KR20160144821A - Casting manufacturing method of cermet and cermet manufactured thereby - Google Patents
Casting manufacturing method of cermet and cermet manufactured thereby Download PDFInfo
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- KR20160144821A KR20160144821A KR1020150081483A KR20150081483A KR20160144821A KR 20160144821 A KR20160144821 A KR 20160144821A KR 1020150081483 A KR1020150081483 A KR 1020150081483A KR 20150081483 A KR20150081483 A KR 20150081483A KR 20160144821 A KR20160144821 A KR 20160144821A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
- C22C1/053—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor with in situ formation of hard compounds
- C22C1/056—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor with in situ formation of hard compounds using gas
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/12—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on oxides
Abstract
Description
The present invention relates to a method for producing a cermet of a cermet and a thermometer produced thereby.
A cermet is a compound of cermaic and metal. It refers to a material that has a wide range of metals and alloys that are matrices and contain ceramic particles, and that have the merits of metals and ceramics. . The cemented carbide is distinguished from the cemented carbide most widely used in manufacturing cutting tools. Compared with cemented carbide of the prior art, there is a limit in application due to remarkably low strength and toughness. To solve this problem, the improved type thermome which can increase the base content and compensate the reduction of the hardness by the heat treatment enhancement on the base . The improved type of cermet is manufactured by mixing ceramic powder and individual elemenet or pre-alloyed powders through a sintering step. The material thus prepared is characterized by the characteristics of the raw powder and the sintering step. The abrasion resistance and toughness are greatly changed according to the manufacturing conditions. In addition, since the sintering is performed under the condition that the matrix phase is changed to the liquid phase for sufficient wetting of the matrix on the substrate, the size of the product that can be manufactured is also limited.
In addition to the powder metallurgy using the sintering process, the method of producing the cermet is to make the casting step and the desired product shape into a preform having a large porosity, And a pressure infiltration method in which pressurized infiltration is performed. Powder metallurgy method among various manufacturing methods requires a high cost due to high base metal price and difficult material processing, has a simple product shape, has a limited size, has complicated steps, and requires a high investment facility cost compared to a liquid phase . Even in the case of pressurized consolidation, it is possible to manufacture a metal composite intermediate having a low volume ratio at a low cost, but a large amount of defects (pores) are generated in the composite material, thereby limiting the improvement of high temperature structural characteristics (high temperature strength and hardness). Particularly, in order to produce a large size, existing methods require a large-sized, high-vacuum equipment, and it is difficult to prepare a preform for forming a preform. As the size of the resultant product increases, problems similar to powder metallurgy are produced in the production of preforms, and it is difficult to form a good interface between the matrix and the reinforcing phase when impregnating the molten metal. Since each step has advantages and disadvantages, excellent interfacial properties between the matrix and the reinforcing phase formed in the production of the metal composite material are required, and excellent mechanical properties (tensile, compression, wear, fatigue, creep, etc.) are required at room temperature and high temperature. In order to solve this problem, a casting method including a strengthening phase element in a molten metal can be used. However, due to the low density of Ti, the casting method is almost lifted in a high temperature casting environment and Ti is floated in the solid state before melting in the alloy melt So that it is difficult to obtain a composite alloy in actual casting.
It is an object of the present invention to overcome the problems of the related art and to overcome the limitations of the cost competitiveness and productivity of the existing powder metallurgy method by using a casting method, Product and a near-net shape, and to provide a method for manufacturing a casting method of a thermite having a small deformed shape and excellent mechanical properties in the manufacture of a large-sized product, and a thermet produced by the method.
However, the problems to be solved by the present invention are not limited to the above-mentioned problems, and other matters not mentioned can be clearly understood by those skilled in the art from the following description.
According to a first aspect of the present invention, Titanium-based materials; An alloy steel matrix containing at least one or more metals selected from the group consisting of Fe, Ni, Si, Mn, Mo, Cr, Cu, W and V to form a molten metal; And casting the molten metal into a mold.
Further comprising the step of deoxidizing the molten metal by adding a deoxidizing agent to the molten metal after the step of forming the molten metal, wherein the deoxidizing the molten metal comprises, after adding the deoxidizing agent, So as to inhibit oxidation.
The deoxidizer may be Fe, Ti, Si, Mn, C, Al, Mn-Si, Ca-Si, Mg- Fe-Ti) and Al-coated Fe-Ti (Al-coated Fe-Ti).
The deoxidizing agent may be 0.05% by weight to 3% by weight of the molten metal.
