EP2450462B1 - Wear-resistant aluminum alloy extruded material having excellent fatigue strength and cutting properties - Google Patents
Wear-resistant aluminum alloy extruded material having excellent fatigue strength and cutting properties Download PDFInfo
- Publication number
- EP2450462B1 EP2450462B1 EP10794039.7A EP10794039A EP2450462B1 EP 2450462 B1 EP2450462 B1 EP 2450462B1 EP 10794039 A EP10794039 A EP 10794039A EP 2450462 B1 EP2450462 B1 EP 2450462B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- mass
- extruded material
- aluminum alloy
- content
- wear
- 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.)
- Active
Links
- 239000000463 material Substances 0.000 title claims description 47
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 36
- 238000005520 cutting process Methods 0.000 title description 5
- 239000011856 silicon-based particle Substances 0.000 claims description 27
- 239000013078 crystal Substances 0.000 claims description 23
- 229910052751 metal Inorganic materials 0.000 claims description 6
- 239000002184 metal Substances 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 4
- 230000000694 effects Effects 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 9
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 238000001953 recrystallisation Methods 0.000 description 7
- 229910052804 chromium Inorganic materials 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 239000002245 particle Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000011156 evaluation Methods 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 229910019752 Mg2Si Inorganic materials 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 235000012438 extruded product Nutrition 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 238000009661 fatigue test Methods 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000010730 cutting oil Substances 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000010720 hydraulic oil Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000003252 repetitive effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
Definitions
- the present invention relates to a wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength in addition to excellent machinability.
- the aluminum alloy extruded material When using an aluminum alloy extruded material for automotive brake parts and the like, the aluminum alloy extruded material is required to exhibit wear resistance against sliding parts, and may also required to exhibit high cutting (machining) accuracy and high caulking accuracy.
- a cylinder, a hydraulic circuit groove, and the like are machined when producing an actuator body (ABS body) used for an automotive antilock brake system, an electronic stability control (ESC) body used for an antiskid brake system, and the like, and a caulking seal is provided after assembly.
- ABS body actuator body
- ESC electronic stability control
- an aluminum alloy extruded material used for such applications is required to exhibit strength, wear resistance against sliding parts, machinability that allows processing into a complicated shape, pressure resistance against a hydraulic oil and the like (caulking section), and high fatigue strength against cyclic (repetitive) load.
- An aluminum alloy extruded material used for such parts is provided with wear resistance and machinability by dispersing Si particles and Fe particles in the metal structure.
- Such an aluminum alloy extruded material exhibits insufficient fatigue strength.
- Patent Document 1 discloses a wear-resistant aluminum alloy extruded material that exhibits excellent machinability and corrosion resistance. However, the aluminum alloy extruded material disclosed in Patent Document 1 exhibits insufficient caulking properties, fatigue strength, and the like.
- Patent Document 1 Japanese Patent No. 3886270
- An object of the invention is to provide a wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength and excellent machinability.
- a wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength and machinability
- the aluminum alloy extruded material being formed using an aluminum alloy that comprises 3.0 to 8.0 mass% of Si, 0.1 to 0.5 mass% of Mg, 0.01 to 0.5 mass% of Cu, 0.1 to 0.5 mass% of Zr, 0.4 to 0.9 mass% of Fe, 0.01 to 0.5 mass% of Mn, 0.01 to 0.5 mass% of Cr, and 0.01 to 0.1 mass% of Ti, with the balance being Al and unavoidable impurities.
- the inventor compared the effects of Zr, Mn, and Cr in detail, and found that Si particles contained in the metal structure (texture) are refined by adding a specific amount of Zr. Mn and Cr did not exhibit a significant Si particle refinement effect, but Zr exhibited a significant Si particle refinement effect.
- the fatigue strength was improved by thus suppressing fatigue propagation.
- the extruded material have an average Si particle size of 20 ⁇ m or less, and an average crystal grain size of 30 ⁇ m or less.
- the content range of each component of the aluminum alloy is adjusted for the following reasons.
- Si forms an Mg 2 Si precipitate with Mg, and provides the aluminum alloy with strength through age hardening.
- the Si particles contained in the metal structure also provide the aluminum alloy with wear resistance.
- the Mg content is set to 0.1 mass% or more taking account of these effects.
- the Mg content is preferably set to 0.3 mass% or more when it is desired to provide the aluminum alloy with higher strength.
- the Mg content is set to 0.5 mass% or less, and preferably 0.45 mass% or less.
- the Si content is set to 8.0 mass% or less.
