CN1662334A - 立方晶氮化硼基超高压烧结材料制切削刀片 - Google Patents
立方晶氮化硼基超高压烧结材料制切削刀片 Download PDFInfo
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- CN1662334A CN1662334A CN038143224A CN03814322A CN1662334A CN 1662334 A CN1662334 A CN 1662334A CN 038143224 A CN038143224 A CN 038143224A CN 03814322 A CN03814322 A CN 03814322A CN 1662334 A CN1662334 A CN 1662334A
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- 238000005520 cutting process Methods 0.000 title claims abstract description 166
- 239000000463 material Substances 0.000 title claims abstract description 34
- 229910052582 BN Inorganic materials 0.000 title claims abstract description 15
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 title claims abstract description 15
- 239000010936 titanium Substances 0.000 claims abstract description 61
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 31
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 29
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 9
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 claims abstract description 9
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims abstract description 8
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 claims abstract description 3
- 239000000203 mixture Substances 0.000 claims description 44
- 238000001704 evaporation Methods 0.000 claims description 11
- 230000008020 evaporation Effects 0.000 claims description 11
- 150000004767 nitrides Chemical class 0.000 claims description 7
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 claims description 5
- 238000002389 environmental scanning electron microscopy Methods 0.000 claims description 4
- 229910000765 intermetallic Inorganic materials 0.000 claims description 4
- 150000003609 titanium compounds Chemical class 0.000 claims 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract 1
- 230000001747 exhibiting effect Effects 0.000 abstract 1
- -1 nitride compound Chemical class 0.000 abstract 1
- 239000000843 powder Substances 0.000 description 54
- 238000005245 sintering Methods 0.000 description 40
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 31
- 229910004349 Ti-Al Inorganic materials 0.000 description 12
- 229910004692 Ti—Al Inorganic materials 0.000 description 12
- 150000001875 compounds Chemical class 0.000 description 12
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 10
- 239000010931 gold Substances 0.000 description 10
- 229910052737 gold Inorganic materials 0.000 description 10
