KR20190125798A - Manufacturing method of mold for high temperature casting and manufactured mold using the same - Google Patents

Abstract

The present invention relates to a manufacturing method of a high-temperature molding mold and a mold manufactured using the same. The manufacturing method of the high-temperature molding mold comprises: a step of molding a mold by processing a heat resistant alloy; a step of heat-treating the manufactured mold; and a step of forming a complex compound on a surface of the mold after the heat-treatment step. Disclosed is a method for manufacturing the mold for the high-temperature molding, which is useful for manufacturing a mold for high-temperature molding which is highly resistant to heat balance even at high temperatures and has a high strength, and can maintain moldability and durability in a process of repeating high-temperature heating and quenching operation.

Description

Method for manufacturing mold for high temperature molding and mold manufactured using the same {MANUFACTURING METHOD OF MOLD FOR HIGH TEMPERATURE CASTING AND MANUFACTURED MOLD USING THE SAME}

The present invention relates to a method for manufacturing a mold for high temperature molding and a mold manufactured using the same, and more particularly, to a method for manufacturing a mold for high temperature molding capable of maintaining excellent physical properties at a high temperature and a mold manufactured using the same. .

Representative examples of high temperature molds include die casting molds, extrusion molds, glass molds, thixo-moulding molds, injection-moulding molds, and squeeze casting molds. When looking at die casting molds and extrusion molds, tools such as SKD8 (AISI H19) and SKD61 (AISI H13), which are commonly used, or materials with high temperature hardness, such as 13Cr martensitic stainless steel (420J2), are mainly used. It was a level that satisfies heat resistance and high temperature strength up to about ℃. In the case where durability is required at temperatures higher than 600 ° C., ceramic layers such as TiN, TiCN, CrN, etc. were used in these molds by PVD coating several microns thick. If it is still not satisfied, after nitriding the mold, the ceramic layer was used by PVD coating again.

Recently, however, die casting and high-temperature extrusion of copper alloys with melting points above 900 ° C are frequently performed for the durability of automotive parts and portable electronic products. Therefore, it is difficult to satisfy the durability of mold required in the field by conventional methods. Is asking. It is also used for food molding, injection molding, and injection molding, in which powder or chip-shaped materials are pressure-molded at a solid and liquid coexistence zone temperature, and glass molding molds that blow or extrude glass. There is a need for a mold with improved heat resistance and high temperature strength. However, in the mold side, the temperature of the injection material is increased to more than 700 ℃ over 650 ℃ due to the lack of heat resistance heat crack (heat check) occurs and peeling of the surface ceramic layer occurs. This is because molten metal or liquid high temperature material is injected and rapid cooling by circulating the heat transfer of the mold or the refrigerant, and the surface contacting the injected material undergoes repeated thermal fatigue, which causes fine hair cracks.

In order to solve this problem, conventionally, instead of the mold material, titanium alloy UNS R56700, high temperature nickel alloy Inconel 718, X-750, 600, 625, 800, etc., or 18-18-2, 20Cb-3 Attempts have been made to use materials such as Nitrinic 50. However, they were excellent in oxidation resistance but were not satisfied with wear resistance and durability in mass production required by molds. In addition, Japanese Patent Application No. 62-328816 suppresses the formation of phosphorus compounds below P 0.010% in low alloy steels of 0.23 ~ 0.3% C (hereinafter, by weight%). Suggested. However, this was due to the formation of carbides having relatively low heat resistance, insufficient resistance to repeated thermal fatigue at high temperatures of 650 ° C. or higher, and was not effective in obtaining sufficient wear resistance. In a similar manner, Japanese Patent Application No. 6-307685 quenched a low alloy steel with 0.1 ~ 0.3% C and tempered it at 550 ~ 650 ℃ to reduce the hardness to HRC 26 ~ 35 and to increase toughness. Suggested. In this case, however, the maximum crack depth was deeper and durability was lower than that of the conventional SIKD61. Japanese Patent No. Hei 5-304154 introduced a nitriding die to improve heat resistance and plastic flow resistance. The nitride layer has a thickness of more than 0.7mm for a layer that is at least 10% harder than the core hardness, and has a hardness of HV750 or more at a depth of 0.2 mm, and a mold having a brittle nitride layer of the outermost surface formed at 5 microns or less is proposed. . However, even in this case, the resistance to thermal fatigue at a high temperature of 700 ° C. or higher has no significant effect. In addition, low-carbon maraging steels with reduced heat checks have been proposed to reduce the impact of carbides and to strengthen them by depositing nickel compounds. Japanese Patent Nos. Hei 6-32097 and Hei 6-54923 proposed maraging steel having high hardness and high heat resistance of HRC 50-54 by solution treatment and aging treatment of low carbon Ni-Co-Mo alloy. However, even in this case, the high temperature oxidation resistance was excellent, but the high temperature crack resistance was rather insufficient than that of the conventional SKD61, which was suitable for use below 500 ° C.

