CN103540727B - Metal two-dimensional nano multi-layer sheet structure and preparation method - Google Patents
Metal two-dimensional nano multi-layer sheet structure and preparation method Download PDFInfo
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- 229910052751 metal Inorganic materials 0.000 title claims abstract description 29
- 239000002184 metal Substances 0.000 title claims abstract description 29
- 238000002360 preparation method Methods 0.000 title claims abstract description 17
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 46
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 19
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 18
- 239000007769 metal material Substances 0.000 claims abstract description 13
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 9
- 239000004411 aluminium Substances 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 9
- 239000010949 copper Substances 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 9
- 239000010936 titanium Substances 0.000 claims abstract description 9
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 8
- 238000000034 method Methods 0.000 claims description 22
- 238000012545 processing Methods 0.000 claims description 7
- 230000006835 compression Effects 0.000 claims description 3
- 238000007906 compression Methods 0.000 claims description 3
- 230000000694 effects Effects 0.000 claims description 3
- 229910000990 Ni alloy Inorganic materials 0.000 claims description 2
- 238000005516 engineering process Methods 0.000 abstract description 15
- 229910001069 Ti alloy Inorganic materials 0.000 abstract description 4
- 230000006872 improvement Effects 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 19
- 230000001419 dependent effect Effects 0.000 description 12
- 239000013078 crystal Substances 0.000 description 9
- 230000008569 process Effects 0.000 description 9
- 229920006395 saturated elastomer Polymers 0.000 description 9
- 238000009826 distribution Methods 0.000 description 8
- 239000002086 nanomaterial Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 229910000754 Wrought iron Inorganic materials 0.000 description 5
- 238000009825 accumulation Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 238000010008 shearing Methods 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 238000005275 alloying Methods 0.000 description 4
- 238000000137 annealing Methods 0.000 description 4
- 230000005540 biological transmission Effects 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 4
- 238000002003 electron diffraction Methods 0.000 description 3
- 238000013508 migration Methods 0.000 description 3
- 230000005012 migration Effects 0.000 description 3
- 239000002159 nanocrystal Substances 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 238000002173 high-resolution transmission electron microscopy Methods 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910001080 W alloy Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000002178 crystalline material Substances 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 229910052752 metalloid Inorganic materials 0.000 description 1
- 150000002738 metalloids Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
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- 238000007670 refining Methods 0.000 description 1
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- 238000000926 separation method Methods 0.000 description 1
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- 239000000126 substance Substances 0.000 description 1
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Abstract
The present invention relates to metal structure improvement in performance technology, be specially a kind of utilize viscous deformation to prepare Metal two-dimensional nano multi-layer sheet structure and preparation method, be applicable to metallic substance nickel, aluminium, copper, iron, titanium and titanium alloys.The present invention is by applying the distortion of high speed, large sstrain and Large strain post deformation failure, obtain the two-dimensional nano multi-layer sheet structure of high strength and high thermal stability, its synusia thickness is below 200 nanometers, length-to-diameter ratio is more than 5, have strong deformation texture, the crystalline orientation difference between synusia inside and synusia is below 15 °.Two-dimensional nano multi-layer sheet structure prepared by the present invention has superior over-all properties, can realize intensity and thermostability has both.
Description
Technical field
The present invention relates to metal structure improvement in performance technology, be specially a kind of utilize viscous deformation to prepare Metal two-dimensional nano multi-layer sheet structure and preparation method, be applicable to metallic substance nickel, aluminium, copper, iron, titanium and titanium alloys.