- 238000012360 testing method Methods 0.000 description 9
- 229910000831 Steel Inorganic materials 0.000 description 7
- 239000010959 steel Substances 0.000 description 7
- 229910052721 tungsten Inorganic materials 0.000 description 7
- 229910000760 Hardened steel Inorganic materials 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 238000005255 carburizing Methods 0.000 description 6
- 238000010791 quenching Methods 0.000 description 6
- 230000000171 quenching effect Effects 0.000 description 6
- 239000007795 chemical reaction product Substances 0.000 description 5
- 238000001125 extrusion Methods 0.000 description 5
- 238000003754 machining Methods 0.000 description 5
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 230000004523 agglutinating effect Effects 0.000 description 4
- 238000010891 electric arc Methods 0.000 description 4
- 230000007774 longterm Effects 0.000 description 4
- 238000012423 maintenance Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 238000005406 washing Methods 0.000 description 4
- 239000000853 adhesive Substances 0.000 description 2
- 230000001070 adhesive effect Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910003460 diamond Inorganic materials 0.000 description 2
- 239000010432 diamond Substances 0.000 description 2
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- 239000007789 gas Substances 0.000 description 2
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- 238000007733 ion plating Methods 0.000 description 2
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- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000012856 packing Methods 0.000 description 2
- 238000012797 qualification Methods 0.000 description 2
- 238000005476 soldering Methods 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 1
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- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- JMANVNJQNLATNU-UHFFFAOYSA-N oxalonitrile Chemical compound N#CC#N JMANVNJQNLATNU-UHFFFAOYSA-N 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 210000001138 tear Anatomy 0.000 description 1
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- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
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Abstract
本发明提供一种耐崩刃性优异的立方晶氮化硼基超高压烧结材料制切削刀片,所述立方晶氮化硼基超高压烧结材料制切削刀片用这样的立方晶氮化硼基超高压烧结材料构成:在扫描电镜的组织观察中实质上显示连续结合相、硬质分散相、以及介在于上述连续结合相和硬质分散相之间的中间粘附相3相组织,并且按质量%计,具有的配合组成包含:作为上述连续结合相形成成分,氮化钛、碳氮化钛、和碳化钛之中的2种或以上、或者碳氮化钛:15-56质量%;作为上述中间粘附相形成成分,Ti与Al的复合氮化物:2-10质量%、碳化钨:2-10质量%;作为上述硬质分散相形成成分,立方晶氮化硼:余量,但是含有35-65质量%。
