CN117144229A - Preparation method of NbC and VC composite reinforced iron-based composite material - Google Patents
Preparation method of NbC and VC composite reinforced iron-based composite material Download PDFInfo
- Publication number
- CN117144229A CN117144229A CN202311073225.5A CN202311073225A CN117144229A CN 117144229 A CN117144229 A CN 117144229A CN 202311073225 A CN202311073225 A CN 202311073225A CN 117144229 A CN117144229 A CN 117144229A
- Authority
- CN
- China
- Prior art keywords
- nbc
- smelting
- iron
- raw materials
- composite material
- 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
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 77
- 239000002131 composite material Substances 0.000 title claims abstract description 61
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 37
- 238000002360 preparation method Methods 0.000 title claims abstract description 22
- 239000002994 raw material Substances 0.000 claims abstract description 35
- 238000003723 Smelting Methods 0.000 claims abstract description 30
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 21
- 239000010955 niobium Substances 0.000 claims abstract description 19
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 17
- 239000000463 material Substances 0.000 claims abstract description 15
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 12
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 11
- 238000005266 casting Methods 0.000 claims abstract description 10
- 238000002156 mixing Methods 0.000 claims abstract description 7
- 238000005303 weighing Methods 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims description 26
- 229910000831 Steel Inorganic materials 0.000 claims description 13
- 239000010959 steel Substances 0.000 claims description 13
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 claims description 8
- 229910000592 Ferroniobium Inorganic materials 0.000 claims description 7
- ZFGFKQDDQUAJQP-UHFFFAOYSA-N iron niobium Chemical compound [Fe].[Fe].[Nb] ZFGFKQDDQUAJQP-UHFFFAOYSA-N 0.000 claims description 7
- 230000006698 induction Effects 0.000 claims description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 229910000975 Carbon steel Inorganic materials 0.000 claims description 2
- 238000011065 in-situ storage Methods 0.000 abstract description 11
- 239000011159 matrix material Substances 0.000 abstract description 11
- 230000002787 reinforcement Effects 0.000 abstract description 7
- 239000007788 liquid Substances 0.000 abstract description 4
- 238000009826 distribution Methods 0.000 abstract description 3
- 238000001816 cooling Methods 0.000 abstract description 2
- 230000001105 regulatory effect Effects 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 16
- 238000005299 abrasion Methods 0.000 description 12
- 239000002245 particle Substances 0.000 description 10
- 230000008018 melting Effects 0.000 description 7
- 238000002844 melting Methods 0.000 description 7
- 239000011156 metal matrix composite Substances 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 5
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 229910052581 Si3N4 Inorganic materials 0.000 description 4
- 239000000919 ceramic Substances 0.000 description 4
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical group N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910000628 Ferrovanadium Inorganic materials 0.000 description 3
- 238000004458 analytical method Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000004663 powder metallurgy Methods 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- 238000001308 synthesis method Methods 0.000 description 3
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 238000000498 ball milling Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 238000010183 spectrum analysis Methods 0.000 description 2
- 238000003786 synthesis reaction Methods 0.000 description 2
- JMAHHHVEVBOCPE-UHFFFAOYSA-N [Fe].[Nb] Chemical compound [Fe].[Nb] JMAHHHVEVBOCPE-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000007667 floating Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 230000005501 phase interface Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000009718 spray deposition Methods 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 230000002194 synthesizing effect Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention relates to the technical field of composite materials, in particular to a preparation method of an NbC and VC composite reinforced iron-based composite material, which comprises the following steps: s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials; s2: smelting the raw material obtained in the step S1 at high temperature and casting to obtain NbC and VC composite reinforced iron-based material; according to the invention, the carbide reinforced iron-based composite material is synthesized in situ by adopting liquid smelting, casting is performed after smelting, the cooling speed is high, grain refinement is facilitated, carbide growth is limited, and thus the reinforcement is refined; the relative content of in-situ synthesized NbC and VC can be controlled by adjusting the proportion of the added niobium-containing raw materials and vanadium-containing raw materials, the distribution of Nb and V elements in carbide and iron matrix is regulated, and the overall performance of the material is improved.
Description
Technical Field
The invention relates to the technical field of composite materials, in particular to a preparation method of an NbC and VC composite reinforced iron-based composite material.
Background
Conventional Metal Matrix Composites (MMCs) typically use various types of secondary phases (particles, fibers, whiskers, etc.) to strengthen the metal matrix for higher hardness, strength, wear resistance, thermal stability, etc. Compared with the composite material taking fiber, whisker and the like as reinforcements, the particle reinforced metal matrix composite material has the advantages of wide sources of raw materials, low preparation cost, various preparation methods, easy molding, easy realization and the like, and is easier to get the attention of researchers. Methods for preparing particle-enhanced MMCs are diverse. At present, the preparation methods commonly adopted at home and abroad are mainly divided into two types according to different particle adding or generating modes: one is an external method, such as a powder metallurgy method, a mechanical alloying method, a spray deposition method, a discharge plasma sintering method, a stirring casting method and the like; one is the endophytic method, which often includes in situ synthesis, internal oxidation, and the like.
The in situ synthesis method becomes the hottest method, and the method is mainly characterized in that: the reinforcement has small granularity, is not polluted, and is metallurgically bonded with the metal matrix; compared with other preparation methods, the in-situ synthesis method avoids the complex pretreatment process of the reinforcement, so that the preparation process becomes very simple, and the phase interface is not easy to be polluted to reduce the interface binding force. Although this method plays an important role in the preparation of MMCs, particularly light MMCs, there are few reports of Fe-based MMCs prepared by this method. The reasons are as follows: (1) The density of the reinforcement (nitride, carbide, oxide and the like) is greatly different from that of the base metal Fe, and segregation is easy to generate in the liquid state so as to influence the overall performance; (2) The solid in-situ synthesis method is still a powder metallurgy method, and interface pollution in the pretreatment process of raw materials cannot be avoided; (3) The lack of means for controlling the morphology of the particle-reinforced phase, the single morphology, and sometimes the improvement of the overall mechanical properties is not obvious.
Therefore, the preparation method of the NbC and VC composite reinforced iron-based composite material has the characteristics of small density difference between reinforced phases NbC and VC and Fe matrix, high hardness, high strength, high wear resistance and the like compared with the traditional preparation technology.
Disclosure of Invention
Aiming at the defects existing in the prior art, the invention provides a preparation method of an NbC and VC composite reinforced iron-based composite material, which aims at improving the strength, hardness, wear resistance and the like of the composite material and finally obtaining Fe-NbC-VC iron-based composite materials with different niobium carbide contents.
In order to achieve the technical purpose, the invention is realized by the following technical scheme:
a preparation method of an NbC and VC composite reinforced iron-based composite material comprises the following steps:
s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials;
s2: smelting the raw material obtained in the step S1 at high temperature and casting to obtain NbC and VC composite reinforced iron-based material;
further, in the step S1, the raw materials specifically include: the ferroniobium comprises 15-80% of niobium, and preferably high-niobium ferroniobium is adopted; wherein the vanadium iron contains 40-80% of vanadium, and vanadium iron with high vanadium content is preferentially adopted; carbon steel is preferably steel with high carbon content, such as T10 and T12 steel, etc.
Further, the mass percentage of carbide in the composite material obtained by smelting in the step S2 is 0-9.5%.
