180 ksi) can be reduced by one third in some cases. Two or more 〇> 9 titanium alloy aging can be performed below θ transition temperature 〇 / 5 titanium alloy aging preferably occurs at a temperature between 800 ° F (427 ° C) and 1 000 T (538 Ό). For certain applications, the aging of the / δ titanium alloy can occur between 800 ° F (427 C) and 1000 ° F (538 ° C), preferably 900 ° F (4 8 2 eC) and 10%. 〇 ° F (538 * 〇). It can be seen in Figure 1 that the ductility (measured by elongation or cross-section shrinkage) of the test piece decreases with the total aging time. However, the ductility decreases slowly with the total aging time and can reach a limit tensile strength exceeding 200 ksi. Maintains fairly good ductility. For certain applications, such as for cars, snowmobiles, motorcycles

The paper size is applicable to China National Standard (CNS) A4 specifications (210 X 297 male: H (Please read the precautions on the back before filling this page) -IIIIIII Order -111111 · 593706 A7 ___B7_ V. Description of the invention (19) Suspension springs for other leisure vehicles and valve springs for piston engines have better short aging time. Automobile production lines can include winding and aging springs according to production requirements. When the conveyor belt passes through the aging furnace, the spring can be rolled on the conveyor belt And then aging. In these and other applications, the aging time of rhenium-titanium alloy is preferably less than 3 hours. The aging time of titanium alloy is more preferably less than 2 hours, even for some time-sensitive applications, the aging time Less than 1 hour or better, less than 45 minutes. The alloy produced by the present invention can also be used in applications other than springs, such as surgical equipment or transplantation in the biomedical industry. Figure 2 illustrates the aging time and temperature. The effect of the ultimate tensile strength of the> 8 titanium alloy test piece in Table 1, and the ζδ titanium alloy of Table 1 in the specific form of the present invention includes cold working to 13% or 15% reduction and increase A higher ultimate tensile temperature was achieved in the specific form of the invention with low temperature aging. This is to be expected, both the growth of the crystal at higher temperatures and the lower alpha phase volume present in the alloy due to the cap processing conditions. Both will negatively affect the strength of Θ titanium alloy. 0 Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs (please read the precautions on the back before filling this page). Figure 3 shows the aging temperature and time for Table 1 > 8 titanium alloy. The effect of the ductility of the test piece is measured by the area reduction. The specific form of the present invention that is used at a higher aging yields higher test piece ductility over time. It is expected that crystals covered at higher temperatures Although the growth negatively affects the strength, it improves the ductility of the titanium alloy. According to the method of the present invention, a second ingot is generated and processed. The composition of the second ingot at three positions is shown in Table 100. Tested at three locations to confirm its composition and ensure a fairly consistent composition throughout the ingot.

The paper size applies to the Chinese National Standard (CNS) A4 specification (210 X 297 full H 593706 A7 B7 V. Description of the invention (20) Table 10: Composition source of the second ingot_Shentai Aluminum Vanadium Chromium Pin Molybdenum Oxide Carbon Clock L- The remainder of the second ingot top 3.65 7.95 6.16 4.06 4 · 08 0.1 0.05 0.01 0.01 The remainder of the second ingot middle section 3.45 7 · 9 6.29 4.12 4.04 0.1 0.06 0.02 0.01 The remainder of the second ingot bottom 3.34 7 · 85 6 · 43 4.14 3 · 98 0 · 1 0.06 0.01 0.01 The second ingot is processed according to the method of the present invention. The second ingot is hot rolled, annealed and air cooled at a temperature not exceeding 1825T (996 1〇). Regarding Table 11, the test piece produced from the second ingot was hot rolled and cold drawn to provide a 16.5% reduction, and then directly aged at the temperature and time shown in the table. The test described in Table 11 The parts are also annealed and air-cooled at a temperature not exceeding 1 450 T (774 1C) before cold drawing. The specific forms listed in Table 11 produce high strength with direct aging in less than 30 minutes (the ultimate tensile strength is greater than 190 ksi). ) And maintain ductility (elongation greater than 8% and cross-sectional shrinkage greater than 20%) 〇 can reach more than 20 in the specific form listed 0 ksi and as high as 220 ksi ultimate tensile strength. 0 The highest ultimate tensile strength is reached again at a lower aging temperature (900 T (482 ° C)). At this temperature, a total aging time of only 60 minutes can be obtained. 220 The ultimate tensile strength of ksi. The highest ductility as measured by elongation and section shrinkage is achieved at a higher temperature of 105 ° F (566 ° F). (Please read the precautions on the back before filling this page) -I ϋ · ϋ 1 nn · 1 1 · ϋ ϋ I ϋ ϋ I. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs. Table 11: Results of the tensile test of a specific form of the present invention produced by a second ingot reduced by 16.5% cold processing. Aging temperature (T) [° C] Aging time (minutes) Ultimate tensile strength (ksi) Ultimate tensile strength (MPa) 0 · 2% drop strength (ksi) Not applicable 0 164.2 1132 150.8 Not applicable 0 154.6 1066 149.2

