CN107119218A - High-intensity high-damping Ti2AlC Mg based composites and its casting preparation method - Google Patents
High-intensity high-damping Ti2AlC Mg based composites and its casting preparation method Download PDFInfo
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- CN107119218A CN107119218A CN201710232463.4A CN201710232463A CN107119218A CN 107119218 A CN107119218 A CN 107119218A CN 201710232463 A CN201710232463 A CN 201710232463A CN 107119218 A CN107119218 A CN 107119218A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
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- 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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
Abstract
The invention discloses a kind of high-intensity high-damping Ti2AlC Mg based composites and its casting preparation method.Ti in the material2AlC volume content is 5 20vol%, and remaining is Mg based alloys.The microstructure of the material is ceramic phase Ti2AlC and metal phase Mg based alloys are each continuously distributed in three dimensions, wherein ceramic phase Ti2AlC distribution of particles shows that firmly, crack initiation is in Ti for the two interface cohesion in Mg matrix grain boundaries, original position stretching experiment2In AlC crystal grain, rather than two-phase interface.Preparation method：By Mg alloys in CO2/SF6Melted under protective atmosphere and be cooled to 450 550 DEG C again, the Ti of different-grain diameter2AlC powders are added in the semisolid Mg melts of high-speed stirred.After 30 60mins of semi-solid state stirring terminate, it is reheated to 680 750 DEG C and stirs.Finally, Ti will be contained2AlC Mg melts are cast to the 100MPa of pressurize 50 in stainless steel grinding tool and are cooled to room temperature.Compared with pure Mg alloys, the material has the distinguishing features such as higher intensity, higher damping and more preferable wearability, can be widely used for the Primary Component in the fields such as space flight, military project, communications and transportation, machine-building.
Description
Technical field
The present invention relates to a kind of high-intensity high-damping Ti2AlC-Mg based composites and its casting preparation method.
Background technology
Because the limitation of the single metal of tradition, ceramic material self performance makes it be difficult to meet develop rapidly advanced
Manufacturing is to the use demand of material property, and the metal-base composites (MMC) with high specific strength, high ratio modulus characteristic goes out
Now arouse widespread concern, the magnesium-based composite material (ginseng especially with high specific strength, specific stiffness and high damping characteristic
Examine document：Schaller,R.,Journal of Alloys and Compounds,2003,[131-135]：355).For example,
Dow Chemical companies of U.S. researcher prepares Si and Al using casting2O3Strengthen AZ91 magnesium-based composite materials, succeeded
Production (bibliography for parts such as belt pulley, sprocket wheel and oil pump covers：Oakley, R., 1995.Trans Tech
Publ.。)
Different reinforcements, such as graphite, SiC, Al2O3、B4The fiber such as C and C nano pipe, whisker and particle etc. are extensive
The preparation for being applied to magnesium-based composite material and obtain it is substantial amounts of research (bibliography：Ye,H.Z.Journal of
Materials Science,2004,153-6171]:39).Wherein, chopped carbon fiber strengthens the damping capacity of magnesium base composite material
Preferably, this is due to that carbon material also has excellent damping capacity in itself.However, there is unsticking and hole in carbon fiber and matrix
Defect, is unfavorable for the raising of mechanical property.Compared to carbon fiber, SiCp has good wetability, but SiCp- with Mg matrixes
The optimal mechanical property of AZ61 magnesium-based composite materials is only obtained in SiC content 6%, and damping capacity is obtained in SiC content 3%
.By the factor of analyzing influence composite materials property and damping capacity, it can be found that a factor of reinforcing is addition
Hard crisp dispersed granules (such as SiC) On Dislocation Motion produce pinning, and excellent damping capacity needs the movement of dislocation.For
This paradox, it would be desirable to find it is a kind of possess in itself plastic deformation and again the reinforcement of high tenacity substitute it is traditional at present hard
Crisp reinforcement (such as TiC, SiC etc.), so as to reduce the dynamic pinning effect of reinforcement contraposition offsetting.Further, since reinforcement and base
The interface binding power of body is not strong, and hard crisp ceramic particle easily occurs to depart from and cause material failure with Mg matrixes.For example, king etc.
