Boron carbide composite

Abstract

The present disclosure relates to boron carbide (B.sub.4C) composite material and the method of making and using the boron carbide (B.sub.4C) composite.

Claims

1. A composite material comprising a sintered product of a mixture comprising 70-95 wt. % of boron carbide (B.sub.4C), 2-15 wt. % of tungsten carbide-cobalt (WC—Co), and 3-15 wt. % of yttrium oxide (Y.sub.2O.sub.3), wherein said boron carbide, tungsten carbide-cobalt (WC—Co), and yttrium oxide are substantially uniformly distributed in the sintered product, wherein the sintered product has a relative density of 90-99%.

2. The composite material of claim 1, wherein the mixture comprises 70-90 wt. % of boron carbide (B.sub.4C), 5-15 wt. % of tungsten carbide-cobalt (WC—Co), and 5-15 wt. % of yttrium oxide (Y.sub.2O.sub.3).

3. The composite material of claim 1, wherein the sintered product has a relative density of 97-99%.

4. The composite material of claim 1, wherein the sintered product is obtained under substantially pressureless condition at a temperature range of 1600-2600° C.

5. The composite material of claim 1, wherein said boron carbide is first attrition milled with tungsten carbide in ethanol to provide attrition milled mixture of boron carbide and tungsten carbide-cobalt (WC—Co), wherein said boron carbide after attrition milled is substantially free of boron oxide (B.sub.2O.sub.3).

6. A method of preparing the composite material of claim 1, comprising: attrition milling boron carbide and tungsten carbide in ethanol to provide an attrition milled powder comprising boron carbide and tungsten carbide-cobalt (WC—Co), wherein said boron carbide after the attrition milling is substantially free of boron oxide (B.sub.2O.sub.3); preparing an aqueous suspension comprising the attrition milled boron carbide and tungsten carbide-cobalt (WC—Co) powder, and yttrium oxide powder; injecting mold said suspension and making it a dried mixture; and sintering the dried mixture at a temperature range of 1600-2600° C. to provide the composite material.

7. The method of claim 6, wherein the sintering is carried out at substantially pressureless condition.

Description

DETAILED DESCRIPTION

(1) For the purposes of promoting an understanding of the principles of the present disclosure, reference will now be made to the embodiments illustrated in the drawings, and specific language will be used to describe the same. It will nevertheless be understood that no limitation of the scope of this disclosure is thereby intended.

(2) In the present disclosure the term “about” can allow for a degree of variability in a value or range, for example, within 10%, within 5%, or within 1% of a stated value or of a stated limit of a range.

(3) In the present disclosure the term “substantially” can allow for a degree of variability in a value or range, for example, within 90%, within 95%, or within 99% of a stated value or of a stated limit of a range.

(4) In the present disclosure the term “relative density” refers to a comparison between the bulk density of a material (i.e. the density measured using the Archimedes' technique which includes voids and other defects) compared to the theoretical density of the material (i.e. the density if there were no voids or defects). It is usually expressed as a percentage.

(5) In one embodiment, the present disclosure provides a novel composite material comprising a sintered product of a mixture comprising 70-95 wt. % of boron carbide (B.sub.4C), 2-15 wt. % of tungsten carbide (WC), and 3-15 wt. % of yttrium oxide (Y.sub.2O.sub.3), wherein said boron carbide, tungsten carbide, and yttrium oxide are substantially uniformly distributed in the sintered product.

(6) In one embodiment, the present disclosure provides a novel composite material comprising a sintered product of a mixture comprising 70-90 wt. % of boron carbide (B.sub.4C), 5-15 wt. % of tungsten carbide (WC), and 5-15 wt. % of yttrium oxide (Y.sub.2O.sub.3), wherein said boron carbide, tungsten carbide, and yttrium oxide are substantially uniformly distributed in the sintered product.

(7) In one embodiment, the present disclosure provides a novel composite material comprising a sintered product of a mixture comprising boron carbide (B.sub.4C), tungsten carbide (WC), and yttrium oxide (Y.sub.2O.sub.3), wherein the sintered product has a relative density of 90-99%.

(8) In one embodiment, the present disclosure provides a novel composite material comprising a sintered product of a mixture comprising boron carbide (B.sub.4C), tungsten carbide (WC), and yttrium oxide (Y.sub.2O.sub.3), wherein the sintered product is obtained under substantially pressureless condition at a temperature range of 1600-2600° C.

(9) In one embodiment, the present disclosure provides a novel composite material comprising a sintered product of a mixture comprising boron carbide (B.sub.4C), tungsten carbide (WC), and yttrium oxide (Y.sub.2O.sub.3), wherein said boron carbide is first attrition milled with tungsten carbide in ethanol to provide attrition milled mixture of boron carbide and tungsten carbide, wherein said boron carbide after attrition milled is substantially free of boron oxide (B.sub.2O.sub.3).

