• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    To produce a cutting tool and the like, with an aluminum oxide coating layer, an a type aluminum oxide with a crystal structure covers at least part of a base material (2) surface by vacuum deposition in a chamber (1). The coated surface is bombarded with ions, using a noble gas in a plasma from a glow wire (9).
    公开号:SE536047C2
    申请号:SE0600585
    申请日:2006-03-16
    公开日:2013-04-16
    发明作者:Toshimitsu Kohara
    申请人:Kobe Steel Ltd；
    IPC主号:
    专利说明:

    25 536 04 2 In Japanese Laid-Open Application no. 2002-53946 describes the formation of a corundum-structured oxide film having a lattice parameter of 4,779 Å or more and 5,000 Å or less and a film thickness of 0.005 μm or more as a sublayer and forming an ot-alumina film on this sublayer by using PVD procedure. Further described in European patent application no. A process for the formation of oL alumina on a TiAlN® with excellent heat resistance and abrasion resistance, which has recently been used for a hard film for tools, by using the PVD method. Also in accordance with this document, the ot alumina is formed after oxidation of the surface of the hard Ti-AlN film.
    However, even in a cutting tool with the ot-alumina film thus formed, the tool life has often been shortened by using it under strict conditions or for machining work material with high frictional resistance. Furthermore, the formation of the ot-alumina layer on a surface of a slider or a metal mold sometimes also causes an increase in the frictional resistance on a contact surface, which could adversely affect the performance of the slider or metal mold. On the other hand, U.S. Pat. 5766782 and 5487625 methods for smoothing a surface of an ot alumina layer to minimize the frictional resistance of the surface of the ot alumina layer. In the procedures described in these documents, the surface is smoothed by a wet blasting treatment using AlzO powder. However, since smoothing by such a method requires a long time and extensive work, a method is required for further effectively smoothing the surface of the alumina layer. SUMMARY OF THE INVENTION In view of such circumstances, it is an object of the present invention to provide a method whereby one can extend the life of a tool and reduce the frictional resistance of a slider, a metal mold and the like, to and from the present invention. with in such cases when an α-alumina layer is formed on such an element, and to perform this process efficiently.
    A process for producing an α-alumina layered element according to the present invention, in which the above-described problems can be overcome, comprises: (1) a process for forming an ot-alumina layer having an ot-type crystal structure on at least one partial surface on a base material; and (2) a method of performing an ion bombardment treatment of the surface of the alumina layer formed. According to the present invention, the service life of the tool can be extended and the frictional resistance of the slider, the metal mold or the like can be reduced.
    The ion bombardment treatment is performed using a plasma noble gas.
    Furthermore, the alumina layer is preferably formed by means of physical gas precipitation. At this time, processes (1) and (2) described above are preferably performed within the same apparatus.
    A method of preforming a hard film as a sublayer to the oz-type crystal oxide alumina layer to be formed in the process (1) is suitably added as a pre-process to the process (1). In this case, the hard film is suitably TiAlN.
    "Alumina with α-type crystal structure" (also referred to as "ot-alumina" in the description) means an alumina composed mainly of α-crystal structure (hexagonal structure) and that the or-type crystal structure in the alumina layer is 70% or more, preferably 90% or more and then in particular 100%, since excellent heat resistance can then be achieved.
    According to the method of forming an α-alumina layered member of the present invention, the smoothness of the surface of the u-alumina layer can be effectively improved to extend the life of the tool. In the case of a sliding member, a metal mold or the like, the frictional resistance can be lowered.
    BEST MODE FOR CARRYING OUT THE INVENTION To solve the above problems, the surface property and machinability of alumina formed under severe conditions were studied and evaluated.
    As a result, it could be found that even an ot-alumina fi film with excellent heat resistance or oxidation resistance causes deterioration of machinability by adhering to work material or the like under certain machining conditions, whereby machinability can be improved by smoothing aluminium alumina aluminium alumina y surface can be effectively smoothed by the ion bombardment treatment, which led to the present invention.
