CN101035917A - An alloying system - Google Patents

An alloying system Download PDF

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Publication number
CN101035917A
CN101035917A CNA2005800339700A CN200580033970A CN101035917A CN 101035917 A CN101035917 A CN 101035917A CN A2005800339700 A CNA2005800339700 A CN A2005800339700A CN 200580033970 A CN200580033970 A CN 200580033970A CN 101035917 A CN101035917 A CN 101035917A
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stablizer
particle
mixture
mechanical alloying
preform
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CN101035917B (en
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查卓瑟卡兰·马格姆
张苏霞
何明光
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Agency for Science Technology and Research Singapore
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/045—Alloys based on refractory metals
    • C22C1/0458—Alloys based on titanium, zirconium or hafnium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
    • B22F2003/175—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging by hot forging, below sintering temperature
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/041—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by mechanical alloying, e.g. blending, milling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Forging (AREA)

Abstract

An alloying system for preparing a titanium alloy, the system comprising a rotating mill to mechanically alloy a mixture of elemental powders in predetermined proportions, the elemental powders including titanium particles, alpha stabilizer particles and beta stabilizer particles; wherein the mixture is mechanically alloyed using low impact energy to layer the titanium particles with beta stabilizer particles whereby sintering of the mechanically alloyed mixture produces alternate layers of alpha and beta stabilizer particles.

Description

Alloying system
Technical field
The present invention relates to prepare the alloying system of titanium alloy.Particularly, the present invention relates to prepare the alloying system of the titanium alloy that is used for cold forging.
Background technology
Titanium (Ti) alloy can be used for various structure applications.Existing Ti alloy uses the alloying element of wide region that specific desired characteristic is provided, for example tensile strength of Ti Gaoing and ductility.Usually, the Ti alloy exists with a kind of crystalline structure or exists with the mixture of two kinds of basic crystalline structure, and described two kinds of basic crystalline structure are: the α phase, and it is six side Mi Dui (HCP) structures; The β phase, it is body-centered cubic (BCC) structure.Purified titanium becomes the β phase in about 882 ℃ of experience polymorphic transformations down mutually from α.Can make the higher element of transition temperature be called as alpha stabilizers, comprise aluminium and lanthanum.Can make the lower element of transition temperature be called as the β stablizer.The β stablizer is divided into two classes: similar shape (isomorphous) β stablizer, for example zirconium, molybdenum, niobium and vanadium; Eutectoid (eutectoid) β stablizer, for example iron, cobalt, chromium and nickel.A kind of common high strength Ti alloy comprises as the vanadium of β stablizer with as the aluminium (Ti-6Al-4V) of alpha stabilizers.This Ti alloy is used for aircraft industry and medical implant.
In order to improve the intensity of Ti, in the Ti sill, add alloy addition, for example aluminium, vanadium, zirconium, molybdenum.Alloy addition reduces or the α phase of rising Ti or the polymorphic transformation temperature of β phase, or helps to improve its density.Therefore, be added with the result of alloy addition that limit the quantity of to avoid not expecting.For example, add aluminium reducing density, and the vanadium that adds as similar shape β stablizer can improve ductility.Yet, at room temperature, but aluminium stable alpha phase.If additive containing aluminium greater than 5wt%, then causes forming in the alloy intermetallic compound, this can limit the workability of alloy.Excessive vanadium additive can increase the density of alloy, thereby increases its weight.
Usually, the Ti alloy is heated to 900 ℃, is higher than its beta transus temperature (882.5 ℃), and under beta transus temperature, crystalline structure becomes the BCC structure with 48 activation slip systems from the HCP structure with 3 activation slip systems.Forge and carry out by the following method: with extremely about 900 ℃ of blank heating; Described blank is transferred to maintenance mould at a lower temperature; Material is forged into desired shape.Another kind method is the isothermal forging of Ti alloy, wherein blank and mould is heated to about 900 ℃ jointly.
