Method for preparing amorphous silicon powder for anode material of lithium ion battery

Abstract

A method for preparing an amorphous silicon powder for an anode material of a lithium-ion battery is disclosed. The amorphous silicon powder is prepared by reducing an oxide of silicon, wherein an X-ray diffraction peak of an amorphous silicon material is weak, and the amorphous silicon material is of an amorphous structure. A structural formula of the oxide of silicon is SiO.sub.x, wherein 0<x≤2.The reduction refers to vapor phase reduction, a vapor phase reduction atmosphere is a mixed gas of hydrogen and carbon monoxide, a reduction temperature ranges from 100° C. to 700° C., and a reduction time ranges from 2 h to 72 h.

Claims

1. A method for preparing an amorphous silicon powder for an anode material of a lithium-ion battery, wherein the amorphous silicon powder is prepared by reducing an oxide of silicon, the reduction refers to vapor phase reduction, and a vapor phase reduction atmosphere is a mixed gas of hydrogen and carbon monoxide.

2. The method for preparing an amorphous silicon powder for an anode material of a lithium-ion battery according to claim 1, wherein a structural formula of the oxide of silicon is SiO.sub.x, wherein 0<x≤2.

3. The method for preparing an amorphous silicon powder for an anode material of a lithium-ion battery according to claim 2, wherein the structural formula of the oxide of silicon is silicon monoxide.

4. The method for preparing an amorphous silicon powder for an anode material of a lithium-ion battery according to claim 3, wherein a reduction temperature ranges from 100° C. to 700° C., and a reduction time ranges from 2 h to 72 h.

5. The method for preparing an amorphous silicon powder for an anode material of a lithium ion battery according to claim 4, wherein a volume ratio of hydrogen to carbon monoxide in the mixed gas is (0.1-10): 1.

6. The method for preparing an amorphous silicon powder for an anode material of a lithium ion battery according to claim 5, wherein the reduction temperature is 300° C., and the reduction time is 5 h.

7. The method for preparing an amorphous silicon powder for an anode material of a lithium ion battery according to claim 6, wherein the oxide of silicon is subjected to ball-milling activation before reduction treatment, a mass ratio of balls to material is (5-30): 1, a ball-milling rotating speed ranges from 100 rpm to 1200 rpm, and a ball-milling time ranges from 1 h to 50 h.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0020] FIG. 1 is an X-ray diffraction pattern of an amorphous silicon powder prepared in an embodiment 1.

[0021] FIG. 2 is an X-ray diffraction pattern of an amorphous silicon powder in a comparative example 1.

[0022] FIG. 3 shows cycle performance curves of electrodes of different materials in an embodiment 5.

DETAILED DESCRIPTION

[0023] Detailed description on the technical method of the present invention content is made below in combination with the embodiments and the comparative examples, and further description on the characteristics and beneficial effects of the amorphous silicon powder applied to the anode of the lithium-ion battery in the present invention is made.

Example 1

[0024] 5 g of silicon monoxide (average grain diameter-100 nm) was ground on a ball mill (a milling ball material was zirconium oxide), a ratio of balls to material was 20:1, a ball-milling rotating speed was 800 rpm, and a ball-milling time was 2 h. The balls and the material were separated after ball-milling was finished, the powder material was subjected to reduction treatment for 5 h at 300° C. in a mixed atmosphere of hydrogen and carbon monoxide (a volume ratio: 1/1), an X-ray diffraction pattern (XRD) of an obtained product was shown in FIG. 1, and it could be seen from FIG. 1 that the diffraction peak of silicon was weak, and the material was in an amorphous state integrally. The product prepared by the method was marked as S1. Charging and discharging cycle performance of S1 was as shown in FIG. 3, the first charging capacity was 2221 mAg/g, the volume after 100-time cycles was 1954 mAg/g, the capacity retention ratio was 88%, and the cycle stability was good.