Background technology
Nano crystal material refers to the single-phase or heterogeneous crystalline material that the microtexture being less than 100nm by size forms.Due to its scantlings of the structure about three orders of magnitude less of common polycrystalline material, the ratio shared by crystal boundary increases substantially.The nanocrystalline of current preparation is the shaft-like such as three-dimensional, and there is high big angle grain boundary density and random crystal orientation, this nano crystal material has the performance being better than traditional material, such as: high strength, high rigidity, high diffusivity performance, excellent wear resistance etc., but its thermostability is very poor, usually show the inversion relation of intensity-thermostability.In addition, severe plastic deformation is the effective ways preparing nano metal material present stage, comprise: high pressure and torsion (highpressuretorsion, channel pressings (the equalchannelangularpressing such as HPT), and accumulation ply rolling (accumulativerollbonding, ARB) etc. ECAP).These grain refinings reduce the crystal grain of metal (as aluminium, iron, nickel etc.) to sub-micrometer scale, but but scantlings of the structure can not be further reduced to nanoscale (<100nm).Major cause increases a certain threshold value when dependent variable, and dislocation accumulation and annihilation reach running balance, and dislocation desity can not continue to increase.For pure nickel, when dependent variable reaches certain value (about 5 ~ 10), grain-size reaches capacity (being about 200nm), intensity is about 1000MPa(document 3:R.Pippan etc., Adv.Eng.Mater. (advanced engineering materials), 2006,8:1046).Break through saturated structures limitation of size, further reinforced metal, obtain the great difficult problem that Good All-around Property is nano metal research.
In recent years, by forming special twin-plane boundary, the saturated grain-size of metallic substance can be significantly reduced to nanoscale, and the over-all properties of nano crystal material is greatly improved simultaneously.People (the document 1:L.Lu etc. such as China material supply section scholar Lu, Science (science), 2004,304:422) by introducing high-density coherence twin-plane boundary in the crystal grain of submicron-scale, invented a kind of novel nano twin structure copper, it has high strength and high thermal stability.American scientist (document 2:T.Chookajorn etc., Science (science), 2012,337:951) by adding a large amount of alloying elements, make alloying element in grain boundaries segregation, reduce the energy of crystal boundary, thus prepare and there is high strength, the Nanostructure tungsten alloy of high thermal stability.Add trace alloying element, significantly can reduce the saturated grain-size of being out of shape and causing, for pure nickel, when adding the Ti of 0.14wt%, its saturated grain-size can be reduced to below 50nm.Be out of shape by cold plasticity, the scantlings of the structure of pure metal material also can be refined to nanoscale.But these methods all have some limitations, such as, nano-twin crystal structure only just easily obtains in having, in the metallic substance of low stacking fault energy, and alloying often changes the physicochemical property of material, and nano metal prepared by low-temperature deformation is more unstable.
As everyone knows, the propagation of dislocation, to reset be the essential reason of structure refinement, and the appearance of saturated mode comes from and is out of shape the dislocation desity caused and increases the dislocation desity caused with dynamic recovery and reduce and reach running balance; And the stability of structure depends on and the transfer ability at interface, the homogeneity storing energy and structure.Break through saturated size restriction requirements to improve the accumulation of dislocation desity-raising dislocation further or reduce dislocation and disappear, and it is even to improve structural stability claimed structure, storing can be low and interfacial migration difficult.Traditional method improving dislocation desity by increasing deflection has locked into the dynamic recovery aggravation that structure refinement causes, and the high-density big angle crystal boundary of ultra-fine grained structure, structural inhomogeneity, high storage energy and interfacial migration are difficult to the structural stability that had in essence.Consider that dislocation accumulation and rate of deformation and strain gradient are closely related, and this influence factor is not high with the attention rate be subject to for a long time.Nearest research shows that high speed plastic distortion accelerates structure evolution, and the dislocation desity when identical deflection is higher, and scantlings of the structure is less, and Large strain gradient obtains the dislocation desity far above saturated mode.In addition, high speed plastic is out of shape the nanostructure obtained based on low angle boundary, and interfacial energy and interfacial migration are far below big angle crystal boundary.Therefore at a high speed, large sstrain and the distortion of the Large strain post deformation failure difficult problem that will be expected to solve nano metal and face.
Summary of the invention
The object of the present invention is to provide a kind of utilize viscous deformation to prepare Metal two-dimensional nano multi-layer sheet structure and preparation method, solve the problem such as saturated limitation of size and over-all properties (as: intensity-thermostability optimization).
Technical scheme of the present invention is:
A kind of Metal two-dimensional nano multi-layer sheet structure, synusia thickness is below 200 nanometers, and length-to-diameter ratio is more than 5, has strong deformation texture, and the crystalline orientation difference between synusia inside and synusia is below 15 °.
