WO2017115987A1 - Revêtement dur pour outil de coupe - Google Patents

Revêtement dur pour outil de coupe Download PDF

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Publication number
WO2017115987A1
WO2017115987A1 PCT/KR2016/011779 KR2016011779W WO2017115987A1 WO 2017115987 A1 WO2017115987 A1 WO 2017115987A1 KR 2016011779 W KR2016011779 W KR 2016011779W WO 2017115987 A1 WO2017115987 A1 WO 2017115987A1
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WO
WIPO (PCT)
Prior art keywords
layer
hkl
mpa
thickness
tic
Prior art date
Application number
PCT/KR2016/011779
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English (en)
Korean (ko)
Inventor
이동열
안진우
강재훈
김정욱
조성우
이성구
Original Assignee
한국야금 주식회사
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
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Publication of WO2017115987A1 publication Critical patent/WO2017115987A1/fr

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
    • B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23C—MILLING
    • B23C5/00—Milling-cutters
    • B23C5/16—Milling-cutters characterised by physical features other than shape
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/56—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material

Definitions

  • the present invention relates to a hard coating formed on a base material for cutting tools, and more particularly, is formed by a chemical vapor deposition method (hereinafter referred to as 'CVD') on the base material for cutting tools made of cemented carbide, and the TiCN layer (006). ⁇ -Al 2 O 3 first grown with cotton
  • the present invention relates to a hard coating including a thin film and excellent in peeling resistance of the thin film against impact generated during cutting, thereby greatly improving the life of the cutting tool.
  • cemented carbide is used as a cutting tool after forming a hard coating layer on its surface to increase abrasion resistance.
  • the hard coating is formed by a CVD method or a physical vapor deposition method (hereinafter referred to as a 'PVD method'). .
  • the cutting edge of the cutting tool is exposed to a high temperature environment of about 1000 °C during high-speed processing of hard materials, not only wear and tear due to friction and oxidation due to contact with the workpiece, but also subjected to mechanical shock such as interruption. Therefore, cutting tools require properties such as proper oxidation resistance, wear resistance and chipping resistance.
  • the hard film for cutting tools is generally composed of a single layer or a multi-layered non-oxide thin film, an oxide-based thin film having excellent oxidation resistance or a mixed layer thereof.
  • the non-oxide thin film include TiN, TiC, TiCN.
  • Carbide, nitride, carbonitride of Group 4, 5 and 6 metal elements on the periodic table such as, and the like is an example of the oxide-based thin film is ⁇ -Al 2 O 3 .
  • ⁇ -Al 2 O 3 is a material that is widely used in cutting tool coatings because it is a phase stable at high temperatures and thus does not generate phase transformation during cutting and exhibits excellent wear resistance.
  • anisotropy anisotropy of the ⁇ -Al 2 O 3 grain size and the ⁇ -Al 2 O 3 grains of.
  • anisotropy anisotropy of the ⁇ -Al 2 O 3 grain size and the ⁇ -Al 2 O 3 grains of.
  • anisotropy of the ⁇ -Al 2 O 3 grains a method of preferentially growing the (110) plane, the (012) plane, the (104) plane, the (006) plane, or the like is known.
  • ⁇ -Al 2 O 3 preferentially grown to (006) plane. In the case of thin films, it suppresses the ductile breakdown of ⁇ -Al 2 O 3 and improves plastic resistance deformation, thereby reducing the insert wear and K T wear of the insert during cutting of steel and greatly improving the tool life. In recent years, it is widely applied to cutting tools.
  • each thin film constituting the hard coating film for the cutting tool differs depending on the base material and the cutting tool used for forming the hard coating, and thus, ⁇ -Al 2 O 3 preferentially grown to the (006) plane. Even if a thin film is applied, it is necessary to further adapt the state of the base material and other thin films in order to improve the life of the cutting tool.
  • Patent Document 1 discloses a technique for improving the life of a cutting tool by applying a compressive residual stress to a hard film through post-treatment such as blasting.
