CN102021504A - Magnesium-based amorphous/porous titanium double-phase three-dimensional communicated composite material and preparation method thereof - Google Patents
Magnesium-based amorphous/porous titanium double-phase three-dimensional communicated composite material and preparation method thereof Download PDFInfo
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- 239000011777 magnesium Substances 0.000 title claims abstract description 87
- 229910052749 magnesium Inorganic materials 0.000 title claims abstract description 76
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 title claims abstract description 75
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 67
- 239000010936 titanium Substances 0.000 title claims abstract description 33
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 32
- 239000002131 composite material Substances 0.000 title claims abstract description 23
- 238000002360 preparation method Methods 0.000 title claims abstract description 21
- 229910000808 amorphous metal alloy Inorganic materials 0.000 claims abstract description 40
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 24
- 239000000956 alloy Substances 0.000 claims abstract description 24
- 238000000034 method Methods 0.000 claims abstract description 24
- 238000004891 communication Methods 0.000 claims abstract description 22
- 239000011148 porous material Substances 0.000 claims abstract description 8
- 239000007788 liquid Substances 0.000 claims abstract description 3
- 239000011159 matrix material Substances 0.000 claims description 58
- 230000006835 compression Effects 0.000 claims description 6
- 238000007906 compression Methods 0.000 claims description 6
- 238000007496 glass forming Methods 0.000 claims description 3
- 238000002844 melting Methods 0.000 abstract description 8
- 230000008018 melting Effects 0.000 abstract description 8
- 238000002474 experimental method Methods 0.000 abstract description 6
- 238000010791 quenching Methods 0.000 abstract description 5
- 230000000171 quenching effect Effects 0.000 abstract description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 abstract description 3
- 230000007547 defect Effects 0.000 abstract description 2
- 238000010438 heat treatment Methods 0.000 abstract 1
- 239000000523 sample Substances 0.000 description 22
- 208000010392 Bone Fractures Diseases 0.000 description 10
- 206010017076 Fracture Diseases 0.000 description 10
- 239000005300 metallic glass Substances 0.000 description 10
- 239000002245 particle Substances 0.000 description 10
- 206010010214 Compression fracture Diseases 0.000 description 9
- 229910052802 copper Inorganic materials 0.000 description 8
- 239000010949 copper Substances 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 6
- 150000001875 compounds Chemical class 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 239000007921 spray Substances 0.000 description 5
- 239000011261 inert gas Substances 0.000 description 4
- 238000010008 shearing Methods 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000000919 ceramic Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000006101 laboratory sample Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000009715 pressure infiltration Methods 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000001816 cooling Methods 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 230000008595 infiltration Effects 0.000 description 2
- 238000001764 infiltration Methods 0.000 description 2
- 239000002923 metal particle Substances 0.000 description 2
- 229910052709 silver Inorganic materials 0.000 description 2
- 229910052691 Erbium Inorganic materials 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- -1 TITANIUM skeleton compound Chemical class 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000004455 differential thermal analysis Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 150000002680 magnesium Chemical class 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 230000032696 parturition Effects 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
- 210000003462 vein Anatomy 0.000 description 1
- 239000002023 wood Substances 0.000 description 1
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Abstract
The invention relates to a magnesium-based amorphous composite material, in particular to a magnesium-based amorphous/porous titanium double-phase three-dimensional communicated composite material and a preparation method thereof. The magnesium-based amorphous/porous titanium double-phase three-dimensional communicated composite material provided by the invention is a composite material of a magnesium-based amorphous alloy and a three-dimensional communicated porous titanium skeleton, and the magnesium-based amorphous alloy is filled into the porous titanium skeleton to form a double-phase three-dimensional communicated structure. The method comprises the following steps of: melting the selected magnesium-based amorphous alloy by heating, then filling the liquid alloy into pores of the three-dimensional communicated porous titanium by a seepage method or a squeezing method, and finally performing water quenching to obtain the magnesium-based amorphous/porous titanium double-phase three-dimensional communicated composite material. The amorphous phase and the reinforced phase of the composite material are in spatial three-dimensional communication, distributed uniformly and reinforced mutually to solve the problem that the magnesium-based amorphous alloy is easy to produce brittle fracture. The amorphous composite material has excellent mechanical property under large-size sample experiment conditions, and has the characteristics of high specific strength, stable performance and no defect.