Described Metal two-dimensional nano multi-layer sheet structure, synusia thickness is preferably 5 ~ 150 nanometers, and length-to-diameter ratio is preferably 5 ~ 100.
Described Metal two-dimensional nano multi-layer sheet structure, the crystalline orientation difference between synusia inside and synusia is preferably 1 ° ~ 10 °.
The preparation method of described Metal two-dimensional nano multi-layer sheet structure, adopt viscous deformation, processing parameters meets following characteristics:
Deformation strain speed range:>=1s
-1;
Deformation strain weight range: >=2, method of calculation:
If mode of texturing is unilateral stretching or compression, ε=| ε
xx|;
If mode of texturing is pure shear distortion,
Deformation strain gradient scope:>=0.05 μm
-1, method of calculation: χ=ε/x, wherein χ is strain gradient, and ε is equivalent strain amount, and x is the range scale of effects of strain, μm.
The preparation method of described Metal two-dimensional nano multi-layer sheet structure, the method has high strain rate, large sstrain and high strain gradient mode of texturing.
The preparation method of described Metal two-dimensional nano multi-layer sheet structure, metallic substance is nickel, aluminium, iron, copper, titanium; Or metallic substance is the alloy of nickel, aluminium, iron, copper, titanium.
The preparation method of described Metal two-dimensional nano multi-layer sheet structure, deformation strain speed preferable range: 10 ~ 10
5s
-1; Deformation strain amount preferable range: 2 ~ 100; Deformation strain gradient preferable range: 0.05 ~ 1 μm
-1.
Tool of the present invention has the following advantages:
1. the present invention utilizes viscous deformation in the metallic substance of nickel, aluminium, copper, iron, titanium and titanium alloys, prepare the method for novel nano structure, proposes the technology of preparing of high strain rate, large sstrain and Large strain gradient, breaches traditional saturated size-constraints.
2. the Metal two-dimensional nano multi-layer sheet structure that prepared by the present invention has superior over-all properties, and such as have high strength and high thermal stability concurrently, this novel nanostructure can improve the performance of material.Such as, prepare one deck nano ply structure at bearing class material surface, the fatigue property and abrasion resistance properties etc. of component can be improved.
3. the present invention is for pure metal Ni, uses high speed shear to produce: equivalent strain amount>=10, strain rate>=10
2s
-1with strain gradient>=0.15 μm
-1viscous deformation, coarse grain is progressively refined to submicron-scale (0.1-0.5 μm), and final forms two-dimensional nano multi-layer sheet structure.This novel metal two-dimensional nano multi-layer sheet structure has following characteristics: the short-axis direction of synusia is of a size of 5 ~ 60nm, and average aspect ratio is greater than 10, has strong shearing strain texture, the crystalline orientation difference <15 ° between synusia inside and synusia.Its hardness is 6 times of corresponding coarse-grain sample, be that the shaft-like such as conventional three-dimensional receive 2 times of Ultra-fine Grained, and its grain growth temperature is more nanocrystalline than shaft-like such as conventional three-dimensional high 55 DEG C.
Accompanying drawing explanation
Fig. 1 is the optical microscope photograph of the pure nickel rod cross section utilizing surface mechanical attrition treatment technical finesse.
Fig. 2 utilizes in the pure nickel rod of surface mechanical attrition treatment technical finesse the distribution curve strained with the degree of depth.
Fig. 3 be in the pure nickel rod utilizing surface mechanical attrition treatment technical finesse strain rate and strain gradient with the distribution curve of the degree of depth.
Fig. 4 utilizes transmission electron microscope photo (a), interface separation statistics (b) of the pure nickel of surface mechanical attrition treatment technical finesse rod top layer nano ply structure and chooses electron diffraction (c).
The high resolution transmission electron microscopy photo observed along [110] orientation that Fig. 5 (A) is nano ply structure, (B), the high resolution Fourier transform phase of (C), (D), (E), (F) and (G) and lamellar boundary inner for corresponding synusia, disclose stacking fault, twin, Small angle misorientation.
