CN107406918A - Alpha-beta Type Titanium Alloy - Google Patents
Alpha-beta Type Titanium Alloy Download PDFInfo
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- CN107406918A CN107406918A CN201680017462.1A CN201680017462A CN107406918A CN 107406918 A CN107406918 A CN 107406918A CN 201680017462 A CN201680017462 A CN 201680017462A CN 107406918 A CN107406918 A CN 107406918A
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
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Abstract
A kind of alpha-beta Type Titanium Alloy is provided, it has the high intensity of the alpha-beta Type Titanium Alloy grade representated by Ti-6Al-4V and excellent hot-workability, and more excellent machinability is shown than the Ti-6Al-4V.The alpha-beta Type Titanium Alloy, it is characterised in that contain Cu in terms of quality %：0.1~2.0% and Ni：0.1~2.0% at least one of element, Al：2.0~8.5%, C：0.08~0.25%, and Cr：0~4.5% and Fe：0~2.5% at least one of element, add up to 1.0~7.0%, surplus is made up of Ti and inevitable impurity.
Description
Technical field
The present invention relates to alpha-beta Type Titanium Alloy.More particularly to the alpha-beta Type Titanium Alloy that machinability is excellent.
Background technology
High intensity alpha-beta Type Titanium Alloy representated by Ti-6Al-4V, in addition to light weight, high intensity, highly corrosion resistant,
It easily can also change strength grade by heat treatment, therefore largely be used centered on airplane industry all the time.
In order to further apply flexibly these characteristics, in recent years, towards auto parts as the engine component of automobile and motorcycle, with height
The consumer product fields such as the sports goods headed by golf ball articles for use, civil construction former material, various tool-class, spectacle-frame, and
Deep-sea and energy development purposes etc. are also being promoted using expanding.
As the alpha-beta Type Titanium Alloy, such as in patent document 1, a kind of excellent alpha-beta type of fatigue strength is disclosed
The manufacture method of titanium alloy extrded material and the alpha-beta Type Titanium Alloy extrded material.Specifically disclose, as alpha-beta type
Titanium alloy extrded material, it contains C, Al of ormal weight, and containing V, Cr, Fe, Mo, Ni, Nb, Ta any one, add up to
2.0~10.0%, the area occupation ratio of primary alpha phase is in certain limit, more than 80% primary α crystal grain among the primary alpha phase
Major diameter direction be in as defined in angular range, also, the average minor axis of secondaryαphase is more than 0.1 μm.
In addition, as the alpha-beta Type Titanium Alloy for improving forgeability, in patent document 2, disclose one kind and compare Ti-
The intensity of 6Al-4V alloys is high, castability excellent casting alpha-beta Type Titanium Alloy.Specifically, a kind of alpha-beta is disclosed
Type Titanium Alloy, it contains Al, Fe+Cr+Ni and C+N+O of ormal weight, further according to need the also V containing ormal weight, surplus by
Ti and the impurity that can not be kept away are formed.
But alpha-beta Type Titanium Alloy, in addition to very high manufacturing cost, particularly machinability is poor, this turns into alpha-beta
The obstacle that Type Titanium Alloy application expands, present situation is that use range is limited.In view of such actual conditions, in recent years, are proposed
Having improves the various titanium alloys of machinability.
Such as in patent document 3, description has a kind of connecting rod titanium alloy, and it makes rare earth element (REM, Rare
Earth Metal) and Ca, S, Se, Te, Pb, Bi suitably contain, by forming granular compound, while suppress toughness, extend
The reduction of property, while improving machinability.In patent document 4, also describing has one kind to cut titanium alloy soon, and it passes through containing dilute
Great soil group element improves machinability, by improving hot-workability containing B.
In patent document 5, description has a kind of free-cutting titanium alloy, as being whittled into soon point, except add P and S, P and Ni,
Or beyond P and S and Ni these elements, REM is also added, and it is achieved in the miniaturization of the ductility reduction and field trash of matrix, one
Side improves free-cutting, while ensuring hot-workability, and suppresses the reduction of fatigue strength.