Especially, titanium alloy is suitable as biomedical implants very much, because:
They have biocompatibility;
They have high strength;
Their hardness is about 5 times (steel or cochrome are 10 times) of cortical bone;
They than steel or cochrome gently and finer and close;
(220GPa) compares with stainless steel, and their Young's modulus is about 110GPa, and cortical bone is about 18-20GPa;
Titanium sintering globule or fiber are the excellent base materials that can make bone grow therein or grow on it.
The tooling cost height of Ti alloy is because need processing to surpass 900 ℃ pyritous speciality tool and environmental chamber.Therefore need handle the Ti alloy inexpensively, and develop the new Ti alloy of also not imagining.
Summary of the invention
First preferred aspect, the invention provides the alloying system that is used to prepare titanium alloy, described system comprises:
To the grindstone that the mixture of the element powders (elemental powder) of predetermined proportion carries out mechanical alloying, described element powders comprises titanium particle, alpha stabilizers particle and β stablizer particle;
Wherein, with described mixture mechanical alloying,, generate α and β stablizer particulate alternating layer (alternate layers) with low striking energy so that the titanium particle carries out sintering to the mixture through mechanical alloying then with β stablizer particle stratification.
The element powders mixture can mechanical alloying in inert atmosphere.
The typical impact of tumbling mill (tumbler mill) can speed can be 0-1 joule/(hit) down, and impact speed is similar to the rotating speed magnitude.As a comparison, the striking energy of high-energy planetary-type grinding machine depends on 200 joules/times of commentaries on classics scooters, and the magnitude of impact speed is apparently higher than rotating speed.Provided the impact kinetic energy of the various shredders that use in the mechanical alloy metallization processes below:
Oscillating mill Planetary ball mill Horizontal shredder
Attritor [27] Pulv.O [27] SPEX [27] Pulv.PS [27] G7 [18，19] G5 [18，19] MHRM (the present invention)
Bead speed (m/s) 0-0.8 0.14-0.24 ＜3.9 2.5-4 0.24-6.58 0.28-11.24 0-1.247
Kinetic energy (10 -3Under the J/) ＜10 3-30 ＜120 10-400 0.4-303.2 0.53-884 0-190
Frequency of impact (Hz) ＞100 15-50 200 About 100 (5.0-92.4 5 beads) (4.5-90.7 5 beads) (0-2.4 1 rod)
Power (W/g bead or rod) ＜0.001 0.005-0.14 ＜0.24 0.01-0.8 0-0.56 0-1.604 0-0.1
The striking energy of tumbling mill depends on the diameter and the rotating speed of used cylinder.In one embodiment of the invention, adopting diameter is the cylinder of 100mm and 65 rev/mins rotating speed.
Grindstone can be a tumbling mill.Depend on required phase distribution pattern, the charging of tumbling mill and the volume ratio of bead are 1: 2 or higher.Tumbling mill can use Al 2O 3Bead.Little spherical diameter can be 5,10 and 20mm, and its ratio is 40: 40: 20.The rotating speed of tumbling mill can be 65-70 rev/min.
Tumbling mill can carry out asynchronous rotation to the mid point of cylinder top and bottom with elliptical orbit, impels charging and bead to move in cylinder, and for each rotation, little pellet impact is on new surface.The track of cylinder can be a spiral-line, to guarantee evenly.This makes owing to impact the temperature rising minimum that causes, because the impact on same position is also discontinuous, thereby produces required distribution mutually.In one embodiment, can use laboratory scale model, the diameter that adopts closed at both ends is that 100mm, long cylindrical tube for 180mm are as mixing drum.
Preferably, β stablizer particle comprises the zirconium as the similar shape stablizer of 1-5wt%.
Preferably, β stablizer particle comprises the iron as the eutectoid stablizer of 1-2wt%.
Preferably, the alpha stabilizers particle comprises the aluminium of 2-4wt%.
Preferably, inert atmosphere is an argon.