    More specifically, the alumina film is characterized in that the grains grow largely in columnar form from the area of a base material or a sublayer to the surface layer of the alumina during the filling process and that a number of raised rock irregularities are formed on film irregularities. to increase the roughness of the film. Electron microscopic images of α-alumina fi lm formed on a TiAlN fi lm are shown in Figs. 1 and 2. Fig. 1 is a TEM image (transmission electron microscopic image) of a part thereof and Fig. 2 shows a SEM image (scanning electron microscopic) of a surface thereon.
    In the case of an alumina fi hn with a ct-type crystal structure, it appears from the TEM image in Fig. 1 that the grains largely grow in columnar form from the area of the bed (a base material or a film formed on the base material: a TiAlN fi lm in the example shown in this figure) to the surface layer of the alumina in the coating process, with a grain size of fl era hundred nm to fl era um near the mylmy layer. Therefore, as shown in Fig. 2, a number of raised rock-shaped irregularities are visible on the surface. The surface roughness of the α-alumina film tends to increase (become coarse) while the grains of alumina with amorphous structure or γ-crystal structure are small. Furthermore, the surface roughness of the ot-alumina film also tends to increase (become coarse) compared to a TiN-mlm or TiAlN film, which is not used as a heat-resistant and surface-resistant film similar to the ot-alumina film. This high surface roughness could easily cause adhesion of working material to tools in the cutting tool with the ot-alumina film formed thereon, shortening the tool life, and increasing the frictional resistance of the slider or metal mold with the alumina film formed thereon.
    In the present invention, therefore, the surface of the ot-alumina film (alumina layer with ot-type crystal structure) is subjected to the ion bombardment treatment.
    This scrapes protruding parts (sharply protruding parts of oi-grain) on the surface of the alumina through the collision with ions and the surface can be smoothed efficiently. Fig. 3 is an SEM image of an α-alumina m lm e fi er that it has been subjected to the ion bombardment treatment. As shown in Fig. 3, the sharply pointed parts of large basins of α-alumina are rounded and the shape of the basin is also broken and flattened. By smoothing the surface in this way, in the case of a tool, the adhesion between working material and tool can be prevented so that the service life of the tool is improved. Furthermore, one can also overcome problems with reduction of machining accuracy, limitation of machinable work material and the like, which effects derive from the extension. The frictional resistance can be reduced in the case of a slider or a metal mold.
    Gations for the ion bombardment treatment can be obtained by generating gas plasma, for example by discharging in a vacuum chamber into which gas is introduced (A. thermoionic emission from a wire by heating a thermionic emitting wire by current through the wire and further applying a track ring between the wire and the chamber; B. glow discharge or arc discharge by applying a voltage between the electrodes; or the like).
    As gas, noble gases are recommended (eg He, Ne, Ar, Kr, Xe, etc). Noble gases are excellent in that there is no possibility that they corrode the base material, film, device or the like, or react with the base material to form new compounds. A preferred noble gas is Ar. Ar is cheap and enables effective ion bombardment treatment.
    The ion generating conditions (process) are not limited to the processes described above as long as a sufficient amount of ion can be obtained to scrape the alumina layer and the ion can be set correctly depending on the gas pressure in the chamber or conditions for collision between the ion and the base material. A specific example is as follows. When a noble gas, such as Ar-ion, is generated using thermoionic emission, it is recommended to set the current to flow between the thermoionic emitting wire and the chamber at 1 A or more, preferably at 5 A or more and especially at 7 A or more. The noble gas plasma can be generated with higher density when the current is higher. However, an excessive current leads to an excessively increased plasma density, which tends to cause arcing on the base material and facilitate local etching of protruding parts on the base material. Consequently, the cutting edge is more easily mentioned in the toolbar. Furthermore, the temperature of the base material can easily increase, which facilitates thermal deformation of the base material 10 15 20 25 30 536 04 7 years. Thus, it is recommended that the current be set to 50 A or lower, suitably to 30 A or lower and then especially to 20 A or lower. At the same time, it is recommended that the noble gas pressure be set at approx. 10 Pa or lower, suitably at approx. 7 Pa or lower and then especially at approx. 5 Pa or lower. However, if the amount of noble gas introduced into the chamber is reduced too much so that the pressure decreases excessively, it becomes difficult to generate the plasma (or an increase in the amount of current passing through the wire is required because it is difficult to achieve high density plasma), at an increased cost. It is therefore recommended that the pressure of the noble gas to be introduced into the chamber be set at 0.1 Pa or more, preferably at 0.5 Pa or more and then especially at 1 Pa or more.