In addition in patent document 6, as machinability and the alpha-beta Type Titanium Alloy having superior hot workability, disclose and contain
There are C, Al of ormal weight, and from V, Cr, Fe, Mo, Ni, Nb, Ta of each ormal weight β stabilizing element groups, contain one
Kind is two or more, adds up to 2.0~10%, surplus is made up of Ti and impurity, and the average area rate of the TiC precipitates in tissue is
Less than 1%, and the average value of the average equivalent circular diameter of TiC precipitates is less than 5 μm.
Look-ahead technique document Prior Art
Patent document
Patent document 1：JP 2012-52219 publications
Patent document 2：JP 2010-7166 publications
Patent document 3：JP 6-99764 publications
Patent document 4：JP 6-53902 publications
Patent document 5：No. 2626344 publication of patent
Patent document 6：JP 2007-84865 publications
But separate out metallic inclusion using REM as so above-mentioned patent document 3 and patent document 4, or as upper
State patent document 5 and so energetically form P field trashes containing P, control the chi of TiC precipitates as patent document 6 in addition
In very little method, the precipitation of these precipitates and field trash, easily by the temperature and cooling velocity of melting-forging process
Influence, it is believed that the size of the precipitate etc. is difficult to control.According further to the shape and size of former material, above-mentioned precipitate and field trash
Size etc. deviation also easily occurs.Therefore, in order that target Inclusion Precipitation and obtain excellent machinability, have and manufacturing
Need tightly to manage the problem of such in process.
The content of the invention
Done currently invention addresses above-mentioned such situation, it is intended that realizing a kind of alpha-beta Type Titanium Alloy, it is not required to
Tight management of above-mentioned manufacturing process etc. is carried out, but still there is the alpha-beta Type Titanium Alloy etc. representated by the Ti-6Al-4V
The high intensity and excellent hot-workability of level, and show the machinability more excellent than the Ti-6Al-4V.
The alpha-beta Type Titanium Alloy of the invention of above-mentioned problem is can solve the problem that, has the feature that, is contained in terms of quality %
Cu：0.1~2.0% and Ni：0.1~2.0% at least one of element, Al：2.0~8.5%, C：0.08~0.25%,
And Cr：0~4.5% and Fe：0~2.5% at least one of element, add up to 1.0~7.0%, surplus is by Ti and can not
The impurity avoided is formed.
The alpha-beta Type Titanium Alloy, can also also it be contained from V in terms of quality %：Higher than 0% and below 5.0%, Mo：It is high
In 0% and below 5.0%, Nb：Higher than 0% and below 5.0% and Ta：Formed higher than 0% and below 5.0%
More than one the element selected in group, add up to higher than 0% and below 10%.
The other alpha-beta Type Titanium Alloy, can also also contain Si in terms of quality %：Higher than 0% and below 0.8%.
In accordance with the invention it is possible to provide a kind of alpha-beta Type Titanium Alloy, it has the alpha-beta type titanium representated by Ti-6Al-4V
The hot-workability such as the high intensity of alloy grade and excellent forgeability, and show more excellent than the Ti-6Al-4V
Machinability, it can be ensured that good life tools.
Brief description of the drawings
Fig. 1 is the microphotograph of the titanium alloy of the present invention.
Embodiment
The present inventors study with keen determination repeatedly in order to solve the problem.Its result find, especially by make Cu and
Ni at least one of contained with ormal weight, then the ductility under high temperature greatly improves, especially because the drop of deformation drag
It is low, during machining chip can be formed very thin, cutting resistance step-down, you can machinability improves.Hereinafter, for the present invention's
The composition composition of alpha-beta Type Titanium Alloy, is illustrated in order from Cu, Ni as the feature of the present invention.
Cu：0.1~2.0%, and Ni：0.1~2.0% at least one of element
It is dissolved in the α phases and β phases of these elements in the alloy, increases the ductility under high temperature, improve hot-workability.
Thus cutting resistance step-down is particularly, machinability improves.These elements can be used alone, can also two kinds be used in combination.It is if each
The content of element is less than 0.1%, then the effect that above-mentioned ductility improves is small.Therefore the content for making each element is more than 0.1%.Respectively
The content of element is preferably respectively more than 0.3%, more preferably respectively more than 0.5%.On the other hand, if the content of each element is high
In 2.0%, then hardness rises, so that the reduction of the hot-workabilities such as reduction and the forgeability of machinability easily occur.Therefore make
The content of each element is less than 2.0%.The content of each element is preferably respectively less than 1.5%, more preferably respectively 1.0% with
Under.
