CN102899606A - Method for controlling recrystallization of directionally solidified Ni-based superalloy by alumetizing - Google Patents
Method for controlling recrystallization of directionally solidified Ni-based superalloy by alumetizing Download PDFInfo
- Publication number
- CN102899606A CN102899606A CN2011102135419A CN201110213541A CN102899606A CN 102899606 A CN102899606 A CN 102899606A CN 2011102135419 A CN2011102135419 A CN 2011102135419A CN 201110213541 A CN201110213541 A CN 201110213541A CN 102899606 A CN102899606 A CN 102899606A
- Authority
- CN
- China
- Prior art keywords
- recrystallize
- directional solidification
- aluminising
- temperature alloy
- base high
- 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.)
- Pending
Links
Images
Abstract
The invention provides a method for controlling the recrystallization of directionally solidified Ni-based superalloy by alumetizing, characterized by carrying out alumetizing on the surface of a directionally solidified Ni-based superalloy component that is deformed by alumetizing,; and carrying out standard solution treatment of alloy matrixes on the alumetized directionally solidified Ni-based superalloy component. According to the invention, the depth of the recrystallization of the directionally solidified Ni-based superalloy is controllable, and the control effect on the recrystallization caused by uniform deformation is significant. Compared with recrystals generated by deformed directionally solidified alloy sample without alumetizing, the recrystals are distributed scatteredly and nonuniformly, the maximum recrystallization depth is obviously reduced, the recrystallization area is correspondingly obviously reduced, there is no residual stress in electroplating process, thus the possibility of generating recrystals by residual stress is avoided. The alumetizing method is one of the most efficient methods for inhibiting the development of recrystallization.
Description
Technical field
The present invention relates to the control techniques of recrystallize, specifically a kind of technology of utilizing calorizing control directional freeze column crystal and monocrystal nickel-base high-temperature alloy recrystallize.
Background technology
Internal combustion turbine, blade of aviation engine all are to use under comparatively high temps, and blade mainly is subjected to centrifugal action, and at high temperature, the intensity of crystal boundary is not as intracrystalline intensity, and transverse grain boundaries has just become the weak link of blade.For this reason, people have been developed directional columnargrain even single crystal blade and have been eliminated transverse grain boundaries or whole crystal boundaries.Compare with traditional polycrystalline blade, these blades have the warm ability of holding of better vertical mechanical property and Geng Gao.
But blade is in the directional freeze process, because the difference of metal and ceramic-mould, core thermal expansivity, foundry goods can produce distortion.Also might produce distortion in school shape subsequently, sandblast, soldering even the military service process.Like this, vanes pyroprocessing (TRANSIENT HIGH TEMPERATURE in solution treatment or the military service process) will produce recrystallize.Recrystallize produces transverse grain boundaries, so formed again the weak link of blade, has a strong impact on the performance of blade.
At present, recrystallize for the directional solidification blade generation, Adopts measure mainly is to control the distortion of blade (as reduce mechanical workout as far as possible, optimization design casting mold, core etc.) prevent blade to produce recrystallize, perhaps set up blade recrystallize standard, the strict detection, the blade that surpasses a certain degree recrystallize is scrapped at once.
Because blade inevitably passes through some operation (such as solidification shrinkage, sandblast etc.) in process of production, the distortion that these operations produce just can't be avoided.The recrystallize meeting decrease Blade roughcast qualification rate of bringing therefrom increases cost, has a strong impact on production efficiency.