The step of forming the molten metal may be performed in a high-frequency induction furnace at a temperature of 1,300 DEG C to 1,800 DEG C and an atmosphere of 760 Torr to 1 x 10-3 Torr for 0.5 to 24 hours.
The casting may be performed at a temperature ranging from room temperature to 1,000 ° C and an atmosphere ranging from 760 Torr to 1 × 10 -3 Torr for 0.5 to 24 hours.
The carbonizer may be at least one selected from the group consisting of graphite, graphene, carbon black, diamond, diamond like carbon (DLC), fullerene, C60, carbon fiber, carbon nanorods and carbon nanotubes , And the carbon dioxide agent may be 0.5% to 4% by weight of the mixture.
The titanium based material may be at least one selected from the group consisting of pure titanium (100% Ti), iron titanium (FeTi), manganese titanium (MnTi), barium titanium (BaTi), strontium titanium (SrTi), nickel titanium (NiTi) and cobalt titanium , And the titanium-based material may be at least 2 wt% to 12 wt% of the mixture.
The catalyst and the titanium-based material may be titanium carbide (TiC) or Ti (M) C (where M is a transition metal).
The TiC may be formed in an in-situ reaction in the alloy steel base.
The TiC may be 3 wt% to 15 wt% of the cermet.
The molar fraction of the carbonizer / titanium-based material may be 0.5 to 1.5.
The alloy steel base includes at least one selected from the group consisting of a mold steel, a high-strength steel, a cemented carbide, a tool steel, and a stainless-steel-based alloy, and the mold steel is at least one selected from the group consisting of SKD11, SKD61, SKH51, SKH55 and SKH59 And at least one selected from the group consisting of < RTI ID = 0.0 >
Wherein the alloy steel base comprises at least one selected from the group consisting of nickel (Ni) exceeding 0 wt% to 5 wt%, silicon (Si) 0.1 wt% to 1.8 wt%, manganese (Mn) (Cu), more than 0 wt% to 12 wt% of tungsten (W), and 3 wt% or more of chromium (Cr) (V) more than 0% by weight and 3% by weight.
The alloy steel base may be 85 wt% to 97 wt% of the mixture.
After the step of casting the molten metal, the thermome formed by the casting is carried out by at least one selected from the group consisting of hot isostatic processing (HIP), quenching and tempering Wherein the hot isostatic pressing is carried out in a temperature range of 1,100 DEG C to 1,300 DEG C and a pressure of from 61 x 10 4 Torr (80 MPa) to 76 x 10 4 Torr (100 MPa) Wherein the quenching is carried out in a temperature range of 900 ° C to 1,100 ° C and a pressure range of 1 × 10 -3 Torr to 1 × 10 1 Torr At a temperature in the range of 160 ° C. to 700 ° C. and a pressure range of 1 × 10 -3 Torr to 1 × 10 1 Torr for a period of from 0.5 hours to 24 hours, of mine It may be maintained for 24 hours range.
The mold may include at least one selected from the group consisting of a mold, a mold, a ceramic mold, and a graphite mold.
The second aspect of the present invention provides a cermet produced by the method of manufacturing a cermet according to the first aspect of the present invention having a relative density of 97% or more after casting.
The method for preparing a casting mold of the present invention and the thermomeat produced by the method according to the present invention can be applied to a large size product, a near-net shape and a thin product having a slope through the production of a casting- Can be manufactured, and mass-produced at low cost. In addition, it is possible to mass-produce the inexpensive large amount of the cermet produced by the in-situ reaction of the ceramic reinforced phase (TiC) in the alloy steel matrix, and it has excellent interfacial properties between the base alloy and the formed strengthened phase, It is possible to produce a thermome having excellent mechanical properties such as compression, wear, fatigue and creep.
1 is a flowchart of a method for manufacturing a thermometer according to an embodiment of the present invention.
2 is a flowchart showing the detailed steps of the deacidification processing step of FIG.
3 is a photograph of a product manufactured according to Example 1 of the present invention.
4 is a photograph of a product manufactured according to Comparative Example 1 of the present invention.
5 is a microstructure photograph of a product manufactured according to an embodiment of the present invention ((a) Example 1, (b) Example 3).
6 is a result of analyzing the components of a precipitate of a product manufactured according to an embodiment of the present invention.
FIG. 7 shows the results of evaluating the high-temperature hardness characteristics of a product manufactured according to an embodiment of the present invention.
