WO2013105283A1 - スパッタリング用チタンターゲット - Google Patents
スパッタリング用チタンターゲット Download PDFInfo
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- WO2013105283A1 WO2013105283A1 PCT/JP2012/061412 JP2012061412W WO2013105283A1 WO 2013105283 A1 WO2013105283 A1 WO 2013105283A1 JP 2012061412 W JP2012061412 W JP 2012061412W WO 2013105283 A1 WO2013105283 A1 WO 2013105283A1
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- WIPO (PCT)
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- sputtering
- target
- titanium target
- mass
- titanium
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
- H01J37/00—Discharge tubes with provision for introducing objects or material to be exposed to the discharge, e.g. for the purpose of examination or processing thereof
- H01J37/32—Gas-filled discharge tubes
- H01J37/34—Gas-filled discharge tubes operating with cathodic sputtering
- H01J37/3411—Constructional aspects of the reactor
- H01J37/3414—Targets
- H01J37/3426—Material
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3407—Cathode assembly for sputtering apparatus, e.g. Target
- C23C14/3414—Metallurgical or chemical aspects of target preparation, e.g. casting, powder metallurgy
Definitions
- the present invention relates to a high-quality sputtering titanium target that can stabilize the sputtering characteristics without generating cracks or cracks even during high-power sputtering (high-speed sputtering).
- impurity concentration described in this specification, all are displayed by mass fraction (mass% or ppm).
- titanium also forms many electronic device thin films such as titanium and its alloy film, titanium silicide film, or titanium nitride film because of its unique metallic properties.
- the above-described titanium and its alloy film, titanium silicide film, or titanium nitride film can be formed by physical vapor deposition such as sputtering or vacuum vapor deposition. Of these, the sputtering method used most widely will be described.
- Nitride can be formed by using titanium or an alloy thereof (such as TiAl alloy) as a target and sputtering in a mixed gas atmosphere of argon gas and nitrogen.
- Patent Document 1 Patent Document 1
- Patent Document 2 Patent Document 2
- Patent Document 3 the present applicant has provided a titanium target for sputtering that is free from cracks and cracks even during high power sputtering (high speed sputtering) and has stable sputtering characteristics. This is extremely effective for the above-mentioned purpose, but for high-purity semiconductor sputtering target applications, it is required to exhibit a high effect with fewer kinds of additive elements and addition amounts. It was an issue.
- the object of the present invention is to provide a high-quality titanium target for sputtering by solving the above-described problems, causing no cracks or cracks even during high-power sputtering (high-speed sputtering), stabilizing the sputtering characteristics. To do.
- the present invention is 1) a high-purity titanium target, containing 0.5 to 5 mass ppm of S as an additive component, and excluding the additive component and the gas component, the purity of the target is 99.995 mass% or more
- a titanium target for sputtering is provided.
- the present invention also relates to 2) a high-purity titanium target, which contains a total of 0.5 to 3 mass ppm (less than) S as an additive component, and the purity of the target is 99 except for the additive component and the gas component.
- a titanium target for sputtering characterized by being 995% by mass or more.
- the present invention provides 3) the titanium target for sputtering according to 1) or 2) above, wherein the purity excluding additive components and gas components is 99.999% by mass or more, and 4) average crystal grains of the target
- the titanium target for sputtering of the present invention has an excellent effect that there is no generation of cracks and cracks even during high power sputtering (high speed sputtering), the sputtering characteristics are stabilized, and high quality film formation is possible.
- the titanium target for sputtering of the present invention is a high-purity titanium target having a purity of 99.995% by mass or more. Furthermore, it is preferably 99.999% by mass or more. Needless to say, the purity of the titanium target excludes added components and gas components. In general, a large amount of gas components such as oxygen, nitrogen, and hydrogen are mixed in comparison with other impurity elements. Although it is desirable that the amount of these gas components to be mixed is small, the amount that is usually mixed is not particularly harmful in order to achieve the object of the present invention.
