CN1602369A - Method for processing beta titanium alloys - Google Patents
Method for processing beta titanium alloys Download PDFInfo
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- CN1602369A CN1602369A CNA028248570A CN02824857A CN1602369A CN 1602369 A CN1602369 A CN 1602369A CN A028248570 A CNA028248570 A CN A028248570A CN 02824857 A CN02824857 A CN 02824857A CN 1602369 A CN1602369 A CN 1602369A
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- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
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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. The method may include fabricating the alloy into the article of manufacture such as, for example, a bar, wire, or a coil spring. The method may be utilized to produce articles with high tensile strength while retain ductility. The beta titanium alloy may be any beta titanium alloy, for example, the alloy comprising, by weight, 3.0 % to 4.0 % aluminium, 7.5 to 8.5 % vanadium, 5.5 to 6.5 % chromiun, 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 irect aged for a total time of less than 4 hours.
Description
Technical field
The invention relates to the manufacturing titanium alloy, especially the method for beta-titanium alloy.The present invention includes the cold working beta-titanium alloy, directly make alloy aging subsequently less than 4 hours.
Describe
The unique property of titanium alloy is applicable to it and requires in the heavy application of high corrosion resistance, high strength and low thing.In view of the reason of price, require erosion-resisting application, usually use the unalloyed titanium stocking of low strength.Unalloyed titanium can manufacture for example employed equipment in chemical process, desalination and generating.In contrast, high performance application usually according to some design factors, comprises the requirement of weight, intensity, ductility and reliability, in a kind of extremely preferred mode, uses high-intensity titanium alloy.In order to satisfy the requirement of this special use, be used for the alloy that high-performance is used, usually than the titanium that is used for corrosion-resistant usefulness, carry out more strict processing, bring extra-pay thereupon.However, various titanium alloy institute inherent high strength, high rigidity, good toughness, low density and good resistance to corrosion wait overall characteristic, are applicable to low in the application of middle temperature, mainly be with in light weight, be used for space structure and other high performance application.This relevant expense of handling titanium alloy that usually can increase again in light weight.
Titanium alloy can be with a kind of classification the in several metallurgical types, and α, approximate α, alpha-beta or β type are for example arranged.Beta-titanium alloy is particularly useful for space structure.Hot worked beta-titanium alloy can be cold worked into final or approximate final form.The cold working process makes alloy have the property relationship of high level intensity and/or suitable ductility/intensity.Some " Aerospace Material Specifications ", among AMS4957A and the AMS 4958A, illustrated the recommendation process condition of beta-titanium alloy Ti-3Al-8V-6Cr-4Zr-4Mo (being called the Ti-38-644 alloy) main as space flight disc spring pole or line really herein to make.Usually, the tensile strength that the application requiring of space flight spring is high, low density and erosion resistance.The Ti-38-644 alloy by weight, contains the aluminium of 3.0-4.0%, the vanadium of 7.5-8.5%, the chromium of 5.5-6.5%, the molybdenum of 3.5-4.5%, the zirconium of 3.5-4.5%, maximum 0.14% oxygen, the nitrogen of maximum 0.05% carbon, maximum 0.03%, and all the other are titanium.AMS 4957B has also proposed some other qualifications to alloying constituent, comprises maximum 0.30% iron, maximum 0.10% palladium, the hydrogen of maximum 300ppm, the yttrium of maximum 50ppm, and all the other elements are 0.40% altogether to the maximum.According to the technical requirements of AMS, alloy must pass through in 850～1050 (454 ℃～566 ℃) heating down, and under selecting temperature ± 10 °F (6 ℃), keeps 6～20 hours to wear out.Desired minimum stretch performance, as what be suitable for, determine according to ASTME8 or ASTME8M, the nominal diameter that depends on the finished product pole or silk, but,, be minimum tensile strength less than 180ksi without any a kind of situation, 8% minimum extensibility and 20% minimum area reduce (" RA ").
No matter the metallurgical type of titanium alloy is any among α, approximate α, alpha-beta or the β, all be subjected to the chemical constitution of alloy, the thermal treatment and the other factors that apply influence.The regulation of metallurgical type all relates to the main crystallization phases that is present under the room temperature in the alloy microstructure.Titanium metal at room temperature has the closelypacked structure of hexagonal crystal (" hcp ") that is called " α ".Under high-temperature, this structure can be transformed into body-centered cubic crystal structure (" bcc ") (" β ").The temperature that this transformation takes place is called " beta transus temperature ".Beta transus temperature for industrial pure titanium alloy is about 1625 °F (885 ℃), and the element that adds some alloy in pure titanium can promote to form the one or another kind of of α and β crystalline structure.The element that helps the α structure is called " alpha stabilizers ", and the element that helps beta structure is called " β stablizer ".For example, aluminium is a kind of alpha stabilizers, aluminium is added in the titanium alloy can increase beta transus temperature.Chromium, iron, molybdenum and vanadium are the β stablizers, and their interpolation can reduce beta transus temperature, can stablize beta structure at low temperatures.The relative quantity of α and β and be applied to heat treatment of alloy in the alloy, in specific temperature range, whether the microtexture of decision alloy mainly is the mixed phase of list-α phase, list-β phase or α, β.
The characteristic of titanium alloy is relevant with its microtexture, and the tensile strength that alpha-beta two phase alloys generally present is greater than α single-phased alloy or β single-phased alloy.By the further reinforcing alpha-beta alloy of thermal treatment, this be because by the control heating, quench and aging circulation the may command microtexture.
Many beta-titanium alloys and more than one β stablizer form alloy.With the β stablizer of q.s, and in the suitable control of thermal treatment and process of cooling, can keep the β phase under the quite low temperature of the common beta transus temperature of alloy being lower than.For example, by from being higher than or cooling off rapidly,, can in titanium alloy, keep the β phase as by quench treatment through beta transus temperature.Yet titanium alloy must have the β stablizer of q.s, is transformed into the α phase to stop β by martensitic transformation.The titanium alloy that contains capacity β stablizer, its amount will be enough to reduce the martensite transformation temperature of alloy to being lower than room temperature, but can not be enough to reduce beta transus temperature below room temperature, this known being called " metastable " beta-titanium alloy, this metastable beta-titanium alloy, behind thermal treatment and cool to room temperature, at least can the retaining part beta structure.Reference to beta-titanium alloy used herein as above-mentioned to metastable beta-titanium alloy.
In addition, except other has explanation, all numerical value of employed expression component, time, temperature, equivalent in this specification sheets and the claim all should be understood in all examples and change with term " about ".Therefore, unless make opposite explanation, the digital parameter of listing in specification sheets and the claim all is an approximation below, and the characteristic that requires that this value can obtain according to the present invention changes.At least plan to limit the application that is equivalent to claim scope principle, each digital parameter should be thought in the scope of the significant figure of being reported and by using the general technology that rounds off at least.
Although wide digital scope and parameter that the present invention sets all are approximations.The numerical value of setting in specific examples is to report as far as possible accurately.Yet any numerical value contains certain error certainly, and this error must be to be caused by the standard deviation of trying to achieve in each time test.
