CN102816913B - Method for improving plasticity of amorphous alloy through supersonic particle bombarding (SPB) technique - Google Patents
Method for improving plasticity of amorphous alloy through supersonic particle bombarding (SPB) technique Download PDFInfo
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- CN102816913B CN102816913B CN2012103242291A CN201210324229A CN102816913B CN 102816913 B CN102816913 B CN 102816913B CN 2012103242291 A CN2012103242291 A CN 2012103242291A CN 201210324229 A CN201210324229 A CN 201210324229A CN 102816913 B CN102816913 B CN 102816913B
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Abstract
The method discloses a method for improving plasticity of an amorphous alloy through the SPB technique and belongs to the field of amorphous materials. The method includes the following steps: (1) selecting a clean Ti-based or Zr-based amorphous alloy specimen; (2) fixing the amorphous alloy specimen on a supersonic power spraying device; (3) and under the condition of a compressed gas with a pressure higher than 620 KPa, and a bombing temperature of 100 DEG C-200 DEG C, using the supersonic power spraying device and Al2O3 or SiC which are provided with an average particle size of 30-50mum for bombing the surface of the amorphous alloy specimen for 2.5-5s so as to obtain the amorphous alloy specimen with improved plasticity. The method has the advantages of being capable of improving the plasticity of the amorphous alloy block by 66% to the utmost without crystallization on the surface of the amorphous alloy, simple in operation, small in consuming time, low in cost and good in repeatability.
Description
Technical field
The present invention relates to a kind of method of utilizing the supersonic particles bombarding technology to improve amorphous alloy plasticity, belong to the non-crystalline material field.
Background technology
Non-crystaline amorphous metal is a kind of new metallic material, and unique long-range is unordered, shot-range ordered structure has been given this material and has been different from the excellent properties of traditional metal, as high-yield strength, high elastic limit etc.; In addition, non-crystaline amorphous metal has good resistance to corrosion, has good soft magnetism, Hard Magnetic and unique physicalies such as expansion characteristics.Yet under stretching, compressive load test, non-crystaline amorphous metal can be along a main shear zone generation shear fails, and almost without any macroscopical plasticity, low plastic deformation ability has seriously limited the engineering application of non-crystaline amorphous metal.
For the poor characteristics of amorphous alloy plasticity, people have carried out the work of a large amount of raising amorphous alloy plasticities.The method that improves at present amorphous alloy plasticity mainly contains two kinds, namely prepares the inhomogeneous non-crystaline amorphous metal of amorphous composite and microstructure.Wherein, amorphous alloy composite material is mainly to hinder the Quick Extended of single shear zone in amorphous phase by introducing second-phase, and the formation of bringing out multiple shear bands as much as possible, to improve to greatest extent amorphous alloy plasticity.The inhomogeneous non-crystaline amorphous metal of microstructure is the characteristics of utilizing the microstructure soft or hard different, and under the yardstick of relative microcosmic, the intersection by bringing out multiple shear bands/obstructions, realize the plasticity raising.At present, amorphous composite mainly contains additional second-phase and strengthens and strengthen mutually amorphous alloy composite material with the in-situ endogenic crystal.Additional second-phase strengthens has particle enhancing, tow to strengthen and the network skeleton enhancing of three-dimensional UNICOM; wherein; particle strengthens amorphous alloy composite material and can only choose and have dystectic metallic particles or ceramic particle as wild phase due to the restriction that is subjected to melt temperature; and the particulates reinforcements of choosing must have the least possible surface reaction with parent phase, and is partially-crystallized to prevent that the two-phase interface place from occurring.In addition, this method has also limited the volume fraction of adding particle.The in-situ endogenic crystal strengthens mutually amorphous alloy composite material and has certain similarity due to in-situ endogenic crystal phase and parent phase interface structure, therefore this enhancement method can obviously strengthen the bonding force of two-phase interface, and then intensity and the toughness of raising material, but being preparation process, the deficiency of this enhancement method maximum seriously is subject to the impact of the factors such as alloying constituent, ratio and complete processing.People also mainly are confined to the composition adjustment based on the understanding of non-crystaline amorphous metal microstructure ununiformity in addition, and research method is still and adopts traditional trial and error, research process not only to be difficult to control, and use range is very narrow, is only applicable to a certain specific composition system.
Above-mentioned several enhancement method is mainly to improve the plasticity of non-crystaline amorphous metal by the weave construction that changes non-crystaline amorphous metal, be subject to as adding mutually and the impact of the surface reaction of matrix phase, interpolation phase volume fraction etc., so the plasticity of non-crystaline amorphous metal is limited.In addition, these mode complicated process of preparation, production cost is higher, has certain limitation.
