CN116117145A - TiB (titanium-boron) 2 Modified Mo 2 FeB 2 Method for producing a base composite material - Google Patents
TiB (titanium-boron) 2 Modified Mo 2 FeB 2 Method for producing a base composite material Download PDFInfo
- Publication number
- CN116117145A CN116117145A CN202211489857.5A CN202211489857A CN116117145A CN 116117145 A CN116117145 A CN 116117145A CN 202211489857 A CN202211489857 A CN 202211489857A CN 116117145 A CN116117145 A CN 116117145A
- Authority
- CN
- China
- Prior art keywords
- feb
- tib
- composite material
- modified
- base composite
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/02—Compacting only
- B22F3/03—Press-moulding apparatus therefor
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
- B22F3/1007—Atmosphere
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
Abstract
The invention discloses a TiB 2 Modified Mo 2 FeB 2 A method for preparing a base composite material. The disclosed method comprises the following steps: mo, feB, fe and TiB 2 Sequentially ball milling and compression molding the mixed powder of the powder to prepare a blank, and then sintering the blank in a vacuum carbon tube furnace to prepare TiB 2 Modified Mo 2 FeB 2 A base composite material; the weight percentages are as follows: 37.0 to 51.0 percent of Mo, 21.0 to 35.0 percent of FeB, 12.0 to 31.0 percent of Fe and TiB 2 2.0 to 10.0 percent. The invention has the advantages of few raw material types, simple preparation process and short preparation period, and the prepared composite material contains Mo 2 FeB 2 Hard phase, fe-based binder phase and TiB 2 Reinforcing phase with excellent comprehensive mechanicsPerformance.
Description
Technical Field
The invention relates to Mo 2 FeB 2 A metal-based ceramic related technology, belonging to the field of structural functional materials. In particular to a TiB 2 Modified Mo 2 FeB 2 A method for preparing a base composite material.
Background
The ternary boride-based metal ceramic is a high-performance metal ceramic prepared by utilizing the reaction boride sintering principle, wherein a hard phase is not directly added from raw materials, but is generated by reacting an intermediate product binary boride with metal, the ternary boride-based metal ceramic has a smooth surface, good wettability with a binding phase and high interface bonding strength, and the problem that the binary boride is difficult to sinter is greatly solved. Mo (Mo) 2 FeB 2 The base cermets are typical of them and are composed of Mo 2 FeB 2 The hard phase and Fe-based binding phase are combined, so that the ceramic has high hardness, excellent wear resistance and chemical stability, high strength of metal and good plasticity and toughness. Thus, mo 2 FeB 2 Base cermets are subject to heat from many researchers.
Mo prepared at present 2 FeB 2 The base metal ceramic has higher mechanical property, can basically meet the conventional service condition, and can be used for preparing extrusion dies, stretching dies, blanking dies, stamping dies and the like. However, with the progress of technology, it is required to further improve the comprehensive mechanical properties so as to meet the more severe working condition environment. For this reason, technological staff have adopted various methods to increase Mo 2 FeB 2 Base cermetIs characterized by the comprehensive mechanical properties. TiC content vs Mo in journal of powder metallurgy industry 2 FeB 2 In the paper of influence of the structure and mechanical properties of the base metal ceramic, mo powder, feB powder, fe powder, tiC powder, cr powder and Ni powder are used as raw materials, and TiC reinforced Mo is prepared by vacuum sintering 2 FeB 2 The metal ceramic is based on the metal ceramic, so that the hardness and the bending strength are both increased, the hardness reaches 89.5HRA at maximum, and the bending strength reaches 1660MPa at maximum. However, the prior art has numerous raw materials, which not only brings difficulty to ensure consistency of raw material components among batches, but also increases friction force among mixed powder during powder compression molding, and a molding agent (SD-E type) is required to be added to improve fluidity of the mixed powder. The method needs to be specially provided with a heat preservation program to decompose and discharge during sintering, so that the preparation period is prolonged, and the hardness and the bending strength of the prepared composite material are insufficient due to the pollution of impurities left in the composite material.
Disclosure of Invention
In order to overcome the defects or shortcomings of the prior art, the invention provides a TiB 2 Modified Mo 2 FeB 2 A method for preparing a base composite material.