Embodiment of the present invention are carried out cold working by comprising to alloy, directly alloy is carried out then total digestion time be less than 4 hours the aged step method and handle beta-titanium alloy.For example beta-titanium alloy can be the Ti-38-644 alloy.This method can comprise makes goods with alloy, for example as rod, silk, disc spring.
Another embodiment of the present invention is the method for being produced spring or other goods by beta-titanium alloy.For example beta-titanium alloy can be the alloy that contains following composition, by weight, is the aluminium of 3.0-4.0%, the vanadium of 7.5-8.5%, the chromium of 5.5-6.5%, the molybdenum of 3.5-4.5%, the zirconium of 3.5-4.5%, and all the other are titanium.Alloy is carried out hot-work, cold working, so that the compression of 5-60% to be provided, and directly aging, its total digestion time is less than 4 hours.Be defined as the various treating processess that under the temperature of the effective aging temperature that is lower than alloy, to carry out as cold working used herein.Therefore, the cold working of titanium alloy can be carried out under the temperature of the beta transus temperature that is lower than alloy.Cold working tension set workpiece when removal causes the load of distortion, can not turn back to original shape.Usually, cold worked degree is to determine with the percentage ratio that dwindles of workpiece cross-sectional area.Therefore, 5% compression that is obtained by cold working is meant and makes the cross-sectional area of workpiece dwindle 5% in the cold working process.Can use any cold processing technique in embodiment of the present invention.Useful cold processing technique comprises, but is not limited to compression process, drawing, wire drawing, trombone slide, deep-draw, rolling, special-shaped die forming, extruding, cold-heading, swaged forging, pressure-sizing, forging, drawing process, stretch forming and spinning.
Can utilize cold working to improve the mechanical property of alloy, comprise hardness, yield strength and tensile strength.Yet, during cold working, can reduce ductility.Ductility is measuring of material ability that viscous deformation is not ruptured.RA in degree of drawing or the tension test is measuring as material ductility generally.Method of the present invention can be used to increase the intensity of beta-titanium alloy, can also keep good ductility simultaneously, and can significantly increase the aging response of alloy.
According to method preparation of the present invention and processing beta-titanium alloy.Then, the performance with it comprises that with use the same component alloy of conventional process of cold working and heat treatment step compares.Below this test is described in more detail.
The melt of preparation Ti38-644 alloy, and be cast as billet.The average composition that alloy has by weight percentage, is shown in table 1.The 1st billet carries out hot rolling being no more than under 1750 the temperature, cools off in annealing and the air.
Table 1: the composition of the 1st billet
| Ti | ??Al | ??V | ??Cr | ??Zr | ??Mo | ??O | ??Fe | ??C | ??N |
| Equal amount | ??3.42 | ??7.84 | ??5.95 | ??3.98 | ??4.15 | ??0.08 | ??0.13 | ??0.01 | ??0.006 |
Part is through hot rolling, annealing and air cooled billet, handle with method of the present invention, and another part is through hot rolling, annealing and air cooled billet, handle in a conventional manner, with the usefulness of making comparisons, the part of Chu Liing in a conventional manner is through hot-work, solution heat treatment and then aging then.Change the thermal treatment parameter, to estimate the influence of mechanical property.Just as known from the prior art, solution heat treatment is a kind of heat treatment step, wherein, alloy is heated to suitable temperature, and keeps for some time under this temperature, is enough to make one or more compositions of alloy to enter into sosoloid.Then this alloy is cooled off rapidly, so that one or more compositions remain in the sosoloid.It mainly is the ductility of improving under given intensity that alloy is carried out solution heat treatment.
The prior heat treatment method and the method for the present invention of several types compare.Comprise in the table 2 under various conditions by prior heat treatment method processing list 1 alloy, at room temperature carry out the result of tension test.All tensile properties of report are all measured according to ASTM E8 in the table 2.Use the maximum tensile strength (" UTS ") of stretching test measurement testpieces, 0.2% yield strength, unit elongation and RA.RA and unit elongation are the measuring of ductility of testpieces.Unit elongation is when adding stress, the elongation of testpieces.In the tensile test, unit elongation is the increasing amount of primary standard length measured after the sample breakage of raw footage, marks on testpieces usually, represents with the per-cent of primary standard length.
Table 2: the Ti-38-644 alloy characteristic of traditional method processing
Rolling and heat treated room temperature tensile data
| The temperature of solution heat treatment and in time of this temperature | The solution-treated postcooling | Aging temperature and time | Aging postcooling | UTS (ksi) | ??0.2％ ??YS(ksi) | Unit elongation (%) | RA (％) | Modulus |
| Rolling state | Rolling state | Rolling state | Rolling state | 128 | ??126 | ??30 | ??67 | ??12.5 |
| ????1400°F/1hr | Shrend | Do not have | Do not have | 130 | ??128 | ??24 | ??61 | ??12.8 |
| ????1400°F/1hr | Shrend | 900°F/8hr | Air cooling | 148 | ??138 | ??17 | ??47 | ??13.8 |
| ????1400°F/20min | Air cooling | 900°F/8hr | Air cooling | 174 | ??160 | ??17 | ??37 | ??14.1 |
| ????1400°F/20min | Air cooling | 900°F/16hr | Air cooling | 193 * | ??180 | ??5 * | ??3 * | ??14.9 |
| ????1400°F/20min | Air cooling | 900°F/24hr | Air cooling | 193 * | ??179 | ??5 * | ??4 * | ??14.8 |
| ????1400°F/20min | Air cooling | 950°F/8hr | Air cooling | 167 | ??155 | ??20 | ??46 | ??13.8 |
| ????1400°F/20min | Air cooling | 950°F/16hr | Air cooling | 184 | ??170 | ??18 | ??43 | ??14.9 |
| ????1400°F/20min | Air cooling | 950°F/24hr | Air cooling | 186 | ??174 | ??14 | ??35 | ??14.8 |
*The nearly punching press sign of=failure
The testpieces of listing in the table 2 is that to be rolled into diameter be 0.569 inch rod to the blank from 4 inches of diameters, and before aging through solution heat treatment, data in the table 2 clearly illustrate that alloy need could obtain the high strength greater than 180ksi greater than 8 hours long-time wearing out.For two tests, solution heat treatment process (following 20 minutes of 1400 (760 ℃) following 1 hour and 1400 (760 ℃)), for the Ti-38-644 rod and the silk of AMS 4957A and AMS 4958B regulation, traditional process need aging greater than 8 hours could obtain the tensile strength of minimum.After AMS 4958A was defined in hot rolling and solution heat treatment, beta-titanium alloy must obtain to be not more than 5% cold working compression, and AMS 4958A also requires alloy to stand to wear out at least 12 hours under aging temperature.In addition, owing under elevated temperature, carry out solution heat treatment and aging, can form the monoxide layer on the alloy surface.AMS 4958A also needs step of acid dipping to remove this layer.