In addition, European patent application 99310240A (Priority US11356698P) adopts a method of adjusting the shape near the injection hole where the high temperature heat deformation of the mold is severe to diecast the melt at 1000 ° C. However, this measure does not solve the thermal cracking of the mold surface caused by the thermal fatigue of repeated high temperature heating and cooling. In addition, Japanese Patent Application No. P2015-110097 proposed a die casting mold in which a nitrogen compound layer and a lithium-iron composite oxide layer were formed on the surface of a mold in a nitride salt bath containing lithium salt. However, such a composite oxide layer has a weak disadvantage in repeated thermal fatigue due to a large difference in thermal expansion rate with the mold base material, and is not suitable in the case of requiring a precise and beautiful surface because it may lower the surface roughness of the molding.

International Publication No. WO2013-035351 proposes a die casting mold made of Co-Cr-Mo alloy, which forms a dense chromium oxide layer with a thickness of 300 to 400 microns on the surface by heating it at high temperature in the air to suppress surface damage caused by molten metal. to be. However, this is because materials containing elements that are highly reactive with oxygen, such as aluminum, titanium or zirconium, are prone to react with the mold, and there are many restrictions on the materials used.

It is an object of the present invention to provide a mold for high temperature molding, which is resistant to high temperature thermal cracking and has high temperature strength.

Another object of the present invention is to provide a mold for high temperature molding which can maintain moldability and durability in a high temperature heating and quenching operation.

In order to achieve the above object, the present invention comprises the steps of forming a mold by processing a heat-resistant alloy; And forming a complex compound on a surface of the mold.

In the method according to a preferred embodiment of the present invention, the heat-resistant alloy is _{AlCoCr (0.5 ~ 2) FeMo 0.5} Ni alloy; AlCoCrFeNbNi alloys; AlCoCrFeNiSi _(0.2-1.0) alloy; Al _(0.2-2.0) CoCrFeNiTi alloy; Al _0.2 Co _1.5 CrFeNi _1.5 Ti alloy; AlCoCrFeNiTi _{(0.5 ~ 1.5)} alloy; AlCoCrCuFeMo _(0.2-1.0) Ni alloy; Al _(0.3-0.5) CrFe _1.5 MnNi _0.5 alloy; CoCeFeMnNiV alloy; Cr ₂ CuFe ₂ MnNi alloys; 20-40% Ti, 10-40% W, and the balance of Nb and inevitable impurities; C 0.17 ~ 0.23%, Si 0.15 ~ 0.35%, Mn 0.4 ~ 0.6%, Cr 9.0 ~ 10.0%, Co 9.50 ~ 10.5%, Mo 1.8 ~ 2.2%, W 5.0 ~ 6.0%, Dissolved Al 0.01 ~ 0.015% and The rest are alloys composed of Fe and inevitable impurities; C 0.1% or less, Si 0.3 ~ 1.0%, Mn 0.3 ~ 1.0%, Cr 14-16%, Ni 6.5 ~ 8.5%, Mo 2-3%, Nb 0.45% or less, Acid dissolving Al 0.75 ~ 1.5%, N 0.01 -0.1%, and the remainder are alloys composed of Fe and inevitable impurities; And C 0.08 ~ 0.12%, Si 0.3 ~ 1.0%, Mn 0.3 ~ 1.0%, Cr 16 ~ 18%, Ni 6.0 ~ 7.5%, Ti 0.8 ~ 1.1%, Dissolved Al 0.9 ~ 1.2%, N 0.1 ~ 0.2% , And the rest may be any one selected from the alloy consisting of Fe and inevitable impurities.

In the manufacturing method according to a preferred embodiment of the present invention, the forming of the complex compound may be performed by subjecting the mold to at least one treatment selected from nitriding treatment, silicification treatment and boration treatment.

In the manufacturing method according to a preferred embodiment of the present invention, before the step of forming the composite compound, may further comprise the step of heat-treating the mold.