Fig. 6 utilizes the size of the two kinds of typical structures (nano ply structure and ultra-fine grained structure) prepared in the pure nickel rod of surface mechanical attrition treatment technical finesse with the change of annealing temperature.
Fig. 7 is the statistical distribution (c) of the transmission electron microscope photo (a) of the IF rod iron top layer nano ply structure utilizing surface mechanical attrition treatment technical finesse, electron diffraction (b) and synusia thickness.
Fig. 8 is the transmission electron microscope photo utilizing 100 μm of dark regions, the pure nickel of surface mechanical attrition treatment technical finesse rod middle distance surface.
Embodiment
The present invention prepares a kind of New Two Dimensional nano ply structure in the metallic substance of nickel, aluminium, copper, iron, titanium and titanium alloys, this nano ply structure has following characteristics: synusia thickness is below 200 nanometers, length-to-diameter ratio is more than 5, have strong deformation texture, the crystalline orientation difference between synusia inside and synusia is below 15 °.
The present invention proposes the method that novel nano structure is prepared in the distortion of a kind of high strain rate, large sstrain and Large strain post deformation failure, comprise following two steps:
The viscous deformation with following characteristics introduced by metallic substance, can prepare two-dimensional nano multi-layer sheet structure.
(1) deformation strain speed:>=1s
-1;
(2) deformation strain weight range: >=2, method of calculation:
If mode of texturing is unilateral stretching or compression, ε=| ε
xx|; If mode of texturing is pure shear distortion,
(3) deformation strain gradient>=0.05 μm
-1, method of calculation: χ=ε/x, wherein χ is strain gradient, and ε is equivalent strain amount, and x is the range scale of effects of strain, μm.
The present invention proposes high strain rate, large sstrain and Large strain gradient three to combine to prepare the technical though of nano structural material first.In order to distortion three elements are incorporated in the middle of a certain concrete viscous deformation technology, (but being not limited to this technology) a kind of surface mechanical attrition treatment technology (document 6:W.L.Li etc. are selected, Scr.Mater. (material bulletin), 2008,59:546).This technology is by introducing shearing strain at a high speed at sample surfaces, by continuous accumulation shear strain, finally making the microtexture of skin-material be refined to nanoscale.Surface mechanical attrition treatment equipment is consisted of digital controlled lathe and sintering skin of cemented carbide cutter, pending axle metalloid sample is installed on the rotation system output terminal of lathe, by rotation system with certain rotating speed V
1drive treated sample high speed rotating; Spherical tool is arranged on the auto feed system bare terminal end of lathe, and after cutter contacts sample surfaces from the direction perpendicular to axle class sample, feed system presets the draught a of each processing
p, and with certain speed V
2from the side of sample to opposite side relative movement, cyclic process like this for several times, until each deformation parameter reaches design requirements of the present invention.
Below by one exemplary embodiment, the present invention is described.It is pointed out that and those skilled in the art will readily understand, following instance be only provide by way of example about one exemplary embodiment more of the present invention, it does not also mean that and carries out any restriction to the present invention.
Embodiment 1:
Utilize surface mechanical attrition treatment technology in the steady nano ply structure of the pure nickel rod surface high-strength height of preparation:
Pure nickel stacking fault energy: 130mJ/m
2;
Pure nickel crystalline structure: face-centered cubic (FCC);
Pure nickel grain-size before processing: 500 μm;
Pure nickel rod diameter: 10mm;
Pure nickel chemical composition (weight percent) is as following table:
| C | Si | Mn | P | S | Cr | Fe | Al | Co | Cu | Ti | Mg | Ni |
| 0.003 | 0.009 | 0.003 | 0.003 | 0.001 | 0.004 | 0.021 | 0.014 | 0.004 | 0.005 | 0.048 | 0.003 | 99.882 |
Equipment: digital controlled lathe;
Main shaft (processed work) rotating speed V
1: 300r/min;
Each draught a
p: 30 μm/secondary;
Axial feed velocity V
2: 6mm/min;
Spherical process tool diameter: 8mm;
Processing number of times: 8 times;
After surface mechanical attrition treatment, the material in nickel rod from outward appearance to inner essence subjected to the dependent variable of graded, and similarly, strain rate and strain gradient also present Gradient distribution.Carry out om observation to the sample processed from cross section, its microstructure as shown in Figure 1.The structure on top layer is by serious refinement, but at the historical rudiment be out of shape compared with deep regions still obviously, one of them bends in plastic history gradually with annealing twin circle of white triangles shape mark.Using this twin boundary as the inherence mark in material deformation process, the distribution of the dependent variable in material deformation process, strain rate and strain gradient can be estimated, as shown in Figure 2 and Figure 3.