    It is suitable that the generated ion collides with the α-alumina layer (base material). The ion can be effectively drawn into the base material (the surface of the alumina), for example by applying a pre-bias (negative bias, pulsating bias with reversed polarities, or the like), and the bombardment effect can be improved.
    The bias voltage is suitably set to a negative value and has an absolute value from 100V to 500V, for example 100 V or more, preferably 200 V or more and then in particular 250 V or more, expressed as absolute value. The higher the bias, the more the bombardment effect can be improved. However, if the bias is excessively high, an excessively increased energy of the ion entering the base material (surface of the alumina layer) causes slight arcing or local etching as described above, which can then cause problems such as rounding of the edge of the cutting tool or an excessively increased temperature of the base material.
    When a pulsating bias voltage is applied to the base material, the frequency is set at 10 kHz to 500 kHz, preferably at 15 kHz or higher and then in particular at 20 kHz or higher. An excessively low frequency tends to cause arcing. However, since the cost of the energy supply generally increases as the frequency increases, the frequency is set to, for example, about 300 kHz or lower. 10 15 20 25 536 047 8 The duration of the ion bombardment treatment can be set correctly according to the above conditions (the gas pressure in the chamber, the ion generating conditions, the ion collision conditions and the like). It is set o fi a for 5 minutes or longer and for 1 hour or less.
    The element to be subjected to the ion bombardment treatment may comprise an ot alumina layer formed on at least one partial surface of a base material and a known method, such as physical gas deposition (PVD method) or the chemical gas deposition method (CVD method), may be applied to the formation thereof. In particular, the thermal deformation of the base material can be easily prevented by using the PVD method (especially reactive understanding, eg reactive understanding using a magnetron understanding cathode, such as an understanding cathode in unbalanced magnetron (UBM). of the ot alumina layer and the ion bombardment treatment are carried out in the same device and the production process for elements provided with ot alumina layer can be simplified.In particular, the device used in the ion bombardment treatment has a specification relatively similar to that of the device used in PVD method Therefore, since the formation of the α-alumina layer is performed by the PVD method, the ion bombardment treatment can be performed in the same device as for the formation of the α-alumina layer, without the need for any major change in the specification.
    The alumina layer can be formed directly on the base material, but is suitably laminated on another layer (a sublayer: especially a hard elm) formed on the base material. If the hard film is formed between the ot-alumina layer and the base material, the abrasion resistance of the formed ot-alumina-formed element can be improved. Examples of the hard film comprise a composite layer composed of one or two elements selected from the elements of groups IVa, Va and VIa, Al, Si, Fe, Cu, Y and the like and one or two elements selected. among C, N, B, O and the like, and a laminate thereof. Preferred examples of the composite layer include a Cr-based hard fi1 m (CrN, etc.), a Ti-based hard fi lm (TiN, TiCN, TiAlN, TiSiN, etc.) and a TiCr-based hard fi lm (TiAlCrN, etc). Among these, the Ti-based hard film is preferred, especially TiAlN. The hard film can be formed by using a known method, such as the PVD method or the CVD method.
    The PVD drying method (especially reactive understanding, arc ion plating, etc.) is preferably used for the formation with regard to such as that the thermal deformation of the base material can be easily prevented and that the same device can be used.
    The base material can be selected correctly depending on the use of the element provided with an alumina layer. More specifically, cemented carbide, cermet, quick tool steel and the like can be suitably adapted in the manufacture of a cutting tool.