The description of invention embodiment
The digestion time of alloy can utilize different standards to measure and represent.For example, the length of weathering process can expose total time under the temperature of oven ageing to the open air with alloy, perhaps remains on total time in the aging temperature scope with the surface of alloy or internal composition, measures.Except that other pointed out, all digestion times to embodiment of the present invention report were that alloy is exposed to the total time in the environment under desired approximately aging temperature herein, and the aging of the testpieces sample of listing in the example carries out in experimental furnace.Add the more effective device of thermalloy, for example produce convection furnace, can conduct heat rapidly, therefore can reduce and give desired performance necessary minimum digestion time alloy to alloy.Method of the present invention is not limited to embodiment described herein, comprises used special aging equipment, but comprises various other embodiments.Therefore, the embodiment of the present invention that presents herein only is the example of invention, and scope of the present invention is not limited.
Directly aging beta-titanium alloy was less than 4 hours after the embodiment of the inventive method was included in the cold working step.Before cold working, beta-titanium alloy can carry out hot-work.After hot-work and before the cold working, alloy also can be annealed.The preferred annealing temperature of beta-titanium alloy is 1425 °F (774 ℃).For utilizing the inventive method, cold working and aging before, carry out the annealed testpieces and do not carry out the annealed testpieces, its intensity shows almost consistent with ductility.
The feature and advantage of embodiment of the present invention with reference to accompanying drawing, can be better understood.
Fig. 1 is that explanation Ti-38-644 alloy stands 13% or 15% cold working compression and 950 °F (510 ℃) wear out down, and digestion time is to UTS, 0.2% yield strength, the influence of unit elongation and RA.
Fig. 2 is that explanation Ti-38-644 alloy stands 13% or 15% cold working compression and aging under 950 (510 ℃), 1000 (538 ℃) and 1050 (566 ℃), and digestion time and aging temperature are to the influence of UTS.With
Fig. 3 is that explanation Ti-38-644 alloy stands 13% or 15% cold working compression and at 950 (510 ℃), 1000 (538 ℃), or 1050 °F (566 ℃) are aging down, and digestion time and aging temperature are to the influence of RA.
Alloy test film in the table 1 is handled according to the inventive method.Should be understood that method of the present invention also is applicable to other alloy composites, do not limit method described herein and use.The application of the invention can be produced the quite high beta-titanium alloy of intensity in the quite short time, can keep ductility simultaneously.Embodiment of the present invention have been listed among the table 3-9.Every kind of situation all is after the cold working step, and testpieces is directly aging, is less than 4 hours total time.Directly aging alloy comprises the aging alloy in processing back, and does not have middle heat treatment step, such as solution heat treatment.Directly wear out and do not get rid of behind the cold working alloy and other treatment steps that carried out before the aging alloy.These processing can be mechanical workout for example, such as deburring, or chemical treatment, such as acidleach.Listed employed treatment step and the mechanical characteristics of the processing alloy sample that tension test obtains under the room temperature in each table.
Table 3-9 lists the embodiment of the inventive method that is applied to the beta-titanium alloy with table 1 composition.Cold worked amount can be any degree, in embodiments of the present invention, and the compression of the preferred cold working to 5% of beta-titanium alloy～60%.Be more preferably the cold working beta-titanium alloy to less than 35% compression.Preferably the embodiment of the inventive method comprises the compression with beta-titanium alloy cold working to 15～35%.About table 3, to test film carry out hot rolling, cold-drawn obtains 8% compression, carries out directly aging according to the temperature and time shown in each table then.The test film of describing in the table 3 is also annealed and centreless grinding before cold-drawn.In the embodiment that table 3 is listed, directly aging less than 4 hours, just very high intensity (UTS is greater than 170ksi) can be produced, and ductility (unit elongation is greater than 8%, and RA is greater than 20%) can be kept.In listed embodiment, can implement the UTS value greater than 180ksi, and up to 199ksi.Under the aging temperature of 950 (510 ℃), realized the highest UTS value, under this temperature,, just obtained the UTS of 199ksi only with 166 minutes aging total time.
By the measurement of unit elongation and RA, under the higher aging temperature of 1050 (566 ℃), be achieved high ductibility.
Table 3: stretch test result with embodiment of the present invention of 8% cold working compression
| Aging temperature (°F) [℃] | Digestion time (minute) | UTS(ksi) | ??UTS ??(MPa) | ??0.2％ ??YS(ksi) | ??0.2％ ??YS(MPa) | Unit elongation (%) | ????RA ????(％) | Modulus |
| ?- | ??0 | ??140.5 | ??969 | ??132.5 | ??913 | ????19 | ????61 | ????12.0 |
| ?950[510] | ??166 | ??199.0 | ??1372 | ??182.2 | ??1256 | ????14 | ????41 | ????14.4 |
| ?950[510] | ??170 | ??197.5 | ??1362 | ??180.6 | ??1245 | ????14 | ????35 | ????13.4 |
| ?1000[538] | ??125 | ??186.7 | ??1287 | ??168.7 | ??1163 | ????18 | ????42 | ????14.2 |
| ?1000[538] | ??200 | ??186.0 | ??1282 | ??167.5 | ??1155 | ????18 | ????41 | ????14.9 |
| ?1050[565] | ??133 | ??175.1 | ??1207 | ??156.9 | ??1082 | ????20 | ????49 | ????14.4 |
| ?1050[565] | ??182 | ??172.8 | ??1191 | ??155.3 | ??1071 | ????21 | ????52 | ????14.5 |
Listed embodiment of the present invention in the table 4, wherein test film is through hot rolling, cold-drawn to 13% compression and directly aging.In addition, the embodiment of describing in the table 4 is after hot rolling, before the cold-drawn, anneals and centreless grinding.The embodiment of the inventive method in the table 4, after 20 minutes digestion time only, presenting intensity increases significantly.Under the aging temperature of 950 (510 ℃) and 1000 (538 ℃), further aging, intensity is increased to greater than desired value in AMS 4958A and the AMS 4957B regulation.Yet aged testpieces under 1050 (565 ℃) does not obtain in the same high intensity of hanging down aged test film gained under the aging temperature.But aged test film under 1050 (565 ℃) has kept by unit elongation and the measured bigger ductility of RA.