In the region that distance 0 ~ 80 μm, top layer is dark, the variation range of dependent variable, strain rate and strain gradient is as shown in the table:
| The degree of depth (μm) | Dependent variable | Strain rate (s -1） | Strain gradient (μm -1) |
| 0～80 | 33～13 | （2～0.7）×10 3 | 0.4～0.15 |
In the region that distance 10 ~ 70 μm, top layer is dark, define typical nano ply structure, as shown in Figure 4.Fig. 4 (a) is the transmission electron microscope photo of nano ply structure, show that the characteristic feature of this structure is the straight lamellar boundary be parallel to each other, synusia elongates along shear direction (being vertical direction in this figure), and minor axis dimension is 20 nanometers and major axis dimension can reach several microns.Inner at synusia, there are some substructures, as dislocation boundary and deformation twins circle etc.Fig. 4 (b) is the statistics of synusia thickness, and average synusia thickness is 20nm.For choosing electron diffraction, Fig. 4 (c) shows that its crystalline orientation is not random, have stronger shearing strain texture.Fig. 5 is high resolution transmission electron microscopy, and show that synusia inside is containing fault, twin and little Jiao dislocation circle, and have the misorientation of 3 ° between synusia, a large amount of Hrtem Observation supports this observations.By 25g load, the experiment of Vickers' hardness impression test is carried out to nano ply structure, show that its hardness value is 6.4 ± 0.32GPa.To nano ply structure from 300 DEG C to 900 DEG C temperature range carry out the annealing experiment of 1h, show that the initial Coarsening Temperature of nanometer is about 506 DEG C of (see figure 6)s.
In the present embodiment, have the two-dimensional nano multi-layer sheet structure of high strength and high thermal stability, synusia thickness is 20 nanometers, and length-to-diameter ratio up to 100, can have strong shearing strain texture, is that little angular orientation is poor, is about 1 ~ 10 ° between synusia inside and synusia.
Embodiment 2:
Surface mechanical attrition treatment technology is utilized to prepare nano ply structure on IF rod iron surface:
IF steel stacking fault energy: ~ 200mJ/m
2;
IF steel crystalline structure: body-centered cubic (BCC);
IF crystalline grain of steel size before processing: 27 μm;
IF rod iron diameter: 12mm;
Equipment: digital controlled lathe;
Main shaft (processed work) rotating speed V
1: 300r/min;
Each draught a
p: 30 μm/secondary;
Axial feed velocity V
2: 6mm/min;
Spherical process tool diameter: 8mm;
Processing number of times: 10 times;
In the region that distance 0 ~ 10 μm, top layer is dark, the variation range of dependent variable, strain rate and strain gradient is as shown in the table:
| The degree of depth (μm) | Dependent variable | Strain rate (s -1） | Strain gradient (μm -1) |
| 0～10 | 20～10 | （1.5～0.7）×10 3 | 0.3～0.1 |
Similar surface mechanical attrition treatment is carried out on IF rod iron surface, in the region that 0 ~ 10 μm, distance surface is dark, defines nano ply structure.Fig. 7 a shows that this structure has typical synusia feature, and length-to-diameter ratio is greater than 10.Similarly, owing to being there occurs localized shear deformation under high strain gradient, this structure has stronger shear texture (see Fig. 7 b).Fig. 7 c is the statistical distribution of IF rod iron top layer nano ply structure, shows that synusia thickness distribution is comparatively concentrated, and average synusia thickness is 22nm.
In the present embodiment, have the two-dimensional nano multi-layer sheet structure of high strength and high thermal stability, synusia thickness is 22 nanometers, and length-to-diameter ratio occurrence is 14.5, has strong shearing strain texture, is that little angular orientation is poor, is about 1 ~ 15 ° between synusia inside and synusia.