    The surface of the base material and the surface of the underlayer can be subjected to a chemical treatment (eg oxidative treatment, nitriding or settling) before lamination on the alumina layer to form a reactive layer. Furthermore, a coarseness-altering treatment (a smoothing, such as polishing, or a surface coarsening treatment, such as cracking or ion bombardment) can be carried out simultaneously with or separately from the chemical treatment. It is also possible to refrain from this chemical treatment and coarseness-changing treatment.
    A layer composed of a material having the same crystal structure as ot-alumina is suitably formed on the surface which is subjected to lamination against the ot-alumina layer (more precisely between the ot-alumina layer and the surface of the base material or between the ot-alumina layer and the sublayer surface in 536 047 In the case where the backsheet is formed) prior to lamination to the alumina layer. By this, the adhesion of the surface which is subjected to lamination (the base material, the lower layer, etc.) to the α-alumina layer can be improved. In addition to otAl1O3, oxides such as aCrzOg and otFezOg are preferred because they have the same corundum structure as otAl2O3. These otCr203 and OLAIZO; can be formed, for example, on a surface of CrN or TiAIN by oxidation of the surface.
    In the present invention, another film (for example, the above-mentioned hard film) can also be laminated as an upper layer of the alumina film. Since the surface of the ot alumina layer is smoothed in the present invention, the surface of the hard surface, even if it is laminated on the ot alumina layer, can be smoothed and the effect of the present invention can be maintained.
    According to the present invention, the ot-alumina layer does not necessarily form the upper layer and the lower layer over the entire surface of the base material, but at least a part is formed which needs to improve the abrasion resistance or decrease the frictional resistance. The thickness of the ot alumina layer, the upper layer and the lower layer can be properly selected depending on the intended use of the ot alumina element. In particular, if the thickness of the alumina layer is excessively small, a sufficient effect can not be achieved and consequently it is recommended that the thickness be set at 0.1 μm or more, preferably at 0.5 μm or more and then in particular at 1 μm or more. . The shape of the element provided with oL-alumina is not particularly limited and can be appropriately selected depending on the intended use.
    The α-alumina element obtained by the manufacturing process of the present invention can be suitably used as a cutting tool, such as a tip, a drill or an end mill, for which elements heat resistance and abrasion resistance are required. and an element such as a sliding part or a metal lining used in cars, for which elements low frictional resistance is required.
    BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a TEM image of AIZO; formed on a TiAlN-fi ch, where the grain is largely grown in column form; Fig. 2 is an SEM image of the surface condition of an α-alumina element obtained in a comparative example; Fig. 3 is an SEM image of the surface condition of an α-alumina element obtained in an example; and Fig. 4 is a schematic view of a vacuum precipitation system which is an example of an apparatus for carrying out a surface treatment method according to the present invention; Fig. 5 is an SEM image of the surface condition of an o1-alumina element obtained in another example.
    DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention is described in more detail with reference to preferred embodiments. The present invention is not to be limited by the following preferred embodiments and may be practiced with appropriate modification within the scope of the invention described above and hereinafter, and such modifications may be included within the technical scope of the present invention.
    In the following embodiments, a vacuum deposition system used in Fig. 4 is used. Physical Gas Precipitation (PVD) means [in this example shown an arc ion plating stripping source (AIP) for forming the hard film and a sputtering stripping source for forming the ot alumina] and ion generating means and ion collision means for performing the ion bombardment treatment. More specifically, this system comprises an arc ion plating cathode (AIP cathode) 7 such as the AIP stripping source, an attenuation cathode (magnetron sputtering cathode (UBM cathode)] 6 as the resonant stripping source, a thermionic ion emitting device 9 and the ionic emission device 9 such as the ionic emission source. 1 denotes a chamber, 2 a base material, 3 and 4 a rotation mechanism for the base material (a rotating table 3 and a planetary rotating jig 4) in pairs, and 5 are heating means (winding device).
    The chamber 1 in this system is adapted to be able to form and maintain a state of vacuum and comprises the winding device 5, which can regulate the internal temperature in the chamber 1, and the rotating table 3, which can have a number of planetary jigs 4 thereon. By controlling this system, the rotating table 3, on which a number of the planet jigs 4 are mounted, can be rotated (rotated) simultaneously with rotation of the planet jigs 4 themselves (rotation around their own axes). Furthermore, a rotation member 10 with a tool rotation jig is read on the plane rotation jig 4.
    In Example 1 and Comparative Example 1, a loose tip of cemented carbide base material (reference code: SNMN 120408) ground to a mirror surface (Ra = approx. and surface properties, and a loose tip of cemented carbide base material (reference code: SNGA 120408) for cutting testing.
    [Hard Bildlm Formation] Using the system of Fig. 4, a 2-3 μm thick TiAlN- film was formed on each of these base materials by the PVD drying process (arc ion plating in this example). More specifically, SNMN 120408 was attached to the planetary rotating jig 4 (2 in the drawing) and attached SNGA 120408 to the rotating member 10 (1 L in the drawing), nitrogen being introduced into the vacuum chamber at about 4 Pa. , a voltage was applied between the cathode 7 mounted on a TiAl alloy target and the chamber 1 inside the chamber 1 to generate metal ion vapor by arc discharge and a bias voltage was applied through the bias energy source 8 to form an elm of TiO_55AlO_45N (atomic ratio).
    [Treatment for cleaning the surface of the hard film] The chamber 1 was evacuated once to vacuum and the temperature of the base material 2 was increased to 550 ° C by means of the heating device 5. Ar-gas was introduced into the chamber 1 at a pressure of 1.33 Pa and a 4 A discharge was generated between the thermoionic emitting wire 9 and the Ar plasma formation chamber. While maintaining the generation of Ar plasma, a pulsating direct current was applied at a frequency of 30 kHz for a total of 18 minutes, or for 2 minutes at -300 V, -350 V, -400 V and -450 V and for 10 minutes at -500 V, whereby the ion bombardment treatment was performed.
    [Oxidation treatment] The base material 2 was heated to 70 ° C by means of the heating device 5. Oxygen was introduced into the system at a flow rate of 300 ml / min up to a pressure of about 0.75 Pa to oxidize the surface of the base material 2.
    [Formation of α-alumina layer] Chamber 1 was then placed in a mixed gas atmosphere of Ar and oxygen. An average power of 5 kW was applied in total over two sputtering cathodes 6 provided with aluminum targets for performing pulsating direct current and the formation of o-alumina was performed under heating conditions substantially the same as at 10 15 20 25 536 04 14 the oxidation treatment temperature for the formation of the elements provided with ot-alumina. The bias voltage at this time was -300 V, 30 kHz pulsating DC voltage. At the time of formation of the alumina, the temperature of the substrate increased slightly by the effect of the heat supply of the coating. In the formation of alumina, the discharge state was maintained in a so-called transition mode through the use of discharge voltage control and plasma emission spectrometry.
    [Bombardment Treatment] In Comparative Example 1, the procedure was carried out only as described above, while in Example 1 Ar gas was further introduced into the chamber 1 at a pressure of 2.66 Pa and a discharge of 10 A was generated between the thermoionic emitting wire 9 and chamber 1 to generate Ar plasma. While the α-alumina element 2 was irradiated with Ar plasma, a pulsating DC voltage was applied at a frequency of 30 kHz for a total of 15 minutes, or for 5 minutes at -300 V and for 10 minutes at -400 V. whereby the ion bombardment treatment was performed. In Example 2, while similarly, the ot-alumina element 2 was irradiated with the Ar plasma, a pulsating DC voltage at a frequency of 30 kHz for 38 minutes in total, or for 2 minutes at -200 V, -250 V, -300 V and -350 V and for 30 minutes at -400 V, whereby the ion bombardment treatment was carried out and the surface of the ot-alumina film was flattened.