Further, in the step S2, the melting may be vacuum arc melting, vacuum induction melting, or arc melting or induction melting with inert shielding gas. The beneficial effects of the invention are as follows:
the preparation method of the NbC and VC composite reinforced iron-based composite material provided by the invention is a method for synthesizing the carbide reinforced iron-based composite material in situ by using a liquid smelting method, and overcomes the defects of long preparation period, multiple procedures, complex preparation process and equipment use, strict production control requirement, high requirement on die materials, high energy consumption, lower production efficiency, high production cost and the like of the traditional powder metallurgy sintering method. The raw materials of the invention do not need pretreatment, and the traditional ball milling process is omitted, because the ball milling process has impurities, the bonding interface of the product is easy to be polluted. Compared with the in-situ synthesis of the invention, the traditional sintering process is characterized in that: (1) the reinforcing phase is formed in the matrix through nucleation and growth, and has thermodynamic stability. (2) The surface of the particle reinforced phase is pollution-free, and the particle reinforced phase is well combined with the matrix because the problem of poor infiltration with the matrix is avoided. (3) The reinforcement size and distribution are easier to control and the number can be adjusted over a larger range. (4) The strength and the elastic modulus of the material can be greatly improved while maintaining better toughness and high-temperature performance. (5) Has the characteristics of simple and convenient process and low cost, and can prepare the component with complex shape and large size.
According to the invention, the carbide reinforced iron-based composite material is synthesized in situ by adopting liquid smelting, casting is performed after smelting, the cooling speed is high, grain refinement is facilitated, carbide growth is limited, and thus the reinforcement is refined; the relative content of in-situ synthesized NbC and VC can be controlled by adjusting the proportion of the added niobium-containing raw materials and vanadium-containing raw materials, the distribution of Nb and V elements in carbide and iron matrix is regulated, and the overall performance of the material is improved. Compared with the adding of niobium and vanadium in different proportions, the hardness of the composite material is maximum when the contents of NbC and VC are equal. The hardness enhancement effect of NbC on the iron-based composite is greater than that of VC. When the NbC and VC contents are relative, the intensity is obviously higher than that of other samples. With the increase of the Nb content, the volume wear rate of the iron-based composite material is gradually reduced, and the wear resistance is gradually improved.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are needed for the description of the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is an XRD pattern for a composite material having 5% total carbide according to the present invention;
FIG. 2 shows a metallographic structure at 500 x (a) pure T12 (b) 5wt% VC (c) 5wt% NbC (d) 2.5wt% NbC+2.5wt% VC (e) 3.33wt% NbC+1.67wt% VC (f) 1.67wt% NbC+3.33wt% VC;
FIG. 3 is a scanning electron microscope and energy spectrum analysis chart of the composite material of the invention.
Detailed Description
The following description of the embodiments of the present invention will be made clearly and completely with reference to the accompanying drawings, in which it is apparent that the embodiments described are only some embodiments of the present invention, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
Example 1
The preparation method of the NbC and VC composite reinforced iron-based composite material comprises the following steps:
s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials; wherein the raw materials are as follows: 2.5% FeV80 (80% V), 2.8% FeNb80 (80% Nb), 76.2% T10 steel and 18.5% pure iron.
S2: and (3) smelting the raw material obtained in the step (S1) at high temperature in a vacuum arc furnace, and casting to obtain the NbC and VC composite reinforced iron-based material.
The mass percentage of theoretical carbide in the composite material obtained by smelting is 5%, and the proportion of theoretical vanadium carbide to niobium carbide is 1:1. the hardness is measured by a Vickers hardness tester, the load is 300N, the pressure is maintained for 10 seconds, and the hardness is highThe degree is 564HV. Compressive Strength test specimen size diameter 3mm, height 6mm, strain rate 0.001s -1 Compressive strength 2518MPa, compressive strain 38.4% and compressive yield strength 1634MPa. The abrasion resistance test adopts a reciprocating frictional abrasion instrument, the pair of the abrasive pair is silicon nitride ceramic balls with the diameter of 6mm, the test time is 60min, the rotating speed is 180rpm, the load is 80N, and the volume abrasion rate is 2.6x10 -6 mm 3 N.m far below 17.7X10 of T12 steel under the same test conditions -6 mm 3 /N·m。
The preparation method of the NbC and VC composite reinforced iron-based composite material comprises the following steps:
s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials; wherein the raw materials are as follows: 6.5% FeV50 (50% V), 2.5% FeNb70 (70% Nb), 82.5% T12 steel, and 8.5% pure iron.