Because the detrimental action of above-mentioned recrystallize, people attempt to control recrystallize by certain processing method.About the control of recrystallize, some relevant reports are arranged abroad.European patent (patent No.: EP 1038982 A1) adopts the method for gas (mainly being the mixed gas of CO and argon gas) carburizing that carbon is diffused into and forms carbide in the alloy substrate, utilize carbide particle hinder crystal boundary migration be used for control recrystallize and recrystallize localized.The method equipment is complicated, operate more loaded down with trivial detailsly, controls recrystallize with the method for control growth, and is mainly used in single crystal alloy.United States Patent (USP) (the patent No.: 5551999) adopt lesser temps repeatedly to reply heat-treating methods and control recrystallize, the method can not suppress recrystallize surface forming core, and it is longer to reply the heat treated time, the easy oxidation of alloy substrate, and it is unfavorable that this alloy uses.The method that adopts in addition the aluminising the inside to add the grain-boundary strengthening element is strengthened the recrystallize crystal boundary, and (patent No.: EP 1036850A1), the method is mainly for monocrystal nickel-base high-temperature alloy in the Crack prevention generation.What this method was mainly considered is after recrystallize produces, and how to manage to eliminate the disadvantageous effect of recrystallize, namely strengthens the recrystallize crystal boundary, rather than manages to suppress the generation of recrystallize.What is more, adopts the method for chemical corrosion directly with the recrystallized layer erosion removal (patent No.: 5413648).Although the method can be removed recrystallized layer, obviously inapplicable for thin-walled monocrystalline or directional columnargrain nickel base superalloy parts.
The problem that the processing method of above-mentioned patent application control recrystallize exists:
(1) equipment of gas carburizing is complicated, operate more loaded down with trivial detailsly, hinders the migration of crystal boundary by the carbide ion and controls recrystallize, is mainly used in single crystal alloy.
(2) lesser temps is repeatedly replied heat treating process and can not be suppressed recrystallize surface forming core, and it is longer to reply the heat treated time, the easy oxidation of alloy substrate, and it is unfavorable that alloy uses.
(3) aluminising the inside adds the method for grain-boundary strengthening element, mainly for be monocrystal nickel-base high-temperature alloy.The method mainly is how to consider to eliminate the disadvantageous effect of recrystallize after crystallization produces.
(4) chemical corrosion method is directly with the recrystallized layer erosion removal.This method is not suitable for thin-walled monocrystalline or directional columnargrain nickel base superalloy parts.
Summary of the invention
The object of the invention provides a kind of method of controlling the directional solidification nickel-base high-temperature alloy recrystallize, and specifically a kind of method of aluminising control directional solidification nickel-base high-temperature alloy recrystallize significantly reduces the recrystallize that produces behind the deformable blade.
The invention provides a kind of method of utilizing calorizing control directional solidification nickel-base high-temperature alloy recrystallize, it is characterized in that: adopt calorizing to carry out aluminising at the directional solidification nickel-base high-temperature alloy device surface that produces distortion and process; Directional solidification nickel-base high-temperature alloy device after the above-mentioned aluminising processing is carried out the standard solution treatment.Different from the patent of gas cementation control recrystallize is that aluminising here coats by part on the one hand and suppresses recrystallize surface forming core, mainly is penetrated into the development that is used for suppressing recrystallize that alloy substrate suppresses Elements Diffusion by aluminium element on the other hand.Different from coating control recrystallize is that the aluminising process does not almost produce unrelieved stress, does not need stress relief annealing, has avoided the possibility of the unrelieved stress formation recrystallize of coating generation.
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, the penetration enhancer of its aluminising are NH
4Cl, Al powder and Al
2O
3Powder.
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, the granularity of Al powder is in its penetration enhancer
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, Al in its penetration enhancer
2O
3The granularity of powder is
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, the proportioning of its penetration enhancer are 5～20%NH
4Cl, 35～60%Al
2O
3The Al powder (weight percent) of powder and surplus.
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, its aluminising temperature is 400～650 ℃.
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, its aluminising time is 5～30h.
The method of control directional solidification nickel-base high-temperature alloy recrystallize provided by the invention, its aluminising protective atmosphere is argon gas, 1～5 normal atmosphere of pressure.
The invention provides a kind of method of aluminizing method control directional solidification nickel-base high-temperature alloy recrystallize, its advantage is:
(1) calorizing provided by the present invention coats by part and can suppress recrystallize.
(2) the present invention is penetrated into the development that is used for suppressing recrystallize that alloy substrate suppresses Elements Diffusion by aluminium element.
(3) aluminising process of the present invention does not almost produce unrelieved stress, does not need stress relief annealing, has avoided unrelieved stress to produce the possibility of recrystallize.
(4) method of control recrystallize provided by the present invention can make the recrystallize behind the deformable blade of internal combustion turbine and aircraft engine significantly reduce.
(5) the present invention's operation is easy to control, enhances productivity.
Description of drawings
After Fig. 1 is water sandblast distortion directional solidification nickel-base high-temperature alloy, there is not aluminising and the direct recrystallized structure that produces of solution treatment.
After Fig. 2 is water sandblast distortion directional solidification nickel-base high-temperature alloy, after the aluminising, the recrystallized structure that produces through solution treatment again.
Embodiment
Give further instruction below by embodiment to the present invention, certainly, the present invention is not limited only to following embodiment.
Embodiment 1 aluminising control DZ125L alloy recrystallization
Apparatus for directional solidification is prepared DZ125L directional solidification nickel-base nickel base superalloy plate, with the square that cuts 2 * 12 * 12mm on the line cutting slave plate.With the face polishing of 12 * 12 (the directional columnargrain directions of growth), carry out sandblasting with sandblast apparatus.The sandblast parameter is as follows: blasting pressure is 0.3MPa, and the sandblast time is 1min, and sand grains is SiO
2Glass sphere.
The preparation penetration enhancer, used diffusion agent formulation is as follows: 40%Al powder, 55%Al
2O
3Powder and 5%NH
4Cl (weight percent).Wherein, the granularity of Al powder is
Al
2O
3The granularity of powder is
Next, part sandblast sample is sneaked in the penetration enhancer, put into heat treatment furnace, temperature is raised to 600 ℃ of beginning aluminisings, and passes into argon shield, the aluminising time is 5h.The print that aluminising is complete takes out, and dries stand-by.
And then with these aluminising samples and directly the sandblast sample carry out the standard solution treatment, behind the air cooling sample cut and observes the recrystallized structure that produces.Directly the average recrystallize degree of depth of the sample of solution treatment reaches
The maximum recrystallize degree of depth reaches
The maximum recrystallize degree of depth of the sample after processing (Fig. 1), and through above-mentioned aluminising is
About (Fig. 2), be lower than the sample of direct sandblasting.And the recrystallize of aluminising sample distributes very inhomogeneous, and some position recrystallize is very little, so its average recrystallize degree of depth is about
About, be far smaller than the recrystallize degree of depth that direct sandblast produces.
Embodiment 2 aluminisings control DZ125L alloy recrystallization
Apparatus for directional solidification is prepared DZ125L directional solidification nickel-base nickel base superalloy plate, with the square that cuts 2 * 12 * 12mm on the line cutting slave plate.With the face polishing of 12 * 12 (the directional columnargrain directions of growth), carry out sandblasting with sandblast apparatus.The sandblast parameter is as follows: blasting pressure is 0.3MPa, and the sandblast time is 1min, and sand grains is SiO
2Glass sphere.
The preparation penetration enhancer, used diffusion agent formulation is as follows: 50%Al powder, 40%Al
2O
3Powder and 10%NH
4Cl (weight percent).Wherein, the granularity of Al powder is
Al
2O
3The granularity of powder is
Next, part sandblast sample is sneaked in the penetration enhancer, put into heat treatment furnace, temperature is raised to 600 ℃ of beginning aluminisings, and passes into argon shield, the aluminising time is 10h.The print that aluminising is complete takes out, and dries stand-by.
And then with these aluminising samples and directly the sandblast sample carry out the standard solution treatment, behind the air cooling sample cut and observes the recrystallized structure that produces.Directly the average recrystallize degree of depth of the sample of solution treatment reaches
The maximum recrystallize degree of depth reaches
And through the maximum recrystallize degree of depth of the sample after the above-mentioned aluminising processing be
About, be lower than the sample of direct sandblasting.And the recrystallize of aluminising sample distributes very inhomogeneous, and some position recrystallize is very little, so its average recrystallize degree of depth is about
About, be far smaller than the recrystallize degree of depth that direct sandblast produces.
Embodiment 3 aluminisings control DZ17G alloy recrystallization
Apparatus for directional solidification is prepared DZ17G directional solidification nickel-base nickel base superalloy plate, with the square that cuts 2 * 12 * 12mm on the line cutting slave plate.With the face polishing of 12 * 12 (the directional columnargrain directions of growth), carry out sandblasting with sandblast apparatus.The sandblast parameter is as follows: blasting pressure is 0.3MPa, and the sandblast time is 1min, and sand grains is SiO
2Glass sphere.
The preparation penetration enhancer, used diffusion agent formulation is as follows: 40%Al powder, 55%Al
2O
3Powder and 5%NH
4Cl (weight percent).Wherein, the granularity of Al powder is
Al
2O
3The granularity of powder is
Next, part sandblast sample is sneaked in the penetration enhancer, put into heat treatment furnace, temperature is raised to 600 ℃ of beginning aluminisings, and passes into argon shield, the aluminising time is 5h.The print that aluminising is complete takes out, and dries stand-by.
And then with these aluminising samples and directly the sandblast sample carry out the standard solution treatment, behind the air cooling sample cut and observes the recrystallized structure that produces.Directly the average recrystallize degree of depth of the sample of solution treatment reaches
The maximum recrystallize degree of depth reaches
And through the maximum recrystallize degree of depth of the sample after the above-mentioned aluminising processing be
About, be lower than the sample of direct sandblasting.And the recrystallize of aluminising sample distributes very inhomogeneous, and some position recrystallize is very little, so its average recrystallize degree of depth is about
About, be far smaller than the recrystallize degree of depth that direct sandblast produces.
Embodiment 4 aluminisings control DZ125L alloy recrystallization
Apparatus for directional solidification is prepared DZ125L directional solidification nickel-base nickel base superalloy plate, with the square that cuts 2 * 12 * 12mm on the line cutting slave plate.With the face polishing of 12 * 12 (the directional columnargrain directions of growth), carry out sandblasting with sandblast apparatus.The sandblast parameter is as follows: blasting pressure is 0.3MPa, and the sandblast time is 1min, and sand grains is SiO
2Glass sphere.
The preparation penetration enhancer, used diffusion agent formulation is as follows: 50%Al powder, 45%Al
2O
3Powder and 5%NH
4Cl (weight percent).Wherein, the granularity of Al powder is
Al
2O
3The granularity of powder is
Next, part sandblast sample is sneaked in the penetration enhancer, put into heat treatment furnace, temperature is raised to 600 ℃ of beginning aluminisings, and passes into argon shield, the aluminising time is 20h.The print that aluminising is complete takes out, and dries stand-by.
And then with these aluminising samples and directly the sandblast sample carry out the standard solution treatment, behind the air cooling sample cut and observes the recrystallized structure that produces.Directly the average recrystallize degree of depth of the sample of solution treatment reaches
The maximum recrystallize degree of depth reaches
And through the maximum recrystallize degree of depth of the sample after the above-mentioned aluminising processing be
About, be lower than the sample of direct sandblasting.And the recrystallize of aluminising sample distributes very inhomogeneous, and some position recrystallize is very little, so its average recrystallize degree of depth is about
About, be far smaller than the recrystallize degree of depth that direct sandblast produces.
By above-described embodiment explanation, the directly recrystallize contrast of being out of shape the generation of directional solidification nickel-base high-temperature alloy device of solution treatment with there not being aluminising, the recrystallize discrete distribution that produces by calorizing, very inhomogeneous, the degree of depth of control recrystallize, special more remarkable for the control action kou of recrystallize that homogeneous deformation produces, the recrystallize area occupied also correspondingly obviously reduces.
Claims (8)
1. method of utilizing calorizing control directional solidification nickel-base high-temperature alloy recrystallize is characterized in that:
(1) adopting calorizing to carry out aluminising at the directional solidification nickel-base high-temperature alloy device surface that produces distortion processes;
(2) the directional solidification nickel-base high-temperature alloy device after the above-mentioned aluminising processing is carried out the standard solution treatment of matrix alloy.
2. according to the method for control directional solidification nickel-base high-temperature alloy recrystallize claimed in claim 1, it is characterized in that: the penetration enhancer of described aluminising is NH
4Cl, Al
2O
3Powder and Al powder.
3. according to the method for control directional solidification nickel-base high-temperature alloy recrystallize claimed in claim 2, it is characterized in that: the granularity of Al powder is in the described penetration enhancer
4. according to the method for control directional solidification nickel-base high-temperature alloy recrystallize claimed in claim 2, it is characterized in that: Al in the described penetration enhancer
2O
3The granularity of powder is
5. according to the method for claim 1,2,3 or 4 described control directional solidification nickel-base high-temperature alloy recrystallize, it is characterized in that: the proportioning of described penetration enhancer is 5～20%NH
4Cl, 35～60%Al
2O
3The Al powder (weight percent) of powder and surplus.
6. according to the method for control directional solidification nickel-base high-temperature alloy recrystallize claimed in claim 5, it is characterized in that: described aluminising temperature is 400～650 ℃.
7. according to the method for control directional solidification nickel-base high-temperature alloy recrystallize claimed in claim 6, it is characterized in that: the described aluminising time is 5～30h.
8. according to the method for control directional solidification nickel-base high-temperature alloy recrystallize claimed in claim 7, it is characterized in that: described aluminising protective atmosphere is argon gas, and pressure is 1～5 normal atmosphere.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2011102135419A CN102899606A (en) | 2011-07-28 | 2011-07-28 | Method for controlling recrystallization of directionally solidified Ni-based superalloy by alumetizing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2011102135419A CN102899606A (en) | 2011-07-28 | 2011-07-28 | Method for controlling recrystallization of directionally solidified Ni-based superalloy by alumetizing |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN102899606A true CN102899606A (en) | 2013-01-30 |
Family
ID=47572091
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2011102135419A Pending CN102899606A (en) | 2011-07-28 | 2011-07-28 | Method for controlling recrystallization of directionally solidified Ni-based superalloy by alumetizing |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102899606A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105671482A (en) * | 2016-03-17 | 2016-06-15 | 南通航运职业技术学院 | Powder-embedded aluminizing medium and aluminizing method for nickel-based high-temperature alloy surface |
| CN105755428A (en) * | 2016-05-10 | 2016-07-13 | 南通中国科学院海洋研究所海洋科学与技术研究发展中心 | Diffusion agent and modification method for thermal diffusion of magnesium alloy surface with diffusion agent powder |
| CN106756684A (en) * | 2016-12-23 | 2017-05-31 | 贵州黎阳航空动力有限公司 | GH4049 spheroid aluminizing methods |
| CN106907952A (en) * | 2017-03-14 | 2017-06-30 | 中国科学院金属研究所 | Storage exchange piece for nontoxic space monopropellant engine and preparation method thereof |
| CN110487832A (en) * | 2019-08-29 | 2019-11-22 | 西安理工大学 | A kind of single crystal super alloy blast recrystallizes the evaluation method of tendency in the process |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101691649A (en) * | 2009-09-25 | 2010-04-07 | 朝阳金达钛业有限责任公司 | Titanizing and aluminizing agents for sponge titanium reactor and method |
| EP2322681A1 (en) * | 2009-11-11 | 2011-05-18 | Siemens Aktiengesellschaft | Method to avoid recrystallisation through alitization |
-
2011
- 2011-07-28 CN CN2011102135419A patent/CN102899606A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101691649A (en) * | 2009-09-25 | 2010-04-07 | 朝阳金达钛业有限责任公司 | Titanizing and aluminizing agents for sponge titanium reactor and method |
| EP2322681A1 (en) * | 2009-11-11 | 2011-05-18 | Siemens Aktiengesellschaft | Method to avoid recrystallisation through alitization |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105671482A (en) * | 2016-03-17 | 2016-06-15 | 南通航运职业技术学院 | Powder-embedded aluminizing medium and aluminizing method for nickel-based high-temperature alloy surface |
| CN105755428A (en) * | 2016-05-10 | 2016-07-13 | 南通中国科学院海洋研究所海洋科学与技术研究发展中心 | Diffusion agent and modification method for thermal diffusion of magnesium alloy surface with diffusion agent powder |
| CN106756684A (en) * | 2016-12-23 | 2017-05-31 | 贵州黎阳航空动力有限公司 | GH4049 spheroid aluminizing methods |
| CN106756684B (en) * | 2016-12-23 | 2018-01-23 | 贵州黎阳航空动力有限公司 | GH4049 spheroid aluminizing methods |
| CN106907952A (en) * | 2017-03-14 | 2017-06-30 | 中国科学院金属研究所 | Storage exchange piece for nontoxic space monopropellant engine and preparation method thereof |
| CN110487832A (en) * | 2019-08-29 | 2019-11-22 | 西安理工大学 | A kind of single crystal super alloy blast recrystallizes the evaluation method of tendency in the process |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Perrut et al. | High temperature materials for aerospace applications: Ni-based superalloys and γ-TiAl alloys | |
| CN109014215B (en) | A kind of heat treatment method of increasing material manufacturing monocrystal nickel-base high-temperature alloy | |
| CN102899606A (en) | Method for controlling recrystallization of directionally solidified Ni-based superalloy by alumetizing | |
| US7584778B2 (en) | Method of producing a castable high temperature aluminum alloy by controlled solidification | |
| CN102071385B (en) | Controlled directional solidification nickel-base high-temperature alloy recrystallizing method | |
| CN108468015B (en) | Nickel-based superalloy surface aluminizing method and product and nickel-based superalloy surface aluminum-chromium-silicon solid powder aluminizing agent | |
| JP2000107852A (en) | Grain-orienting solidified cast product and production thereof | |
| CN103451736B (en) | A kind of method reducing single crystal super alloy precision castings recrystallize | |
| GB2462704A (en) | A nickel-based single crystal component with regions having different precipitate microstructures | |
| CN102071384B (en) | Controlled directional solidification nickel-base high-temperature alloy recrystallizing method | |
| CN102071426B (en) | Method for eliminating recrystallization of directionally solidified nickel-based high-temperature alloy | |
| CN113444920B (en) | Nickel-based single crystal superalloy with low tendency to loose formation and preparation process thereof | |
| CN113265563B (en) | Ni high-temperature alloy with good heat corrosion resistance and preparation method thereof | |
| CN102071383B (en) | Method for controlling re-crystallization of directionally solidified nickel base high-temperature alloy by using coating method | |
| CN102899696B (en) | A kind of coating controls the method for directional solidification nickel-base high-temperature alloy recrystallize | |
| CN109385590A (en) | A kind of control method of single crystal super alloy recrystallization | |
| Lacaze et al. | Directionally solidified materials: nickel-base superalloys for gas turbines | |
| WU et al. | Kinetics and microstructural evolution during recrystallization of a Ni3Al-based single crystal superalloy | |
| Zheng et al. | Preparation of alumina/aluminide coatings on molybdenum metal substrates, and protection performance evaluation utilizing a DZ40M superalloy casting test | |
| US11198931B2 (en) | Process for preventing recrystallization of shot peened blade roots during a heat treatment process | |
| EP2450146A1 (en) | Shot peening in combination with an heat treatment and a component | |
| CN112160031B (en) | Method for prolonging high-temperature durable life of directionally solidified columnar crystal or monocrystal high-temperature alloy casting | |
| US20080138648A1 (en) | Layer system with blocking layer, and production process | |
| CN102071393A (en) | Carburization method for controlling recrystallization of unidirectionally solidified nickel-based high temperature alloy | |
| Zhu et al. | Tensile deformation behaviors and damage mechanisms of SRR99 superalloy bicrystals with different grain boundary misorientations |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20130130 |