- a sputtering apparatus In high power sputtering (high speed sputtering), the target is heated strongly with the electric power introduced for sputtering. For this reason, a sputtering apparatus is usually provided with a mechanism for cooling the target from the back side of the target, but no matter how it is cooled, a temperature rise in the vicinity of the sputtering surface of the target is inevitable.
- the target surface temperature in high-power sputtering reaches 700 ° C, but this is the temperature at the outermost surface that is directly exposed to the plasma, and even in this case, the surface as a bulk whose strength should be discussed Since the maximum temperature in the vicinity is about 500 ° C., 0.2% proof stress at 500 ° C. is an effective index in the present invention.
- a high purity of 99.995% by mass or more, more preferably 99.999% by mass or more is required.
- the yield stress of a high-purity metal is relatively lower than that of the low-purity metal. Less than 20 MPa.
- One of the major features of the present invention is that 0.5 to 5 ppm by mass of S is added as an additive component. Although it is difficult to thermodynamically accurately calculate the solid solution limit of S in a low concentration region proposed by the present invention in terms of thermodynamics, as a result of various studies, S exceeds 5 mass ppm in titanium. It was found that it was not preferable because it deposited on the Ti substrate. A more preferable range of S addition is 0.5 to 3 ppm by mass (less than). This is because even if various variations are taken into account, the precipitation of S can be almost completely suppressed if it is 3 mass ppm (less than).
- the 0.2% yield strength at 500 ° C. can be 25 MPa or more, and further 30 MPa or more. Further, the addition of S is as small as 5 mass ppm or less, and the purity excluding gas components can be maintained at 99.995 mass% or more after the addition.
- a stable strength can be obtained by appropriately forming a homogeneous crystal structure with an average crystal grain size of 60 ⁇ m or less, further 30 ⁇ m or less by plastic deformation and a subsequent heat treatment step.
- the number of S precipitates in the crystal structure is 20 pieces / mm 2 or less, more preferably 10 pieces / mm 2 or less. As described above, since these S precipitates vary depending on the plastic deformation process and the subsequent heat treatment process, it can be said that it is desirable to produce them with the intention of reducing them as much as possible.
- Precipitates in the sputtering target can potentially cause arcing and particle generation, so it is effective to reduce the precipitates.
- These characteristics can be obtained by containing 0.5 to 5 ppm by mass of S, and in particular, by containing S in a total of 0.5 to 3 ppm by mass (less than). These numerical ranges show the range in which the effectiveness of the present invention can be realized. If it is less than the lower limit, the object of the present invention cannot be achieved, and if it exceeds the upper limit, the characteristics as a high purity target are impaired, so the above range is used.
- the atmosphere is preferably an inert atmosphere.
- the initial cathode current density is preferably set to 0.6 A / cm 2 or less, which is a low current density.
- the electrolysis temperature is preferably 600 to 800 ° C.
- a predetermined amount of the deposited Ti and S thus obtained is mixed and melted by EB (electron beam), and this is cooled and solidified to produce an ingot, hot forging or hot extrusion at 800 to 950 ° C., etc.
- the billet is produced by performing the hot plastic working. By appropriately adjusting these processes, the cast structure in which the ingot is uneven and coarse can be broken and uniformly refined.
- the billet obtained in this way is cut, and cold plastic deformation such as cold forging or cold rolling is repeatedly performed, and by applying high strain to the billet, the disc shape can finally secure the target dimensions.
- the amount of strain is preferably 1.0 to 5.0
- the processing rate is preferably 50 to 90%. Although it can be carried out outside the range of these conditions, the above conditions are suitable production conditions.
- the target having a processed structure in which high strain is stored is rapidly heated using a fluidized bed furnace or the like and heat-treated at 400 to 600 ° C. for a short time.
- a target having a fine recrystallized structure of 60 ⁇ m or less, further 30 ⁇ m or less can be obtained. If the temperature is increased and the heat treatment time is lengthened, the crystal becomes coarser, so it is necessary to adjust according to the purpose.