Titanium alloy by the present invention's preparation has the ultimate tensile strength (UTS) of 650-800MPa.The Young's modulus of titanium alloy is 40-45GPa.After the forging, the Young's modulus of titanium alloy is about 40GPa.
In second aspect, the invention provides the method for preparing titanium alloy, described method comprises:
Mixture to the element powders of predetermined proportion carries out mechanical alloying, and described element powders comprises titanium particle, alpha stabilizers particle and β stablizer particle;
Wherein, with described mixture mechanical alloying,, generate α and β stablizer particulate alternating layer with low striking energy so that the titanium particle carries out sintering to the mixture through mechanical alloying then with β stablizer particle stratification.
Advantageously, through the mixture of mechanical alloying the forging of titanium alloy is being lower than under its recovery temperature carries out.Usually, recovery temperature is less than 380 ℃.Preferably, depend on the complicacy of part to be forged and the design of preform, titanium alloy forges down at 200-400 ℃.
The element powders mixture can mechanical alloying in inert atmosphere.
Described method also can comprise the step of screening through the mixture of mechanical alloying.Can use 325 mesh sieves, with from through the mixture of mechanical alloying, removing bead and pollutent.
Described method also can comprise the step that the mixture through mechanical alloying is pressed into preform.Described mixture can be pressed into the mould spherolite (die pellet) of stretching rod and 10mm.
Described method also can comprise the step of sintering preform with fixed mixture through mechanical alloying.Preform can be at 1110-1300 ℃ sintering temperature.But preform sintering 1-2 hour.Sintering can take place in inert atmosphere (for example argon).
Can be preform and prepare forging mold.Described method also can comprise preform is positioned at step in the forging mold.
Described method also can comprise and will cause predetermined shape (for example hip joint stalk) through agglomerating preform isothermal forging.
Described method also can comprise equipment (tooling) and the preform isothermal heating step to 200-500 ℃.
Preferably, under 200-350 ℃ temperature, isothermal forging is through the agglomerating preform under the rate of stressing of 0.5-1 crust/second (18-37Kg/s).Can under the rate of stressing of 0.1-10MPa/s, forge through the agglomerating preform.
Can make and with lubricator forge through the agglomerating preform.Lubricant can be graphite or molybdenumdisulphide.
Advantageously, the cold forging of titanium alloy provides better surface smoothness, lower tooling cost, has reduced expensive facility investment, has improved dimensional precision, has realized the precise shape forging.
In the third aspect, the invention provides the titanium base alloy of forming by following alloy compositions basically:
The zirconium of about 1-5wt%;
The iron of about 1-2wt%;
The aluminium of about 2-4wt%.
Description of drawings
With reference now to accompanying drawing, embodiments of the invention are described, wherein:
Figure 1A is the synoptic diagram that the tumbling mill of powder motion is shown;
Figure 1B is the synoptic diagram that cylinder top and bottom centre rotate along elliptical orbit;
Fig. 2 is the process flow sheet of preparation titanium alloy;
Fig. 3 is the XRD spectra of form and a kind of concrete composition of titanium alloy composition;
Fig. 4 is a kind of XRD spectra and microstructure synoptic diagram thereof of concrete composition, said composition by mechanical alloying 40 hours and under 1250 ℃ in argon sintering 2 hours;
Fig. 5 is tensile strength and the strain of composition under average room temperature and high temperature;
Fig. 6 is the STA Thermogram of two kinds of compositions, shows the DTA spectrum variation that phase transformation causes.