Hereinafter, embodiments of the present invention will be described in detail with reference to the accompanying drawings. In the following description of the present invention, detailed description of known functions and configurations incorporated herein will be omitted when it may make the subject matter of the present invention rather unclear. Also, terminologies used herein are terms used to properly represent preferred embodiments of the present invention, which may vary depending on the user, intent of the operator, or custom in the field to which the present invention belongs. Therefore, the definitions of these terms should be based on the contents throughout this specification. Like reference symbols in the drawings denote like elements.
Throughout the specification, when an element is referred to as "comprising ", it means that it can include other elements as well, without excluding other elements unless specifically stated otherwise.
BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, a method of manufacturing a casting mold of the present invention and a method of producing the same will be described in detail with reference to examples and drawings. However, the present invention is not limited to these embodiments and drawings.
According to a first aspect of the present invention, Titanium-based materials; An alloy steel matrix containing at least one or more metals selected from the group consisting of Fe, Ni, Si, Mn, Mo, Cr, Cu, W and V to form a molten metal; And casting the molten metal into a casting mold.
According to an embodiment of the present invention, a method of manufacturing a casting method of a thermometer is to manufacture a large-sized product, a near-net shape, and a thin product having a slope through the production of a cast- Can be mass-produced at low cost. In addition, the in-situ reaction of TiC or Ti (M) C (M is a transition metal) in the alloy steel matrix can be mass-produced at low cost and the interface between the base alloy and the formed TiC It is possible to produce a thermite having excellent mechanical properties such as tensile, compression, wear, fatigue and creep at room temperature and high temperature.
FIG. 1 is a flow chart of a method of manufacturing a corn meal according to an embodiment of the present invention, and FIG. 2 is a flowchart showing detailed steps of a deoxidation process of FIG. 1 and 2, a method of manufacturing a casting method of a thermometer according to an embodiment of the present invention includes forming a molten metal (S100), a deoxidizing process (S200), a casting process (S300), and a heat treatment step (S400). The deoxidation treatment step (S200) may be divided into a dehydrogenation treatment step (S210) and a titanium protective deoxidation treatment step (S220).
First, the molten metal forming step (S100) Titanium-based materials; (Al 2 O 3 or ceramics such as MgO, etc.) containing at least one metal selected from the group consisting of Fe, Ni, Si, Mn, Mo, Cr, Cu, Type or graphite type) and then heated to form a molten metal.
The molten
The carbonizer may be at least one selected from the group consisting of graphite, graphene, carbon black, diamond, diamond like carbon (DLC), fullerene, C60, carbon fiber, carbon nanorods and carbon nanotubes But the present invention is not limited thereto.
The carbonating agent may be 0.5 wt% to 4 wt% of the mixture.
The titanium based material may be at least one selected from the group consisting of pure titanium (100% Ti), iron titanium (FeTi), manganese titanium (MnTi), barium titanium (BaTi), strontium titanium (SrTi), nickel titanium (NiTi) and cobalt titanium But it is not limited thereto.
The titanium-based material may be 2 wt% to 12 wt% of the mixture.
The carbonizer and the titanium-based material may be titanium carbide (TiC) or titanium complex carbide (Ti (M) C, where M is a transition metal). The TiC may be a strengthened phase and may be formed in an in-situ reaction in the alloy steel base. The TiC may have a spherical shape. In this case, since the surface area is small, it is possible to maintain a higher applied stress, thereby having better mechanical characteristics. In addition, crack propagation and dislocation movement And a decrease in the possibility of crack formation.
The TiC may be 3 wt% to 15 wt% of the cermet. When the content of TiC is less than 3% by weight, the abrasion resistance of the base alloy is not significantly improved. When the content of TiC exceeds 15% by weight, And the possibility of oxidation of Ti is increased to cause a problem in forming a good molten metal due to the increase of viscosity and oxidation.
The molar ratio of the carbonizer / the titanium-based material may be 0.5 to 1.5. If the molar ratio of the carbonizer / the titanium-based material is less than 0.5, the residual Ti that does not form carbide remains in the base alloy in the form of oxides and acts as inclusions, thereby significantly lowering the physical properties at low temperature and high temperature If it is more than 1.5, it may cause problems such that the casting stability is deteriorated due to the residual in the base alloy of the excess carbon which can not participate in the reaction, and the produced thermite also has brittleness.
The alloy steel base may include at least one selected from the group consisting of a die steel, a high-strength steel, a cemented carbide, a tool steel, and a stainless steel alloy, but is not limited thereto.
The mold steel may include at least one selected from the group consisting of SKD11 (cold metal mold), SKD61 (hot mold steel), SKH 51, SKH 55 and SKH 59.