S2: and (3) smelting the raw material obtained in the step (S1) at a high temperature in a vacuum induction furnace, and casting to obtain the NbC and VC composite reinforced iron-based material.
The mass percentage of theoretical carbide in the composite material obtained by smelting is 6 percent, and the proportion of theoretical vanadium carbide to niobium carbide is 2:1. the hardness was measured by a Vickers hardness tester, the load was 300N, the pressure was maintained for 10 seconds, and the hardness was 503HV. Compressive Strength test specimen size diameter 3mm, height 6mm, strain rate 0.001s -1 Compressive strength 1827MPa, compressive strain 45.8%, compressive yield strength 1134MPa. The abrasion resistance test adopts a reciprocating frictional abrasion instrument, the pair of the abrasive pair is silicon nitride ceramic balls with the diameter of 6mm, the test time is 60min, the rotating speed is 180rpm, the load is 80N, and the volume abrasion rate is 9.3 multiplied by 10 -6 mm 3 N.m far below 17.7X10 of T12 steel under the same test conditions -6 mm 3 /N·m。
Example 3
The preparation method of the NbC and VC composite reinforced iron-based composite material comprises the following steps:
s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials; wherein the raw materials are as follows: 2.1% FeV75 (75% V), 5.9% FeNb60 (60% Nb), 83.8% T10 steel and 8.2% pure iron.
S2: and (3) smelting the raw material obtained in the step (S1) at high temperature in an arc furnace protected by high-purity argon, and casting to obtain the NbC and VC composite reinforced iron-based material.
The mass percentage of theoretical carbide in the composite material obtained by smelting is 6 percent, and the proportion of theoretical vanadium carbide to niobium carbide is 1:2. the hardness was measured by a Vickers hardness tester, the load was 300N, the pressure was maintained for 10 seconds, and the hardness was 531HV. Compressive Strength test specimen size diameter 3mm, height 6mm, strain rate 0.001s -1 Compressive strength 2125MPa, compressive strain 33.5% and compressive yield strength 1393MPa. . The abrasion resistance test adopts a reciprocating frictional abrasion instrument, the pair of the abrasive pair is silicon nitride ceramic balls with the diameter of 6mm, the test time is 60min, the rotating speed is 180rpm, the load is 80N, and the volume abrasion rate is 6.2 multiplied by 10 -6 mm 3 N.m far below 17.7X10 of T12 steel under the same test conditions -6 mm 3 /N·m。
Example 4
The preparation method of the NbC and VC composite reinforced iron-based composite material comprises the following steps:
s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials; wherein the raw materials are as follows: 1.6% pure metal V, 5.3% pure metal Nb, 88.8% T12 steel and 4.3% pure iron.
S2: and (3) smelting the raw material obtained in the step (S1) at high temperature in an induction furnace protected by high-purity argon, and casting to obtain the NbC and VC composite reinforced iron-based material.
The mass percentage of theoretical carbide in the composite material obtained by smelting is 8%, and the proportion of theoretical vanadium carbide to niobium carbide is 1:3. hardness was measured using a vickers hardness tester, with a load of 300N, a dwell time of 10 seconds, and a hardness of 591HV. Compressive Strength test specimen size diameter 3mm, height 6mm, strain rate 0.001s -1 Compressive strength 2332MPa, compressive strain 28.2%. The abrasion resistance test adopts a reciprocating frictional abrasion instrument, the pair of the abrasive pair is silicon nitride ceramic balls with the diameter of 6mm, the test time is 60min, the rotating speed is 180rpm, the load is 80N, and the volume abrasion rate is 1.8x10 -6 mm 3 N.m, far lower17.7X10 of T12 Steel under the same test conditions -6 mm 3 /N·m。
Example 5
As shown in fig. 1-3
FIG. 1 is an X-ray diffraction pattern of a composite sample prepared by adding ferroniobium and ferrovanadium in different proportions. (V, nb) C was detected in comparison to samples of 2.5wt% NbC+2.5wt% VC, 3.33wt% NbC+1.67wt% VC, and 1.67wt% NbC+3.33wt% VC, to achieve the material design expectations.