Embodiment
Referring to Figure 1A and 1B, alloying system 10 is provided, be used to prepare titanium alloy and forge described titanium alloy being low to moderate under 200-400 ℃ the temperature.Described system comprises tumbling mill 20.Tumbling mill 20 in preferred inert atmosphere (for example argon) with mixture 22 mechanical alloyings of element powders.The element powders 22 of weighing predetermined proportion.Element powders 22 comprise the titanium particle,, alpha stabilizers particle (aluminium) and β stablizer particle (iron and zirconium).Use the low striking energy that provides by tumbling mill 20 with mixture 22 mechanical alloyings, so that the titanium particle is with β stablizer particle stratification.Referring to Figure 1B, a series of photos show, tumbling mill 20 can carry out asynchronous rotation to the mid point of cylinder top and bottom with elliptical orbit.This impels charging 22 and bead 21 to move in cylinder, and for each rotation, bead 21 impacts on new surface.The track of cylinder is a spiral-line, to guarantee evenly.This makes owing to impact the temperature rising minimum that causes, because the impact on same position is also discontinuous, thereby produces required distribution mutually.In the process of the mixture of mechanical alloying, generate α and β stablizer particulate alternating layer at sintering.
Referring to Fig. 2, in step 30, weighing is the powder 22 of ratio separately, is respectively Fe and the Zr of 1-5wt% and the Ti of surplus of Al, the 1-3wt% of 1-3wt%.Keep less alloy addition Fe and Zr, this mainly is because they are respectively to the influence of creep resistance and resistance of oxidation.The mutual diffusion coefficient of Fe in Ti is higher, and cooling the time has residual β phase.The Fe alloy addition helps to improve the proof strength of alloy, but reduces the low-temperature toughness of Ti alloy.With the volume ratio of 1: 2 charging and bead with powder 22 and Al 2O 3Grind bead and insert plastic containers together.The diameter of bead 21 is 5,10 and 20mm, and its ratio is respectively 40: 40: 20% of bead 21 sums.The rotating speed of roll-type mixing machine 20 is set to 65-70 rev/min.In step 31, powder 22 was carried out in roll-type mixing machine 20 alloying 8-48 hour.This can make in the mixture 22 each reach best of breed mutually.That is, make coating β phase particulate thin layer on the α phase particle.
Tumbling mill 20 can't cause particle to wear away and pollute mixture 22 from bead 21, and pollution can make the character variation of alloy mixture.One of reason is that tumbling mill 20 has used low striking energy.Roll-type mixing machine 20 exposes each titanium particulate surface newly in each circulation of rolling.This has improved the homogeneity that distributes mutually.In order to carry out alloying, the striking energy of tumbling mill is very low.Tumbling mill 20 forms the top coat of the thin β phase of one deck on the Ti particle.In sintering process, generate α phase and β alternating layer mutually.β exists to help distortion mutually mainly as crystal boundary, and α is unaffected relatively mutually.
After mechanical alloying, open plastic containers 23 carefully to avoid the oxidation of powder 22.In step 32,,, collect powdered mixture 22 then through mechanical alloying to remove bead 21 and all contaminants with the content screening of plastic containers 23.Sieve powdered alloy 22 with 325 mesh sieve (not shown).Remove powdered alloy 22, it is carried out XRD analysis and sem analysis, be used for forming mutually and morphological research.
Next, in step 33, powder 22 is placed the preform (not shown), and in step 34, be pressed into the stretching sample.Use assembled preform mould (not shown) under the pressing pressure of 400-600MPa (about 25 tons power), the powder 22 through mechanical alloying to be suppressed.Powdered alloy 22 is pressed into the mould spherolite (not shown) of stretching sample and 10mm.
In step 35, under 1250 ℃, in argon with downtrodden powder sintered 2 hours through mechanical alloying.Perhaps, can be in a vacuum with its sintering.Depend on compositions for use, the hardness of preform is maintained at 280-370Hv.Fig. 3 provides the form of test with composition.In sintering process, the ratio that changes each phase is to provide more uniform distribution.β is white crystal grain mutually, and α is the lead particle mutually.Form by comparing with the standard microstructure and analyzing with the part of observing crystal grain by some EDX, can qualitative definite α mutually with β mutually.α mutually with β uniform distribution from the teeth outwards all basically mutually.The intermetallic compound that can see formation is the lead globule on the crystal grain.Referring to Fig. 5, behind elevated temperature, intensity increases, and strain simultaneously also increases.The increase of intensity conforms to STA observation, and observes phase transformation by XRD.Referring to Fig. 3 and 4, they show the XRD spectra of composition 6 after the mechanical alloying and the microstructure of composition 6.
Design preform (not shown) has the basic configuration of hip joint stalk, being positioned in the forging mold (not shown) through the agglomerating preform.Design and produce forging mold based on required net shape.Mould and heating component are placed in the mold base (not shown) between slide block and base plate.In step 36,, in heat-processed, make its drying then with the lubricated mould wall of molybdenumdisulphide coating.Perhaps, also can use graphite as forging lubricant.Graphite produces smooth surface, but it is not effectively lubricant.Advantageously, MoS 2Can make the forging zero defect.In step 37, use the strip heater (not shown) forging mold to be heated to 200-500 ℃ temperature.
In step 38, preform is placed mold heat cavity and location, then to avoid the non-uniform Distribution of power in the forging process.In step 39, under 200-350 ℃ differing temps (step-length is 30 ℃), under the rate of stressing of 0.5-10 crust/second (0.05-1MPa/s), forge.Forging under 200 ℃ and 230 ℃ of step 39 needs extremely low rate of stressing.At this moment the rate of stressing of Cai Yonging can be controlled strain rate in forming process, thereby completes successfully forging under the situation without any defective.Comparatively speaking, forged sample needs medium strain rate finish forging under greater than 250 ℃ temperature.
In the microstructure near the cross section of the forging of hip joint stalk base portion, β phase crystal grain (white crystal grain) is elongated, and α keeps initial shape and size mutually.At neck near forging, may determine the place that is out of shape in the crystal boundary slippage, crystal grain is distortion relatively.Although reduce to cause the situation of local stress increase approaching with cross-sectional area, β phase crystal grain still elongates with the plastic flow in the adaptation material.This shows, compares with α, and β has played active effect in distortion.Therefore, this has eliminated the requirement to very high forging temperature.
Heat is analyzed
Referring to Fig. 6, with composition mechanical alloying 40 hours, sintering 2 hours in argon then.Use the transformation mutually (25 ℃) of scanning moisture analyse (not shown) test composition, up to 800 ℃.Fig. 6 shows the STA Thermogram of composition 1 and composition 6, and shows the DTA spectrum variation that phase transformation causes.
Thermogram shows that α starts from about 400 ℃ to the transformation of β phase mutually.This can change by the DTA slope of a curve finds out, and for other composition, transformation may be progressively since 100 ℃ (being shown by the variation of DTA slope of a curve).In the time of 100 ℃, all compositions present intensity and increase, and have bigger strain in damaged process.Thermogram shows that also up to 100 ℃, μ V improves, and μ V value reduces then, and this may be because independent element and matrix and the intermetallic compound of element reaction generation on every side precipitation.Yet the further rising of temperature can make the element dissolving get back in the matrix, and this helps the stable of β phase.Except that composition 1 and 2, other composition is owing to the existence stable and intermetallic compound of β phase has negative voltage.For this character is plotted on the logarithmically calibrated scale, with μ V negative value be converted on the occasion of.At complete transition point, μ V reduces to its minimum value, and this value is a negative value for most compositions, shows the transformation of β phase.Owing to can't draw logarithmically calibrated scale to negative value, therefore negative value is converted on the occasion of, and suitably regulate to reflect trend.Whole values of composition 6 are negative value, be translated on the occasion of, be reflected on the logarithmically calibrated scale.From Thermogram as can be seen, the distortion of sample or forge and under 200 ℃ and higher temperature, to carry out.