The stainless alloy system may include at least one selected from the group consisting of STS 430, STS 409, STS 410, STS 440 (C) and STS 630 (17-4 PH).
Wherein the alloy steel base comprises at least one selected from the group consisting of nickel (Ni) exceeding 0 wt% to 5 wt%, silicon (Si) 0.1 wt% to 1.8 wt%, manganese (Mn) More than 0 wt% to 12 wt% of tungsten (W), more than 0 wt% to 3.0 wt% of chromium (Cr), 3 wt% to 25 wt% (V) more than 0% by weight and 3% by weight. At least one or more selected from the group consisting of nickel (Ni), silicon (Si), manganese (Mn), molybdenum (Mo), chrome (Cr), copper (Cu), tungsten (W) and vanadium In addition, it can further improve tensile strength, hardness, toughness, rigidity, abrasion resistance, impact resistance, corrosion resistance, and creep characteristics. For this reason, alloy steel bases employing alloying elements with higher oxygen affinity than Fe, such as Cr, Mo, Ni, Mn and Al, have excellent wettability at the interface between reinforcing phases containing some oxides. Cr, Ni, And the transition elements such as Cr, Mo, V, W, and Nb serve as C and carbide formation and fine grain refinement.
The alloy steel base may be 85 wt% to 97 wt% of the mixture. The strengthened phase and the alloy steel base may be of coherency. Consistency is related to atomic array matching between newly formed particles (reinforced phase, TiC) and alloy steel bases. Generally, excellent atomic arrangement provides excellent mechanical properties especially at high temperatures. Composite carbides, mechanically alloying (MA) particles (oxide dispersion strengthened alloy ODS) in the form of precipitation hardening (including in situ reaction) and Ti (M) C have conformity, The mechanical properties are remarkably superior to those of the characteristics. This consistency can be observed by observing the atomic arrangement directly with a high magnification TEM by atomic arrangement difference or by observing the lattice parameter change at the interface through XRD and confirming the degree of conformity.
The deoxidation treatment step S200 may be divided into a molten metal deoxidation treatment step S210 and a titanium protective deoxidation treatment step S220. In the deoxidation treatment step S210, oxygen contained in the molten metal is removed In the present invention, a deoxidizing agent may be added to the molten metal to remove oxygen. After the deoxidizer is added, the deoxidizer is immersed in the molten metal to prevent oxidation. At this time, the slag flocculant can be further added, and the slag flocculant can remove the slag flocculation and purify the slag through the SiO 2 material.
The deoxidizing agent for deoxidation of the molten metal is at least one selected from the group consisting of Fe, Ti, Si, Mn, C, Al, Mn-Si, Ca-Si, Mg-Ca, Al- But it is not limited thereto.
The deoxidizing agent may be 0.05% by weight to 3% by weight of the molten metal.
Oxygen concentration and activity in the molten steel are reduced due to the deoxidizing agent. Therefore, it can be mass-produced at a low cost in accordance with deoxidation treatment that minimizes the occurrence of oxidation, and it is possible to manufacture a large-sized product, a near-net shaped product, and a thin product with a slope, and to reduce the cost.
The titanium protective deoxidation treatment step S220 is a step for protecting the Ti source, wherein the titanium protective deoxidizer is an Al-foiled Fe-Ti or an Al-coated Fe-Ti (Al-coated Fe-Ti). It is important that the titanium protective deoxidizer is added to the melt before being immersed in the melt. This is because oxidation can proceed through contact with air even during short floating time. That is, Al-foiled Fe-Ti or Al-coated Fe-Ti has a low specific gravity and floats on the molten metal. Thus, Fe (Al-foiled Fe-Ti) or Al-coated Fe-Ti (Al-foiled Fe-Ti) because the oxidation proceeds from the exposed upper part when the Al- - Coated Fe-Ti (Al-coated Fe-Ti) can be rapidly charged into the melt and pressurized by mechanical stirring. For example, using Fe-Ti, which is the same as that of the base composition, it exerts mechanical pressure externally until the Fe-Ti melts in the melt, thereby melting only trace amounts of Fe-Ti. In this case, since the Ti source is phylonized or coated with Al, Al is oxidized before Ti, and the reaction of oxidizing Ti can be suppressed. If the thickness of the foil or coated Al is greater than 2 mm, Al reacts with oxygen in the molten steel and the continuous dissolution and diffusion of the internal Al is suppressed for a certain period of time after forming the Al 2 O 3 coating, The residence time in the molten steel of the foilized Al-foiled Fe-Ti or Al-coated Fe-Ti must be increased. The higher the Ti content, the higher the possibility of oxidation and thus the viscosity and flocculation can be increased. Therefore, it is possible to increase the Ti recovery rate in the molten metal through oxidation prevention treatment and uniformly disperse Ti through stirring by high frequency induction.
