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TWI542714B - An oxide sintered body, and a sputtering target made of the oxide sintered body - Google Patents

An oxide sintered body, and a sputtering target made of the oxide sintered body Download PDF

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TWI542714B
TWI542714B TW104103400A TW104103400A TWI542714B TW I542714 B TWI542714 B TW I542714B TW 104103400 A TW104103400 A TW 104103400A TW 104103400 A TW104103400 A TW 104103400A TW I542714 B TWI542714 B TW I542714B
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sintered body
igzo
oxide sintered
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TW201536936A (en
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Koji Kakuta
Kozo Osada
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Jx Nippon Mining & Metals Corp
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    • C23COATING 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
    • C23CCOATING 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
    • C23C14/00Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/22Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
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    • C04B35/453Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zinc, tin, or bismuth oxides or solid solutions thereof with other oxides, e.g. zincates, stannates or bismuthates
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    • C04B2235/02Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30Constituents and secondary phases not being of a fibrous nature
    • C04B2235/32Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
    • C04B2235/3286Gallium oxides, gallates, indium oxides, indates, thallium oxides, thallates or oxide forming salts thereof, e.g. zinc gallate
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Description

氧化物燒結體及由該氧化物燒結體構成之濺鍍靶 Oxide sintered body and sputtering target composed of the oxide sintered body

本發明係關於一種由銦(In)、鎵(Ga)、鋅(Zn)、氧(O)及不可避免之雜質構成之氧化物(一般被稱作「IGZO」)。視需要使用此「IGZO」進行說明),尤其有關於一種IGZO燒結體及由該燒結體構成之濺鍍靶。 The present invention relates to an oxide (generally referred to as "IGZO") composed of indium (In), gallium (Ga), zinc (Zn), oxygen (O), and unavoidable impurities. In particular, there is an IGZO sintered body and a sputtering target composed of the sintered body.

以往,於FPD(平面顯示器),其底板之TFT(薄膜電晶體)一直使用α-Si(非晶矽)。然而,α-Si無法獲得充足之電子遷移率,近年來正在進行使用電子遷移率較α-Si高之In-Ga-Zn-O系氧化物(IGZO)的TFT之研究開發。而且,使用IGZO-TFT之次世代高性能平面顯示器被部分實用化而獲得注意。 Conventionally, in FPD (Planar Display), the TFT (thin film transistor) of the bottom plate has been using α-Si (amorphous germanium). However, α-Si cannot obtain sufficient electron mobility, and research and development of TFTs using In-Ga-Zn-O-based oxides (IGZO) having higher electron mobility than α-Si have been under development in recent years. Moreover, the next generation high-performance flat panel display using IGZO-TFT has been partially put into practical use.

IGZO膜主要係對由IGZO燒結體製作之靶進行濺鍍而形成。作為IGZO濺鍍靶,例如於專利文獻1中揭示了可藉由生成含有In、Ga及Zn而In的含量較周圍多之組織,而即使不進行於高溫之還原處理,亦可製作比電阻低之靶。又,於專利文獻2中,揭示有藉由含有特定比例之In、Ga、Zn,共存有二種以上之同質結晶,而可使濺鍍穩定,減少顆粒(particle)之產生。 The IGZO film is mainly formed by sputtering a target made of an IGZO sintered body. As an IGZO sputtering target, for example, Patent Document 1 discloses that a structure containing In, Ga, and Zn and having a higher content of In than that of the surrounding can be produced, and the specific resistance can be made even without performing a reduction treatment at a high temperature. The target. Further, in Patent Document 2, it is disclosed that by containing a specific ratio of In, Ga, and Zn, two or more kinds of homogeneous crystals are coexisted, and sputtering can be stabilized, and generation of particles can be reduced.

因此,將此種IGZO膜用作TFT膜之活性層之情形時,膜中的氧缺乏之量係對膜之電特性造成影響的要因之一。為了控制此氧缺乏量,在濺鍍成膜時於除了氬氣等非活性氣體外,一般還會導入氧氣。氧之 濺鍍效率較氬氣低,於濺鍍時若導入氧氣則被濺鍍之原子之量會減少,成膜速率降低。於IGZO膜之濺鍍成膜中,為了控制膜之載體濃度為期望之值,而必須導入大量之氧,因此有成膜速率降低而使得生產性降低之問題。 Therefore, when such an IGZO film is used as an active layer of a TFT film, the amount of oxygen deficiency in the film is one of the factors that affect the electrical characteristics of the film. In order to control the amount of oxygen deficiency, oxygen is generally introduced in addition to an inert gas such as argon at the time of sputtering film formation. Oxygen The sputtering efficiency is lower than that of argon. When oxygen is introduced during sputtering, the amount of atoms that are sputtered is reduced, and the film formation rate is lowered. In the sputtering film formation of the IGZO film, in order to control the carrier concentration of the film to a desired value, a large amount of oxygen must be introduced, so that there is a problem that the film formation rate is lowered and the productivity is lowered.

[專利文獻1]日本特開2011-105995號公報 [Patent Document 1] Japanese Laid-Open Patent Publication No. 2011-105995

[專利文獻2]日本專利第5288141號 [Patent Document 2] Japanese Patent No. 5288141

本發明之課題為提供一種IGZO氧化物燒結體,可減低為了獲得具有期望之載體濃度的膜所必需之濺鍍時的氧濃度。由該燒結體構成之濺鍍靶可提高濺鍍速率,可顯著提升生產性。 An object of the present invention is to provide an IGZO oxide sintered body which can reduce the oxygen concentration at the time of sputtering necessary for obtaining a film having a desired carrier concentration. The sputtering target composed of the sintered body can increase the sputtering rate and can significantly improve productivity.

為了解決上述課題,本發明人等努力研究,結果得知藉由在IGZO燒結體中增加Zn(鋅)的含量,可降低膜之載體濃度,其結果可減低濺鍍時之氧濃度。本發明人等基於以上見解,提供以下發明。 In order to solve the problem, the inventors of the present invention have made an effort to reduce the carrier concentration of the film by increasing the content of Zn (zinc) in the IGZO sintered body, and as a result, the oxygen concentration at the time of sputtering can be reduced. The present inventors have provided the following invention based on the above findings.

1)一種氧化物燒結體,係由銦(In)、鎵(Ga)、鋅(Zn)、氧(O)及不可避免之雜質構成,其特徵在於:具備由以In、Ga及Zn之原子比計In:Ga:Zn為1:1:1構成之IGZO(111)相與較IGZO(111)相含有更多Zn的IGZO相,其中,較IGZO(111)相含有更多Zn的IGZO相以面積比率計,為1~10%,該氧化物燒結體之In、Ga及Zn的原子數比由In:Ga:Zn=1:1:(1.02~1.10)構成。 1) An oxide sintered body comprising indium (In), gallium (Ga), zinc (Zn), oxygen (O), and unavoidable impurities, characterized by having an atom of In, Ga, and Zn The IGZO (111) phase composed of In:Ga:Zn is 1:1:1 and the IGZO phase containing more Zn than the IGZO (111) phase, wherein the IGZO phase containing more Zn than the IGZO (111) phase In the area ratio, the atomic ratio of In, Ga, and Zn is composed of In:Ga:Zn=1:1:(1.02 to 1.10).

2)如上述1)之氧化物燒結體,其平均粒徑為20μm以下。 2) The oxide sintered body according to the above 1), which has an average particle diameter of 20 μm or less.

3)如上述1)或2)任一項之氧化物燒結體,其體電阻為30mΩcm以下。 (3) The oxide sintered body according to any one of the above 1) or 2), which has a bulk resistance of 30 m?cm or less.

4)如上述1)至3)中任一項之氧化物燒結體,其燒結體密度為6.3g/cm3以上。 The oxide sintered body according to any one of the above 1) to 3, wherein the sintered body has a sintered body density of 6.3 g/cm 3 or more.

5)一種濺鍍靶,由上述1)至4)中任一項之氧化物燒結體製作。 5) A sputtering target produced by the oxide sintered body according to any one of the above 1) to 4).

本發明藉由在由(In)、鎵(Ga)、鋅(Zn)、氧(O)及不可避免之雜質構成之IGZO系氧化燒結體中具備含有大量Zn之IGZO相,而可減低為了形成具有期望之載體濃度的薄膜所必需之濺鍍時的氧濃度,因此具有可提升濺鍍速率之優異效果。 In the IGZO-based oxidized sintered body composed of (In), gallium (Ga), zinc (Zn), oxygen (O), and unavoidable impurities, the IGZO phase containing a large amount of Zn is provided to reduce the formation of IGZO phase. The oxygen concentration at the time of sputtering necessary for the film having the desired carrier concentration has an excellent effect of increasing the sputtering rate.

[圖1]係表示實施例1之氧化物燒結體由EPMA獲得之組織影像的圖。 Fig. 1 is a view showing a tissue image obtained by EPMA of the oxide sintered body of Example 1.

[圖2]係表示實施例2之氧化物燒結體由EPMA獲得之組織影像的圖。 Fig. 2 is a view showing a tissue image obtained by EPMA of the oxide sintered body of Example 2.

[圖3]係表示實施例3之氧化物燒結體由EPMA獲得之組織影像的圖。 Fig. 3 is a view showing a tissue image obtained by EPMA of the oxide sintered body of Example 3.

[圖4]係表示比較例之氧化物燒結體由EPMA獲得之組織影像的圖。 Fig. 4 is a view showing a tissue image obtained by EPMA of an oxide sintered body of a comparative example.

[圖5]係表示成膜環境中之氧濃度與成膜速率之關係的圖。 Fig. 5 is a graph showing the relationship between the oxygen concentration in the film formation environment and the film formation rate.

[圖6]係表示成膜環境中之氧濃度與薄膜之載體濃度之關係的圖。 Fig. 6 is a graph showing the relationship between the oxygen concentration in the film formation environment and the carrier concentration of the film.

本發明之氧化燒結體的特徵在於:由銦(In)、鎵(Ga)、鋅(Zn)、氧(O)及不可避免之雜質構成,具備由以In、Ga及Zn之原子比計In:Ga:Zn為1:1:1構成之IGZO(111)相與較IGZO(111)相含有更多Zn的IGZO相,較IGZO(111)相含有更多Zn的IGZO相以面積比率計,為1~10%。藉由具備較IGZO(111)相含有更多Zn的IGZO相(富含Zn之IGZO相),可減低為了獲得具有期望之載體濃度的膜所必需之濺鍍時的氧濃度,因此可提升濺鍍速率(成膜速率)。 The oxidized sintered body of the present invention is characterized in that it is composed of indium (In), gallium (Ga), zinc (Zn), oxygen (O), and unavoidable impurities, and has an atomic ratio of In, Ga, and Zn. :Ga:Zn is an IGZO (111) phase composed of 1:1:1 and an IGZO phase containing more Zn than the IGZO (111) phase, and an IGZO phase containing more Zn than the IGZO (111) phase is measured by area ratio. It is 1~10%. By having an IGZO phase (an Zn-rich IGZO phase) containing more Zn than the IGZO (111) phase, the oxygen concentration at the time of sputtering necessary for obtaining a film having a desired carrier concentration can be reduced, thereby enhancing the sputtering. Plating rate (film formation rate).

若使用含有大量Zn之存在IGZO相之IGZO燒結體進行濺鍍 成膜,則機制雖不清楚,但膜之載體濃度會降低。藉由使用此種靶,可將為了獲得期望之載體濃度而導入的氧氣濃度較以往降得更低,因此可抑制起因於氧濃度之濺鍍速率之減低。再者,本發明之氧化物燒結體在將氧氣濃度設為與以往相同之情形時,具有可降低載體濃度之效果,更不用說濺鍍速率之降低不會成為本發明之要件。 If IGZO sintered body containing ZnZO phase containing a large amount of Zn is used for sputtering Film formation, although the mechanism is not clear, but the carrier concentration of the membrane will decrease. By using such a target, the concentration of oxygen introduced to obtain a desired carrier concentration can be lowered lower than in the related art, so that the decrease in the sputtering rate due to the oxygen concentration can be suppressed. Further, the oxide sintered body of the present invention has an effect of lowering the concentration of the carrier when the oxygen concentration is set to be the same as in the related art, and it is needless to say that the reduction in the sputtering rate does not become a requirement of the present invention.

較IGZO(111)相含有更多Zn之IGZO相(富含Zn之IGZO相),較佳於燒結體中以面積比率計,為1~10%。若富含Zn之IGZO相的面積比率未達1%,則降低膜之載體濃度的效果不充分,另一方面,若富含Zn之IGZO相的面積比率超過10%,則濺鍍成膜之膜的載體濃度增加。 The IGZO phase (IGZ phase rich in Zn) containing more Zn than the IGZO (111) phase is preferably 1 to 10% in area ratio in the sintered body. If the area ratio of the Zn-rich IGZO phase is less than 1%, the effect of lowering the carrier concentration of the film is insufficient. On the other hand, if the area ratio of the Zn-rich IGZO phase exceeds 10%, the film is deposited by sputtering. The carrier concentration of the membrane is increased.

又,於本發明中,氧化物燒結體之In、Ga及Zn之原子比,較佳為In:Ga:Zn=1:1:(1.02~1.10)。藉此,可有效率地產生富含Zn之相,可使膜之載體濃度降低。若Zn之原子比未達1.02,則降低膜之載體濃度的效果變小。另一方面,若Zn之原子比超過1.10,則相較於氧化物燒結體為IGZO(111)相單相之情形,膜之載體濃度雖低,但載體濃度轉為增加傾向。因此,IGZO燒結體之In、Ga、Zn的原子比,較佳為上述數值範圍。 Further, in the present invention, the atomic ratio of In, Ga, and Zn in the oxide sintered body is preferably In:Ga:Zn = 1:1: (1.02 to 1.10). Thereby, the Zn-rich phase can be efficiently produced, and the carrier concentration of the film can be lowered. If the atomic ratio of Zn is less than 1.02, the effect of lowering the carrier concentration of the film becomes small. On the other hand, when the atomic ratio of Zn exceeds 1.10, the carrier concentration of the film tends to increase as compared with the case where the oxide sintered body is a single phase of the IGZO (111) phase. Therefore, the atomic ratio of In, Ga, and Zn of the IGZO sintered body is preferably in the above numerical range.

本發明之氧化物燒結體之平均粒徑較佳為20μm以下。藉由將平均粒徑減小,可提高機械強度。若平均粒徑超過20μm,則機械強度降低,於在濺鍍時投入過多電力的情形時,有可能會因濺鍍靶與接合該靶之背板的熱膨脹差所產生之應力,使得燒結體發生破裂。 The oxide sintered body of the present invention preferably has an average particle diameter of 20 μm or less. The mechanical strength can be improved by reducing the average particle diameter. When the average particle diameter exceeds 20 μm, the mechanical strength is lowered, and when excessive electric power is applied during sputtering, there is a possibility that a stress generated by a difference in thermal expansion between the sputtering target and the backing plate to which the target is bonded may cause the sintered body to occur. rupture.

又,本發明之氧化物燒結體之體電阻較佳為30mΩcm以下。若體電阻低,則於濺鍍中發生異常放電之可能性變低,可抑制產生對成膜中之膜造成不良影響的顆粒。另一方面,若體電阻超過30mΩcm,則 即便是可進行直流濺鍍之情形,於長時間之濺鍍中有時會發生異常放電、根據狀況,有時於DC不發生放電,而必須使用裝置成本高且成膜速率亦降低的射頻濺鍍。 Moreover, the bulk resistance of the oxide sintered body of the present invention is preferably 30 mΩcm or less. When the bulk resistance is low, the possibility of occurrence of abnormal discharge during sputtering becomes low, and generation of particles which adversely affect the film in the film formation can be suppressed. On the other hand, if the bulk resistance exceeds 30mΩcm, then Even in the case of DC sputtering, abnormal discharge may occur during long-time sputtering. Depending on the situation, there may be no discharge in DC, and RF sputtering with high device cost and reduced film formation rate must be used. plating.

又,本發明之氧化物燒結體之燒結體密度較佳為6.2g/cm3以上。於將本發明之氧化物燒結體作為濺鍍靶使用之情形時,燒結體之高密度化具有提高濺鍍膜之均勻性,又,可在濺鍍時顯著減低顆粒之產生的優異效果。 Moreover, the sintered body density of the oxide sintered body of the present invention is preferably 6.2 g/cm 3 or more. When the oxide sintered body of the present invention is used as a sputtering target, the high density of the sintered body has an effect of improving the uniformity of the sputtering film and significantly reducing the generation of particles during sputtering.

若表示本發明之氧化物燒結體的製造步驟之代表例,則為如下。 A representative example of the production steps of the oxide sintered body of the present invention is as follows.

準備氧化銦(In2O3)、氧化鎵(Ga2O3)及氧化鋅(ZnO)作為原料。為了避免雜質對電特性造成不良影響,較佳使用純度為4N以上之原料。將各原料秤量成特定之組成比。再者,於該等之原料含有無法避免之雜質。 Indium oxide (In 2 O 3 ), gallium oxide (Ga 2 O 3 ), and zinc oxide (ZnO) were prepared as raw materials. In order to prevent impurities from adversely affecting electrical characteristics, it is preferred to use a raw material having a purity of 4N or more. Each raw material is weighed to a specific composition ratio. Furthermore, these raw materials contain unavoidable impurities.

接下來,以氧化物燒結體成為特定組成比之方式添加、混合各原料。若此時混合不充分,則靶中之各成分會發生偏析,成為於濺鍍中電弧等之異常放電的原因,或成為顆粒產生之原因,因此較佳充分進行混合。進而,藉由將混合粉進行微粉碎、造粒,使混合粉之成形性及燒結性提升,可獲得高密度之燒結體。作為混合、粉碎之手段,例如可使用市售之混合器或球磨機、珠磨機等,作為造粒之手段,例如可使用市售之噴霧乾燥器。 Next, each raw material is added and mixed so that the oxide sintered body becomes a specific composition ratio. When the mixing is insufficient at this time, segregation occurs in each component in the target, which causes abnormal discharge such as arc during sputtering, or causes particles to be generated. Therefore, it is preferable to sufficiently mix. Further, by finely pulverizing and granulating the mixed powder, the formability and the sinterability of the mixed powder are improved, and a sintered body having a high density can be obtained. As means for mixing and pulverizing, for example, a commercially available mixer, a ball mill, a bead mill or the like can be used, and as a means for granulation, for example, a commercially available spray dryer can be used.

繼而,將混合粉末填充於金屬模具,以面壓力400~1000kgf/cm2,維持1~3分之條件進行單軸加壓,獲得成形體。若未達面壓力400kgf/cm2則無法獲得充分之密度的成形體。又,即使施加過度之面壓力,成 形體之密度亦難以提升至某一定之值以上,及於單軸加壓原理性地在成形體內容易產生密度分布,成為燒結時之變形或破裂的原因,因此1000kgf/cm2以上之面壓力,在生產上並不被認為特別需要。 Then, the mixed powder was filled in a metal mold, and uniaxially pressurized under the conditions of a surface pressure of 400 to 1000 kgf/cm 2 for 1 to 3 minutes to obtain a molded body. If the surface pressure is not 400 kgf/cm 2 , a molded body having a sufficient density cannot be obtained. Further, even if an excessive surface pressure is applied, it is difficult to increase the density of the molded body to a certain value or more, and the uniaxial pressing principle is likely to cause a density distribution in the molded body, which causes deformation or cracking during sintering. Therefore, the surface pressure of 1000 kgf/cm 2 or more is not considered to be particularly required in production.

接著,以塑膠對此成形體進行雙重真空包裝,以壓力1500~4000kgf/cm2,維持1~3分之條件實施CIP(冷均壓法)。若未達壓力1500kgf/cm2,則無法獲得充分之CIP的效果,另一方面即使施加4000kgf/cm2以上之壓力,成形體之密度亦難以提升至某一定之值以上,因此4000kgf/cm2以上之面壓,在生產上並不被認為特別需要。 Next, the molded body was double vacuum-packed with a plastic, and CIP (cold pressure equalization method) was carried out under the conditions of a pressure of 1500 to 4000 kgf/cm 2 and maintaining 1 to 3 minutes. If the pressure is not 1500 kgf/cm 2 , sufficient CIP effect cannot be obtained. On the other hand, even if a pressure of 4000 kgf/cm 2 or more is applied, the density of the molded body is hard to increase to a certain value or more, so 4000 kgf/cm 2 The above surface pressure is not considered to be particularly necessary in production.

繼而,對成形體以溫度1300~1500℃、維持時間5~24小時、大氣環境或氧環境下進行燒結,獲得燒結體。若燒結溫度低於1300℃則無法獲得充分之密度的燒結體,若燒結溫度在1500℃以上,則燒結體中之結晶粒的尺寸變得過大,而有使得燒結體的機械強度降低之虞。又若維持時間未達5小時則無法獲得充分之密度的燒結體,若維持時間超過24小時,則由生產成本之觀點而言,並不佳。 Then, the formed body is sintered at a temperature of 1300 to 1500 ° C for a period of 5 to 24 hours, in an atmosphere or an oxygen atmosphere, to obtain a sintered body. When the sintering temperature is lower than 1300 ° C, a sintered body having a sufficient density cannot be obtained. When the sintering temperature is 1500 ° C or higher, the size of the crystal grains in the sintered body becomes excessively large, and the mechanical strength of the sintered body is lowered. Further, if the maintenance time is less than 5 hours, a sintered body having a sufficient density cannot be obtained, and if the maintenance time exceeds 24 hours, it is not preferable from the viewpoint of production cost.

又,於成形、燒結工程中,除了上述方法以外,亦可使用HP(熱壓法)或HIP(熱均壓法)。以上述方法獲得之燒結體,可藉由研削、研磨等機械加工形成靶形狀,藉此製成濺鍍靶。 Further, in the molding and sintering process, in addition to the above methods, HP (hot pressing method) or HIP (heat equalizing method) may be used. The sintered body obtained by the above method can be formed into a target shape by mechanical processing such as grinding or polishing to thereby form a sputtering target.

當製作本發明之氧化物燒結體時,對以上述方式獲得之濺鍍靶以特定之條件實施濺鍍而成膜,視需要以特定溫度將此膜退火,可藉此獲得氧化物半導體膜。又,當製作本發明之薄膜電晶體時,將上述氧化物半導體膜使用作為如圖1所示之閘電極,可藉此獲得薄膜電晶體。 When the oxide sintered body of the present invention is produced, the sputtering target obtained in the above manner is sputter-deposited under specific conditions, and the film is annealed at a specific temperature as necessary, whereby an oxide semiconductor film can be obtained. Further, when the thin film transistor of the present invention is produced, the above oxide semiconductor film is used as a gate electrode as shown in Fig. 1, whereby a thin film transistor can be obtained.

[實施例] [Examples]

以下基於實施例以及比較例進行說明。再者,本實施例僅為一例,本發明並未受本例之任何限制。即,本發明係僅受申請專利範圍之限制,並包含本發明所含之實施例以外的各種變形。 Hereinafter, description will be made based on examples and comparative examples. Furthermore, this embodiment is only an example, and the present invention is not limited by this example. That is, the present invention is limited only by the scope of the patent application, and includes various modifications other than the embodiments included in the invention.

(實施例1) (Example 1)

以燒結體之組成比以In、Ga及Zn的原子比計成為1.00:1.00:1.02之方式,秤量In2O3粉、Ga2O3粉、ZnO粉之後,將該等粉末以濕式進行混合、微粉碎,之後,以噴霧乾燥器進行乾燥、造粒,獲得混合粉末。接著,將此混合粉末以面壓力400~1000kgf/cm2進行單軸加壓而獲得成形體。繼而,將所獲得之成形體以塑膠進行雙重真空包裝,以1500~4000kgf/cm2進行CIP成形後,在氧環境中以溫度1430℃燒結20小時。 In the case where the composition ratio of the sintered body is 1.00:1.00:1.02 in terms of the atomic ratio of In, Ga, and Zn, the In 2 O 3 powder, the Ga 2 O 3 powder, and the ZnO powder are weighed, and the powder is wet-processed. After mixing and finely pulverizing, it was dried and granulated by a spray dryer to obtain a mixed powder. Next, the mixed powder was uniaxially pressed at a surface pressure of 400 to 1000 kgf/cm 2 to obtain a molded body. Then, the obtained molded body was double vacuum-packed with plastic, CIP molding was performed at 1500 to 4000 kgf/cm 2 , and then sintered at a temperature of 1430 ° C for 20 hours in an oxygen atmosphere.

將以此方式獲得之IGZO燒結體由EPMA獲得之組織照片表示於圖1(圖中,白色部分相當於富含Zn之IGZO相)。自EPMA的組織照片確認實施例1之燒結體係由IGZO(111)相與富含Zn之IGZO相構成。又,自組織照片求出富含Zn之IGZO相的面積,由其與組織照片整體之面積的比率算出富含Zn之IGZO相的面積比率。其結果,富含Zn之IGZO相之面積比率為1.7%。 A photograph of the structure of the IGZO sintered body obtained in this manner from EPMA is shown in Fig. 1 (in the figure, the white portion corresponds to the Zn-rich IGZO phase). It was confirmed from the tissue photograph of EPMA that the sintering system of Example 1 was composed of an IGZO (111) phase and a Zn-rich IGZO phase. Further, the area of the Zn-rich IGZO phase was determined from the photomicrograph, and the area ratio of the Zn-rich IGZO phase was calculated from the ratio of the area of the IGZO phase. As a result, the area ratio of the Zn-rich IGZO phase was 1.7%.

又,燒結體之平均粒徑為19.7μm,燒結體密度高達6.3g/cm3。進而,體電阻低至30.0mΩcm。將以上結果示於表1。再者,藉由弦線法(chord method)算出平均粒徑,藉由阿基米德法求出燒結體密度,藉由四探針法算出體電阻。 Further, the sintered body had an average particle diameter of 19.7 μm and a sintered body density of 6.3 g/cm 3 . Further, the volume resistance is as low as 30.0 m Ω cm. The above results are shown in Table 1. Further, the average particle diameter was calculated by a chord method, the sintered body density was determined by the Archimedes method, and the bulk resistance was calculated by a four-probe method.

繼而,將燒結體機械加工,精加工成6吋之濺鍍靶,使用此靶進行濺鍍。濺鍍條件如下:成膜方法:直流磁控濺鍍;成膜溫度:室溫; 成膜壓力:0.5Pa(O2+Ar);輸入功率:2.74W/cm2,將成膜時之氧濃度改為2vol%、6vol%、10vol%,形成各厚度約4000Å之膜。 Then, the sintered body was machined and finished into a 6-inch sputtering target, and sputtering was performed using this target. The sputtering conditions are as follows: film formation method: DC magnetron sputtering; film formation temperature: room temperature; film formation pressure: 0.5 Pa (O 2 + Ar); input power: 2.74 W/cm 2 , oxygen at the time of film formation The concentration was changed to 2 vol%, 6 vol%, and 10 vol% to form a film having a thickness of about 4000 Å.

自表面形貌儀所得到之膜厚測定值與成膜時間算出各氧濃度的成膜速率。將其結果表示於表1及圖4。如表1所示,確認到與下述之比較例相比,成膜速率有些許提升。 The film formation rate of each oxygen concentration was calculated from the film thickness measurement value and the film formation time obtained by the surface topographer. The results are shown in Table 1 and Figure 4. As shown in Table 1, it was confirmed that the film formation rate was slightly improved as compared with the comparative example described below.

又,針對各自之膜,於大氣中以400℃進行退火1小時,測量霍爾效應,藉此測量載體濃度與霍爾遷移率。將其結果表示於表1與圖6。如表1所示,確認到與下述之比較例相比,各氧濃度之載體濃度均降低。再者,於霍爾效應之測量,係使用東陽特克尼卡股份有限公司製造之ResiTest8400。 Further, for each film, annealing was performed at 400 ° C for 1 hour in the atmosphere, and the Hall effect was measured, thereby measuring the carrier concentration and the Hall mobility. The results are shown in Table 1 and Figure 6. As shown in Table 1, it was confirmed that the carrier concentration of each oxygen concentration was lowered as compared with the comparative example described below. Furthermore, the ResiTest 8400 manufactured by Dongyang Teknika Co., Ltd. was used for the measurement of the Hall effect.

(實施例2) (Example 2)

以燒結體之組成比以In、Ga及Zn的原子比計成為1.00:1.00:1.05之方式秤量In2O3粉、Ga2O3粉、ZnO粉之後,將該等粉末以濕式進行混合、微粉碎,之後,以噴霧乾燥器進行乾燥、造粒,獲得混合粉末。接著,將此混合粉末以以面壓力400~1000kgf/cm2進行單軸加壓而獲得成形體。繼而,將所獲得之成形體以塑膠進行雙重真空包裝,以1500~4000kgf/cm2進行CIP成形後,在氧環境中以溫度1430℃燒結20小時。 The In 2 O 3 powder, the Ga 2 O 3 powder, and the ZnO powder are weighed so that the composition ratio of the sintered body is 1.00:1.00:1.05 in terms of the atomic ratio of In, Ga, and Zn, and the powders are mixed in a wet manner. After the fine pulverization, drying and granulation were carried out in a spray dryer to obtain a mixed powder. Next, the mixed powder was uniaxially pressed at a surface pressure of 400 to 1000 kgf/cm 2 to obtain a molded body. Then, the obtained molded body was double vacuum-packed with plastic, CIP molding was performed at 1500 to 4000 kgf/cm 2 , and then sintered at a temperature of 1430 ° C for 20 hours in an oxygen atmosphere.

將以此方式獲得之IGZO燒結體由EPMA獲得之將組織照片表示於圖2(圖中,白色部分相當於富含Zn之IGZO相)。自EPMA的組織照片確認實施例2之燒結體係由IGZO(111)相與富含Zn之IGZO相構成。又,以與實施例1相同之方式算出富含Zn之IGZO相的面積之結果,富含Zn之IGZO相之面積比率為5.2%。 The IGZO sintered body obtained in this manner was obtained from EPMA, and the photograph of the structure is shown in Fig. 2 (in the figure, the white portion corresponds to the Zn-rich IGZO phase). It was confirmed from the tissue photograph of EPMA that the sintering system of Example 2 was composed of an IGZO (111) phase and a Zn-rich IGZO phase. Further, as a result of calculating the area of the Zn-rich IGZO phase in the same manner as in Example 1, the area ratio of the Zn-rich IGZO phase was 5.2%.

又,燒結體之平均粒徑為14.9μm,燒結體密度高達6.3g/cm3。進而,體電阻低至23.0mΩcm。將以上結果示於表1。再者,於平均粒徑、燒結體密度、體電阻之測量,使用與實施例1相同之方法。 Further, the sintered body had an average particle diameter of 14.9 μm and a sintered body density of 6.3 g/cm 3 . Further, the volume resistance was as low as 23.0 m Ω cm. The above results are shown in Table 1. Further, in the measurement of the average particle diameter, the sintered body density, and the bulk resistance, the same method as in Example 1 was used.

繼而,將燒結體機械加工,精加工成6吋之濺鍍靶,使用此靶進行濺鍍。濺鍍條件設為與實施例1相同。然後,自表面形貌儀所得到之膜厚測定值與成膜時間算出各氧濃度的成膜速率。將其結果表示於表1及圖5。如表1所示,確認到與下述之比較例相比,成膜速率提升。 Then, the sintered body was machined and finished into a 6-inch sputtering target, and sputtering was performed using this target. The sputtering conditions were set to be the same as in the first embodiment. Then, the film formation rate of each oxygen concentration was calculated from the film thickness measurement value obtained by the surface topographer and the film formation time. The results are shown in Table 1 and Figure 5. As shown in Table 1, it was confirmed that the film formation rate was improved as compared with the comparative example described below.

接著,針對各自之膜,於大氣中以400℃進行退火1小時,測量霍爾效應,藉此測量載體濃度與霍爾遷移率。將其結果表示於表1與圖6。如表1所示,確認到與下述之比較例相比,各氧濃度之載體濃度均降低。 Next, the respective films were annealed at 400 ° C for 1 hour in the atmosphere, and the Hall effect was measured, thereby measuring the carrier concentration and the Hall mobility. The results are shown in Table 1 and Figure 6. As shown in Table 1, it was confirmed that the carrier concentration of each oxygen concentration was lowered as compared with the comparative example described below.

(實施例3) (Example 3)

以燒結體之組成比以In、Ga及Zn的原子比計成為1.00:1.00:1.10之方式秤量In2O3粉、Ga2O3粉、ZnO粉之後,將該等粉末以濕式進行混合、微粉碎,之後,以噴霧乾燥器進行乾燥、造粒,獲得混合粉末。接著,將此混合粉末以以面壓力400~1000kgf/cm2進行單軸加壓而獲得成形體。繼而,將所獲得之成形體以塑膠進行雙重真空包裝,以1500~4000kgf/cm2進行CIP成形後,在氧環境中以溫度1430℃燒結20小時。 The In 2 O 3 powder, the Ga 2 O 3 powder, and the ZnO powder are weighed so that the composition ratio of the sintered body is 1.00:1.00:1.10 in terms of the atomic ratio of In, Ga, and Zn, and the powders are mixed in a wet manner. After the fine pulverization, drying and granulation were carried out in a spray dryer to obtain a mixed powder. Next, this mixed powder at a surface pressure of 400 ~ 1000kgf / cm 2 to uniaxial pressing to obtain a molded body. Then, the obtained molded body was double vacuum-packed with plastic, CIP molding was performed at 1500 to 4000 kgf/cm 2 , and then sintered at a temperature of 1430 ° C for 20 hours in an oxygen atmosphere.

將以如此方式獲得之IGZO燒結體由EPMA獲得之將組織照片表示於圖3(圖中,白色部分相當於富含Zn之IGZO相)。自EPMA的組織照片確認實施例3之燒結體係由IGZO(111)相與富含Zn之IGZO相構成。又,以與實施例1相同之方式算出富含Zn之IGZO相的面積之結果,富含Zn之IGZO相之面積比率為9.8%。 The photograph of the structure obtained by EPMA obtained from the IGZO sintered body obtained in this manner is shown in Fig. 3 (in the figure, the white portion corresponds to the Zn-rich IGZO phase). From the tissue photograph of EPMA, it was confirmed that the sintering system of Example 3 consisted of an IGZO (111) phase and a Zn-rich IGZO phase. Further, as a result of calculating the area of the Zn-rich IGZO phase in the same manner as in Example 1, the area ratio of the Zn-rich IGZO phase was 9.8%.

又,燒結體之平均粒徑為8.9μm,燒結體密度高達6.3g/cm3。進而,體電阻低至21.0mΩcm。將以上結果示於表1。再者,於平均粒徑、燒結體密度、體電阻之測量,使用與實施例1相同之方法。 Further, the sintered body had an average particle diameter of 8.9 μm and a sintered body density of 6.3 g/cm 3 . Further, the volume resistance was as low as 21.0 m Ω cm. The above results are shown in Table 1. Further, in the measurement of the average particle diameter, the sintered body density, and the bulk resistance, the same method as in Example 1 was used.

繼而,將燒結體機械加工,精加工成6吋之濺鍍靶,使用此靶進行濺鍍。濺鍍條件設為與實施例1相同。然後,自表面形貌儀所得到之膜厚測定值與成膜時間算出各氧濃度的成膜速率。將其結果表示於表1及圖5。如表1所示,確認到與下述之比較例相比,成膜速率提升。 Then, the sintered body was machined and finished into a 6-inch sputtering target, and sputtering was performed using this target. The sputtering conditions were set to be the same as in the first embodiment. Then, the film formation rate of each oxygen concentration was calculated from the film thickness measurement value obtained by the surface topographer and the film formation time. The results are shown in Table 1 and Figure 5. As shown in Table 1, it was confirmed that the film formation rate was improved as compared with the comparative example described below.

接著,針對各自之膜,於大氣中以400℃進行退火1小時,測量霍爾效應,藉此測量載體濃度與霍爾遷移率。將其結果表示於表1與圖6。如表1所示,確認到與下述之比較例相比,各氧濃度之載體濃度均降低。 Next, the respective films were annealed at 400 ° C for 1 hour in the atmosphere, and the Hall effect was measured, thereby measuring the carrier concentration and the Hall mobility. The results are shown in Table 1 and Figure 6. As shown in Table 1, it was confirmed that the carrier concentration of each oxygen concentration was lowered as compared with the comparative example described below.

(比較例) (Comparative example)

以燒結體之組成比以In、Ga及Zn的原子比計成為1.00:1.00:1.00之方式秤量In2O3粉、Ga2O3粉、ZnO粉之後,將該等粉末以濕式進行混合、微粉碎,之後,以噴霧乾燥器進行乾燥、造粒,獲得混合粉末。接著,將此混合粉末以以面壓400~1000kgf/cm2進行單軸加壓而獲得成形體。繼而,將所獲得之成形體以塑膠袋真空包裝成2重,以1500~4000kgf/cm2進行CIP成形後,在氧環境中以溫度1430℃燒結20小時。 The In 2 O 3 powder, the Ga 2 O 3 powder, and the ZnO powder are weighed so that the composition ratio of the sintered body is 1.00:1.00:1.00 in terms of an atomic ratio of In, Ga, and Zn, and the powders are mixed in a wet manner. After the fine pulverization, drying and granulation were carried out in a spray dryer to obtain a mixed powder. Next, this mixed powder was uniaxially pressed at a surface pressure of 400 to 1000 kgf/cm 2 to obtain a molded body. Then, the obtained molded body was vacuum-packed into a plastic bag to a weight of 2, and CIP was formed at 1500 to 4000 kgf/cm 2 , and then sintered at a temperature of 1430 ° C for 20 hours in an oxygen atmosphere.

藉由如此獲得之IGZO燒結體的EPMA將組織照片表示於圖4(圖中,白色部分相當於富含Zn之IGZO相)。自EPMA的組織照片確認比較例之燒結體僅由IGZO(111)相構成。 The photograph of the structure of the IGZO sintered body thus obtained is shown in Fig. 4 (in the figure, the white portion corresponds to the Zn-rich IGZO phase). It was confirmed from the tissue photograph of EPMA that the sintered body of the comparative example was composed only of the IGZO (111) phase.

又,獲得燒結體之平均粒徑為24.6μm,燒結體密度為6.3g/cm3之高密度物。進而,獲得體電阻為37.3mΩcm之低電阻物。將以上結果示於表1。再者,於平均粒徑、燒結體密度、體電阻之測量,使用與實施例1相同之方法。 Further, a high-density material having an average particle diameter of the sintered body of 24.6 μm and a sintered body density of 6.3 g/cm 3 was obtained. Further, a low resistance of 37.3 mΩcm was obtained. The above results are shown in Table 1. Further, in the measurement of the average particle diameter, the sintered body density, and the bulk resistance, the same method as in Example 1 was used.