Table 4: stretch test result with embodiment of the present invention of 13% cold working compression
| Aging temperature (°F) [℃] | Digestion time (branch) | ??UTS ??(ksi) | ??UTS ??(MPa) | ??0.2％ ??YS(ksi) | ??0.2％ ??YS(MPa) | Unit elongation (%) | ??RA ??(％) | Modulus |
| The drawing attitude | The drawing attitude | ??145.3 | ??1002 | ??137.5 | ??948 | ????17 | ????55 | ????11.0 |
| ?950[510] | ??20 | ??172.8 | ??1191 | ??163.1 | ??1124 | ????21 | ????50 | ????13.7 |
| ?950[510] | ??166 | ??203.5 | ??1403 | ??187.1 | ??1290 | ????14 | ????32 | ????15.0 |
| ?950[510] | ??170 | ??202.9 | ??1399 | ??185.8 | ??1281 | ????15 | ????36 | ????15.1 |
| ?1000[538] | ??20 | ??168.7 | ??1163 | ??156.8 | ??1081 | ????24 | ????51 | ????14.4 |
| ?1000[538] | ??125 | ??189.9 | ??1309 | ??172.1 | ??1186 | ????18 | ????44 | ????14.7 |
| ?1000[538] | ??200 | ??189.8 | ??1308 | ??173.3 | ??1195 | ????16 | ????41 | ????15.0 |
| ?1050[565] | ??20 | ??164.4 | ??1133 | ??151.3 | ??1043 | ????26 | ????51 | ????14.4 |
| ?1050[565] | ??133 | ??178.7 | ??1232 | ??161.7 | ??1115 | ????20 | ????47 | ????14.4 |
| ?1050[565] | ??182 | ??176.6 | ??1217 | ??159.3 | ??1098 | ????20 | ????52 | ????14.0 |
The embodiment of the present invention of listing in the table 5, wherein, test film is through hot rolling, cold-drawn to 13% compression and directly aging, form class is similar to the embodiment shown in the table 4.Yet the test film of listing in table 5 is not annealed and centreless grinding before cold-drawn.However, the embodiment of the present invention of listing in the table 5, the test film of manufacturing presents very high intensity and ductility.Embodiment in the table 5 when digestion time shortens to 69～72 minutes, makes beta-titanium alloy produce very high intensity (UTS is more than 190ksi).The result shows when the present invention is applied to beta-titanium alloy in the table 1 can get rid of annealing steps in embodiments of the invention, and can obviously not influence mechanical property.
Table 5: have 13% cold working compression, not the stretch test result of annealed embodiment of the present invention
| Aging temperature (°F) [℃] | Digestion time (branch) | ??UTS ??(ksi) | ??UTS ??(MPa) | ??0.2％ ??YS(ksi) | ??0.2％ ??YS(MPa) | Unit elongation (%) | ??RA ??(％) | Modulus |
| The drawing attitude | The drawing attitude | ??147.2 | ??1015 | ??141.0 | ??972 | ????18 | ????67 | ????12.4 |
| ?950[510] | ????69 | ??199.3 | ??1374 | ??181.0 | ??1248 | ????18 | ????37 | ????14.6 |
| ?950[510] | ????94 | ??199.7 | ??1377 | ??181.7 | ??1253 | ????17 | ????42 | ????15.1 |
| ?1000[538] | ????72 | ??194.7 | ??1342 | ??176.8 | ??1219 | ????20 | ????43 | ????14.5 |
| ?1000[538] | ????89 | ??190.2 | ??1311 | ??173.3 | ??1195 | ????20 | ????37 | ????14.6 |
| ?1000[538] | ????125 | ??190.8 | ??1315 | ??172.8 | ??1191 | ????16 | ????45 | ????14.5 |
| ?1000[538] | ????200 | ??191.8 | ??1322 | ??173.8 | ??1198 | ????16 | ????46 | ????15.1 |
| ?1050[565] | ????81 | ??179.0 | ??1234 | ??162.2 | ??1118 | ????24 | ????57 | ????15.0 |
| ?1050[565] | ????88 | ??178.9 | ??1233 | ??161.6 | ??1114 | ????24 | ????57 | ????14.6 |
The embodiment of the present invention of listing in the table 6, wherein, test film is through hot rolling, cold-drawn to 15% compression and directly aging.In addition, the test film in the table 6 is not annealed and centreless grinding before cold-drawn.Certain embodiments of the present invention comprise the digestion time less than 60 minutes in the table 6.Comprise that cooling is worked into the embodiment of 15% compression, the intensity that presents is higher than the embodiment that comprises cold working to 8% compression, and ductility does not have corresponding loss.The embodiment of cold working to 15% compression, under 900 °F (482 ℃) and 950 °F (510 ℃), aging total time is only after 45 minutes, just can obtain UTS greater than 190ksi, under same temperature, only after 60 minutes, the UTS of acquisition is greater than 200ksi for digestion time.
Table 6: stretch test result with embodiment of the present invention of 15% cold working compression
| Aging temperature (°F) [℃] | Digestion time (branch) | ????UTS ????(ksi) | ????0.2％ ????YS(ksi) | Unit elongation (%) | ????RA ????(％) |
| ?- | ????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 |
| ?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 | ????174.8 | ????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 |
The embodiment of the present invention of listing in the table 7, wherein, test film is through hot rolling, cold-drawn to 19% and directly aging.In addition, the embodiment of describing in the table 7 is to anneal before cold-drawn and centreless grinding.
Table 7: stretch test result with embodiment of the present invention of 19% cold working compression
| Aging temperature (°F) [℃] | Digestion time (branch) | ??UTS ??(ksi) | ??UTS ??(MPa) | ??0.2％ ??YS(ksi) | ??0.2％ ??YS(MPa) | Unit elongation (%) | ??RA ??(％) | Modulus |
| The drawing attitude | ????0 | ??153.3 | ??1057 | ??141.0 | ????972 | ????13 | ????57 | ????13.3 |
| ?950[510] | ????166 | ??210.2 | ??1449 | ??193.3 | ????1333 | ????12 | ????27 | ????14.2 |
| ?950[510] | ????170 | ??209.4 | ??1444 | ??191.6 | ????1321 | ????14 | ????31 | ????14.7 |
| ?1000[538] | ????72 | ??191.7 | ??1322 | ??173.8 | ????1198 | ????22 | ????47 | ????15.4 |
| ?1000[538] | ????89 | ??196.9 | ??1357 | ??179.3 | ????1236 | ????19 | ????32 | ????15.3 |
| ?1000[538] | ????125 | ??196.5 | ??1355 | ??179.1 | ????1235 | ????14 | ????33 | ????14.1 |
| ?1000[538] | ????200 | ??196.0 | ??1351 | ??178.6 | ????1231 | ????15 | ????40 | ????14.4 |
| ?1050[565] | ????81 | ??183.8 | ??1267 | ??166.6 | ????1149 | ????22 | ????54 | ????14.1 |
| ?1050[565] | ????88 | ??186.3 | ??1284 | ??169.0 | ????1165 | ????23 | ????52 | ????15.1 |
| ?1050[565] | ????133 | ??183.1 | ??1262 | ??165.4 | ????1140 | ????20 | ????54 | ????13.6 |
| ?1050[565] | ????182 | ??181.7 | ??1253 | ??164.5 | ????1134 | ????20 | ????50 | ????15.1 |
The embodiment of the present invention that table 8 is listed, wherein, testpieces is through hot rolling, cold-drawn to 20% compression and directly aging.In addition, the test film in the table 8 is annealed before cold-drawn and centreless grinding.Embodiment of the present invention in the table 8 has about 5% UTS to increase and the increase of 6% 0.2% yield strength, has surpassed and has used the 15% cold working embodiment of compressing.The embodiment of cold working to 20% compression has reduced ductility 5% (measuring with unit elongation) or 9% (measuring with RA).