    The alumina films obtained according to Examples 1, 2 and Comparative Example 1 were subjected to X-ray diffraction analysis for thin film (thin film XRD analysis) using CuKa rays to determine the respective the crystal structures from the height of diffraction peaks of α- and γ-crystal structures at an X-ray angle of incidence of 1 °. The surface properties were examined based on SEM images. To determine the machinability, a continuous cutting test was performed under the following conditions, using a SNGA 120408 cemented carbide tip with the alumina laminated film.
    Working material: FCD 400 Cutting speed: 200 m / min Feed rate: 0.2 mm / rpm Cutting depth: 3.0 mm Conditions: Dry The result of the assessment is shown in Table 1 and the SBM images from Example 1 and Comparative Example 1 are shown in Fig. 3 resp. An SBM image of Example 2 is shown in Fig. 5.
    [Table 1] TiAlN- a- Jon- Crystal- SEM Cutting base- alumina- bombardment structure - test materi- id. treatment -picture (Depth of al- layer eñer aluminum- crater- treat- oxide- abrasion ling layer e fi er formation 4 minutes skämin Comparison- 2.1 um 1.7 pm No Mainly Fig. 2 17.2 pm de u, Example 1 + very small L Example 1 2.1 μm 1.7 μm Yes Mainly Fig. 3 9.65 μm a + very small J 10 15 535 04 16 (F OrtS.) TiAlN- a- Jon- Crystal- SEM Cutting grll fl d- aluminum ox- bombardment structure - testing material- treatment -imaging (Depth of all layers e fl er aluminum- crater- treatment- oxide- abrasion ling the layer or formation 4 minutes cutting] Example 2 2.4 pm 1.7 μm Yes Mainly Fig. 5 - a + very small Y From the results in Table 1 it can be seen that both the alumina elements in Comparative Example 1 and in Examples 1 and 2 were mainly composed of an ot-type crystal structure. clearly in Comparative Example 1, without the ion bombardment treatment, as shown in Fig. 2, sharply pointed rock-shaped grains of ot-alumina of fl are 100 nm up to fl era pm. In Example 1 with the ion bombardment treatment was observed, as shown in Figs. 3, that sharply pointed parts of large grains of ot-alumina were rounded, with interrupted shapes of grains, and that the surface was relatively smoothed, in comparison with the comparative example 1.
    In Example 1, the depth of the crate encounter in the cutting test was small, compared to Comparative Example 1, and the tool life was improved. In Example 2, as can be seen from the SEM image in Fig. 5, the shape of the grains is interrupted to become thinner and more flat in comparison with Example 1.
    权利要求:
    Claims (15)
    [1] 1. A method for producing an oralumina layer-formed memberincluding an alumina layer of a-type crystal structure formed on at least apartial surface of a base material, comprisingï a process for forming said alumina layer of ovtype crystal structureon at least the partial surface of said base material; and a process for performing an ion bombardment treatment to thesurface of said formed alumina layer.
    [2] 2. The method for producing an oc-alumina layer-formed memberaccording to claim 1, Wherein said ion bombardment treatment is performedby use of an ion of rare gas in plasma.
    [3] 3. The method for producing an cx-alumina layer-formed memberaccording to claim 2, Wherein said rare gas is Ar.
    [4] 4. The method for producing an ovalumina layer-formed memberaccording to claim 1, Wherein said ion bombardment treatment is performedby use of a metal ion generated from an electrode.
    [5] 5. The method for producing an a-alumina layer-formed memberaccording to claim 4, Wherein said metal ion is an ion of Ti or Al.
    [6] 6. The method for producing an oralumina layer-formed memberaccording to claim 1, Wherein the formation of said alumina layer isperformed by physical vapor deposition method.
    [7] 7. The method for producing an ovalumina layer-formed memberaccording to claim 6, Wherein the process for forming said alumina layer andthe process for performing said ion bombardment treatment are carried out within the same apparatus. 19
    [8] 8. The method for producing an ovalumina layer-formed memberaccording to claim 1, further comprising a process for forming a hard film onat least a partial surface of said base material as a pre-process of the processfor forming said alumina layer so as to form the hard film as an under layerof said alumina layer.