Paper size applies to China National Standard (CNS) A4 specifications (210 X 297 full H 593706 A7 _B7 V. Description of invention (21) Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economy 900 [482] 30 2 05.5 1417 191.0 900 [482] 45 207.6 1431 191.7 900 [482] 45 216.0 1489 197.7 900 [482] 60 220.4 1519 202.7 900 [482] 60 216.2 1490 201.1 N / A 0 164.2 1132 150.8 N / A 0 154.6 1066 149.2 950 [510] 30 198.7 1370 182.7 950 [ 510] 30 198.7 1370 181.3 950 [510] 45 207.0 1427 191.7 950 [510] 45 205.1 1414 190.5 950 [510] 60 210.5 1451 192.6 950 [510] 60 209.3 1443 193.5 N / A 0 164.2 1132 150.8 N / A 0 154.6 106 6 149.2 1000L538] 30 190.9 1316 175.2 1000L538] 45 197.8 1364 182.4 1000L538] 45 199.9 1378 182.9 1000 [538] 60 201.5 1389 185.1 1000L538] 60 204.7 1411 189.5 (continued from the table above) 0.2% drop strength (MPa) elongation (%) break Face shrinkage (%) 1040 16.1 52.5 (Please read the precautions on the back before filling this page) Order --------- line. Feng paper size applies to Chinese national standards CNS) A4 specification (210 X 297 ^ ^ B. Z 3 Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs 593706 A7 _B7_ V. Invention Description (22) 1029 17.9 52.9 1317 11.5 33.3 1322 11.5 31.4 1363 10.9 29.1 1 397 1 1.0 30 · 4 1386 10.5 28.0 1040 16.1 52.5 1029 17.9 52.9 1260 13.7 35.9 1250 14.3 35.0 1322 13.7 32.0 1313 12.6 30 · 8 1328 13.8 24.7 1334 13.1 29.8 1040 16.1 52.5 1029 17.9 52.9 1208 17.6 37.0 1257 14.036.8 1261 20.4 35.1 1276- 34.5 1306 16.0 39 · 5 In general, the test pieces produced in the specific form of the processing method of the present invention described in Table 11 have a shorter aging time than those in the present invention described in Tables 3 to 9

Jie paper size applies to China National Standard (CNS) A4 (210 X 297 H free

: Ί A (Please read the precautions on the back before filling this page) Order --------- line · 593706 A7 B7 V. Description of the invention (23) The tensile strength of the test piece produced in the specific form of the processing method Strength 0 However, in general, the ductility of the test piece described in Table 11 is low. I believe that the higher rolling temperature experienced by the second ingot results in lower ductility. This is because the higher processing temperature is beneficial for the larger The previous / 9 particle size. Higher strength is considered to be related to slow cooling after annealing, and cooling allows some aging before cold working. Table 1 2 shows the rotating beam fatigue test performed on articles prepared by the method of the present invention. As a result, the articles were hot-rolled, cold-extended to 15% shrinkage, and directly aged for one hour at 950 卞 (510 ° C). The rotating beam fatigue test was performed according to the international test standard ISO 11 43 at a frequency of 50 Hz. , R = -l and the use of round rods to determine bending fatigue. The results show the number of cycles each sample has experienced before damage or the total number of cycles performed on the sample when no damage has occurred. Table 12: Includes 15% cold working shrinkage and 950 T (510 t!) Direct aging for one hour Rotating beam fatigue test results in bulk form Maximum stress Maximum stress cycles Note ksi MPa (Please read the precautions on the back before filling out this page) Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs 73 500 13401000 No fire 83 575 10017100 Running fire without cracking 87 600 10804700 Running fire without cracking 87 600 151900 Rupture 91 625 620800 Clamping Rupture 94 650 525100 Rupture 98 675 79300 Rupture 102 700 395200 Rupture