Description
Technical field
The present invention relates to magnesium base amorphous matrix material, be specially a kind of magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material and preparation method thereof.
Background technology
Because have the atomic arrangement structure of unique unordered short range order of long-range, the amorphous metal material has some excellent use propertieies, for example: high strength, high elastic limit and excellent corrosion resisting performance or the like.Magnesium base amorphous alloy has the high unique advantage of specific tenacity and becomes the new engineering material with application prospect.In addition, China has abundant magnesium resource, more makes the magnesium base amorphous metallic substance of R and D have realistic meaning.
The intrinsic fragility of magnesium base amorphous alloy has seriously restricted its application, and when deformation at room temperature, nearly all magnesium base amorphous alloy does not all show the viscous deformation behavior, often because the rapid expansion of certain bar shear zone makes material that the moment brittle rupture take place.In order to overcome magnesium base amorphous moment brittle failure, magnesium base amorphous alloy is prepared into matrix material as matrix, not only keep the high advantage of magnesium base amorphous alloy specific tenacity, and improved the non-deformability of material effectively.At present, the method for toughness reinforcing magnesium base amorphous alloy mainly contains interpolation high-strength ceramic particle and separates out toughness mutually with tough metal particle or interior life.In these several different method for toughening, the room temperature compressive plastic deformation amount of adding the prepared magnesium base amorphous matrix material of high-strength ceramic particle is 1～3%; Interior giving birth to separated out the toughness phase or added the expansion that the tough metal particle can effectively hinder shear zone, absorb the energy of shear zone, and bring out multiple shear bands, greatly improved the distortion of materials ability, the room temperature compressive plastic deformation amount of the magnesium base amorphous matrix material by the preparation of these methods is 12～40%.Because the dimensional effect and the imperfection sensitivity of non-crystaline amorphous metal mechanical property, utilize the magnesium base amorphous and matrix material of traditional copper mold spray to cast method preparation, the excellent mechanical performances that under the small sample experiment condition, has, its mechanical property significantly descends under large size sample experiment condition; Up to the present, also do not report the magnesium base amorphous matrix material that has excellent mechanical performances under the experiment condition of specimen diameter greater than 3mm.
The practical application of magnesium base amorphous matrix material also is subjected to the restriction of its preparation method except being subjected to the restriction of its scantling.Because in the situ composite material, the pattern of separating out of interior looks is subjected to preparing the curing condition remarkably influenced with the amount of separating out, and makes the weave construction of its sample have unpredictability, this has also had a strong impact on its practical application.For the particle reinforced Mg-base amorphous composite, the ceramic particle reinforced composite does not have actual application value basically because its non-deformability is very weak; In order to guarantee that toughness particle reinforced Mg-base amorphous composite has high specific tenacity, the particulate volume fraction can not be too high.And have only usually when the toughness phase that adds higher volume fraction, the mechanical property of magnesium base amorphous matrix material just can be significantly improved.In addition, adopt traditional copper mold castmethod, when adding grain volume fraction when too high, particulate distributes and is difficult to control in the sample, thereby causes the uneven components of sample; Particularly when large-sized amorphous of preparation and matrix material thereof, the copper mold castmethod also can be introduced more defective, as bubble, is mingled with etc., has a strong impact on the stability of its mechanical property.
In sum, in order to make magnesium base amorphous and matrix material becomes the engineering Material Used, we must optimize alloying constituent, development of new preparation technology, prepare composition evenly, Stability Analysis of Structures, large-sized magnesium base amorphous matrix material with good mechanical property.