The uniform dispersion of TiC in the molten metal is also directly influenced by the flowability of the molten metal. The flowability of the molten metal is improved by adding an alloying element containing a large amount of melting point elements C and Si, or adding an alloy element from the outside, increasing the melting operation temperature, preventing viscosity increase through prevention of oxidation of Ti source, inducing stirring at high frequency , Gas agitation may also be included), and the like.
The casting step (S300) may be performed by casting the molten metal into a mold. The mold may include at least one selected from the group consisting of a mold, a mold, a ceramic mold such as Al 2 O 3 or MgO, and a graphite mold. At this time, the mold can be preheated by placing it in advance.
The casting step (S300) may be performed at a temperature ranging from room temperature to 1,000 ° C and a range of from 0.5 hour to 24 hours in an atmosphere or vacuum atmosphere of 760 Torr to 1 × 10 -3 Torr. The molten metal may be directionally solidified in the mold to form a cermet.
If an alloy steel base having a large amount of transition elements in the casting step (S300) is used, free carbon formation of C remaining at a rapid cooling rate can be prevented. When an alloy steel base having a large amount of transition elements is used, abrasion resistance is increased due to carbides such as TiC, Ti (M) C composite carbide and MC. In addition to the molar ratio between the gas phase and the titanium, the effect of the carbon content of the alloy base and other types of transition elements is described by Thermal Calc. Or J Mat Pro, and finally determine the amount of carbon added (thus representing the C / Ti molar ratio range from 0.5 to 1.5). The faster the cooling rate is, the more segregation of alloy components can be controlled and the size of dendrite can be reduced to achieve uniform grain size dispersion of a few tens of micro- Instead, the amount of the fine secondary TiC fraction formed in the secondary arm of the resin is small, but the shape of the primary TiC precipitate formed in the primary branch is close to the spherical shape. For reference, the grain size of the strengthened phase has the greatest influence on the solute (Ti) gradient at the solid phase at the resinous phase when cooling from the molten metal. The higher the grain boundary fraction, the more uneven nucleation sites are, So that the degree of dispersion can be increased. On the other hand, when focusing on a thermal shock environment due to harsh rapid heating and cooling rather than heat and abrasion characteristics among the high temperature characteristics of the manufactured material, it can also be applied to a gas atomizing process. When the molten metal is made into a sintered material by pre-alloyed powder through atomization, it may lead to refinement of the strengthening phase and induction of precipitation.
The heat treatment step (S400) may be performed by at least one selected from the group consisting of hot isostatic processing (HIP), quenching and tempering.
The temperature increases the temperature of the cermet through the high-temperature isostatic pressing step, thereby promoting densification. It is possible to improve the characteristics by removing defects such as residual pores and to produce a cermet having a theoretical density. The high temperature isostatic pressing during the heat treatment is carried out by heating the cermet formed by the casting in a temperature range of 1,100 ° C. to 1,300 ° C. and a pressure range of 61 × 10 4 Torr (80 MPa) to 76 × 10 4 Torr (100 MPa) In the range of 0.5 hours to 24 hours.
The quenching during the heat treatment is carried out by maintaining the thermo formed by the casting in a temperature range of 900 ° C to 1,100 ° C and a pressure range of 1 × 10 -3 Torr to 1 × 10 1 Torr for a range of 0.5 hours to 24 hours Nitrogen and helium gas cooling, atmospheric air cooling, oil cooling, and water cooling.
Tempering during the heat treatment may be such that the thermoform formed by the casting is maintained in the temperature range of 160 ° C to 700 ° C and the pressure range of 760 Torr to 1 × 10 -3 Torr for the range of 0.5 to 24 hours . When the heating temperature is less than 160 캜 and the holding time is less than 0.5 hours, deformation due to retained austenite due to the expansion due to retained austenite can not be sufficiently removed. When the temperature exceeds 700 캜, The heating temperature is preferably less than 700 占 폚, particularly preferably 200 占 폚 to 600 占 폚. The cooling at the time of the heat treatment includes a furnace cooling which is left in a heat treatment furnace and cooled by natural cooling.
The tempering during the heat treatment may be performed at least once in the thermoform formed by the casting, or may be carried out plural times. When the heat treatment is performed once, the productivity is low due to a small number of manufacturing steps, and in the case where the heat treatment is performed a plurality of times, the strength of the thermite can be increased or the processing strain can be removed to improve toughness.