Jie paper size is applicable to China National Standard (CNS) A4 specifications (210 X 297 full f I 4 * MZ / 593706 printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs A7 _B7______ V. Description of the invention (24) Table 1 3 The results of the fatigue test on the load control shaft of the article prepared by the method of the invention, wherein the article was hot rolled and cold stretched to 15% shrinkage, and was directly aged at 950 ° F (510 ° C) for one hour. 0 Load control shaft fatigue The test was performed at 29 Hz at K = 0 · 1 in accordance with ASTM E-466-96 to determine the fatigue of the article. The results show the number of cycles each sample experienced before damage. Using different conditions such as long aging in the method of the present invention Samples prepared with different ages, different aging temperatures, or different degrees of cold working can cause an increase in the number of cycles before damage during fatigue testing. Table 13: Includes 15% cold working shrinkage and direct aging at 950 ° F (510 ° C) for one hour. Load control shaft fatigue test results of specific forms of the present invention Maximum stress Maximum number of stress cycles Note ksi MPa 142 979 2313507 Rupture 145 1000 286613. Rupture 150 1034 170773 Rupture 160 1103 22532 Fracture Although the method of the present invention is described above with respect to certain compositions of / δ titanium alloy, I believe that the method of the present invention can be more widely applied to the processing of other / 9 titanium alloys. For example, rather than the invention The method is limited, and some of the additional commercial / 6 titanium alloys that can benefit from the present invention are titanium alloys with the following nominal composition (weight% units). Titanium-12 molybdenum-6 锴-2 iron (a type containing 12% molybdenum) , 6% cone, 2% iron and titanium alloys, and can be purchased in at least one form such as ALLVAC TMZF alloy); titanium-4.5 iron-6.8 molybdenum-^ paper size applies Chinese National Standard (CNS) A4 specifications (210 X 297 public: ^ (Please read the notes on the back before filling this page)

593706 A7 B7 V. Description of the invention (25 1.5 Ming (an alloy with a coating, and can be purchased in at least one form such as TIMETAL LCB alloy containing 4.5% iron, 6.8% indium, 1.5% saw and sintered); I Taiyi 1 5 molybdenum-2 · 6 niobium-3 aluminum-0 · 2 silicon (an alloy containing 15% molybdenum, 2.6% niobium, 3% aluminum, 0.2% silicon and titanium, and can be at least as TI-metal 21S alloy Available in one form); titanium—15 vanadium—3 chromium—3 tin—3 inscriptions (a type containing 15% sharp, 3% iron, 3% tin, 3%, such as at least one shape of ALLVAC 15-3 alloy—6 Zirconium-4 · 5 tin (an alloy containing 11.5% and titanium, and can be printed by the UNITEK Beta Intellectual Property Bureau of the Intellectual Property Bureau of the Ministry of Economic Affairs and printed by the consumer co-operative society, and molybdenum, 6 III and 5.7 iron 2. 7% a shape One element may include the fact that the present invention should be clearly understood, although the technical person has changed and changed the alloy, and can); titanium-11.5 molybdenum% chromium, 4.5% tin-gold at least one form); and Titanium-6 vanadium-6 molybdenum-2.7 aluminum (an alloy containing 6% vanadium, 6% molybdenum, 5.7% iron, aluminum and titanium, and can be as high as TIMETAL 125 alloy The alloy composition listed above is a nominal composition, and each content can be changed by at least 2% or more, and these alloys also have additional components. It is understood that this description is an example suitable for a clear understanding of this Various developments of the invention will not be listed to some ordinary people skilled in the industry and will not be conducive to more inventions. In order to simplify the present invention has been described in some specific forms, but the industry is generally When thinking about the previous description, the scholars will recognize that the present invention can adopt a variety of modifications. All changes and modifications are intended to be covered by the scope of the above-mentioned patent application.