In a preferred embodiment, the heat treatment may be performed by a solution treatment at 1020 to 1250 ℃.

In this preferred embodiment after the solvation, the forming of the complex compound may be performed by a method of performing a boration treatment or a silicification treatment.

In a preferred embodiment of the present invention, the nitriding treatment may be performed at 1000 ~ 1900 ℃.

In a preferred embodiment of the present invention, the boration treatment or silicification treatment may be performed at 800 ~ 1200 ℃.

In another embodiment of the present invention provides a mold for high temperature molding manufactured by the method according to the above examples.

In a preferred embodiment of the present invention, the mold may have a surface hardness of 1200 HV or more.

It is useful for the production of high temperature molds having high strength and high resistance to thermal balance even at high temperatures according to the present invention.

In addition, it is possible to manufacture a mold for high temperature molding that can maintain moldability and durability in the operation of repeating high temperature heating and rapid cooling.

1 is a flowchart illustrating a method of manufacturing a mold for high temperature molding according to an embodiment of the present invention in order.
Figure 2 is an SEM image of the tissue of the high entropy alloy borated for 3 hours at 1000 ℃.
Figure 3 is an SEM image of the tissue of the high entropy alloy nitrided for 1150 ℃, 0.84 bar, 1.5 hours.

In the present invention, it was intended to identify a method for manufacturing a high temperature molding die having high resistance to thermal cracking even at high temperatures and applicable to various materials.

The present inventors pay attention to the fact that a mold for molding a material having a temperature higher than 700 ° C. is made of a material having higher thermal crack resistance and high temperature strength than a conventional mold material, and improving the surface durability thereof. Efforts have been made to find a treatment has led to the present invention.

In the present invention, for this purpose, after the mold is manufactured from a heat resistant alloy, a process of forming a complex compound on the surface of the mold is performed. As a result, it was confirmed that due to the formation of a composite compound decomposed at a high temperature of more than 2000 ℃ excellent surface hardness and resistance to thermal cracking.

That is, in one embodiment of the present invention it was confirmed that excellent resistance to thermal cracking even at high temperatures.

In the present invention, first, the mold is formed by processing the heat resistant alloy (S10). The heat-resistant alloy that is used is possible the high entropy alloys, high entropy alloys each element are source as adjusted composition dongyul or only some proportion to the ratio, _{(~ 0.5 2)} AlCoCr indicating HV300 or higher hardness at a high temperature FeMo _0.5 Ni Alloy, AlCoCrFeNbNi Alloy, AlCoCrFeNiSi _{(0.2 ~ 1.0)} Alloy, Al _{(0.2 ~ 2.0)} CoCrFeNiTi Alloy, Al _0.2 Co _1.5 CrFeNi _1.5 Ti Alloy, AlCoCrFeNiTi _{(0.5 ~ 1.5)} Alloy, AlCoCrCuFeMo _{(0.2 ~ 1.0)} Ni Alloy, Al _{( 0.3-0.5)} CrFe _1.5 MnNi _0.5 alloy, CoCeFeMnNiV alloy or Cr ₂ CuFe ₂ MnNi alloy may be one.

Specifically, the heat resistant alloy of the present invention includes C 0.17 to 0.23%, Si 0.15 to 0.35%, Mn 0.4 to 0.6%, Cr 9.0 to 10.0%, Co 9.50 to 10.5%, Mo 1.8 to 2.2%, and W 5.0 to 6.0% In addition, the acid dissolving Al may be an alloy containing 0.01 ~ 0.015% and the remainder is composed of Fe and inevitable impurities.

In addition, mold is 0.1% or less of C, 0.3 to 1.0% of Si, 0.3 to 1.0% of Mn, 14 to 16% of Cr, Ni 6.5 to 8.5%, Mo 2 to 3%, Nb 0.45% or less, acid soluble Al 0.75 to 1.5 %, N 0.01 ~ 0.1% and the rest may be an alloy composed of Fe and inevitable impurities.

 In addition, C 0.08 to 0.12%, Si 0.3 to 1.0%, Mn 0.3 to 1.0%, Cr 16 to 18%, Ni 6.0 to 7.5%, Ti 0.8 to 1.1%, acid soluble Al 0.9 to 1.2%, N 0.1 to 0.2 And the remainder may be an alloy composed of Fe and inevitable impurities.

 In addition, Ti 20-40%, W 10-40% remainder may be an alloy of the composition consisting of Nb and unavoidable impurities.