Therefore, the preparation method provided by the invention comprises the following steps: mo, feB, fe and TiB 2 Sequentially ball milling and compression molding the mixed powder of the powder to prepare a blank, and then sintering the blank in a vacuum carbon tube furnace to prepare TiB 2 Modified Mo 2 FeB 2 A base composite material;
the weight percentages are as follows: 37.0 to 51.0 percent of Mo, 21.0 to 35.0 percent of FeB, 12.0 to 31.0 percent of Fe and TiB 2 2.0 to 10.0 percent.
Optionally, the sintering process parameters are as follows: raising the temperature from room temperature to 1250-1350 ℃ at a heating rate of 5-15 ℃/min, preserving the temperature for 0-50 min, and cooling to room temperature.
Further, the TiB 2 Modified Mo 2 FeB 2 The base composite material comprises three phases: mo (Mo) 2 FeB 2 Hard phase, fe-based binder phase, tiB 2 And an enhancement phase. The TiB is 2 Modified Mo 2 FeB 2 The hardness of the base composite material is88.6-91.0 HRA, and the flexural strength is 1689.2-2013.6 MPa.
Compared with the prior art, (1) the invention has the advantages of few raw material types, simple preparation process and short preparation period, and the prepared composite material contains Mo 2 FeB 2 Hard phase, fe-based binder phase and TiB 2 An enhancement phase; (2) the composite material prepared by the invention has excellent comprehensive mechanical properties.
Drawings
FIG. 1 shows TiB in example 3 of the present invention 2 Modified Mo 2 FeB 2 XRD pattern of the base composite;
FIG. 2 is a schematic diagram of TiB in example 3 of the present invention 2 Modified Mo 2 FeB 2 Microscopic photograph of the base composite.
Detailed Description
Unless specifically stated otherwise, scientific and technical terms and methods herein have been understood or implemented by those of ordinary skill in the relevant art based on the knowledge of one of ordinary skill in the relevant art. It should also be understood that the temperature, hold time, and the like referred to herein are approximations for purposes of illustration. Although methods and materials similar or equivalent to those described herein can be used in the practice of the present disclosure, some suitable methods and materials are described below. Publications, patent applications, patents, and other references mentioned herein are incorporated by reference in their entirety to the extent that any conflict arises. In addition, the materials, methods, material ratios, and examples are illustrative only and not intended to be limiting. In a specific scheme, a person skilled in the art can optimize the material proportion and the operation parameter value involved in the method according to the disclosure of the invention by adopting a conventional experimental period to achieve the aim of the invention.
The purpose of the press forming according to the invention is to initially densify the powdery raw material, the shape and size of the green body produced depending on the shape of the mould. The molds used in the prior art of ceramics, such as molds with volume dimensions greater than 3mm by 3mm, are suitable for use in the present invention.
Based on the disclosure of the present invention, a person skilled in the art may optimize specific sintering by using a conventional experimental means for different formulation materials and effects of the present invention, and the specific sintering process adopted in the following examples is only one specific example to explain the scheme of the present invention, and the sintering process of the present invention is not limited thereto. The sintering process conditions are exemplified by raising the temperature from room temperature to 1250-1350 ℃ at a heating rate of 5-15 ℃/min, and maintaining the temperature for 0-50 min, and then furnace cooling to room temperature.
The invention is illustrated in further detail by the following examples. The raw materials Mo, fe, B and TiB used in the examples of the invention 2 The powder is a commercially available chemical pure powder reagent; the ball mill used was a planetary ball mill (QM-3 SP 4). The present invention is not limited to these specific devices.
TiB measurement in the present invention using an HRS-150 Rockwell hardness tester 2 Modified Mo 2 FeB 2 Hardness of the base composite; referring to national standard GB/T6569-2006, a three-point bending test method is adopted for TiB 2 Modified Mo 2 FeB 2 The flexural strength of the base composite samples was tested.
Example 1:
in this example, mo, feB, fe and TiB having a purity of not less than 99.0% are selected 2 The powder is used as a raw material and comprises the following components in percentage by mass: mo 51.0%, feB 35.0%, fe 12.0%, tiB 2 2.0%;
ball milling and compacting the mixed powder to prepare a cylindrical (diameter 44mm, height 8-9 mm) blank;
then placing the blank into a vacuum carbon tube furnace for sintering, wherein the sintering process parameters are as follows: the temperature was raised from room temperature to 1250℃at a heating rate of 5℃per minute and kept at that temperature for 0min, after which the furnace was cooled to room temperature.