Comparative example 1
With pure nickel sample prepared by surface mechanical attrition treatment technology in embodiment 1, about 100 μm of dark regions, distance surface, the deformation parameter of its correspondence is as follows: dependent variable is 10, and strain rate is 6 × 10
2s
-1, strain gradient is 0.12 μm
-1.Typical ultra-fine grained structure is defined, as shown in Figure 8 in this region.The average grain size of this Ultra-fine Grained is 230nm, and length-to-diameter ratio is less than 2, and crystal grain has the crystalline orientation of stochastic distribution.By 25g load, the experiment of Vickers' hardness impression test is carried out to ultra-fine grained structure, show that its hardness value is 2.76 ± 0.26GPa.To ultra-fine grained structure from 300 DEG C to 900 DEG C temperature range carry out the annealing experiment of 1h, show that the initial Coarsening Temperature of Ultra-fine Grained is about 467 DEG C of (see figure 6)s.Nano ply structure prepared by the present invention and the most basic difference of ultra-fine grained structure are that former structure size is less, and hardness (or intensity) is higher, thermostability better, are a kind of high-strength, high steady nano ply structures.
Comparative example 2
After high pressure torsion (HPT) process, the grain-size of pure nickel is about 130nm, and vickers hardness number is about 3.2GPa, and the initial Coarsening Temperature of ultra-fine grained structure is less than 160 DEG C.The deformation parameter of this high pressure torsion process is as follows: dependent variable is 100, strain rate <20s
-1, strain gradient is less than 0.06 μm
-1.The present invention and the method fundamental difference are to have employed high strain rate, and in conjunction with the deformation technology of Large strain gradient, the grain-size of pure nickel can be made to be reduced to nanoscale, realize the strengthening of pure material.
Comparative example 3
After dynamic plasticity distortion (DPD) process, the synusia thickness of pure nickel is about 110nm, and vickers hardness number is about 3.0GPa.The deformation parameter of this dynamic deformation technology is as follows: dependent variable is 2.3, and strain rate is 10
2~ 10
3s
-1, strain gradient is little.Superiority of the present invention is the distortion that can apply large sstrain amount, and in conjunction with high strain gradient, material microstructure is refine to nanoscale, further strengthening material.
Comparative example 4
After ply rolling (ARB) process, the grain-size of IF steel is about 210nm.The deformation parameter of this ply rolling deformation technology is as follows: dependent variable is 4, strain rate <20s
-1, strain gradient is little.The present invention by applying two-forty gross distortion, and ties the strain gradient of overall height, can prepare nano ply structure in IF steel.
Embodiment and comparative example result show, the present invention's utilize viscous deformation to prepare intensity and thermostability that New Two Dimensional nano ply structure has superelevation, are better than the shaft-like nanostructures such as three-dimensional prepared by traditional gross distortion technology.The present invention by applying at a high speed, large sstrain and the distortion of Large strain post deformation failure realize, being applicable to take dislocation glide as metal and the alloy of primary deformable mode.
Claims (5)
1. a preparation method for Metal two-dimensional nano multi-layer sheet structure, is characterized in that: synusia thickness is 5 ~ 150 nanometers, and length-to-diameter ratio is greater than 10 to 100, has strong deformation texture, and the crystalline orientation difference between synusia inside and synusia is below 15 °;
The preparation method of described Metal two-dimensional nano multi-layer sheet structure, adopt viscous deformation, processing parameters meets following characteristics:
Deformation strain speed range:>=1s
-1;
Deformation strain weight range: >=2, method of calculation:
If mode of texturing is unilateral stretching or compression, ε=| ε
xx|;
If mode of texturing is pure shear distortion,
Deformation strain gradient scope:>=0.05 μm
-1, method of calculation: χ=ε/x, wherein χ is strain gradient, and ε is equivalent strain amount, and x is the range scale of effects of strain, μm.
2. according to Metal two-dimensional nano multi-layer sheet structure preparation method according to claim 1, it is characterized in that, the method has high strain rate, large sstrain and high strain gradient mode of texturing.