A complex compound is formed on the surface of the mold (S30). Specifically, the composite compound is at least one of a nitride layer, a boride layer or a silicide layer. Therefore, one or more of nitriding treatment, boration treatment, and silicide treatment may be selectively performed on the surface of the heat-treated mold.

The mold for high temperature molding in the present invention is a high entropy alloy, characterized in that the fine precipitate is present in the austenitic single-phase structure or austenitic matrix, the mold is one of a nitride layer, a boride layer and a silicide layer on the surface or It is to form a composite compound layer thereof to improve the hardness of the surface.

As described above, AlCoCr _(0.5-2) FeMo _0.5 Ni alloy, AlCoCrFeNbNi alloy, AlCoCrFeNiSi _(0.2-1.0) alloy, Al _(0.2-2.0) CoCrFeNiTi alloy, Al _0.2 Co _1.5 CrFeNi _1.5 Ti exhibiting hardness above HV300 at high temperature Alloy, AlCoCrFeNiTi _{(0.5 ~ 1.5)} Alloy, AlCoCrCuFeMo _{(0.2 ~ 1.0)} Ni Alloy, Al _{(0.3 ~ 0.5)} CrFe _1.5 MnNi _0.5 Alloy, CoCeFeMnNiV Alloy or Cr ₂ CuFe ₂ MnNi Alloy and Ti 20-40%, W 10 ~ The 40% remainder is nitridated, borated or silicified in a die made of an alloy of Nb and an unavoidable impurity, which has the highest melting point and highest solid solubility (e.g. Mo, Ti Etc.), a compound layer is formed, and a compound compound layer in which other elements are mixed is formed to form a mold having excellent wear resistance and heat resistance. The decomposition temperature of these compound layers is mostly 2000 ° C. or more, so that a mold having excellent wear resistance and heat resistance can be provided.

In the present invention, nitriding treatment may be preferably performed at 1000 ~ 1900 ℃.

In addition, the boration treatment and silicification treatment in the present invention is preferably carried out at 800 ~ 1200 ℃. Preferably it is 900-1050 degreeC. At this time, if it is performed below 900 ℃, the amount of boride or silicide combined with the elements in the heat-resistant alloy is small, which may not help to improve the surface hardness. If the temperature exceeds 1050 ℃, the surface by the formation of boride or silicide The amount of energy consumed compared to the ratio of hardness improvement can be inefficient.

On the other hand, depending on the steel species may be heat treatment before the step of forming a composite compound (S20). At this time, the heat treatment of the mold may be performed by a solution treatment at 1020 to 1250 ℃. In one embodiment of the present invention, quenching may be further performed after the solution treatment. In this case, if the solution treatment temperature is performed at 1000 ° C. or higher, an increase in ductility may be obtained due to an increase in residual austenite phase in the alloy. In addition, after the solution treatment, sub-zero treatment at -80 ° C. or less may be performed to prevent deformation and cracking while reducing residual austenite.

In an embodiment of the present invention, in the alloy subjected to the solution and quenching, forming the composite compound may include nitriding and TiN coating.

At this time, TiN coating is preferably performed by PVD (Physical Vapor Deposition) method.

On the other hand, the composite compound layer can be formed by performing boration treatment or silicidation treatment to the alloy which carried out the solution solution as mentioned above.

In the present invention, the high-temperature molding die manufactured through such a process has a high hardness of 1200 HV or more. In addition, the surface of the composite compound layer has a high temperature wear resistance and corrosion resistance at a decomposition temperature of more than 1800 ℃.

EXAMPLE

Hereinafter, the present invention will be described in more detail with reference to Examples. These examples are only for illustrating the present invention, and it will be apparent to those skilled in the art that the scope of the present invention is not to be construed as being limited by these examples.

Preparation of Examples 1-1 and 1-2

Example 1-1 is an AlCoCr ₂ FeMo _0.5 Ni alloy, and Example 1-2 is an Al _0.2 Co _1.5 CrFeNi _1.5 Ti alloy. The alloy compositions of Examples 1-1 and 1-2 are shown in Table 1 below and may contain trace amounts of unavoidable impurities. Within the range of approximately 10% in the composition of each element of these alloys, an allowable range in which equivalent physical properties can be obtained.