    [9] 9. The method for producing an a-alumina layer-formed memberaccording to claim 8, Wherein said hard film is composed of TiAlN.
    [10] 10. The method for producing an oralumina layer-formed memberaccording to claim 1, Wherein said alumina layer is formed so that thethickness of said alumina layer is 0.1 um or more.
    [11] 11. A surface treatment method of oralumina layer for enhancingsmoothness of a surface of an alumina layer of ortype crystal structure,comprising performing an ion bombardment treatment to the surface of saidalumina layer.
    [12] 12. The surface treatment method of oralumina layer according toclaim 11, Wherein said ion bombardment treatment is performed by use of anion of rare gas in plasma.
    [13] 13. The surface treatment method of ovalumina layer according toclaim 12, Wherein said rare gas is Ar.
    [14] 14. The surface treatment method of oz-alumina layer according toclaim 11, Wherein said ion bombardment treatment is performed by use of ametal ion generated from an electrode.
    [15] 15. The surface treatment method of ovalumina layer according to claim 14, Wherein said metal ion is an ion of Ti or Al.
    类似技术:
    公开号 | 公开日 | 专利标题
    SE536047C2|2013-04-16|Process for the preparation of elements and surface treatment provided with a-alumina layer
    EP1553210B1|2014-05-28|PROCESS FOR PRODUCING ALUMINA COATING COMPOSED MAINLY OF a-TYPE CRYSTAL STRUCTURE
    US7169485B2|2007-01-30|Multilayer coating excellent in wear resistance and heat resistance
    JP2004332004A|2004-11-25|Alumina protective film, and its production method
    EP1616974B1|2013-05-22|Method for preparing an alpha alumina coating
    JP4824173B2|2011-11-30|PVD coated cutting tool and manufacturing method thereof
    CN101426947A|2009-05-06|Coated body
    JP5782019B2|2015-09-24|Cutting tools
    JP5190971B2|2013-04-24|Coating, cutting tool, and manufacturing method of coating
    JP6222675B2|2017-11-01|Surface-coated cutting tool and method for manufacturing the same
    JP4975906B2|2012-07-11|Method for producing cutting tool coated with PVD aluminum oxide
    JP2006307318A|2006-11-09|Method for producing alpha-alumina layer-formed member and surface treatment
    JP2008290163A|2008-12-04|Coating film, cutting tool and coating film making method
    JP3914686B2|2007-05-16|Cutting tool and manufacturing method thereof
    JP2008238281A|2008-10-09|Coated tool
    JP2004332003A|2004-11-25|METHOD OF PRODUCING ALUMINA FILM CONSISTING MAINLY OF alpha TYPE CRYSTAL STRUCTURE, AND METHOD OF PRODUCING MEMBER COATED WITH ALUMINA FILM CONSISTING MAINLY OF alpha TYPE CRYSTAL STRUCTURE
    KR101590203B1|2016-01-29|Oxide coated cutting insert
    JP2004332005A|2004-11-25|METHOD OF PRODUCING ALUMINA FILM CONSISTING MAINLY OF alpha TYPE CRYSTAL STRUCTURE, MEMBER COATED WITH ALUMINA FILM CONSISTING MAINLY OF alpha TYPE CRYSTAL STRUCTURE, AND ITS PRODUCTION METHOD
    JP3971293B2|2007-09-05|Laminated film excellent in wear resistance and heat resistance, production method thereof, and multilayer film coated tool excellent in wear resistance and heat resistance
    KR100682416B1|2007-02-15|Process for producing alumina coating composed mainly of ?-type crystal structure, alumina coating composed mainly of ?-type crystal structure, laminate coating including the alumina coating, member clad with the alumina coating or laminate coating, process for producing the member, and physical evaporation apparatus
