CN1049647A - 陶瓷金属复合物 - Google Patents
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Abstract
由金属侵入多孔性陶瓷组成的陶瓷金属复合物,
其特征在于,陶瓷由几层组成,层厚保持在10-150
微米,平均孔径保持在100-1000mm之间,开孔孔隙
率为5-14%,总孔隙率为5-30%,除去剩余孔隙率
之外填入金属的孔隙体积为最新的孔隙率的
0.1-10%。
Description
本发明涉及由金属浸入多孔性陶瓷组成的陶瓷金属复合物。
这种类型的陶瓷金属复合物在欧洲专利O155 831(Lanxide)中揭示出。按照Lanxide专利的权利要求11,要使陶瓷体具有良好的渗透性,其小角晶粒周边必须保持在一定的范围内。
1985年7月23日日本专利61/163224(Sumitomo Electric Industries)揭示,在压力作用下,将铝熔体浸入孔隙为85-90%的陶瓷体。
再者,1985年5月30日英国专利21 48 270(British Ceramic Research Association)揭示,在6.72Kpsi的压力下,将在700℃熔化的铝浸入孔隙率为39%的多孔性SiC陶瓷,可得到陶瓷合金。
此外,1983年10月1日捷克和斯洛伐克专利CS20 61 32中描述的陶瓷合金的制造方法为:清除多孔性陶瓷材料中90-95%的Al2O3,剩余的是SiO2,并在压力超过1Mpa的惰性气体下,浸入700°-900℃的铝或铝复合物。浸入之前,模制陶瓷品的孔隙率为41%。
因此,将金属熔体浸入这种高度多孔性陶瓷材料,以使其产品具有显著的金属特征。陶瓷金属复合物的主要特征表现为金属性特征,这样它的硬度、耐温性、耐磨性就大大低于严格的陶瓷材料。
本发明的目标是改善陶瓷材料的弯曲强度、刚度、弹性系数、硬度以及耐磨性。处理后的陶瓷材料的硬度、耐高温性和耐磨性等特征优于金属材料。
实现该目标的方法是制成了由金属侵入多孔性陶瓷组成的陶瓷金属复合物,其特征左右,陶瓷由几层组成,层厚保持在10-150微米,平均孔径保持在100-1000mm之间,开孔孔隙率为5-14%,总孔隙率为5-30%,除去剩余孔隙率之外填入金属的孔隙体积为最新的孔隙率的0.1-10%。已查明,将熔化金属浸入总孔隙率为5-30%的多层结构的陶瓷,能够得到想要的特征组合。此外,所谓总孔隙率就是陶瓷在浸入熔化金属前的原有孔隙率。这里尤为重要的是,借助Carlo-Erba水银孔率计测定的平均孔隙半径为100-1000nm。
本发明中使用的金属有铝或铝合金,尤其是铝-硅合金,镁,铅,锌或铜,钢或灰铸铁,钛或钛合金。而用作陶瓷的有纯氧化物陶瓷,预反应态的以氧化物为基础的多成份物料尤其是2种或多种纯金属氧化物在等离子流中就地反应后的氧化物陶瓷。
借助多层结构得到的陶瓷材料的孔网结构使浸入熔化金属的方法变的十分便利。按照本发明,可通过陶瓷材料的粒径以及液态等离子流的流速来控制该孔网结构。
如果陶瓷具有由彼此相互连接的孔和孔道组成的孔网结构,Lanxide专利中的小角晶粒周边则不必借助实验设备确定。按照本发明,如果陶瓷由几个不同孔隙率的薄层依次组成,该特殊结构就存在。
对于应用像焊接或低温焊接陶瓷/金属这样的金属连接结构来说,陶瓷材料的孔隙率由里向外增加以使金属的比例朝外增加,被让实是有效的。这样的孔网结构被称为“梯度结构”。其复合物的外部主要表现为金属特征,内部主要表现为陶瓷特征。
通过改变喷射到基体上的液态稳定等离子流的粒径获得这种梯度结构。例如,最新最好用d粒径为20微米,陶瓷材料外层的粒径增加到d值超过100微米。反之亦然,这取决于金属表面的朝向,主要的是,陶瓷材料最接近金属结构的表面是用大粒径粉产生的。
建立在氧化层基础上的多层复合材料,在预反应状态下能够有利地被用来增加硬度和改善耐磨性。多层复合材料被看成两种或更多种陶瓷氧化材料,通过碾磨并在烧结温度预反应形成的粉末的混合物。此后,将它们加入等离子燃烧器的反应区。
下面通过几个操作例子更详细地描述该发明。本发明的陶瓷金属复合物的生产,先要经过等离子喷射,然后将金属浸入CMC。与通常的Lanxide专利的CMC材料相比,通过以上操作,本发明的CMC材料的特征被认为得到了显著改善,如果他们的梯度结构定义为:复合物中不同层的陶瓷颗粒有不同的形状系数,特别是有一个从内到外增加或减少的形状系数。陶瓷颗粒层形状系数大于5。
密度和孔隙率通过DIN51056方法测定,维氏硬度用DIN50133方法测定。首先,Al2O3和Al2TiO5材料板通过等离子喷射产生,d50粒径在60-70微米之间,等离子流速为300m/a,单层厚度为100微米,氧化铝的总孔隙率达到18%,钛酸铝为15%。形成的喷射表面氧化铝对于氧化铝1∶5-1∶20,对于钛酸铝1∶15-1∶25。
从这些板块中割取100×100×300mm大小的试样测定材料的特征值,将试样预热到1000℃,并在压力差为35巴、最多5秒钟内,浸入由Al Si 10Mg合金组成的温度为750℃的金属熔体。在程序控制炉内,浸入后的冷却速度为每小时200℃,以使试样在5小时内冷却到室内温度。
在这之后,发现剩余的孔隙体积为氧化铝陶瓷的最新孔隙率的5%,以及钛酸铝的7%。
进一步的实验体产生于本发明的梯度结构,制造方法同上;只是用40和100微米这两种不同的d50粒径分别通过两孔道。d50值为40微米的颗粒连续从O增加到25kg/h,d50值为100微米的颗粒在25kg/h到O这个相同的范围内减少。从一个孔道转换到另一个孔道的时间,取决于陶瓷体的大小和它的壁的厚度。这样获得的单层厚度保持在80-100微米,总孔隙率为12%。在用Al Si 10Mg合金浸入后,实验体剩余孔隙体积为最新孔隙率的0.6%。
在实验体上测定的(特征)值见表1。弯曲强度(4点装置测定),弹性模数,断裂强度在大小为3.5×4.5∶45mm的标准抗弯样品上测定。给定文献中通常的Al2O3陶瓷烧结整体材料数据进行比较,结果是,按照本发明得到的金属-陶瓷复合物的弯曲强度,断裂强度和硬度值较好,与常规材料的复合材料特征值以及个别特征值相比较有明显改善。
Claims (16)
1、由金属侵入多孔性陶瓷组成的陶瓷金属复合物,其特征左右,陶瓷由几层组成,层厚保持在10-150微米,平均孔径保持在100-1000mm之间,开孔孔隙率为5-14%,总孔隙率为5-30%,除去剩余孔隙率之外填入金属的孔隙体积为最新的孔隙率的0.1-10%。
2、权利要求1的陶瓷金属复合物,其特征在于,由陶瓷颗粒形成的层的形状系数大于5。
3、以上权利要求之一的陶瓷金属复物,其特征在于,复合物中不同层的陶瓷颗粒有不同的形状系数。
4、以上权利要求之一的陶瓷金属复合物,其特征在于,陶瓷颗粒有一个从内到外增加的形状系数。
5、以上权利要求之一的陶瓷金属复合物,其特征在于,提出颗粒具有一个从内向外减少的形状系数。
6、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的金属为铝或铝合金。
7、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的金属为铝-硅合金。
8、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的金属为铝、镁、铅、锌、铜。
9、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的金属为钢或灰铸铁。
10、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的金属为钛或钛合金。
11、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的陶瓷为纯氧化物陶瓷材料。
12、以上权利要求之一的陶瓷金属复合物,其特征在于,在预反应状态使用的陶瓷为建立在氧化层基础之上的多层材料。
13、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的陶瓷为氧化物陶瓷材料-通过在等离子流中就地反应的方法,由两种或更多种纯金属氧化物形成。
14、以上权利要求之一的陶瓷金属复合物,其特征在于,使用的陶瓷为氧化铝或钛酸铝。
15、用金属结构固接的陶瓷金属复合物的应用,其特征在于,面向金属结构的复合物。面与壁开金属结构的面相比较,前者富含金属。
16、以上权利要求之一的陶瓷金属复合物的应用,其特征在于,陶瓷朝向金属结构的面与壁开金属结构的面相比较,前者具有一个大倍数的形状系数。
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Cited By (4)
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CN103072363A (zh) * | 2012-12-12 | 2013-05-01 | 西北工业大学 | 结构可设计的抗高能和二次冲击的金属/陶瓷层状复合材料的制备方法 |
CN108129169A (zh) * | 2016-12-01 | 2018-06-08 | 比亚迪股份有限公司 | 一种金属陶瓷制品及其制备方法 |
CN108745491A (zh) * | 2018-06-21 | 2018-11-06 | 湖北秦鸿新材料股份有限公司 | 一种磨煤机高耐磨辊套及其制备方法 |
CN109071365A (zh) * | 2016-02-26 | 2018-12-21 | 贺利氏德国有限两合公司 | 铜-陶瓷复合物 |
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GB2287038A (en) * | 1993-09-30 | 1995-09-06 | Automotive Products Plc | Metal matrix composites |
GB9320150D0 (en) * | 1993-09-30 | 1993-11-17 | Automotive Products Plc | Metal matrix composite components |
GB2365875B (en) * | 1998-12-30 | 2003-03-26 | Intellikraft Ltd | Solid state material |
ES2153708T5 (es) * | 1999-04-09 | 2006-06-01 | W.C. Heraeus Gmbh | Preparado brillante de metal noble. |
DE10113590A1 (de) * | 2001-03-20 | 2002-10-02 | Drm Druckgus Gmbh | Verfahren zum Herstellen eines Konstruktionsteils |
CN105734325A (zh) * | 2016-03-17 | 2016-07-06 | 合肥晨煦信息科技有限公司 | 一种陶瓷金属基复合材料及其制备方法 |
DE102021004325A1 (de) | 2021-08-24 | 2023-03-02 | HiPer Medical AG | Mehrphasiger Keramik- Keramik- Verbundkörper und Verfahren zu dessen Herstellung |
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NZ211405A (en) * | 1984-03-16 | 1988-03-30 | Lanxide Corp | Producing ceramic structures by oxidising liquid phase parent metal with vapour phase oxidising environment; certain structures |
DE3543342A1 (de) * | 1985-12-07 | 1987-06-11 | Bojak Kurt | Verbund-werkstoff mit hoher verschleiss- und form-festigkeit und verfahren zur herstellung |
JPS62156938A (ja) * | 1985-12-28 | 1987-07-11 | 航空宇宙技術研究所 | 傾斜機能材料の製造方法 |
US4718941A (en) * | 1986-06-17 | 1988-01-12 | The Regents Of The University Of California | Infiltration processing of boron carbide-, boron-, and boride-reactive metal cermets |
DE3724995A1 (de) * | 1987-02-26 | 1988-09-08 | Radex Heraklith | Verfahren zur herstellung eines verbundkoerpers und verbundkoerper selbst |
DE3914010C2 (de) * | 1989-04-26 | 1995-09-14 | Osaka Fuji Corp | Verfahren zur Herstellung von Metall-Keramik-Verbundwerkstoffen sowie Verwendung des Verfahrens zur Steuerung der Materialeigenschaften von Verbundwerkstoffen |
-
1989
- 1989-07-22 DE DE3924268A patent/DE3924268A1/de not_active Withdrawn
-
1990
- 1990-07-04 KR KR1019900010060A patent/KR910002737A/ko not_active Application Discontinuation
- 1990-07-06 NO NO90903034A patent/NO903034L/no unknown
- 1990-07-18 AT AT90113734T patent/ATE112249T1/de not_active IP Right Cessation
- 1990-07-18 CS CS903565A patent/CS356590A3/cs unknown
- 1990-07-18 DE DE59007316T patent/DE59007316D1/de not_active Expired - Lifetime
- 1990-07-18 EP EP90113734A patent/EP0410284B1/de not_active Expired - Lifetime
- 1990-07-20 HU HU904567A patent/HU904567D0/hu unknown
- 1990-07-20 CA CA002021645A patent/CA2021645A1/en not_active Abandoned
- 1990-07-20 FI FI903677A patent/FI903677A0/fi not_active IP Right Cessation
- 1990-07-21 CN CN90104772A patent/CN1049647A/zh active Pending
- 1990-07-23 JP JP2193198A patent/JPH03141182A/ja active Pending
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103072363A (zh) * | 2012-12-12 | 2013-05-01 | 西北工业大学 | 结构可设计的抗高能和二次冲击的金属/陶瓷层状复合材料的制备方法 |
CN109071365A (zh) * | 2016-02-26 | 2018-12-21 | 贺利氏德国有限两合公司 | 铜-陶瓷复合物 |
US11021406B2 (en) | 2016-02-26 | 2021-06-01 | Heraeus Deutschland GmbH & Co. KG | Copper-ceramic composite |
CN109071365B (zh) * | 2016-02-26 | 2022-03-08 | 贺利氏德国有限两合公司 | 铜-陶瓷复合物 |
CN108129169A (zh) * | 2016-12-01 | 2018-06-08 | 比亚迪股份有限公司 | 一种金属陶瓷制品及其制备方法 |
CN108129169B (zh) * | 2016-12-01 | 2021-01-19 | 比亚迪股份有限公司 | 一种金属陶瓷制品及其制备方法 |
CN108745491A (zh) * | 2018-06-21 | 2018-11-06 | 湖北秦鸿新材料股份有限公司 | 一种磨煤机高耐磨辊套及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
DE59007316D1 (de) | 1994-11-03 |
HU904567D0 (en) | 1990-12-28 |
NO903034D0 (no) | 1990-07-06 |
ATE112249T1 (de) | 1994-10-15 |
FI903677A0 (fi) | 1990-07-20 |
EP0410284B1 (de) | 1994-09-28 |
CS356590A3 (en) | 1992-01-15 |
NO903034L (no) | 1991-01-23 |
KR910002737A (ko) | 1991-02-26 |
EP0410284A3 (en) | 1991-03-20 |
EP0410284A2 (de) | 1991-01-30 |
CA2021645A1 (en) | 1991-01-23 |
JPH03141182A (ja) | 1991-06-17 |
DE3924268A1 (de) | 1991-01-31 |
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