  • ⁇ -Al 2 O 3 First Grows Technology to (006) Plane When applied to a hard film for cutting tools including a thin film as it is, there is a side that the improvement in life improvement is not enough.
  • the present invention aims to solve the problem of providing a hard film for a cutting tool that can improve the life of the cutting tool compared to the conventional one by suppressing the peeling of the hard film formed on the cutting tool against the impact generated during cutting. .
  • TC (hkl) I (hkl ) / Io (hkl) ⁇ 1 / n ⁇ I (hkl) / Io (hkl) ⁇ -1
  • I (hkl) (hkl) reflectivity
  • Io (hkl) standard intensity according to JCPDS card 46-1212
  • n number of reflections used in the calculation
  • (hkl) reflections are (012), (104 ), Using (110), (006), (113) and (116))
  • the residual stress of the alumina layer is in the compressive stress state
  • the stress difference between the alumina layer and the TiCN layer is 500 MPa or less
  • TC (006) of the alumina is By making it exceed 1.4, the effect which remarkably improves cutting tool life compared with the conventional cutting tool can be acquired.
  • the present inventors can suppress the peeling of a hard film with respect to the impact which arises at the time of cutting when it is applied to the cutting insert for milling with the hard film containing the alpha-phase alumina layer which was first grown to the (006) plane.
  • the coefficient of thermal expansion of the cemented carbide base material for milling containing 7 to 15% by weight of Co is about 6.0 to 6.5 ⁇ 10 -6 / K
  • the coefficient of thermal expansion of the c-axis of alumina having HCP crystal structure is about 7.0 ⁇ 10, and the -6 / degree K
  • the thermal expansion coefficient of TiN about 9.35 ⁇ 10 -6 / K
  • the thermal expansion coefficient of the TiC consider about 7.4 ⁇ 10 -6 / K around a point, constituting the base material and the hard coating
  • the alumina layer is grown first in the (006) orientation, and the TiCN layer formed as the lower layer forms a carbon-rich layer as much as possible, and forms a hard film.
  • Alpha phase grown preferentially to (006) plane When the residual stress state of the alumina layer is maintained in the compressive stress state and the stress difference between the TiCN layer and the alpha phase alumina layer is controlled, the peeling between the thin films or the base material and the thin film constituting the hard coating by external impact is reduced,
  • the present invention has been found to suppress the breakdown at and to obtain an improved service life compared to the prior art.
  • the hard coating according to the present invention comprises a base material phase comprising Co 7 to 15 wt%, carbides or carbonitrides containing elements of Group 4, 5 or 6 and 0 to 5 wt%, and the remaining WC and unavoidable impurities.
  • the thickness is 1 ⁇ 10 ⁇ m
  • the residual stress is 0 ⁇ 400MPa
  • TC (hkl) I (hkl ) / Io (hkl) ⁇ 1 / n ⁇ I (hkl) / Io (hkl) ⁇ -1
  • I (hkl) (hkl) reflectivity
  • Io (hkl) standard intensity according to JCPDS card 46-1212
  • n number of reflections used in the calculation
  • (hkl) reflections are (012), (104 ), Using (110), (006), (113) and (116))
  • the base material is brittle increases when the content of Co is less than 7% by weight, wear resistance is reduced when the content of more than 15% by weight, it is preferable to add in the range of 7 to 15% by weight.
  • Carbide or carbonitride containing the elements of the Group 4, 5 or 6 group is more than 5% by weight since the occurrence of thermal cracks due to repeated thermal shock increases when the content exceeds 5% by weight, Do.
  • the residual stress is preferably a compressive stress, but when it is in a compressive stress state, it is difficult to maintain the residual stress difference between the alumina layers located above 500 MPa or less, or because the damage of the alumina layer becomes large, a tensile stress of more than 400 MPa is preferable. In the state, since the thin film loss easily occurs due to external impact, the range of 0 to 400 MPa is preferable.
  • the alpha phase alumina layer does not exhibit abrasion resistance and oxidation resistance when the thickness is less than 1 ⁇ m, and becomes brittle strong ceramic layer when it exceeds 10 ⁇ m, the range of 1 to 10 ⁇ m is preferable. .