Although the present invention assigns to describe with reference to the group of alloys of aluminium, iron and zirconium, following table has been listed other alloy addition and the character thereof that can be added into Ti:
Alloying element The phase that is stabilized Stabilizer types
Aluminium α
Tin α
Vanadium β Similar shape (BCC)
Molybdenum β Similar shape
Iron β Eutectoid
Niobium β Similar shape
Tantalum β Similar shape
Silicon β Eutectoid
Chromium β Eutectoid
Zirconium β/α Similar shape
Palladium β Eutectoid
Cobalt β Eutectoid
Manganese β Eutectoid
Hafnium β/α Similar shape
Can expect that Ti alloy prepared in accordance with the present invention can be used for biomedical implants, mobile telephone cover, watchcase, spacecraft and structural partsof automobiles.Other application comprises accurate fastening piece, microphone Ti barrier film, the finger piece of wave soldering machine and the chassis of hard disk, camera or notebook computer.
It will be understood by those of skill in the art that and under the prerequisite that does not break away from broadly described scope of the present invention or spirit, can carry out various changes and modifications the present invention shown in the embodiment.Therefore, should regard these embodiments as illustrative in all respects, and nonrestrictive.
 Claims
(according to the modification of the 19th of treaty) [international office was received on November 11st, 2005 (11.11.2005)]
1. be used to prepare the alloying system of titanium alloy, described system comprises:
To the grindstone that the mixture of the element powders of predetermined proportion carries out mechanical alloying, described element powders comprises titanium particle, alpha stabilizers particle and β stablizer particle;
Wherein, with described mixture mechanical alloying,, generate α and β stablizer particulate alternating layer with low striking energy so that described titanium particle carries out sintering to the mixture through mechanical alloying then with β stablizer particle stratification.
2. system as claimed in claim 1, wherein said grindstone is a tumbling mill.
3. system as claimed in claim 2, the charging of wherein said tumbling mill and the volume ratio of bead are 1: 2.
4. system as claimed in claim 2, wherein said tumbling mill uses Al 2O 3Bead.
5. system as claimed in claim 4, the diameter of wherein said bead is respectively 5,10 and 20mm, and its ratio is 40: 40: 20.
6. system as claimed in claim 2, the rotating speed of wherein said tumbling mill is 65-70 rev/min.
7. system as claimed in claim 1, wherein said β stablizer particle comprises the zirconium as the similar shape stablizer of 1-5wt%.
8. system as claimed in claim 1, wherein said β stablizer particle comprises the iron as the eutectoid stablizer of 1-2wt%.
9. system as claimed in claim 1, wherein said alpha stabilizers particle comprises the aluminium of 2-4wt%.
10. system as claimed in claim 1, the mixture of wherein said element powders in inert atmosphere by mechanical alloying.
11. system as claimed in claim 1, the striking energy speed of wherein said grindstone are 0-1 joule/down.
12. system as claimed in claim 1, the impact speed of wherein said grindstone is essentially identical magnitude with the rotating speed of described grindstone.
13. system as claimed in claim 2, wherein said tumbling mill has the cylinder that diameter is 100mm.
14. as the system of claim 13, the track of wherein said cylinder is that spiral-line is to guarantee evenly.
15. as the system of claim 13, the mid point of wherein said cylinder top and bottom impels described powder and bead to move in described cylinder with the asynchronous rotation of elliptical orbit, makes that bead all impacts on new surface for each rotation.
16. as the system of claim 10, wherein said inert atmosphere is an argon.
17. be used to prepare the method for titanium alloy, described method comprises:
Mixture to the element powders of predetermined proportion carries out mechanical alloying, and described element powders comprises titanium particle, alpha stabilizers particle and β stablizer particle;
Wherein, with described mixture mechanical alloying,, generate α and β stablizer particulate alternating layer with low striking energy so that described titanium particle carries out sintering to the mixture through mechanical alloying then with β stablizer particle stratification.
18., also comprise the step of the described mixture through mechanical alloying of screening as the method for claim 17.
19., wherein use 325 mesh sieves to come from described described bead and the pollutent through the mixture of mechanical alloying, removed as the method for claim 18.
20., also comprise the step that described mixture through mechanical alloying is pressed into preform as the method for claim 17.
21. as the method for claim 20, wherein said mixture is pressed into the mould spherolite of stretching rod and 10mm.