Summary of the invention
The object of the present invention is to provide a kind of magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material and preparation method thereof, this matrix material amorphous phase and wild phase space three-dimensional are communicated with and are evenly distributed, two-phase is strengthened mutually, has solved the problem that brittle rupture easily takes place magnesium base amorphous alloy.This amorphous composite has good mechanical property under large size sample experiment condition, have specific tenacity height, stable performance, flawless characteristics.
Technical scheme of the present invention is:
The invention provides a kind of magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material, this matrix material is the matrix material of magnesium base amorphous alloy and three-dimensional connected porous titanium skeleton, magnesium base amorphous alloy is filled in the POROUS TITANIUM skeleton, forms the structure of two-phase three-dimensional communication.Wherein, magnesium base amorphous alloy is various magnesium base amorphous alloys with big glass forming ability.
The preparation method of this magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material, with selected magnesium base amorphous alloy heat fused, by the THROUGH METHOD or the method for clamp-oning liquid alloy is filled into the hole of three-dimensional connected porous titanium then, last shrend obtains magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material.The composite materials property index of this method preparation is as follows: compression plastic strain ε
p=8%～50%; Compressed rupture strength σ
f=1000～1700MPa.
Provided by the invention magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material, this matrix material can for: what have certain plastic deformation ability and high breaking tenacity contains Er (rare earth element-erbium) magnesium base amorphous alloy Mg
63Cu
16.8Ag
11.2Er
9(at.%) and the matrix material of three-dimensional connected porous titanium skeleton, magnesium base amorphous alloy is filled in the POROUS TITANIUM skeleton, forms the structure of two-phase three-dimensional communication.
Among the present invention, the porosity of POROUS TITANIUM skeleton is 10%～90% (being preferably 20%～80%), and pore size is 30～500 μ m (being preferably 100～200 μ m), and the purity of titanium is more than the 99.9wt%.
Above-mentioned magnesium base amorphous alloy Mg
63Cu
16.8Ag
11.2Er
9(at.%) and the preparation method of three-dimensional connected porous titanium skeleton matrix material, concrete steps are as follows:
(1) with Cu, Ag and three kinds of pure metal of Er (purity is more than the 99.9wt%) proportionately branch ratio proportioning weigh mix after, arc melting becomes master alloy in inert gas atmosphere;
(2) proportionately divide ratio, with after master alloy mixes, induction melting becomes Mg in inert gas atmosphere with Mg (purity is more than the 99.9wt%) pure metal piece
63Cu
16.8Ag
11.2Er
9(at.%) alloy;
(3) (vacuum tightness is lower than 2 * 10 in high vacuum
-3Pa) under the condition, with three-dimensional connected porous titanium skeleton and Mg
63Cu
16.8Ag
11.2Er
9(at.%) alloy is heated to 600～650 ℃, adopts the THROUGH METHOD or the method for clamp-oning the alloy liquation to be filled into the hole of three-dimensional connected porous titanium skeleton;
(4) treat that the alloy liquation is fully filled the hole of full POROUS TITANIUM skeleton after, fast cooling (quenching) obtains magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material.
Magnesium base amorphous alloy matrix material prepared among the present invention confirms that through X-ray diffraction (XRD) and differential thermal analysis (DSC) amorphous alloy composite material that is obtained has the feature of typical non-crystaline amorphous metal.After checking with the POROUS TITANIUM skeleton, the amorphous formation ability and the thermodynamic property of magnesium base amorphous alloy all do not change.
Room temperature compression testing sample size is that diameter is 4mm, aspect ratio 2: 1, and the test strain rate is 5 * 10
-4s
-1, and utilize scanning electron microscope (SEM) that the surface and the shear surface of sample after the compression fracture are all observed.Performance index are:
Breaking tenacity: σ
f=1400 ± 15MPa (POROUS TITANIUM matrix porosity 30%, pore size are 100～200 μ m);
Amount of plastic deformation: ε
Plastic=28 ± 2% (POROUS TITANIUM matrix porosity 30%, pore size are 100～200 μ m).
The present invention has the following advantages:
1. the magnesium base amorphous alloy of the present invention's employing is Mg
63Cu
16.8Ag
11.2Er
9(at.%), the porosity of POROUS TITANIUM skeleton is 10%～90%, and the purity of titanium is 99.9wt%, and this matrix material is that magnesium base amorphous alloy and three-dimensional connected porous titanium skeleton are compound, has that non-deformability is strong, intensity is high, low density feature.With the POROUS TITANIUM skeleton compound after, the amorphous formation ability of noncrystal substrate does not change.Because the density of titanium and the density of magnesium base amorphous alloy are very approaching, can in very large range adjust the porosity of POROUS TITANIUM skeleton, make that the density of the density of matrix material and complex matrix is also very approaching, thereby kept the advantage of magnesium base amorphous alloy high specific strength.
2. after the POROUS TITANIUM skeleton of different aperture degree of the present invention and magnesium base amorphous alloy are compound, amorphous phase and wild phase are evenly distributed, and the structure of two-phase three-dimensional communication, make magnesium base amorphous shearing strain uniform distribution, by the cooperative transformation of magnesium base amorphous alloy and toughness titanium skeleton, greatly improved the plastic deformation ability of material.
3. complex method of the present invention is the infiltration water quenching, compare with traditional amorphous composite preparation method (spray to cast method), the infiltration water quenching can be prepared large-size and the stable sample of excellent performance, the sample for preparing has less defects, as pore, be mingled with etc., and processing condition simply are easy to control.
4. the present invention can prepare large size or matrix material in irregular shape, and this matrix material has the good mechanical performance under the large size experiment condition.
In a word, above-mentioned advantage shows that the present invention has certain future in engineering applications, and various magnesium base amorphous alloys with big glass forming ability all are applicable to this preparation method.
Description of drawings
Fig. 1 is the SEM photo in matrix material cross section.
Fig. 2 is the X-ray diffraction curve that magnesium base amorphous alloy and POROUS TITANIUM skeleton strengthen the magnesium base amorphous alloy matrix material.
Fig. 3 is the room temperature compression fracture curve that magnesium base amorphous alloy and POROUS TITANIUM skeleton strengthen the magnesium base amorphous alloy matrix material.
Fig. 4 a-Fig. 4 d is sample outside surface and a fracture SEM photo behind the fracture of composite materials.Wherein, Fig. 4 a is a composite wood sample outside surface macro morphology; Fig. 4 b is the partial enlarged drawing of outside surface; Fig. 4 c is the completing a business transaction mutually of shear zone in the non-crystaline amorphous metal; Fig. 4 d is the local pattern of the fracture of matrix material.
Embodiment
The present invention is described in detail in detail by the following examples.
The present invention is prepared as follows magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material:
With Cu, Ag and three kinds of pure metal of Er (purity is more than the 99.9wt%) proportionately branch ratio proportioning weigh mix after, arc melting becomes master alloy in inert gas atmosphere; Proportionately divide ratio, with after master alloy mixes, induction melting becomes Mg in inert gas atmosphere with Mg (purity is more than the 99.9wt%) pure metal piece
63Cu
16.8Ag
11.2Er
9(at.%) alloy.With the three-dimensional connected porous titanium skeleton of different aperture degree and non-crystaline amorphous metal in high vacuum (vacuum tightness 1.5 * 10
-3Pa) be heated to 640 ℃ under, after alloy fully melts, adopt air pressure infiltration or height to be pressed into method, the alloy liquation is filled into the hole of three-dimensional connected porous titanium skeleton, after treating that the alloy liquation is fully filled the hole of full POROUS TITANIUM skeleton, cooling (quenching) obtains magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material fast.The SEM photo of matrix material as shown in Figure 1, magnesium base amorphous alloy well is filled in the hole of POROUS TITANIUM skeleton.Composite material surface pattern after the observation compression fracture, as shown in Figure 4, the POROUS TITANIUM skeleton has stoped the motion and the expansion of shear zone effectively, a large amount of intensive shear zones are evenly distributed in the surface of matrix material, by the distortion of self, the POROUS TITANIUM skeleton can absorb the nonaffine deformation that the shear zone expansion is brought effectively, the expansion of shear zone is limited in very little zone, what promoted shear zone effectively completes a business transaction germinating with the secondary shearing band mutually, distortion is evenly distributed on the whole sample, thereby has given material good plastic deformation ability.
Among the present invention, THROUGH METHOD adopts the air pressure infiltration, and the processing parameter of air pressure infiltration is as follows:
The alloy melting time: 1～3 minute;
Alloy melt temperature: 6000～650 ℃;
Skeleton temperature: 600～650 ℃;
Additional gas pressure pressure: 2～4 normal atmosphere;
The air pressure hold-time: 2～4 minutes.
Among the present invention, the method for clamp-oning adopts height to be pressed into, and the processing parameter that height is pressed into is as follows:
The alloy melting time: 1～3 minute;
Alloy melt temperature: 600～650 ℃;
Skeleton temperature: 600～650 ℃;
Squeeze pressure: 50～80MPa;
Clamp-on and the dwell time: 1～2 minute.
Mg
63Cu
16.8Ag
11.2Er
9(at.%) non-crystaline amorphous metal, its room temperature compression fracture curve is seen Fig. 3 curve 1.
Room temperature compression testing sample size is that diameter is 4mm, aspect ratio 2: 1, and the test strain rate is 5 * 10
-4s
-1, and utilize scanning electron microscope (SEM) that the surface and the shear surface of sample after the compression fracture are all observed.Performance index are:
Breaking tenacity: σ
f=1098 ± 20MPa;
Amount of plastic deformation: ε
Plastic=0%.
Work as Mg
63Cu
16.8Ag
11.2Er
9(at.%) alloy and 50% porosity POROUS TITANIUM skeleton (pore size is 100～200 μ m) compound after, its room temperature compression fracture curve is seen Fig. 3 curve 2.
Room temperature compression testing sample size is that diameter is 4mm, aspect ratio 2: 1, and the test strain rate is 5 * 10
-4s
-1, and utilize scanning electron microscope (SEM) that the surface and the shear surface of sample after the compression fracture are all observed.Performance index are:
Breaking tenacity: σ
f=1190 ± 20MPa;
Amount of plastic deformation: ε
Plastic=19 ± 2%.
Work as Mg
63Cu
16.8Ag
11.2Er
9(at.%) alloy and 30% porosity POROUS TITANIUM skeleton (pore size is 100～200 μ n) compound after, its room temperature compression fracture curve is seen Fig. 3 curve 3.
Room temperature compression testing sample size is that diameter is 4mm, aspect ratio 2: 1, and the test strain rate is 5 * 10
-4s
-1, and utilize scanning electron microscope (SEM) that the surface and the shear surface of sample after the compression fracture are all observed.Performance index are:
Breaking tenacity: σ
f=1400 ± 15MPa;
Amount of plastic deformation: ε
Plastic=28 ± 2%.
As shown in Figure 2, relatively any chemical reaction does not take place after magnesium base amorphous alloy matrix and POROUS TITANIUM skeleton are compound in the X-ray diffraction curve of magnesium base amorphous alloy and present embodiment as can be known, does not influence the amorphous formation ability of non-crystaline amorphous metal yet.
Fig. 4 a-Fig. 4 d is the SEM photo of outside surface and fracture behind the fracture of composite materials.Shown in Fig. 4 (a), by the distortion of self, the POROUS TITANIUM skeleton has stoped the motion and the expansion of shear zone effectively, a large amount of abundant shear zones are evenly distributed in the surface of sample, it is protruding significantly owing to be out of shape to be exposed to the titanium skeleton on surface, and wherein inserting figure is the titanium particle that specimen surface produces fold; The motion of shear zone and expansion are limited in very little zone by the POROUS TITANIUM skeleton, have avoided the quick expansion of main shear zone effectively.After Fig. 4 (b) illustrates a shear zone and passed the titanium particle, germinate at the end of shear zone and a large amount of secondary shearing bands, and impel the shear zone of different directions to complete a business transaction.Fig. 4 (c) is for being 45 ° of multiple shear bands of completing a business transaction mutually with the sample deformation direction after amplifying.Fig. 4 (d) illustrates on the matrix material fracture surface of sample, produce the fracture feature of tear face after the titanium particle process intensive shearing strain of existing POROUS TITANIUM skeleton fracture back, have the typical vein fracture of non-crystaline amorphous metal feature again, very significantly melting phenomenon has taken place in the metal drop surface non-crystaline amorphous metal on the fracture.
Relevant comparative example 1
The toughness molybdenum particle reinforced Mg-base amorphous composite [reference: J.S.C.Jang, X.H.Du.Appl.Phys.Lett.92 (2008) 011930] of copper mold spray to cast method preparation.This matrix material
The breaking tenacity 1100MPa of laboratory sample, plastix strain about 10%.
Relevant comparative example 2
The magnesium base amorphous alloy matrix material [Acta.Mater.55 (2007) 907 for reference: X.Hui, K.F.Yao] that contains interior raw cook shape precipitated phase of copper mold spray to cast method preparation.This matrix material
The laboratory sample breaking tenacity be 1163MPa, plastix strain is 18.5%.
Relevant comparative example 3
The Ti particle reinforced Mg-base amorphous composite [reference: M.Kinaka, A.Inoue.Mat.Sci.Eng.A.494 (2008) 299] of copper mold spray to cast method preparation.This matrix material
The laboratory sample breaking tenacity be 900MPa, plastix strain about 40%.
The result shows, two-phase three-dimensional communication matrix material of the present invention has excellent mechanical property, overcome non-crystaline amorphous metal brittle rupture and the mechanical property shortcoming to the susceptibility of defective easily takes place.Compare with traditional magnesium base amorphous alloy and matrix material, the present invention is simple and easy to do, has the important engineering application prospect.
Claims (5)
1. magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material, it is characterized in that: this matrix material is the matrix material of magnesium base amorphous alloy and three-dimensional connected porous titanium skeleton, magnesium base amorphous alloy is filled in the POROUS TITANIUM skeleton, forms the structure of two-phase three-dimensional communication.
According to claim 1 described magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material, it is characterized in that: the porosity of POROUS TITANIUM skeleton is 10%～90%, pore size is 30～500 μ m, the purity of titanium is more than the 99.9wt%.
According to claim 1 described magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material, it is characterized in that: magnesium base amorphous alloy is various magnesium base amorphous alloys with big glass forming ability.
According to claim 1 described magnesium base amorphous/preparation method of POROUS TITANIUM two-phase three-dimensional communication matrix material, it is characterized in that: with selected magnesium base amorphous alloy heat fused, by the THROUGH METHOD or the method for clamp-oning liquid alloy is filled into the hole of three-dimensional connected porous titanium then, last shrend obtains magnesium base amorphous/POROUS TITANIUM two-phase three-dimensional communication matrix material.
According to claim 4 described magnesium base amorphous/preparation method of POROUS TITANIUM two-phase three-dimensional communication matrix material, it is characterized in that the composite materials property index of this method preparation is as follows:
Compression plastic strain ε
p=8%～50%, compressed rupture strength σ
f=1000～1700MPa.
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| DE19541658A1 (en) * | 1995-11-08 | 1997-05-15 | Basf Ag | Water-soluble or water-dispersible graft polymers, their preparation and their use |
| JP4087612B2 (en) * | 2002-01-30 | 2008-05-21 | ヨンセイ ユニバーシティ | Process for producing amorphous matrix composites reinforced with ductile particles |
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