Summary of the invention
The plasticity that is difficult to effectively improve non-crystaline amorphous metal for existing method, and complex process, deficiency that cost is higher, the object of the present invention is to provide a kind of method of utilizing the supersonic particles bombarding technology to improve amorphous alloy plasticity.The highest whole plasticity of non-crystaline amorphous metal that can make of described method improves 66%, and the crystallization phenomenon does not occur on the non-crystaline amorphous metal top layer; That described method also has advantages of is simple to operate, expend time in less, cost is low, good reproducibility.
Purpose of the present invention is realized by following technical scheme:
A kind of method of utilizing the supersonic particles bombarding technology to improve amorphous alloy plasticity, described method steps is as follows:
(1) choose clean Ti base or Zr base noncrystal alloy sample;
(2) the non-crystaline amorphous metal sample is fixed on supersonic speed dynamic spraying equipment;
(3) utilize supersonic speed dynamic spraying equipment, higher than 620KPa, the bombardment temperature is under 100 ℃～200 ℃ conditions at compression pressure, and adopting median size is the Al of 30～50 μ m
2O
3Or SiC partickle bombardment non-crystaline amorphous metal specimen surface, the time length is 2.5～5s, namely obtains the non-crystaline amorphous metal sample that plasticity improves;
Described pressurized gas is N
2Or He;
Supersonic speed dynamic spraying equipment spraying principle:
First with gas N
2Or He be compressed to guarantee higher than under the gaseous tension of twice velocity of sound namely higher than 620KPa, then by the well heater of supersonic speed dynamic spraying equipment gas heating to 100 ℃～200 ℃, described gas is expanded in the DaLava jet pipe of supersonic speed dynamic spraying equipment, and at the exit velocity of supersonic speed dynamic spraying equipment spray gun, reach supersonic speed 500～1200m/s, adopting median size is the Al of 30～50 μ m
2O
3Perhaps SiC particle, particle mixes with described gas in the front portion of described spray gun, and by the heated air that expands, accelerates to 500～1200m/s, Al under the gaseous tension effect
2O
3Perhaps the SiC particle is mapped to the non-crystaline amorphous metal specimen surface from described spray gun, and the time length is 2.5～5s, namely obtains the non-crystaline amorphous metal sample that plasticity improves.
Beneficial effect
(1) the non-crystaline amorphous metal specimen surface that utilizes the method for the invention to process has a layer thickness to be about the compressive stress layer of 30 μ m, room temperature quasistatic compression experiment shows that the whole plasticity raising of non-crystaline amorphous metal reaches more than 39%, reach as high as 66%, and any crystallization phenomenon does not occur in the non-crystaline amorphous metal top layer.
(2) the method for the invention simple to operate, expend time in less, cost is low, good reproducibility.
(3) the bombardment temperature of the method for the invention is 100 ℃～200 ℃,, far below the crystallization temperature of non-crystaline amorphous metal, can guarantee, at bombardment Process For Amorphous alloy substrate, crystallization does not occur.
Description of drawings
Fig. 1 is bombardment sample X ray diffracting spectrum in embodiment 1;
Fig. 2 be in embodiment 1 after bombardment sample be scanning electron microscope (SEM) photograph under 1000 times in magnification;
Fig. 3 is the transmission electron microscope picture of the rear sample of bombardment in embodiment 1 and the corresponding electron-diffraction diagram of choosing;
Fig. 4 be in embodiment 2 after bombardment sample be scanning electron microscope (SEM) photograph under 1000 times in magnification.
Embodiment
Below in conjunction with the drawings and specific embodiments in detail the present invention is described in detail, but is not limited to this.
The manufacturer of the supersonic speed dynamic spraying equipment described in embodiment 1～8 is American I NOVRTI company, and model is the KM-CDS3 type.
(1) preparation Ti
32.8Zr
30.2Ni
5.3Cu
9Be
22.7Non-crystaline amorphous metal plate: the Ti of purity 〉=99.95%, Zr, Ni, Cu, five kinds of metal blocks of Be are carried out proportioning according to atomic percent 32.8:30.2:5.3:9:22.7; then under the high-purity argon gas atmosphere protection; carry out melting with arc-melting furnace, repeat melting 4 times, form alloy cast ingot.Adopt the method for turnover casting,, with injecting copper mold after the alloy cast ingot fusing, prepare Ti base noncrystal alloy plate.
(2) preliminary treatment: the non-crystaline amorphous metal printed line that step (1) is made cuts into and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is N
2, under the 620KPa gaseous tension, temperature is selected 100 ℃, and adopting median size is the Al of 30 μ m
2O
3Partickle bombardment non-crystaline amorphous metal block sample surface, time length 2.5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, as shown in Figure 1, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is Al
2O
3, and in the amorphous matrix without Al, O element, judge this Al
2O
3For being embedded in the particle in noncrystal substrate in the partickle bombardment process, the crystallization phenomenon does not occur in noncrystal substrate.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, non-crystaline amorphous metal block sample surface is uneven after the supersonic speed bombardment as seen in Figure 2, has crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, as shown in Figure 3, by transmission electron microscope picture, can find out that described sample is amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and bombarding the compression plasticity of non-crystaline amorphous metal block sample afterwards, find that not bombarding non-crystaline amorphous metal block sample breaking strain is 1.8%, and the breaking strain of non-crystaline amorphous metal block sample is 2.5% after partickle bombardment, and plasticity has improved 39%.