The second aspect of the present invention provides a cermet produced by the method of manufacturing a cermet according to the first aspect of the present invention having a relative density of 97% or more after casting. The cermet according to the present invention can produce a large size product, a near net shape and a thin slim product through the production of casting base rather than the conventional powder molding, , Mechanical properties such as tensile, compression, wear, fatigue and creep are excellent.
Hereinafter, the present invention will be described in more detail with reference to the following examples. However, the following examples are for illustrative purposes only and are not intended to limit the scope of the present invention.
[Example 1]
A, C / Ti ratio for the production of TiC composite to 1.0, creates a molten metal melt SKD61 94.44% by weight of the base alloy, gatan the 0.66% by weight to 1,650 ℃ to 1,680 ℃ crucible, slacks as a slag aggregation removing agent (SiO 2 0.1% by weight of Mn, 0.8% by weight of Si and 0.2% by weight of Al were mixed for the purpose of deoxidation, and 3.66% by weight of Al foilized Fe-70Ti was rapidly charged into the melt and the surface portion was stirred. (Including the foiled weight in weight percent of Al). The melt was then poured into a mold for casting molds and cooled to give directionally solidified. Subsequently, HIP treatment was performed at 1,200 占 폚, quenching was performed at 1,035 占 폚, first 550 占 폚 and second 580 占 폚 to produce a cermet. TiC in the prepared cermet had 4 vol%.
[Example 2]
A, C / Ti ratio for the production of TiC composite to 1.0, creates a molten metal melt SKD61 90.08% by weight of the base alloy, gatan the 1.34% by weight to 1,650 ℃ to 1,680 ℃ crucible, slacks as a slag aggregation removing agent (SiO 2 0.15% by weight of Mn, 0.85% by weight of Si and 0.18% by weight of Al were mixed and 7.45% by weight of Al foilized Fe-70Ti was rapidly charged into the melt and the surface portion was stirred (weight% (Including weighted weight). Subsequently, the molten metal was poured into a casting casting mold and cooled so as to be directionally solidified. Subsequently, the resultant was subjected to HIP treatment at 1200 占 폚, quenching at 1,035, first 550 占 폚 and second 580 占 폚 to produce a cermet. TiC in the prepared cermet had 9% by volume.
[Example 3]
For the production of TiC composite, a C / Ti ratio to 1.0, creates a molten metal melt SKD11 85.51% by weight of the base alloy, gatan the 2.04% by weight to 1,650 ℃ to 1,680 ℃ crucible, slacks as a slag aggregation removing agent (SiO 2 0.1 wt% of Mn, 0.8 wt% of Si and 0.2 wt% of Al were mixed and 11.39 wt% of Al foilized Fe-70Ti was rapidly charged into the melt and the surface portion was stirred (weight% of Al) (Including weighted weight). Subsequently, the molten metal was poured into a casting casting mold and cooled so as to be directionally solidified. Subsequently, HIP treatment was performed at 1,200 占 폚, quenching at 1,050 占 폚, and heating at 200 占 폚 were conducted to produce a cermet. The TiC content of the prepared cermets was 13% by volume.
[Comparative Example 1]
Base alloy SKD61 content of 93.47% by weight, and TiC content of 6.53% by weight. Then, the ball mill was filled with a mixed powder and a heptane as a solvent. Then, the prepared ball mill was placed on a ball mill and the ball mill process was carried out for 20 hours at an optimum rotation speed of about 150 rpm considering ball falling. Respectively. The pulverized powder was recovered and charged into a hydraulic press to form a compact at a pressure of 50 MPa. The compact was sintered in a vacuum atmosphere of 5 × 10 -2 Torr in a vacuum furnace maintained at a temperature of 1435 ° C. for 2 hours, And then cooled to room temperature. Subsequently, HIP treatment was performed at 1,320 DEG C, and quenching at 1,035 DEG C, first 550 DEG C and second 580 DEG C were conducted to produce a cermet. The TiC content of the prepared cermets was 10% by volume.
[Comparative Example 2]
Commercial material SKD61 was quenched in 1035, first tempered at 550 ° C, secondly at 580 ° C.
[Comparative Example 3]
Commercial material SKD11 was quenched in 1035, first tempered at 550 ° C, secondly at 580 ° C.
The design and characteristics of the fabricated materials are shown in Tables 1 and 2 below.