Jie paper size applies to China National Standard (CNS) A4 specifications (210 X 297 free of H (Please read the precautions on the back before filling this page)

Claims (1)

593706 Patent park for patent application: : Meter®: positive) 1. A method for processing a titanium alloy, the method comprising: cold working a β-perylene alloy; and directly aging the / 9-perylene alloy to a total aging time of less than 4 hours 2 as in the first patent application The method, wherein the million titanium alloy includes at least one of aluminum, vanadium, molybdenum, chromium, and zirconium. 3. The method according to item 1 of the patent application scope, comprising: hot rolling the > 8 titanium alloy before cold working the / 8 titanium alloy. 4 · The method according to item 3 of the patent application, wherein cold working the titanium alloy includes cold working the > 9 titanium alloy to at least 5% reduction. 05 · The method according to item 4 of the patent application, wherein cold processing the titanium alloy The alloy includes cold working the / S titanium alloy to a reduction of at least 15%. The method of item 5 of the patent application, wherein cold working the titanium alloy includes cold working the > 9 titanium alloy to a reduction of less than 60%. For example, the method of applying for item 6 in the scope of patent application, wherein cold working the titanium alloy includes cold working the alloy to a reduction of less than 35%. 8 The method of applying for the scope of item 7, wherein cold processing the / 8 titanium alloy includes Cold-working this alloy is reduced to less than 20%. 9 · The method according to item 1 of the patent application range, wherein the Θ titanium alloy is directly aged within a temperature range of 800 T (427 t!) To 1200 ° F (649 ° C). Ageing. 1 0. The method according to item 1 of the patent application range, wherein the > 9 titanium alloy is directly aged within a temperature range of 800 ° F (427 ° F) to 1000 ° F (538 ° C). / 3 titanium alloy directly aging. -30- 593706 11. The method according to item 1 of the patent application range, wherein the Θ titanium alloy is directly aged within a temperature range of 900 (482 °) to loooop (538 C), and the θ titanium alloy is directly aged. 0 12. The method according to item 1 of the patent application range, wherein directly ageing the Θ titanium alloy includes directly ageing the rhenium titanium alloy for less than 3 hours. 1 3. The method of claim 1 in the patent application, wherein directly aging the rhenium-titanium alloy includes directly aging the rhenium-titanium alloy for less than 2 hours. 0 14. The method of claim 1 in the patent application, wherein the老化 Direct aging of titanium alloy includes directly aging the β titanium alloy for less than 1 hour. 0 1 5. The method of item 1 in the patent application scope, wherein direct aging of the / 3 titanium alloy includes direct aging of the titanium alloy. Less than 45 minutes. 16. The method according to item 1 of the patent application range, wherein the> 8 titanium alloy contains (by weight) 3.0 to 4.0% aluminum, 7.5% to 8.5% vanadium, 5.5 to 6.5% complex, 3.5 to 4. 5% molybdenum, 3.5 to 4.5% pins, and rhenium. 1 7. A method of producing a product, including providing a content (based on weight) of 3.0 to 4.0% aluminum, 7.5 to 8.5% vanadium, 5.5 to 6.5% chromium, 3.5 to 4.5% molybdenum, 3.5 to 4.5% zirconium, and titanium / 9 titanium alloys; hot-processed the Θ 纟 alloy; cold-worked titanium alloys to provide 5 to 60% reduction; and 800 to 427 (427 t) to In the temperature range of 1100T (593.0), the Θ 纟 alloy is directly aged for a total aging time of less than 2 hours. ○ 18. The method of item 17 in the patent application scope, wherein the product is elastic yellow -31-593706 19 · The method according to item 17 of the patent application, wherein cold working the / 3 titanium alloy includes extending the hafnium titanium alloy through a die. The method according to item 17 of the patent application, wherein the Θ titanium is hot processed. The alloy includes making the > 9 titanium alloy into a rod, rod, or coil. 2 1 · As in the method of claim 17 of the patent application, wherein the / 3 titanium alloy is directly aged, including a total aging time of less than 1 hour. 