Description
技术领域
本发明涉及在以高速进行例如高硬度淬火钢等的难切削材料的精切削的场合,也发挥优异的耐崩刃性的立方晶氮化硼基超高压烧结材料制切削刀片(以下叫做c-BN基烧结切削刀片)。
背景技术
过去,一般作为c-BN基烧结切削刀片,例如特开昭53-77811号公报所记载,人们知道使用作为加压成型体的烧结体的,立方晶氮化硼基超高压烧结材料(以下叫做c-BN基材料)构成的c-BN基烧结切削刀片,所述加压成型体的烧结体在扫描电镜的组织观察中,实质上显示连续结合相和硬质分散相2相组织,并且包含下述组成:按质量%计,作为上述连续结合相形成成分,选自氮化钛(以下用TiN表示)、碳氮化钛(以下用TiCN表示)和碳化钛(以下用TiC表示)之中的1种或2种或以上:20-45%;作为上述硬质分散相形成成分,立方晶氮化硼(以下用c-BN表示):余量;也知道该切削刀片用于例如各种钢和铸铁等的表面精切削等。
另一方面,近年的切削装置的高性能化和高功率化惊人地显著,另外,对切削加工的省力和节能的要求也强烈,与之相伴,切削加工有高速化的倾向,但以上述的现有c-BN基烧结切削刀片为首、及其他的c-BN基烧结切削刀片中,当用于以高速进行例如高硬度淬火钢等的难切削材料的精切削等时,作为硬质分散相的c-BN相对实质上构成连续结合相的TiCN相粘附性不足,因此上述c-BN相易剥离,其结果,切削刃发生崩刃(微小缺损),因此现状是在比较短的时间就达到使用寿命。
发明内容
于是,本发明人从上述的观点出发,为开发耐崩刃性优异的c-BN基烧结切削刀片而进行研究的的结果得到下述研究结果:
在制造c-BN基烧结切削刀片时,除了作为原料粉末而使用的c-BN粉末、TiN粉末、TiCN粉末、和TiCN粉末以外,还使用Ti与Al的复合氮化物[以下用(Ti,Al)N表示]粉末和碳化钨(以下用WC表示)粉末作为原料粉末,将这些粉末配合成这样的配合组成,用质量%(以下%表示质量%)表示,该配合组成包含:
TiN、TiCN、和TiC之中的2种或以上、或者TiCN:15-56%;
(Ti,Al)N:2-10%、
WC:2-10%;
c-BN:余量(但是含有35-65%)。当将混合上述配合组成的粉末而形成的加压成型体进行超高压烧结时,这些构成成分之中的(Ti,Al)N粉末和WC粉末在烧结时优先地聚集在c-BN粉末表面,反应,形成反应生成物,在烧结后的c-BN基材料中,上述反应生成物实质上介于包含TiCN相的连续结合相和包含c-BN相的硬质分散相之间,而且该反应生成物与构成连续结合相的上述TiCN相、以及构成硬质分散相的上述c-BN相的任一个都极为牢固地粘附,作为中间粘附相而作用,因此用该c-BN基材料构成的c-BN基烧结切削刀片即使用于以高速进行例如高硬度淬火钢等的难切削材料的精切削等,在切削刃上也不会发生c-BN相的粘附性不足为原因的崩刃,长期发挥优异的切削性能。
本发明是基于上述研究结果完成的,本发明的耐崩刃性优异的c-BN基烧结切削刀片具有下述特征:由作为加压成型体的烧结体的c-BN基材料构成,所述加压成型体的烧结体在扫描电镜的组织观察中实质上显示连续结合相、硬质分散相、以及介于上述连续结合相和硬质分散相之间的中间粘附相3相组织,并且具有的配合组成包含:
作为上述连续结合相形成成分,
TiN、TiCN、和TiC之中的2种或以上、或者TiCN:15-56%(以下均用质量%表示);
作为上述中间粘附相形成成分,
(Ti,Al)N:2-10%、
WC:2-10%;
作为上述硬质分散相形成成分,c-BN:余量(但是含有35-65%)。
下面说明在本发明的c-BN基烧结切削刀片中,按照上述限定构成该刀片的c-BN基材料的配合组成的理由。
(a)TiN、TiCN、和TiC
这些成分具有提高烧结性,同时形成实质上包含TiCN相的连续结合相从而提高强度的作用,但其配合比例小于15%时,不能确保所期望的强度,另一方面其配合比例超过56%时,耐磨性急剧降低,因此其配合比例规定为15-56%。优选为30-50%。
(b)(Ti,Al)N和WC
按照上述的那样,这些成分在烧结时优先地聚集在c-BN粉末的表面,反应,形成反应生成物,烧结后的c-BN基材料介于上述连续结合相的TiCN相、和上述硬质分散相c-BN相之间。而且,该反应生成物具有与上述连续结合相的TiCN相、上述硬质分散相c-BN相的任一个都牢固地粘附接合的性质,因此上述c-BN相对作为连续结合相的TiCN相的粘附性显著提高,其结果,切削刃的耐崩刃性提高,但这些成分中的任何成分的配合比例脱离上述范围,作为中间粘附相不能确保对上述硬质分散相与连续结合相之间牢固的粘附性,因此(Ti,Al)N和WC的上述配合比例在确保牢固的粘附性上是经验性地确定的。优选均分别为3-8%。
(c)c-BN
构成硬质分散相的c-BN是极硬的,由此可谋求耐磨性提高,但其配合比例小于35%时,不能确保所期望的优异的耐磨性,另一方面当其配合比例超过65%时,c-BN基材料自身的烧结性降低,其结果切削刃易发生崩刃,因此其比例规定为35-65%。优选为45-60%。
对于上述本发明的c-BN基烧结切削刀片,也可以在其表面蒸镀形成具有黄金色色调的氮化钛(以下用TiN表示)层,以此作为切削刀片使用前后识别层,该情况下的蒸镀层厚度,当平均层厚小于0.5μm时,不能付与足够识别的黄金色的色调,另一方面,识别在高至5μm的平均层厚时即足够,因此规定为0.5-5μm的平均层厚即可。
另外,本发明人等为开发耐崩刃性优异的c-BN基烧结切削刀片而进一步研究的的结果得到下述研究结果:
在制造c-BN基烧结切削刃片时,除了作为原料粉末而使用的c-BN粉末、TiN粉末和/或TiCN粉末以外,还使用Ti与Al的金属间化合物[以下用Ti-Al化合物表示]粉末、Ti与Al的复合氮化物[以下用(Ti,Al)N表示]粉末和碳化钨(以下用WC表示)粉末作为原料粉末,将这些粉末按质量%(以下%表示质量%)以
Ti-Al化合物:3-8%、
(Ti,Al)N:5-10%、
WC:5-15%的比例配合时,这些Ti-Al化合物粉末、(Ti,Al)N粉末、和WC粉末在烧结时优先地反应,形成Ti和Al和W的复合碳氮化物[以下用(Ti,Al,W)CN表示],聚集在c-BN粉末表面,因此在烧结后的c-BN基材料中,上述(Ti,Al,W)CN介于包含TiN和/或TiCN的连续结合相与包含c-BN的硬质分散相之间,而且该(Ti,Al,W)CN与构成连续结合相的上述TiN和TiCN、以及构成硬质分散相的上述c-BN的任一个都极为牢固地粘附,作为中间粘附相而作用,因此用该c-BN基材料构成的c-BN基烧结切削刀片即使用于以高速进行例如高硬度淬火钢等的难切削材料的精切削等,在切削刃上也不会发生崩刃,长期发挥优异的切削性能。
本发明是基于上述研究结果而完成的,本发明的耐崩刃性优异的c-BN基烧结切削刀片具有下述特征:用c-BN基材料构成,所述c-BN基材料在扫描电镜的组织观察中实质上显示连续结合相、硬质分散相、以及介于上述连续结合相和硬质分散相之间的中间粘附相3相组织,并且具有的配合组成包含:
作为上述连续结合相形成成分,TiN和/或TiCN:20-37%;
作为上述中间粘附相形成成分,Ti-Al化合物:3-8%、(Ti,Al)N:5-10%、WC:5-15%;
作为上述硬质分散相形成成分,c-BN:余量(但是含有35-55%)。
下面说明在本发明的c-BN基烧结切削刀片中按照上述限定构成该刀片的c-BN基材料的配合组成的理由。
(d)TiN和/或TiCN
这些成分具有提高烧结性,同时形成连续结合相从而提高强度的作用,但其配合比例小于20%时,不能确保所期望的强度,另一方面其配合比例超过37%时,耐磨性急剧降低,因此其配合比例规定为20-37%。另外还知道,即使将作为连续结合相形成成分的TiN和/或TiCN的一部分(5-10质量%)置换成碳化钽(TaC)、或碳化铌(NbC),也不发生特别弊端并得到与不含这些成分的情况相同的优异的耐崩刃性。
(e)Ti-Al化合物、(Ti,Al)N、和WC
按照上述的那样,这些成分在烧结时优先地反应,形成(Ti,Al,W)CN,聚集在作为硬质分散相的c-BN表面,因此在烧结后的c-BN基材料中,介于上述连续结合相的TiN和TiCN、与上述硬质分散相c-BN之间。而且该(Ti,Al,W)CN具有与TiN、TiCN、以及c-BN的任一个都牢固地粘附接合的性质,因此上述c-BN对TiN和TiCN的粘附性显著提高,其结果,切削刃的耐崩刃性提高,但这些成分中的任何成分的配合比例脱离上述范围,作为中间粘附相不能确保对上述硬质分散相与连续结合相之间牢固的粘附性,因此Ti-Al化合物、(Ti,Al)N、和WC的上述配合比例在确保牢固的粘附性上是经验性地确定的。
(f)c-BN
构成硬质分散相的c-BN是极硬的,由此可谋求耐磨性提高,但其配合比例小于35%时,不能确保所期望的优异的耐磨性,另一方面当其配合比例超过55%时,c-BN基材料自身的烧结性降低,其结果切削刃易发生崩刃,因此其比例规定为35-55%。
对于上述本发明的c-BN基烧结切削刀片,也可以在其表面蒸镀形成具有黄金色色调的氮化钛(以下用TiN表示)层,以此作为切削刀片使用前后识别层,该情况下的蒸镀层厚度,当平均层厚小于0.5μm时,不能付与足够识别的黄金色的色调,另一方面,识别在高至5μm的平均层厚时即足够,因此规定为0.5-5μm的平均层厚即可。
发明的具体实施方式
首先,通过第1实施例具体地说明本发明的c-BN基烧结切削刀片。
作为原料粉末,准备均具有0.5-2μm范围内的规定的平均粒径的、连续结合相形成用的TiN粉末和TiCN粉末、以及TiC粉末、作为中间粘附相形成用的WC粉末、还有作为(Ti,Al)N粉末的(Ti0.65Al0.35)N粉末、(Ti0.50Al0.50)N粉末、和(Ti0.355Al0.65)N粉末(组成式内的数字均表示原子比)、以及硬质分散相形成用的c-BN粉末,将这些原料粉末配合成表1、2所示的配合组成,用球磨机湿式混合72小时,干燥后,以100MPa的压力加压成型为具有直径:50mm×厚度:1.5mm的尺寸的成型体,将此成型体在压力:1Pa的真空气氛中、在900-1300℃的范围内的规定温度保持1小时的条件下预烧结,接着,在将它与另行准备的具有直径:50mm×厚度:2mm的尺寸的超硬合金刀片(组成:WC-8%Co)重合的状态下装入超高压烧结装置,在1200-1400℃的范围内的规定温度在5GPa的压力下保持30分钟的条件下烧结,烧结后使用金刚石磨料磨削上下面,采用电火花放电的线切割进行尺寸制备,由此分别制造了用上述超硬合金衬里的本发明c-BN基烧结切削刀片(以下叫做本发明切削刀片)1-12和比较c-BN基烧结切削刀片(以下叫做比较切削刀片)1-12。
比较切削刀片1-12,均具有作为中间粘附相形成成分的(Ti,Al)N粉末和WC粉末之中的某一配合比例脱离本发明的范围的配合组成。
另外,关于本发明切削刀片11和比较切削刀片11,将其在丙酮中超声波洗涤,干燥,在此状态下安装在通常的电弧离子镀装置内,安装金属Ti作为阴极(蒸发源),首先将装置内排气,一边保持在0.5Pa或以下的真空,一边用加热器将装置内加热至500℃后,对上述切削刀片外加-1000V的直流偏电压,另一方面,在阴极上述金属Ti与阳极之间流过100A的电流,使发生电弧放电,就此将上述切削刀片表面进行Ti轰击洗涤,接着向装置内导入反应气体氮气,形成5Pa的反应气氛,同时对上述切削刀片外加-100V的直流偏电压,另一方面,在阴极与阳极之间流过100A的电流,使发生电弧放电,就此,在上述本发明切削刀片11和比较切削刀片11的表面蒸镀形成了均为1.5μm的平均层厚、具有黄金色的色调的TiN层。