3. according to Metal two-dimensional nano multi-layer sheet structure preparation method according to claim 1, it is characterized in that, metallic substance is nickel, aluminium, iron, copper, titanium; Or metallic substance is the alloy of nickel, aluminium, iron, copper, titanium.
4., according to Metal two-dimensional nano multi-layer sheet structure preparation method according to claim 1, it is characterized in that,
Deformation strain speed preferable range: 10 ~ 10
5s
-1;
Deformation strain amount preferable range: 2 ~ 100;
Deformation strain gradient preferable range: 0.05 ~ 1 μm
-1.
5. according to Metal two-dimensional nano multi-layer sheet structure preparation method according to claim 1, it is characterized in that: the crystalline orientation difference between synusia inside and synusia is preferably 1 ° ~ 10 °.
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| CN106735925B (en) * | 2017-03-21 | 2018-07-17 | 商丘师范学院 | A kind of femtosecond laser direct write preparation method of two dimension sub-micron butterfly metal micro structure |
| CN115074648B (en) * | 2021-03-11 | 2023-11-10 | 中国科学院金属研究所 | Method for preparing nano block metal material by electromagnetic impact and special equipment thereof |
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1377987A (en) * | 2002-01-24 | 2002-11-06 | 天津大学 | Method for making metal surface structure become nanometer one by high speed plastic shearing and deformation |
| CN1905986A (en) * | 2004-01-21 | 2007-01-31 | 国立大学法人丰桥技术科学大学 | Process for forming ultrafine crystal layer, machine component having ultrafine crystal layer formed by the ultrafine crystal layer forming process, process for producing the machine component, proces |
| CN101616764A (en) * | 2007-04-13 | 2009-12-30 | 住友大阪水泥股份有限公司 | Ni-Fe-nickel-iron-zinc alloy nanoparticle |
| CN101704503A (en) * | 2009-04-30 | 2010-05-12 | 中国计量学院 | New method for controllably synthetizing one-dimensional nano material graft |
| CN101999007A (en) * | 2008-04-10 | 2011-03-30 | 新日本制铁株式会社 | High-strength steel sheets which are extremely excellent in the balance between burring workability and ductility and excellent in fatigue endurance, zinc-coated steel sheets, and processes for production of both |
| CN102220641A (en) * | 2011-05-13 | 2011-10-19 | 南京师范大学 | Synthesis method of monoclinic crystal phase rare-earth iso-oxy-sulfur superfine nanowire and wire-based superstructure |
-
2013
- 2013-10-31 CN CN201310536227.3A patent/CN103540727B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1377987A (en) * | 2002-01-24 | 2002-11-06 | 天津大学 | Method for making metal surface structure become nanometer one by high speed plastic shearing and deformation |
| CN1905986A (en) * | 2004-01-21 | 2007-01-31 | 国立大学法人丰桥技术科学大学 | Process for forming ultrafine crystal layer, machine component having ultrafine crystal layer formed by the ultrafine crystal layer forming process, process for producing the machine component, proces |
| CN101616764A (en) * | 2007-04-13 | 2009-12-30 | 住友大阪水泥股份有限公司 | Ni-Fe-nickel-iron-zinc alloy nanoparticle |
| CN101999007A (en) * | 2008-04-10 | 2011-03-30 | 新日本制铁株式会社 | High-strength steel sheets which are extremely excellent in the balance between burring workability and ductility and excellent in fatigue endurance, zinc-coated steel sheets, and processes for production of both |
| CN101704503A (en) * | 2009-04-30 | 2010-05-12 | 中国计量学院 | New method for controllably synthetizing one-dimensional nano material graft |
| CN102220641A (en) * | 2011-05-13 | 2011-10-19 | 南京师范大学 | Synthesis method of monoclinic crystal phase rare-earth iso-oxy-sulfur superfine nanowire and wire-based superstructure |
Non-Patent Citations (1)
| Title |
|---|
| "Fabrication of a gradient nano-micro-structured surface layer on bulk copper by means of a surface mechanical grinding treatment";W.L. Li ETAL;《Scripta Materialia》;20080515;第59卷;第546-549页 * |
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