CN100516276C - Niobium particle enhanced magnesium base amorphous alloy composite material and its preparation method - Google Patents
Niobium particle enhanced magnesium base amorphous alloy composite material and its preparation method Download PDFInfo
- Publication number
- CN100516276C CN100516276C CNB2006101342961A CN200610134296A CN100516276C CN 100516276 C CN100516276 C CN 100516276C CN B2006101342961 A CNB2006101342961 A CN B2006101342961A CN 200610134296 A CN200610134296 A CN 200610134296A CN 100516276 C CN100516276 C CN 100516276C
- Authority
- CN
- China
- Prior art keywords
- amorphous alloy
- composite material
- base amorphous
- particle
- alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 53
- 239000002245 particle Substances 0.000 title claims abstract description 40
- 239000002131 composite material Substances 0.000 title claims abstract description 30
- 238000002360 preparation method Methods 0.000 title claims abstract description 9
- 239000010955 niobium Substances 0.000 title claims description 44
- 229910052758 niobium Inorganic materials 0.000 title claims description 12
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 title claims description 8
- 239000011777 magnesium Substances 0.000 title description 15
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 title description 4
- 229910052749 magnesium Inorganic materials 0.000 title description 4
- 239000010949 copper Substances 0.000 claims abstract description 23
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 21
- 239000000956 alloy Substances 0.000 claims abstract description 21
- 238000002844 melting Methods 0.000 claims abstract description 13
- 230000008018 melting Effects 0.000 claims abstract description 13
- 230000006698 induction Effects 0.000 claims abstract description 12
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 239000011159 matrix material Substances 0.000 claims description 22
- 239000011261 inert gas Substances 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 8
- 239000007921 spray Substances 0.000 claims description 5
- 239000007788 liquid Substances 0.000 claims description 4
- 238000002156 mixing Methods 0.000 claims description 3
- 229910052709 silver Inorganic materials 0.000 claims description 3
- 238000003756 stirring Methods 0.000 claims description 3
- 238000005303 weighing Methods 0.000 claims description 3
- 238000000034 method Methods 0.000 abstract description 8
- 230000015572 biosynthetic process Effects 0.000 abstract description 3
- 229910000861 Mg alloy Inorganic materials 0.000 abstract description 2
- 238000003723 Smelting Methods 0.000 abstract 1
- 238000000465 moulding Methods 0.000 abstract 1
- 208000010392 Bone Fractures Diseases 0.000 description 6
- 206010017076 Fracture Diseases 0.000 description 6
- 206010010214 Compression fracture Diseases 0.000 description 5
- 238000010008 shearing Methods 0.000 description 4
- 239000000919 ceramic Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000008187 granular material Substances 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000004455 differential thermal analysis Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 238000007496 glass forming Methods 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 230000004807 localization Effects 0.000 description 1
- 239000011208 reinforced composite material Substances 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 210000003462 vein Anatomy 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Images
Landscapes
- Powder Metallurgy (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention relates to a technique for preparing magnesium alloys, in particular to composite material of magnuminium amorphous alloy which is strengthened by plastic Nb particles and process for preparation. The basic components of the composite material include Mg65Cu20Ag5Gd10 (at. %). The intensity and the plasticity of the composite material can be obviously increased through adding Nb particles with different volume percentages in the process of melting alloy, under the condition that the formation capability of amorphous alloy is kept to be unchangeable. The composite material can be prepared by the method of induction smelting and copper mould molding. Compared with the conventional amorphous alloy, the plasticity of the index composite material is obviously increased, and the invention overcomes the shortcoming of brittle fracture of the typical amorphous alloy, thereby having certain application value.
Description
Technical field
The present invention relates to the magnesium alloy technology of preparing, be specially a kind of plasticity Nb particle enhanced magnesium-base amorphous alloy composite material and preparation method thereof.
Background technology
Amorphous metallic material is because its unique atom arrangement, and promptly long-range is unordered and short range order makes it have excellent use properties, for example: high strength, high elastic limit and excellent corrosion resisting performance or the like.And magnesium-base amorphous alloy is owing to its high specific strength, special advantages such as be easy to recycle and become the new engineering material that has application prospect.In addition, China has abundant magnesium resource, more makes the magnesium-base amorphous metallic substance of R and D have realistic meaning.
But the distortion of amorphous alloy is a kind of distortion of height localization.Main deflection concentrates in several limited shear zones.Though the relative deformation in the shear zone can be very big, the amount of plastic deformation of amorphous alloy integral body is very limited.On the whole, amorphous alloy is a kind of hard brittle material.Magnesium-base amorphous alloy then is one of the most crisp several amorphous alloys, and its fracture mode can be considered to a kind of typical brittle rupture.This intrinsic fragility has greatly limited the practical application of magnesium-base amorphous alloy.