关于构成此结果得到的各种切削刀片的各自的c-BN基材料,用扫描电镜观察其组织,任何切削刀片实质上都显示出包含连续结合相、硬质分散相、以及介在于上述连续结合相和硬质分散相之间的中间粘附相的3相组织。
此外,将这些切削刀片钎焊在超硬合金本体(组成:WC-10%Co)的切削刃端头部形成的切槽台部,由此制成具有JIS·TNMA160408规定的形状的多刃刀片型切削工具,关于本发明切削刀片1-4和比较切削刀片1-4,进行在被削材:渗碳淬火钢(JIS·SCM415、硬度:HRC62)的圆棒、
切削速度:350m/min、
切削深度:0.15mm、
走刀量:0.1mm/rev、
切削时间:30分的条件下的难切削材的干式高速连续车削试验;关于本发明切削刀片5-8和比较切削刀片5-8,进行在被切削材:渗碳淬火钢(JIS·SCM415、硬度:HRC62)的长度方向等间隔开有4条纵沟槽的圆棒、
切削速度:300m/min、
切削深度:0.15mm、
走刀量:0.2mm/rev、
切削时间:60分的条件下的难切削材的干式高速断续表面精切削试验;关于本发明切削刀片9-12和比较切削刀片9-12,进行在被切削材:球墨铸铁(JIS·FCD70)、
切削速度:450m/min、
切削深度:0.15mm、
走刀量:0.2mm/rev、
切削时间:30分的条件下的难切削材的干式高速连续表面精切削试验,所有切削试验都测定了切削刃的后隙面磨损宽。表1、2表示出该测定结果。
另外,对于在上述切削刀片表面蒸镀形成了作为切削刀片使用前后识别层的具有黄金色色调的TiN层的切削刀片,观察了上述切削试验后的表面,切削刃部的前倾面和后隙面的切粉接触部、以及前倾面和后隙面交叉的切削刃棱线部的上述TiN层磨损减少,在上述TiN层磨损减少部分上露出切削刀片基体具有的灰色色调,由这些上述TiN层磨损减少部分以外的部分的黄金色与上述切削刀片基体的灰色的对比,可容易地进行使用前后的识别。
表1
种类 | 配合组成(质量%) | 后隙面磨损宽(mm) | ||||||||
TiN | TiCN | Tic | (Ti0.65Al0.35)N | (Ti0.50Al0.50)N | (Ti0.35Al0.65)N | WC | c-BN | |||
本发明切削刀片 | 1 | 16 | 30 | - | 2 | - | - | 2 | 余量(50) | 0.24 |
2 | 20 | - | 17 | 2 | 4 | - | 3 | 余量(54) | 0.24 | |
3 | - | 43 | - | - | 2 | 2 | 5 | 余量(48) | 0.22 | |
4 | - | 30 | 15 | - | 8 | - | 7 | 余量(40) | 0.20 | |
5 | 6 | 18 | 5 | - | - | 7 | 8 | 余量(56) | 0.25 | |
6 | 18 | 8 | - | 3 | - | 5 | 8 | 余量(58) | 0.24 | |
7 | - | 22 | 6 | 1 | 1 | 2 | 8 | 余量(60) | 0.20 | |
8 | 10 | - | 8 | 2 | 3 | 2 | 10 | 余量(65) | 0.20 | |
9 | 16 | 16 | - | 3 | - | 4 | 6 | 余量(55) | 0.23 | |
10 | 14 | - | 13 | - | 2 | 3 | 6 | 余量(62) | 0.20 | |
11 | 10 | 17 | 10 | - | - | 7 | 4 | 余量(52) | 0.18 | |
12 | 22 | - | 22 | 2 | 2 | 2 | 7 | 余量(43) | 0.18 |
表2
种类 | 配合组成(质量%) | 切削试验结果 | ||||||||
TiN | TiCN | Tic | (Ti0.65Al0.35)N | (Ti0.50Al0.50)N | (Ti0.35Al0.65)N | WC | c-BN | |||
比较切削刀片 | 1 | 16 | 31 | - | 1※ | - | - | 2 | 余量(50) | 2分钟达到使用寿命 |
2 | 21.5 | - | 18 | 2 | 4 | - | 0.5※ | 余量(54) | 8分钟达到使用寿命 | |
3 | - | 36 | - | - | 4※ | 4※ | 5 | 余量(48) | 9分钟达到使用寿命 | |
4 | - | 30 | 10 | - | 8 | - | 12※ | 余量(40) | 8分钟达到使用寿命 | |
5 | 9 | 18 | 8.5 | - | - | 0.5※ | 8 | 余量(56) | 2分钟达到使用寿命 | |
6 | 18 | 14.5 | - | 3 | - | 5 | 1.5※ | 余量(58) | 1分钟达到使用寿命 | |
7 | - | 18 | 2 | 4※ | 2※ | 6※ | 8 | 余量(60) | 1分钟达到使用寿命 | |
8 | 10 | - | 7 | 2 | 3 | 2 | 11※ | 余量(65) | 4分钟达到使用寿命 | |
9 | 19 | 19 | - | 0.5※ | - | 0.5※ | 6 | 余量(55) | 8分钟达到使用寿命 | |
10 | 11 | - | 10 | - | 6※ | 5※ | 6 | 余量(62) | 12分钟达到使用寿命 | |
11 | 10 | 20 | 10 | - | - | 7 | 1※ | 余量(52) | 10分钟达到使用寿命 | |