- the titanium target of the present invention thus obtained has a 0.2% proof stress of 25 MPa or more, further 30 MPa or more when heated to 500 ° C., has a high 0.2% proof stress at high temperatures, and high power. There is an effect that cracks and cracks can be suppressed even during sputtering (high-speed sputtering).
- the amount of S is adjusted to 0.5 to 5 mass ppm even when the forging or rolling process conditions and heat treatment conditions exceeding the above ranges are manufactured, and the crystal grain size or the number of S precipitates changes.
- the proof stress can be maintained at 25 MPa or more, and further 30 MPa or more. That is, the S amount is a major factor, and the adjustment of the S amount is important.
- the proof stress can be maintained at 25 MPa or more, further 30 MPa or more by appropriately adjusting the crystal grain size or the number of S precipitates.
- the adjustment of the crystal grain size or the number of S precipitates can be said to be a condition under which the proof stress can be stably maintained at 25 MPa or more, further 30 MPa or more.
- These manufacturing steps show an example of a method for obtaining the high-purity titanium target of the present invention, containing 0.5 to 5 ppm by mass of S, the balance being titanium and inevitable impurities,
- the production process is not particularly limited as long as a titanium target for sputtering having a target purity of 99.995% by mass or more can be obtained except for components and gas components.
- a present Example is an example to the last, and is not restrict
- Example 1 A Ti ingot was prepared by adding S: 5 mass ppm to 99.995 mass% purity Ti and melting by electron beam.
- the component analysis results are shown in Table 1.
- the processing conditions processing and heat treatment conditions
- the heat treatment temperature was 400 to 550 ° C. The same applies to the following embodiments.
- Example 2 A Ti ingot was prepared by adding S: 3.5 mass ppm to Ti having a purity of 99.995 mass% and melting by electron beam. The component analysis results are shown in Table 1.
- Example 3 A Ti ingot was prepared by adding S: 2 mass ppm to 99.995 mass% Ti and purging by electron beam. The component analysis results are shown in Table 1.
- Example 4 S: 1 mass ppm was added to Ti having a purity of 99.995 mass%, and electron beam melting was performed to prepare a Ti ingot.
- the component analysis results are shown in Table 1.
- Example 5 A Ti ingot was prepared by adding S: 3.5 mass ppm to Ti having a purity of 99.995 mass% and melting by electron beam. The component analysis results are shown in Table 1.
- Example 6 S: 3.3 ppm by mass was added to 99.995% by mass of Ti, and an electron beam was melted to prepare a Ti ingot.
- the component analysis results are shown in Table 1.
- Example 7 S: 2.2 mass ppm was added to Ti with a purity of 99.995 mass%, and electron beam melting was performed to prepare a Ti ingot.
- the component analysis results are shown in Table 1.
- Comparative Example 1 Except for not adding S, Ti having the same purity of 99.995% by mass was produced. Comparative Example 1 does not satisfy the condition of the lower limit of 0.5% by mass of S. The component analysis results are shown in Table 1.
- Comparative Example 2 12 mass ppm was added to Ti having a purity of 99.995 mass%, and electron beam melting was performed to prepare a Ti ingot. Comparative Example 1 does not satisfy the condition of the upper limit of 5 ppm by mass of S. The component analysis results are shown in Table 1.
- Example 1-7 and Comparative Example 1-2 was processed into a target shape using the manufacturing conditions in paragraphs [0023] to [0026] as appropriate.
- Example 1-7 The average crystal grain size of the targets of Example 1-7 and Comparative Example 1 was examined. The results are shown in Table 2. Regarding Example 1-4, the average crystal grain size was 10 ⁇ m or less, and good results were obtained. For Example 5-7, the average crystal grain size was 35-60 ⁇ m or less. Although the crystal grain size was large, cracks did not occur, and the average number of particles after sputtering film formation was not so large, so it was in a range that could be used as a target.