In order to improve the plasticity and toughness energy of amorphous alloy, people have been developed various amorphous alloy composite materials.Give birth to precipitated phase in various containing or add particle and the amorphous alloy composite material of fiber has all shown certain plasticity.At present, the main method of enhancing magnesium-base amorphous alloy is that interior life is separated out the toughness phase or hindered the expansion of shear zone to improve its plasticity by adding the high-hardness ceramic particle.But, because the size of interior living precipitated phase is limited, or the intrinsic fragility of ceramic particle, these methods are very limited to the inhibition of shear zone.The room temperature compressive plastic deformation amount of the magnesium-base amorphous alloy composite material by the preparation of these methods only has 1%～3%.In order to make magnesium-base amorphous alloy become a kind of engineering materials of practicality, an urgent demand is sought and is more effectively strengthened means.
Summary of the invention
The object of the present invention is to provide a kind of plasticity Nb particle enhanced magnesium-base amorphous alloy composite material and preparation method thereof, solve magnesium-base amorphous alloy fragility big, be prone to problem such as brittle rupture, finally obtain the magnesium-base amorphous alloy composite material of high strength, high-ductility deformability.
Technical scheme of the present invention is:
The invention provides a kind of plasticity niobium particle enhanced magnesium-base amorphous alloy composite material, the composition of this matrix material is Mg
65Cu
20Ag
5Gd
10(at.%) compound with the Nb particle, Nb particulate percent by volume V
fBe 4%～8%, Nb particulate granularity is 20～50 μ m.
The present invention also provides the preparation method of above-mentioned plasticity Nb particle enhanced magnesium-base amorphous alloy composite material, and concrete steps are as follows:
(1) with Cu, after three kinds of elements of Ag and Gd (weight purity＞99.9%) mixed by the composition proportion weighing, arc melting was made master alloy in inert gas atmosphere;
(2) again with master alloy with after Mg mixes, induction melting is made Mg in inert gas atmosphere
65Cu
20Ag
5Gd
10(at.%) alloy;
(3) in inert gas atmosphere, with the Nb particle and the Mg of different volumes percentage ratio
65Cu
20Ag
5Gd
10Alloy liquid mixes, and the matrix material of induction stirring to obtain mixing;
(4) with matrix material alloy pig induction melting in inert gas atmosphere, and spray to cast obtains niobium particle enhanced magnesium-base amorphous alloy composite material in copper mold.
Magnesium-base amorphous alloy composite material prepared among the present invention confirms that through X-ray diffraction (XRD) and differential thermal analysis (DSC) the amorphous alloy composite material sample that is obtained has the feature of typical amorphous alloy.The Nb particulate adds the formation ability of both not damaged the amorphous alloy matrix, does not also change its thermodynamic behavior.Through being that to carry out strain rate be 2 * 10 for the composite sample of 2mm to diameter
-4s
-1The room temperature compression testing, and utilize scanning electron microscope (SEM) that the sample after the compression fracture is observed.
Performance index are:
Yield strength: σ
y=901 ± 30MPa (V
f=8%);
Amount of plastic deformation: ε
Plastic=12.1 ± 3% (V
f=8%).
The present invention has the following advantages:
1, the magnesium-base amorphous alloy of the present invention's employing is Mg
65Cu
20Ag
5Gd
10(at.%), Nb particulate percent by volume is 4%～8%.The Nb particulate adds the formation ability that does not change the amorphous alloy matrix, has kept the advantage of its high specific strength.The Nb particle of magnesium-base amorphous alloy and certain content is compared with typical amorphous alloy after the two is used, and Nb particle reinforced composite materials has higher intensity and plastic deformation ability.
2, the present invention has adopted that arc melting prepares that master alloy, induction melting prepare that magnesium-base amorphous alloy, Nb particle and magnesium-base amorphous alloy liquid electromagnetic mix, the induction melting spray to cast is to the medium step combination of copper mold, can obtain amorphous alloy composite material, preparation technology is simple.
Description of drawings
Fig. 1 a is the SEM Photomicrograph of matrix material.
Fig. 1 b is the X-ray diffraction curve of magnesium-base amorphous alloy and Nb particle enhanced magnesium-base amorphous alloy composite material.
Fig. 2 is the room temperature compression fracture curve of magnesium-base amorphous alloy and Nb particle enhanced magnesium-base amorphous alloy composite material.