Embodiment 2
(1) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that makes in embodiment 1 is cut into and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is He, and under the 620KPa gaseous tension, temperature is selected 150 ℃, and adopting median size is the Al of 40 μ m
2O
3Partickle bombardment non-crystaline amorphous metal block sample surface, time length 2.5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is Al
2O
3, and in the amorphous matrix without Al, O element, judge this Al
2O
3For being embedded in the particle in noncrystal substrate in the partickle bombardment process, and the crystallization phenomenon itself does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, non-crystaline amorphous metal block sample surface is uneven after the supersonic speed bombardment as seen in Figure 4, has crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 1.8%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 2.8%, and plasticity has improved 55%.
Embodiment 3
(1) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that makes in embodiment 1 is cut into and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is He, and under the 620KPa gaseous tension, temperature is selected 200 ℃, and adopting median size is the Al of 50 μ m
2O
3Partickle bombardment non-crystaline amorphous metal block sample surface, time length 3s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is Al
2O
3, and in the amorphous matrix without Al, O element, judge this Al
2O
3For being embedded in the particle in noncrystal substrate in the partickle bombardment process, and the crystallization phenomenon does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, can find out that the non-crystaline amorphous metal block sample surface of polishing originally is uneven after the supersonic speed bombardment, have crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 1.8%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 3.0%, and plasticity has improved 66%.
Embodiment 4
(1) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that makes in embodiment 1 is cut out and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is N
2, under the 620KPa gaseous tension, temperature is selected 200 ℃, and adopting median size is the Al of 50 μ m
2O
3Partickle bombardment non-crystaline amorphous metal block sample surface, time length 5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is Al
2O
3, and in the amorphous matrix without Al, O element, judge this Al
2O
3For being embedded in the particle in noncrystal substrate in the partickle bombardment process, and the crystallization phenomenon does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, can find out that the non-crystaline amorphous metal block sample surface of polishing originally is uneven after the supersonic speed bombardment, have crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 1.8%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 2.9%, and plasticity has improved 61%.
(1) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that makes in embodiment 1 is cut out and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is He, and under the 620KPa gaseous tension, temperature is selected 200 ℃, and adopting median size is the SiC partickle bombardment non-crystaline amorphous metal block sample surface of 50 μ m, time length 2.5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is SiC, and in the amorphous matrix without Si, C element, judge that this SiC is the particle that is embedded in the partickle bombardment process in noncrystal substrate, and the crystallization phenomenon does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, can find out that the non-crystaline amorphous metal block sample surface of polishing originally is uneven after the supersonic speed bombardment, have crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 1.8%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 2.7%, and plasticity has improved 50%.
Embodiment 6
(1) preparation Zr
60Ti
14Ni
11Cu
10Be
25Non-crystaline amorphous metal plate: the Zr of purity 〉=99.95%, Ti, Ni, Cu, five kinds of metal blocks of Be are carried out proportioning according to atomic percent 60:14:11:10:25; then under the high-purity argon gas atmosphere protection; carry out melting with arc-melting furnace, repeat melting 4 times, form alloy cast ingot.Adopt the method for turnover casting,, with injecting copper mold after the alloy cast ingot fusing, prepare Zr base noncrystal alloy plate.
(2) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that step (1) is made cuts out and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is N
2, under the 620KPa gaseous tension, temperature is selected 150 ℃, and adopting median size is the Al of 50 μ m
2O
3Partickle bombardment non-crystaline amorphous metal block sample surface, time length 2.5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is Al
2O
3, and in the amorphous matrix without Al, O element, judge this Al
2O
3For being embedded in the particle in noncrystal substrate in the partickle bombardment process, and the crystallization phenomenon does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, can find out that the non-crystaline amorphous metal block sample surface of polishing originally is uneven after the supersonic speed bombardment, have crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 2%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 2.8%, and plasticity has improved 40%.
Embodiment 7
(1) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that makes in embodiment 6 is cut out and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is He, and under the 620KPa gaseous tension, temperature is selected 200 ℃, and adopting median size is the SiC partickle bombardment non-crystaline amorphous metal block sample surface of 50 μ m, time length 5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is SiC, and in the amorphous matrix without Si, C element, judge that this SiC is the particle that is embedded in the partickle bombardment process in noncrystal substrate, and the crystallization phenomenon does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, can find out that the non-crystaline amorphous metal block sample surface of polishing originally is uneven after the supersonic speed bombardment, have crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 2%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 3.2%, and plasticity has improved 60%.
