CN108165975A - A kind of laser melting coating Al/TiB2 complex intensifying layers - Google Patents
A kind of laser melting coating Al/TiB2 complex intensifying layers Download PDFInfo
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- CN108165975A CN108165975A CN201611116902.7A CN201611116902A CN108165975A CN 108165975 A CN108165975 A CN 108165975A CN 201611116902 A CN201611116902 A CN 201611116902A CN 108165975 A CN108165975 A CN 108165975A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
- C23C24/106—Coating with metal alloys or metal elements only
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- Mechanical Engineering (AREA)
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- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Coating By Spraying Or Casting (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Abstract
A kind of laser melting coating Al/TiB2 complex intensifying layers, using Al TiB2 composite granules as strengthening layer raw material（Wherein aluminium is binding agent）, using Nd：YAG laser carries out laser melting coating intensive treatment in magnesium gadolinium system Mg alloy surface.Reaction in-situ has occurred in the elements such as aluminium element and gadolinium, the yttrium in matrix in strengthening layer, generate the intermetallic compounds such as high-temperature rigid phase Al2Gd and Al2Y, and the hardening constituent TiB2 introduced does not decompose, it is good with the intermetallic compound and matrix compatibility of fabricated in situ, but characteristic distributions and architectural difference are notable；When TiB2 mass fractions are less than 70% in composite granule, strengthening layer fine microstructures are uniform；Strengthening layer microhardness increases with the increase of TiB2 contents, improves 46 times than matrix hardness, wear-resisting property significantly improves.
Description
Technical field
The present invention relates to a kind of surface-alloyization material more particularly to a kind of laser melting coating Al/TiB2 complex intensifying layers.
Background technology
Magnesium alloy is to realize that light-weighted one of equipment is important as the structural metallic materials for having used density minimum at present
Approach, but the anti-corrosion and wear-resisting of it waits poor-performings, limits it and further develops.Failure (such as corrosion, wear of metal material
With fracture etc.) more start from surface, therefore theoretically can effectively be carried by the optimization to its surface microstructure and performance
Its high performance such as anti-corrosion, wear-resisting.
The common surface intensified technique of magnesium alloy mainly has thermal spraying, plating and differential arc oxidation etc..Laser technology is by clear
The features such as clean, energy saving and easily-controllable, makes the laser reinforcing process such as laser melting coating obtained in terms of material surface processing increasingly wider
General application.
Invention content
The purpose of the invention is to improve the hardness of magnesium alloy, wearability, devise a kind of laser melting coating Al/TiB2 and answer
Close strengthening layer.
The technical solution adopted by the present invention to solve the technical problems is：
The raw material for preparing of laser melting coating Al/TiB2 complex intensifying layers includes：Basis material becomes for As-extruded Mg-15Gd-3Y rare earths
Shape magnesium alloy, chemical composition (mass fraction) be 15.26Gd, 2.11Y, remaining Mg.Using Al-TiB2 composite granules as Rankine
Material, wherein the mass fraction of TiB2 is respectively 0,30%, 50%, 70% and 100%.
The preparation process of laser melting coating Al/TiB2 complex intensifying layers is：By composite granule ball milling in nitrogen protection atmosphere
30min is uniformly mixed, then using mass fraction to be coated in after 5% poly-vinyl alcohol solution and alloying powder mixing through sand
Mg alloy surface after paper milled processed, the coating layer thickness after air-drying are controlled in 0.6mm or so.Using LCY-400 types Nd：YAG
Pulse laser carries out cladding and hardening processing, Optimizing Process Parameters to Mg alloy surface：Pulsewidth 0.8ms, frequency 45Hz, hot spot are straight
Diameter 1.0mm, electric current 220A, sweep speed 350mm/min.To prevent magnesium alloy substrate and composite granule in laser cladding process
It aoxidizes, employs the steady airflow atmosphere protection device of double-deck micro-grid.