22., also comprise the step of the described preform of sintering with fixed described mixture through mechanical alloying as the method for claim 20.
23. as the method for claim 22, wherein said preform is sintered under 1110-1300 ℃.
24. as the method for claim 22, wherein said preform is sintered 1-2 hour.
25. as the method for claim 24, wherein sintering occurs in the inert atmosphere.
26., also comprise and to cause predetermined shape through agglomerating preform isothermal forging as the method for claim 22.
27. as the method for claim 26, wherein said through the agglomerating preform under 200-350 ℃ temperature by isothermal forging.
28., wherein saidly under the 0.5-1 rate of stressing of crust/second, forged through the agglomerating preform as the method for claim 26.
29., wherein make with lubricator and forge through the agglomerating preform with described as the method for claim 26.
30. as the method for claim 29, wherein said lubricant is graphite or molybdenumdisulphide.
31. as the method for claim 17, wherein said β stablizer particle comprises the zirconium as the similar shape stablizer of 1-5wt%.
32. as the method for claim 17, wherein said β stablizer particle comprises the iron as the eutectoid stablizer of 1-2wt%.
33. as the method for claim 17, wherein said alpha stabilizers particle comprises the aluminium of 2-4wt%.
34. according to the titanium base alloy of the method for claim 17 preparation, described alloy is made up of following alloy compositions basically:
The zirconium of about 1-5wt%;
The iron of about 1-2wt%;
The aluminium of about 2-4wt%.

Claims (34)

1. be used to prepare the alloying system of titanium alloy, described system comprises:
To the grindstone that the mixture of the element powders of predetermined proportion carries out mechanical alloying, described element powders comprises titanium particle, alpha stabilizers particle and β stablizer particle;
Wherein, with described mixture mechanical alloying,, generate α and β stablizer particulate alternating layer with low striking energy so that described titanium particle carries out sintering to the mixture through mechanical alloying then with β stablizer particle stratification.
2. system as claimed in claim 1, wherein said grindstone is a tumbling mill.
3. system as claimed in claim 2, the charging of wherein said tumbling mill and the volume ratio of bead are 1: 2.
4. system as claimed in claim 2, wherein said tumbling mill uses Al 2O 3Bead.
5. system as claimed in claim 4, the diameter of wherein said bead is respectively 5,10 and 20mm, and its ratio is 40: 40: 20.
6. system as claimed in claim 2, the rotating speed of wherein said tumbling mill is 65-70 rev/min.
7. system as claimed in claim 1, wherein said β stablizer particle comprises the zirconium as the similar shape stablizer of 1-5wt%.
8. system as claimed in claim 1, wherein said β stablizer particle comprises the iron as the eutectoid stablizer of 1-2wt%.
9. system as claimed in claim 1, wherein said alpha stabilizers particle comprises the aluminium of 2-4wt%.
10. system as claimed in claim 1, the mixture of wherein said element powders in inert atmosphere by mechanical alloying.
11. system as claimed in claim 1, the striking energy speed of wherein said grindstone are 0-1 joule/down.
12. system as claimed in claim 1, the impact speed of wherein said grindstone is essentially identical magnitude with the rotating speed of described grindstone.
13. system as claimed in claim 2, wherein said tumbling mill has the cylinder that diameter is 100mm.
14. as the system of claim 13, the track of wherein said cylinder is that spiral-line is to guarantee evenly.
15. as the system of claim 13, the mid point of wherein said cylinder top and bottom impels described powder and bead to move in described cylinder with the asynchronous rotation of elliptical orbit, makes that bead all impacts on new surface for each rotation.
16. as the system of claim 10, wherein said inert atmosphere is an argon.
17. be used to prepare the method for titanium alloy, described method comprises:
Mixture to the element powders of predetermined proportion carries out mechanical alloying, and described element powders comprises titanium particle, alpha stabilizers particle and β stablizer particle;
Wherein, with described mixture mechanical alloying,, generate α and β stablizer particulate alternating layer with low striking energy so that described titanium particle carries out sintering to the mixture through mechanical alloying then with β stablizer particle stratification.