TiC
content
(volume%)
(weight
%
)
density
(g / cm
3
)
base
sauce
(94.44)
Q: 1035
T1: 530
T2: 580
(90.08)
Q: 1035
T1: 530
T2: 580
(85.51)
Q: 1050
T: 200
(93.47)
(6.53)
Q: 1035
T1: 530
T2: 580
(100)
T1: 530
T2: 580
(100)
T: 200
H: HIP, Q: quenching, T: tempering, 1,2: primary, secondary
base
TiC content
(volume%)
content
(
volume%
)
density
(g /
cm
3
)
density
(%)
(
HV
,
Load 5kgf
)
As described above, it was found that the cast materials of Examples 1 to 3 had better hardness characteristics than those of Comparative Examples 1 to 3 at room temperature to 500 ° C, which is the temperature range of use of the material.
FIG. 3 is a photograph of a product manufactured according to Example 1 of the present invention, and FIG. 4 is a photograph of a product manufactured according to Comparative Example 1 of the present invention. Referring to FIGS. 3 and 4, in the case of FIG. 3, the thermat produced by the casting method according to the first embodiment of the present invention is excellent in both density and relative density, Could know. On the other hand, in the case of the cermet produced by the powder metallurgy method according to Comparative Example 1 of the present invention, debinding is difficult, and as the length ratio becomes larger, the difference in density at the time of taking out causes a crack. Accordingly, it has been confirmed that the thermat produced by the casting method of the present invention can produce a high-strength TiC dispersed material for use as a tool material.
5 is a microstructure photograph ((a) of Example 1, (b) of Example 3) observed with an optical microscope of a product manufactured according to an embodiment of the present invention. Referring to FIG. 5, it was confirmed that carbide was precipitated at a level of 80% or more of the target fraction of TiC.
6 is a result of analyzing the components of a precipitate of a product manufactured according to an embodiment of the present invention. Referring to FIG. 6, SEM-EDS was used to confirm the composition of the precipitated carbide. As a result, it was confirmed that it was a carbide of Ti (M) C type.
FIG. 7 shows the results of evaluating the high-temperature hardness characteristics of a product manufactured according to an embodiment of the present invention. Referring to FIG. 7, evaluation of the mechanical properties of the manufactured material within the operating temperature range was performed. In the high temperature hardness test, test pieces having a diameter of Φ10 mm (tolerance of 0.1), a thickness of 5 mm (tolerance of 0.1), a hole diameter of Φ3 mm and a depth of 4 mm for a side surface thermocouple insertion hole were prepared. The heat treatment was carried out at a heating rate of 100 ° C / min and a holding time of 5 minutes. Then, the load of the particles was increased to 5 kgf. As a result, it was confirmed that the material of the examples had excellent mechanical properties as compared with the materials of the comparative examples.
While the invention has been shown and described with reference to certain preferred embodiments thereof, it will be understood by those of ordinary skill in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention as defined by the appended claims. This is possible. Therefore, the scope of the present invention should not be limited to the described embodiments, but should be determined by the equivalents of the claims, as well as the claims.
Claims (18)
Casting the molten metal into a mold;
≪ / RTI >
After the step of forming the molten metal,
Further comprising deoxidizing the molten metal by adding a deoxidizing agent to the molten metal,
Wherein the step of deoxidizing the molten metal is characterized in that after the deoxidizing agent is added, the deoxidizing agent is immersed in the molten metal to inhibit oxidation.
The deoxidizer may be Fe, Ti, Si, Mn, C, Al, Mn-Si, Ca-Si, Mg- Fe-Ti) and Al-coated Fe-Ti (Al-coated Fe-Ti).
Wherein the deoxidizing agent is 0.05 to 3% by weight of the molten metal.
Wherein the forming of the molten metal comprises:
In a high frequency induction furnace in a temperature range of 1,300 DEG C to 1,800 DEG C and an atmospheric environment of 760 Torr to 1 x 10-3 Torr for a period of 0.5 to 24 hours.
Wherein the casting comprises:
In a temperature range of from room temperature to 1,000 ° C and in an air atmosphere of from 760 Torr to 1 x 10 -3 Torr for a period of from 0.5 hours to 24 hours.
The carbonizer may be at least one selected from the group consisting of graphite, graphene, carbon black, diamond, diamond like carbon (DLC), fullerene, C60, carbon fiber, carbon nanorods and carbon nanotubes And at least one selected from the group consisting of
Wherein the carbonizer is 0.5 wt% to 4 wt% of the mixture.