Fig. 3 is the specimen surface SEM photo behind the fracture of composite materials.
Embodiment
The present invention is described in detail in detail by the following examples.
The present invention prepares plasticity Nb particle enhanced magnesium-base amorphous alloy composite material as follows:
With Cu, after three kinds of elements of Ag and Gd (weight purity＞99.9%) mix by the composition proportion weighing, in inert gas atmosphere, adopt conventional arc melting to make master alloy; Again with master alloy with after Mg mixes, in inert gas atmosphere, adopt conventional induction melting to make Mg
65Cu
20Ag
5Gd
10(at.%) alloy; In inert gas atmosphere, with the Nb particle (granularity is 20～50 μ m) and the Mg of different volumes percentage ratio
65Cu
20Ag
5Gd
10Alloy liquid mixes, and adopts the matrix material of conventional induction stirring to obtain mixing; The matrix material alloy pig is adopted conventional induction melting in inert gas atmosphere, and spray to cast obtains Nb particle enhanced magnesium-base amorphous alloy composite material, present embodiment rare gas element employing argon gas in copper mold.The copper mold concrete processing parameter of casting is as follows: the copper mold spray to cast is 10 in vacuum tightness
-3Pa, temperature are to carry out under 700 ℃ the condition.The SEM Photomicrograph of matrix material as shown in Figure 1a, as can be seen from the figure: the Nb particle of plasticity has hindered the motion and the expansion of shear zone effectively.By the homogeneous deformation of self, the nonhomogeneous strain that the Nb particle can absorb shear zone effectively and brought has also effectively promoted the germinating and the fork of secondary shearing band, feasible distortion is evenly distributed on the whole sample more, thereby has given sample good plastic deformation ability.
Embodiment 1
When at Mg
65Cu
20Ag
5Gd
10Add V in the alloy
fDuring=4% Nb particle, its room temperature compression fracture curve is seen the curve 2 among Fig. 2:
Yield strength: σ
y=839 ± 40MPa;
Amount of plastic deformation: ε
Plastic=5 ± 2.4%.
When at Mg
65Cu
20Ag
5Gd
10Add V in the alloy
fDuring=6% Nb particle,
Yield strength: σ
y=876 ± 40MPa;
Amount of plastic deformation: ε
Plastic=7 ± 3.2%.
When at Mg
65Cu
20Ag
5Gd
10Add V in the alloy
fDuring=8% Nb particle, its room temperature compression fracture curve is seen the curve 3 among Fig. 2:
Yield strength: σ
y=901 ± 30MPa;
Amount of plastic deformation: ε
Plastic=12.1 ± 3%.
Shown in Fig. 1 (b), from the diffraction curve of magnesium-base amorphous alloy (Nb granule content be zero) and present embodiment (Nb particle volume percentage composition is 8%) more as can be seen, the Nb particle adds the back and with matrix any chemical reaction does not take place, and does not also have obviously to influence the glass forming ability of amorphous alloy matrix.
Fig. 3 is the specimen surface SEM photo behind the fracture of composite materials.
Shown in Fig. 3 (a), the Nb particle of plasticity has hindered the motion and the expansion of shear zone effectively.Fig. 3 (b) shows the situation after shear zone moves to the Nb granule interior.By the homogeneous deformation of self, the nonhomogeneous strain that the Nb particle can absorb shear zone effectively and brought.Wherein inserting figure is the enlarged view of shear zone at particle and basal body interface place.Fig. 3 (c) shows the situation of a large amount of shear zone germinatings in distortion back.The Nb particulate adds germinating and the fork that has effectively promoted the secondary shearing band, makes distortion be evenly distributed in more on the whole sample.Inserting figure is the germinating of secondary shearing band and the enlarged view of fork situation.Fig. 3 (d) shows the situation of matrix material fracture surface.As seen on fracture surface, both there had been the typical vein columnar fracture of amorphous alloy matrix feature, had the tear face that forms after the shearing strain of plasticity Nb particle process intensive again.
Relevant comparative example 1
Single-phase magnesium-base amorphous alloy [J.Mater.Res.18 (2003) 1502 for H.Men, D.H.Kim].The about 800MPa of this YIELD STRENGTH, amount of plastic deformation is 0, its room temperature compression fracture curve is seen the curve 1 among Fig. 2.
Relevant comparative example 2
Give birth to the magnesium base amorphous matrix material [H.Ma, J.Xu, and E.Ma, Appl.Phys.Lett.83,2793 (2003)] of precipitated phase α-Fe in containing.This matrix material yield strength is near 1GPa, and amount of plastic deformation is about 1%.