- Example 1-7 and Comparative Example 1-2 the orientation of crystals appearing on the target was examined.
- the results are also shown in Table 2.
- the basal plane orientation ratio in Table 2 is calculated by the formula shown in Table 3.
- Example 1-7 As shown in Table 2, there was no difference in the average crystal grain size between Example 1-4 and Comparative Example 1-2. As shown in Table 2, regarding the basal plane orientation ratio, no difference was found between Example 1-7 and Comparative Example 1-2.
- Example 1-7 From Table 2, there was no difference in crystal structure and orientation after target production in Example 1-7 and Comparative Example 1-2. Also in actual sputtering, the distance between the targets of Example 1-7 was the same as that of Comparative Example 1 in the film forming speed and other behaviors.
- test pieces were prepared from the targets prepared in Example 1-7 and Comparative Example 1-2, a tensile test was performed at 500 ° C., and 0.2% yield strength at that time was measured.
- the test piece is a case where three points of the center, 1 / 2R, and outer periphery of the target are sampled. The results are shown in Table 4.
- the conditions of the tensile test are as follows. Specimen shape: JIS shape (G0567II-6) Test method: Conforms to JIS G 0567 Test machine: 100 kN high-temperature tensile test machine Test temperature: 500 ° C Marking distance: 30mm Test speed: displacement control 0.3% / min, after yield strength 7.5% / min Temperature rising rate: 45 ° C / min, holding 15 minutes Temperature measurement: Bundled thermocouples in the specimen
- Example 1-7 and Comparative Example 1-2 a 15 mm ⁇ 15 mm test piece was collected from the targets prepared in Example 1-7 and Comparative Example 1-2, subjected to electrolytic polishing and etching, and a crystal structure observation surface was prepared, and the surface was subjected to FE-SEM ( JSOL-made JSM-7000F) was observed with an acceleration voltage of 15 kV and a 2000-fold field of view, and S precipitates in the Ti crystal structure were examined.
- the area per field of view is 2.7 ⁇ 10 ⁇ 3 mm 2 .
- the number of S precipitates was observed by FE-SEM under the above conditions, and when precipitate-like foreign substances were observed, it was confirmed by SDX of the field of view that they were S precipitates containing S or a sulfurized S compound as a component. By this operation, the number of S precipitates was measured by observing a plurality of visual fields in each sample, and the number per unit area was calculated from the average number. The results are shown in Table 4. In addition, when 40 visual fields were observed and no precipitate was found, it was set to less than 10 pieces / mm 2 . Examples of the FE-SEM image and its EDX image are shown in FIGS. The images shown in FIGS. 1 and 2 are examples observed in Example 1.
- Example 1-7 and Comparative Example 1-2 were mounted on a sputtering apparatus and actually subjected to high power sputtering, and the presence of cracks in the target and the number of particles on a 300 mm silicon wafer on which Ti was formed by sputtering. was measured. The results are shown in Table 4.
- the average value of the tensile test was 0.2% proof stress of 30 MPa or more in each of Examples 1 to 4, and stable characteristics were obtained. In Examples 5 to 7, the 0.2% proof stress was in the range of 25 to 28 MPa. In the high power sputtering (high speed sputtering) test, neither crack nor crack occurred.
- Comparative Example 1 the condition that the 0.2% proof stress is 25 MPa or more is not satisfied, and after erosion of about 1 mm by sputtering in a high power sputtering (high speed sputtering) test, the sputtering chamber is opened and the target surface is opened. As a result of visual observation, several cracks having a width of about 0.1 to 2 mm occurred at the portion where the erosion was deepest.
- Comparative Example 2 the 0.2% proof stress was 30 MPa or more, and no cracks or cracks occurred in the high power sputtering (high speed sputtering) test. Compared to Examples 1 to 7, it was about twice. In Comparative Example 2, the number of S precipitates is higher than that in Examples 1 to 4, and it can be said that the number of S precipitates is a cause of particle generation.