(bibliography：Wang,X.J.,et al.,Composites Science and Technology,2007,[2253-
2260]：67) finding that the SiC in SiC-AZ91D magnesium-based composite materials departs from matrix by experiment in situ causes composite to lose
Effect.Therefore, new reinforcement also needs to produce close adhesion with matrix, could more effectively improve the mechanics of composite
Performance.
Ti2The ceramic MAX material in novel tertiary laminated metal that AlC can be machined, hexagonal crystal system is belonged to together with Mg.
Ti2AlC has the hexagonal crystallographic texture of layering, and each Ti layers of its intimate solid matter intersects with Al layers, C atoms filling Ti6The eight of C
Face body position, Al atoms are then located at the center of the trigonal prism with larger space.In this special structure, Ti atoms and C
Strong covalent bond is combined between atom, and between Ti atoms and Al atoms is weak binding, similar to lamellar graphite, interlayer is by model
De Huali is combined.(bibliography：N.V.Tzenov and M.W.Barsoum, J.Am.Ceram.Soc., 2000,83 [4]:825)
Under 0.8MPa pressure and 60m/s sliding speeds, the dry friction coefficient to mild steel is about 0.1, and wear rate is about 2.510-6mm3/
Nm (bibliography：H-X Zhai, et al, Mater.Sci.Forum, 2005 [475-479]:1251) structures shape performance, ⊥
C-axis is between layers easily slided in the presence of shearing force, and occurs the bending band plastic deformation of metalloid,.
For this phenomenon, Barsoum seminars (bibliography：Barsoum,M.,et al.,Nature Materials,2003,
[107-111]:2.) the kinking Non-linear elastic deformation mechanism of MAX material is proposed, the gold for the close-packed hexagonal structure such as this is with Mg, Ti
Micro- modeling deformation mechanism (Incipent kink bands) of category is similar, and thus MAX possesses excellent damping capacity.So as to MAX
Material can turn into the preferable reinforcement of High Damping Performance structural metallic materials.Therefore, mutually answered as enhancing to strengthen Ni bases
Condensation material, can have high intensity, high-damping and wearability etc..For example, seminar researcher uses method of impregnation and powder
Metallurgy method prepares different content Ti2AlC Mg based composites, wherein, under 250MPa compression, 50%volTi2AlC/
The specific energy input coefficient of Mg based composites is 0.34MJm-3, the energy of single cycle absorbable 30% in CYCLIC LOADING experiment
Amount, this is to show optimal composite (bibliography in current all material：Anasori,B.,et al.,Magnesium
Technology 2011,[463-468]).Compared with powder metallurgic method (mechanical alloying method), molten liquid forming method, casting
The ratio damping capacity that magnesium-based composite material device prepared by technique possesses is up to 40%-60%.This is primarily due to casting technique
Under the conditions of, Mg matrixes have bigger crystal grain, dislocation are more beneficial in the movement of basal plane and the wrong generation of geminal, so that damping and amortization
Can be better.Meanwhile, stirring casting method has that process is few, technique is simple, cost is low, it is easy to produce complex-shaped part and easily
The advantages of realizing batch production.
Therefore, possesses plastic deformation in composite in itself but the Ti of high tenacity enhancing phase2AlC can be in Mg matrixes
Dislocation priming play pinning effect, while allowing the micromotion of dislocation to carry out damping at two-phase interface.As can be seen here,
Ti2AlC2- Mg based composites have excellent mechanics and damping capacity and industry should as new light structures damping material
With prospect, extensive Ti can be realized by making method by stirring cast2AlC2The production of-Mg based composites, ultimately facilitates solution modern
Some industrial key areas are to lightweight, high intensity, the market demand of the vibration-absorptive material of high damping characteristic.
The content of the invention
It is an object of the invention to provide a kind of ternary Ti of high-intensity high-tenacity2AlC cermets reinforcement and Mg bases
Alloy pig is the high intensity and high-damping Ti that raw material is made2AlC2- Mg based composites and its stirring casting preparation method.
The high-intensity high-damping Ti of the present invention2AlC2- Mg based composites, its composition is as follows：
Ti2AlC volume content is 5-20vol%, and remaining is Mg based alloys.
The Ti of the present invention2AlC/Mg based composites, its microstructure is as follows：
Ceramic phase Ti2AlC and metal phase Mg based alloys are each continuously distributed in three dimensions, wherein ceramic phase Ti2AlC
Grain is distributed in Mg matrix grain boundaries, and the two interface cohesion is firm.