12 | 20 | - | 19 | 2 | 2 | 2 | 12※ | 余量(43) | 15分钟达到使用寿命 |
(表中,※号表示本发明范围以外,使用寿命以切削刀发生的崩刃为原因)
由表1、2所示的结果明确知道,本发明切削刀片1-12,即使以高速进行车削或表面精切削作为难切削材的渗碳淬火钢,切削刃均不会发生崩刃,显示优异的耐磨性,长期发挥优异的切削性能,相比之下,如在比较切削刀片1-12上所见,作为中间粘附相形成成分的Ti-Al化合物粉末和WC粉末之中的任一配合比例脱离本发明范围,切削刃都发生崩刃,以此为因,在比较短的时间就达到使用寿命。
如上述,本发明的c-BN基烧结切削刀片,构成硬质分散相的c-BN相通过中间粘附相的介在而极为牢固地粘附在实质上构成连续结合相的TiCN相上,通常条件下的切削加工不用说,按照上述即使高速切削或高速表面精切削高硬度淬火钢等难切削材,也发挥优异的耐崩刃性,因此也能够充分满足地适应切削装置的高性能化和高输出功率化、以及切削加工的省力和节能化。
下面,通过第2实施例具体地说明本发明的c-BN基烧结切削刀片。
作为原料粉末,准备均具有0.5-4μm范围内的规定的平均粒径的、连续结合相形成用的TiN粉末和TiCN粉末、作为中间粘附相形成用的Ti-Al化合物粉末、Ti2AlN粉末、和WC粉末、以及硬质分散相形成用的c-BN粉末,将这些原料粉末配合成表3所示的配合组成,用球磨机湿式混合72小时,干燥后,以100MPa的压力加压成型为具有直径:50mm×厚度:1.5mm的尺寸的成型体,将此成型体在真空中、在900-1300℃的范围内的规定温度保持1小时的条件下预烧结,接着,在将它与另行准备的具有直径:50mm×厚度:2mm的尺寸的超硬合金刀片(组成:WC-8%Co)重合的状态下装入超高压烧结装置,在1200-1400℃的范围内的规定温度在5GPa的压力下保持30分钟的条件下烧结,烧结后使用金刚石磨料磨削上下面,实施电火花放电的线切割,由此分别制造了用上述超硬合金衬里的本发明c-BN基烧结切削刀片(以下叫做本发明切削刀片)1-8和比较c-BN基烧结切削刀片(以下叫做比较切削刀片)1-6。
比较切削刀片1-6,均具有作为中间粘附相形成成分的Ti-Al化合物粉末、Ti2AlN粉末、和WC粉末之中的任一的配合比例脱离本发明的范围的配合组成。
另外,关于本发明切削刀片8和比较切削刀片6,将其在丙酮中超声波洗涤,干燥,在此状态下安装在通常的电弧离子镀装置内,安装金属Ti作为阴极(蒸发源),首先将装置内排气,一边保持在0.5Pa或以下的真空,一边用加热器将装置内加热至500℃后,对上述切削刀片外加-1000V的直流偏电压,另一方面,在阴极上述金属Ti与阳极之间流过100A的电流,使发生电弧放电,就此将上述切削刀片表面进行Ti轰击洗涤,接着向装置内导入反应气体氮气,形成5Pa的反应气氛,同时对上述切削刀片外加-100V的直流偏电压,另一方面,在阴极与阳极之间流过100A的电流,使发生电弧放电,就此,在上述本发明切削刀片8和比较切削刀片6的表面蒸镀形成了均为1.5μm的平均层厚、具有黄金色的色调的TiN层。
关于构成此结果得到的各种切削刀片的各自的c-BN基材料,用扫描电镜观察其组织,任何切削刀片实质上都显示出包含连续结合相、硬质分散相、以及介于上述连续结合相和硬质分散相之间的中间粘附相的3相组织。
此外,将这些切削刀片钎焊在在超硬合金本体(组成:WC-10重量%Co)的切削刃端头部形成的切槽台部,由此制成具有JIS·TNMA160408规定的形状的多刃刀片型切削工具,进行在被削材:渗碳淬火钢(JIS·SCM415、硬度:HRC62)的长度方向等间隔开有4条纵沟槽的圆棒、切削速度:300m/min、切削深度:0.12mm、走刀量:0.15mm/rev、切削时间:45分的条件下的难切削材的干式高速表面精切削试验,测定了切削刃的后隙面磨损宽。表3表示出该测定结果。
另外,对于在上述切削刀片表面蒸镀形成了作为切削刀片使用前后识别层的具有黄金色色调的TiN层的切削刀片,观察了上述切削试验后的表面,切削刃部的前倾面和后隙面的切粉接触部、以及前倾面和后隙面交叉的切削刃棱线部的上述TiN层磨损减少,在上述TiN层磨损减少部分上露出切削刀片基体具有的灰色色调,由这些上述TiN层磨损减少部分以外的部分的黄金色与上述切削刀片基体的灰色的对比,可容易地进行使用前后的识别。
表3
种类 | 配合组成(质量%) | 后隙面磨损宽(mm) | 烧结体组成(质量%) | ||||||||||
Ti-Al化合物 | Ti2AlN | WC | TiN | TiCN | c-BN | TiN | TiCN | (Ti,Al,W)CN | c-BN | ||||
本发明切削刀片 | 1 | 3 | 7 | 8 | - | 37 | 余量(45) | 0.24 | 5 | 35 | 15 | 余量(45) | |
2 | 6 | 7 | 8 | 17 | 8 | 余量(54) | 0.2 | 22 | 7 | 17 | 余量(54) | ||
3 | 8 | 7 | 8 | 25 | - | 余量(52) | 0.22 | 27 | - | 21 | 余量(52) | ||
4 | 6 | 5 | 8 | 21 | 5 | 余量(55) | 0.19 | 28 | 5 | 15 | 余量(52) | ||
5 | 6 | 10 | 5 | - | 30 | 余量(46) | 0.23 | 4 | 29 | 21 | 余量(46) | ||
6 | 6 | 7 | 5 | 37 | - | 余量(45) | 0.22 | 41 | - | 14 | 余量(45) | ||
7 | 6 | 7 | 12 | 10 | 15 | 余量(50) | 0.18 | 12 | 15 | 23 | 余量(50) | ||