- S is contained in an amount of 0.5 to 5 mass ppm, more preferably a total of S is 0.5 to 3 mass ppm (less than), and the additive component and the gas component are excluded.
- a sputtering titanium target having a purity of 99.995% by mass or more can provide a great effect that no cracks or cracks are generated even in a high power sputtering (high speed sputtering) test.
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Abstract
Description
なお、本明細書中に記載する不純物濃度については、全て質量分率(mass%又はppm)で表示する。
このような中で、電子、デバイス機器がより微小化し、かつ集積度が高まる方向にある。これら多くの製造工程の中で多数の薄膜が形成されるが、チタンもその特異な金属的性質からチタン及びその合金膜、チタンシリサイド膜、あるいは窒化チタン膜などとして、多くの電子機器薄膜の形成に利用されている。
一般に上記のチタン及びその合金膜、チタンシリサイド膜、あるいは窒化チタン膜等はスパッタリングや真空蒸着などの物理的蒸着法により形成することができる。この中で最も広範囲に使用されているスパッタリング法について説明する。
一般に、ある程度の酸素、窒素、水素等のガス成分は他の不純物元素に比べて多く混入する。これらのガス成分の混入量は少ない方が望ましいが、通常混入する程度の量は、本願発明の目的を達成するためには、特に有害とならない。
ハイパワースパッタリング(高速スパッタリング)時における亀裂や割れの発生は、この加熱/冷却の繰り返しに伴い、特に最も高温になるターゲット表面近傍が熱膨張/収縮を繰り返すことによる低サイクル疲労破壊により引き起こされるという問題が発生する。
S添加のより好ましい範囲は、0.5~3質量ppm(未満)である。これは各種ばらつきを考慮しても、3質量ppm(未満)であればほぼ完全にSの析出を抑止できるという理由による。
これらの数値範囲は、本願発明の有効性を実現できる範囲を示すものである。下限値未満では本願発明の目的を達成できず、また上限値を超えるものは高純度ターゲットとしての特性を損なうので、上記の範囲とする。
純度99.995質量%のTiに、S:5質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。加工条件(加工と熱処理条件)は、段落0024、0025、0026に記載する条件で実施した。ただし、熱処理温度については、400~550℃とした。以下の実施例も同様である。
純度99.995質量%のTiに、S:3.5質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。
純度99.995質量%のTiに、S:2質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。
純度99.995質量%のTiに、S:1質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。
純度99.995質量%のTiに、S:3.5質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。
純度99.995質量%のTiに、S:3.3質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。
純度99.995質量%のTiに、S:2.2質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。成分分析結果を、表1に示す。
Sを添加しないこと以外は、全く同一の純度99.995質量%のTiを作製した。比較例1はSの下限値0.5質量%の条件を満たしていない。成分分析結果を、表1に示す。
純度99.995質量%のTiに、S:12質量ppm添加して、電子ビーム溶解しTiインゴットを作製した。比較例1はSの上限値5質量ppmの条件を満たしていない。成分分析結果を、表1に示す。
表2に示すように、Basalの面配向率については、実施例1-7及び比較例1-2で差異は見られなかった。
試験片形状:JIS形状(G 0567II-6)
試験方法:JIS G 0567に準拠
試験機:100kN高温引張り試験機
試験温度:500°C
標点距離:30mm
試験速度:変位制御0.3%/min、耐力以降7.5%/min
昇温速度:45°C/min、保持15分
温度測定:試験体中央熱電対括り付け
結果を表4に示す。なお、40視野観察し、析出物が見つからなかった場合、10個/mm2未満とした。またFE-SEM像及びそのEDX像の例を図1及び図2に示す。なお、この図1及び図2に示す像は、いずれも実施例1において観察された例である。
Claims (10)
- 高純度チタンターゲットであって、添加成分として、Sを合計0.5~5質量ppmを含有し、添加成分とガス成分を除き、ターゲットの純度が99.995質量%以上であることを特徴とするスパッタリング用チタンターゲット。
- 高純度チタンターゲットであって、添加成分として、Sを合計0.5~3質量ppm(未満)を含有し、添加成分とガス成分を除き、ターゲットの純度が99.995質量%以上であることを特徴とするスパッタリング用チタンターゲット。
- 添加成分とガス成分を除く純度が99.999質量%以上であることを特徴とする請求項1又は2記載のスパッタリング用チタンターゲット。
- ターゲットの平均結晶粒径が60μm以下であることを特徴とする請求項1~3のいずれか一項に記載のスパッタリング用チタンターゲット。
- ターゲットの平均結晶粒径が30μm以下であることを特徴とする請求項1~3のいずれか一項に記載のスパッタリング用チタンターゲット。
- チタンターゲットを500°Cに加熱した場合のターゲットの、0.2%耐力が25MPa以上であることを特徴とする請求項1~5のいずれか一項に記載のスパッタリング用チタンターゲット。
- チタンターゲットを500°Cに加熱した場合のターゲットの、0.2%耐力が30MPa以上であることを特徴とする請求項1~5のいずれか一項に記載のスパッタリング用チタンターゲット。
- チタンターゲット結晶組織中のS析出物が100個/mm2以下であることを特徴とする請求項1~7のいずれか一項に記載のスパッタリング用チタンターゲット。
- チタンターゲット結晶組織中のS析出物が30個/mm2以下であることを特徴とする請求項1~7のいずれか一項に記載のスパッタリング用チタンターゲット。
- チタンターゲット結晶組織中のS析出物が10個/mm2以下であることを特徴とする請求項1~7のいずれか一項に記載のスパッタリング用チタンターゲット。
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US14/353,507 US9666418B2 (en) | 2012-01-12 | 2012-04-27 | Titanium target for sputtering |
CN201910337427.3A CN110129744B (zh) | 2012-01-12 | 2012-04-27 | 溅射用钛靶 |
JP2013506020A JP5689527B2 (ja) | 2012-01-12 | 2012-04-27 | スパッタリング用チタンターゲット |
SG11201400327SA SG11201400327SA (en) | 2012-01-12 | 2012-04-27 | Titanium target for sputtering |
KR1020147008123A KR20140054377A (ko) | 2012-01-12 | 2012-04-27 | 스퍼터링용 티탄 타겟 |
EP12865255.9A EP2738285B1 (en) | 2012-01-12 | 2012-04-27 | Titanium target for sputtering |
KR1020167023961A KR20160106772A (ko) | 2012-01-12 | 2012-04-27 | 스퍼터링용 티탄 타겟 |
CN201280052810.0A CN103890227A (zh) | 2012-01-12 | 2012-04-27 | 溅射用钛靶 |
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US (1) | US9666418B2 (ja) |
EP (1) | EP2738285B1 (ja) |
JP (1) | JP5689527B2 (ja) |
KR (2) | KR20160106772A (ja) |
CN (2) | CN103890227A (ja) |
SG (1) | SG11201400327SA (ja) |
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JP5420609B2 (ja) | 2010-08-25 | 2014-02-19 | Jx日鉱日石金属株式会社 | スパッタリング用チタンターゲット |
CN103180482B (zh) | 2010-10-25 | 2016-05-04 | 吉坤日矿日石金属株式会社 | 溅射用钛靶 |
EP2772327B1 (en) * | 2012-02-14 | 2017-05-17 | JX Nippon Mining & Metals Corporation | High-purity titanium ingots, manufacturing method therefor, and titanium sputtering target |
WO2014136702A1 (ja) | 2013-03-06 | 2014-09-12 | Jx日鉱日石金属株式会社 | スパッタリング用チタンターゲット及びその製造方法 |
CN105154834A (zh) * | 2015-09-07 | 2015-12-16 | 云南钛业股份有限公司 | 一种圆柱形钛溅射靶材的生产方法 |
CN116949410B (zh) * | 2023-09-20 | 2023-12-19 | 西安聚能医工科技有限公司 | 一种合金基体表面磁控溅射涂层的方法及其产品与应用 |
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WO2001038598A1 (fr) | 1999-11-22 | 2001-05-31 | Nikko Materials Company, Limited | Cible en titane pour la pulverisation cathodique |
JP2001509548A (ja) | 1997-07-11 | 2001-07-24 | ジョンソン マッティー エレクトロニクス インコーポレイテッド | チタンスパッタターゲット及びその製造方法 |