Table 8: tension test result with embodiment of the present invention of 20% cold working compression
| Aging temperature (°F) [℃] | Digestion time (branch) | ????UTS ????(ksi) | ????0.2％ ????YS(ksi) | Unit elongation (%) | ????RA ????(％) |
| ??- | ????0 | ????155.2 | ????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 |
The embodiment of the present invention of listing in the table 9, wherein, test film is through hot rolling, cold-drawn to 25% compression and directly aging.In addition, before cold-drawn, the embodiment of describing in the table 9 is without annealing and centreless grinding.The embodiment of the present invention of listing in the table 9 shows that on average UTS has increased by about 7% and 0.2% yield strength and increased by 9%, has surpassed to use the embodiment that is worked into 15% compression.Compare with the embodiment of utilizing cold working to 15% compression, the embodiment of cold working to 25% compression reduces ductility 11% (measuring with unit elongation) or 2% (measuring with RA).
Table 9: stretch test result with embodiment of the present invention of 25% cold working compression
| Aging temperature (°F) [℃] | Digestion time (branch) | ????UTS ????(ksi) | ????0.2％ ????YS(ksi) | Unit elongation (%) | ????RA ????(％) |
| ????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 |
| ?950[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 property that comprises the embodiment of the present invention of cold working to 13% or 15% compression step is shown among Fig. 1-3.Fig. 1 is that digestion time is to having the explanatory view of the Ti-38-644 beta-titanium alloy sample effects of forming shown in the table 1.Wherein method comprises the step of cold working to 13% or 15% compression.For at least 60 minutes at first of aging total time, UTS and 0.2% yield strength increased sharply.For these embodiments, the UTS of testpieces just reaches 180ksi in about 30 minutes digestion time.These testpieces wear out in the test furnace in the laboratory usually, produce ageing oven heating product and therefore in producing stove more effectively seemingly, expectation can reduce total digestion time of the required usefulness of the inventive method when reaching high strength, in some cases, might need 2/3 or more more time.
Beta-titanium alloy can wear out under the temperature that is lower than the β transformation.Beta-titanium alloy aging is preferably under the temperature of 800 (427 ℃)～1100 (538 ℃) and carries out.Use for some, carry out under aging can being preferably in 900 (482 ℃)～1000 (538 ℃) of beta-titanium alloy at 800 (427 ℃)～1000 (538 ℃).
As seen from Figure 1, the ductility of the testpieces of measuring with unit elongation or RA is with reducing aging total time.Yet ductility still can obtain to surpass the UTS of 200ksi along with total digestion time slowly reduces, and has kept suitable good ductility simultaneously again.Use for some, such as automobile, snowmobile, motorcycle and other reproduce the pendulum spring of vehicle and piston-engined valve spring preferably the short period of time aging.Auto production line can comprise the installation of producing desired coiling and aging spring.For example, spring can be to reel, and wears out by ageing oven with band shape on travelling belt then.In these and other was used, beta-titanium alloy was preferably aging less than 3 hours.Preferably make beta-titanium alloy aging, even in the application for some time-sensitive, wearing out to be less than 1 hour, most preferably less than 45 minutes less than 2 hours.The alloy that the present invention produces not only can be used for spring, during other are used in addition, for example is used for surgical instrument or implant in biological medicine industry.
Fig. 2 is that explanation digestion time and aging temperature exert an influence to the UTS that comprises the beta-titanium alloy testpieces that cold working to 13% or 15% embodiment of the present invention of compressing are handled.Embodiment of the present invention are used low temperature to wear out down and have been obtained higher UTS.Can predict and since crystal be under comparatively high temps growth with since the α that processing conditions causes existing in the alloy a little volume mutually, both of these case all can produce negatively influencing to beta-titanium alloy.
Fig. 3 is that explanation digestion time and aging temperature comprise cold working to 13% or 15% embodiment of the present invention of compressing to use, reduces the influence that ductility was produced of beta-titanium alloy testpieces in the meter 1 with area.Embodiment of the present invention use comparatively high temps aging down, and testpieces produces higher ductility in time.Can predict,,, improved the ductility of beta-titanium alloy under comparatively high temps though intensity is had negatively influencing because crystal is to grow.
Made according to the method for the present invention and handle the 2nd titanium blank.The composition of the 2nd blank at three positions has been shown in the table 10.Composition to three parts of alloy is tested, and to confirm its composition, guarantees that whole billet has a good consistence and forms.
Table 10: the composition of the 2nd billet
| The source | Ti | ??Al | ??V | ??Cr | ??zr | ??Mo | ??O | ??Fe | ??C | ??N |
| The 2nd billet top | Equal amount | ??3.65 | ??7.95 | ??6.16 | ??4.06 | ??4.08 | ??0.1 | ??0.05 | ??0.01 | ??0.01 |
| The 2nd billet middle part | Equal amount | ??3.45 | ??7.9 | ??6.29 | ??4.12 | ??4.04 | ??0.1 | ??0.06 | ??0.02 | ??0.01 |
| The 2nd billet bottom | Equal amount | ??3.34 | ??7.85 | ??6.43 | ??4.14 | ??3.98 | ??0.1 | ??0.06 | ??0.01 | ??0.01 |
The method according to this invention is handled the 2nd billet, and the 2nd billet carries out hot rolling under the temperature that is no more than 1825 (996 ℃), and anneal and air in cool off.About table 11, the test film by the 2nd billet is made carries out hot rolling, and cold-drawn is carried out directly aging under the temperature and time shown in the table to obtain 16.5% compression then.Describe test film in the table 11, before cold-drawn, under the temperature that is no more than 1450 (774 ℃), anneal, and in air, cool off.The embodiment of listing in the table 11 is used direct the wearing out less than 30 minutes, has just obtained higher intensity (greater than the UTS of 190ksi), and has kept ductility (unit elongation is greater than 8%, and RA is greater than 20%).In the embodiment of listing, realized greater than 200ksi, even reached the UTS of 220ksi.Have, implemented the highest UTS value under lower aging temperature, under 900 °F (482 ℃), total digestion time has only 60 minutes, has just obtained the UTS of 220ksi.Under the higher aging temperature of 1050 (566 ℃), implemented the high ductibility of measuring by unit elongation and RA.