Al：2.0~8.5%
Al is α stabilizing elements, in order that α phases generate and be allowed to containing.If Al amounts are less than the generation of 2.0%, α phases
It is few, it cannot get sufficient intensity.Therefore Al amounts are more than 2.0%.Al amounts be preferably more than 2.2%, more preferably 3.0% with
On.On the other hand, if Al amounts become superfluous higher than 8.5%, ductility deterioration.Therefore Al amounts are less than 8.5%.Al amounts are excellent
Elect less than 8.0%, more preferably less than 7.0%, more preferably less than 6.0% as.
C：0.08~0.25%
C is the element for showing strength-enhancing effect, in order to play this effect, it is necessary to make C amounts be more than 0.08%.C amounts
Preferably more than 0.10%.On the other hand, if C amounts are higher than 0.25%, the thick TiC not being dissolved in α phases is remained, machinery
Deterioration in characteristics.Therefore C amounts are less than 0.25%.C amounts are preferably less than 0.20%.
Cr：0~4.5% and Fe：0~2.5% at least one of element, add up to 1.0~7.0%
These elements are β stabilizing elements.These elements can be used alone, can also two kinds be used in combination.On playing
Effect is stated, it is necessary to make these elements add up to more than 1.0%.The content of these elements preferably adds up to more than 2.0%, more preferably
Add up to more than 3.0%.As described above, total amount is more than 1.0% to the lower limit of the content of these elements, and each element contains
The lower limit of amount is not particularly limited.The lower limit of the content of each element is, for example, to make Cr containing sometimes can be more than 0.5%, energy
Enough is further more than 1.0%.It can be further more than 1.0% containing that can be more than 0.5% sometimes to make Fe.
On the other hand, during the total amount surplus of these elements, ductility can also deteriorate.Therefore these elements add up to
Less than 7.0%.It is preferred that adding up to less than 5.0%, less than 4.0% is more preferably added up to.In the range of above-mentioned total amount,
If Fe amounts are superfluous, the reduction of ductility can also become notable.Therefore Fe amounts suppress below 2.5%.Fe amounts are preferably
Less than 2.0%.When Cr amounts are superfluous in addition, machinability reduces.Therefore Cr amounts are less than 4.5%.Cr amounts be preferably 4.0% with
Under, more preferably less than 3.0%.
The alpha-beta Type Titanium Alloy of the present invention, containing mentioned component, surplus is made up of Ti and inevitable impurity.As not
Evitable impurity, P, N, S, O etc. can be enumerated.In the alpha-beta Type Titanium Alloy of the present invention, P amounts suppress below 0.005%, N amounts
Suppress below 0.05%, S amounts suppress below 0.05%, and O amounts suppress below 0.25%.The alpha-beta Type Titanium Alloy of the present invention
In, it can also also contain following elements.
From V：Higher than 0% and below 5.0%, Mo：Higher than 0% and below 5.0%, Nb：Higher than 0% and 5.0%
Below and Ta：More than one the element selected in the group formed higher than 0% and below 5.0%, add up to higher than 0% simultaneously
Below 10%
These elements are β stabilizing elements.These elements may be used alone, used in two or more.In order that β
Mutually generate, preferably make these elements are total to contain more than 2.0%, more preferably add up to more than 3.0%.Total amount is higher than 0%
Can, the lower limit of the content of each element is not particularly limited.The lower limit of the content of each element is, for example, to contain V sometimes can
Can be further more than 2.0% more than 0.5%.It can be further 1.0% containing that can be more than 0.1% sometimes to make Mo
More than.It can be further more than 1.0% containing that can be more than 0.1% sometimes to make Nb.Make Ta containing sometimes can be 0.1% with
On, can be further more than 1.0%.
On the other hand, if the total amount of these elements is superfluous, ductility deterioration.It is therefore preferable that make the conjunction of these elements
Measure as less than 10%, more preferably less than 5.0%.In addition in the range of the total amount, at least any one element
When superfluous, ductility can also deteriorate.Therefore, no matter which kind of element, it is preferably to make the upper limit be less than 5.0%.Any element is more
Preferably less than 4.0%.