JP2010235998A (ja) | 2009-03-31 | 2010-10-21 | Nippon Mining & Metals Co Ltd | スパッタリング用チタンターゲット |
JP2012067386A (ja) * | 2010-08-25 | 2012-04-05 | Jx Nippon Mining & Metals Corp | スパッタリング用チタンターゲット |
WO2012057057A1 (ja) * | 2010-10-25 | 2012-05-03 | Jx日鉱日石金属株式会社 | スパッタリング用チタンターゲット |
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JPH11269621A (ja) * | 1997-12-24 | 1999-10-05 | Toho Titanium Co Ltd | 高純度チタン材の加工方法 |
US8663440B2 (en) * | 2010-09-28 | 2014-03-04 | Jx Nippon Mining & Metals Corporation | Titanium target for sputtering |
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2012
- 2012-04-27 CN CN201280052810.0A patent/CN103890227A/zh active Pending
- 2012-04-27 WO PCT/JP2012/061412 patent/WO2013105283A1/ja active Application Filing
- 2012-04-27 EP EP12865255.9A patent/EP2738285B1/en active Active
- 2012-04-27 KR KR1020167023961A patent/KR20160106772A/ko active Search and Examination
- 2012-04-27 CN CN201910337427.3A patent/CN110129744B/zh active Active
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- 2012-04-27 US US14/353,507 patent/US9666418B2/en active Active
- 2012-04-27 KR KR1020147008123A patent/KR20140054377A/ko active Search and Examination
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Patent Citations (5)
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JP2001509548A (ja) | 1997-07-11 | 2001-07-24 | ジョンソン マッティー エレクトロニクス インコーポレイテッド | チタンスパッタターゲット及びその製造方法 |
WO2001038598A1 (fr) | 1999-11-22 | 2001-05-31 | Nikko Materials Company, Limited | Cible en titane pour la pulverisation cathodique |
JP2010235998A (ja) | 2009-03-31 | 2010-10-21 | Nippon Mining & Metals Co Ltd | スパッタリング用チタンターゲット |
JP2012067386A (ja) * | 2010-08-25 | 2012-04-05 | Jx Nippon Mining & Metals Corp | スパッタリング用チタンターゲット |
WO2012057057A1 (ja) * | 2010-10-25 | 2012-05-03 | Jx日鉱日石金属株式会社 | スパッタリング用チタンターゲット |
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Also Published As
Publication number | Publication date |
---|---|
EP2738285A4 (en) | 2015-01-07 |
JPWO2013105283A1 (ja) | 2015-05-11 |
SG11201400327SA (en) | 2014-06-27 |
US20140251802A1 (en) | 2014-09-11 |
CN110129744A (zh) | 2019-08-16 |
EP2738285A1 (en) | 2014-06-04 |
JP5689527B2 (ja) | 2015-03-25 |
KR20160106772A (ko) | 2016-09-12 |
TWI541370B (zh) | 2016-07-11 |
TW201329262A (zh) | 2013-07-16 |
US9666418B2 (en) | 2017-05-30 |
CN110129744B (zh) | 2022-10-28 |
KR20140054377A (ko) | 2014-05-08 |
CN103890227A (zh) | 2014-06-25 |
EP2738285B1 (en) | 2020-12-23 |
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