TiB prepared in this example 2 Modified Mo 2 FeB 2 The base composite material comprises Mo 2 FeB 2 Hard phase, fe-based binder phase and TiB 2 The reinforcing phase has a hardness of 88.6HRA and a flexural strength of 1689.2MPa.
Example 2:
in this embodiment, mo, feB and F with purity not lower than 99.0% are selectede and TiB 2 The powder is used as a raw material and comprises the following components in percentage by mass: mo 44.0%, feB 28.0%, fe 22.0%, tiB 2 6.0%;
ball milling and compacting the mixed powder to prepare a cylindrical (diameter 44mm, height 8-9 mm) blank;
then placing the blank into a vacuum carbon tube furnace for sintering, wherein the sintering process parameters are as follows: the temperature was raised from room temperature to 1300 ℃ at a heating rate of 10 ℃/min and kept for 25min, after which the furnace was cooled to room temperature.
TiB prepared in this example 2 Modified Mo 2 FeB 2 The base composite material comprises Mo 2 FeB 2 Hard phase, fe-based binder phase and TiB 2 The reinforcing phase has a hardness of 89.9HRA and a flexural strength of 1847.2MPa.
Example 3:
in this example, mo, feB, fe and TiB having a purity of not less than 99.0% are selected 2 The powder is used as a raw material and comprises the following components in percentage by mass: 37.0% Mo, 22.0% FeB, 31.0% Fe, tiB 2 10.0%;
ball milling and compacting the mixed powder to prepare a cylindrical (diameter 44mm, height 8-9 mm) blank;
then placing the blank into a vacuum carbon tube furnace for sintering, wherein the sintering process parameters are as follows: the temperature was raised from room temperature to 1350 ℃ at a ramp rate of 15 ℃/min and incubated for 50min, after which the furnace cooled to room temperature.
TiB prepared in this example 2 Modified Mo 2 FeB 2 The base composite material comprises Mo 2 FeB 2 Hard phase, fe-based binder phase and TiB 2 The enhancement phase (XRD pattern, see FIG. 1), and the microstructure, see FIG. 2; the hardness of the composite material is 91.0HRA, and the bending strength is 2013.6MPa.
Comparative example:
this comparative example differs from example 3 in that the raw material does not contain TiB 2 And (5) powder.
Mo obtained in this comparative example 2 FeB 2 The base composite material comprises Mo 2 FeB 2 A hard phase and a Fe-based binder phase, the hardness of which is 87.3HRA, and the flexural strength of which is1446.8MPa。
The test properties of the composites of the above examples and comparative examples are shown in Table 1.
TABLE 1 mechanical Properties of composite materials
| Sample of | hardness/HRA | Flexural Strength/MPa |
| Comparative example | 87.3 | 1446.8 |
| Example 1 | 88.6 | 1689.2 |
| Example 2 | 89.9 | 1847.2 |
| Example 3 | 91.0 | 2013.6 |
As can be seen from the test results of Table 1, the TiB prepared according to the present invention is compared with the comparative example 2 Modified Mo 2 FeB 2 The hardness and the bending strength of the base composite material are both increased, the maximum hardness reaches 91.0HRA, the bending strength is improved by about 3.7HRA, the maximum bending strength is improved by about 39.2%, and the comprehensive mechanical property is obviously improved.
Claims (4)
1. TiB (titanium-boron) 2 Modified Mo 2 FeB 2 A method of preparing a base composite material, the method comprising: mo, feB, fe and TiB 2 Sequentially ball milling and compression molding the mixed powder of the powder to prepare a blank, and then sintering the blank in a vacuum carbon tube furnace to prepare TiB 2 Modified Mo 2 FeB 2 A base composite material;
the weight percentages are as follows: 37.0 to 51.0 percent of Mo, 21.0 to 35.0 percent of FeB, 12.0 to 31.0 percent of Fe and TiB 2 2.0 to 10.0 percent.