(1) preparation Zr
50Cu
40Al
10Non-crystaline amorphous metal plate: the Zr of purity 〉=99.95%, Cu, three kinds of metal blocks of Al are carried out proportioning according to atomic percent 50:40:10, then under the high-purity argon gas atmosphere protection, with arc-melting furnace, carry out melting, repeat melting 4 times, form alloy cast ingot.Adopt the method for turnover casting,, with injecting copper mold after the alloy cast ingot fusing, prepare Zr base noncrystal alloy plate.
(2) preliminary treatment: the monoblock non-crystaline amorphous metal printed line that step (1) is made cuts out and is of a size of 22 * 5 * 1.8mm
3Block sample.
(3) the non-crystaline amorphous metal block sample is fixed on supersonic speed dynamic spraying equipment.
(4) utilize supersonic speed dynamic spraying equipment, pressurized gas is He, and under the 620KPa gaseous tension, temperature is selected 200 ℃, and adopting median size is the Al of 50 μ m
2O
3Partickle bombardment non-crystaline amorphous metal block sample surface, time length 2.5s.
(5) the non-crystaline amorphous metal block sample after supersonic particles bombarding is completed is clean with the acetone ultrasonic cleaning.
By to bombarding rear non-crystaline amorphous metal block sample surface X-ray diffractogram, analyzing, can find to be distributed with sharp-pointed crystal peak in amorphous diffuse scattering peak, utilize MDI jade software to carry out the phase retrieval, adopt chemical element restriction method to determine that crystal is Al
2O
3, and in the amorphous matrix without Al, O element, judge this Al
2O
3For being embedded in the particle in noncrystal substrate in the partickle bombardment process, and the crystallization phenomenon does not occur in the amorphous matrix.
Utilize the surface topography of scanning electron microscopic observation non-crystaline amorphous metal block sample after bombardment, can find out that by surface sweeping Electronic Speculum figure the non-crystaline amorphous metal block sample surface of polishing originally is uneven after the supersonic speed bombardment, have crisscross gully.
Utilize the changes in microstructure of non-crystaline amorphous metal block sample impact layer after the transmission electron microscope observing supersonic particles bombarding, by transmission electron microscope picture, can find out that described sample is uniform amorphous structure.Can find out to only have the diffuse scattering ring that characterizes amorphous in figure, and, without other diffraction spots or polycrystalline diffraction ring, illustrate that described sample, in the bombardment process, crystallization does not occur by choosing accordingly electron-diffraction diagram.
At room temperature carry out the quasistatic compression experiment, strain rate is 10
-4/ s, do not compare carrying out the non-crystaline amorphous metal block sample of partickle bombardment and the compression plasticity of the non-crystaline amorphous metal block sample after bombardment, find that the non-crystaline amorphous metal block sample breaking strain of bombardment is not 2%, and the non-crystaline amorphous metal block sample breaking strain that carries out after partickle bombardment is 2.8%, and plasticity has improved 40%.
The present invention includes but be not limited to above embodiment, every any being equal to of carrying out under the principle of spirit of the present invention, replace or local improvement, all will be considered as within protection scope of the present invention.
Claims (1)
1. method of utilizing the supersonic particles bombarding technology to improve amorphous alloy plasticity, it is characterized in that: described method steps is as follows:
(1) choose clean Ti base or Zr base noncrystal alloy sample;
(2) the non-crystaline amorphous metal sample is fixed on supersonic speed dynamic spraying equipment;
(3) utilize supersonic speed dynamic spraying equipment, higher than 620KPa, the bombardment temperature is under 100 ℃～200 ℃ conditions at compression pressure, and adopting median size is the Al of 30～50 μ m
2O
3Or SiC partickle bombardment non-crystaline amorphous metal specimen surface, the time length is 2.5～5s, namely obtains the non-crystaline amorphous metal sample that plasticity improves;
Described pressurized gas is N
2Or He.
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|---|---|---|---|---|
| FR2726579A1 (en) * | 1994-11-07 | 1996-05-10 | Neuville Stephane | PROCESS FOR DEPOSITING A PROTECTIVE COATING OF THE PSEUDO CARBON DIAMOND AMORPHOUS TYPE |
| CN100368589C (en) * | 2004-07-27 | 2008-02-13 | 中国科学院金属研究所 | Method for preparing coat in use for nickel based amorhpous alloy |
| CN101806928B (en) * | 2010-03-31 | 2011-11-16 | 西安交通大学 | Hard resin lens and organic glass lens surface ultra-hard coat coating method |
| CN101838791B (en) * | 2010-04-16 | 2011-06-08 | 南京理工大学 | Method for depositing amorphous carbon film by modifying surface of magnesium alloy |
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2012
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