WO2022025033A1 - Cr-Si-C系焼結体 - Google Patents
Cr-Si-C系焼結体 Download PDFInfo
- Publication number
- WO2022025033A1 WO2022025033A1 PCT/JP2021/027671 JP2021027671W WO2022025033A1 WO 2022025033 A1 WO2022025033 A1 WO 2022025033A1 JP 2021027671 W JP2021027671 W JP 2021027671W WO 2022025033 A1 WO2022025033 A1 WO 2022025033A1
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- WIPO (PCT)
- Prior art keywords
- sintered body
- chromium
- silicon
- powder
- carbon
- Prior art date
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- 239000011651 chromium Substances 0.000 claims abstract description 144
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 98
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 79
- 229910010271 silicon carbide Inorganic materials 0.000 claims abstract description 76
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 72
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 70
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 70
- 239000010703 silicon Substances 0.000 claims abstract description 70
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 59
- 229910018540 Si C Inorganic materials 0.000 claims abstract description 41
- 238000000034 method Methods 0.000 claims abstract description 40
- 239000011148 porous material Substances 0.000 claims abstract description 38
- 238000005477 sputtering target Methods 0.000 claims abstract description 37
- 238000004519 manufacturing process Methods 0.000 claims abstract description 21
- 239000000843 powder Substances 0.000 claims description 117
- 229910019974 CrSi Inorganic materials 0.000 claims description 58
- 238000010304 firing Methods 0.000 claims description 41
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims description 40
- 239000002994 raw material Substances 0.000 claims description 39
- 239000012298 atmosphere Substances 0.000 claims description 37
- 229910045601 alloy Inorganic materials 0.000 claims description 36
- 239000000956 alloy Substances 0.000 claims description 36
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 27
- 239000001301 oxygen Substances 0.000 claims description 27
- 229910052760 oxygen Inorganic materials 0.000 claims description 27
- 238000009689 gas atomisation Methods 0.000 claims description 24
- 239000000203 mixture Substances 0.000 claims description 18
- 238000002156 mixing Methods 0.000 claims description 13
- 229910021332 silicide Inorganic materials 0.000 claims description 13
- FVBUAEGBCNSCDD-UHFFFAOYSA-N silicide(4-) Chemical compound [Si-4] FVBUAEGBCNSCDD-UHFFFAOYSA-N 0.000 claims description 12
- 238000005452 bending Methods 0.000 claims description 8
- 238000007731 hot pressing Methods 0.000 claims description 3
- 239000010408 film Substances 0.000 description 57
- 239000013078 crystal Substances 0.000 description 50
- 239000007789 gas Substances 0.000 description 41
- 229910052751 metal Inorganic materials 0.000 description 35
- 239000002184 metal Substances 0.000 description 30
- 238000005259 measurement Methods 0.000 description 28
- 239000002245 particle Substances 0.000 description 21
- 238000004544 sputter deposition Methods 0.000 description 16
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 14
- 239000007858 starting material Substances 0.000 description 14
- 229910021357 chromium silicide Inorganic materials 0.000 description 13
- 238000002844 melting Methods 0.000 description 13
- 230000008018 melting Effects 0.000 description 13
- 229910003470 tongbaite Inorganic materials 0.000 description 13
- 230000015572 biosynthetic process Effects 0.000 description 12
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 12
- 239000012535 impurity Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 239000012528 membrane Substances 0.000 description 10
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 9
- 238000010586 diagram Methods 0.000 description 9
- 238000000137 annealing Methods 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 8
- 239000002243 precursor Substances 0.000 description 8
- 229910052786 argon Inorganic materials 0.000 description 7
- 239000012300 argon atmosphere Substances 0.000 description 7
- 239000002585 base Substances 0.000 description 6
- 239000011521 glass Substances 0.000 description 6
- 238000010191 image analysis Methods 0.000 description 6
- 229910019819 Cr—Si Inorganic materials 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 238000002441 X-ray diffraction Methods 0.000 description 5
- 238000010521 absorption reaction Methods 0.000 description 5
- 238000004458 analytical method Methods 0.000 description 5
- 238000002360 preparation method Methods 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 4
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 4
- 238000007580 dry-mixing Methods 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- -1 or (3) Cr Si 2 Inorganic materials 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 239000004065 semiconductor Substances 0.000 description 4
- 239000000758 substrate Substances 0.000 description 4
- 238000007088 Archimedes method Methods 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 238000001354 calcination Methods 0.000 description 3
- 239000011362 coarse particle Substances 0.000 description 3
- 238000000227 grinding Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000007751 thermal spraying Methods 0.000 description 3
- 239000010409 thin film Substances 0.000 description 3
- 229910052582 BN Inorganic materials 0.000 description 2
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 2
- 241000209094 Oryza Species 0.000 description 2
- 235000007164 Oryza sativa Nutrition 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- DYRBFMPPJATHRF-UHFFFAOYSA-N chromium silicon Chemical compound [Si].[Cr] DYRBFMPPJATHRF-UHFFFAOYSA-N 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000012790 confirmation Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000006837 decompression Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 238000007429 general method Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000000395 magnesium oxide Substances 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 235000009566 rice Nutrition 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 230000003746 surface roughness Effects 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 229910019878 Cr3Si Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 235000013339 cereals Nutrition 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000007772 electrode material Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052752 metalloid Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 229920000642 polymer Polymers 0.000 description 1
- 238000000634 powder X-ray diffraction Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000002285 radioactive effect Effects 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000011863 silicon-based powder Substances 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000009692 water atomization Methods 0.000 description 1
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Definitions
- the present invention relates to a Cr—Si—C based sintered body for film formation.
- silicides such as chromium silicide such as CrSi 2 have been used as a film (thin film) in many applications such as semiconductors and solar cells due to their characteristics.
- the sputtering method is widely used industrially as a method for producing a film, mainly a thin film.
- a composition containing silicide for example, a sintered body
- CrSi 2 generally has low strength
- a phenomenon such as cracking occurs during processing to a sputtering target and discharge of a film formation. .. Therefore, it is known that it is difficult to use a composition containing silicide as a sputtering target.
- Patent Document 1 a sputtering target of a crystal phase of Cr and Si (an alloy target mainly composed of a Cr phase and a Si phase) is manufactured by a thermal spraying method.
- the sputtering target produced by the thermal spraying method does not have sufficient strength in the composition region where the proportion of Cr is small.
- a sputtering target produced by a thermal spraying method using a powder of the silicide phase does not have sufficient strength.
- Patent Document 2 a composition having a fine eutectic structure is produced by a melting method.
- the composition obtained by the melting method has insufficient strength in a composition region in which the proportion of eutectic structure is small and the proportion of primary crystals (that is, the crystal phase having the highest proportion in the composition) is large. ..
- the size of such a composition is increased, it becomes difficult to control the crystal structure due to the difference in the cooling rate between the phases, and the unevenness of the strength of the composition as a whole becomes large.
- Patent Documents 3 and 4 do not mention a system containing a large amount of silicide.
- An object of the present invention is to provide a high-density Cr—Si—C-based sintered body containing chromium (Cr), silicon (Si), and carbon (C), and further to provide a high-density Cr—Si—C-based sintered body. It is an object of the present invention to provide at least one of a sintered body, a sputtering target including the sintered body, and a method for producing a film using the sputtering target.
- the present invention uses a Cr—Si—C-based sintered body in which particle generation is suppressed more than a conventional Cr—Si-based sintered body, a method for producing the same, a sputtering target containing the same, and the sputtering target. It is an object of the present invention to provide at least one of the methods for producing a membrane.
- the present inventors have diligently studied the Cr—Si—C-based sintered body and its manufacturing process. As a result, by using a quenching alloy powder (molten metal powder) such as gas atomize powder, a high-density Cr—Si—C-based sintered body can be obtained, and Cr—Si—C having a specific structure can be obtained. We have found that the generation of particles is suppressed when the system sintered body is used as a sputtering target, and have completed the present invention.
- a quenching alloy powder molten metal powder
- gas atomize powder molten metal powder
- Cr—Si—C having a specific structure can be obtained.
- the Cr—Si—C-based sintered body according to (1) or (2) which comprises chromium silicide and one or more selected from the group of chromium carbide, silicon carbide and carbon.
- the Cr—Si—C-based sintered body according to any one of (1) to (5) which has a bending strength of 100 MPa or more.
- the method for producing a Cr—Si—C-based sintered body according to any one of (1) to (6) which comprises a firing step of hot-pressing at a firing temperature of 1350 ° C. or higher and 1800 ° C. or lower at 50 MPa or less.
- a high-density Cr—Si—C-based sintered body containing chromium, silicon, and carbon is provided, and further, a high-density Cr—Si—C-based sintered body, a sputtering target containing the same, and the sputtering thereof.
- At least one of the methods for producing a membrane using a target can be provided.
- the Cr—Si—C-based sintered body of the present invention has a relative density of 90% or more, and when used as a sputtering target, there are few particles when used as a sputtering target, and higher productivity can be obtained. Is possible.
- the present invention uses a Cr—Si—C-based sintered body in which particle generation is suppressed more than a conventional Cr—Si-based sintered body, a method for producing the same, a sputtering target containing the same, and the sputtering target. It is possible to provide at least one of the methods for producing a membrane.
- the present invention is a Cr—Si—C-based sintered body containing chromium (Cr), silicon (Si), and carbon (C), in which the relative density of the sintered body is 90% or more and the pore ratio is 13% or less. It is a Cr—Si—C based sintered body characterized by being.