18., also comprise the step of the described mixture through mechanical alloying of screening as the method for claim 17.
19., wherein use 325 mesh sieves to come from described described bead and the pollutent through the mixture of mechanical alloying, removed as the method for claim 18.
20., also comprise the step that described mixture through mechanical alloying is pressed into preform as the method for claim 17.
21. as the method for claim 20, wherein said mixture is pressed into the mould spherolite of stretching rod and 10mm.
22., also comprise the step of the described preform of sintering with fixed described mixture through mechanical alloying as the method for claim 20.
23. as the method for claim 22, wherein said preform is sintered under 1110-1300 ℃.
24. as the method for claim 22, wherein said preform is sintered 1-2 hour.
25. as the method for claim 24, wherein sintering occurs in the inert atmosphere.
26., also comprise and to cause predetermined shape through agglomerating preform isothermal forging as the method for claim 22.
27. as the method for claim 26, wherein said through the agglomerating preform under 200-350 ℃ temperature by isothermal forging.
28., wherein saidly under the 0.5-1 rate of stressing of crust/second, forged through the agglomerating preform as the method for claim 26.
29., wherein make with lubricator and forge through the agglomerating preform with described as the method for claim 26.
30. as the method for claim 29, wherein said lubricant is graphite or molybdenumdisulphide.
31. as the method for claim 17, wherein said β stablizer particle comprises the zirconium as the similar shape stablizer of 1-5wt%.
32. as the method for claim 17, wherein said β stablizer particle comprises the iron as the eutectoid stablizer of 1-2wt%.
33. as the method for claim 17, wherein said alpha stabilizers particle comprises the aluminium of 2-4wt%.
34. the titanium base alloy of forming by following alloy compositions basically:
The zirconium of about 1-5wt%;
The iron of about 1-2wt%;
The aluminium of about 2-4wt%.
CN2005800339700A 2004-08-05 2005-08-03 An method for preparing titanium alloy Expired - Fee Related CN101035917B (en)

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CN107470385A (en) * 2017-08-02 2017-12-15 安徽骏达起重机械有限公司 Suspend track processing method in midair
CN115815595A (en) * 2023-02-02 2023-03-21 西安稀有金属材料研究院有限公司 Core-shell structure titanium-based composite powder and preparation method of net structure titanium-based composite material

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CN104550517B (en) * 2014-11-17 2016-08-24 南京航空航天大学 A kind of oil-containing slide block for steel pipe expanding head and alloy used thereof and preparation technology
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Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62287028A (en) * 1986-06-04 1987-12-12 Nippon Tungsten Co Ltd High-strength titanium alloy and its production
RU1593259C (en) * 1989-02-20 1994-11-15 Всероссийский научно-исследовательский институт авиационных материалов Titanium-base alloy
JP2824507B2 (en) * 1995-03-29 1998-11-11 工業技術院長 Method for producing titanium-aluminum intermetallic compound powder
JPH09256080A (en) * 1996-03-21 1997-09-30 Honda Motor Co Ltd Sintered friction material made of titanium or/and titanium alloy
JP3353618B2 (en) * 1996-09-03 2002-12-03 住友金属工業株式会社 High strength titanium alloy
CN2279955Y (en) * 1996-11-17 1998-04-29 中南工业大学 Rolling abrasive type high energy ball mill
JP3361072B2 (en) * 1998-02-20 2003-01-07 株式会社豊田中央研究所 Method for producing metal member having excellent oxidation resistance
US6797137B2 (en) * 2001-04-11 2004-09-28 Heraeus, Inc. Mechanically alloyed precious metal magnetic sputtering targets fabricated using rapidly solidfied alloy powders and elemental Pt metal
TW499341B (en) * 2001-04-25 2002-08-21 Li Li Ju Ti-based amorphous alloy powder with broad super-cooled liquid region and method for preparing the same

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