The detecting step of laser melting coating Al/TiB2 complex intensifying layers is：Using 450 type scanning electron microscope of FEI Quanta
(SEM) observe and analyze the microstructure of strengthening layer；Using JEM-2100 types high-resolution-ration transmission electric-lens (TEM) analysis strengthening layer
Microcosmic fine structure and compatibility, sample are derived from and 20 μm away from surface layer depths parallel with surface, with fine sandpaper grinding sample extremely
Ion milling is used after 50 μm；The object phase of strengthening layer is surveyed using Xpert pro MPD types X-ray diffractometers (XRD)；Using
Micromet-3 type microhardnesses instrument measure Laser Strengthening Layer through-thickness hardness distribution, added load be 0.5N, pressurize
Time 15s；Using MMS-1G type pin disk-type friction abrasion testers, friction disk material is GCr15 steel for friction and wear behavior test
(being quenched through 850 DEG C of oil baths, 180 DEG C of lonneal processing, hardness 62HRC), polishes flour milling, acetone is clear with 600# sand paper
It washes, friction rate is 4m/s, and load 40N, test period 200s are tested at room temperature.
The laser melting coating Al/TiB2 complex intensifying layers, when TiB2 mass fractions are less than 70%, laser melting coating is strengthened
The fine microstructures of layer are uniform, during more than 70%, block-like TiB2 hardening constituents occur in strengthening layer；The high-temperature rigid of fabricated in situ
The intermetallic compounds such as phase Al2Gd, Al2Y size is evenly distributed in 100nm or so, and the hardening constituent TiB2 introduced is in disperse point
Cloth, grain size are 200nm or so, " chain-type " agglomeration locally occur.
The laser melting coating Al/TiB2 complex intensifying layers, gadolinium, the yttrium in aluminium element and matrix in composite granule etc. are first
Element produces reaction in-situ, generates the intermetallic compounds such as high-temperature rigid phase Al2Gd and Al2Y, and introduced in cladding process
Hardening constituent TiB2 does not decompose, good with the high-temperature-phase and matrix compatibility that are newly formed, but characteristic distributions and architectural difference are shown
It writes.
The laser melting coating Al/TiB2 complex intensifying layers, compared with magnesium alloy substrate, the microhardness of strengthening layer improves
4-6 times, and increasing with TiB2 contents, the hardness of alloying layer is in increased trend；Suitable TiB2 reinforced phases are advantageous
In the friction and wear behavior for improving magnesium alloy materials.
The beneficial effects of the invention are as follows：
To improve the corrosion resisting property and wear-resisting property of magnesium alloy materials, using Al-TiB2 composite granules as strengthening material, using laser
Melting and coating process has carried out magnesium alloy surface Hardening Treatment, and the microhardness of strengthening layer increases with the increase of TiB2 amounts, than
Matrix hardness improves 4-6 times, and wear-resisting property significantly improves.
Specific embodiment
Case study on implementation 1：
The raw material for preparing of laser melting coating Al/TiB2 complex intensifying layers includes：Basis material becomes for As-extruded Mg-15Gd-3Y rare earths
Shape magnesium alloy, chemical composition (mass fraction) be 15.26Gd, 2.11Y, remaining Mg.Using Al-TiB2 composite granules as Rankine
Material, wherein the mass fraction of TiB2 is respectively 0,30%, 50%, 70% and 100%.The system of laser melting coating Al/TiB2 complex intensifying layers
It is for step：Composite granule ball milling 30min is uniformly mixed in nitrogen protection atmosphere, then using mass fraction be 5% it is poly-
Glycohol solution is with being coated in the Mg alloy surface after sand paper milled processed after alloying powder mixing, the painting thickness after air-drying
Degree control is in 0.6mm or so.Using LCY-400 types Nd：YAG pulse lasers carry out cladding and hardening processing to Mg alloy surface,
Optimizing Process Parameters：Pulsewidth 0.8ms, frequency 45Hz, spot diameter 1.0mm, electric current 220A, sweep speed 350mm/min.It is anti-
Only magnesium alloy substrate and composite granule aoxidize in laser cladding process, employ the steady airflow atmosphere protection of double-deck micro-grid
Device.The detecting step of laser melting coating Al/TiB2 complex intensifying layers is：Using 450 type scanning electron microscope (SEM) of FEI Quanta
Observation and the microstructure of analysis strengthening layer；Using the microcosmic of JEM-2100 types high-resolution-ration transmission electric-lens (TEM) analysis strengthening layer
Fine structure and compatibility, sample are derived from and 20 μm away from surface layer depths parallel with surface, and sample is ground to 50 μm with fine sandpaper
After use ion milling；The object phase of strengthening layer is surveyed using Xpert pro MPD types X-ray diffractometers (XRD)；Using Micromet-3
Type microhardness instrument measures the hardness distribution of Laser Strengthening Layer through-thickness, and added load is 0.5N, dwell time 15s；It rubs
Scouring damage performance test is GCr15 steel (through 850 DEG C of oil using MMS-1G type pin disk-type friction abrasion testers, friction disk material
Bath quenching, 180 DEG C of lonneal processing, hardness 62HRC), flour milling is polished with 600# sand paper, acetone cleaning, friction speed
Rate is 4m/s, and load 40N, test period 200s are tested at room temperature.
Case study on implementation 2：
Alloying layer, transition zone and matrix three parts can be divided into after surface peening, and with the increase of TiB2 contents, alloying layer
The uniformity of tissue is in downward trend.When TiB2 mass fractions are less than 70%, the tissue of alloying layer is more uniform, introduces
Reinforced phase be in Dispersed precipitate；When TiB2 mass fractions are more than 70%, due to there is no enough aluminum meltings in molten bath as bonding
Agent leads to alloying nonuniform organization；When TiB2 mass fractions are 100%, in its own gravity and molten bath convection current comprehensive function
Under there is the phenomenon that TiB2 " insertion " matrix, overall distribution uniformity is poor.From the point of view of the thickness of alloying layer, with
When the increase of TiB2 contents, especially mass fraction are more than 70%, the depth of alloying layer is shallower, this may be due to aluminium and
TiB2 is to caused by laser absorption utilization rate difference.In addition, the stickiness of molten metal bath is also to influence alloying layer group in molten bath
It knits and an important factor for homogeneity of ingredients, in the moment of laser scanning, the alloy powder for being layered on Mg alloy surface in advance is heated first
Fusing, is then only the fusing of basis material, therefore, the presence of a certain amount of aluminium can increase the convection effect in molten bath, be conducive to
The uniformity of alloying layer microstructure and the Dispersed precipitate of reinforced phase.
Case study on implementation 3：
The object of magnesium alloy substrate is mainly mutually magnesium；The primary product of pure aluminum alloy layer is mutually aluminium, Al2Gd and Al2Y etc.；It is pure
The main object of TiB2 alloying layers is mutually magnesium and TiB2；Object phase in remaining alloying layer is main other than aluminium, Al2Gd and Al2Y
If TiB2.The fusing point of original object phase (such as MgGd3, GdMg5 and Mg24Y5) in magnesium alloy substrate is relatively low, since it is molten
It is decomposed during covering, its characteristic diffraction peak is caused to be not obvious；And decomposite the gadolinium come and yttrium and alloy element aluminium
In-situ reactive synthesis high-temperature rigid phase Al2Gd and Al2Y.With the increase of aluminium mass fraction in composite granule, high-temperature rigid phase
The characteristic diffraction peak intensity of Al2Gd and Al2Y is in the trend gradually enhanced, this shows cenotype Al2Gd and Al2Y in alloying layer
Relative amount with aluminium element in alloying layer ingredient the increase of ratio and increase, and remaining aluminium is mainly in the form of solid solution
It is present in alloying layer, so as to form the alloying layer of rich aluminium.Due to compound Mg 2Al3 and Al12Mg17 etc. between magnalium
The fusing point of object phase is relatively low, in laser melting coating, swashs the characteristics of heat shock is cold and determines that they are difficult to be formed in the process of setting of molten bath,
Therefore diffraction peak intensity is very low.In Mg alloy surface laser cladding process, gadolinium, yttrium almost all form aluminide high-temperature rigid
Phase, this shows that laser melting coating is a kind of nonequilibrium processing procedure.Without finding the compounds of other titaniums and boron other than TiB2,
This shows that TiB2 does not decompose in laser cladding process, is only solid-solution in alloying in the Quench process of setting in molten bath
In layer, so as to play invigoration effect as the second opposite alloying layer.
Case study on implementation 4：
The distribution of the cenotype of fabricated in situ such as Al2Gd and Al2Y in alloying layer than more uniform, the overwhelming majority in subsphaeroidal,
This pattern ensure that it will not generate the effect of isolating in stress to tissue；The compound size of formation is largely less than
100nm, the slightly larger precipitated phase of grain size is not single precipitated phase, but the aggregate of multiple particles.Micron order precipitated phase is real
It is the aggregate of nanoscale fabricated in situ phase on border, this is because caused by convection current is insufficient in molten bath in laser cladding process.
The TiB2 reinforced phase overall distributions of introducing are uniform, and grain size is relatively large, are 200nm or so, but locally lie in the group of " chain-type "
Poly- phenomenon, and pattern, based on quadrangle, this may be because the initial size of the TiB2 reinforced phases introduced is larger, and moment cannot
It is completely melt or caused by the melt that melts is difficult to disperse in Quench process of setting.All in all, the cenotype of fabricated in situ is such as
The compatibility of the TiB2 reinforced phases and matrix of Al2Gd and Al2Y and introducing is good, and there is no pointed shape or acicular structure,
This using cermet for improving alloying layer performance, the especially wear-resisting property containing brittleness hard phases strengthening layer
It is of great significance.
Case study on implementation 5：
Compared with magnesium alloy substrate, the surface microhardness of strengthening layer improves 4-6 times；With TiB2 contents in composite granule
Increase, the hardness of strengthening layer is in the trend gradually increased, and thickness is generally at 220 μm or so, and the thickness of pure TiB2 alloying layers
Minimum, only 120 μm or so, transition zone is relatively large.The raising of strengthening layer microhardness mainly has both sides reason：One
It is to swash the cold caused crystal grain of heat shock significantly to refine；Second is that the intermetallic compound of fabricated in situ and reinforced phase TiB2 in alloying layer
Introducing.In addition, an important factor for " class enamel " ceramic on its surface is also hardness raising.When the hardening constituent TiB2 matter of introducing
When amount score is 70%, friction factor has reached maximum, but still less than without Alloying Treatment magnesium alloy, pure TiB2 strengthening layers
Friction factor it is minimum；With the increase of TiB2 contents, mass loss during abrasion first increases and then decreases, 70% when, is maximum, and pure TiB2 is strong
The mass loss during abrasion for changing layer is minimum.It is formd in situ in strengthening layer between the metal that grain size is tiny, hardness is higher and is evenly distributed
Compound, it is larger to the integral hardness contribution for improving strengthening layer, and the hardening constituent TiB2 with higher melt introduced is in laser
It takes the lead in being precipitated during claddingization, " be inlayed " in matrix under the convection action in molten bath, these hardening constituents are in fretting wear
Come off in journey by the effect of shear stress, accelerated wear test, so as to play negative effect to polishing machine, wear mechanism also by
Adhesive wear is changed into based on abrasive wear.Compared with the magnesium alloy without intensive treatment, the friction of laser surface intensified layer
Factor and mass loss during abrasion all show a degree of reduction, especially pure TiB2 strengthening layers, in high energy laser beam
Under effect, ceramic is showed, does not occur apparent wear phenomenon substantially, therefore suitable TiB2 contents (such as 30%) are conducive to
Improve the friction and wear behavior of magnesium alloy materials.
Claims (4)
1. a kind of laser melting coating Al/TiB2 complex intensifying layers, prepare raw material and include：Basis material is dilute for As-extruded Mg-15Gd-3Y
Native wrought magnesium alloy, chemical composition (mass fraction) be 15.26Gd, 2.11Y, remaining Mg, using Al-TiB2 composite granules as by force
Change material, the wherein mass fraction of TiB2 is respectively 0,30%, 50%, 70% and 100%.
2. laser melting coating Al/TiB2 complex intensifying layers according to claim 1, it is characterized in that laser melting coating Al/TiB2 is answered
Close strengthening layer preparation process be：Composite granule ball milling 30min is uniformly mixed in nitrogen protection atmosphere, then utilizes quality
The poly-vinyl alcohol solution that score is 5% is with being coated in the Mg alloy surface after sand paper milled processed, wind after alloying powder mixing
Coating layer thickness control after dry is in 0.6mm or so, using LCY-400 types Nd：YAG pulse lasers melt Mg alloy surface
Cover intensive treatment, Optimizing Process Parameters：Pulsewidth 0.8ms, frequency 45Hz, spot diameter 1.0mm, electric current 220A, sweep speed
To prevent magnesium alloy substrate and composite granule from being aoxidized in laser cladding process, it is steady to employ double-deck micro-grid by 350mm/min
Airflow atmosphere protection device.