Table 11: to embodiment of the present invention stretch-proof test-results with 16.5% cold working compression by the 2nd billet manufacturing
| Aging temperature (°F) [℃] | Digestion time (branch) | ????UTS ????(ksi) | ????UTS ????(MPa) | ????0.2％ ????YS(ksi) | ???0.2％ ???YS(MPa) | Unit elongation (%) | ????RA ????(％) |
| ?NA | ????0 | ????164.2 | ????1132 | ????150.8 | ????1040 | ????16.1 | ????52.5 |
| ?NA | ????0 | ????154.6 | ????1066 | ????149.2 | ????1029 | ????17.9 | ????52.9 |
| ?900[482] | ????30 | ????205.5 | ????1417 | ????191.0 | ????1317 | ????11.5 | ????33.3 |
| ?900[482] | ????45 | ????207.6 | ????1431 | ????191.7 | ????1322 | ????11.5 | ????31.4 |
| ?900[482] | ????45 | ????216.0 | ????1489 | ????197.7 | ????1363 | ????10.9 | ????29.1 |
| ?900[482] | ????60 | ????220.4 | ????1519 | ????202.7 | ????1397 | ????11.0 | ????30.4 |
| ?900[482] | ????60 | ????216.2 | ????1490 | ????201.1 | ????1386 | ????10.5 | ????28.0 |
| ?NA | ????0 | ????164.2 | ????1132 | ????150.8 | ????1040 | ????16.1 | ????52.5 |
| ?NA | ????0 | ????154.6 | ????1066 | ????149.2 | ????1029 | ????17.9 | ????52.9 |
| ?950[510] | ????30 | ????198.7 | ????1370 | ????182.7 | ????1260 | ????13.7 | ????35.9 |
| ?950[510] | ????30 | ????198.7 | ????1370 | ????181.3 | ????1250 | ????14.3 | ????35.0 |
| ?950[510] | ????45 | ????207.0 | ????1427 | ????191.7 | ????1322 | ????13.7 | ????32.0 |
| ?950[510] | ????45 | ????205.1 | ????1414 | ????190.5 | ????1313 | ????12.6 | ????30.8 |
| ?950[510] | ????60 | ????210.5 | ????1451 | ????192.6 | ????1328 | ????13.8 | ????24.7 |
| ?950[510] | ????60 | ????209.3 | ????1443 | ????193.5 | ????1334 | ????13.1 | ????29.8 |
| ?NA | ????0 | ????164.2 | ????1132 | ????150.8 | ????1040 | ????16.1 | ????52.5 |
| ?NA | ????0 | ????154.6 | ????1066 | ????149.2 | ????1029 | ????17.9 | ????52.9 |
| ?1000[538] | ????30 | ????190.9 | ????1316 | ????175.2 | ????1208 | ????17.6 | ????37.0 |
| ?1000[538] | ????45 | ????197.8 | ????1364 | ????182.4 | ????1257 | ????14.0 | ????36.8 |
| ?1000[538] | ????45 | ????199.9 | ????1378 | ????182.9 | ????1261 | ????20.4 | ????35.1 |
| ?1000[538] | ????60 | ????201.5 | ????1389 | ????185.1 | ????1276 | ????- | ????34.5 |
| ?1000[538] | ????60 | ????204.7 | ????1411 | ????189.5 | ????1306 | ????16.0 | ????39.5 |
Usually, the test film that the embodiment of the inventive method of being described by table 11 is made, the testpieces of the inventive method embodiment manufacturing of describing with utilization table 3-9 is compared, and has just obtained advantages of higher tensile strength in short digestion time.Yet, totally say, the test film of describing in the table 11, ductility is all lower, can think, and the 2nd billet stands higher hot-rolled temperature, can obtain lower ductility, and this is because the high processing temperature helps the beta-particle of large-size.Consider that higher-strength is relevant with the low cooling after the annealing, so aging for some, annealing will be carried out before cold working.
Table 12 shows the result who is rotated the beam type fatigue test by the goods of the inventive method preparation, wherein goods are through hot rolling, cold-drawn to 15% compression, directly wore out 1 hour down with 950 °F (510 ℃), according to international touchstone ISO1143, in the frequency of 50Hz, R=-1 utilizes level and smooth rod, be rotated the beam type fatigue test, to measure flexural fatigue.The result is illustrated in the cycle number that preceding each sample of fracture stands, and perhaps, if do not rupture, sample is carried out the round-robin sum.
Table 12: embodiment of the present invention are rotated the result of beam type fatigue test, and the present invention program comprises that 15% cold working compression and 950 directly wore out 1 hour down.
| Maximum stress ksi | Maximum stress Mpa | Cycle number | Annotate |
| ????73 | ????500 | ????13401000 | End, not fracture |
| ????83 | ????575 | ????10017100 | End, not fracture |
| ????87 | ????600 | ????10804700 | End, not fracture |
| ????87 | ????600 | ????151900 | Fracture |
| ????91 | ????625 | ????620800 | The clamping fracture |
| ????94 | ????650 | ????525100 | Fracture |
| ????98 | ????675 | ????79300 | Fracture |
| ????102 | ????700 | ????395200 | Fracture |
Table 13 represents the goods that utilize the inventive method to prepare are carried out the axial fatigue test-results of negative load control, and wherein test film is through directly wearing out 1 hour under hot rolling, cold-drawn to 15% compression and 950 (510 ℃).According to ASTM E-466-96, use the 29Hz frequency, at R=0.1, carry out the axial fatigue test of load control, to measure the degree of fatigue of goods.Before the result represents fracture, the cycle number that each sample stands.With method of the present invention, use the goods of different condition preparations, such as long digestion time, different aging temperatures, or different degree of cold works, in fatigue test, the increase of the cycle number before all can causing rupturing.
Table 13: to the axial fatigue test-results that the negative load of embodiment of the present invention is controlled, cold working compression and 950 (510 ℃) comprising 15% directly wore out 1 hour down.
| Maximum stress ksi | Maximum stress MPa | Circulation | Annotate |
| ????142 | ????979 | ????2313507 | Fracture |
| ????145 | ????1000 | ????286613 | Fracture |
| ????150 | ????1034 | ????170773 | Fracture |
| ????160 | ????1103 | ????22532 | Fracture |
Though above beta-titanium alloy to some composition has been described the inventive method,, can think that method of the present invention has application widely, also can handle for other beta-titanium alloy.For example, the inventive method is not limited, some that can benefit from the present invention discussed in addition and sold beta-titanium alloy is the titanium alloy with following specified composition, by weight percentage.Ti-12Mo-6Zr-2Fe (alloy contains 12% molybdenum, 6% zirconium, 2% iron and titanium, and commercial a kind of form that at least can ALLVAC TMZF alloy is buied) is for example arranged; Ti-4.5Fe-6.8Mo-1.5Al (this alloy contains 4.5% iron, 6.8% molybdenum, 1.5% aluminium and titanium, and commercial a kind of form that at least can TIMETAL LCB alloy is buied); Ti-15Mo-2.6Nb-3Al-0.2Si (alloy contains 15% molybdenum, 2.6% niobium, 3% aluminium, 0.2% silicon and titanium, and commercial a kind of form that at least can TIMETAL 21S alloy is buied); Ti-15V-3Cr-3Sn-3Al (alloy contains 15% vanadium, 3% chromium, 3% tin, 3% aluminium and titanium, and commercial a kind of form that at least can ALLVAC 15-3 alloy is buied); Ti-11.5Mo-6Zr-4.5Sn (alloy contains 11.5% molybdenum, 6% zirconium, 4.5% tin and titanium, and commercial a kind of form that at least can UNITEK β III alloy is buied); And Ti-6V-6Mo-5.7Fe-2.7Al (alloy contains 6% vanadium, 6% molybdenum, 5.7% iron, 2.7% aluminium and titanium, and commercial a kind of form that at least can TIMETAL 125 alloys is buied).The alloy composition that more than provides is specified composition, and the content of every kind of element can change, at least 2% or more, and alloy also can contain other components.