Si：Higher than 0% and below 0.8%
Si makes to separate out Ti in titanium alloy5Si3.During cutting, stress is in the Ti5Si3Concentrate, with the Ti5Si3Occur for starting point
Hole, chip easily disconnect.Its result thinks that cutting resistance reduces.In order to fully play this effect, preferably contain Si
More than 0.1%, more preferably more than 0.3%.
On the other hand, if Si amounts are superfluous, the intensity of titanium alloy is too high, and instrument is significantly worn away or defect, difficult cutting.Cause
This, Si amounts are preferably less than 0.8%.More preferably less than 0.7%, more preferably less than 0.6%.
As the present invention titanium alloy, can enumerate at room temperature, its tissue is made up of α phases with β phases, or by α phases, β phases and
Such as Ti2Cu and Ti2Ni etc. third phase is formed.In addition, when containing Si, there is Ti in titanium alloy as described above5Si3Separate out.
The manufacture method of the alpha-beta Type Titanium Alloy is not particularly limited, such as can be manufactured in following method.That is, melting institute
The titanium alloy of composition is stated, hot-working is carried out for its ingot bar, that is, after carrying out hot forging or hot rolling, implements annealing as needed and makes
Make.In the hot-working, ingot bar is heated to β phase transition temperatures Tβ~(Tβ+ 250) temperature field DEG C or so the, with " section of script
Rough forge of the processing than progress 1.2~4.0 or so or roughing representated by basal area after product/hot-working ", then in (Tβ- 50)
~800 DEG C or so of temperature field, it is processed the final processing than more than 1.7., can also be according to need after the final processing
To implement to anneal with 700~800 DEG C.Annealing can for example enumerate carry out 2~24 hours.Afterwards, when can also implement as needed
Effect processing.
Further, above-mentioned TβTried to achieve by following formula (1).Following formula (1) equivalent to it is gloomy forever etc., " set using the titanium alloy of d electronic theories
Meter ", light metal, Vol.42, No.11 (1992), p.614-621 in formula (1)~(3).
Boave=0.326Mdave-1.95 × 10-4Tβ+2.217…(1)
In formula (1),
Boave=Σ Xi (Bo) I ... (2)
Mdave=Σ Xi (Md) I ... (3)
TβMean β phase transition temperatures (K).
In formula (2), when each element is shown as into element i,
Boave represents element i bond order Bo average value, and Xi represents element i atom ratio, and (Bo) i represents element i's
Bond order Bo value.
In formula (3), when each element is shown as into element i,
Mdave represents element i d orbital energy parameters Md average value, and Xi represents element i atom ratio, (Md) i tables
Show element i d orbital energy parameters Md value.
Bond order Bo and d the orbital energy parameter Md of each element, is described in the table 1 p.616 of above-mentioned document.Other Xi roots
Tried to achieve according to composition composition.According to these data, the Boave and Mdave of each element containing Ti are tried to achieve, is substituted into above formula (1),
T can be calculatedβ.Further, in the publication, without C Bo and Md data, but in the present invention because C amounts are few, so ignoring
C and calculate Tβ。
The application is based on Japan's patent application filed in 26 days March in 2015 No. 2015-064275 and 2016 1
The interests of Japan's patent application 2016-009417 CLAIM OF PRIORITYs filed in the moon 21.On March 26th, 2015 applies
Japan's patent application the 2015-064275th specification full content and on January in 2016 21 filed in Japan
The full content for the specification that patent application the 2016-009417th, is quoted for the reference of the application.
Embodiment
Hereinafter, enumerate embodiment and further illustrate the present invention, but the present invention is not limited by following embodiments certainly, in energy
Implementation can certainly suitably be changed by enough meeting the scope of the forward and backward objective stated, and these are all contained in the technology of the present invention
In the range of.