- Cu improves the strength of the aluminum alloy while ensuring caulking properties. Since Cu is solid-dissolved to a certain extent, the strength and the machinability of the aluminum alloy are improved due to solid-solution hardening.
- the Cu content is set to 0.01 mass% or more taking account of these effects. If the Cu content is too high, potential difference corrosion tends to occur. Therefore, the Cu content is set to 0.50 mass% or less. The Cu content is preferably set to 0.10 to 0.20 mass%.
- the upper limit of the Cu content is more preferably set to 0.14 mass% or less.
- the Fe content is preferably set to 0.40 mass% or more taking account of these effects. If the Fe content exceeds 0.9 mass%, a large number of Fe particles may precipitate at the crystal grain boundaries. In this case, the caulking properties of the aluminum alloy may deteriorate due to a decrease in toughness.
- the Fe content is set to 0.4 to 0.9 mass%, and preferably 0.5 to 0.8 mass%.
- Zr suppresses recrystallization, and refines the crystal grains. Moreover, fatigue propagation is suppressed due to refinement of the Si particles, so that the fatigue strength and the machinability of the aluminum alloy are improved.
- the Zr content is set to 0.1 mass% or more in order to obtain these effects. If the Zr content exceeds 0.5 mass%, Zr may produce a primary crystal product, so that the caulking properties of the aluminum alloy may deteriorate.
- the Zr content is set to 0.1 to 0.5 mass%.
- the Zr content is set to 0.14 mass% or more when it is desired to further refine the Si particles.
- the Zr content is set to 0.3 mass% or less from the viewpoint of caulking properties.
- Mn has a small Si particle refinement effect. However, Mn suppresses recrystallization, and refines the crystal grains.
- Mn contributes to an improvement in fatigue strength and machinability through refinement of the crystal grains.
- the Mn content is set to 0.01 mass% or more in order to obtain these effects. If Mn precipitates at the crystal grain boundaries, potential difference corrosion and a decrease in caulking properties may occur. Therefore, the Mn content is set to 0.5 mass% or less.
- the Mn content is preferably set to 0.05 to 0.15 mass%.
- the Cr content is set to 0.01 mass% or more in order to obtain these effects. Since Cr may produce a primary crystal product, and may cause a decrease in caulking properties, the Cr content is set to 0.5 mass% or less.
- the Cr content is preferably set to 0.05 to 0.15 mass%.
- the wear-resistant aluminum alloy extruded material according to one embodiment of the invention exhibits caulking properties and machinability while maintaining wear resistance as a result of adjusting the content of Si, Mg, Fe, Cu, Mn, and Cr. Moreover, the Si particles can be refined by adjusting the Zr content, so that the fatigue strength of the aluminum alloy extruded material can be improved.
- Zn shown in FIG. 1 is regarded as impurities. No problem occurs if the Zn content is 0.05 mass% or less.
- the resulting extruded material was evaluated under the following conditions. The results are shown in FIG. 2 .
- a JIS No. 1 (1-8) specimen (rotating bending fatigue test specimen) was prepared using the extruded material in accordance with JIS Z 2274. The specimen was subjected to a fatigue test using an Ono-type rotating bending fatigue tester conforming to the JIS standard. The fatigue strength of the specimen was calculated from the resulting S-N curve.
- a JIS No. 13B tensile test specimen was prepared using the extruded material in accordance with JIS Z 2241. The specimen was subjected to a tensile test using a tensile tester conforming to the JIS standard to measure the tensile strength, the 0.2% proof stress, and the elongation at break of the specimen.
- the surface hardness of the extruded material was measured using a Rockwell B scale hardness tester.
- the caulking properties were measured using a cold upsetting test method.
- a specimen (diameter: 14 mm, height: 21 mm) was sampled from the extruded material, and subjected to cold upsetting press in the axial direction to determine the critical upsetting ratio when microcracks started to occur in the side surface of the specimen.
- the test was performed at room temperature and a compression rate of 10 mm/s using a tester "Autograph” (25 t) (manufactured by Shimadzu Corporation).
- the cutting length (20 mm or less) shown in FIG. 2 refers to the maximum chip length.
- the maximum chip length refers to the maximum length of chips produced under the following test conditions.
- Chip test conditions cutting tool: step drill (4.2 ⁇ 6.8 (diameter)), rotational speed: 1200 rpm, feed: 0.05 mm/rev, processing amount: 15 mm, number of holes formed: 3, cutting oil: used
- the wear resistance was measured using a frictional wear tester ("EFM-III-F” manufactured by Orientec Co., Ltd.).
- the pin (diameter: 5 mm, height: 8 mm) was formed of an SCr20 (carburized quenched) material.