The high-intensity high-damping Ti of the present invention2AlC2- Mg based composites stirring casting preparation methods, this method include with
Under each step：
Step 1, by Mg alloys in CO2/SF6Fusing is warming up under protective atmosphere, being then cooled to 450-550 DEG C again reaches
The semisolid of Mg alloys simultaneously opens agitating function, Ti2AlC powders are added in the semisolid Mg melts of high-speed stirred.
Step 2, Ti is finished in semi-solid state addition2After AlC powders, it is reheated to 680-750 DEG C and stirs 30-
60mins.Finally, Ti will be contained2AlC Mg melts are cast to pressurize 50-100MPa in stainless steel grinding tool and are cooled to room temperature, i.e.,
Obtain the Ti of two-arch tunnel2AlC-Mg based composites.
The present invention is had the advantage that：
Mechanical test shows yield strength, and Vickers hardness, compressive strength increases with the increase of enhancing phase fraction, and highest is drawn
Intensity is stretched in Ti2AlC is obtained when strengthening phase 10%, can reach 215MPa.The SiC-Mg bases of same content prepared by same procedure are answered
Condensation material tensile strength is 172MPa, and this shows Ti2AlC possesses more preferable enhancing effect.Original position stretching, which is tested, to be shown, crackle
Ti2Germinate in AlC particles and extended along α-Mg crystal boundaries, ultimately result in failure.During this, and traditional TiC, SiC and
Al2O3The reinforcement strengthened in magnesium-based composite material is different with magnesium matrix interface unbound.In addition, Ti2AlC strengthens AZ91D composite woods
The damping capacity of material increases with the increase of enhancing phase volume fraction.The Ti of the present invention2AlC2- Mg based composites stirring castings
Preparation method, it is mainly advantageous in that technique is simple, it is easy to operate, and is widely used in communications and transportation, space flight, military project, machinery system
The field such as make, such as the anti-friction bearing in the brake disc for manufacturing high-speed railway, machinery industry, turbo blade.
Brief description of the drawings
Fig. 1 is Ti2The preparation method schematic diagram of AlC-Mg based composites.
Fig. 2 is the Ti of the present invention2The backscattered electron microstructure photograph of AlC-Mg based composites.Brilliant white color part is
Ti2AlC particles, dark parts are Mg based alloys.
Fig. 3 is the Ti of the present invention2AlC-Mg based composites original position stretching experiment crack initiation Electronic Speculum (SEM) catches figure
Piece.
Fig. 4 is the Ti of the present invention2AlC-Mg based composites compress Electronic Speculum (SEM) photo of fracture.
Embodiment
The invention provides a kind of Ti2AlC-Mg based composites stirring casting preparation methods and performance evaluation, are tied below
Drawings and examples are closed the present invention is described in detail, but the present invention is not limited thereto.
Embodiment 1
By Mg alloys in CO2/SF6Melted under protective atmosphere and be cooled to 480 DEG C again, magnesium alloy is in semisolid.Unlatching is stirred
Function is mixed, the Ti of 5% volume fraction2AlC powders are added in the semisolid Mg melts of high-speed stirred, continue to stir 40mins
After end, it is reheated to 700 DEG C and stirs.Ti will be contained2AlC Mg melts are cast to pressurize 100MPa in stainless steel grinding tool
It is cooled to room temperature.By the Ti of preparation2The enhanced Mg based composites of AlC are required according to GB228, are processed into length for 18mm, wide
The flat tensile sample that degree is 3mm and thickness is 2mm, is loaded with 0.5mm/min speed on universal testing machine, is measured
The tensile strength of composite is 195MPa., will according to single armed beam sample using dynamic mechanically instrument (Model TA Q800, USA)
Ask, by composite processing into 35mm × 8mm × 1mm shapes.1.3 × 10-3Under strain amplitude and 1Hz frequencies, room temperature damping
Capacity is 0.011.Tested according to original position stretching, as shown in figure 3, part Ti2AlC particles crack into two.Meanwhile, in Ti2AlC and
Break-off does not occur for AZ91D interfaces, shows Ti2AlC and AZ91D has very strong interface binding power.