Relevant comparative example 3
With the magnesium base amorphous matrix material of TiB ceramic particle enhanced [Y.K.Xu, H.Ma, J.Xu, E.Ma, Acta.Mater.53,1857 (2005)].This matrix material yield strength is near 1.3GPa, and amount of plastic deformation is about 1%～3%.
From embodiment 1-3 as can be seen, Nb particulate percent by volume Vf is 4%～8% o'clock, keeping amorphous alloy to form under the constant condition of ability, can obviously improve the intensity and the plasticity of matrix material; Compare with traditional amorphous alloy, the plasticity index of this matrix material has had tangible rising, has overcome the shortcoming of typical amorphous alloy brittle rupture.
Claims (3)
1, a kind of niobium particle enhanced magnesium-base amorphous alloy composite material, it is characterized in that: the composition of this matrix material is Mg
65Cu
20Ag
5Gd
10Compound with the Nb particle, Nb particulate percent by volume is 4%～8%, wherein Mg
65Cu
20Ag
5Gd
10Subscript refer to atomic percent.
2, according to the described niobium particle of claim 1 enhanced magnesium-base amorphous alloy composite material, it is characterized in that: Nb particulate granularity is 20～50 μ m.
3, according to the preparation method of the described niobium particle of claim 1 enhanced magnesium-base amorphous alloy composite material, it is characterized in that concrete steps are as follows:
(1) with Cu, after three kinds of elements of Ag and Gd mixed by the composition proportion weighing, in inert gas atmosphere, arc melting was made master alloy;
(2) again with master alloy with after Mg mixes, in inert gas atmosphere, induction melting is made Mg
65Cu
20Ag
5Gd
10Alloy;
(3) in inert gas atmosphere, with the Nb particle and the Mg of described percent by volume
65Cu
20Ag
5Gd
10Alloy liquid mixes, and the matrix material of induction stirring to obtain mixing;
(4) with matrix material alloy pig induction melting in inert gas atmosphere, and spray to cast obtains niobium particle enhanced magnesium-base amorphous alloy composite material in copper mold.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006101342961A CN100516276C (en) | 2006-11-17 | 2006-11-17 | Niobium particle enhanced magnesium base amorphous alloy composite material and its preparation method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006101342961A CN100516276C (en) | 2006-11-17 | 2006-11-17 | Niobium particle enhanced magnesium base amorphous alloy composite material and its preparation method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101186996A CN101186996A (en) | 2008-05-28 |
| CN100516276C true CN100516276C (en) | 2009-07-22 |
Family
ID=39479600
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2006101342961A Expired - Fee Related CN100516276C (en) | 2006-11-17 | 2006-11-17 | Niobium particle enhanced magnesium base amorphous alloy composite material and its preparation method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100516276C (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101368242B (en) * | 2008-10-16 | 2012-03-21 | 上海市机械制造工艺研究所有限公司 | Amorphous particle reinforced magnesium-base composite material and manufacture process |
| CN113913709B (en) * | 2021-10-09 | 2022-04-08 | 华中科技大学 | In-situ authigenic hybrid phase reinforced magnesium-based amorphous composite material based on selective phase dissolution and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20030140987A1 (en) * | 2002-01-25 | 2003-07-31 | Bae Dong Hyun | Ductile particle-reinforced amorphous matrix composite and method for manufacturing the same |
| JP2003221657A (en) * | 2002-01-30 | 2003-08-08 | Yonsei Univ | Amorphous matrix composite material reinforced by ductile particle, and manufacturing method therefor |
| CN1548572A (en) * | 2003-05-16 | 2004-11-24 | 中国科学院金属研究所 | Endogenous composite material of high-strength magnesium-base metallic glass |
| US20060130943A1 (en) * | 2002-07-17 | 2006-06-22 | Atakan Peker | Method of making dense composites of bulk-solidifying amorphous alloys and articles thereof |
| CN1844433A (en) * | 2005-04-06 | 2006-10-11 | 中国科学院金属研究所 | Magnesium alloy cast into amorphous block with centimeter size |
-
2006
- 2006-11-17 CN CNB2006101342961A patent/CN100516276C/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20030140987A1 (en) * | 2002-01-25 | 2003-07-31 | Bae Dong Hyun | Ductile particle-reinforced amorphous matrix composite and method for manufacturing the same |
| JP2003221657A (en) * | 2002-01-30 | 2003-08-08 | Yonsei Univ | Amorphous matrix composite material reinforced by ductile particle, and manufacturing method therefor |