(10) In one embodiment, the present disclosure provides a method of preparing the novel boron carbide (B.sub.4C) composite material of the present disclosure, wherein the method comprises:

(11) attrition milling boron carbide and tungsten carbide in ethanol to provide an attrition milled powder comprising boron carbide and tungsten carbide, wherein said boron carbide after the attrition milling is substantially free of boron oxide (B.sub.2O.sub.3);

(12) preparing an aqueous suspension comprising the attrition milled boron carbide and tungsten carbide powder, and yttrium oxide powder;

(13) injecting mold said suspension and making it a dried mixture; and

(14) sintering the dried mixture at a temperature range of 1600-2600° C.

(15) In one embodiment, the present disclosure provides a method of preparing the novel boron carbide (B.sub.4C) composite material of the present disclosure, wherein the sintering is carried out at substantially pressureless condition.

Experimental Sections

(16) Boron carbide (B.sub.4C) powder (H. C. Starck, Germany) with an average particle size of 1.1 micron was used as a starting powder, which had a chemical composition as provided in Table 1:

(17) TABLE-US-00001 TABLE 1 Chemical composition of the as-received boron carbide. Element Wt. % B 75.8 C 22.3 N 0.5 O 1.3 Fe 0.02 Si 0.06 Al <0.01

(18) Three different powder treatments were performed. The first was as-received powder with no treatment.

(19) The second kind of treatment was that the as-received boron carbide was treated by washing in ethanol.

(20) The third was attrition milling in ethanol with sintering aids. In the process utilized in the present disclosure, B.sub.4C powder is first attrition milled in ethanol to remove the thin layer of B.sub.2O.sub.3 that forms on the surface of B.sub.4C particles. Due to the extreme hardness of B.sub.4C, the WC—Co milling media is slowly eroded and mixed into the B.sub.4C powder during attrition milling. As a result, the attrition milled powder is about 2-15% by weight WC—Co. The using of attrition milling increases final densities when compared to using as-received or ethanol washed powders. However, it was noticed the relative density is still below 85% with only WC addition (Table 2).

(21) B.sub.4C powder was suspended in ethanol and attrition milled with ⅛″ 94% tungsten carbide-6% cobalt (WC—Co) milling media for 2 hours at 50 rpm. The milling media to powder ratio was 6.7:1. The powders were dried overnight and then ball milled for 24 hours. During attrition milling, an amount of the WC—Co milling media was worn away and integrated into the B.sub.4C powder. This amount ranged from 2-10 wt. % depending on the batch. Ethanol washed powder was treated in a manner identical to attrition milling, except no WC—Co milling media was added. Tungsten carbide (WC) powder with an average particle size of 0.75 micron was added to the as-received and ethanol washed powders. Powder mixtures with the compositions provided in Table 2 were prepared, with variation of the quantity of sintering aids from 0-20 wt. %.

(22) TABLE-US-00002 TABLE 2 Samples 1-9 Sample Powder B.sub.4C WC—Co WC Relative No. Preparation (wt. %) (wt. %) (wt. %) Density (%) 1 As-received 100 NA NA 76.63 2 As-received 90 NA 10 77.85 3 As-received 85 NA 15 78.83 4 As-received 80 NA 20 78.79 5 Ethanol 100 NA NA 78.23 washed 6 Ethanol 90 NA 10 79.03 washed 7 Ethanol 85 NA 15 79.86 washed 8 Ethanol 80 NA 20 79.92 washed 9 Attrition 85 15 NA 81.13 milled

(23) Pellets of each composition were uniaxially pressed at 34.5 MPa for 20 seconds in a steel die with a diameter of 15 mm. Pellets were placed in a graphite crucible and sintered in a flowing argon atmosphere for 1 hour at 2000° C. with a ramp rate of 25° C./min. After cooling, the pellets were removed and cleaned. Density was measured using Archimedes' method (ASTM C373-14a).

(24) The data of samples 1-9 in Table 2 showed that the addition of WC is beneficial to the pressureless sintering of B.sub.4C. Ethanol washing is also beneficial, as the layer of boric oxide (B.sub.2O.sub.3) found on the surface of B.sub.4C particles dissolves in ethanol. Attrition milling has a significant benefit over ethanol washing, even when WC is intentionally added to match the WC—Co concentration from attrition milling.