    JP2008229759A|2008-10-02|Surface-coated cutting tool having hard coat layer exhibiting excellent chipping resistance and wear resistance during high-speed cutting, and its manufacturing method
    JP5035980B2|2012-09-26|Surface-coated cutting tool that exhibits high wear resistance with a hard coating layer in high-speed milling and a method for producing the same
    JP5035979B2|2012-09-26|Surface-coated cutting tool that exhibits high wear resistance with a hard coating layer in high-speed milling and a method for producing the same
    JP5580906B2|2014-08-27|Coating, cutting tool, and manufacturing method of coating
    JP2012228735A|2012-11-22|Coated tool excellent in wear resistance and method for manufacturing the same
    同族专利:
    公开号 | 公开日
    DE102006000149B4|2016-09-22|
    DE102006000149A1|2006-10-05|
    SE0600585L|2006-10-01|
    US20060219325A1|2006-10-05|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JP2613935B2|1988-12-15|1997-05-28|松下電工株式会社|Manufacturing method of ceramic circuit board|
    US5205871A|1990-06-01|1993-04-27|The United States Of America As Represented By The Secretary Of The Navy|Monocrystalline germanium film on sapphire|
    SE501527C2|1992-12-18|1995-03-06|Sandvik Ab|Methods and articles when coating a cutting tool with an alumina layer|
    SE502223C2|1994-01-14|1995-09-18|Sandvik Ab|Methods and articles when coating a cutting tool with an alumina layer|
    WO1995019884A1|1994-01-21|1995-07-27|The Regents Of The Universtiy Of California|Surface treatment of ceramic articles|
    US7261957B2|2000-03-31|2007-08-28|Carl Zeiss Smt Ag|Multilayer system with protecting layer system and production method|
    JP2002187793A|2000-10-11|2002-07-05|Osg Corp|Method of smoothing diamond film and method of manufacturing diamond coated member|
    US20030224620A1|2002-05-31|2003-12-04|Kools Jacques C.S.|Method and apparatus for smoothing surfaces on an atomic scale|
    EP1553210B1|2002-08-08|2014-05-28|Kabushiki Kaisha Kobe Seiko Sho|PROCESS FOR PRODUCING ALUMINA COATING COMPOSED MAINLY OF a-TYPE CRYSTAL STRUCTURE|EP2042261A3|2007-09-26|2015-02-18|Sandvik Intellectual Property AB|Method of making a coated cutting tool|
    SE531933C2|2007-12-14|2009-09-08|Seco Tools Ab|Coated cemented carbide inserts for machining steel and stainless steel|
    US8277958B2|2009-10-02|2012-10-02|Kennametal Inc.|Aluminum titanium nitride coating and method of making same|
    US8409702B2|2011-02-07|2013-04-02|Kennametal Inc.|Cubic aluminum titanium nitride coating and method of making same|
    KR101297298B1|2011-06-03|2013-08-16|한국야금 주식회사|Coated layer for cutting tools|
    KR20130060544A|2011-11-30|2013-06-10|현대자동차주식회사|Method and apparatus for forming coating layer with nano multi-layer|
    US9914243B2|2012-06-06|2018-03-13|Sharp Kabushiki Kaisha|Mold base material, production method for mold base material, mold production method, and mold|
    US9103036B2|2013-03-15|2015-08-11|Kennametal Inc.|Hard coatings comprising cubic phase forming compositions|
    US9168664B2|2013-08-16|2015-10-27|Kennametal Inc.|Low stress hard coatings and applications thereof|
    US9896767B2|2013-08-16|2018-02-20|Kennametal Inc|Low stress hard coatings and applications thereof|
    US9993878B2|2013-11-08|2018-06-12|Tungaloy Corporation|Coated cutting tool|
    CN110109328A|2019-06-04|2019-08-09|深圳市科洛德打印耗材有限公司|A kind of manufacturing process of long-life high-resolution wide cut diameter printer toner cartridge|
    法律状态:
    2016-11-01| NUG| Patent has lapsed|
    优先权:
    申请号 | 申请日 | 专利标题
    JP2005102445|2005-03-31|
    [返回顶部]