- the specimen disk (diameter: 60 mm, height: 5 mm) was cut from the extruded material, and processed to have a surface roughness of 1.6 Z or less and a flatness of 0.01 or less.
- a brake fluid was used as a lubricant.
- the rotational speed was 160 rpm
- the testing time was 50 hours
- the applied load was 20 MPa.
- the wear rate of the wear-out part of the specimen disk was measured using a roughness measuring instrument.
- a specimen 35 (L) ⁇ 35 (W) ⁇ 35 (H) (see FIG. 6 ) was cut from the extruded material.
- a dacrotized bolt was assembled to the center threaded portion of the specimen. The basic cycle shown in FIG. 6 was repeated ten times.
- the corrosion resistance was evaluated by measuring the corrosion depth of the contact surface with the dacrotized bolt and an area around the contact surface.
- a sample was cut from the center area of the extruded material, mirror-finished, etched, and then observed using an optical microscope (magnification: 400).
- the measured value in the lengthwise direction was used as the crystal grain size or the Si particle size.
- a sample was cut from the surface area of the extruded material, mirror-finished, etched, and then observed using an optical microscope (magnification: 50) to measure the surface recrystallization depth in an average area.
- Each property target value shown in FIG. 2 indicates a value that is expected to be required to reduce the size and the weight of an automotive ABS body.
- the target average Si particle size was not achieved in Comparative Example 6 in which Mn was added in an amount of 0.50 mass%, and Comparative Examples 5 and 6 in which Cr was added in an amount of 0.30 mass%.
- Example 1 The extruded material obtained in Example 1 was compared with the extruded material obtained in Comparative Example 1.
- FIG. 3 shows the measurement results for the S-N curve
- FIG. 4 shows the measurement results for the average crystal grain size and the average Si particle size
- FIG. 5 shows the measurement results for the surface recrystallization depth.
- the extruded materials obtained in Comparative Example 7 had poor wear resistance due to low Si content and high Mg content.
- the aluminum alloy extruded material according to the invention exhibits excellent wear resistance, caulking properties, machinability, and fatigue strength
- the aluminum alloy extruded material may be used for automotive brake parts, hydraulic control parts of industrial machines, and the like.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Description
- The present invention relates to a wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength in addition to excellent machinability.
- When using an aluminum alloy extruded material for automotive brake parts and the like, the aluminum alloy extruded material is required to exhibit wear resistance against sliding parts, and may also required to exhibit high cutting (machining) accuracy and high caulking accuracy.
- For example, a cylinder, a hydraulic circuit groove, and the like are machined when producing an actuator body (ABS body) used for an automotive antilock brake system, an electronic stability control (ESC) body used for an antiskid brake system, and the like, and a caulking seal is provided after assembly.
- Therefore, an aluminum alloy extruded material used for such applications is required to exhibit strength, wear resistance against sliding parts, machinability that allows processing into a complicated shape, pressure resistance against a hydraulic oil and the like (caulking section), and high fatigue strength against cyclic (repetitive) load.
- An aluminum alloy extruded material used for such parts is provided with wear resistance and machinability by dispersing Si particles and Fe particles in the metal structure. However, such an aluminum alloy extruded material exhibits insufficient fatigue strength.
- In recent years, a further reduction in size and weight of the ABS body has been desired to reduce the weight of automobiles. However, an aluminum alloy extruded material that meets such a demand has not been proposed.
- For example,
Patent Document 1 discloses a wear-resistant aluminum alloy extruded material that exhibits excellent machinability and corrosion resistance. However, the aluminum alloy extruded material disclosed inPatent Document 1 exhibits insufficient caulking properties, fatigue strength, and the like.
Patent Document 1: Japanese Patent No.3886270 - The published US patent application
US 2005/252581 A1 discloses Al-Si alloys that have been designed for use in sliding wear applications such as automotive brake parts. - An object of the invention is to provide a wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength and excellent machinability.
- According to one embodiment of the invention, there is provided a wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength and machinability, the aluminum alloy extruded material being formed using an aluminum alloy that comprises 3.0 to 8.0 mass% of Si, 0.1 to 0.5 mass% of Mg, 0.01 to 0.5 mass% of Cu, 0.1 to 0.5 mass% of Zr, 0.4 to 0.9 mass% of Fe, 0.01 to 0.5 mass% of Mn, 0.01 to 0.5 mass% of Cr, and 0.01 to 0.1 mass% of Ti, with the balance being Al and unavoidable impurities.
- It has been known that the crystal grains of an extruded material are refined by adding small amounts of Zr, Mn, and Cr.
