JP5734599B2 - CrTi alloy sputtering target material and method for producing perpendicular magnetic recording medium using them - Google Patents
CrTi alloy sputtering target material and method for producing perpendicular magnetic recording medium using them Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims description 15
- 229910045601 alloy Inorganic materials 0.000 title claims description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 238000005477 sputtering target Methods 0.000 title claims description 13
- 239000013077 target material Substances 0.000 title claims description 13
- 238000001816 cooling Methods 0.000 claims description 21
- 238000002441 X-ray diffraction Methods 0.000 claims description 15
- 238000000465 moulding Methods 0.000 claims description 13
- 239000000843 powder Substances 0.000 claims description 13
- 238000004544 sputter deposition Methods 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 4
- 239000002245 particle Substances 0.000 description 15
- 150000001875 compounds Chemical class 0.000 description 13
- 239000010408 film Substances 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 4
- 238000001513 hot isostatic pressing Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910001069 Ti alloy Inorganic materials 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
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000001755 magnetron sputter deposition Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
Classifications
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- G—PHYSICS
- G11—INFORMATION STORAGE
- G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
- G11B5/00—Recording by magnetisation or demagnetisation of a record carrier; Reproducing by magnetic means; Record carriers therefor
- G11B5/84—Processes or apparatus specially adapted for manufacturing record carriers
- G11B5/8404—Processes or apparatus specially adapted for manufacturing record carriers manufacturing base layers
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/06—Alloys based on chromium
-
- 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
-
- G—PHYSICS
- G11—INFORMATION STORAGE
- G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
- G11B5/00—Recording by magnetisation or demagnetisation of a record carrier; Reproducing by magnetic means; Record carriers therefor
- G11B5/62—Record carriers characterised by the selection of the material
- G11B5/73—Base layers, i.e. all non-magnetic layers lying under a lowermost magnetic recording layer, e.g. including any non-magnetic layer in between a first magnetic recording layer and either an underlying substrate or a soft magnetic underlayer
- G11B5/739—Magnetic recording media substrates
- G11B5/73911—Inorganic substrates
- G11B5/73917—Metallic substrates, i.e. elemental metal or metal alloy substrates
- G11B5/73919—Aluminium or titanium elemental or alloy substrates
-
- G—PHYSICS
- G11—INFORMATION STORAGE
- G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
- G11B5/00—Recording by magnetisation or demagnetisation of a record carrier; Reproducing by magnetic means; Record carriers therefor
- G11B5/84—Processes or apparatus specially adapted for manufacturing record carriers
- G11B5/851—Coating a support with a magnetic layer by sputtering
Description
本発明は、スパッタリングにより薄膜を形成するために用いられる化合物の生成を抑制したCrTi系合金スパッタリング用ターゲット材およびそれらを使用した垂直磁気記録媒体の製造方法に関するものである。 The present invention relates to a manufacturing method of the perpendicular magnetic recording medium using them was CrTi interlockable Kims sputtering target material and suppress the formation of compounds used to form a thin film by sputtering.
一般に、CrTi系ターゲットは垂直磁気記録媒体の下磁膜に使用されており、純Cr粉末と純Ti粉末を熱間成形することで得られる。そのCrTi系ターゲットは脆い化合物相を多く含み、スパッタリング時に脆い化合物相がパーティクル起因となり、スパッタ膜へパーティクルが付着し製品歩留まりを下げている。そのため、CrTiターゲット中の化合物を減らす必要がある。 In general, a CrTi-based target is used for a lower magnetic film of a perpendicular magnetic recording medium, and is obtained by hot forming a pure Cr powder and a pure Ti powder. The CrTi target contains a lot of fragile compound phases, and the fragile compound phases are caused by particles at the time of sputtering, and the particles adhere to the sputtered film, reducing the product yield. Therefore, it is necessary to reduce the compound in the CrTi target.
上記、CrTiターゲット中の化合物を減らすための対策として、例えば、特公平01−2659号公報(特許文献1)に開示されているように、溶湯を急冷することで、化合物を減らしている。しかし、CrTi系ターゲットは粉末冶金法にて作製する材料で溶湯にすることは出来ないという問題がある。 As a countermeasure for reducing the compound in the above CrTi target, for example, as disclosed in Japanese Patent Publication No. 01-2659 (Patent Document 1), the molten metal is rapidly cooled to reduce the compound. However, there is a problem that the CrTi target cannot be made into a molten metal by a material produced by powder metallurgy.