Example 2

[0025] The reduction time was prolonged, and the rest of treatment methods was as same in the example 1. The balls and the material were separated after silicon monoxide (average grain diameter-100 nm) was subjected to ball-milling, the powder material was subjected to reduction treatment for 10 h at 300° C. in a mixed atmosphere of hydrogen and carbon monoxide (1/1), and the product prepared by the method was marked as S2. Charging and discharging cycle performance of S2 was as shown in FIG. 3. The first charging capacity was 2211 mAg/g, the volume after 100-time cycles was 1890 mAg/g, and the capacity retention ratio was 85%. Compared with the example 1, the reversible capacities were approximate, and the cycle stability was slightly decreased. Prolonging of the reduction time did not further improve the cycle stability of the material. The phenomenon was mainly because of partial crystallization and decrease of defect concentration of the silicon material as a result of increase of the reduction temperature.

Example 3

[0026] The reduction temperature was prolonged, and the rest of treatment methods was as same in the example 1. The balls and the material were separated after silicon monoxide (average grain diameter-100 nm) was subjected to ball-milling, and the powder material was subjected to reduction treatment for 5 h at 700° C. in a mixed atmosphere of hydrogen and carbon monoxide (1/1). The product prepared by the method was marked as S3. Charging and discharging cycle performance of the S3 was as shown in FIG. 3. The first charging capacity was 2002 mAg/g, the volume after 100-time cycles was 1492 mAg/g, and the capacity retention ratio was 75%. Compared with the example 1, the reversible capacities were decreased, and the cycle stability was obviously decreased. In combination with trend of the example 2, prolonging of the reduction time and increase of the reduction temperature caused partial crystallization of the silicon material, so that the reversible capacity and the cycle stability were decreased.

Example 4

[0027] The reduction temperature was 500° C., the reduction time was 5 h, and the rest of treatment methods was as same in the example 1. The first charging capacity was 2010 mAg/g, the volume after 100-time cycles was 1688 mAg/g, and the capacity retention ratio was 84%.

Example 5

[0028] Silicon monoxide was replaced by silicon dioxide, and the rest of treatment methods were as same in the example 1. The first charging capacity was 1980 mAg/g, the volume after 100-time cycles was 1662 mAg/g, and the capacity retention ratio was 84%.

Example 6

[0029] Silicon monoxide was replaced by a mixture of silicon dioxide and silicon monoxide, wherein 2 g of silicon dioxide and 3 g of silicon monoxide was used, and the rest of treatment methods were as same in the example 1. The first charging capacity was 1976 mAg/g, the volume after 100-time cycles was 1670 mAg/g, and the capacity retention ratio was 85%.

Example 7

[0030] The reduction atmosphere was a mixed gas of hydrogen and carbon monoxide (H.sub.2/CO=10:1), and the rest of treatment methods was as same in the example 1. The first charging capacity was 2001 mAg/g, the volume after 100-time cycles was 1720 mAg/g, and the capacity retention ratio was 86%.

Example 8

[0031] The reduction atmosphere was a mixed gas of hydrogen and carbon monoxide (H.sub.2/CO=15:1), and the rest of treatment methods was as same in the example 1. The first charging capacity was 1880 mAg/g, the volume after 100-time cycles was 1601 mAg/g, and the capacity retention ratio was 85%.

Example 9

[0032] The reduction atmosphere was a mixed gas of hydrogen and carbon monoxide (H.sub.2/CO=0.2:1), and the rest of treatment methods was as same in the example 1. The first charging capacity was 1988 mAg/g, the volume after 100-time cycles was 1670 mAg/g, and the capacity retention ratio was 84%.

Comparative Example 1

[0033] The ball-milling material of silicon monoxide was replaced by a nano silicon powder (average grain diameter-100 nm), and the rest of treatment methods was as same in the example 1. X-ray diffraction pattern (XRD) of a product was as shown in FIG. 2, a high strength characteristic diffraction peak of crystalline silicon could be seen, and the material was high in crystallinity. It verified that the silicon raw material (necessarily an amorphous silicon oxide) is of great importance to prepare the amorphous silicon powder successfully. The product prepared by the method was marked as S4. Charging and discharging cycle performance of the S4 was as shown in FIG. 3. The first charging capacity was 2098 mAg/g, the volume after 100-time cycles was 462 mAg/g, and the capacity retention ratio was 22%. Compared with amorphous silicon, cycle stability of the crystalline silicon material was very poor.

Comparative Example 2

[0034] A raw material was not subjected to ball-milling activation treatment, and the rest of treatment methods as same in the example 1. The product prepared by the method was marked as S5. Charging and discharging cycle performance of S5 was as shown in FIG. 3. The first charging capacity was 1272 mAg/g, the volume after 100-time cycles was 987 mAg/g, and the capacity retention ratio was 78%. Compared with the example 1, the reversible capacities were obviously decreased. The phenomenon verified that the ball-milling process could activate active sites in the material via negativa, so that the reversible capacity of the material was improved.

Comparative Example 3

[0035] A raw material was subjected to reduction treatment at 900° C., and the rest of operating methods as same in the example 1. The product prepared by the method was marked as S6. Charging and discharging cycle performance of S6 was as shown in FIG. 3, the first charging capacity was 1997 mAg/g, the volume after 100-time cycles was 1094 mAg/g, the capacity retention ratio was 55%, and the cycle stability was poor. This showed that the reduction temperature was of great importance to cycle stability of the material.

Comparative Example 4

[0036] The reduction atmosphere was hydrogen, and the rest of treatment methods were as same in the example 1. The first charging capacity was 1450 mAg/g, the volume after 100-time cycles was 1140 mAg/g, and the capacity retention ratio was 79%.

Comparative Example 5

[0037] The reduction atmosphere was carbon monoxide, and the rest of treatment methods were as same in the example 1. The first charging capacity was 1782 mAg/g, the volume after 100-time cycles was 1362 mAg/g, and the capacity retention ratio was 76%.

Example 10

[0038] Capacities and charging and discharging cycle performance of the products in the examples 1-9 and the comparative examples 1-5 were tested with a button cell. A method for preparing the button cell for all samples in the present invention includes: an active substance, acetylene black (CB) and polyvinylidene fluoride (PVDF) were dissolved in N-methyl pyrrolidone (NMP) in a mass ratio of 7:2:1 to prepare slurry; the slurry was scrape-coated to a copper foil; and vacuum drying was conducted for 12 h. A polypropylene (PP) film and an electrolyte (solvent ratio:DMC:EMC:EC=5:3:2, LiPF.sub.6 concentration: 1.1 M, 1.5 wt. % of FEC) formed the button cell (CR2025) by taking a metal lithium foil as a counter electrode. A current density in a charging and discharging experiment was 200 mA/g and a voltage range was 0.01-1.5 V. In cycle charging and discharging tests, the capacity retention ratio of the material referred to the post-cycle charging (de-lithiated) capacity/first charging capacity.

[0039] The above embodiments are not all the embodiments, and other non-original embodiments put forward by related technicians in the field based on the embodiments of the present invention shall fall within the scope of protection of the present invention. To highlight the beneficial effects of the present invention, a part of process parameters in the examples 2-9 were changed, thereby demonstrating the technical advantages of the example 1 via negativa; compared with the example 1, the amorphous silicon oxide in the comparative example 1 was replaced by crystalline silicon without obtaining the amorphous silicon material; in the comparative example 2, there was no ball-milling activation process, so that the capacity of the material was very low; in the comparative example 3, the reduction temperature was high, so that the cycle stability of the material was very poor; and in the comparative examples 4 and 5, the reduction atmosphere was changed, so that the capacity of the material was very low and the cycle stability was very poor. The above 5 comparative examples demonstrated three critical elements to prepare amorphous silicon involved in the technical scheme via negativa: amorphous silicon oxide raw material, ball-milling activation process and reduction process.