[embodiment 1]
It is fabricated for trying material by following main points.By button type electric arc melting (dissolving of ボ タ ン ア ー Network), table 1 below is manufactured
The titanium alloy of shown each composition composition, its size are diameter about 40mm × high 20mm ingot bar.Further, no matter which example,
P amounts are suppressed below 0.005% respectively, N amounts suppress below 0.05%, and S amounts suppress below 0.05%, and O amounts suppress
Below 0.25%.In addition, "-" means and does not add the element in table 1.The ingot bar is heated to 1200 DEG C, with " originally
Basal area/hot-working after basal area " represented by processing compare and carry out rough forges for 2.4, then with 870 DEG C, compare processing to be
4.4 is forged and finish.Afterwards, implement, with 750 DEG C of annealing for being kept for 12 hours, to obtain for examination material.Further, such as table 1 below
Comparative example 7 shown in, in rough forge occur crackle without finish-forging.
The evaluation of forgeability
In the present embodiment, the evaluation of hot-workability is evaluated with the forgeability under hot.In detail, it is exactly basis
There is flawless to be evaluated during each forging of above-mentioned rough forge and finish-forging.That is, after each forging, the table for examination material is visually observed
Face, occur to be judged as NG during crackle, do not occur to be judged as OK during crackle.Then, when rough forge and finish-forging are OK, it is evaluated as forging
Property is excellent.
The evaluation of machinability
The evaluation as object, as follows progress machinability good using the forgeability.That is, from described for examination
On material, the test film of following sizes is extracted, cutting test is carried out with following machining conditions.Then, on machinability, use
The cutting dynamometer of キ ス ラ ー societies, model：9257B, measure the cutting of the incision direction terminated since cutting to cutting
Resistance, the average value of the cutting resistance terminated since the cutting to cutting is tried to achieve, as average cutting resistance.Then, same
Under the conditions of for as in general alpha-beta Type Titanium Alloy Ti-6Al-4V carry out cutting test when, due to average cutting resistance
For 180N, so in this embodiment 1, average cutting resistance is evaluated as machinability when lower than 180N excellent, average cutting resistance
It is poor that power is evaluated as machinability in more than 180N.
Machining condition
Test film：High 10mm × wide 10mm × long 150mm
Instrument：サ Application ドビック society superhard cutting blade S30T (nozzle 0.4mm)
サ Application ドビック society slotting cutter R390 (diameter 20mm, single-blade)
Cutting speed Vc：100m/min
Axial approach：1.2mm
Radial direction approach：1mm
Feed velocity：0.08mm/ knives
Length of cut：150mm
Cutting oil：Nothing
The measurement of tensile strength
With reference to the tensile strength for the alpha-beta Type Titanium Alloy for before, also measuring the present invention.In detail, using embodiment 1, reality
The titanium alloy of example 3 and comparative example 1 is applied, tension test is carried out with the condition of following test film shapes and following test speeds.It is tied
Fruit is that embodiment 1 is 948MPa, and embodiment 3 is 1125MPa, and comparative example 1 is 948MPa, and intensity is high, is used in general
The intensity of the Ti-6Al-4V of alpha-beta Type Titanium Alloy annealing material：896MPa shows higher intensity.
Test plate shape：ASTM E8/E8M Fig.8Specimen3
Test speed：4.5mm/min
The value of the evaluation result of above-mentioned forgeability and average cutting resistance describes in table 1 in the lump.
[table 1]
Following content as shown in Table 1.Embodiment 1~8 understands that being satisfied by composition specified in the present invention forms, can be good
Forge well, there is excellent forgeability.In addition understand, in these examples, compared to as in general alpha-beta Type Titanium Alloy
For Ti-6Al-4V, average cutting resistance is small, also possesses good machinability in the lump.
Formed in contrast, comparative example 1~7 is unsatisfactory for composition specified in the present invention, thus it is poor for forgeability, or can
The result of machinability difference.In detail, comparative example 1 because Cu and Ni which is not all contained, average cutting resistance is big.Should
Comparative example 1 is formed with the same composition of patent document 6.If by the embodiment 1~3, with containing element beyond Cu and Ni
And its amount is contrasted with the identical comparative example 1 of embodiment 1~3, then understand in order that average cutting resistance fully reduces
And obtain good machinability really, it is necessary to as the present invention, make Cu, Ni at least any one contained with ormal weight.