Fig. 2 is a metallographic structure diagram of a composite material sample prepared by adding ferroniobium and ferrovanadium in different proportions at 500 times. It is apparent that particles dispersed on the matrix are seen, which from XRD phase analysis is presumed to be the particulate phase of VC or (V, nb) C. Comparing fig. 2 (a) and 2 (c), the grains of the sample to which niobium was added became finer, demonstrating the effect of niobium from the finer grains. In summary, in combination with XRD results, the structures from fig. 2 (a) to 2 (f) are pearlite+network cementite, ferrite+vc, ferrite, ferrite+ (V, nb) C, respectively. In combination with the previous XRD diffraction phase analysis results and metallographic structure diagram, the generated vanadium carbide in the 5% VC sample is presented as particles, and in combination with the energy spectrum analysis in fig. 3, the carbide particles generated by the sample added with the niobium element and the vanadium element are both particles and rods, which indicates that the shape of the generated carbide is changed by adding the niobium element. The 5wt% VC, 1.67wt% NbC, 3.33wt% NbC samples produced grain sizes between 1-7 microns, while the 2.50wt% NbC samples had lamellar carbide sizes between 12-20 microns. The experiment selects NbC and VC with different contents as variables, and vanadium and niobium are very expensive and pure metals have high melting points, so vanadium iron and niobium iron are selected as raw materials. The melting point of ferrovanadium and ferroniobium is lower than that of pure metal, the T12 steel mainly comprises carbon and iron, wherein the carbon and V, nb are in-situ synthesized into carbide, and the density of the carbide (VC: 5.77 g/cm) 3 ，NbC:7.6g/cm 3 ) Density with iron (7.86 g/cm) 3 ) Near, the floating or sinking is not easy to occur.
FIG. 3 is a scanning electron microscope and a spectrogram of the composite material of the invention. As can be seen from the figure, the rod-like region in the figure is (V, nb) C, and the matrix is ferrite, which is consistent with the metallographic analysis. Niobium is predominantly distributed in the carbide and vanadium is predominantly distributed in the matrix, indicating that niobium is a stronger carbide forming element than vanadium.
In the description of the present specification, the descriptions of the terms "one embodiment," "example," "specific example," and the like, mean that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the present invention. In this specification, schematic representations of the above terms do not necessarily refer to the same embodiments or examples. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples.
The preferred embodiments of the invention disclosed above are intended only to assist in the explanation of the invention. The preferred embodiments are not exhaustive or to limit the invention to the precise form disclosed. Obviously, many modifications and variations are possible in light of the above teaching. The embodiments were chosen and described in order to best explain the principles of the invention and the practical application, to thereby enable others skilled in the art to best understand and utilize the invention. The invention is limited only by the claims and the full scope and equivalents thereof.
Claims (4)
1. A preparation method of an NbC and VC composite reinforced iron-based composite material is characterized by comprising the following steps: the method comprises the following steps:
s1: weighing and mixing all required raw materials according to a designed proportion to obtain smelting raw materials;
s2: and (3) smelting the raw material obtained in the step (S1) at high temperature and casting to obtain the NbC and VC composite reinforced iron-based material.
2. The method for preparing the NbC and VC composite reinforced iron-based composite material according to claim 1, wherein the raw materials in step S1 specifically include: the ferroniobium comprises 15-80% of niobium, and preferably high-niobium ferroniobium is adopted; wherein the vanadium iron contains 40-80% of vanadium, and vanadium iron with high vanadium content is preferentially adopted; carbon steels are preferably high carbon containing steels including, but not limited to, T10, T12 steels.
3. The method for preparing the NbC and VC composite reinforced iron-based composite material according to claim 1, wherein the mass percentage of carbide in the composite material obtained by smelting in the step S2 is 0-9.5%.