一方、通常粉末焼結体の場合は融点の80%程度の温度で成形するもので、例えば、CrTi系類似組成のものである、特開2003−226963号公報(特許文献2)に開示されているように、ホットプレスにて1200℃以上の温度で成形している。また、特開2002−212607号公報(特許文献3)に開示されているように、アプセット法にて1200℃の温度で成形している。しかし、この焼結温度が高ければ高いほど化合物は増加する傾向にある。
上述した特許文献2、3は、いずれも成形温度が高いために、ターゲット中の化合物が多く存在するために、スパッタ時にパーティクルを多く発生し、スパッタ膜の製品歩留りを低下させるという問題がある。 Patent Documents 2 and 3 described above have a problem in that since the molding temperature is high, there are many compounds in the target, so that many particles are generated during sputtering and the product yield of the sputtered film is lowered.
上述したような問題を解消するために、発明者らは鋭意開発を進めた結果、ターゲット中の化合物を減少させることで、スパッタ膜に生じるパーティクルを減らしたCrTi系合金スパッタリング用ターゲット材およびそれらを使用した垂直磁気記録媒体の製造方法を提供するものである。
その発明の要旨とするところは、
(1)Tiを35〜65原子%含み、残部Crおよび不可避的不純物からなるCrTi系合金スパッタリング用ターゲット材の製造方法において、該CrTi系合金粉末を800〜1100℃で熱間成形後、成形温度から冷却速度500〜36000℃/hrで冷却して得られたCr(110)のX線回折強度[I(Cr)]とCr2 Ti(311)のX線回折強度[I(Cr2 Ti)]の強度比[I(Cr2 Ti)/I(Cr)]を0.50以下とすることを特徴とするCrTi系合金スパッタリング用ターゲット材の製造方法。
To solve the problems described above, inventors have conducted intensive result of developing, by reducing the compound in the target, CrTi interlockable Kims sputtering target material with a reduced particle occurring sputtered film And a method of manufacturing a perpendicular magnetic recording medium using them.
The gist of the invention is that
(1) In a method for producing a CrTi alloy sputtering target material containing 35 to 65 atomic% of Ti, the balance being Cr and inevitable impurities, the CrTi alloy powder is hot formed at 800 to 1100 ° C., and then the forming temperature X-ray diffraction intensity [I (Cr)] of Cr (110) obtained by cooling at a cooling rate of 500 to 36000 ° C./hr from the above and X-ray diffraction intensity [I (Cr 2 Ti) of Cr 2 Ti (311) intensity ratio [I (Cr 2 Ti) / I (Cr)] the manufacturing method of CrTi alloy sputtering target material, characterized in that 0.50 the following.
(2)Tiを35〜65原子%含み、残部Crおよび不可避的不純物からなるCrTi系合金スパッタリング用ターゲット材を用いた垂直磁気記録媒体の製造方法において、該CrTi系合金粉末を800〜1100℃で熱間成形後、成形温度から冷却速度500〜36000℃/hrで冷却して得られたCr(110)のX線回折強度[I(Cr)]とCr2 Ti(311)のX線回折強度[I(Cr2 Ti)]の強度比[I(Cr2 Ti)/I(Cr)]を0.50以下とすることを特徴とするCrTi系合金スパッタリング用ターゲット材を用いたスパッタリングにより得られた磁性膜を有する垂直磁気記録媒体の製造方法にある。 (2) In a method for producing a perpendicular magnetic recording medium using a CrTi alloy sputtering target material containing 35 to 65 atomic% of Ti, the balance being Cr and unavoidable impurities, the CrTi alloy powder is heated at 800 to 1100 ° C. After hot forming, X-ray diffraction intensity [I (Cr)] of Cr (110) obtained by cooling at a cooling rate of 500 to 36000 ° C./hr from the forming temperature and X-ray diffraction intensity of Cr 2 Ti (311) obtained by sputtering using a [I (Cr 2 Ti)] intensity ratio [I (Cr 2 Ti) / I (Cr)] a CrTi alloy sputtering target material, characterized in that 0.50 the following And a method of manufacturing a perpendicular magnetic recording medium having a magnetic film.
以上述べたように、本発明におけるCrTi系合金およびスパッタリングターゲット材は化合物が少なく、スパッタリング時のパーティクル発生を抑えることにより、スパッタ膜の製品歩留りの向上を図ることが出来る極めて優れた効果を奏するものである。 As described above, the CrTi-based alloy and the sputtering target material in the present invention have few compounds, and exhibit an extremely excellent effect that can improve the product yield of the sputtered film by suppressing the generation of particles during sputtering. It is.
以下、本発明について詳細に説明する。
本発明に係る成分組成として、Tiを35〜65原子%とした理由は、スパッタリングターゲット材としてTiが35原子%未満では、スパッタ後の膜がアモルファスにならず、また、65原子%を超えるとスパッタ後の膜がアモルファスにならない。したがって、その範囲を35〜65原子%とした。好ましくは、40〜60原子%とする。
Hereinafter, the present invention will be described in detail.
As the component composition according to the present invention, the reason why Ti is set to 35 to 65 atomic% is that when Ti is less than 35 atomic% as a sputtering target material, the film after sputtering does not become amorphous and exceeds 65 atomic%. The sputtered film does not become amorphous. Therefore, the range was 35 to 65 atomic%. Preferably, it is 40-60 atomic%.
また、Cr(110)のX線回折強度[I(Cr)]とCr2 Ti(311)のX線回折強度[I(Cr2 Ti)]の強度比が[I(Cr2 Ti)/I(Cr)]が0.50以下とした理由は、0.50より高い場合パーティクルを多く発生するからである。好ましくは0.07以下、より好ましくは0.03以下とする。 Further, X-ray diffraction intensity [I (Cr)] and the intensity ratio of X-ray diffraction intensity of Cr 2 Ti (311) [I (Cr 2 Ti)] is [I (Cr 2 Ti) of Cr (110) / I The reason why (Cr)] is 0.50 or less is that when it is higher than 0.50, many particles are generated. Preferably it is 0.07 or less, More preferably, it is 0.03 or less.
上記の製法としては、原料粉末を800〜1100℃で熱間成形する。800℃未満では、十分な密度が得られない。1100℃を超える温度であると、X線回折強度比の値が大きくなり、かつスパッタ時にパーティクルが多く発生し、スパッタ膜へパーティクルが付着し製品歩留りを低下させる。したがって、その範囲を800〜1100℃とした。好ましくは800〜1050℃とする。より好ましくは、アップセット法では上限を1000℃以下、HIP法で900℃以下とする。 As said manufacturing method, raw material powder is hot-molded at 800-1100 degreeC. If it is less than 800 degreeC, sufficient density cannot be obtained. When the temperature is higher than 1100 ° C., the value of the X-ray diffraction intensity ratio increases, and many particles are generated during sputtering, and the particles adhere to the sputtered film, resulting in a decrease in product yield. Therefore, the range was set to 800-1100 ° C. Preferably it is set as 800-1050 degreeC. More preferably, the upper limit is set to 1000 ° C. or lower in the upset method and 900 ° C. or lower in the HIP method.
また、熱間成形後、熱間成形温度から冷却速度144〜36000℃/hrで冷却することで化合物の生成抑制効果がさらに増す。すなわち、上記冷却速度による急冷をすることで高温相のCrTi固溶体を低温まで維持し、固溶体が化合物へ変態するのを抑制するためである。上記冷却速度の下限の好ましい速度は500℃/hr以上とする。 Moreover, the production | generation suppression effect of a compound increases further by cooling with a cooling rate 144-36000 degrees C / hr from hot forming temperature after hot forming. In other words, the rapid cooling at the cooling rate maintains the CrTi solid solution in the high temperature phase to a low temperature and suppresses the solid solution from transforming into a compound. A preferable lower limit of the cooling rate is 500 ° C./hr or more.
以下、本発明について実施例によって具体的に説明する。
粒度が250μm以下の純Cr粉末と粒度が150μm以下の純Ti粉末を表1に示すCr−Ti合金組成に配合し、混合したものを、スチール材質からなる封入缶に充填し、到達真空度10-1Pa以上で脱気真空封入した後、HIP(熱間等方圧プレス)の場合は、加熱温度800〜1100℃、成形圧力150MPa、加熱保持時間1時間の条件で成形し、その後表1に示す条件で300℃まで冷却速度を空冷(No.3、4、5、7、11、12、13、15、16、19、21、22、23、25、29、30、31、33)か水冷(No.8、9、17、26、27、34)で制御し成形体を作製した。また、アップセット法の場合は、加熱温度800〜1100℃、成形圧力500MPa、加熱保持時間1時間の条件で成形し、その後表1に示す条件で300℃まで冷却速度を空冷か水冷で制御し成形体を作製した。次いで機械加工によりターゲットを作製した。
Hereinafter, the present invention will be specifically described with reference to examples.
A pure Cr powder having a particle size of 250 μm or less and a pure Ti powder having a particle size of 150 μm or less were blended in the Cr—Ti alloy composition shown in Table 1 and mixed into a sealed can made of a steel material, and the ultimate vacuum was 10 After degassing vacuum sealing at -1 Pa or higher, in the case of HIP (hot isostatic pressing), molding is performed under the conditions of a heating temperature of 800 to 1100 ° C., a molding pressure of 150 MPa, and a heating and holding time of 1 hour, and then Table 1 The cooling rate is reduced to 300 ° C. under the conditions shown in (No. 3, 4, 5, 7, 11, 12, 13, 15, 16, 19, 21, 22, 23, 25, 29, 30, 31, 33) It was controlled by water cooling (No. 8, 9, 17, 26, 27, 34) to produce a molded body. In the case of the upset method, molding is performed under conditions of a heating temperature of 800 to 1100 ° C., a molding pressure of 500 MPa, and a heating and holding time of 1 hour, and then the cooling rate is controlled by air cooling or water cooling to 300 ° C. under the conditions shown in Table 1. A molded body was produced. Subsequently, the target was produced by machining.
なお、評価方法としては、化合物ピーク比[I(Cr2 Ti)/I(Cr)]はX線源がCu−Kα線で、スキャンスピード4°/minの条件のX線回折にて測定した。また、パーティクル評価方法は、直径95mm、板厚1.75mmのアルミ基板上にDCマグネトロンスパッタにてArガス圧力0.9Paで成膜し、Optical Surface Analyzerにてパーティクル数を評価した。 As an evaluation method, the compound peak ratio [I (Cr 2 Ti) / I (Cr)] was measured by X-ray diffraction under the condition that the X-ray source was Cu—Kα ray and the scan speed was 4 ° / min. . In the particle evaluation method, a film was formed on an aluminum substrate having a diameter of 95 mm and a plate thickness of 1.75 mm by DC magnetron sputtering at an Ar gas pressure of 0.9 Pa, and the number of particles was evaluated by an optical surface analyzer.
表1に示す、比較例No.36、38、40は、成形温度が低く冷却速度が遅いために、得られた粉末成形体の密度が低かったので評価していない。比較例No.37、39、41は、いずれも成形温度が高く、かつ冷却速度が遅いために、X線回折強度比の値が大きく、かつパーティクル数が大きい。比較例No.42は、成形温度が低いために得られた粉末成形体の密度が低かったので評価していない。比較例No.43は、成形後の冷却速度が遅いために、X線回折強度比の値が大きく、かつパーティクル数が大きい。 As shown in Table 1, Comparative Example No. 36, 38 and 40 were not evaluated because the density of the obtained powder compact was low because the molding temperature was low and the cooling rate was slow. Comparative Example No. 37, 39, and 41 all have a high molding temperature and a low cooling rate, so that the value of the X-ray diffraction intensity ratio is large and the number of particles is large. Comparative Example No. No. 42 was not evaluated because the density of the obtained powder compact was low because the molding temperature was low. Comparative Example No. No. 43 has a large X-ray diffraction intensity ratio and a large number of particles because the cooling rate after molding is slow.
比較例No.44は、Ti含有量が低いために、スパッタ後の膜がアモルファスにならないために評価していない。比較例No.45は、Ti含有量が高いために、比較例No.44と同様に、スパッタ後の膜がアモルファスにならないために評価していない。これに対し、本発明例である、No.1〜35は、いずれも本発明条件を満足していることから、X線回折強度を0.5以下に抑えることができ、かつパーティクル数の小さいことが分かる。 Comparative Example No. No. 44 is not evaluated because the Ti content is low and the film after sputtering does not become amorphous. Comparative Example No. No. 45 is a comparative example No. 45 because of its high Ti content. Similar to 44, the film after sputtering is not evaluated because it does not become amorphous. In contrast to this, No. 1 to 35 all satisfy the conditions of the present invention, so that the X-ray diffraction intensity can be suppressed to 0.5 or less and the number of particles is small.
以上のように、本発明による原料粉末を800〜1100℃の温度範囲で熱間成形し、かつその熱間成形後に成形温度から冷却速度144〜36000℃/hrの急速冷却することで、化合物生成量の少ないCrTi系合金およびCrTi系ターゲットを製造することが可能となり、スパッタ膜の製品歩留りの向上を図ることが出来た。
特許出願人 山陽特殊製鋼株式会社
代理人 弁理士 椎 名 彊
As described above, the raw material powder according to the present invention is hot-molded in a temperature range of 800 to 1100 ° C., and after the hot molding, rapid cooling is performed at a cooling rate of 144 to 36000 ° C./hr from the molding temperature. It was possible to manufacture a CrTi-based alloy and a CrTi-based target with a small amount, and it was possible to improve the product yield of the sputtered film.
Patent Applicant Sanyo Special Steel Co., Ltd.
Attorney: Attorney Shiina
Claims (2)
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2010182144A JP5734599B2 (en) | 2010-08-17 | 2010-08-17 | CrTi alloy sputtering target material and method for producing perpendicular magnetic recording medium using them |
CN201180039730.7A CN103119186B (en) | 2010-08-17 | 2011-08-10 | CrTi-based alloy and sputtering target material, perpendicular magnetic recording medium, and processes for producing same |
PCT/JP2011/068290 WO2012023475A1 (en) | 2010-08-17 | 2011-08-10 | CrTi-BASED ALLOY AND SPUTTERING TARGET MATERIAL, PERPENDICULAR MAGNETIC RECORDING MEDIUM, AND PROCESSES FOR PRODUCING SAME |
MYPI2013700253A MY164775A (en) | 2010-08-17 | 2011-08-10 | CrTi-BASED ALLOY AND SPUTTERING TARGET MATERIAL, PERPENDICULAR MAGNETIC RECORDING MEDIUM, AND PRODUCTION METHODS THEREOF |
TW100129208A TWI500791B (en) | 2010-08-17 | 2011-08-16 | CrTi alloy and sputtering target material, vertical magnetic recording medium and their manufacturing method |
Applications Claiming Priority (1)
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JP2010182144A JP5734599B2 (en) | 2010-08-17 | 2010-08-17 | CrTi alloy sputtering target material and method for producing perpendicular magnetic recording medium using them |
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CN (1) | CN103119186B (en) |
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JP5854308B2 (en) * | 2010-05-06 | 2016-02-09 | 日立金属株式会社 | Cr-Ti alloy target material |
JP5964121B2 (en) * | 2012-04-18 | 2016-08-03 | 山陽特殊製鋼株式会社 | CrTi alloy for adhesion film layer and sputtering target material used for magnetic recording medium, and perpendicular magnetic recording medium using the same |
JP6312009B2 (en) * | 2015-02-12 | 2018-04-18 | 日立金属株式会社 | Cr-Ti alloy sputtering target material and method for producing the same |
CN112517917B (en) * | 2020-11-25 | 2023-04-18 | 河南东微电子材料有限公司 | Preparation method of CrTiLa alloy powder for chromium-titanium target material |
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JPH083893B2 (en) * | 1987-02-12 | 1996-01-17 | 株式会社日立製作所 | In-plane magnetic recording medium |
JPH10134631A (en) * | 1996-10-31 | 1998-05-22 | Tokyo Gas Co Ltd | Liminaire installation device responding to double ceiling |
JPH10298742A (en) * | 1997-04-23 | 1998-11-10 | Hitachi Metals Ltd | Cr-ti series target |
JPH11134631A (en) * | 1997-10-27 | 1999-05-21 | Hitachi Metals Ltd | Magnetic record medium |
JPH11140506A (en) * | 1997-11-10 | 1999-05-25 | Daido Steel Co Ltd | Production of multielement metal powder sintered target |
CN1195098C (en) * | 2002-10-28 | 2005-03-30 | 天津大学 | Manufacturing method for producing target material with high resistance used in metal film resistor with high stability by using sputtering technique |
JP4499044B2 (en) * | 2006-01-04 | 2010-07-07 | ヒタチグローバルストレージテクノロジーズネザーランドビーブイ | Perpendicular magnetic recording medium and magnetic storage device using the same |
JP4331182B2 (en) * | 2006-04-14 | 2009-09-16 | 山陽特殊製鋼株式会社 | Soft magnetic target material |
JP2009059431A (en) * | 2007-08-31 | 2009-03-19 | Showa Denko Kk | Magnetic recording medium and magnetic recording and reproducing apparatus |
JP5854308B2 (en) * | 2010-05-06 | 2016-02-09 | 日立金属株式会社 | Cr-Ti alloy target material |
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MY164775A (en) | 2018-01-30 |
WO2012023475A1 (en) | 2012-02-23 |
TWI500791B (en) | 2015-09-21 |
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