- The inventor of the invention conducted extensive studies, and found that the fatigue strength of the extruded material is not improved to the desired extent by merely refining the crystal grains.
- The inventor compared the effects of Zr, Mn, and Cr in detail, and found that Si particles contained in the metal structure (texture) are refined by adding a specific amount of Zr. Mn and Cr did not exhibit a significant Si particle refinement effect, but Zr exhibited a significant Si particle refinement effect.
- The fatigue strength was improved by thus suppressing fatigue propagation.
- It is preferable that the extruded material have an average Si particle size of 20 µm or less, and an average crystal grain size of 30 µm or less.
- The content range of each component of the aluminum alloy is adjusted for the following reasons.
- Si forms an Mg2Si precipitate with Mg, and provides the aluminum alloy with strength through age hardening. The Si particles contained in the metal structure also provide the aluminum alloy with wear resistance.
- Therefore, it is necessary to add Mg in order to provide the aluminum alloy with strength. Since Si forms Mg2Si with Mg, the number (amount) of Si particles that contribute to wear resistance is significantly affected by the amount of Mg.
- The Mg content is set to 0.1 mass% or more taking account of these effects. The Mg content is preferably set to 0.3 mass% or more when it is desired to provide the aluminum alloy with higher strength.
- If the Mg content is too high, a decrease in caulking properties and extrudability may occur. Therefore, the Mg content is set to 0.5 mass% or less, and preferably 0.45 mass% or less.
- When the Mg content is set within the above range, the Si content is set to 3.0 mass% or more. The Si content is preferably set to 4.1 to 6.1 mass% when it is desired to provide the aluminum alloy with stable wear resistance.
- When a large number of hard and fine Si particles are present in the metal structure, chips are dispersed from the Si particles. Therefore, the Si content is set to 8.0 mass% or less.
- Since fatigue cracking occurs from the Si particles, it is necessary to refine the Si particles (described later).
- Cu improves the strength of the aluminum alloy while ensuring caulking properties. Since Cu is solid-dissolved to a certain extent, the strength and the machinability of the aluminum alloy are improved due to solid-solution hardening.
- The Cu content is set to 0.01 mass% or more taking account of these effects. If the Cu content is too high, potential difference corrosion tends to occur. Therefore, the Cu content is set to 0.50 mass% or less. The Cu content is preferably set to 0.10 to 0.20 mass%.
- The upper limit of the Cu content is more preferably set to 0.14 mass% or less.
- Fe particles are dispersed at the crystal grain boundaries, and chips break from the Fe particles. As a result, the machinability of the aluminum alloy is improved.
- The Fe content is preferably set to 0.40 mass% or more taking account of these effects. If the Fe content exceeds 0.9 mass%, a large number of Fe particles may precipitate at the crystal grain boundaries. In this case, the caulking properties of the aluminum alloy may deteriorate due to a decrease in toughness.
- Therefore, the Fe content is set to 0.4 to 0.9 mass%, and preferably 0.5 to 0.8 mass%.
- Zr suppresses recrystallization, and refines the crystal grains. Moreover, fatigue propagation is suppressed due to refinement of the Si particles, so that the fatigue strength and the machinability of the aluminum alloy are improved.
- The Zr content is set to 0.1 mass% or more in order to obtain these effects. If the Zr content exceeds 0.5 mass%, Zr may produce a primary crystal product, so that the caulking properties of the aluminum alloy may deteriorate.
- Therefore, the Zr content is set to 0.1 to 0.5 mass%. The Zr content is set to 0.14 mass% or more when it is desired to further refine the Si particles. The Zr content is set to 0.3 mass% or less from the viewpoint of caulking properties.
- Mn has a small Si particle refinement effect. However, Mn suppresses recrystallization, and refines the crystal grains.
- Specifically, Mn contributes to an improvement in fatigue strength and machinability through refinement of the crystal grains.
- The Mn content is set to 0.01 mass% or more in order to obtain these effects. If Mn precipitates at the crystal grain boundaries, potential difference corrosion and a decrease in caulking properties may occur. Therefore, the Mn content is set to 0.5 mass% or less.
- The Mn content is preferably set to 0.05 to 0.15 mass%.
- Cr has a small Si particle refinement effect. However, Cr suppresses recrystallization, and refines the crystal grains.
- The Cr content is set to 0.01 mass% or more in order to obtain these effects. Since Cr may produce a primary crystal product, and may cause a decrease in caulking properties, the Cr content is set to 0.5 mass% or less.
- The Cr content is preferably set to 0.05 to 0.15 mass%.
- Ti refines the crystal grains. The machinability of the aluminum alloy is improved when the Ti content is small. If the Ti content exceeds 0.1 mass%, the life of a cutting tool may decrease.
- Therefore, the Ti content is set to 0.01 to 0.1 mass%.
- The wear-resistant aluminum alloy extruded material according to one embodiment of the invention exhibits caulking properties and machinability while maintaining wear resistance as a result of adjusting the content of Si, Mg, Fe, Cu, Mn, and Cr. Moreover, the Si particles can be refined by adjusting the Zr content, so that the fatigue strength of the aluminum alloy extruded material can be improved.
-
-
FIG. 1 shows the alloy composition of each extruded material that was evaluated. -
FIG. 2 shows the evaluation results. -
FIG. 3 shows a comparison between the S-N curve of the extruded product obtained in Example 1 and the S-N curve of the extruded material obtained in Comparative Example 1. -
FIG. 4 shows examples of a micrograph used to measure the crystal grain size and the Si particle size. -
FIG. 5 shows examples of a micrograph used to measure the surface recrystallization depth. -
FIG. 6 shows corrosion resistance evaluation conditions. - An 8-inch billet was cast at a casting speed of 70 to 100 mm/min (see
FIG. 1 ) using a molten metal containing the chemical components shown inFIG. 1 (balance: aluminum and unavoidable impurities), and homogenized at 460 to 590°C for 6 hours or more. - Note that Zn shown in
FIG. 1 is regarded as impurities. No problem occurs if the Zn content is 0.05 mass% or less. - The billet was preheated to 450 to 510°C, and extruded into a rectangular extruded material having dimensions of about 40×100 mm at an extrusion speed of 5 to 10 m/min.
- A T6 heat treatment was performed by quenching the extruded material at the end of the die through water-cooling immediately after extrusion, and subjecting the extruded material to artificial aging at 160 to 195°C for 2 to 8 hours.
- The resulting extruded material was evaluated under the following conditions. The results are shown in
FIG. 2 . - A JIS No. 1 (1-8) specimen (rotating bending fatigue test specimen) was prepared using the extruded material in accordance with JIS Z 2274. The specimen was subjected to a fatigue test using an Ono-type rotating bending fatigue tester conforming to the JIS standard. The fatigue strength of the specimen was calculated from the resulting S-N curve.
- A JIS No. 13B tensile test specimen was prepared using the extruded material in accordance with JIS Z 2241. The specimen was subjected to a tensile test using a tensile tester conforming to the JIS standard to measure the tensile strength, the 0.2% proof stress, and the elongation at break of the specimen.
- The surface hardness of the extruded material was measured using a Rockwell B scale hardness tester.
- The caulking properties were measured using a cold upsetting test method.
- A specimen (diameter: 14 mm, height: 21 mm) was sampled from the extruded material, and subjected to cold upsetting press in the axial direction to determine the critical upsetting ratio when microcracks started to occur in the side surface of the specimen.
-
- The test was performed at room temperature and a compression rate of 10 mm/s using a tester "Autograph" (25 t) (manufactured by Shimadzu Corporation).
- The cutting length (20 mm or less) shown in
FIG. 2 refers to the maximum chip length. The maximum chip length refers to the maximum length of chips produced under the following test conditions. - Chip test conditions: cutting tool: step drill (4.2×6.8 (diameter)), rotational speed: 1200 rpm, feed: 0.05 mm/rev, processing amount: 15 mm, number of holes formed: 3, cutting oil: used
- The wear resistance was measured using a frictional wear tester ("EFM-III-F" manufactured by Orientec Co., Ltd.).
- Specifically, two cylindrical samples (pin and specimen disk) were rotated around the centerline, and a constant load was applied to the pin so that the pin was pressed against the disk (frictional wear occurred).
- The pin (diameter: 5 mm, height: 8 mm) was formed of an SCr20 (carburized quenched) material.
- The specimen disk (diameter: 60 mm, height: 5 mm) was cut from the extruded material, and processed to have a surface roughness of 1.6 Z or less and a flatness of 0.01 or less.
- A brake fluid was used as a lubricant. The rotational speed was 160 rpm, the testing time was 50 hours, and the applied load was 20 MPa.
- The wear rate of the wear-out part of the specimen disk was measured using a roughness measuring instrument.
- A specimen (35 (L) × 35 (W) × 35 (H)) (see
FIG. 6 ) was cut from the extruded material. A dacrotized bolt was assembled to the center threaded portion of the specimen. The basic cycle shown inFIG. 6 was repeated ten times. - The corrosion resistance was evaluated by measuring the corrosion depth of the contact surface with the dacrotized bolt and an area around the contact surface.
- A sample was cut from the center area of the extruded material, mirror-finished, etched, and then observed using an optical microscope (magnification: 400). The crystal grain size and the Si particle size were measured at twenty (n=20) average areas displayed on a monitor, and the average crystal grain size and the average Si particle size were calculated.
- When the crystal grains or the Si particles have an elliptical or elongate shape, the measured value in the lengthwise direction was used as the crystal grain size or the Si particle size.
- A sample was cut from the surface area of the extruded material, mirror-finished, etched, and then observed using an optical microscope (magnification: 50) to measure the surface recrystallization depth in an average area.
- Each property target value shown in
FIG. 2 indicates a value that is expected to be required to reduce the size and the weight of an automotive ABS body. - The extruded materials obtained in the examples according to the invention had a high fatigue strength (i.e., 130 MPa or more) as compared with the extruded materials obtained in the comparative examples.
- In Comparative Examples 1 to 7 in which Mn and Cr were added, the average crystal grain size was not reduced to 30 µm or less, and the average Si particle size was not reduced to 20 µm or less. In Examples 1 to 3 in which Zr was added in addition to Mn and Cr, the average crystal grain size was reduced to 30 µm or less, and the average Si particle size was reduced to 20 µm or less. It is considered that fatigue propagation was thus suppressed, so that the fatigue strength was improved.
- For example, the target average Si particle size was not achieved in Comparative Example 6 in which Mn was added in an amount of 0.50 mass%, and Comparative Examples 5 and 6 in which Cr was added in an amount of 0.30 mass%.
- The extruded material obtained in Example 1 was compared with the extruded material obtained in Comparative Example 1.
FIG. 3 shows the measurement results for the S-N curve,FIG. 4 shows the measurement results for the average crystal grain size and the average Si particle size, andFIG. 5 shows the measurement results for the surface recrystallization depth. - As is clear from the evaluation results shown in
FIG. 2 , it was confirmed that the extruded products obtained in the examples according to the invention had improved machinability. - Note that the extruded materials obtained in Comparative Examples 1, 2, 5, 6, and 7 had poor machinability since the Fe content was less than 0.4 mass%.
- The extruded materials obtained in Comparative Example 7 had poor wear resistance due to low Si content and high Mg content.
- The target fatigue strength was not achieved in Comparative Examples 3 and 4 although the composition was similar to those of the examples except that Zr was not added.
- Since the aluminum alloy extruded material according to the invention exhibits excellent wear resistance, caulking properties, machinability, and fatigue strength, the aluminum alloy extruded material may be used for automotive brake parts, hydraulic control parts of industrial machines, and the like.
Claims (3)
- A wear-resistant aluminum alloy extruded material that exhibits excellent fatigue strength and machinability, the aluminum alloy extruded material being formed using an aluminum alloy that comprises 3.0 to 8.0 mass% of Si, 0.1 to 0.5 mass% of Mg, 0.01 to 0.5 mass% of Cu, 0.1 to 0.5 mass% of Zr, 0.4 to 0.9 mass% of Fe, 0.01 to 0.5 mass% of Mn, 0.01 to 0.5 mass% of Cr, and 0.01 to 0.1 mass% of Ti, with the balance being Al and unavoidable impurities.
- The aluminum alloy extruded material according to claim 1, a metal structure of the extruded material having an average Si particle size of 20 µm or less.
- The aluminum alloy extruded material according to claim 1 or 2, the extruded material having an average crystal grain size of 30 µm or less.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2009154439 | 2009-06-29 | ||
PCT/JP2010/060644 WO2011001870A1 (en) | 2009-06-29 | 2010-06-23 | Wear-resistant aluminum alloy extruded material having excellent fatigue strength and cutting properties |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2450462A1 EP2450462A1 (en) | 2012-05-09 |
EP2450462A4 EP2450462A4 (en) | 2016-07-27 |
EP2450462B1 true EP2450462B1 (en) | 2017-03-22 |
Family
ID=43410945
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP10794039.7A Active EP2450462B1 (en) | 2009-06-29 | 2010-06-23 | Wear-resistant aluminum alloy extruded material having excellent fatigue strength and cutting properties |
Country Status (5)
Country | Link |
---|---|
US (1) | US20120045359A1 (en) |
EP (1) | EP2450462B1 (en) |
JP (1) | JP4755725B2 (en) |
CN (1) | CN102459672A (en) |
WO (1) | WO2011001870A1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN110622243A (en) * | 2017-05-12 | 2019-12-27 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, method for producing same, and magnetic disk using same |
Families Citing this family (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103849797A (en) * | 2014-01-16 | 2014-06-11 | 滁州东润电子科技有限公司 | Casting aluminum alloy material for light-emitting diode (LED) lamp radiator and preparation technology thereof |
KR102156008B1 (en) * | 2014-07-31 | 2020-09-15 | 가부시키가이샤 고베 세이코쇼 | Aluminum alloy extruded material having excellent machinability and method for manufacturing same |
WO2018017894A1 (en) | 2016-07-21 | 2018-01-25 | Johnson & Johnson Visioncare, Inc. | Biomedical device including encapsulation |
CN107022703A (en) * | 2017-04-27 | 2017-08-08 | 马鞍山常裕机械设备有限公司 | A kind of automotive hub high-strength aluminum alloy material and its production technology |
CN107245614B (en) * | 2017-07-27 | 2019-01-22 | 广州致远新材料科技有限公司 | A kind of wear-resistant aluminum alloy and application thereof |
CN109050870B (en) * | 2018-11-13 | 2019-02-22 | 烟台工程职业技术学院 | A kind of fast assembling-disassembling part and its processing method |
CN115700288A (en) * | 2022-10-26 | 2023-02-07 | 江苏艾速特低碳科技有限公司 | Automobile exhaust valve aluminum-based alloy material and preparation method and application thereof |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06240399A (en) * | 1993-02-16 | 1994-08-30 | Honda Motor Co Ltd | Heat resistant aluminum alloy excellent in notch fatigue strength |
JP3107517B2 (en) | 1995-03-30 | 2000-11-13 | 株式会社神戸製鋼所 | High corrosion resistant aluminum alloy extruded material with excellent machinability |
JP3654695B2 (en) * | 1995-12-25 | 2005-06-02 | アイシン軽金属株式会社 | Wear resistant aluminum alloy |
DE69822152T2 (en) * | 1997-10-31 | 2004-09-09 | Honda Giken Kogyo K.K. | EXTRUDED MATERIAL FROM AN ALUMINUM ALLOY FOR STRUCTURAL PARTS OF A AUTOMOTIVE AND METHOD FOR THE PRODUCTION THEREOF |
JP3398085B2 (en) * | 1999-04-28 | 2003-04-21 | 古河電気工業株式会社 | Aluminum alloy materials for welded structures and their welded joints |
US20030143102A1 (en) * | 2001-07-25 | 2003-07-31 | Showa Denko K.K. | Aluminum alloy excellent in cutting ability, aluminum alloy materials and manufacturing method thereof |
EP1413636B9 (en) * | 2001-07-25 | 2009-10-21 | Showa Denko K.K. | Aluminum alloy excellent in machinability and aluminum alloy material and method for production thereof |
JP3846702B2 (en) * | 2001-11-09 | 2006-11-15 | 株式会社神戸製鋼所 | Al-Mg-Si aluminum alloy extruded material for cutting |
ATE419404T1 (en) * | 2002-02-28 | 2009-01-15 | Aisin Keikinzoku Co Ltd | ABRASION-RESISTANT ALUMINUM ALLOY WITH EXCELLENT STACKING BEHAVIOR AND EXTRUDED PRODUCT MADE THEREOF |
JP2004277762A (en) * | 2003-03-13 | 2004-10-07 | Nippon Light Metal Co Ltd | Method for manufacturing heat treatment type aluminum alloy material for cold working |
JP4189974B2 (en) * | 2003-09-01 | 2008-12-03 | アイシン軽金属株式会社 | Aluminum alloy extruded material with excellent machinability, caulking properties, and wear resistance |
US20050109429A1 (en) * | 2003-11-21 | 2005-05-26 | Showa Denko K.K. | Aluminum alloy, bar-like material, forge-formed article, machine-formed article, wear-resistant aluminum alloy with excellent anodized coat using the same and production methods thereof |
-
2010
- 2010-06-23 EP EP10794039.7A patent/EP2450462B1/en active Active
- 2010-06-23 WO PCT/JP2010/060644 patent/WO2011001870A1/en active Application Filing
- 2010-06-23 JP JP2010542442A patent/JP4755725B2/en active Active
- 2010-06-23 CN CN2010800284747A patent/CN102459672A/en active Pending
-
2011
- 2011-11-02 US US13/287,353 patent/US20120045359A1/en not_active Abandoned
Non-Patent Citations (1)
Title |
---|
None * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN110622243A (en) * | 2017-05-12 | 2019-12-27 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, method for producing same, and magnetic disk using same |
CN110622243B (en) * | 2017-05-12 | 2021-08-10 | 株式会社Uacj | Aluminum alloy substrate for magnetic disk, method for producing same, and magnetic disk using same |
Also Published As
Publication number | Publication date |
---|---|
EP2450462A4 (en) | 2016-07-27 |
WO2011001870A1 (en) | 2011-01-06 |
US20120045359A1 (en) | 2012-02-23 |
CN102459672A (en) | 2012-05-16 |
JP4755725B2 (en) | 2011-08-24 |
JPWO2011001870A1 (en) | 2012-12-13 |
EP2450462A1 (en) | 2012-05-09 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2450462B1 (en) | Wear-resistant aluminum alloy extruded material having excellent fatigue strength and cutting properties | |