Embodiment 2
By Mg alloys in CO2/SF6Melted under protective atmosphere and be cooled to 500 DEG C again, magnesium alloy is in semisolid.Unlatching is stirred
Function is mixed, the Ti of 10% volume fraction2AlC powders are added in the semisolid Mg melts of high-speed stirred, continue to stir
After 40mins terminates, it is reheated to 700 DEG C and stirs.Ti will be contained2AlC Mg melts are cast to pressurize in stainless steel grinding tool
100MPa is cooled to room temperature.By the Ti of preparation2The enhanced Mg based composites of AlC require that being processed into length is according to GB228
18mm, the flat tensile sample that width is 3mm and thickness is 2mm, is added on universal testing machine with 0.5mm/min speed
Carry.By the Ti of preparation2The enhanced Mg based composites of AlC require according to GB228, are processed into length for 18mm, width be 3mm and
Thickness is 2mm flat tensile sample, is loaded on universal testing machine with 0.5mm/min speed, measures composite
Tensile strength be 215MPa.Using dynamic mechanically instrument (Model TA Q800, USA), required according to single armed beam sample, will be multiple
Condensation material is processed into 35mm × 8mm × 1mm shapes.1.3 × 10-3Under strain amplitude and 1Hz frequencies, room temperature damping capacity is
0.011.Fig. 4 is 10vol%Ti2The AlC/Mg based composites tensile failure planes of disruption, it can be seen that Ti2Fracture solution smooth AlC
The side surrounded from face and by Mg matrixes.
Embodiment 3
By Mg alloys in CO2/SF6Melted under protective atmosphere and be cooled to 530 DEG C again, magnesium alloy is in semisolid.Unlatching is stirred
Function is mixed, the Ti of 15% volume fraction2AlC powders are added in the semisolid Mg melts of high-speed stirred, continue to stir
After 50mins terminates, it is reheated to 700 DEG C and stirs.Ti will be contained2AlC Mg melts are cast to pressurize in stainless steel grinding tool
100MPa is cooled to room temperature.By the Ti of preparation2The enhanced Mg based composites of AlC require that being processed into length is according to GB228
18mm, the flat tensile sample that width is 3mm and thickness is 2mm, is added on universal testing machine with 0.5mm/min speed
Carry.By the Ti of preparation2The enhanced Mg based composites of AlC require according to GB228, are processed into length for 18mm, width be 3mm and
Thickness is 2mm flat tensile sample, is loaded on universal testing machine with 0.5mm/min speed, measures composite
Tensile strength be 175MPa.Using dynamic mechanically instrument (Model TA Q800, USA), required according to single armed beam sample, will be multiple
Condensation material is processed into 35mm × 8mm × 1mm shapes.1.3 × 10-3Under strain amplitude and 1Hz frequencies, room temperature damping capacity is
0.017。
Embodiment 4
By Mg alloys in CO2/SF6Melted under protective atmosphere and be cooled to 500 DEG C again, magnesium alloy is in semisolid.Unlatching is stirred
Function is mixed, the Ti of 20% volume fraction2AlC powders are added in the semisolid Mg melts of high-speed stirred, continue to stir
After 40mins terminates, it is reheated to 700 DEG C and stirs.Ti will be contained2AlC Mg melts are cast to pressurize in stainless steel grinding tool
100MPa is cooled to room temperature.By the Ti of preparation2The enhanced Mg based composites of AlC require that being processed into length is according to GB228
18mm, the flat tensile sample that width is 3mm and thickness is 2mm, is added on universal testing machine with 0.5mm/min speed
Carry.By the Ti of preparation2The enhanced Mg based composites of AlC require according to GB228, are processed into length for 18mm, width be 3mm and
Thickness is 2mm flat tensile sample, is loaded on universal testing machine with 0.5mm/min speed, measures composite
Tensile strength be 175MPa.Using dynamic mechanically instrument (Model TA Q800, USA), required according to single armed beam sample, will be multiple
Condensation material is processed into 35mm × 8mm × 1mm shapes.1.3 × 10-3Under strain amplitude and 1Hz frequencies, room temperature damping capacity is
0.021。
Claims (3)
1. a kind of high-intensity high-damping Ti2AlC-Mg based composites, it is characterised in that：Its composition is as follows：
Ti2AlC volume content is 5-20vol%, and remaining is Mg based alloys.