(25) Samples 10-31 were prepared in a manner similar to examples 1-9 except yttrium oxide (Y.sub.2O.sub.3) powder with a specific surface area of 6.49 m.sup.2/g was also used as a sintering aid. Powder mixtures with the compositions provided in Table 3 were prepared. Powders were mixed in a planetary mixer (Flacktek, South Carolina) at 800 rpm to ensure even mixing.

(26) Sample 32 was prepared by first mixing a highly loaded (>50 vol. %) aqueous suspension using the attrition milled B.sub.4C/WC—Co powder, Y.sub.2O.sub.3 powder, concentrated 12M HCl, and small amount of branched polyethylenimine (PEI, M.sub.w=25,000 g/mol) for improved green body strength. The suspension is then injection molded at room temperature. Afterwards, the component is allowed to dry before undergoing binder burnout and sintering. The final composition of the sintered components is 70-95% B.sub.4C, 2-15% WC—Co, and 3-15% Y.sub.2O.sub.3 by weight. The addition of Y.sub.2O.sub.3 significantly increases the final density of B.sub.4C over a wide variety of compositions and outperforms traditional B.sub.4C sintering aids over much of that range (Table 3). Sample 33-35 are made essentially the same as Sample 32.

(27) TABLE-US-00003 TABLE 3 Samples 10-35 Sintering Relative Sample Powder B.sub.4C WC—Co Y.sub.2O.sub.3 WC aids total density No. Preparation (wt. %) (wt. %) (wt. %) (%) (wt. %) (%) 10 As-received 90 10 10 86.65 11 As-received 87.5 10 2.5 12.5 86.94 12 As-received 85 10 5 15 86.96 13 As-received 82.5 10 7.5 17.5 88.18 14 As-received 80 10 10 20 88.18 15 As-received 77.5 10 12.5 22.5 89.3 16 As-received 75 10 15 25 89.51 17 Ethanol 90 10 10 87.27 washed 18 Ethanol 87.5 10 2.5 12.5 87.1 washed 19 Ethanol 85 10 5 15 87.58 washed 20 Ethanol 82.5 10 7.5 17.5 89.24 washed 21 Ethanol 80 10 10 20 88.37 washed 22 Ethanol 77.5 10 12.5 22.5 89.1 washed 23 Ethanol 75 10 25 89.92 washed 24 Attrition 85 5 10 15 87.73 milled 25 Attrition 82.5 7.5 10 17.5 88.71 milled 26 Attrition 80 5.08 10 4.92 20 89.49 milled 27 Attrition 77.5 5.08 10 7.67 22.5 89.48 milled 28 Attrition 75 5.08 10 9.92 25 91.17 milled 29 Attrition 90 5 5 10 86.45 milled 30 Attrition 85 5 10 15 90.98 milled 31 Attrition 80 5 15 20 93.81 milled 32 Attrition 84 6 10 16 97.28 milled 33 Attrition 82.79 7.21 10 17.21 97.67 milled 34 Attrition 90.34 4.66 5 9.66 94.06 milled 35 Attrition 78.59 5.91 15 21.41 95.43 milled

(28) The data of samples 10-35 in Table 3 showed that Y.sub.2O.sub.3 has a strong beneficial effect on densification of B.sub.4C over a wide variety of compositions, regardless of powder treatment. In addition, adding 10 wt. % Y.sub.2O.sub.3 increases the effect of WC additions. This suggests that there is a synergic benefit to using both sintering aids simultaneously.

(29) To compare the performance of the composites of the present disclosure and the performance of the composites of U.S. Pat. No. 7,309,672B2, a comparison study was carried out. The results can be found in Table 4.

(30) TABLE-US-00004 TABLE 4 Samples 36*-37* Sintering Relative Sample Powder B.sub.4C Al.sub.2O.sub.3 Y.sub.2O.sub.3 aids total density No. Preparation (wt. %) (wt. %) (wt. %) (wt. %) (%) 36* As-received 95 3 2 5 85.22 37* As-received 98 1.2 0.8 2.0 83.12

(31) Samples 36* and 37* are made corresponding to the method of preparing the Examples 5 and 7 in the U.S. Pat. No. 7,309,672B2. It is clear that composites of the present disclosure provided higher relative density. For example, sample 32 had over 97% relative density, which is more than 10% improvement.

(32) Pellets of each composition was uniaxially pressed at 34.5 MPa for 20 seconds in a steel die with a diameter of 15 mm. Pellets were placed in a graphite crucible and sintered in a flowing argon atmosphere for 1 hour at 2000° C. with a ramp rate of 25° C./min. After cooling, the pellets were removed and cleaned. Density was measured using Archimedes' method (ASTM C373-14a).

(33) Those skilled in the art will recognize that numerous modifications can be made to the specific implementations described above. The implementations should not be limited to the particular limitations described. Other implementations may be possible.