US7648594B2 (en) | Extruded aluminum alloy which excels in machinability, caulking properties, and wear resistance | |
EP2518171B1 (en) | Aluminum alloy for anodization and aluminum alloy component | |
Chegini et al. | Effect of equal channel angular pressing on the mechanical and tribological behavior of Al-Zn-Mg-Cu alloy | |
EP2811043B1 (en) | High-strength aluminum alloy extrudate with excellent corrosion resistance, ductility, and hardenability and process for producing same | |
Sharath et al. | Effect of multi directional forging on the microstructure and mechanical properties of Zn-24 wt% Al-2 wt% Cu alloy | |
JP6796356B1 (en) | Free-cutting copper alloy and method for manufacturing free-cutting copper alloy | |
Elhefnawey et al. | On dry sliding wear of ECAPed Al-Mg-Zn alloy: Wear rate and coefficient of friction relationship | |
Xu et al. | Dry sliding wear behavior of AZ91 alloy processed by rotary-die equal channel angular pressing | |
Palacios-Robledo et al. | Tribological analysis in Al–Mg–Zn alloy casting processed through equal channel angular pressing, compared with Al-7075 T6 alloy | |
JP6937663B2 (en) | Abrasion resistant aluminum alloy extruded material with excellent caulking and fatigue strength and aluminum alloy used for it | |
Latif | Effect of loading rates and single edge notch bending (SENB) specimen thicknesses on shear lips formation for Al6061 alloy | |
EP1479785B1 (en) | Wear-resistant aluminum alloy excellent in caulking property and extruded product made thereof | |
WO2020261666A1 (en) | Free-cutting copper alloy and method for producing free-cutting copper alloy | |
Aksoy et al. | Effect of Mg addition on microstructure and mechanical properties of AlSi12 alloy produced by high-pressure casting method | |
CN102952974A (en) | Aluminum alloy with excellent abrasion resistance, caulking performance and fatigue strength | |
Hurtalová et al. | Optical and electron microscopy study of the mechanical properties improvement on recycled AlSi9Cu3 cast alloy along the hardening | |
Pai et al. | A Finite Element Approach to Conduct Machinability Studies on Age-Hardened AA6061 Matrix Hybrid Composites. | |
JP2005256015A (en) | Abrasion-resistant aluminum alloy extruded material superior in machinability | |
Babu et al. | Optimization of Process Parameters of Cyclic Expansion Extrusion Process for Effective Grain Refinement of Al-Mg-Si Alloy | |
EP3128020A1 (en) | Low-lead brass alloy for plumbing member | |
Hassani et al. | The effects of friction stir processing on the wear behavior of cast AZ91C magnesium alloy | |
Rac et al. | Tribological properties of thixoforming al-alloy a356 and influence of heat treatment | |
WO2019007906A1 (en) | Titanium-containing zinc wrought alloy | |
Džugan et al. | Study of the Microstructure, Tensile Properties and Hardness of AZ61 Magnesium Alloy Subjected to Severe Plastic Deformation |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20111025 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR |
|
DAX | Request for extension of the european patent (deleted) | ||
RA4 | Supplementary search report drawn up and despatched (corrected) |
Effective date: 20160628 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22C 21/02 20060101AFI20160622BHEP |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
INTG | Intention to grant announced |
Effective date: 20161117 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 877850 Country of ref document: AT Kind code of ref document: T Effective date: 20170415 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602010040990 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170623 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170622 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 877850 Country of ref document: AT Kind code of ref document: T Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170622 Ref country code: SE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: AT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: IT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: ES Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170722 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170724 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: PL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602010040990 Country of ref document: DE |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
26N | No opposition filed |
Effective date: 20180102 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 602010040990 Country of ref document: DE Representative=s name: WUNDERLICH & HEIM PATENTANWAELTE PARTNERSCHAFT, DE |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST Effective date: 20180228 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170630 Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170623 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170623 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170630 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170630 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20170630 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170630 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170623 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20100623 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CY Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170322 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20230622 Year of fee payment: 14 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20240628 Year of fee payment: 15 |