〇22 The method of claim 17 in which the direct aging of the / 3 titanium alloy includes less than 45 points The total aging time. 23. The method of claim 22, wherein the direct aging of the / 3 titanium alloy includes a direct aging temperature within a temperature range of 900 T (482 eC) to 1000 ° F (538 ° C). 24. The method according to item 18 of the patent application, wherein the spring is a component of an automobile, snowmobile, motorcycle, recreational vehicle or engine. 25. The method according to item 17 of the patent application, including: Centerless honing The / 9 titanium alloy; and annealing the / 8 titanium alloy before cold working the / 8 titanium alloy. 26. The method of claim 25, wherein cold working the titanium alloy includes extending the > 8 through a die. Titanium alloy 〇27. The method according to item 17 of the patent application range, wherein the cold working of the alloy provides a reduction of 5 to 35% 〇28 · —a method of processing titanium alloy, including: directly aging the cold-processed Θ titanium alloy to age Total aging time of less than 4 hours 0-32-593706 29. The method according to item 28 of the patent application, wherein the 0 titanium alloy includes at least one of aluminum, vanadium, molybdenum, chromium, and zirconium. The method of applying for the scope of patent No. 28,尙 Contains: Hot rolling the stone titanium alloy before cold working of the / 5 titanium alloy 0 31. The method according to item 28 of the patent application, wherein the cold titanium alloy is directly aged and contained between 800 T (427 eC) and 12 °. 〇 ° F (649 * C) in the temperature range of the stone titanium alloy directly aging 32. The method of the scope of the patent application No. 28, wherein the / 3 titanium alloy is directly aged at 800 ° F (427 eC) Directly age the > 8 titanium alloy within the temperature range of 1000T (538 t :). 33. The method of item 28 of the patent application range, wherein the direct ageing of the cold titanium alloy is included in the range of 900 Τ (482 t) to This rhenium-titanium alloy is directly aged in a temperature range of 1 000 Τ (538 ° C). 34. A method as claimed in item 28 of the patent application, wherein direct aging of the cold titanium alloy includes directly aging the titanium alloy for less than 3 hours. 9 direct aging of titanium alloys includes direct aging of the > 8 titanium alloy for less than 2 hours 0 36. The method of item 2S of the patent application scope, wherein direct aging of the / 9 titanium alloy includes the > 8 titanium Direct aging of the alloy for less than 1 hour 0 37. The method of claim 2S, wherein direct aging of the / 3 titanium alloy includes directly aging the > 8 titanium alloy for less than 45 minutes. 3S · The method according to item 28 of the patent application range, wherein the 0 titanium alloy contains (based on weight) 3.0 to 4.0% aluminum, 7.5 to 8.5% vanadium, 5.5 to 6.5% chromium, 3.5 to 4.5 % Molybdenum, 3.5 to 4.5% zirconium and titanium 0 -33-593706 3 9-a product prepared by a method comprising the following steps: cold working an article, wherein the article contains a hafnium titanium alloy; and directly The total aging time is less than 4 hours. If the product is in the scope of patent application 39, the article is one of the rod, rod, or coil. The titanium alloy contains (based on weight) 3.0 to 4.0% aluminum, 7.5 to 8.5% vanadium, 5.5 to 6.5% chromium, 3.5 to 4.5% molybdenum, 3.5 to 4.5% zirconium, and titanium. 42. The article of claim 39, wherein the direct aging of the > 8 titanium alloy is included in the temperature range of 800T (427 t!) To 1200T (649 eC), and the / 8 titanium alloy is directly aged. 43. The article of claim 39, wherein directly aging the titanium alloy includes directly aging the / 3 titanium alloy for less than 2 hours. 44. If the product under the scope of patent application 39 is applied, the direct aging of the / 5 titanium alloy includes directly aging the / 8 titanium alloy (less than 1 hour). 45. If the product under the scope of patent application 39 is applied, the The direct aging of the titanium alloy includes directly aging the > 8 titanium alloy for less than minutes.