- the Cr—Si—C-based sintered body of the present invention (hereinafter, also referred to as “sintered body of the present invention”) is a sintered body containing chromium, silicon and carbon as main components, and is preferably chromium and silicon. And a sintered body made of carbon.
- the sintered body of the present invention preferably contains chromium silicide and one or more selected from the group of chromium carbide, silicon carbide and carbon.
- chromium silicide contained in the sintered body of the present invention one or more selected from the group of chromium mono silicide, di silicide and tri silicide, and further selected from the group of CrSi, CrSi 2 , Cr 3 Si and Cr 5 Si 3 1 Further, 1 or more selected from the group of CrSi, Cr 3 Si and Cr 5 Si 3 can be mentioned.
- the sintered body of the present invention may contain two or more chromium silicides, preferably two or more selected from the group of CrSi, CrSi 2 , Cr 3 Si and Cr 5 Si 3 , and CrSi, Cr 3 It is more preferable to contain 2 or more selected from the group of Si and Cr 5 Si 3 , and further preferably to contain Cr Si or Cr 3 Si and Cr 5 Si 3 .
- the sintered body of the present invention contains at least one of chromium carbide (Cr 3 C 2 ), silicon carbide (SiC) and carbon (C), further at least one of silicon carbide and carbon, and further silicon carbide. Is preferable.
- the sintered body of the present invention may be a sintered body composed of chromium silicide and one or more selected from the group of chromium carbide, silicon carbide and carbon, but in addition to these, silicon (Si) and It may contain at least one of chromium (Cr) and even silicon.
- the sintered body of the present invention preferably has chromium silicide as the main phase, more preferably one or more selected from the group of CrSi, CrSi 2 and Cr 3 Si as the main phase, and CrSi as the main phase. Is even more preferable.
- the main phase in the present invention is the crystal phase having the highest ratio in the crystal phase of the sintered body.
- the mass ratio of the crystal phase of the main phase to the mass of the sintered body is more than 50 wt%, 60 wt% or more, or It is mentioned that it is 70 wt% or more.
- the mass ratio (wt%) of chromium silicide to the sintered body of the present invention is 70 wt% or more or 75 wt% or more, and 80 wt% or less or 95 wt% or less.
- the crystal phase contained in the sintered body such as chromium silicide can be identified from the powder X-ray diffraction (hereinafter, also referred to as “XRD”) pattern.
- the XRD pattern can be measured by a general XRD device (for example, RINT Ultima III, manufactured by Rigaku). Examples of the XRD measurement conditions in the present invention include the following conditions.
- the relative density of the sintered body of the present invention is 90% or more, preferably 92% or more, more preferably 94% or more, and particularly preferably 96% or more. Further, the relative density may be 100% or less or 99% or less.
- a sintered body having a relative density lower than 90% a part of the sintered body is desorbed as coarse particles (that is, when a film is formed using the sintered body). , Particles are generated).
- coarse pores for example, pores having a maximum length of 50 ⁇ m or more; hereinafter also referred to as “coarse pores” are generated in the sintered body.
- particles are formed while adhering as a film (that is, a film incorporating the particles is formed).
- a film containing particles cannot be used because its physical properties and properties are non-uniform.
- a sintered body having a relative density lower than 90% reduces the productivity of the membrane.
- the "relative density” (%) in the present invention is the ratio of the measured density to the true density, and is a value obtained from (measured density [g / cm 3 ] / true density [g / cm 3 ]) ⁇ 100.
- the measured density is the bulk density obtained from the dry mass with respect to the volume measured by the Archimedes method in accordance with JIS R 1634.
- the pretreatment is preferably a boiling method, and the sintered body may be boiled in water.
- d is the true density [g / cm 3 ] of the sintered body, and M 1 to M 8 and R 1 to R 8 are Si, C, Cr, SiC, respectively contained in the sintered body.
- the ICDD numbers of each crystal phase are 00-026-1481 for Si, 00-026-1080 for C, 01-077-759 for Cr, 00-02-105 for SiC, and 03-065-3298 for CrSi.
- CrSi 2 is 01-072-6184
- Cr 3 C 2 is 01-071-2287
- Cr 5 Si 3 is 01-072-0347
- Cr 3 Si is 01-070-301.
- the mass ratio of each crystal phase is determined from the ratio of the crystal phase of the sintered body identified using the XRD) pattern measured under the above conditions and the elements (Cr, Si and C) constituting the sintered body. It is the required mass ratio [wt%] of each crystal phase.
- the crystal phases contained in the XRD pattern of the sintered body are CrSi, Cr5Si3 and SiC , and the composition of the sintered body obtained from the composition analysis is Cr is Xmol%, Si is Ymol% and When C is Z mol%, it is a mass ratio [wt%] obtained by multiplying the molar ratio [mol%] obtained from the following formula by the true density of each crystal phase.
- M CrSi is the molar ratio of CrSi [mol%]
- M Cr5Si3 is the molar ratio of Cr5Si3 [mol%]
- MSiC is the molar ratio of SiC [mol%].
- the true density of the sintered body of the present invention containing three kinds of crystal phases can be obtained from the following formula.
- d is the true density [g / cm 3 ] of the sintered body
- a, b and c are the masses [g] of the crystal phases A, B and C contained in the sintered body, respectively.
- Ma, Mb and Mc are true densities [g / cm 3 ] of the crystal phases A, B and C contained in the sintered body, respectively, and Ra, Rb and Rc are sintered respectively. It is the mass ratio [wt%] of the crystal phases A, B and C contained in the body.
- the crystal phases A, B and C are three types selected from the group of Si, C, Cr, SiC, CrSi, CrSi 2 , Cr 3 C 2 and Cr 5 Si 3 , and preferably (1) CrSi, Cr 5 Si 3 and SiC, (2) Cr 3 Si, Cr 5 Si 3 and SiC, or (3) Cr Si 2 , Si and C, more preferably Cr Si, Cr 5 Si 3 and SiC.
- the sintered body of the present invention is characterized in that the pore ratio is 13% or less.
- the pore ratio is preferably 8% or less, more preferably 6% or less, and particularly preferably 4% or less.
- the sintered body of the present invention may contain pores, but preferably does not contain pores (that is, the pore ratio is 0%), and the pore ratio of the sintered body of the present invention is 0% or more and more than 0%. , 0.5% or more or 1% or more.
- the "pore ratio" is the ratio of pores obtained from the observation diagram of the surface of the sintered body, and image analysis of the observation diagram of the surface of the sintered body having a surface roughness Ra ⁇ 0.02 ⁇ m. Percentage of pores measured by.
- the pore ratio can be obtained from the observation diagram of the surface of the sintered body having any state value before and after sputtering, but it is preferably obtained from the observation view of the surface of the sintered body having any state value before and after sputtering.
- the shape of the pore is arbitrary, and examples thereof include a substantially spherical shape, a substantially polyhedral shape, or an indefinite shape.
- the observation diagram may be any observation diagram obtained by laser microscope observation using a general laser microscope (for example, VX-250, manufactured by KEYENCE CORPORATION). The following conditions can be mentioned as observation conditions for laser microscope observation.
- Observation magnification 200 times Observation field of view: 5 fields or more, preferably 5 to 8 fields, More preferably 5 fields of view
- FIG. 1 shows one field of view of the observation diagram obtained by laser microscope observation.
- the pore ratio (%) of each visual field may be obtained as the ratio (%) of the black region to the total area of the black region and the white region in each observation map.
- the average value of the pore rate of each observed field of view may be used as the pore rate of the present invention.
- the image analysis may be performed by analyzing the obtained observation map with general-purpose image analysis software (for example, Image-Pro, manufactured by Media Cybernetics). The following conditions can be mentioned as image analysis conditions.
- the contrast ratio is a value that takes any of 0 to 100.
- Measurement field of view 5 or more fields of view, preferably 5 to 8 fields of view, More preferably 5 field of view contrast ratio: 100
- the sintered body of the present invention preferably has a silicon (Si) amount in the range of 20 to 70 wt%, more preferably 25 to 65 wt%, more preferably 30 to 60 wt%, still more preferably 35 to 55 wt%. Is.
- Si silicon
- the amount of silicon is lower than 20 wt%, the amount of the semiconductor phase (that is, the SiC phase and the Si phase) of the entire sintered body tends to be small, and the temperature change of the resistivity tends to be large.
- the amount of silicon is higher than 70 wt%, and further, when the amount of silicon is higher than 50 wt%, the amount of the semiconductor phase is large, and the temperature change of the resistivity of the obtained film tends to be large.
- the preferable amount of silicon in the sintered body of the present invention is 20 wt% or more, 25 wt% or more or 30 wt% or more, and 70 wt% or less, 65 wt% or less, 50 wt% or less, 45 wt% or less or 40 wt% or less. Can be mentioned.
- the amount of silicon in the sintered body of the present invention is the mass ratio (wt%) of silicon to the mass of the sintered body of the present invention obtained by mass measurement.
- the silicon contained in the sintered body of the present invention can be measured by a general method used in the present technology, and examples thereof include measurement by ICP analysis.
- the sintered body of the present invention preferably has a carbon (C) amount in the range of 1 to 20 wt%, more preferably 1 to 15 wt%, still more preferably 1 to 10 wt%, still more preferably 5 to 10 wt%. be.
- C carbon
- the amount of carbon is lower than 1 wt%, the temperature change characteristic of the resistivity of the film is not improved (that is, the temperature dependence is unlikely to be reduced).