3. laser melting coating Al/TiB2 complex intensifying layers according to claim 1, it is characterized in that laser melting coating Al/TiB2 is answered
Close strengthening layer detecting step be：The microcosmic of strengthening layer is observed and analyzed using 450 type scanning electron microscope (SEM) of FEI Quanta
Tissue；It is taken using the microcosmic fine structure and compatibility, sample of JEM-2100 types high-resolution-ration transmission electric-lens (TEM) analysis strengthening layer
From at and away from surface 20 μm layer depths parallel with surface, sample is ground to using ion milling after 50 μm with fine sandpaper；Utilize Xpert
Pro MPD types X-ray diffractometers (XRD) survey the object phase of strengthening layer；It is strong that laser is measured using Micromet-3 type microhardnesses instrument
Change the hardness distribution of layer through-thickness, added load is 0.5N, dwell time 15s；Friction and wear behavior test is using MMS-
1G type pin disk-type friction abrasion testers, friction disk material (quench, at 180 DEG C of lonneals for GCr15 steel through 850 DEG C of oil baths
Manage, hardness 62HRC), flour milling is polished with 600# sand paper, acetone cleaning, friction rate is 4m/s, load 40N, is tested
Time is 200s, is tested at room temperature.
4. laser melting coating Al/TiB2 complex intensifying layers according to claim 1, it is characterized in that the laser melting coating Al/
TiB2 complex intensifying layers, when TiB2 mass fractions are less than 70%, the fine microstructures of laser melting coating strengthening layer are uniform, more than 70%
When, there are block-like TiB2 hardening constituents in strengthening layer；The intermetallics such as high-temperature rigid phase Al2Gd, Al2Y of fabricated in situ
Object size is evenly distributed in 100nm or so, and the hardening constituent TiB2 introduced is in Dispersed precipitate, and grain size is 200nm or so, part
There is " chain-type " agglomeration, the laser melting coating Al/TiB2 complex intensifying layers, aluminium element and base in composite granule
The elements such as gadolinium, yttrium in body produce reaction in-situ, generate the intermetallic compounds such as high-temperature rigid phase Al2Gd and Al2Y, and
The hardening constituent TiB2 introduced in cladding process does not decompose, good with the high-temperature-phase and matrix compatibility that are newly formed, but is distributed
Feature and architectural difference are notable, the laser melting coating Al/TiB2 complex intensifying layers, compared with magnesium alloy substrate, strengthening layer
Microhardness improves 4-6 times, and increasing with TiB2 contents, and the hardness of alloying layer is in increased trend；It is suitable
TiB2 reinforced phases are conducive to improve the friction and wear behavior of magnesium alloy materials.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110412063A (en) * | 2019-07-16 | 2019-11-05 | 武汉理工大学 | The experimental method of spheroidising laser direct forming biphase titanium alloy α precipitated phase |
| CN110426410A (en) * | 2019-07-16 | 2019-11-08 | 武汉理工大学 | Adjust the experimental method of titanium alloy α/β phase interface local state |
| CN111235567A (en) * | 2020-03-10 | 2020-06-05 | 昆明理工大学 | Rare earth doped material and preparation method of coating thereof |
| CN111521622A (en) * | 2020-04-10 | 2020-08-11 | 燕山大学 | Method for researching oxidation process of metal film transmission electron microscope sample |
-
2016
- 2016-12-07 CN CN201611116902.7A patent/CN108165975A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110412063A (en) * | 2019-07-16 | 2019-11-05 | 武汉理工大学 | The experimental method of spheroidising laser direct forming biphase titanium alloy α precipitated phase |
| CN110426410A (en) * | 2019-07-16 | 2019-11-08 | 武汉理工大学 | Adjust the experimental method of titanium alloy α/β phase interface local state |
| CN111235567A (en) * | 2020-03-10 | 2020-06-05 | 昆明理工大学 | Rare earth doped material and preparation method of coating thereof |
| CN111521622A (en) * | 2020-04-10 | 2020-08-11 | 燕山大学 | Method for researching oxidation process of metal film transmission electron microscope sample |
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Application publication date: 20180615 |