The titanium based material may be at least one selected from the group consisting of pure titanium (100% Ti), iron titanium (FeTi), manganese titanium (MnTi), barium titanium (BaTi), strontium titanium (SrTi), nickel titanium (NiTi) and cobalt titanium And at least one selected from the group consisting of < RTI ID = 0.0 >
Wherein the titanium-based material is 2 wt% to 12 wt% of the mixture.
Wherein the carbonizer and the titanium-based material form titanium carbide (TiC) or Ti (M) C (M is a transition metal).
Wherein the TiC is formed by an in-situ reaction in the alloy steel base.
Wherein the TiC is 3 wt% to 15 wt% of the cermet.
Wherein the molar fraction of the carbonizer / the titanium-based material is 0.5 to 1.5.
The alloy steel base includes at least one selected from the group consisting of a metal mold, a high steel, a cemented carbide, a tool steel, and a stainless alloy,
Wherein the mold steel comprises at least one selected from the group consisting of SKD11, SKD61, SKH51, SKH55 and SKH59.
The alloy steel base,
The alloy steel according to any one of claims 1 to 3, wherein the alloy steel contains at least 5 wt% of Ni, at least 0.1 wt% of Si, at least 1.0 wt% of Mn, (W), more than 0 wt% to 12 wt% of vanadium (V) and 0 wt% of vanadium (V) % To 3% by weight based on the total weight of the cermet.
Wherein the alloy steel base is 85 wt% to 97 wt% of the mixture.
After the casting of the molten metal,
Further comprising a heat treatment step performed by at least one selected from the group consisting of hot isostatic processing (HIP), quenching and tempering,
The high temperature isostatic pressing is carried out in a temperature range of 1,100 ° C. to 1,300 ° C. and a pressure range of 61 × 10 4 Torr (80 MPa) to 76 × 10 4 Torr (100 MPa) for 0.5 to 24 hours Time range,
The quenching is carried out by maintaining the thermoform formed by the casting in a temperature range of 900 ° C to 1,100 ° C and a pressure range of 1 × 10 -3 Torr to 1 × 10 1 Torr for a range of 0.5 hours to 24 hours,
Wherein the tempering maintains the thermoform formed by the casting in a temperature range of 160 ° C to 700 ° C and a pressure range of 1 × 10 -3 Torr to 1 × 10 1 Torr for a range of 0.5 hours to 24 hours.
A method for producing a sourdough meal.
Wherein the mold comprises at least one member selected from the group consisting of a mold, a mold, a ceramic mold, and a graphite mold.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106521204A (en) * | 2016-12-16 | 2017-03-22 | 天津大学 | Preparation method of in-situ grown graphene reinforced metal-based composite material |
| CN109872831A (en) * | 2017-12-04 | 2019-06-11 | 北京市合众创能光电技术有限公司 | Compound silver paste of modified graphene and preparation method thereof |
| CN110423959A (en) * | 2019-08-01 | 2019-11-08 | 安徽科蓝特铝业有限公司 | A kind of aluminium base high-ductility composite material and preparation method thereof |
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| KR102220359B1 (en) | 2019-07-08 | 2021-02-25 | 부경대학교 산학협력단 | Method for manufacturing highly thermal conductive and electrically insulating metal-polymer composite material and said composite material manufactured thereby |
| KR20210037919A (en) | 2019-09-30 | 2021-04-07 | 주식회사 새롬테크 | The method of manufacturing copper added alloy tool steel |
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| EP1534451B1 (en) * | 2002-08-20 | 2007-02-14 | Ex One Corporation | Casting process |
| JP4059118B2 (en) * | 2003-03-24 | 2008-03-12 | Ｊｆｅスチール株式会社 | Method for producing Fe-Ni alloy cold rolled sheet material for shadow mask with excellent etching perforation |
| KR101505372B1 (en) * | 2014-07-15 | 2015-03-23 | 주식회사 대화알로이테크 | Cermet and method of manufacturing the same |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106521204A (en) * | 2016-12-16 | 2017-03-22 | 天津大学 | Preparation method of in-situ grown graphene reinforced metal-based composite material |
| CN106521204B (en) * | 2016-12-16 | 2018-07-06 | 天津大学 | A kind of preparation method of growth in situ graphene reinforced metal-matrix composite |
| CN109872831A (en) * | 2017-12-04 | 2019-06-11 | 北京市合众创能光电技术有限公司 | Compound silver paste of modified graphene and preparation method thereof |
| CN110423959A (en) * | 2019-08-01 | 2019-11-08 | 安徽科蓝特铝业有限公司 | A kind of aluminium base high-ductility composite material and preparation method thereof |
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