| US20060130943A1 (en) * | 2002-07-17 | 2006-06-22 | Atakan Peker | Method of making dense composites of bulk-solidifying amorphous alloys and articles thereof |
| CN1548572A (en) * | 2003-05-16 | 2004-11-24 | 中国科学院金属研究所 | Endogenous composite material of high-strength magnesium-base metallic glass |
| CN1844433A (en) * | 2005-04-06 | 2006-10-11 | 中国科学院金属研究所 | Magnesium alloy cast into amorphous block with centimeter size |
Non-Patent Citations (1)
| Title |
|---|
| Synthesis and characterization of particulate reinforcedMg-based bulk metallic glass composites. Jieqiong Li et al.Materials Letters. 2006 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101186996A (en) | 2008-05-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109338172A (en) | A kind of 2024 aluminum matrix composites and preparation method thereof of high-entropy alloy enhancing | |
| CN110257684B (en) | Preparation process of FeCrCoMnNi high-entropy alloy-based composite material | |
| CN103952588A (en) | High-strength and high-conductivity graphene copper-based composite material and preparation method thereof | |
| CN102400001B (en) | Method for preparing granule reinforced aluminum-based composite material of in-situ intermetallic compound | |
| CN110273078B (en) | Magnetic (FeCoNi)1.5CuBmREn)PAl composite material and preparation method thereof | |
| CN103137281A (en) | Bonding La (Fe, Si) 13 base magnetocaloric effect material and preparation method and use thereof | |
| CN102154596A (en) | Zirconium-based amorphous alloy and preparation method thereof | |
| CN101492781A (en) | High-ductility titanium based ultra-fine crystal composite material and method for producing the same | |
| CN110273092A (en) | A kind of CoCrNi particle reinforced magnesium base compound material and preparation method thereof | |
| CN102212733B (en) | High-performance multi-principal-element alloy of nano cellular crystal texture structure | |
| CN102719769B (en) | High-strength aluminum-based bulk amorphous composite material | |
| CN101921930A (en) | Multicomponent microalloyed titanium alloy and preparation method thereof | |
| CN108326302A (en) | A kind of graphene enhancing aluminum alloy materials and preparation method thereof | |
| CN102021504A (en) | Magnesium-based amorphous/porous titanium double-phase three-dimensional communicated composite material and preparation method thereof | |
| CN110724885B (en) | Preparation method of large-size light magnesium-aluminum-based amorphous alloy | |
| CN114058892A (en) | Wear-resistant corrosion-resistant high-entropy alloy-based composite material and preparation method thereof | |
| Wang et al. | Achieving super-high strength in an aluminum based composite by reinforcing metallic glassy flakes | |
| CN1161483C (en) | High-strength in-situ Al-base composition | |
| CN102127668B (en) | Hybrid reinforced magnesium-based composite material of in-situ authigene magnesium oxide and intermetallic compound and preparation method thereof | |
| CN112410601B (en) | Preparation method of graphene-boron heterostructure titanium-based composite material | |
| CN100516276C (en) | Niobium particle enhanced magnesium base amorphous alloy composite material and its preparation method | |
| Xie et al. | Microstructure and properties of ceramic particulate reinforced metallic glassy matrix composites fabricated by spark plasma sintering | |
| CN105385902A (en) | AIN and AIB2 particle reinforced aluminum matrix composite material and preparation method thereof | |
| CN101451208A (en) | Block body aluminum-based alloy and preparation method thereof | |
| CN110846545B (en) | Metal ceramic composite material produced from powdered quartz ore and used for 3D printing and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| ASS | Succession or assignment of patent right |
Owner name: SHANGDONG HAIYUAN PHOTOELECTRIC SCIENCE + TECHNOLO Free format text: FORMER OWNER: METALLIC INST., CHINESE ACADEMY OF SCIENCES Effective date: 20140217 |
|
| COR | Change of bibliographic data |
Free format text: CORRECT: ADDRESS; FROM: 110016 SHENYANG, LIAONING PROVINCE TO: 265100 YANTAI, SHANDONG PROVINCE |
|
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20140217 Address after: 265100 Nanjing street, Haiyang Economic Development Zone, Shandong, Yantai Patentee after: SHANDONG HAIYUAN OPTOELECTRONICS Co.,Ltd. Address before: 110016 Shenyang, Liaoning Province Cultural Road, No. 72, Shenhe Patentee before: INSTITUTE OF METAL RESEARCH CHINESE ACADEMY OF SCIENCES |
|
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20090722 Termination date: 20211117 |