Method for toughening corrosion-resistant Mo2NiB2 ceramic by doping trace amount of nano FeO

Abstract

The invention discloses a method for toughening corrosion-resistant Mo2NiB2 ceramic by doping a trace amount of nano FeO, and belongs to the technical field of ceramic preparation. The corrosion-resistant Mo2NiB2 ceramic is toughened by doping a trace amount of nano FeO, the toughened Mo2NiB2 ceramic has an obvious dimple phenomenon and an obvious toughening effect, and the toughness of the Mo2NiB2 ceramic can be improved by more than two times at most.

Description

Technical Field

[0001] The invention belongs to the technical field of ceramic preparation, and particularly relates to a micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 Ceramic method. Background Art

[0002] Mo 2 NeB 2 Ceramics are different from Mo 2 NeB 2 Based on metal ceramics, the former is to make full use of the single hard phase Mo 2 NeB 2 The block can exert its excellent performance of wear resistance and corrosion resistance, and has a wide range of application prospects, such as in high-temperature oxidation pipelines and containers, cutting tools and other parts or component coatings. 2 NeB 2 Ceramics have obvious cost-effectiveness advantages compared to other W and Co-containing ceramics, but Mo 2 NeB 2 If the toughness of ceramics can be significantly improved, their applications will become more extensive. Obviously, the invention of a micro-doped FeO toughened corrosion-resistant Mo 2 NeB 2 The ceramic method has important innovation and engineering application significance. Summary of the invention

[0003] The purpose of this section is to summarize some aspects of embodiments of the present invention and briefly introduce some preferred embodiments. Some simplifications or omissions may be made in this section and the specification abstract and the invention title of this application to avoid blurring the purpose of this section, the specification abstract and the invention title, and such simplifications or omissions cannot be used to limit the scope of the present invention.

[0004] In view of the above problems and / or the problems existing in the prior art, the present invention is proposed.

[0005] Therefore, the purpose of the present invention is to overcome the deficiencies in the prior art and provide a micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 Ceramic method.

[0006] In order to solve the above technical problems, the present invention provides the following technical solutions, including: FeO powder, Mo 2 NeB 2 The powders are weighed in a mass ratio of (0.01-0.1):1 and then mixed to obtain a mixed powder; the mixed powder is ball-milled and then vacuum pressure sintered; after sintering, the mixture is cooled to obtain FeO-toughened Mo 2 NeB 2 ceramics.

[0007] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the purity of the FeO powder is ≥98%, and the particle size is ≤200nm.

[0008] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the Mo 2 NeB 2 The purity of the powder is ≥99% and the particle size is ≤300μm.

[0009] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the ball-to-material ratio of the ball mill is 9-10:1, the ball milling speed is 200-300 rpm, and the time is 4-20 hours.

[0010] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the heating rate of the vacuum pressure sintering is 2-5°C / s.

[0011] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the sintering temperature of the vacuum pressure sintering is 900-1200°C.

[0012] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the sintering time of the vacuum pressure sintering is 10 to 30 minutes.

[0013] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the method for ceramics, wherein: the vacuum degree of the vacuum pressure sintering is less than 10 -1 Pa.

[0014] As the micro-doped nano-FeO toughened and corrosion-resistant Mo 2 NeB 2 A preferred embodiment of the ceramic method, wherein: the pressure of the vacuum pressure sintering is 200-500 MPa.

[0015] The purpose of the present invention is to overcome the deficiencies in the prior art and provide a toughened and corrosion-resistant Mo 2 NeB 2 ceramics.

[0016] Beneficial effects of the present invention:

[0017] The Mo prepared by the present invention 2 NeB 2 The toughness of ceramics is significantly improved, up to more than 2 times. The raw materials used in the invention are low in price, the equipment is simple, the energy consumption is small, the time is short, and the safety is high. BRIEF DESCRIPTION OF THE DRAWINGS

[0018] In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the following briefly introduces the drawings required for describing the embodiments. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without creative work. Among them:

[0019] Figure 1 The toughened Mo obtained in Example 1 of the present invention 2 NeB 2 SEM image of the ceramic fracture morphology. DETAILED DESCRIPTION

[0020] In order to make the above-mentioned objects, features and advantages of the present invention more obvious and easy to understand, the specific implementation methods of the present invention are described in detail below in conjunction with the embodiments of the specification.

[0021] In the following description, many specific details are set forth to facilitate a full understanding of the present invention, but the present invention may also be implemented in other ways different from those described herein, and those skilled in the art may make similar generalizations without violating the connotation of the present invention. Therefore, the present invention is not limited to the specific embodiments disclosed below.

[0022] Secondly, the term "one embodiment" or "embodiment" as used herein refers to a specific feature, structure, or characteristic that may be included in at least one implementation of the present invention. The term "in one embodiment" that appears in different places in this specification does not necessarily refer to the same embodiment, nor does it refer to a separate or selective embodiment that is mutually exclusive with other embodiments.

[0023] The raw materials used in the present invention are all commercially available unless otherwise specified.

[0024] The performance of the material prepared in the embodiment of the present invention was tested as follows:

[0025] Refer to GB / T 23806-2009 to measure toughened Mo 2 NeB 2Fracture toughness of ceramics.

[0026] Example 1

[0027] This embodiment provides a toughened Mo 2 NeB 2 The preparation method of ceramics is specifically as follows:

[0028] (1) FeO powder with a purity of 99% and a particle size of 200 nm, Mo powder with a purity of 99.5% and a particle size of 300 μm 2 NeB 2 The powder is quickly weighed at a mass ratio of 0.02:1 and then loaded into a ball mill;

[0029] (2) Place the ball mill in a ball mill and grind the mixed powder for 5 hours at a ball-to-material ratio of 10:1 and a ball mill speed of 250 rpm. Quickly fill the taken-out mixed powder into a graphite crucible;

[0030] (3) Place the graphite crucible containing the mixed powder into a plasma activated sintering furnace and perform vacuum pressure sintering at 950°C. The vacuum degree of vacuum pressure sintering is 10 -3 The vacuum pressure sintering temperature rise rate is 3°C / s, and the temperature is kept for 30 minutes. After the sintering is completed, the furnace is cooled to finally obtain FeO toughened Mo 2 NeB 2 ceramics.

[0031] Figure 1 The toughened Mo obtained in Example 1 of the present invention 2 NeB 2 The scanning electron microscope image of the ceramic fracture morphology shows that the dimple phenomenon is obvious, indicating that the toughening effect is significant.

[0032] Example 2

[0033] The difference between this embodiment and embodiment 1 is that the FeO powder and Mo 2 NeB 2 The mass ratio of the powder was 0.01:1, and the rest of the preparation process was the same as in Example 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0034] Example 3

[0035] The difference between this embodiment and embodiment 1 is that the FeO powder and Mo 2 NeB 2 The mass ratio of the powder was 0.1:1, and the rest of the preparation process was the same as in Example 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0036] Comparative Example 1

[0037] The difference between this embodiment and embodiment 1 is that the FeO powder and Mo 2 NeB 2 The mass ratio of the powder was 0:1, and the rest of the preparation process was the same as in Example 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0038] The performance of the material prepared in the above embodiment was tested, and the comparison results with those in Example 1 are shown in Table 1.

[0039] Table 1

[0040]

[0041] It can be seen from the above table that adjusting FeO powder, Mo 2 NeB 2 Powder quality ratio for toughening Mo 2 NeB 2 The performance of ceramics is significantly affected, and the reasons need further analysis and research. At present, according to the results in the above table, the FeO powder and Mo in the present invention 2 NeB 2 The best technical effect can be obtained when the mass ratio of the powder is 0.02:1.

[0042] Example 4

[0043] The difference between this embodiment and embodiment 1 is that the ball milling time is adjusted to 4 hours, and the rest of the preparation process is the same as that of embodiment 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0044] Example 5

[0045] The difference between this embodiment and embodiment 1 is that the ball milling time is adjusted to 10 hours, and the rest of the preparation process is the same as that of embodiment 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0046] Example 6

[0047] The difference between this embodiment and embodiment 1 is that the ball milling time is adjusted to 20 hours, and the rest of the preparation process is the same as that of embodiment 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0048] The performance of the material prepared in the above embodiment was tested, and the comparison results with those in Example 1 are shown in Table 2.

[0049] Table 2

[0050]

[0051] It can be seen from the above table that adjusting the ball milling time has a significant effect on the toughening of Mo 2 NeB 2 The performance of the ceramic is significantly affected because the extension of the ball milling time is conducive to the uniform distribution of FeO, but the change in the toughening effect is not obvious with the further extension of time. According to the results in the above table, the best technical effect can be obtained when the ball milling time is 5h in the present invention.

[0052] Example 7

[0053] The difference between this embodiment and embodiment 1 is that the sintering temperature is adjusted to 900°C, and the rest of the preparation process is the same as that of embodiment 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0054] Example 8

[0055] The difference between this embodiment and embodiment 1 is that the sintering temperature is adjusted to 1200°C, and the rest of the preparation process is the same as that of embodiment 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0056] The performance of the material prepared in the above embodiment was tested, and the comparison results with those in Example 1 are shown in Table 1.

[0057] Table 1

[0058]

[0059] It can be seen from the above table that adjusting the sintering temperature has an important effect on the toughening of Mo 2 NeB 2 The performance of ceramics is significantly affected, because the increase of sintering temperature is conducive to the reaction of FeO and Mo. 2 NeB 2 The improvement of the bonding ability is beneficial to the improvement of toughness. According to the results in the above table, the best technical effect can be obtained when the sintering temperature in the present invention is 950°C.

[0060] Comparative Example 2

[0061] The difference between this comparative example and Example 1 is that the sintering temperature is adjusted to 1500°C, and the rest of the preparation process is the same as that of Example 1 to obtain toughened Mo 2 NeB 2 ceramics.

[0062] The holes are obvious and the toughening effect is poor.

[0063] In summary, the present invention uses trace doped nano-FeO to toughen and resistant Mo 2 NeB 2 The ceramic method has a simple process and significantly improves the Mo 2 NeB 2 The toughness of ceramics has been increased by more than 2 times, which has important application prospects.

[0064] It should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention rather than to limit it. Although the present invention has been described in detail with reference to the preferred embodiments, those skilled in the art should understand that the technical solutions of the present invention may be modified or replaced by equivalents without departing from the spirit and scope of the technical solutions of the present invention, which should all be included in the scope of the claims of the present invention.

Claims

1. A method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping with nano-FeO, characterized in that: include, The FeO powder and Mo2NiB2 powder are weighed in a mass ratio of (0.01-0.1):1 and then mixed evenly to obtain a mixed powder; the mixed powder is ball-milled and then vacuum pressure sintered; after sintering, the powder is cooled to obtain FeO toughened Mo2NiB2 ceramics.

2. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The purity of the FeO powder is ≥98%, and the particle size is ≤200nm.

3. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The purity of the Mo2NiB2 powder is ≥99% and the particle size is ≤300 μm.

4. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The ball mill has a ball-to-material ratio of 9 to 10:1, a ball mill speed of 200 to 300 rpm, and a time of 4 to 20 hours.

5. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The heating rate of the vacuum pressure sintering is 2-5°C / s.

6. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The sintering temperature of the vacuum pressure sintering is 900-1200°C.

7. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The sintering time of the vacuum pressure sintering is 10 to 30 minutes.

8. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The vacuum degree of the vacuum pressure sintering is less than 10 -1 Pa.

9. The method for toughening and corrosion-resistant Mo2NiB2 ceramics by trace doping of nano-FeO as claimed in claim 1, characterized in that: The pressure of the vacuum pressure sintering is 200-500 MPa.

10. Mo2NiB2 ceramics prepared by the method of trace-doped nano-FeO toughening and corrosion-resistant Mo2NiB2 ceramics as described in any one of claims 1 to 9.

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