- the amount of carbon is more than 20 wt%, the amount of the SiC phase showing a high resistivity close to the insulating property tends to increase in the sintered body, which tends to cause particles to be generated when the SiC phase discharges DC. ..
- Preferred carbon amounts of the sintered body of the present invention include 1 wt% or more, 3 wt% or more or 4 wt% or more, and 20 wt% or less, 15 wt% or less, 10 wt% or less or 9 wt% or less.
- the carbon content in the sintered body of the present invention is the mass ratio (wt%) of carbon to the mass of the sintered body.
- Carbon can be measured by common methods used in the art, for example, combustion-infrared absorption using a common carbon / sulfur analyzer (eg, LECO-CS844 carbon / sulfur analyzer). Can be exemplified by measuring carbon.
- the balance of silicon and carbon may be chromium, and the chromium content of the sintered body of the present invention is more than 10 wt% and less than 79 wt%, further 15 to 75 wt%, and further. It can be exemplified that it is 35 to 70 wt%. Further, preferable composition ranges of the sintered body of the present invention include 1 to 20 wt% of carbon, 20 to 70 wt% of silicon, and chromium in the balance.
- the metal elements (including metalloid elements; the same shall apply hereinafter in the present specification) contained in the sintered body of the present invention are preferably chromium and silicon.
- the sintered body of the present invention may contain metal impurities such as iron (Fe) and aluminum (Al) in addition to chromium (Cr), silicon (Si) and carbon (C).
- Metallic elements such as iron and aluminum are included as unavoidable impurities. That is, the sintered body of the present invention may contain unavoidable impurities, and may contain metal impurities (metal elements other than chromium and silicon) as unavoidable impurities, and iron and aluminum as unavoidable impurities.
- the total amount of these metal impurities may be 1 wt% or less, preferably 0.5 wt% or less, and more preferably 0.3 wt% or less.
- the sintered body of the present invention preferably does not contain metal impurities, and it can be exemplified that the total amount of metal elements other than chromium and silicon is 0 wt% or more, more than 0 wt%, or 0.1 wt% or more.
- the sintered body of the present invention may contain oxygen as long as it does not deteriorate the characteristics when it is used as a sputtering target.
- the amount of oxygen (O) in the sintered body of the present invention is preferably small, for example, preferably 1 wt% or less. When the amount of oxygen is more than 1 wt%, a large amount of insulating oxide-derived particles are likely to be generated during the film formation. More preferably, the oxygen content of the sintered body of the present invention is 0.5 wt% or less, and particularly preferably 0.1 wt% or less.
- the sintered body of the present invention preferably does not contain oxygen (that is, the amount of oxygen is 0 wt%), but it can be exemplified that it is more than 0 wt% or 0.01 wt% or more.
- the amount of oxygen in the sintered body of the present invention is the mass ratio (wt%) of oxygen to the mass of the sintered body.
- Oxygen contained in the sintered body of the present invention can be measured by a general method used in the present art.
- the oxygen content can be measured by analysis by the Inactive Gas Melting-Infrared Absorption Method.
- a general oxygen / nitrogen analyzer for example, LECO-ON736 oxygen / nitrogen analyzer
- the sintered body of the present invention may have an arbitrary shape according to the purpose, for example, from a group of disc-shaped, columnar, plate-shaped, rectangular parallelepiped, cube-shaped, polyhedral-shaped, and substantially polyhedral-shaped. One or more selected.
- the sintered body of the present invention preferably has a bending strength of 100 MPa or more, and particularly preferably 150 MPa or more. Since the bending strength is within this range, even when the sintered body of the present invention is manufactured as a sintered body having a large size exceeding 300 mm, the risk of cracking during processing and the occurrence of defects during processing are reduced. Further, it becomes easy to suppress the occurrence of defects such as cracks when used as a sputtering target. It can be exemplified that the bending strength of the sintered body of the present invention is 300 MPa or less, 250 MPa or 200 MPa or less. The bending strength in the present invention may be measured by a method according to JIS R 1601.
- a preferred embodiment of the sintered body of the present invention is a sintered body having a pore ratio of 13% or less and containing chrome silicide and one or more selected from the group of chrome carbide, silicon carbide and carbon.
- the pore ratio is 11% or less, 10% or less or 6% or less, and preferably 0% or more, more than 0% or 0.3% or more.
- the chromium silicide preferably contains 2 or more selected from the group of CrSi, CrSi 2 , Cr 3 Si and Cr 5 Si 3 , and further contains 1 or more selected from the group of CrSi, CrSi 2 and Cr 3 Si. More preferably, CrSi and Cr 3 Si, and Cr 5 Si 3 are more preferable.
- the sintered body contains CrSi and Cr3Si and silicon carbide. Furthermore, it is preferable that the sintered body has a relative density of 90% or more, and more preferably 93% or more and 100% or less. Further, the sintered body preferably has a bending strength of 150 MPa or more and 250 MPa or less, and more preferably 180 MPa or more and 220 MPa or less.
- the method for producing a sintered body of the present invention is to mix powders using chromium, silicon, and carbon (1) in the process of preparing alloy raw material powder, and the obtained alloy raw material powder is pressured at 50 MPa using a pressure firing furnace such as a hot press furnace.
- a pressure firing furnace such as a hot press furnace.
- it can be produced by a step including (2) firing step of firing at a firing temperature of 1200 ° C to 1800 ° C.
- the raw materials used in the alloy raw material preparation process are chromium, silicon and carbon.
- the chromium is preferably high-purity chromium, and examples thereof include 3N (purity 99.9% or more) and 4N (purity 99.99% or more) chromium.
- the silicon is preferably high-purity silicon, for example, 3N (purity 99.9% or more), 4N (purity 99.99% or more), and further 5N (purity 99.99% or more), respectively. It can be mentioned that it is silicon.
- the carbon (carbon source) may be carbon (C) or a compound thereof, and is preferably a carbide of at least one of chromium and silicon, and is chromium carbide (Cr 3 C 2 ), silicon carbide (SiC), and carbon.
- chromium carbide Cr 3 C 2
- silicon carbide SiC
- One or more selected from the group (C), and at least one of chrome carbide and silicon carbide can be mentioned.
- Chromium carbide and silicon carbide can also be considered as starting materials for chromium and silicon, respectively.
- the starting material for example, chromium (Cr), silicon (Si), chromium carbide (Cr 3C 2 ), silicon carbide (SiC), and carbon (C) can be used. Further, the starting material may contain an alloy of chromium and silicon in addition to chromium and silicon, or instead of chromium and silicon, and preferably contains a molten metal powder of chromium and silicon.
- the "molten metal powder” is a powder in which the molten metal is cooled, and further, a powder in which the molten metal is rapidly cooled, and is a powder having a fine structure.
- the molten metal powder for example, a powder obtained by one or more selected from the group of quenching ribbon, arc melting, gas atomizing, water atomizing, centrifugal atomizing and vacuum atomizing, and further selected from the group of quenching ribbon, arc melting and gas atomizing. Examples include the powder obtained by one or more of the above, and further the powder obtained by gas atomization. Since the molten metal powder is a powder obtained without requiring a crushing step and further without going through a crushing step, the amount of impurities tends to be smaller than that of the powder obtained through the crushing step.
- the starting material preferably contains a powder obtained by gas atomization (hereinafter, also referred to as "gas atomizing powder”), and particularly preferably contains a gas atomizing powder of chromium and silicon.
- gas atomizing powder obtained by gas atomization
- the particles produced by the gas atomizing method have a spherical shape of about several tens of ⁇ m and have a fine crystal phase in the spherical shape. Since the gas atomized powder is a powder having a small surface surface and composed of fine particles, the sintered body after firing has low oxygen and high strength, that is, the amount of oxygen is small, and the sintered body has high strength. Can be provided as an alloy raw material powder obtained.
- the gas atomized powder is, for example, a powder having an average particle diameter of 5 ⁇ m or more and 100 ⁇ m or less, a powder having at least one of spherical and substantially spherical shapes, and composed of polycrystalline particles of chromium silicide. It can be exemplified as a powder, further, a powder composed of particles containing polycrystals of chromium silicide having different crystal phases from each other.
- the gas atomized powder preferably contains at least CrSi 2 in the crystal phase, and may contain at least one selected from the group of Si, Cr, CrSi, Cr 3 C 2 and Cr 5 Si 3 and CrSi 2 in the crystal phase. It is more preferable that at least one of Si and CrSi and CrSi 2 are contained in the crystal phase.
- the conditions of the gas atomizing method are arbitrary, but for example, the treatment temperature for melting chromium and silicon is preferably a melting temperature of +50 to 300 ° C, and more preferably a melting temperature of +100 to 250 ° C. As a result, a molten metal, that is, a metal in a liquid state, is obtained.
- the “melting temperature” is the temperature at which a precursor substance such as a raw material powder of chromium or silicon or flakes melts, and is a value peculiar to the substance.
- the melting temperature 1300 ° C. to 1500 ° C. can be exemplified. Therefore, the treatment temperature can be exemplified by 1350 ° C. or higher and 1800 ° C. or lower, and may be 1350 ° C. or higher, 1370 ° C. or higher or 1390 ° C. or higher, and 1800 ° C. or lower, 1700 ° C. or lower, 1550 ° C. or lower or 1470 ° C. or lower. Can be mentioned.
- the difference between the melting temperature and the processing temperature is small (for example, when the difference is less than 50 ° C.), the one with the higher melting point of the two-phase crystal phase precipitates first, and the alloy particles constituting the obtained powder are fine. It is difficult to change.
- the difference between the melting temperature and the processing temperature is large, the particles are sintered after atomization, and the particles adhere to the wall surface of the gas atomizing device, resulting in poor powder recovery rate (yield is poor).
- a precursor that can obtain a gas atomizing powder of chromium and silicon to be used as a starting material may be provided.
- the precursor may be at least one of chromium and silicon and a compound thereof, and may be chromium and silicon powder, flakes or bulk, preferably chromium and silicon flakes.
- the chromium precursor is preferably a high-purity chromium frame, and may be, for example, 3N (purity 99.9% or higher) and even 4N (purity 99.99% or higher) chromium flakes. ..
- the precursor of silicon is preferably high-purity silicon flakes, for example, 3N (purity 99.9% or higher), 4N (purity 99.99% or higher), and further 5N (purity 99% or higher), respectively. .999% or more) of silicon flakes.
- the gas atomizing powder is obtained by dropping the obtained molten metal into the gas stream so as to pass through the gas stream.
- the gas flow may be an inert gas, and examples thereof include one or more selected from the group of argon (Ar), nitrogen (N 2 ) and helium (He), and further, argon.
- the pressure of the gas flow (hereinafter, also referred to as “gas pressure”) may be 1 MPa or more, 4 MPa or more, or 6 MPa or more, and may be 10 MPa or less, further 9 MPa or less.
- the gas atomizing method may be at least one of a crucible type and an electrode type, and is preferably a crucible type.
- the crucible used in the gas atomization method by the crucible method is selected from, for example, a crucible consisting of one or more selected from the group of carbon, alumina, magnesia, silicon nitride, zirconia and boron nitride, or a group of carbon, alumina, magnesia and zirconia. It is preferable that the crucible is a crucible in which at least one of boron nitride and silicon carbide is coated on a main body composed of one or more.
- the powder after gas atomization (gas atomized powder) is preferably managed (stored) in a vacuum atmosphere or in an inert atmosphere such as nitrogen or argon, and is preferably not exposed to an oxidizing atmosphere before being subjected to the subsequent firing step. ..
- an oxidizing atmosphere such as by placing the powder in the atmosphere, oxidation occurs from the surface of the atomized powder, and the amount of oxygen in the powder increases.
- a mixed powder obtained by mixing chromium and silicon by a powder mixing method is used as a starting material for a sintered body.
- a high-strength sintered body can be produced even in fine powder mixing (physical mixing of fine powder).
- the sintered body obtained by firing the powder obtained by this method has a large amount of oxygen.
- by mixing the coarse particles physical mixing of the powder containing the coarse particles
- Examples of the method for producing other raw materials (molten metal powder) include rapid cooling methods such as quenching thin band and arc melting.
- the amount of oxygen in the starting material is small.
- the amount of oxygen in the starting material is large, the amount of oxygen in the sputtering target using the sintered body of the present invention is large. Such a large amount of oxygen tends to cause the generation of particles.
- the starting material preferably has an oxygen content of 0.5 wt% or less, more preferably 0.1 wt% or less, and can be exemplified to be 0 wt% or more, more than 0 wt%, or 0.01 wt% or more, respectively.
- Particularly preferable starting materials to be used in the alloy raw material preparation step include chromium and silicon gas atomized powder, chromium and silicon carbide, chromium and silicon gas atomized powder, and chromium carbide.
- the shape of the starting material is arbitrary, but may be powder.
- the powder (starting raw material) may be mixed by any method as long as the starting raw materials are uniformly mixed, and any mixer such as a V-type mixer or a mixer can be used.
- the mixing method may be at least one of dry mixing and wet mixing, and dry mixing is preferable, and dry mixing using a V-type mixer is more preferable. As a result, an alloy raw material powder can be obtained.
- the mixed atmosphere is preferably an atmosphere in which the starting material is not easily oxidized, and examples thereof include at least one of a vacuum atmosphere and an inert atmosphere, further at least one of a nitrogen atmosphere and an argon atmosphere, and further an argon atmosphere.
- the mixing speed such as the rotation speed and stirring speed of the mixer, is 10 rpm or more and 200 rpm or less, and further 50 rpm or more and 100 rpm or less. Further, the mixing time may be 30 minutes or more and 5 hours or less, and further 45 minutes or more and 3 hours or less.
- the purity of the raw material (alloy raw material powder) obtained in the alloy raw material preparation step is preferably 99% or more, more preferably 99.9% or more.
- the impurities are likely to cause abnormal grain growth in the firing step.
- the abnormally grown particles tend to be a source of particles at the time of film formation.
- a molten metal powder of chromium and silicon (a molten alloy powder of chromium silicon) and a starting material containing a carbon source are mixed at least in either a vacuum atmosphere or an inert atmosphere to obtain an alloy raw material powder.
- the process of obtaining is mentioned.
- the molten metal powder is preferably a gas atomized powder of chromium and silicon.
- the carbon source preferably contains a carbide containing at least one of chromium and silicon, more preferably at least one of chromium carbide (Cr 3 C 2 ) and silicon carbide (SiC), and is chromium carbide. Is more preferable.
- the obtained alloy raw material powder is calcined using a pressure calcining furnace such as a hot press furnace at a pressure of 50 MPa or less and a calcining temperature of 1200 ° C. to 1800 ° C.
- a pressure firing furnace such as a hot press furnace. Since the diffusion coefficient of silicon is low, it is difficult to increase the density of the obtained sintered body in a non-pressurized furnace.
- the alloy raw material powder is fired by pressure firing. Examples of the pressure firing in the step include at least one of a hot press and a hot hydrostatic pressure press, preferably a hot press.
- the hot press pressure during firing (hereinafter, also simply referred to as “pressure”) is preferably 50 MPa or less. If it exceeds 50 MPa, it is difficult to prepare a hot press mold (press die) that can be pressurized (it is difficult to use a general-purpose mold). A carbon mold can be exemplified as a general-purpose mold.
- the hot press pressure is preferably 5 to 45 MPa, more preferably 10 to 40 MPa, and particularly preferably 15 to 40 MPa.
- the preferable hot press pressure is 5 MPa or more, 10 MPa or more or 15 MPa or more, and 50 MPa or less, 45 MPa or less or 40 MPa or less.
- the firing temperature is 1350 ° C to 1800 ° C. Below 1350 ° C, the density of the obtained sintered body does not increase sufficiently. On the other hand, if the firing temperature exceeds 1800 ° C., the material (sintered body) may be melted during firing.
- Particularly preferable firing temperatures include 1300 ° C. or higher, 1325 ° C. or higher, or 1350 ° C. or higher, and 1800 ° C. or lower, 1600 ° C. or lower, or 1400 ° C. or lower.
- the temperature raising rate and the temperature lowering rate are not particularly limited, and can be appropriately determined in consideration of the volume of the firing furnace, the size and shape of the sintered body, the fragility, and the like.
- the rate of temperature rise may be, for example, 100 ° C./hour or more or 150 ° C./hour or more, and 300 ° C./hour or less or 250 hours or less.
- the holding time at the time of firing is 1 to 5 hours, and further, 1.5 hours or more and 3.5 hours or less.
- the firing atmosphere is preferably a vacuum atmosphere, a vacuum reduced pressure atmosphere, or an inert atmosphere such as argon, more preferably an argon atmosphere or a vacuum atmosphere, and even more preferably a vacuum atmosphere.
- a particularly preferable firing step is a step of pressure firing the alloy raw material powder in a vacuum atmosphere at a pressure of 50 MPa or less and a firing temperature of 1350 ° C. or higher and 1800 ° C. or lower.
- the pressure firing is preferably a hot press treatment
- the alloy raw material powder preferably contains a molten metal powder of chromium and silicon, and the molten metal powder of chromium and silicon and at least one of chromium and silicon. It is more preferable that the powder composition contains the carbides of the above.
- a step of mixing a gas atomizing powder of chromium and silicon and a carbon source containing at least one of chromium and silicon and carbon to obtain an alloy raw material powder and A production method comprising a firing step of hot-pressing the alloy raw material powder in a vacuum atmosphere at a pressure of 50 MPa or less and a firing temperature of 1350 ° C. or higher and 1800 ° C. or lower can be mentioned.
- the carbon source is preferably a carbide containing at least one of chromium and silicon, and more preferably chromium carbide.
- the sintered body of the present invention can be ground into a plate shape using a machining machine such as a surface grinding machine, a cylindrical grinding machine, a lathe, a cutting machine, and a machining center. As a result, any shape may be obtained according to the purpose.
- a machining machine such as a surface grinding machine, a cylindrical grinding machine, a lathe, a cutting machine, and a machining center.
- the sintered body of the present invention can be used for known silicide applications such as structural materials, electrode materials and semiconductor materials, and is particularly preferable to be used as a sputtering target (hereinafter, also simply referred to as “target”). .. It can be a sputtering target made of the sintered body of the present invention.
- the method for manufacturing the sputtering target is arbitrary, and the sintered body of the present invention may be used as it is as the sputtering target. Further, if necessary, a backing plate made of oxygen-free copper, titanium, etc., and an indium solder or the like are used for the backing tube, and the sintered body of the present invention and the backing plate are bonded to each other to form the present invention.
- the sintered body can be a sputtering target.
- the sintered body of the present invention can be a sputtering target provided with the sintered body of the present invention, a backing plate and a backing tube, and a method for producing a film, which is sputtering using the sputtering target. Can be used for.
- Sputtering conditions are arbitrary, but for example, the following conditions can be mentioned.
- Film formation power 100W or more and 800W or less, Preferably, 150 W or more and 300 W or less Gas pressure: 0.2 Pa or more and 1.0 Pa or less, Preferably 0.3 Pa or more and 0.7 Pa or less Gas atmosphere: Inactive atmosphere, preferably argon atmosphere Film formation time: 0.5 hours or more and 3 hours or less, Preferably 0.5 hours or more and 1.5 hours or less
- the film after sputtering In order to reduce the temperature dependence of resistivity, it is preferable to heat-treat (anneal) the film after sputtering.
- the following conditions can be mentioned as the conditions for the annealing treatment.
- Annealing atmosphere Vacuum atmosphere Annealing time: 1 hour Annealing temperature: Any temperature from 200 ° C to 600 ° C
- the film obtained by using the sintered body of the present invention may have an arbitrary thickness, and for example, the film thickness may be 5 nm or more or 10 nm or more. It is also mentioned that it is 1 ⁇ m or less or 500 nm or less.
- the film of the present invention is a Si—Cr—C-based film, which is an amorphous film containing chrome silicide and one or more selected from the group of chrome carbide, silicon carbide and carbon, and preferably chrome silicide. , Silicon carbide or carbon amorphous film.
- the film of the present invention is a film existing on the substrate, that is, a film formed on the substrate, and is particularly a sputtered film. Therefore, the film of the present invention is different from the self-standing film, and can be regarded as a laminated body in which the film of the present invention and the base material are laminated.
- the base material may be a base material made of any material according to the purpose, and is a base material made of one or more selected from the group of metal, semi-metal, ceramics, glass and polymer, and further metal, semi-metal. And a base material made of one or more selected from the group of glass, and further, a base material made of glass.
- the film of the present invention preferably has a small rate of change in resistivity when the temperature of the film changes by 1 ° C., that is, a so-called temperature coefficient of resistance (Temperature Cofficient of Resistance; hereinafter, also referred to as “TCR”), and the measurement temperature is 40. It is preferable that the maximum value of TCR at ° C. to 150 ° C. (hereinafter, also referred to as “maximum TCR”) is 100 ppm / ° C. or lower or 98 ppm / ° C. or lower.
- the minimum value of TCR at the measurement temperature of 40 ° C. to 150 ° C. (hereinafter, also referred to as “minimum TCR”) is ⁇ 25 ppm / ° C. or higher or 0 ppm / ° C. or higher.
- the TCR uses the resistivity value of the membrane measured using a general resistivity measuring device (for example, 8403 type AC / DC Hall measuring system, manufactured by Toyo Corporation), and the following equation is used. Can be obtained from.
- a general resistivity measuring device for example, 8403 type AC / DC Hall measuring system, manufactured by Toyo Corporation
- TCR (R-R 30 ) / ⁇ R 30 x (T-30) ⁇ x 10 6
- TCR is the temperature coefficient of resistance [ppm / ° C]
- R is the resistivity at the measured temperature [ ⁇ ⁇ cm]
- R 30 is the resistivity at 30 ° C. [ ⁇ ⁇ cm]
- T is the measured temperature [° C.].
- the film of the present invention preferably has an average TCR value (hereinafter, also referred to as “average TCR”) at a measurement temperature of 40 ° C. to 150 ° C. of 100 ppm / ° C. or lower, 50 ppm / ° C. or lower, or 15 ppm / ° C. or lower.
- the average TCR may be 0 ppm / ° C. or higher, 1 ppm / ° C. or higher, or 10 ppm / ° C. or higher.
- TCR 40 is the absolute value of TCR [ppm / ° C] at the measurement temperature of 40 ° C
- TCR 50 is the absolute value of TCR at the measurement temperature of 50 ° C [ppm / ° C]. Absolute value of TCR at temperature [ppm / ° C].
- the membrane of the present invention has a linear inclination (hereinafter, also referred to as "TCR inclination”) of a linear approximation formula (straight line approximation) obtained from 13 points of TCR plots measured in a temperature range of 30 ° C to 150 ° C at 10 ° C intervals. ) Is preferably ⁇ 0.7 ppm / ° C 2 , ⁇ 0.5 ppm / ° C 2 , ⁇ 0.3 ppm / ° C 2 , ⁇ 0.2 ppm / ° C 2 , ⁇ 0.1 ppm / ° C 2 or 0 (.). Zero) ppm / ° C. 2 is preferable.
- TCR inclination is within this range, the detection sensitivity in a sensor application used in an environment with a large temperature change such as an in-vehicle sensor is stable.
- Crystal phase of sintered body The crystal phase of the sintered body was measured and identified by measuring and identifying an XRD pattern under the above-mentioned conditions.
- d is the true density [g / cm 3 ] of the sintered body
- M 1 to M 9 and R 1 to R 9 are Si, C, Cr, respectively contained in the sintered body.
- the crystal phase contained in the sintered body identified the XRD pattern measured under the above conditions, and the composition of the sintered body was determined by ICP analysis. The mass ratio of each crystal phase was determined from the measured element and the obtained crystal phase.
- the true density of the sintered body is the mass a [g] of the crystal phase A, the mass b [g] of the crystal phase B, and the mass c [g] of the crystal phase C.
- Pore rate of the sintered body The surface was polished, observed with a laser microscope, and measured from the obtained sintered body structure image by image analysis. Mirror polishing was performed using DP-suspension 1 ⁇ m (manufactured by Marumoto Strial Co., Ltd.) so that the surface roughness Ra ⁇ 2 ⁇ m. Observe at least any 5 fields of view, calculate the pore area from image analysis, measure the pore rate 5 times (that is, once for each field of view), and average the measurement results of the pore rate of each field of view. Was taken as the pore rate.
- a sintered body having a diameter of 10.16 cm was cut out from an arbitrary place of the sintered body, and In bonding was performed to use it as a sputtering target.
- a sputtering test was performed under the following conditions, and the number of holes having a maximum target length of 50 ⁇ m or more after sputtering was counted with a laser microscope to obtain coarse holes.
- Oxygen content After grinding the surface of the sintered body by 1 mm or more, the oxygen content in the sample (square shape with a length of 3 mm, a width of 20 mm, and a thickness of 4 mm) cut out from an arbitrary part of the sintered body is determined. Measured by melting-infrared absorption method.
- Example 1 Cr flakes (4N): 33 wt% and Si flakes (5N): 67 wt% were used as precursors. Cr flakes and Si flakes were melted in a carbon crucible at a treatment temperature of 1650 ° C. to obtain molten metals of chromium and silicon. Then, a powder (gas atomized powder) was prepared by a gas atomizing method in which the molten metal was dropped so as to pass an argon gas stream having a gas pressure of 7 MPa, and this was used as a starting material for chromium and silicon. The gas atomized powder had a crystal phase composed of CrSi 2 and Si.
- this alloy raw material powder was placed in a carbon mold (press die: diameter 15.2 cm) and fired by a hot press method to obtain a sintered body of this example.
- the firing conditions are shown below.
- Baking furnace Hot press furnace Temperature rise rate: 200 ° C / hour Temperature rise atmosphere: Vacuum depressurization atmosphere (vacuum atmosphere) Firing atmosphere: Vacuum decompression atmosphere (vacuum atmosphere) Baking temperature: 1350 ° C Pressure: 40MPa Baking time: 3 hours
- the sintered body of this example was a Cr — Si—C based sintered body composed of CrSi, Cr5Si3 and SiC.
- the relative densities of the sintered body of this example were 52 wt% for crystal phase A: CrSi (true density 5.36 [g / cm 3 ]) and crystal phase B: Cr 5 Si 3 (true density 5.36 [g / cm 3]).
- the true density was calculated using 27 wt% of true density 5.87 / cm 3 ]) and 21 wt% of crystal phase C: SiC (true density 3.21 / cm 3 ]).
- Example 2 A sintered body (Cr—Si—C-based sintered body) was produced in the same manner as in Example 1 except that the firing conditions were changed to the conditions shown in Table 1.
- the obtained sintered bodies were all Cr — Si—C based sintered bodies composed of CrSi, Cr5Si3 and SiC.
- Example 8 Cr flakes (4N): 59 wt% and Si flakes (5N): 41 wt% were used as precursors.
- the treatment temperature was set to 1650 ° C. and these were melted to obtain a molten metal.
- a gas atomizing powder was produced by a gas atomizing method by dropping the molten metal so as to pass an argon gas stream having a gas pressure of 7 MPa.
- the gas atomized powder had a crystal phase composed of CrSi 2 and CrSi.
- the Cr 3 C 2 powder and the gas atomized powder were mixed in the same manner as in Example 1 except that the Cr 3 C 2 powder was mixed so that the gas atomized powder was 62 wt% and the Cr 3 C 2 powder was 36 wt%, and the Cr was 69 wt%.
- Si was 26 wt%
- C was 5 wt% as the alloy raw material powder of this example.
- a Cr—Si—C-based sintered body was obtained by firing in the same manner as in Example 1 except that the alloy raw material powder was used, and this was used as the sintered body of this example. From the results of the XRD measurement, the relative density of the sintered body is 23 wt% for the crystal phase A: Cr 5 Si 3 (true density 5.87 [g / cm 3 ]) and the crystal phase B: Cr 3 Si (true density 6). It was calculated using the true density calculated as 61 wt% for .46 / cm 3 ]) and 16 wt% for the crystal phase C: SiC (true density 3.21 / cm 3 ]).
- Example 9 Cr flakes (4N): 42 wt% and Si flakes (5N): 58 wt% were used as precursors.
- the treatment temperature was set to 1650 ° C. and these were melted to obtain a molten metal.
- a gas atomizing powder was produced by a gas atomizing method by dropping the molten metal so as to pass an argon gas stream having a gas pressure of 7 MPa.
- the gas atomized powder had a crystal phase composed of CrSi 2 and Si.
- the C powder and the gas atomized powder were mixed in the same manner as in Example 1 except that the C powder and the gas atomized powder were mixed so that the gas atomized powder was 95 wt% and the C powder was 5 wt%.
- Cr was 40 wt% and Si was 55 wt%. And, it was used as the alloy raw material powder of this example in which C was 5 wt%.
- a disk-shaped sintered body having a diameter of 15.2 cm and a thickness of 7 mm and having no microcracks was obtained by firing in the same manner as in Example 1 except that the alloy raw material powder was used. This was used as the sintered body of this example.
- the sintered body of this example was a Cr—Si—C based sintered body composed of CrSi 2 , Si and C. From the results of the XRD measurement results, the relative density of the sintered body of this example was calculated using the true density calculated assuming that CrSi 2 is 83 wt%, Si is 12 wt%, and C is 5 wt%.
- Example 10 In this example, Cr is 36 wt%, Si is 49 wt%, and C is 15 wt% by the same method as in Example 9 except that C powder and gas atomized powder are mixed so that C powder is 15 wt%. Was used as the alloy raw material powder.
- a disk-shaped sintered body having a diameter of 15.2 cm and a thickness of 7 mm and having no microcracks was obtained by firing in the same manner as in Example 1 except that the alloy raw material powder was used. rice field. From the results of the XRD measurement, it was confirmed that the sintered body of this example was a Cr—Si—C based sintered body composed of CrSi 2 , Si and C. From the results of the XRD measurement results, the relative density of the sintered body of this example was calculated using the true density calculated as 74 wt% for CrSi 2 , 11 wt% for Si, and 15 wt% for C.
- Comparative Example 2 By the same method as in Example 9, a gas atomized powder having 42 wt% Cr and 58 wt% Si and having a crystal phase composed of CrSi 2 and Si was obtained.
- a sintered body was prepared by the same method as in Comparative Example 1 except that the gas atomized powder was used, the firing temperature was set to 1250 ° C, and the pressure was set to 15 MPa.
- the sintered body of this example was a Cr—Si-based sintered body composed of CrSi 2 and Si (a sintered body of chromium silicide). From the measurement result of the XRD and the result of the composition analysis by ICP, the relative density of the sintered body of this comparative example was calculated using the true density calculated assuming that CrSi 2 was 87 wt% and Si was 13 wt%.
- Table 1 shows the production conditions of Examples 1 to 10 and Comparative Examples 1 and 2, and Table 2 shows the evaluation results of the obtained sintered body.
- the film was formed multiple times to obtain multiple films (sputtering films).
- the obtained membranes sputtering membranes
- a plurality of sputtering films having a film thickness of 100 nm were obtained for each example.
- the film after the annealing treatment was evaluated under the following conditions.
- the resistivity of the film was measured at 30 ° C. using an 8403 type AC / DC Hall measuring system (manufactured by Toyo Corporation). The measurement was performed on a glass substrate provided with a sputtering film cut out at a 1 cm square.
- TCR The resistivity of the film was measured from 30 ° C. to 150 ° C. at 10 ° C. intervals, and the TCR at each temperature was obtained from the following formula.
- TCR (ppm / ° C) (R-R 30 ) / (R 30 x (T-30)) x 10 6
- the maximum value was the maximum TCR
- the minimum value was the minimum TCR
- the average of the absolute values of TCR was the average TCR.
- TCR tilt The value of TCR of 40 ° C. to 150 ° C. obtained by the measurement of TCR was plotted by temperature ⁇ TCR, and the linear approximation formula obtained from the plot was obtained. The value of the slope of the linear approximation formula was taken as the TCR slope.
- the table below shows the annealing temperature at which the average TCR value became the smallest, and the evaluation results of the film after annealing at the annealing temperature.
- Comparative Example 2 has a higher relative density and a lower pore ratio than the Examples, the obtained film has a large TCR slope and a large change in resistivity with respect to temperature. ..
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Abstract
Description
さらに、シリサイド相が脆いことから、特許文献3及び4ではシリサイドを多く含む系については言及がない。
(1) クロム(Cr)、シリコン(Si)、カーボン(C)を含むCr-Si-C系焼結体であり、焼結体の相対密度が90%以上かつ、ポア率が13%以下であることを特徴とするCr-Si-C系焼結体。
(2) 組成範囲としてカーボンが1~20wt%、シリコンが20~70wt%、残部がクロムである(1)に記載のCr-Si-C系焼結体。
(3) クロムシリサイドと、クロムカーバイド、シリコンカーバイド及びカーボンの群から選ばれる1以上と、を含む(1)又は(2)に記載のCr-Si-C系焼結体。
(4) CrSi、CrSi2及びCr3Siの群から選ばれる1以上を主相とする(1)乃至(3)のいずれかひとつに記載のCr-Si-C系焼結体。
(5) 酸素量が1wt%以下である(1)乃至(4)のいずれかひとつに記載のCr-Si-C系焼結体。
(7) クロム及びシリコンのガスアトマイズ粉末、並びに、クロム及びシリコンの少なくともいずれかとカーボンとを含むカーボン源と、を混合して合金原料粉末を得る工程、及び、該合金原料粉末を真空雰囲気で、圧力50MPa以下、及び、焼成温度1350℃以上1800℃以下で、ホットプレスする焼成工程、を有する(1)乃至(6)のいずれかひとつに記載のCr-Si-C系焼結体の製造方法。
(8) 前記カーボン源は、クロム及びシリコンの少なくともいずれかを含む炭化物である(7)に記載の製造方法。
(9) (1)乃至(6)のいずれかひとつに記載のCr-Si-C系焼結体からなるスパッタリングターゲット。
(10) (9)に記載のスパッタリングターゲットを用いてスパッタリングする膜の製造方法。
本発明は、クロム(Cr)、シリコン(Si)、カーボン(C)を含むCr-Si-C系焼結体であり、焼結体の相対密度が90%以上かつ、ポア率が13%以下であることを特徴とするCr-Si-C系焼結体である。
本発明のCr-Si-C系焼結体(以下、「本発明の焼結体」ともいう。)は、クロム、シリコン及びカーボンを主成分とする焼結体であり、好ましくはクロム、シリコン及びカーボンからなる焼結体である。
本発明の焼結体は、クロムシリサイドと、クロムカーバイド、シリコンカーバイド及びカーボンの群から選ばれる1以上と、を含むことが好ましい。
本発明の焼結体は、クロムシリサイドと、クロムカーバイド、シリコンカーバイド及びカーボンの群から選ばれる1以上と、からなる焼結体であってもよいが、これらに加えて、シリコン(Si)及びクロム(Cr)の少なくともいずれか、更にはシリコンを含んでいてもよい。
線源 : CuKα線(λ=1.5405Å)
測定モード : 連続スキャン
スキャン条件 : 2°/分
測定範囲 : 2θ=20°から80°
発散縦制限スリット: 10mm
発散/入射スリット: 1/2°
受光スリット : 0.3mm
得られるXRDパターンとICDDのデータベースを対比することで、焼結体の結晶相を同定すればよい。
実測密度は、JIS R 1634に準拠して、アルキメデス法により測定される体積に対する乾燥質量から求められるかさ密度である。アルキメデス法に先立ち、前処理は煮沸法であることが好ましく、焼結体を水中で煮沸すればよい。
d=1/{(R1/M1)+(R2/M2)+(R3/M3)+(R4/M4)+(R5/M5)+(R6/M6)+(R7/M7)+(R8/M8)+(R9/M9)}
上式において、dは焼結体の真密度[g/cm3]であり、M1乃至M8及びR1乃至R8は、それぞれ、焼結体に含まれるSi、C、Cr、SiC、CrSi、CrSi2、Cr3Si、Cr3C2及びCr5Si3の各結晶相の真密度[g/cm3]、並びに、焼結体に占める各結晶相の質量割合[wt%]である。
Si : 2.33g/cm3(=M1)
C : 2.28g/cm3(=M2)
Cr : 7.20g/cm3(=M3)
SiC : 3.12g/cm3(=M4)
CrSi : 5.36g/cm3(=M5)
CrSi2 : 4.98g/cm3(=M6)
Cr3C2 : 6.66g/cm3(=M7)
Cr5Si3 : 5.87g/cm3(=M8)
Cr3Si : 6.46g/cm3(=M9)
Y=1×MCrSi + 3×MCr5Si3 + 1×MSiC
Z=1×MSiC
上式においてMCrSiはCrSiのモル割合[mol%]、MCr5Si3はCr5Si3のモル割合[mol%]及び、MSiCはSiCのモル割合[mol%]である。
又は、
d=1/((Ra/Ma)+(Rb/Mb)+(Rc/Mc))
観察視野 :5視野以上、好ましくは5~8視野、
より好ましくは5視野
より好ましくは5視野
コントラスト比 : 100
本発明における抗折強度は、JIS R 1601に準拠する方法により測定すればよい。
合金原料調製工程に供する原料(以下、「出発原料」ともいう。)は、クロム、シリコン及びカーボンである。
クロムは、高純度クロムであることが好ましく、例えば、3N(純度99.9%以上)、更には4N(純度99.99%以上)のクロムであることが挙げられる。
シリコンは、高純度シリコンであることが好ましく、例えば、それぞれ、3N(純度99.9%以上)、更には4N(純度99.99%以上)、また更には5N(純度99.999%以上)のシリコンであることが挙げられる。
カーボン(カーボン源)は、炭素(C)及びその化合物であればよく、クロム及びケイ素の少なくともいずれかの炭化物であることが好ましく、クロムカーバイド(Cr3C2)、炭化ケイ素(SiC)及び炭素(C)の群から選ばれる1以上、更にはクロムカーバイド及びシリコンカーバイドの少なくともいずれか、が挙げられる。クロムカーバイド及びシリコンカーバイドは、それぞれ、クロム及びケイ素の出発原料としても、みなすことができる。
さらに、出発原料は、クロム及びシリコンに加え、又は、クロム及びシリコンに代わり、クロム及びシリコンの合金を含んでいてもよく、クロム及びシリコンの溶融金属粉末を含んでいることが好ましい。
シリコンの前駆物質は、高純度シリコンのフレークであることが好ましく、例えば、それぞれ、3N(純度99.9%以上)、更には4N(純度99.99%以上)、また更には5N(純度99.999%以上)のシリコンのフレークであることが挙げられる。
該ガス流は、不活性ガスであればよく、例えば、アルゴン(Ar)、窒素(N2)及びヘリウム(He)の群から選ばれる1以上、更にはアルゴンが挙げられる。
ガス流の圧力(以下、「ガス圧」ともいう。)は、1MPa以上、4MPa以上又は6MPa以上であり、また、10MPa以下更には9MPa以下であればよい。
粉末(出発原料)の混合方法としては、出発原料が均一に混合される方法であればよく、また、V型混合、ミキサーなどあらゆる混合機を使用することが可能である。混合方法は、乾式混合及び湿式混合の少なくともいずれかであればよく、乾式混合であることが好ましく、V型混合機を使用した乾式混合であることがより好ましい。これにより合金原料粉末が得られる。
焼成工程では、得られた合金原料粉末をホットプレス炉等の加圧焼成炉を用い圧力50MPa以下、焼成温度1200℃~1800℃で焼成する。焼成には、ホットプレス炉等の加圧焼成炉を使用すること好ましい。シリコンの拡散係数が低いことから無加圧炉では、得られる焼結体を高密度化するのが困難である。
焼成工程では、加圧焼成により合金原料粉末を焼成する。該工程における加圧焼成として、ホットプレス及び熱間静水圧プレスの少なくともいずれか、好ましくはホットプレス、が挙げられる。
大型の焼結体を作製するにあたり、ホットプレス圧力は好ましくは5~45MPa、さらに好ましくは10~40MPa、特に好ましくは15~40MPaである。本工程において、好ましいホットプレス圧力は、5MPa以上、10MPa以上又は15MPa以上であり、かつ、50MPa以下、45MPa以下又は40MPa以下であることが挙げられる。
焼成雰囲気は、真空雰囲気、真空減圧雰囲気、またはアルゴン等の不活性雰囲気が好ましく、アルゴン雰囲気又は真空雰囲気がより好ましく、真空雰囲気が更に好ましい。真空雰囲気で焼成することにより、原料合金粉末と同等な組成を有する焼結体が得られやすくなる。なお、本発明において、真空雰囲気と真空減圧雰囲気とは互換的に使用している。
本発明の焼結体からなるスパッタリングターゲットとすることができる。
好ましくは150W以上300W以下
ガス圧 :0.2Pa以上1.0Pa以下、
好ましくは0.3Pa以上0.7Pa以下
ガス雰囲気:不活性雰囲気、好ましくはアルゴン雰囲気
成膜時間 :0.5時間以上3時間以下、
好ましくは0.5時間以上1.5時間以下
アニール時間 : 1時間
アニール温度 : 200℃~600℃の任意の温度
上式において、TCRは抵抗温度係数[ppm/℃]、Rは測定温度における抵抗率[Ω・cm]、R30は30℃における抵抗率[Ω・cm]、及び、Tは測定温度[℃]である。
本発明の膜は、測定温度40℃~150℃におけるTCRの平均値(以下、「平均TCR」ともいう。)が100ppm/℃以下、50ppm/℃以下又は15ppm/℃以下であることが好ましい。平均TCRは0ppm/℃以上、1ppm/℃以上又は10ppm/℃以上であることが挙げられる。
平均TCR=(TCR40+TCR50+…+TCR150)/12
焼結体の結晶相は、上述した条件で、XRDパターンを測定及び同定した。
焼結体の相対密度は、真密度に対する実測密度の割合(%)として求めた。まず、JIS R 1634に準拠して、アルキメデス法により測定される体積に対する乾燥質量により持てられるかさ密度を測定し、これを実測密度とした。
d=1/{(R1/M1)+(R2/M2)+(R3/M3)+(R4/M4)+(R5/M5)+(R6/M6)+(R7/M7)+(R8/M8)+(R9/M9)}
d=(a+b+c)/((a/Ma)+(b/Mb)+(c/Mc))
鏡面研磨し、レーザー顕微鏡で観察し、得られた焼結体組織画像から画像解析により測定した。鏡面研磨は、DP-懸濁液1μm(丸本ストリアル社製)を用いて、表面粗さRa≦2μmとなるように行った。少なくとも任意の5視野を観察し、画像解析よりポアの面積を算出し、ポア率を5回(すなわち、各視野に対して1回ずつ)測定し、各視野のポア率の測定結果の平均値をポア率とした。
各視野のポア率(%)=(画像解析で算出したポアの面積/測定面積)× 100
焼結体の任意の場所から直径10.16cmの焼結体を切り出し、Inボンディングを行い、スパッタリングターゲットとした。下記条件により、スパッタリング試験を行い、スパッタリング後のターゲットの最大長さが50μm以上の穴の数をレーザー顕微鏡により数え、粗大孔とした。
焼結体の表面を1mm以上研削した後、焼結体の任意の部分より切り出されたサンプル(縦3mm×横20mm×厚み4mmの角型形状)中の酸素の含有量を溶融-赤外線吸収法により測定した。
装置 :LECO ON736 酸素・窒素分析装置
焼結体の抗折強度は、JIS R 1601に準拠する方法により測定した。
試験方法 :3点曲げ試験
支点間距離 :30mm
試料サイズ :3×4×40mm
ヘッド速度 :0.5mm/分。
前駆物質としてCrフレーク(4N):33wt%、及び、Siフレーク(5N):67wt%を使用した。カーボンルツボ内で処理温度を1650℃としてCrフレーク及びSiフレークを溶融してクロム及びシリコンの溶融金属を得た。その後、ガス圧7MPaのアルゴンガス流を通過させるように該溶融金属を滴下するガスアトマイズ法により粉末(ガスアトマイズ粉末)を作製し、これをクロム及びシリコンの出発原料とした。当該ガスアトマイズ粉は、CrSi2とSiとからなる結晶相を有していた。その後、ガスアトマイズ粉末が62wt%、Cr3C2粉末が38wt%となるように、ガスアトマイズ粉末とCr3C2粉末(製品名:Chromium Carbide、PPM社製)をアルゴン雰囲気下でV型混合機を使用して60rpmで1時間乾式混合により混合し、Crが55wt%、Siが39wt%、Cが6wt%である合金原料粉末とした。
昇温速度 :200℃/時間
昇温雰囲気:真空減圧雰囲気(真空雰囲気)
焼成雰囲気:真空減圧雰囲気(真空雰囲気)
焼成温度 :1350℃
圧力 :40MPa
焼成時間 :3時間
焼成条件を表1に示す条件に変更したこと以外は、実施例1と同様の方法で焼結体(Cr-Si-C系焼結体)を作製した。得られた焼結体は、いずれもCrSi、Cr5Si3及びSiCからなるCr-Si-C系焼結体であった。
前駆物質として、Crフレーク(4N):59wt%、及び、Siフレーク(5N):41wt%を使用した。カーボンルツボ内で、処理温度を1650℃としてこれらを溶解して溶融金属を得た。ガス圧7MPaのアルゴンガス流を通過させるように該溶融金属を滴下することでガスアトマイズ法によりガスアトマイズ粉末を作製した。当該ガスアトマイズ粉は、CrSi2とCrSiとからなる結晶相を有していた。その後、上記ガスアトマイズ粉が62wt%、Cr3C2粉末が36wt%となるようにCr3C2粉末とガスアトマイズ粉末を混合したこと以外は実施例1と同様な方法で混合し、Crが69wt%、Siが26wt%、及び、Cが5wt%である本実施例の合金原料粉末とした。