Al Co Cr Fe  Mo Ni Ti  Example 1-1 (wt%) 7.7 16.7 29.5 15.8 13.6 16.7 -  Example 1-2 (wt%) 1.6 26.1 15.4 16.5 - 26.2 14.2

When the alloy having the composition shown in Table 1 is subjected to nitriding treatment, silicification treatment or boration treatment, a compound layer is formed around the element having the highest melting point and the highest solid solubility (for example, Mo, Ti, Cr, etc.). It will form a composite boride layer mixed with other elements. The decomposition temperature of these compound layers is 1800 degreeC or more mostly, and the metal mold | die excellent in abrasion resistance and heat resistance can be obtained.

 In the present invention, the hardness of the mold before forming the composite compound is about HV700 ~ 900, but the surface hardness is improved to HV1200 or more by nitriding, silicifying or boring treatment at 900 ~ 1100 ℃. Thus, at the outermost surface of the nitrided or borated compound layer, not only the hardness of HV1200 or more is obtained, but the surface of the compound layer has high temperature abrasion resistance and corrosion resistance at a decomposition temperature of 1800 ° C or more, and thus shows excellent life in high temperature forming operations.

As an example, the SEM image of the tissue of the high entropy alloy borated for 3 hours at 1000 ℃ is shown in FIG.

In another embodiment, the SEM image of the tissue of the high entropy alloy nitrided at 1150 ° C., 0.84 bar and 1.5 hours is shown in FIG. 2.

<Example 2>

Ti 30%, W 20% The remainder of the alloy consisting of Nb and inevitable impurities was subjected to nitriding 4h at 1875 ℃. After the nitriding treatment, a composite nitride layer was obtained from the surface to about 1.6 mm in depth, and a titanium nitride layer of about 0.25 mm was formed on the outermost layer. The core hardness of mold material was about HV220 ~ 500, but after nitriding, it was over HV2000. In the case of boration, HV1700-1800 was obtained at the surface of HV2000 or more and 75 micrometers depth, and the decomposition temperature of these nitrides was about 2000 degreeC or more. Therefore, this mold had the durability enough to be used for shaping | molding a material which is about 1000 degreeC or more high temperature.

<Example 3>

C 0.17 ~ 0.23%, Si 0.15 ~ 0.35%, Mn 0.4 ~ 0.6%, Cr 9.0 ~ 10.0%, Co 9.50 ~ 10.5%, Mo 1.8 ~ 2.2%, W 5.0 ~ 6.0%, Acid Dissolve Al 0.01 ~ 0.015% The rest was quenched by air cooling or oil cooling after maintaining the hot forged material as a hot pore made of Fe and unavoidable impurities. Then, after boring for 3 hours at 980 ℃ surface hardness was measured and showed a surface hardness of HV1200 or more.

<Example 4>

C 0.1% or less, Si 0.3 ~ 1.0%, Mn 0.3 ~ 1.0%, Cr 14-16%, Ni 6.5 ~ 8.5%, Mo 2-3%, Nb 0.45% or less, Acid dissolving Al 0.75 ~ 1.5%, N 0.01 It contains ~ 0.1%, and the remainder is an alloy composed of Fe and unavoidable impurities. The solution treatment temperature is higher than 1038 ℃ increases the ductility due to the increase of residual austenite. Subzero treatment below -80 ° C after solution treatment reduces residual austenite and prevents deformation and cracking.

After the solution treatment, the structure of the mold is martensitic matrix structure and after boride treatment, it is a structure reinforced with Ni- (Cr, Mo) precipitate on martensite. After the solution treatment, the surface hardness was measured by boring at 1050 ° C. for 3 hours to obtain a hardness value of HV1200 or more.

Example 5

C 0.08 ~ 0.12%, Si 0.3 ~ 1.0%, Mn 0.3 ~ 1.0%, Cr 16 ~ 18%, Ni 6.0 ~ 7.5%, Ti 0.8 ~ 1.1%, acid soluble Al 0.9 ~ 1.2%, N 0.1 ~ 0.2% The remainder is an alloy composed of Fe and unavoidable impurities, and the forging is heated at 1025 to 1050 ° C. for 15 minutes. At this time, Cr carbide is dissolved in austenite and 10% delta-ferrite and Ti carbide are distributed. After solution treatment the martensite and retained austenite tissues have a hardness of HRC 25. The higher the carbon content, the higher the solution temperature and the lower the start of martensite transformation (Ms). Therefore, subzero treatment below -80 ° C reduces residual austenite and prevents deformation and cracking.

In the case of solution treatment at 980 ° C. or lower, the Ti carbide solid solubility becomes low, so that the hardness decreases due to the increase of residual austenite. After solution treatment and boride treatment at 1000 ° C. for 3 hours, the surface hardness was measured, and the surface hardness of HV1200 was higher.

As confirmed in the above embodiments, the mold for high temperature molding manufactured by the method of the present invention exhibited a hardness value of 1200 HV or more after manufacturing, and thus, it was confirmed that the mold was manufactured with high thermal cracking resistance at high temperature. Therefore, the high temperature molding mold manufactured by the present invention has higher heat resistance and higher wear resistance than the conventional mold, and is suitable for use at high temperature, and is suitable for high temperature die casting or extrusion mold, food molding, injection molding, and squeeze with long life and durability. It can be used as a mold for high temperature property such as casting or glass molding, especially for applications requiring high resistance to thermal fatigue which repeats high temperature heating and rapid cooling.

As described above in detail specific parts of the present invention, it will be apparent to those skilled in the art that these specific descriptions are merely preferred embodiments, and thus the scope of the present invention is not limited thereto. will be. Thus, the substantial scope of the present invention will be defined by the appended claims and their equivalents.

Claims (10)

Molding a mold by processing the heat resistant alloy; And
Forming a complex compound on the surface of the mold; comprising,
Manufacturing method of high temperature molding die. The method according to claim 1,
The heat resistant alloy is AlCoCr _{(0.5 ~ 2)} FeMo _0.5 Ni alloy; AlCoCrFeNbNi alloys; AlCoCrFeNiSi _(0.2-1.0) alloy; Al _(0.2-2.0) CoCrFeNiTi alloy; Al _0.2 Co _1.5 CrFeNi _1.5 Ti alloy; AlCoCrFeNiTi _(0.5-1.5) alloy; AlCoCrCuFeMo _{(0.2 ~ 1.0)} Ni alloy; Al _(0.3-0.5) CrFe _1.5 MnNi _0.5 alloy; CoCeFeMnNiV alloy; Cr ₂ CuFe ₂ MnNi alloys; 20-40% Ti, 10-40% W, and the balance of Nb and inevitable impurities; C 0.17 ~ 0.23%, Si 0.15 ~ 0.35%, Mn 0.4 ~ 0.6%, Cr 9.0 ~ 10.0%, Co 9.50 ~ 10.5%, Mo 1.8 ~ 2.2%, W 5.0 ~ 6.0%, Dissolved Al 0.01 ~ 0.015% and The rest are alloys composed of Fe and inevitable impurities; C 0.1% or less, Si 0.3 ~ 1.0%, Mn 0.3 ~ 1.0%, Cr 14-16%, Ni 6.5 ~ 8.5%, Mo 2-3%, Nb 0.45% or less, Acid dissolving Al 0.75 ~ 1.5%, N 0.01 -0.1%, and the remainder are alloys composed of Fe and inevitable impurities; And C 0.08 ~ 0.12%, Si 0.3 ~ 1.0%, Mn 0.3 ~ 1.0%, Cr 16 ~ 18%, Ni 6.0 ~ 7.5%, Ti 0.8 ~ 1.1%, Dissolved Al 0.9 ~ 1.2%, N 0.1 ~ 0.2% And, the rest is characterized in that any one selected from the alloy consisting of Fe and inevitable impurities,
Manufacturing method of high temperature mold. The method according to claim 1,
Forming the complex compound, characterized in that the mold is carried out by performing at least one treatment selected from nitriding treatment, silicification treatment and boration treatment
Manufacturing method of high temperature mold. The method according to claim 1 or 3,
Before the forming of the composite compound, characterized in that it comprises the step of heat-treating the mold,
Manufacturing method of high temperature mold. The method according to claim 4,
The heat treatment is characterized in that it is carried out by a solution treatment method at 1020 to 1250 ℃,
Manufacturing method of high temperature mold. The method according to claim 5,
Forming the complex compound is characterized in that it is carried out by a method of performing a boration treatment or silicidation treatment,
Manufacturing method of high temperature mold. The method according to claim 3,
The nitriding treatment is characterized in that performed at 1000 ~ 1900 ℃,
Manufacturing method of high temperature mold. The method according to claim 3 or 6,
The boration treatment or silicification treatment is characterized in that carried out at 800 ~ 1200 ℃,
Manufacturing method of high temperature mold. A mold for high temperature molding, prepared by the method of claim 1. The method according to claim 9,
The mold is characterized in that the surface hardness of 1200HV or more,
High temperature molding mold.

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