Be to be understood that relevant clear understanding those aspects of the present invention of this specification sheets explanation.Some aspect of the present invention will be clearly for those skilled in the art, not promote better some aspect of understanding to the present invention, in order to simplify this specification sheets, and not provide.Though described the present invention in conjunction with some embodiment, but technician in the art according to above description, can recognize and can carry out multiple improvement and variation to the present invention, all these improvement of the present invention and variation are all covered by foregoing description and following claim.
Claims (45)
1. method of handling titanium alloy, method comprise cold working beta-titanium alloy and directly aging beta-titanium alloy, and its aging total time is less than 4 hours.
2. according to the process of claim 1 wherein, beta-titanium alloy contains a kind of in aluminium, vanadium, molybdenum, chromium and the zirconium at least.
3. according to the method for claim 1, also comprise the cold working beta-titanium alloy before, beta-titanium alloy is carried out hot rolling.
4. according to the method for claim 3, wherein the cold working beta-titanium alloy comprises that the cold working beta-titanium alloy is at least 5% compression.
5. according to the method for claim 4, wherein the cold working beta-titanium alloy comprises that the cold working beta-titanium alloy is at least 15% compression.
6. according to the method for claim 5, wherein the cold working beta-titanium alloy comprises that the cold working beta-titanium alloy is to compressing less than 60%.
7. according to the method for claim 6, wherein the cold working beta-titanium alloy comprises that the cold working beta-titanium alloy is to compressing less than 35%.
8. according to the method for claim 7, wherein the cold working beta-titanium alloy comprises that the cold working beta-titanium alloy is to compressing less than 20%.
9. according to the process of claim 1 wherein directly aging beta-titanium alloy, comprising beta-titanium alloy is carried out directly wearing out in the temperature range of about 800 (427 ℃)～about 1200 (649 ℃).
10. according to the process of claim 1 wherein directly aging beta-titanium alloy, comprising beta-titanium alloy is carried out directly wearing out in the temperature range of about 800 (427 ℃)～about 1000 (538 ℃).
11. beta-titanium alloy is carried out directly wearing out in the temperature range of about 900 (482 ℃)～about 1000 (538 ℃) according to the process of claim 1 wherein directly aging beta-titanium alloy, comprising.
12., comprise direct the wearing out of beta-titanium alloy is less than 3 hours according to the process of claim 1 wherein directly aging beta-titanium alloy.
13., comprise direct the wearing out of beta-titanium alloy is less than 2 hours according to the process of claim 1 wherein directly aging beta-titanium alloy.
14., comprise direct the wearing out of beta-titanium alloy is less than 1 hour according to the process of claim 1 wherein directly aging beta-titanium alloy.
15., comprise direct the wearing out of beta-titanium alloy is less than 45 minutes according to the process of claim 1 wherein directly aging beta-titanium alloy.
16. according to the process of claim 1 wherein by weight, beta alloy contains 3.0～4.0% aluminium, 7.5～8.5% vanadium, 5.5～6.5% chromium, 3.5～4.5% molybdenum, 3.5～4.5 zirconium and titanium.
17. a method of making fabricated product comprises, beta-titanium alloy is provided, it contains 3.0～4.0% aluminium, 7.5～8.5% vanadium, 5.5～6.5% chromium, 3.5～4.5% molybdenums, 3.5～4.5 zirconiums and titanium by weight,
Beta-titanium alloy is carried out hot-work,
Beta-titanium alloy is carried out cold working, compresses to obtain 5～60%,
Under the temperature range of about 800 (427 ℃)～about 1100 (593 ℃), beta-titanium alloy is carried out being less than total time 2 hours direct wearing out.
18. according to the method for claim 17, wherein fabricated product is a spring.
19. according to the method for claim 17, wherein, the cold working beta-titanium alloy comprises by mould cold-drawn beta-titanium alloy.
20. according to the method for claim 17, wherein, the hot-work beta-titanium alloy comprises beta-titanium alloy is processed into rod, bar, the roll coil of strip.
21. according to the method for claim 17, wherein, directly aging beta-titanium alloy, comprising wears out is less than 1 hour total time.
22. according to the method for claim 17, wherein, directly aging beta-titanium alloy, comprising wears out is less than 45 minutes total time.
23. according to the method for claim 22, wherein, directly aging beta-titanium alloy, be included in carry out under the temperature range of about 900 (482 ℃)～about 1000 (538 ℃) directly aging.
24. according to the method for claim 18, wherein, spring is automobile, snowmobile, motorcycle, reproduce the part of vehicle or engine.
25., wherein, also comprise beta-titanium alloy carried out centreless grinding and before beta-titanium alloy is carried out cold working, beta-titanium alloy annealed according to the method for claim 17.
26. according to the method for claim 25, wherein, the cold working beta-titanium alloy comprises by mould cold-drawn beta-titanium alloy.
27. according to the method for claim 17, wherein, the cold working alloy is to obtain 5～35% compression.
28. a method of handling titanium alloy comprises cold worked beta-titanium alloy is carried out being less than total time 4 hours direct wearing out.
29. according to the method for claim 28, wherein, beta-titanium alloy contains at least a in aluminium, vanadium, molybdenum, chromium and the zirconium.
30. according to the method for claim 28, also be included in the cold working beta-titanium alloy before, beta-titanium alloy is carried out hot rolling.
31. according to the method for claim 28, wherein, directly aging beta-titanium alloy is included under the temperature range of about 800 (427 ℃)～about 1200 (649 ℃), beta-titanium alloy is carried out directly aging.
32. according to the method for claim 28, wherein, directly aging beta-titanium alloy is included under the temperature range of about 800 (427 ℃)～about 1000 (538 ℃), beta-titanium alloy is carried out directly aging.
33. according to the method for claim 28, wherein, directly aging beta-titanium alloy is included in the temperature range of about 900 (482 ℃)～about 1000 (538 ℃), beta-titanium alloy is carried out directly aging.
34. according to the method for claim 28, wherein, directly aging beta-titanium alloy comprises being less than 3 hours to beta-titanium alloy is directly aging.
35. according to the method for claim 28, wherein, directly aging beta-titanium alloy comprises being less than 2 hours to beta-titanium alloy is directly aging.
36. according to the method for claim 28, wherein, directly aging beta-titanium alloy comprises being less than 1 hour to beta-titanium alloy is directly aging.
37. according to the method for claim 28, wherein, directly aging beta-titanium alloy comprises being less than 45 minutes to beta-titanium alloy is directly aging.
38. according to the method for claim 28, wherein, by weight, beta-titanium alloy contains 3.0～4.0% aluminium, 7.5～8.5% vanadium, 5.5～6.5% chromium, 3.5～4.5% molybdenums, 3.5～4.5 zirconiums and titanium.
39. utilize the goods of method for preparing, comprise cold-worked article, wherein goods contain beta-titanium alloy and
Directly aging goods is less than 4 hours goods total time.
40. according to the goods of claim 39, wherein, goods are a kind of in rod, bar or the roll coil of strip.