8 | 6 | 7 | 15 | 12 | 8 | 余量(52) | 0.19 | 15 | 8 | 25 | 余量(52) | ||
比较切削刀片 | 1 | 1.5※ | 7 | 8 | - | 37 | 余量(46.5) | 18分钟达到使用寿命 | 2.5 | 37 | 14 | 余量(46.5) | |
2 | 9.5※ | 7 | 8 | 25 | - | 余量(50.5) | 15分钟达到使用寿命 | 28.5 | - | 21 | 余量(50.5) | ||
3 | 6 | 3.5※ | 8 | 21 | 5 | 余量(56.5) | 17分钟达到使用寿命 | 23.5 | 5 | 15 | 余量(56.5) | ||
4 | 6 | 11※ | 3 | - | 30 | 余量(45) | 12分钟达到使用寿命 | 2 | 30 | 23 | 余量(45) | ||
5 | 6 | 7 | 3※ | 37 | - | 余量(47) | 17分钟达到使用寿命 | 40 | - | 13 | 余量(47) | ||
6 | 6 | 7 | 17※ | 12 | 8 | 余量(50) | 9分钟达到使用寿命 | 14 | 8 | 28 | 余量(50) | ||
其它实施例 | 配合组成(质量%) | 后隙面磨损宽(mm) | |||||||||||
Ti-Al化合物 | Ti2AlN | WC | TiN | TiCN | c-BN | TaC | NbC | ||||||
9 | 8 | 7 | 8 | 12 | 5 | 余量(50) | 10 | - | 0.21 | ||||
10 | 8 | 7 | 8 | 12 | 5 | 余量(50) | - | 10 | 0.19 |
(表中,※号表示本发明范围以外,使用寿命以切削刀发生的崩刃为原因)
由表3所示的结果明确知道,本发明切削刀片1-8,即使以高速进行表面精切削作为难切削材的渗碳淬火钢,切削刃均不会发生崩刃,显示优异的耐磨性,长期发挥优异的切削性能,相比之下,如在比较切削刀片1-6上所见,即使作为中间粘附相形成成分的Ti-Al化合物粉末、Ti2AlN粉末、和WC粉末之中的某种的配合比例脱离本发明范围,切削刃也发生崩刃,以此为因,在比较短的时间就达到使用寿命。
表3中,作为其他实施例,也记载了利用将作为连续结合相形成成分的TiN和TiCN的一部分置换成TaC(碳化钽)的切削刀片9、同样将TiN和TiCN的一部分置换成NbC的切削刀片10,与上述同样地进行难切削材的干式高速表面精切削试验时的切削刃的后隙面磨损宽。这些切削刀片9、10有与切削刀片1-8一样,即使以高速进行渗碳淬火钢的表面精切削,切削刃也不会发生崩刃,显示优异的耐磨损性。
如上述,本发明的c-BN基烧结切削刀片,构成硬质分散相的c-BN相通过中间粘附相的介在而极为牢固地粘附在构成连续结合相的TiN和TiCN上,通常条件下的表面精切削不用说,按照上述即使高速表面精切削高硬度淬火钢等难切削材,也发挥优异的耐崩刃性,因此也能够充分满足地适应切削装置的高性能化和高输出功率化、以及切削加工的省力和节能化。
Claims (6)
1.一种切削刀片,其特征在于,是用立方晶氮化硼基超高压烧结材料构成,所述烧结材料在扫描电镜的组织观察中实质上显示连续结合相、硬质分散相、以及介于上述连续结合相和硬质分散相之间的中间粘附相3相组织,
作为上述连续结合相形成成分含有钛化合物,
作为上述中间粘附相形成成分至少含有Ti与Al的复合氮化物、和碳化钨,
作为上述硬质分散相形成成分含有立方晶氮化硼。
2.根据权利要求1所述的切削刀片,其特征在于,其具有下述的配合组成,即包含:
作为上述连续结合相形成成分,
氮化钛、碳氮化钛、和碳化钛之中的2种或以上、或者碳氮化钛:15-56质量%;
作为上述中间粘附相形成成分,
Ti与Al的复合氮化物:2-10质量%、
碳化钨:2-10质量%;
作为上述硬质分散相形成成分,
立方晶氮化硼:余量,但是含有35-65质量%。
3.根据权利要求1所述的切削刀片,其特征在于,其具有下述的配合组成,即包含:
作为上述连续结合相形成成分,
氮化钛和/或碳氮化钛:20-37质量%;
作为上述中间粘附相形成成分,
Ti与Al的金属间化合物:3-8质量%、
Ti与Al的复合氮化物:5-10质量%、
碳化钨:5-15质量%;
作为上述硬质分散相形成成分,
立方晶氮化硼:余量,但是含有35-55质量%。
4.根据权利要求1所述的切削刀片,其特征在于,其具有如下的配合组成,即包含:
作为上述连续结合相形成成分,
氮化钛和/或碳氮化钛:10-32质量%、
碳化钽:5-10质量%;
作为上述中间粘附相形成成分,
Ti与Al的金属间化合物:3-8质量%、
Ti与Al的复合氮化物:5-10质量%、
碳化钨:5-15质量%;
作为上述硬质分散相形成成分,
立方晶氮化硼:余量,但是含有35-55质量%。
5.根据权利要求1所述的切削刀片,其特征在于,其具有如下的配合组成,即包含:
作为上述连续结合相形成成分,
氮化钛和/或碳氮化钛:10-32质量%、
碳化铌:5-10质量%;
作为上述中间粘附相形成成分,
Ti与Al的金属间化合物:3-8质量%、
Ti与Al的复合氮化物:5-10质量%、
碳化钨:5-15质量%;
作为上述硬质分散相形成成分,
立方晶氮化硼:余量,但是含有35-55质量%。
6.根据权利要求1所述的切削刀片,其特征在于,在切削刀片表面蒸镀形成作为刀片使用前后识别层的具有0.5-5μm的平均层厚的氮化钛层。
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CN101892412A (zh) * | 2010-06-23 | 2010-11-24 | 郑州博特硬质材料有限公司 | 一种立方氮化硼/碳化钛复合烧结刀具材料及其制备方法 |
CN101293773B (zh) * | 2007-04-27 | 2012-12-12 | 山特维克知识产权股份有限公司 | 切削工具刀片 |
CN103011832A (zh) * | 2012-12-03 | 2013-04-03 | 合肥杰事杰新材料股份有限公司 | 一种立方氮化硼复合材料钳子及其制作方法 |
CN104418594B (zh) * | 2013-08-27 | 2018-11-23 | 三菱综合材料株式会社 | 立方晶氮化硼烧结体切削工具及其制造方法 |
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JP4927559B2 (ja) | 2004-10-28 | 2012-05-09 | 京セラ株式会社 | 立方晶窒化硼素質焼結体およびそれを用いた切削工具 |
SE529290C2 (sv) | 2005-10-28 | 2007-06-19 | Sandvik Intellectual Property | Skär av kubisk bornitrid beständigt mot urflisning och eggbrott |
US8507082B2 (en) | 2011-03-25 | 2013-08-13 | Kennametal Inc. | CVD coated polycrystalline c-BN cutting tools |
JP5892423B2 (ja) * | 2012-03-08 | 2016-03-23 | 三菱マテリアル株式会社 | 靭性にすぐれたcBN焼結体切削工具 |
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- 2003-02-28 US US10/510,239 patent/US7112235B2/en not_active Expired - Lifetime
- 2003-02-28 WO PCT/JP2003/002362 patent/WO2003089172A1/ja active Application Filing
- 2003-02-28 KR KR1020097017127A patent/KR101121412B1/ko active IP Right Grant
- 2003-02-28 DE DE60333829T patent/DE60333829D1/de not_active Expired - Lifetime
- 2003-02-28 KR KR10-2004-7016416A patent/KR20040101476A/ko active Search and Examination
- 2003-02-28 EP EP03746884A patent/EP1498199B1/en not_active Expired - Lifetime
- 2003-02-28 CN CN038143224A patent/CN1662334B/zh not_active Expired - Lifetime
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
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CN101293773B (zh) * | 2007-04-27 | 2012-12-12 | 山特维克知识产权股份有限公司 | 切削工具刀片 |
CN101892412A (zh) * | 2010-06-23 | 2010-11-24 | 郑州博特硬质材料有限公司 | 一种立方氮化硼/碳化钛复合烧结刀具材料及其制备方法 |
CN101892412B (zh) * | 2010-06-23 | 2012-05-23 | 郑州博特硬质材料有限公司 | 一种立方氮化硼/碳化钛复合烧结刀具材料及其制备方法 |
CN103011832A (zh) * | 2012-12-03 | 2013-04-03 | 合肥杰事杰新材料股份有限公司 | 一种立方氮化硼复合材料钳子及其制作方法 |
CN103011832B (zh) * | 2012-12-03 | 2016-08-17 | 合肥杰事杰新材料股份有限公司 | 一种立方氮化硼复合材料钳子及其制作方法 |
CN104418594B (zh) * | 2013-08-27 | 2018-11-23 | 三菱综合材料株式会社 | 立方晶氮化硼烧结体切削工具及其制造方法 |
Also Published As
Publication number | Publication date |
---|---|
EP1498199A1 (en) | 2005-01-19 |
KR20040101476A (ko) | 2004-12-02 |
US20050145066A1 (en) | 2005-07-07 |
US7112235B2 (en) | 2006-09-26 |
EP1498199B1 (en) | 2010-08-18 |
CN1662334B (zh) | 2010-09-01 |
DE60333829D1 (de) | 2010-09-30 |
KR20090101383A (ko) | 2009-09-25 |
WO2003089172A1 (fr) | 2003-10-30 |
EP1498199A4 (en) | 2007-05-02 |
KR101121412B1 (ko) | 2012-03-22 |
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