前駆物質として、Crフレーク(4N):42wt%、及び、Siフレーク(5N):58wt%を使用した。カーボンルツボ内で、処理温度を1650℃としてこれらを溶解して溶融金属を得た。ガス圧7MPaのアルゴンガス流を通過させるように、該溶融金属を滴下することでガスアトマイズ法によりガスアトマイズ粉末を作製した。当該ガスアトマイズ粉は、CrSi2とSiとからなる結晶相を有していた。その後、上記ガスアトマイズ粉が95wt%、C粉末が5wt%となるようにC粉末とガスアトマイズ粉末を混合したこと以外は実施例1と同様な方法で混合し、Crが40wt%、Siが55wt%、及び、Cが5wt%である本実施例の合金原料粉末とした。
C粉末が15wt%となるようにC粉末とガスアトマイズ粉末を混合したこと以外は実施例9と同様な方法で、Crが36wt%、Siが49wt%、及び、Cが15wt%である本実施例の合金原料粉末とした。
XRD測定の結果より、本実施例の焼結体はCrSi2、Si及びCからなるCr-Si-C系焼結体であることが確認できた。当該XRDの測定結果の結果より、本実施例の焼結体の相対密度は、CrSi2が74wt%、Siが11wt%、及び、Cが15wt%として算出した真密度、を用いて算出した。
Cr粉末:31wt%、CrSi2粉末:48wt%、SiC粉末:21wt%として、V型混合機で粉末混合を行い合金原料粉末を得たこと以外は実施例1と同様な方法で、CrSi、Cr5Si3及びSiCの結晶相からなる焼結体を得た。
実施例9と同様な方法で、Crが42wt%及びSiが58wt%であり、CrSi2とSiとからなる結晶相を有するガスアトマイズ粉末を得た。
当該ガスアトマイズ粉末を使用したこと、焼成温度を1250℃としたこと、及び、圧力を15MPaとしたこと以外は比較例1と同様な方法で焼結体を作製した。
実施例1及び8、並びに、比較例1の焼結体を、それぞれ、旋盤加工し、該焼結体から直径10.16mm、厚み5mmの円板状の焼結体を切り出した。得られた焼結体をバッキングプレートにボンディングすることでスパッタリングターゲットとし、以下の条件でガラス基板(製品名:無アルカリガラスC、ミツル工学研究所社製)上への成膜(スパッタリング)を行った。
成膜電力 :800W
ガス圧 :0.5Pa
ガス雰囲気:Arのみ(アルゴン雰囲気)
成膜時間 :1時間
実施例7、9及び10、並びに、比較例2の焼結体を使用したこと、及び、以下の条件を適用したこと以外は、<粗大孔の確認>と同様な方法でスパッタリングを行い、成膜した。
成膜電力 :200W
ガス圧 :0.5Pa
ガス雰囲気:アルゴン雰囲気
成膜時間 :1時間
膜の抵抗率は、8403型AC/DCホール測定システム(東陽テクニカ製)を用い、30℃で測定した。測定は、スパッタリング膜を備えたガラス基板を1cm角で切り出したものについて行った。
30℃から150℃まで10℃間隔で膜の抵抗率を測定し、以下の式から各温度におけるTCRを求めた。
TCR(ppm/℃)=(R-R30)/(R30×(T-30))×106
TCRの測定で得られた40℃~150℃のTCRの値を温度-TCRでプロットし、該プロットから得られる一次直線近似式を求めた。該一次直線近似式の傾きの値をTCR傾きとした。
10 黒色領域(ポア)
11 白色領域(焼結体)
Claims (10)
- クロム(Cr)、シリコン(Si)、カーボン(C)を含むCr-Si-C系焼結体であり、焼結体の相対密度が90%以上かつ、ポア率が13%以下であることを特徴とするCr-Si-C系焼結体。
- 組成範囲としてカーボンが1~20wt%、シリコンが20~70wt%、残部がクロムである請求項1に記載のCr-Si-C系焼結体。
- クロムシリサイドと、クロムカーバイド、シリコンカーバイド及びカーボンの群から選ばれる1以上と、を含む請求項1又は2に記載のCr-Si-C系焼結体。
- CrSi、CrSi2及びCr3Siの群から選ばれる1以上を主相とする請求項1乃至3のいずれか一項に記載のCr-Si-C系焼結体。
- 酸素量が1wt%以下である請求項1乃至4のいずれか一項に記載のCr-Si-C系焼結体。
- 抗折強度が100MPa以上である請求項1乃至5のいずれか一項に記載のCr-Si-C系焼結体。
- クロム及びシリコンのガスアトマイズ粉末、並びに、クロム及びシリコンの少なくともいずれかとカーボンとを含むカーボン源と、を混合して合金原料粉末を得る工程、及び、該合金原料粉末を真空雰囲気で、圧力50MPa以下、及び、焼成温度1350℃以上1800℃以下で、ホットプレスする焼成工程、を有する請求項1乃至6のいずれか一項に記載のCr-Si-C系焼結体の製造方法。
- 前記カーボン源は、クロム及びシリコンの少なくともいずれかを含む炭化物である請求項7に記載の製造方法。
- 請求項1乃至6のいずれか一項に記載のCr-Si-C系焼結体からなるスパッタリングターゲット。
- 請求項9に記載のスパッタリングターゲットを用いてスパッタリングする膜の製造方法。
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Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0786004A (ja) * | 1993-09-13 | 1995-03-31 | Fujitsu Ltd | 薄膜抵抗材料及び薄膜抵抗器の製造方法 |
JP2002173765A (ja) | 2000-12-05 | 2002-06-21 | Toshiba Corp | スパッタリングターゲット |
JP2003167324A (ja) | 2001-11-30 | 2003-06-13 | Nikko Materials Co Ltd | 金属シリサイドスパッタリングターゲット及びその製造方法 |
JP2004325835A (ja) * | 2003-04-25 | 2004-11-18 | Toppan Printing Co Ltd | スパッタリングターゲット |
JP2006313785A (ja) * | 2005-05-06 | 2006-11-16 | Sumitomo Metal Mining Co Ltd | 薄膜抵抗体およびその製造方法 |
JP2007019274A (ja) * | 2005-07-07 | 2007-01-25 | Sumitomo Metal Mining Co Ltd | 抵抗薄膜、薄膜抵抗体およびその製造方法 |
WO2014157054A1 (ja) * | 2013-03-26 | 2014-10-02 | Jx日鉱日石金属株式会社 | スパッタリング用シリサイドターゲット及びその製造方法 |
JP2017082314A (ja) | 2015-10-30 | 2017-05-18 | 三菱マテリアル株式会社 | スパッタリングターゲット及びスパッタリングターゲットの製造方法 |
JP2017218621A (ja) * | 2016-06-06 | 2017-12-14 | 三井金属鉱業株式会社 | ターゲット材及びその製造方法 |
WO2020105591A1 (ja) * | 2018-11-22 | 2020-05-28 | 東ソー株式会社 | Cr-Si系焼結体 |
JP2020129947A (ja) | 2019-02-12 | 2020-08-27 | 株式会社三社電機製作所 | 半導体素子の過渡熱抵抗測定用電源回路 |
JP2021063955A (ja) | 2019-10-16 | 2021-04-22 | 敬二 池森 | 撮像光学系 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE59605278D1 (de) * | 1995-03-09 | 2000-06-29 | Philips Corp Intellectual Pty | Elektrisches Widerstandsbauelement mit CrSi-Widerstandsschicht |
EP1741685B1 (de) * | 2005-07-05 | 2014-04-30 | MANN+HUMMEL Innenraumfilter GmbH & Co. KG | Poröser beta-SiC-haltiger keramischer Formkörper und Verfahren zu dessen Herstellung. |
EP2878693A1 (en) | 2009-08-21 | 2015-06-03 | Massachusetts Institute of Technology | Silicon-rich alloys |
CN109957764B (zh) * | 2017-12-14 | 2021-04-02 | 中国科学院宁波材料技术与工程研究所 | 水基液体环境用CrSiC复合涂层及其制备方法与应用 |
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Patent Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0786004A (ja) * | 1993-09-13 | 1995-03-31 | Fujitsu Ltd | 薄膜抵抗材料及び薄膜抵抗器の製造方法 |
JP2002173765A (ja) | 2000-12-05 | 2002-06-21 | Toshiba Corp | スパッタリングターゲット |
JP2003167324A (ja) | 2001-11-30 | 2003-06-13 | Nikko Materials Co Ltd | 金属シリサイドスパッタリングターゲット及びその製造方法 |
JP2004325835A (ja) * | 2003-04-25 | 2004-11-18 | Toppan Printing Co Ltd | スパッタリングターゲット |
JP2006313785A (ja) * | 2005-05-06 | 2006-11-16 | Sumitomo Metal Mining Co Ltd | 薄膜抵抗体およびその製造方法 |
JP2007019274A (ja) * | 2005-07-07 | 2007-01-25 | Sumitomo Metal Mining Co Ltd | 抵抗薄膜、薄膜抵抗体およびその製造方法 |
WO2014157054A1 (ja) * | 2013-03-26 | 2014-10-02 | Jx日鉱日石金属株式会社 | スパッタリング用シリサイドターゲット及びその製造方法 |
JP2017082314A (ja) | 2015-10-30 | 2017-05-18 | 三菱マテリアル株式会社 | スパッタリングターゲット及びスパッタリングターゲットの製造方法 |
JP2017218621A (ja) * | 2016-06-06 | 2017-12-14 | 三井金属鉱業株式会社 | ターゲット材及びその製造方法 |
WO2020105591A1 (ja) * | 2018-11-22 | 2020-05-28 | 東ソー株式会社 | Cr-Si系焼結体 |
JP2020129947A (ja) | 2019-02-12 | 2020-08-27 | 株式会社三社電機製作所 | 半導体素子の過渡熱抵抗測定用電源回路 |
JP2021063955A (ja) | 2019-10-16 | 2021-04-22 | 敬二 池森 | 撮像光学系 |
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CN115667182A (zh) | 2023-01-31 |
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JPWO2022025033A1 (ja) | 2022-02-03 |
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