41. according to the goods of claim 39, wherein, by weight, beta-titanium alloy contains 3.0～4.0% aluminium, 7.5～8.5% vanadium, 5.5～6.5% chromium, 3.5～4.5% molybdenums, 3.5～4.5 zirconiums and titanium.
42. according to the goods of claim 39, wherein, directly aging beta-titanium alloy, be included under the temperature range of about 800 (427 ℃)～about 1200 (649 ℃) beta-titanium alloy is carried out directly aging.
43. according to the goods of claim 39, wherein, directly aging beta-titanium alloy comprises being less than 2 hours to beta-titanium alloy is directly aging.
44. according to the goods of claim 39, wherein, directly aging beta-titanium alloy comprises being less than 1 hour to beta-titanium alloy is directly aging.
45. according to the goods of claim 39, wherein, directly aging beta-titanium alloy comprises being less than 45 minutes to beta-titanium alloy is directly aging.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US34067101P | 2001-12-14 | 2001-12-14 | |
| US60/340,671 | 2001-12-14 | ||
| US10/165,348 US20030168138A1 (en) | 2001-12-14 | 2002-06-07 | Method for processing beta titanium alloys |
| US10/165,348 | 2002-06-07 |
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| Publication Number | Publication Date |
|---|---|
| CN1602369A true CN1602369A (en) | 2005-03-30 |
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| CNA028248570A Pending CN1602369A (en) | 2001-12-14 | 2002-06-07 | Method for processing beta titanium alloys |
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| Country | Link |
|---|---|
| US (1) | US20030168138A1 (en) |
| EP (1) | EP1466028A4 (en) |
| JP (1) | JP2005527699A (en) |
| CN (1) | CN1602369A (en) |
| AU (1) | AU2002322053A1 (en) |
| BG (1) | BG108742A (en) |
| BR (1) | BR0214771A (en) |
| CA (1) | CA2468263A1 (en) |
| NO (1) | NO20042923L (en) |
| PL (1) | PL369514A1 (en) |
| RU (1) | RU2004121454A (en) |
| TW (1) | TW593706B (en) |
| WO (1) | WO2003052155A1 (en) |
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Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2974076A (en) * | 1954-06-10 | 1961-03-07 | Crucible Steel Co America | Mixed phase, alpha-beta titanium alloys and method for making same |
| US2804409A (en) * | 1956-02-06 | 1957-08-27 | Titanium Metals Corp | Heat treating titanium-base alloy products |
| US4799975A (en) * | 1986-10-07 | 1989-01-24 | Nippon Kokan Kabushiki Kaisha | Method for producing beta type titanium alloy materials having excellent strength and elongation |
| JPH01279736A (en) * | 1988-05-02 | 1989-11-10 | Nippon Mining Co Ltd | Heat treatment for beta titanium alloy stock |
| JPH0781177B2 (en) * | 1990-10-12 | 1995-08-30 | 新日本製鐵株式会社 | Method for manufacturing β-type titanium alloy strip |
| US5201967A (en) * | 1991-12-11 | 1993-04-13 | Rmi Titanium Company | Method for improving aging response and uniformity in beta-titanium alloys |
| JPH05195175A (en) * | 1992-01-16 | 1993-08-03 | Sumitomo Electric Ind Ltd | Production of high fatigue strength beta-titanium alloy spring |
| JPH11223221A (en) * | 1997-07-01 | 1999-08-17 | Nippon Seiko Kk | Rolling bearing |
| US6258182B1 (en) * | 1998-03-05 | 2001-07-10 | Memry Corporation | Pseudoelastic β titanium alloy and uses therefor |
| US6402859B1 (en) * | 1999-09-10 | 2002-06-11 | Terumo Corporation | β-titanium alloy wire, method for its production and medical instruments made by said β-titanium alloy wire |
-
2002
- 2002-06-07 CA CA002468263A patent/CA2468263A1/en not_active Abandoned
- 2002-06-07 WO PCT/US2002/018269 patent/WO2003052155A1/en not_active Application Discontinuation
- 2002-06-07 BR BR0214771-8A patent/BR0214771A/en not_active IP Right Cessation
- 2002-06-07 PL PL02369514A patent/PL369514A1/en unknown
- 2002-06-07 JP JP2003553022A patent/JP2005527699A/en not_active Withdrawn
- 2002-06-07 AU AU2002322053A patent/AU2002322053A1/en not_active Abandoned
- 2002-06-07 CN CNA028248570A patent/CN1602369A/en active Pending
- 2002-06-07 US US10/165,348 patent/US20030168138A1/en not_active Abandoned
- 2002-06-07 RU RU2004121454/02A patent/RU2004121454A/en not_active Application Discontinuation
- 2002-06-07 EP EP02756143A patent/EP1466028A4/en not_active Ceased
- 2002-06-28 TW TW091114485A patent/TW593706B/en active
-
2004
- 2004-06-03 BG BG108742A patent/BG108742A/en unknown
- 2004-07-08 NO NO20042923A patent/NO20042923L/en not_active Application Discontinuation
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN105951017A (en) * | 2010-07-19 | 2016-09-21 | 冶联科技地产有限责任公司 | Processing of Alpha/Beta Titanium Alloys |
| CN103341520A (en) * | 2013-07-04 | 2013-10-09 | 中国科学院金属研究所 | Preparation process of TB9 titanium alloy wire with rectangular section |
| TWI645055B (en) * | 2018-01-10 | 2018-12-21 | 大田精密工業股份有限公司 | Golf club head alloy and method for fabricating same |
| CN114921684A (en) * | 2018-05-07 | 2022-08-19 | 冶联科技地产有限责任公司 | High-strength titanium alloy |
| CN114921684B (en) * | 2018-05-07 | 2023-10-31 | 冶联科技地产有限责任公司 | High strength titanium alloy |
| CN112317993A (en) * | 2021-01-04 | 2021-02-05 | 西安稀有金属材料研究院有限公司 | Preparation method of Ti35HS titanium alloy welding wire material |
| CN115612876A (en) * | 2022-10-31 | 2023-01-17 | 洛阳双瑞精铸钛业有限公司 | Preparation method of beta-type titanium alloy plate |
| CN115612876B (en) * | 2022-10-31 | 2023-11-14 | 洛阳双瑞精铸钛业有限公司 | Preparation method of beta-type titanium alloy plate |
Also Published As
| Publication number | Publication date |
|---|---|
| BG108742A (en) | 2005-03-31 |
| PL369514A1 (en) | 2005-04-18 |
| WO2003052155A1 (en) | 2003-06-26 |
| US20030168138A1 (en) | 2003-09-11 |
| BR0214771A (en) | 2004-12-14 |
| NO20042923L (en) | 2004-07-08 |
| EP1466028A1 (en) | 2004-10-13 |
| RU2004121454A (en) | 2005-06-10 |
| JP2005527699A (en) | 2005-09-15 |
| TW593706B (en) | 2004-06-21 |
| CA2468263A1 (en) | 2003-06-26 |
| EP1466028A4 (en) | 2005-04-20 |
| AU2002322053A1 (en) | 2003-06-30 |
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