Example containing Ni in comparative example 2, but Ni amounts are superfluous, and comparative example 5 is the example containing Cu in addition, but Cu amounts are superfluous,
Therefore averagely cutting resistance is higher than 180N, and machinability is poor.Comparative example 3 and comparative example 6, because Cu and Ni each amount is superfluous,
So average cutting resistance is higher than 180N, machinability is poor.
Because Cu amounts are superfluous, forgeability reduces comparative example 4.Comparative example 7 is because Cu and Ni each amount is significantly superfluous, institute
So that crackle occurs in the stage of rough forge, turn into the result of forgeability difference.
[embodiment 2]
In the present embodiment, in the case of containing Si, influence to study particularly to caused by machinability.Such as table
Shown in 2, the ingot bar of various Si amounts is manufactured, is obtained similarly to Example 1 for examination material.Further, each example respectively suppresses P amounts
Less than 0.005%, N amount suppress below 0.05%, and S amounts suppress below 0.05%, and O amounts suppress below 0.25%.Separately
Outside, the "-" meaning does not add this element in table 2.
Using above-mentioned for trying material, such as following, confirmation whether there is precipitated phase, and in example 2 as intensity index and
Measure Vickers hardness.In addition, being evaluated similarly to Example 1 for forgeability, and machinability is carried out in the following manner
Evaluation.Further, with reference to before, for the No.3 of table 2, when measuring tensile strength similarly to Example 1, it is 968MPa, compares
Intensity as the Ti-6Al-4V of in general alpha-beta Type Titanium Alloy annealing material：896MPa, show higher intensity.
Whether there is the evaluation of precipitated phase
Mirror ultrafinish is carried out to section, using nitric hydrofluoric acid, after the acid treatment for carrying out crystal boundary visible level, uses FE-
SEM (Field Emission-Scanning Electron Microscope, field emission type SEM), with again
4000 times of rate, for 40 μ m of visual field sizes, 40 μm of observations for carrying out adding up to 10 visuals field.Then, more than 2 μm of diameter of equivalent circle
Precipitated phase, when above-mentioned 10 visuals field total is able to confirm that more than 5, precipitated phase is evaluated as " having ", above-mentioned 10 visuals field
When adding up to less than 4, precipitated phase is evaluated as "None".Further, in above-mentioned precipitated phase, as Ti5Si3With XRD (X-Ray
Diffraction, X-ray diffraction) separately confirm.
With a display of above-mentioned microscope observation in Fig. 1.Fig. 1 is measured for the No.3 of table 2, and arrow is analysis
Go out one of phase.
The measurement of vickers hardness hv
With load 10kgf condition is measured to vickers hardness hv at 5 points, be averaged.
The evaluation of machinability
It is good that forgeability is evaluated as similarly to Example 1, i.e., whole examples of table 2 are object, are carried out in the following manner
The evaluation of machinability.That is, from described on examination material, extracting the test film of following sizes, being cut with following machining conditions
Cut experiment.Then machinability, the cutting dynamometer of キ ス ラ ー societies, model are used：9257B, measure since cutting to
The cutting resistance of the incision direction terminated is cut, tries to achieve the average value conduct of the cutting resistance terminated since the cutting to cutting
Average cutting resistance.Then, using under the same terms for being cut as the Ti-6Al-4V of in general alpha-beta Type Titanium Alloy
During experiment, because average cutting resistance is 122N, so in this embodiment 2, it is evaluated as when averagely cutting resistance is lower than 122N
Machinability is excellent, and it is poor that average cutting resistance is evaluated as machinability in more than 122N.
Machining condition
Test film：High 10mm × wide 10mm × long 60mm
Instrument：サ Application ドビック society superhard cutting blade S30T (nozzle 0.4mm)
サ Application ドビック society slotting cutter R390 (diameter 20mm, single-blade)
Cutting speed Vc：100m/min
Axial approach：1.2mm
Radial direction approach：1mm
Feed velocity：0.08mm/ knives
Length of cut：15mm
Cutting oil：Nothing
These results describe in table 2 in the lump.[table 2]
It is as follows as shown in Table 2.That is, by the No.1 with the identical component of embodiment 1 of table 1 composition, with No.2~6, it is particularly
With contrast of the content beyond Si with identical No.2~4 of embodiment 1 of the table 1, show accordingly, by containing Si,
Average cutting resistance can be further reduced during than without Si, it is known that be able to ensure that very high machinability.On the other hand, such as
During the such Si contents surpluses of No.7 and No.8, then excessive high hardness, average cutting resistance are uprised on the contrary, and generating tool damage etc. is asked
Topic.