4. The method for preparing the NbC and VC composite reinforced iron-based composite material according to claim 1, wherein the smelting in the step S2 is vacuum arc smelting, vacuum induction smelting, or arc smelting or induction smelting with inert shielding gas.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311073225.5A CN117144229A (en) | 2023-08-24 | 2023-08-24 | Preparation method of NbC and VC composite reinforced iron-based composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311073225.5A CN117144229A (en) | 2023-08-24 | 2023-08-24 | Preparation method of NbC and VC composite reinforced iron-based composite material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN117144229A true CN117144229A (en) | 2023-12-01 |
Family
ID=88903686
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202311073225.5A Pending CN117144229A (en) | 2023-08-24 | 2023-08-24 | Preparation method of NbC and VC composite reinforced iron-based composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN117144229A (en) |
-
2023
- 2023-08-24 CN CN202311073225.5A patent/CN117144229A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112391556B (en) | High-strength high-conductivity Cu-Cr-Nb alloy reinforced by double-peak grain size and double-scale nanophase | |
| Teber et al. | Effect of SPS process sintering on the microstructure and mechanical properties of nanocrystalline TiC for tools application | |
| CN1325681C (en) | Ceramic granule reinforced aluminium-base composite material and its preparing method | |
| CN109338172A (en) | A kind of 2024 aluminum matrix composites and preparation method thereof of high-entropy alloy enhancing | |
| Li et al. | Towards high strengthening efficiency by in-situ planting nano-TiB networks into titanium matrix composites | |
| Yan et al. | Effects of Cr content on microstructure and mechanical properties of WMoNbTiCr high-entropy alloys | |
| WO2023231744A1 (en) | High-entropy alloy-based nano super-hard composite material reinforced by embedded particles, and preparation method therefor | |
| Bai et al. | Microstructure and impact properties of Ta-TaC core–shell rod-reinforced iron-based composite fabricated by in situ solid-phase diffusion | |
| Gao et al. | Interfacial structure and properties of microwave sintered FeCoNi1. 5CrCu/Al composites | |
| Verma et al. | Microstructure evolution and mechanical properties of aluminium matrix composites reinforced with CoMoMnNiV high-entropy alloy | |
| Vidyasagar et al. | Improvement of mechanical properties of 2024 AA by reinforcing yttrium and processing through spark plasma sintering | |
| CN114293087B (en) | Single-phase high-entropy alloy with micron/nano-crystalline grain composite structure | |
| Ma et al. | Study on strengthening mechanism and high temperature mechanical properties of TiC-Fe-HEA cemented carbide | |
| Xiao et al. | Effect of heat treatment process on mechanical properties and microstructure of FeAlCoCrNiTi0. 5 alloy | |
| Nie | Patents of methods to prepare intermetallic matrix composites: A Review | |
| Cai et al. | Effect of pre-annealing on microstructure and compactibility of gas-atomized Al-Si alloy powders | |
| Wang et al. | Preparation and mechanical behavior of Co‐based hard particles reinforced aluminum matrix composites | |
| Rangaraj et al. | Synthesis, characterization, and mechanical properties evaluation of Mg-Ti 3 AlC 2 composites produced by powder metallurgy/hot pressing | |
| Li et al. | Structures and properties of cast irons reinforced by trace addition of modified SiC nanopowders | |
| Qi et al. | Effect of TiO2 nano-ceramic particles on microstructure and mechanical properties of Al0. 4CoCrFe2Ni2 high-entropy alloy | |
| Suriyaprakash et al. | Investigation of mechanical properties on Mg/TiC/graphite hybrid composites fabricated by powder metallurgy techniques | |
| CN117144229A (en) | Preparation method of NbC and VC composite reinforced iron-based composite material | |
| Siheng et al. | Effect of ball milling speed and sintering temperature on microstructure and properties of TiAl alloy prepared by powder metallurgy | |
| Kamrani et al. | Synthesis and characterization of Al–SiC nanocomposites produced by mechanical milling and Sintering | |
| Daoush et al. | Effect of binder compositions on microstructure, hardness and magnetic properties of (Ta, Nb) C–Co and (Ta, Nb) C–Ni cemented carbides |
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 |