2. TiB according to claim 1 2 Modified Mo 2 FeB 2 The preparation method of the base composite material is characterized in that the sintering process parameters are as follows: raising the temperature from room temperature to 1250-1350 ℃ at a heating rate of 5-15 ℃/min, preserving the temperature for 0-50 min, and cooling to room temperature.
3. TiB according to claim 1 2 Modified Mo 2 FeB 2 A method for preparing a base composite material, characterized in that the TiB 2 Modified Mo 2 FeB 2 The base composite material comprises three phases: mo (Mo) 2 FeB 2 Hard phase, fe-based binder phase, tiB 2 And an enhancement phase.
4. TiB according to claim 1 2 Modified Mo 2 FeB 2 A method for preparing a base composite material, characterized in that the TiB 2 Modified Mo 2 FeB 2 The hardness of the base composite material is 88.6-91.0 HRA, and the bending strength is 1689.2-2013.6 MPa.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211489857.5A CN116117145A (en) | 2022-11-25 | 2022-11-25 | TiB (titanium-boron) 2 Modified Mo 2 FeB 2 Method for producing a base composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211489857.5A CN116117145A (en) | 2022-11-25 | 2022-11-25 | TiB (titanium-boron) 2 Modified Mo 2 FeB 2 Method for producing a base composite material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN116117145A true CN116117145A (en) | 2023-05-16 |
Family
ID=86306997
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211489857.5A Pending CN116117145A (en) | 2022-11-25 | 2022-11-25 | TiB (titanium-boron) 2 Modified Mo 2 FeB 2 Method for producing a base composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN116117145A (en) |
-
2022
- 2022-11-25 CN CN202211489857.5A patent/CN116117145A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109576545B (en) | Ti (C, N) -based metal ceramic with mixed crystal structure and preparation method thereof | |
| CN108611539B (en) | A kind of complex intensifying hard alloy and preparation method thereof | |
| CN110819842A (en) | Preparation method of formed part based on reduced graphene oxide and copper composite material | |
| CN112853187B (en) | Weak core ring structure fine-grain homogeneous TiCN-based metal ceramic and preparation method thereof | |
| CN111235452A (en) | Ti (C, N) -based hard alloy material and preparation method thereof | |
| CN111531166A (en) | Method for improving sintering density of iron-based powder metallurgy part | |
| CN110499442B (en) | High-strength corrosion-resistant Cr3C2Light metal ceramic alloy and preparation method thereof | |
| CN109852862A (en) | A kind of high rigidity composite hard alloy and the preparation method and application thereof | |
| CN110438384B (en) | Iron-nickel-based ultrafine-grained hard alloy and preparation method thereof | |
| CN109576546A (en) | A kind of preparation method of the high-strength tenacity without magnetic Ti (C, N) based ceramic metal | |
| CN111747748A (en) | Ultrahigh-temperature heat-insulation integrated ZrC/Zr2C complex phase material and preparation method thereof | |
| CN114250379B (en) | Preparation method of in-situ particle reinforced metal matrix composite material | |
| CN116117145A (en) | TiB (titanium-boron) 2 Modified Mo 2 FeB 2 Method for producing a base composite material | |
| CN112941391B (en) | NbC-containing high-density composite metal ceramic material and preparation method thereof | |
| CN110576176A (en) | Preparation method of high-performance diamond tool | |
| CN102747249B (en) | Enhanced titanium-based composite material and powder metallurgy preparation method thereof | |
| CN114262834A (en) | High-temperature self-lubricating composite material and preparation method and application thereof | |
| CN115849926B (en) | Preparation method of WC reinforced MoCoB-based composite material | |
| CN115637347B (en) | Preparation method of high-strength WCoB-based metal ceramic | |
| CN113173789A (en) | Non-binding phase corrosion-resistant hard alloy and production process and application thereof | |
| CN116121616A (en) | TiN modified Mo 2 NiB 2 Method for producing a base composite material | |
| CN112609106A (en) | Zr-Ti-Nb alloy and preparation method thereof | |
| CN111961900A (en) | Novel titanium-aluminum-based composite material and preparation method thereof | |
| CN116121579A (en) | Preparation method of MoCoB-WCoB based composite material | |
| CN116790953B (en) | High-performance nano hard alloy product and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination |