TWI651293B - 韌性陶瓷材料 - Google Patents

韌性陶瓷材料 Download PDF

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TWI651293B
TWI651293B TW106140767A TW106140767A TWI651293B TW I651293 B TWI651293 B TW I651293B TW 106140767 A TW106140767 A TW 106140767A TW 106140767 A TW106140767 A TW 106140767A TW I651293 B TWI651293 B TW I651293B
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ceramic material
refractory metal
boride
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陳瑞凱
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國立清華大學
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Priority to CN201810195522.XA priority patent/CN109824363A/zh
Priority to US15/962,101 priority patent/US10562821B2/en
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Abstract

一種韌性陶瓷材料，該韌性陶瓷材料的組成係由至少一種硼化物及一種耐火金屬或是至少兩種硼化物、至少一種碳化物及一種耐火金屬，其中使用上述材料進行加熱熔煉能夠形成該韌性陶瓷材料，而於加熱熔煉為韌性陶瓷材料的過程中，該耐火金屬皆會與硼化物或/及碳化物反應，因此金屬膠結相會流失而形成為一具有高韌性的純陶瓷結構。

Description

韌性陶瓷材料
本發明係關於一種韌性陶瓷材料，特別是一種能夠將至少一種硼化物及一種耐火金屬或是至少兩種硼化物、至少一種碳化物及一種耐火金屬進行加熱熔煉形成為一具有高韌性的純陶瓷結構。
Cemented carbides為膠結碳化物，是一種由WC與Co組成的複合材料。十九世紀初，Henri Moissan人造合成碳化鎢(WC)。碳化鎢硬度高，原欲作為鑽石的替代材料，卻因存在易脆及孔洞等缺點，而不便用於工程上。1923年Schröter 和Baumhauer發現碳化鎢與鈷或鎳，經燒結製程後，可同時保有陶瓷材料的硬度，以及金屬的韌性，這對模具工業，造成巨大影響，材料並廣泛應用在切削工具、礦產採掘、與軍事武器的部分零件上。原料鎢約有60 %用在膠結碳化物的生產上。1930年使用需求量為十公噸，2008年使用需求量則達五萬公噸，78年內成長了5000倍。
膠結碳化物由兩部份組成，一為強化相、另一為膠結相。如上述所提的碳化鎢WC扮演著強化相的角色，擁有高熔點、高韌性、以及良好抗磨耗等特性，而鈷則為膠結相，擁有金屬良好的導電、導熱性之外，還有提供最重要的特性--韌度，使複材不易脆裂。近年的研究，大多以WC 與 Co系統硬質金屬為基礎，將強化相衍生出TiC與TaC等，膠結相衍生出Mo, Ni與Fe等，並通稱這些材料為「瓷金複材」 (Cermet composites)；傳統Hard metals硬質金屬以及瓷金複材，主要生產製程為燒結法，並且將膠結相進行「少量」之多元添加；然而，上述以傳統燒結法製成的超硬合金需擔心複材緻密度問題，且製程相對較複雜，成本較高，複材的工作溫度也有其極限。
因此，若能夠以熔煉方式進行製備材料，將能夠克服上述問題，然而若是能夠於加熱熔煉為韌性陶瓷材料的過程中，透過不同配方，使耐火金屬能夠僅與硼化物或/及碳化物反應，而金屬膠結相會流失並形成為一具有高韌性的純陶瓷結構，如此應為一最佳解決方案。
一種韌性陶瓷材料，該韌性陶瓷材料的組成係為至少一種硼化物及一種耐火金屬，其中該硼化物係選自於TiB 2、ZrB 2、NbB 2、HfB 2、TaB 2、W 2B 5，而該耐火金屬係為鎢或鉭，其中使用硼化物與耐火金屬進行加熱熔煉形成該韌性陶瓷材料。
於一較佳實施例中，其中使用硼化物與耐火金屬進行加熱熔煉為韌性陶瓷材料的過程中，該耐火金屬皆會與硼化物反應，因此金屬膠結相會流失而形成為一純陶瓷結構。
於一較佳實施例中，其中韌性陶瓷材料之微結構係由MB 2相、MB相或/及W 2B相所組成。
一種韌性陶瓷材料，該韌性陶瓷材料的組成係為至少兩種硼化物、至少一種碳化物及一種耐火金屬，其中該硼化物係選自於TiB 2、ZrB 2，而該碳化物係選自於SiC、B 4C、TiC、NbC、TaC、WC，且該耐火金屬係為鎢，其中使用硼化物、碳化物與耐火金屬進行加熱熔煉形成該韌性陶瓷材料。
於一較佳實施例中，其中使用硼化物、碳化物與耐火金屬進行加熱熔煉為韌性陶瓷材料的過程中，該耐火金屬會與硼化物或/及碳化物反應，因此金屬膠結相會流失而形成為一純陶瓷結構。
於一較佳實施例中，其中韌性陶瓷材料之微結構係由MB 2相、MC相、MB相或/及W 2B相所組成。
有關於本發明其他技術內容、特點與功效，在以下配合參考圖式之較佳實施例的詳細說明中，將可清楚的呈現。
請參閱第1圖，其製備方法如下： (1) 本發明是將至少一種硼化物及一種耐火金屬(或是至少兩種硼化物、至少一種碳化物及一種耐火金屬)充分混合後，置於真空電弧熔煉爐之水冷銅模的凹槽中101； (2) 之後將真空電弧熔煉爐抽真空(將腔體壓力抽至2.4 × 10 -2torr)後，通純氬氣(Ar氣體)使壓力提升至8.0 torr左右，並再度抽真空(抽至2.4 × 10 -2torr，此通Ar氣體再抽氣的動作稱為purge)，而上述動作反覆數次後，最後通Ar氣體使腔體壓力回到8.0 torr並進行熔煉102； (3) 而熔煉完成後待試片冷卻，將其翻面後再度熔煉，並反覆此動作數次，以確保試片的均勻度，最後等待試片冷卻後，使腔體壓力回到1大氣壓，並取出所形成的韌性陶瓷材料試片103。
而本發明會舉出幾個以下不同實施例，以下幾個實施例皆能夠明顯看出金屬膠結相會流失並形成為一具有高韌性的純陶瓷結構，其中第一實施(B1B2 + Ta)之成份為 (TiB 2) 0.3(ZrB 2) 0.3Ta 0.4，其中XRD分析如第2圖所示，峰值分析顯示相組成為MB, MB 2, M 2B，且明顯沒有膠結相Ta固溶體訊號，其中第一實施所製備出的韌性陶瓷材料具有近似純陶瓷之特性，且M 2B相分率高造成機械性質硬脆，整體硬度值為1842 ± 74 HV，破裂韌性為6.44 ± 0.99 MPa m 1/2。
其中第二實施(SB4)的成份為(NbB 2) 0.6W 0.4，其中XRD峰值第3圖所示，峰值顯示此成份有三種相，分別為M 2B, MB, MB 2，由於第二實施中之W幾乎全和B反應形成MB或M 2B，因此耐火金屬膠結相流失形成純陶瓷結構，而第二實施之硬度和韌性表現算是相當優秀，複材整體硬度值為1944 ± 56 HV，破裂韌性為7.72 ± 0.72 MPa m 1/2。
其中第三實施(B3B5)的成份為[(HfB 2)(TaB 2)] 0.6W 0.4，其中XRD峰值如第4圖所示，峰值顯示此成份有三種相，分別為M 2B, MB, MB 2，而第三實施之成份整體硬度值為1911 ± 93 HV，破裂韌性為5.12 ± 0.34 MPa m 1/2。
其中第四實施（ B3B6）的成份為[(HfB 2)(W 2B 5) 0.5] 0.6W 0.4，其中XRD峰值如第5圖所示，峰值顯示此成份有兩種相，分別為MB及MB 2，而第四實施之整體硬度值為1841 ± 87 HV，破裂韌性為5.66 ± 0.34 MPa m 1/2。
其中第五實施（ B4B5）的成份為[(NbB 2)(TaB 2)] 0.6W 0.4，其中XRD峰值如第6圖所示，峰值顯示此成份有兩種相，分別為MB及MB 2，第五實施中同樣沒有保留住膠結相，因此同為純陶瓷的結構，而複材整體硬度值為1996 ± 81 HV，破裂韌性為6.06 ± 0.24 MPa m 1/2。
其中第六實施（B4B6）的成份為[(NbB 2)(W 2B 5) 0.5] 0.6W 0.4，其中XRD峰值如第7圖所示，峰值顯示此成份有三種相，分別為M 2B, MB, MB 2，而第六實施之硬度韌性表現相當良好，此成份整體硬度值為2165 ± 28 HV，破裂韌性為7.88 ± 0.17 MPa m 1/2。
其中第七實施（(6B)6W4）的成份為[(TiB 2)(ZrB 2)(HfB 2)(NbB 2)(TaB 2)(W 2B 5) 0.5] 0.6W 0.4，其中XRD峰值如第8圖所示，峰值顯示此成份有兩種相，分別為MB及MB 2，而第七實施之整體硬度為1841 ± 87 HV，破裂韌性為5.06 ± 0.41 MPa m 1/2。
其中第八實施（B3B4 + W）的成份為[(HfB 2)(NbB 2)] 0.4W 0.6，其中XRD峰值如第9圖所示，峰值顯示此成份有三種相，分別為M 2B, MB, MB 2，而第八實施也如同前幾個實施例一般，也是失去金屬膠結相（大部份鎢金屬皆反應形成此硬脆相以及部份形成MB），而複材整體硬度值為1742 ± 48 HV，破裂韌性為6.88 ± 0.44 MPa m 1/2。
其中第九實施（B3B5 + W）的成份為[(HfB 2)(TaB 2)] 0.4W 0.6，其中XRD峰值如第10圖所示，峰值顯示此成份有兩種相，分別為W 2B和MB，而第九實施也同樣沒有明顯膠結相殘留，其整體硬度值為1863 ± 66 HV，破裂韌性為6.56 ± 0.44 MPa m 1/2。
其中第十實施（(5B)5W5）的成份為[(TiB 2)(ZrB 2)(HfB 2)(NbB 2)(TaB 2)] 0.5W 0.5，其中XRD峰值如第11圖所示，峰值顯示此成份有三種相，分別為W 2B, MB, MB 2，而第十實施之成份整體硬度值為2076 ± 56 HV，破裂韌性為5.99 ± 0.50 MPa m 1/2。
其中第十一實施（(4B)4W6）的成份為[(TiB 2)(ZrB 2)(NbB 2)(TaB 2)] 0.4W 0.6，其XRD峰值如第12圖所示，峰值顯示此成份有三種相，同樣為W 2B, MB, MB 2，其機械性質和(5B)5W5相近，硬度值為2045 ± 47 HV，破裂韌性為5.77 ± 0.37 MPa m 1/2。
其中第十二實施（+ SiC）的成份為[(TiB 2)(ZrB 2)(SiC)] 0.6W 0.4，其中XRD峰值如第13圖所示，峰值顯示此成份有四種相，分別為SiC, MSi 2, MB, MB 2，此試片的整體硬度值為1898 ± 65 HV，破裂韌性為5.89 ± 0.53 MPa m 1/2。
其中第十三實施（+B 4C）的成份為[(TiB 2)(ZrB 2)(B 4C)] 0.6W 0.4，其中XRD峰值如第14圖所示，峰值顯示此成份有三種相，分別為MC, MB, MB 2，本實施例成份因含有過多硼原子而產生大量粗大的MB 2相以及少量MB相，膠結相鎢均反應成此類陶瓷硼化物因而沒有觀察到有金屬固溶體生成。
其中第十四實施（+TZ）的成份為[(TiC)(NbC)(TaC)(WC)(TiB 2)(ZrB 2)] 0.6W 0.4，其中XRD峰值如第15圖所示，峰值顯示此成份有三種相，分別為MC, MB及M 2B，本實施例中微結構中未觀察到膠結相鎢固溶體，也沒有原先NT系列的層狀結構，僅有大量M 2B伴隨MC點狀分佈其中，其整體硬度值為2203 ± 83 HV，破裂韌性為6.03 ± 0.25 MPa m 1/2。
而上述實施中的微結構都沒有觀察到金屬膠結相殘留，因成份中含有大量的硼原子，加上金屬膠結相易和硼反應，因此難以保留膠結相鎢固溶體，故複材會形成近似純陶瓷的結構。
本發明所提供之韌性陶瓷材料，與其他習用技術相互比較時，其優點如下： 1. 本發明能夠以熔煉方式進行製備材料，將能夠克服上述問題，然而若是能夠於加熱熔煉為韌性陶瓷材料的過程中，透過不同配方，使耐火金屬能夠僅與硼化物或/及碳化物反應，而金屬膠結相會流失並形成為一具有高韌性的純陶瓷結構。 2. 由於本發明是的韌性陶瓷是由熔融反應而來，更由於因熔融製成而可有100%密度，而有高韌性，且熔煉出的製品更具有一定的硬度及韌性，且高溫下的硬度穩定性好，因此非常是適用於一般產業的使用。
本發明已透過上述之實施例揭露如上，然其並非用以限定本發明，任何熟悉此一技術領域具有通常知識者，在瞭解本發明前述的技術特徵及實施例，並在不脫離本發明之精神和範圍內，當可作些許之更動與潤飾，因此本發明之專利保護範圍須視本說明書所附之請求項所界定者為準。
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[第1圖]係本發明韌性陶瓷材料之製備流程示意圖。 [第2圖]係本發明韌性陶瓷材料之第一實施之XRD分析示意圖。 [第3圖]係本發明韌性陶瓷材料之第二實施之XRD分析示意圖。 [第4圖]係本發明韌性陶瓷材料之第三實施之XRD分析示意圖。 [第5圖]係本發明韌性陶瓷材料之第四實施之XRD分析示意圖。 [第6圖]係本發明韌性陶瓷材料之第五實施之XRD分析示意圖。 [第7圖]係本發明韌性陶瓷材料之第六實施之XRD分析示意圖。 [第8圖]係本發明韌性陶瓷材料之第七實施之XRD分析示意圖。 [第9圖]係本發明韌性陶瓷材料之第八實施之XRD分析示意圖。 [第10圖]係本發明韌性陶瓷材料之第九實施之XRD分析示意圖。 [第11圖]係本發明韌性陶瓷材料之第十實施之XRD分析示意圖。 [第12圖]係本發明韌性陶瓷材料之第十一實施之XRD分析示意圖。 [第13圖]係本發明韌性陶瓷材料之第十二實施之XRD分析示意圖。 [第14圖]係本發明韌性陶瓷材料之第十三實施之XRD分析示意圖。 [第15圖]係本發明韌性陶瓷材料之第十四實施之XRD分析示意圖。

Claims (2)

  1. 一種韌性陶瓷材料，該韌性陶瓷材料的組成係為至少一種硼化物及一種耐火金屬，其中該硼化物係選自於TiB2、ZrB2、NbB2、HfB2、TaB2、W2B5，而該耐火金屬係為鎢或鉭，其中使用硼化物與耐火金屬進行加熱熔煉形成該韌性陶瓷材料，而該韌性陶瓷材料之微結構係由MB2相、MB相或/及W2B相所組成，且使用硼化物與耐火金屬進行加熱熔煉為韌性陶瓷材料的過程中，該耐火金屬皆會與硼化物反應，因此金屬膠結相會流失而形成為一純陶瓷結構。
  2. 一種韌性陶瓷材料，該韌性陶瓷材料的組成係為至少兩種硼化物、至少一種碳化物及一種耐火金屬，其中該硼化物係選自於TiB2、ZrB2，而該碳化物係選自於SiC、B4C、TiC、NbC、TaC、WC，且該耐火金屬係為鎢，其中使用硼化物、碳化物與耐火金屬進行加熱熔煉形成該韌性陶瓷材料，而該韌性陶瓷材料之微結構係由MB2相、MC相、MB相或/及W2B相所組成，且使用硼化物、碳化物與耐火金屬進行加熱熔煉為韌性陶瓷材料的過程中，該耐火金屬會與硼化物或/及碳化物反應，因此金屬膠結相會流失而形成為一純陶瓷結構。
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