  • the residual stress of the alumina layer in the alpha phase is in a compressive stress state, and when the absolute value is less than 50 MPa, the thin film toughness does not function. Since it is highly likely to occur, it is preferable to maintain the range of -1,000 MPa to -50 MPa.
  • the alpha phase alumina layer is preferentially grown to the (006) plane, and the TC (006) calculated by the above formula (1) is more than 1.4, more preferably more than 3.0, and most preferably more than 4.0.
  • the possibility of peeling increases due to stress nonuniformity, and it is preferable to maintain it at 500 MPa or less, and more preferably 400 MPa or less.
  • a hard coating having a structure shown in Table 1 was formed on a cemented carbide base material having the composition shown in Table 1 below.
  • the hard film according to Comparative Example 1 to Comparative Example 4 was formed for comparison with the embodiment of the present invention.
  • the cemented carbide base material is an insert prepared by pressing and sintering a powder composed of 10 wt% Co and 1.5 wt% of carbide with TaC and the remaining WC with SPCN1203EDR (Korean metallurgy model number), and then grinding the upper and lower surfaces and honing the edges.
  • SPCN1203EDR Korean metallurgy model number
  • the surface of the insert is a hydrocarbon gas such as TiCl 4 gas, CH 3 CN, N 2 , H 2 , C 2 H 4 , C 2 H 6 , at a process partial pressure of 60 to 80 mbar and a process temperature of 750 to 900 ° C.
  • TiC x N 1-x x ⁇ 0.6
  • TC (006) by using a gas of AlCl 3 and gas such as CO 2 or CO, HCl, H 2 S, H 2 at a process partial pressure of 50 ⁇ 80 mbar, a process temperature of 1000 ⁇ 1050 °C.
  • ⁇ -Al 2 O 3 with preferential orientation so that A layer was formed.
  • ⁇ -Al 2 O 3 with a preferred orientation of (006) The layer was formed through the control of the flow rate of H 2 S gas in the range of 100 ⁇ 600ml and the flow rate of HCl gas in the range of 1-3L.
  • TiN titanium nitride
  • CVD chemical vapor deposition
  • the outermost TiN layer is intended for wear identification and is a layer that can be selectively formed.
  • the formation of the TiCN layer, the interfacial layer, the TiN layer is the same as the embodiment of the present invention, and through the flow rate control of the reaction gas when forming the alumina of the alpha phase (006) Residual stresses were controlled in such a way that they did not preferentially grow into cotton or do not undergo post-treatment.
  • the composition of the hard base material according to the Examples and Comparative Examples 1 to 4 is the same, and the thickness of the MT-TiCN layer, TiAlCNO layer, alpha-phase alumina layer and TiN layer is almost similar. Formed.
  • the cutting tool insert thus prepared was evaluated for cutting life as follows.
  • SKD11 (Dimension 100mm ⁇ 200 ⁇ 300mm)
  • TC (006) shows the preferential growth tendency toward the (006) plane of the alpha phase alumina
  • '-' in the residual stress means a compressive stress
  • the stress difference ⁇ S means an absolute value of the stress difference between the TiCN layer and the alumina layer
  • the lifespan means the amount of chip removal per unit area (cm 2) per unit minute (min).
  • the TC (006) of the alpha phase alumina layer of Comparative Example 4 is 4.8, compared with 3.4 of the TC (006) of the alpha phase alumina layer of Comparative Example 3
  • the preferential growth tendency of was higher, the stress state of the alpha-phase alumina layer was in the tensile stress state, and the life of the cutting tool was lower than in Comparative Example 3.
  • both hard coatings had a TC (006) of more than 3 alpha-alumina layers, and the alumina had a compressive stress state or a comparative stress in the stress difference between the alumina and TiCN layers.
  • 3 exceeds 500 MPa, but the embodiment has a difference of 500 MPa or less, and in the residual stress of the alpha-phase alumina layer, there is a difference in that the comparative compressive stress is present in Comparative Example 3, which is significantly higher than that of Comparative Example 3. Improved cutting tool life.
  • the difference in residual stress between the alumina layer and the TiCN layer is preferably 500 MPa or less, and more preferably 400 MPa or less.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • General Chemical & Material Sciences (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Chemical Vapour Deposition (AREA)