繼而,將燒結體機械加工,精加工成6吋之濺鍍靶,使用此靶進行濺鍍。濺鍍條件設為與實施例1相同。然後,自表面形貌儀所得到膜厚測定值與成膜時間算出各氧濃度的成膜速率。將其結果表示於表1及圖5。如表1所示,與實施例相比,結果成膜速率變低。接著,針對各自之膜,於大氣中以400℃進行退火1小時,測量霍爾效應,藉此測量載體濃度與霍爾遷移率。將其結果表示於表1與圖6。如表1所示,確認與實施例相比,載體濃度結果變高。 Then, the sintered body was machined and finished into a 6-inch sputtering target, and sputtering was performed using this target. The sputtering conditions were set to be the same as in the first embodiment. Then, the film formation rate of each oxygen concentration was calculated from the film thickness measurement value and the film formation time obtained from the surface topographer. The results are shown in Table 1 and Figure 5. As shown in Table 1, as a result, the film formation rate became lower as compared with the examples. Next, the respective films were annealed at 400 ° C for 1 hour in the atmosphere, and the Hall effect was measured, thereby measuring the carrier concentration and the Hall mobility. The results are shown in Table 1 and Figure 6. As shown in Table 1, it was confirmed that the carrier concentration result was higher as compared with the examples.

自以上結果,可確認實施例之Zn組成1.02、1.05、1.10之任 一者與比較例之Zn組成相比,載體濃度降低。得知於比較例中,將氧濃度設為10%以上對載體濃度降至一定程度以下(例如1e+15cm-3以下)係為必要,但實施例1~3中,2%便充分。進而,即便於以相同氧濃度進行成膜之情形時,實施例之成膜速率較比較例稍高,因此不必為了獲得預期之載體濃度(於一般之TFT膜之載體濃度為自1e+15cm-3以下)而增加氧,可維持高成膜速率。 From the above results, it was confirmed that the carrier concentration of any of the Zn compositions of the examples of 1.02, 1.05, and 1.10 was lower than that of the Zn composition of the comparative example. It is found that in the comparative example, it is necessary to set the oxygen concentration to 10% or more and to reduce the carrier concentration to a certain level or less (for example, 1e + 15 cm -3 or less), but in Examples 1 to 3, 2% is sufficient. Further, even in the case of film formation at the same oxygen concentration, the film formation rate of the examples is slightly higher than that of the comparative example, so it is not necessary to obtain the desired carrier concentration (the carrier concentration of the conventional TFT film is from 1e + 15 cm). -3 or less) while increasing oxygen, a high film formation rate can be maintained.

【產業上之可利用性】 [Industrial Availability]

本發明之氧化物燒結體可作為濺鍍靶,於使用此濺鍍靶進行濺鍍成膜之情形時,可減少濺鍍環境中之氧濃度,故可提升濺鍍速率(成膜速率)。因此,藉著如此般使用濺鍍靶,而具有可將氧化物半導體膜及薄膜電晶體穩定地進行量產之優異效果。本發明之氧化物半導體膜尤其可作為平板顯示或可撓性面板顯示(flexible panel display)等底板之TFT的活性層而發揮作用。 The oxide sintered body of the present invention can be used as a sputtering target, and when the sputtering target is used for sputtering, the oxygen concentration in the sputtering environment can be reduced, so that the sputtering rate (film formation rate) can be improved. Therefore, by using a sputtering target as described above, it is excellent in that the oxide semiconductor film and the thin film transistor can be stably mass-produced. The oxide semiconductor film of the present invention can function particularly as an active layer of a TFT of a substrate such as a flat panel display or a flexible panel display.

Claims (6)

一種氧化物燒結體,係由銦(In)、鎵(Ga)、鋅(Zn)、氧(O)及不可避免之雜質構成,其特徵在於:具備由以In、Ga及Zn之原子比計In:Ga:Zn為1:1:1構成之IGZO(111)相與較IGZO(111)相含有更多Zn的IGZO相,其中,較IGZO(111)相含有更多Zn的IGZO相以面積比率計,為1~10%,該氧化物燒結體之In、Ga及Zn的原子數比由In:Ga:Zn=1:1:(1.02~1.10)構成。 An oxide sintered body comprising indium (In), gallium (Ga), zinc (Zn), oxygen (O), and unavoidable impurities, characterized by having an atomic ratio of In, Ga, and Zn In:Ga:Zn is an IGZO (111) phase composed of 1:1:1 and an IGZO phase containing more Zn than the IGZO (111) phase, wherein the IGZO phase containing more Zn than the IGZO (111) phase is in an area The ratio is 1 to 10%, and the atomic ratio of In, Ga, and Zn of the oxide sintered body is composed of In:Ga:Zn = 1:1: (1.02 to 1.10). 如申請專利範圍第1項之氧化物燒結體,其平均粒徑為20μm以下。 The oxide sintered body of the first aspect of the patent application has an average particle diameter of 20 μm or less. 如申請專利範圍第1項之氧化物燒結體,其體電阻為30mΩcm以下。 The oxide sintered body of the first aspect of the patent application has a bulk resistance of 30 mΩcm or less. 如申請專利範圍第2項之氧化物燒結體,其體電阻為30mΩcm以下。 The oxide sintered body of the second aspect of the patent application has a bulk resistance of 30 mΩcm or less. 如申請專利範圍第1至4項中任一項之氧化物燒結體,其燒結體密度為6.3g/cm3以上。 The oxide sintered body according to any one of claims 1 to 4, which has a sintered body density of 6.3 g/cm 3 or more. 一種濺鍍靶,其係由申請專利範圍第1至5項中任一項之氧化物燒結體構成。 A sputtering target comprising the oxide sintered body according to any one of claims 1 to 5.
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