Claims (3)
1. a kind of alpha-beta Type Titanium Alloy, it is characterised in that contain following element in terms of quality %：
Cu：0.1~2.0% and Ni：0.1~2.0% at least one of element；
Al：2.0~8.5%；
C：0.08~0.25%；And
Cr：0~4.5% and Fe：0~2.5% at least one of element, add up to 1.0~7.0%,
Surplus is made up of Ti and inevitable impurity.
2. alpha-beta Type Titanium Alloy according to claim 1, wherein, in terms of quality % also containing it is total higher than 0% and
Less than 10% from V：Higher than 0% and below 5.0%, Mo：Higher than 0% and below 5.0%, Nb：Higher than 0% and
Less than 5.0% and Ta：More than one the element selected in the group formed higher than 0% and below 5.0%.
3. alpha-beta Type Titanium Alloy according to claim 1 or 2, wherein, also contain Si in terms of quality %：Higher than 0% and
Less than 0.8%.
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| JP2015-064275 | 2015-03-26 | ||
| JP2015064275 | 2015-03-26 | ||
| JP2016-009417 | 2016-01-21 | ||
| JP2016009417A JP6719216B2 (en) | 2015-03-26 | 2016-01-21 | α-β type titanium alloy |
| PCT/JP2016/058247 WO2016152663A1 (en) | 2015-03-26 | 2016-03-16 | α-β TITANIUM ALLOY |
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| CN107406918A true CN107406918A (en) | 2017-11-28 |
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| CN201680017462.1A Pending CN107406918A (en) | 2015-03-26 | 2016-03-16 | Alpha-beta Type Titanium Alloy |
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|---|---|
| US (1) | US20180044763A1 (en) |
| EP (1) | EP3276016B1 (en) |
| JP (1) | JP6719216B2 (en) |
| KR (1) | KR102027100B1 (en) |
| CN (1) | CN107406918A (en) |
| RU (1) | RU2695852C2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107858558A (en) * | 2017-11-23 | 2018-03-30 | 北京有色金属研究总院 | A kind of Superplastic Titanium Alloys sheet material and preparation method thereof |
| CN108559872A (en) * | 2018-06-05 | 2018-09-21 | 中国航发北京航空材料研究院 | A kind of TiAl alloy and preparation method thereof |
| CN113165032A (en) * | 2019-04-17 | 2021-07-23 | 日本制铁株式会社 | Titanium alloy sheet, method for producing titanium alloy sheet, copper foil production drum, and method for producing copper foil production drum |
| TWI818544B (en) * | 2021-05-19 | 2023-10-11 | 美商卡斯登製造公司 | Beta enhanced titanium alloys and methods for manufacturing beta enhanced titanium alloys |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6927418B2 (en) * | 2018-04-10 | 2021-08-25 | 日本製鉄株式会社 | Titanium alloy and its manufacturing method |
| JP7387139B2 (en) * | 2019-08-22 | 2023-11-28 | 国立研究開発法人物質・材料研究機構 | Titanium alloy, its manufacturing method, and engine parts using it |
| KR102544467B1 (en) * | 2022-10-05 | 2023-06-20 | 한밭대학교 산학협력단 | Chromium-added titanium alloy having stress corrosion cracking and manufacturing method thereof |
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Also Published As
| Publication number | Publication date |
|---|---|
| EP3276016B1 (en) | 2019-10-09 |
| RU2017134565A3 (en) | 2019-04-09 |
| RU2017134565A (en) | 2019-04-09 |
| EP3276016A1 (en) | 2018-01-31 |
| JP2016183407A (en) | 2016-10-20 |
| KR102027100B1 (en) | 2019-10-01 |
| US20180044763A1 (en) | 2018-02-15 |
| KR20170125981A (en) | 2017-11-15 |
| RU2695852C2 (en) | 2019-07-29 |
| JP6719216B2 (en) | 2020-07-08 |
| EP3276016A4 (en) | 2018-08-22 |
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