Abstract

La présente invention concerne un revêtement dur, qui est formé sur un matériau de base constituée d'un carbure cémenté pour un outil de coupe, qui comprend une couche de TiCN et un film mince de α-Al2O3 initialement formé dans le plan (006), et présente une excellente résistance au pelage de film mince contre le choc survenant lors du traitement de coupe, de manière à améliorer grandement la durée de vie de l'outil de coupe. Le revêtement dur selon la présente invention est formé avec une épaisseur de 5 à 30 µm sur un matériau de base comprenant 7 à 15 % en poids de Co, 0 à 5 % en poids d'un carbure ou un carbonitrure contenant un élément du groupe 4, 5 ou 6 et le reste étant WC et des impuretés inévitables. Le revêtement dur comprend : une couche de TiCxNyOz (x+y+z=1, x＞0, y＞0, z≥0), qui est formée sur le matériau de base, présente une épaisseur de 2 à 15 µm et une contrainte résiduelle de 0 à 400 MPa, et est formée de cristaux colonnaires ; une couche de Al1-aTiaCxNyOz (a≥0, x+y+z=1, x＞0, y＞0, z≥0), qui est formée sur la couche de TiCxNyOz (x+y+z=1, x＞0, y＞0, z≥0) et présente une épaisseur de 1 à 2 µm ; et une couche d'alumine en phase alpha, qui est formée sur la couche de Al1-aTiaCxNyOz (a≥0, x+y+z=1, x＞0, y＞0, z≥0) et présente une épaisseur de 1 à 10 µm et une contrainte résiduelle de -1 000 à -50 MPa, la différence de contrainte résiduelle (ΔS) entre la couche de TiCxNyOz (x+y+z=1, x＞0, y＞0, z≥0) et la couche d'alumine en phase alpha étant de 500 MPa ou moins et le TC(006) de la couche d'alumine en phase alpha étant supérieur à 1,4.
PCT/KR2016/011779 2015-12-29 2016-10-20 Revêtement dur pour outil de coupe WO2017115987A1 (fr)

Applications Claiming Priority (2)

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KR10-2015-0188079 2015-12-29
KR1020150188079A KR101737709B1 (ko) 2015-12-29 2015-12-29 절삭공구용 경질피막

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111893457A (zh) * 2020-08-14 2020-11-06 株洲钻石切削刀具股份有限公司 一种涂层切削刀具及其制备方法
US11311946B2 (en) * 2018-03-20 2022-04-26 Kyocera Corporation Coated tool and cutting tool including the same

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102055320B1 (ko) 2019-05-29 2019-12-13 한국생산기술연구원 물리증착용 타겟, 이에 의한 질화물 경질피막 및 이들의 제조방법
KR102265210B1 (ko) * 2019-12-24 2021-06-15 한국야금 주식회사 인성이 향상된 절삭공구
KR102450430B1 (ko) 2020-08-21 2022-10-04 한국야금 주식회사 절삭공구용 초경합금

Citations (5)

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Publication number Priority date Publication date Assignee Title
JP2010089201A (ja) * 2008-10-07 2010-04-22 Mitsubishi Materials Corp 硬質被覆層がすぐれた耐チッピング性を発揮する表面被覆切削工具
KR20120073322A (ko) * 2009-11-06 2012-07-04 가부시키가이샤 탕가로이 피복 공구
KR20140001694A (ko) * 2012-06-28 2014-01-07 대구텍 유한회사 절삭 인서트
JP2014166657A (ja) * 2013-02-28 2014-09-11 Mitsubishi Materials Corp 高速切削加工で硬質被覆層がすぐれた耐摩耗性を発揮する表面被覆切削工具
KR20140109857A (ko) * 2011-12-26 2014-09-16 미쓰비시 마테리알 가부시키가이샤 경질 피복층이 우수한 내치핑성과 내마모성을 발휘하는 표면 피복 절삭 공구

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2010089201A (ja) * 2008-10-07 2010-04-22 Mitsubishi Materials Corp 硬質被覆層がすぐれた耐チッピング性を発揮する表面被覆切削工具
KR20120073322A (ko) * 2009-11-06 2012-07-04 가부시키가이샤 탕가로이 피복 공구
KR20140109857A (ko) * 2011-12-26 2014-09-16 미쓰비시 마테리알 가부시키가이샤 경질 피복층이 우수한 내치핑성과 내마모성을 발휘하는 표면 피복 절삭 공구
KR20140001694A (ko) * 2012-06-28 2014-01-07 대구텍 유한회사 절삭 인서트
JP2014166657A (ja) * 2013-02-28 2014-09-11 Mitsubishi Materials Corp 高速切削加工で硬質被覆層がすぐれた耐摩耗性を発揮する表面被覆切削工具

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11311946B2 (en) * 2018-03-20 2022-04-26 Kyocera Corporation Coated tool and cutting tool including the same
CN111893457A (zh) * 2020-08-14 2020-11-06 株洲钻石切削刀具股份有限公司 一种涂层切削刀具及其制备方法

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