2. Ti according to claim 12AlC-Mg based composites, it is characterised in that：
Microstructure is ceramic phase Ti2AlC and metal phase Mg based alloys are each continuously distributed in three dimensions, wherein ceramic phase
Ti2AlC distribution of particles is in Mg matrix grain boundaries, and the two interface cohesion is firm.The yield strength of composite is 100-170MPa,
Tensile strength is 175-225MPa, 1.3 × 10-3Under strain amplitude and 1Hz frequencies, room temperature damping capacity is 0.01-0.25.
3. a kind of high intensity and high-damping Ti2The casting preparation method of AlC-Mg based composites, it is characterised in that：This method bag
Include following steps：
Step 1, by Mg alloys in CO2/SF6Fusing is warming up under protective atmosphere, 450-550 DEG C is then cooled to again and reaches that Mg melts
The semisolid of body simultaneously opens agitating function, Ti2AlC powders are added in the semisolid Mg melts of high-speed stirred.
Step 2, Ti is finished in semi-solid state addition2After AlC powders, it is reheated to 680-750 DEG C and stirs 30-60mins.
Finally, Ti will be contained2AlC Mg melts are cast to pressurize 50-100MPa in stainless steel grinding tool and are cooled to room temperature, that is, obtain doubly-linked
The Ti of continuous phase2AlC-Mg based composites.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109292371A (en) * | 2018-12-06 | 2019-02-01 | 福建省泉州市众创机械有限公司 | Ceramic glazing-applied pipeline composite material special belt pulley |
| CN109750197A (en) * | 2019-03-26 | 2019-05-14 | 北京交通大学 | A kind of ternary ceramics enhancing magnesium-based composite material cylinder jacket and preparation method thereof |
| CN109881059A (en) * | 2019-03-26 | 2019-06-14 | 北京交通大学 | Magnesium-based composite material engine piston and preparation method thereof |
| CN111690858A (en) * | 2019-03-13 | 2020-09-22 | 北京交通大学 | Wear-resistant self-lubricating Ti3Al1-xSixC2Self-interface regulation and control method of-Mg-based composite material |
| CN113277851A (en) * | 2021-06-29 | 2021-08-20 | 中国科学院金属研究所 | Ceramic-metal bionic nano composite material and preparation method thereof |
| CN113560542A (en) * | 2021-07-15 | 2021-10-29 | 北京交通大学 | Dual-continuous-phase Ti with controllable reinforced phase2AlN/Mg-based composite material and pressureless infiltration preparation method thereof |
| CN113600792A (en) * | 2021-07-15 | 2021-11-05 | 北京交通大学 | Spatial two-phase continuous structure Ti2AlC/Mg-based composite material and pressureless infiltration preparation method thereof |
-
2017
- 2017-04-11 CN CN201710232463.4A patent/CN107119218A/en active Pending
Non-Patent Citations (1)
| Title |
|---|
| WENBO YU: "Microstructure, mechanical properties and fracture mechanism of Ti2AlC reinforced AZ91D composites fabricated by stir casting", 《JOURNAL OF ALLOYS AND COMPOUNDS》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109292371A (en) * | 2018-12-06 | 2019-02-01 | 福建省泉州市众创机械有限公司 | Ceramic glazing-applied pipeline composite material special belt pulley |
| CN111690858A (en) * | 2019-03-13 | 2020-09-22 | 北京交通大学 | Wear-resistant self-lubricating Ti3Al1-xSixC2Self-interface regulation and control method of-Mg-based composite material |
| CN109750197A (en) * | 2019-03-26 | 2019-05-14 | 北京交通大学 | A kind of ternary ceramics enhancing magnesium-based composite material cylinder jacket and preparation method thereof |
| CN109881059A (en) * | 2019-03-26 | 2019-06-14 | 北京交通大学 | Magnesium-based composite material engine piston and preparation method thereof |
| CN113277851A (en) * | 2021-06-29 | 2021-08-20 | 中国科学院金属研究所 | Ceramic-metal bionic nano composite material and preparation method thereof |
| CN113560542A (en) * | 2021-07-15 | 2021-10-29 | 北京交通大学 | Dual-continuous-phase Ti with controllable reinforced phase2AlN/Mg-based composite material and pressureless infiltration preparation method thereof |
| CN113600792A (en) * | 2021-07-15 | 2021-11-05 | 北京交通大学 | Spatial two-phase continuous structure Ti2AlC/Mg-based composite material and pressureless infiltration preparation method thereof |
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