WO2012115025A1 - Manufacturing method for cold-working die - Google Patents
Manufacturing method for cold-working die Download PDFInfo
- Publication number
- WO2012115025A1 WO2012115025A1 PCT/JP2012/053929 JP2012053929W WO2012115025A1 WO 2012115025 A1 WO2012115025 A1 WO 2012115025A1 JP 2012053929 W JP2012053929 W JP 2012053929W WO 2012115025 A1 WO2012115025 A1 WO 2012115025A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- cold
- cutting
- hardness
- less
- steel
- Prior art date
Links
Images
Classifications
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
Definitions
- the present invention relates to a method for manufacturing a cold working mold for molding, for example, home appliances, mobile phones, and automobile-related parts.
- thermoforming In a cold working die used for press forming such as bending, drawing, and punching of a plate material at room temperature, in order to improve its wear resistance, it is 55 HRC or higher by quenching and tempering (hereinafter referred to as “tempering”). Steel materials that can achieve hardness have been proposed (Patent Documents 1 to 3). When such a high hardness steel material is used, it is difficult to cut into a mold shape after tempering. Therefore, normally, after carrying out rough processing in the annealing state with low hardness after hot-working a steel ingot, it tempers to use hardness of 55HRC or more.
- an oxide ((FeO) 2 ⁇ SiO 2 , Fe 2 SiO 4 or (FeSi) having a melting point of 1200 ° C. or lower is used to suppress tool wear caused by friction between the cutting tool and the steel material during cutting.
- a cold tool steel in which self-lubricating properties are imparted by adding an element that forms a) Cr 2 O 2 and forming the oxide on the mold surface by heat generated during cutting.
- the cold tool steel disclosed in Patent Document 4 is an excellent prehardened steel that achieves both machinability during cutting and wear resistance as a mold.
- the quenching temperature is also limited, so this can be obtained when the tempered hardness is 60 HRC or higher.
- Nb and V which are preferably added in Patent Document 4 for the purpose of suppressing crystal grain growth during quenching heating, are elements that easily form insoluble MC carbide at the quenching temperature. It is. Since MC carbide is hard, the component composition disclosed in Patent Document 4 has a problem that the machinability after tempering is significantly reduced.
- the cold tool steel disclosed in Patent Document 5 uses a low melting point oxide as a self-lubricating film, but if the cutting temperature does not increase to the melting point of the oxide, the lubricating effect cannot be obtained. On the contrary, when the cutting temperature is excessively increased, the viscosity of the oxide is remarkably lowered, and there is a problem that the function as the lubricating film may not be performed.
- the object of the present invention is based on a component composition that can stably achieve a high tempering hardness of 60 HRC or more as well as 58 HRC or more, and preferably even if the amount of insoluble carbide is further increased, cutting is performed.
- a method of manufacturing a cold working die that cuts cold work tool steel with remarkably improved machinability after tempering at a temper hardness of 58 to 62 HRC without depending on temperature. That is.
- the inventor has intensively studied a method for improving the machinability of cold tool steel.
- Al 2 O 3 which is a high melting point oxide is positively introduced, and a composite lubricating protective film composed of this and MnS which is a highly ductile inclusion is formed on the surface of the cutting tool by heat during cutting.
- the steel material which can achieve the refining hardness of 60HRC or more as well as 58HRC or more and can form this composite lubricating protective film has an optimum component range, and this could be specified.
- the present invention has been reached.
- the present invention is mass%, C: 0.6 to 1.2% Si: 0.8 to 2.5%, Mn: 0.4 to 2.0%, S: 0.03-0.1%, Cr: 5.0 to 9.0%, Mo and W are used alone or in combination (Mo + 1 / 2W): 0.5 to 2.0%, Al: 0.04 to less than 0.3%,
- the steel ingot of the cold tool steel composed of the remaining Fe and inevitable impurities is hot-worked into a raw material, and the material is quenched and tempered to adjust the hardness to 58 to 62 HRC, and then cut.
- a method for manufacturing a cold working mold wherein the mold is finished in the shape of a mold.
- a method of manufacturing a cold working mold in which a material subjected to hot working is annealed and then quenched and tempered.
- quenching is a method for manufacturing a cold working mold, which is direct quenching performed in the cooling process after the hot working.
- the hardness after tempering is 60 HRC or more.
- the cold tool steel according to the present invention may contain 1.0% or less of Ni, or 1.0% or less of Cu.
- cold tool steel according to the present invention may further contain 1.0% or less of V, or further 0.5% or less of Nb.
- the hardness is adjusted to a hardness of 60 HRC or more as well as 58 HRC or more, and the amount of undissolved carbide is further increased. Even if an alloy design with a large amount of steel is used, it is possible to obtain a cold work tool steel that greatly improves the machinability after tempering without depending on the cutting temperature. Therefore, it is possible to freely select the tempered hardness of the cold tool steel and the amount of undissolved carbide according to various functions.
- this cold tool steel is tempered to a hardness of 58 to 62 HRC and then machined, the problems related to heat treatment deformation and refinishing can be solved, and the mold can be manufactured.
- this is an indispensable technique for the practical application of a cold working die using pre-hardened cold tool steel.
- Sample No. which is an example of the present invention. 3 is a digital microscope photograph showing the rake face and flank face of the cutting tool used in the cutting process of No. 3.
- the upper side of the drawing shows the rake face, and the lower side of the drawing shows the flank face.
- Sample No. which is an example of the present invention. 5 is a digital microscope photograph showing a rake face and a flank face of a cutting tool used in the cutting process of No. 5.
- the upper side of the drawing shows the rake face, and the lower side of the drawing shows the flank face.
- the upper side of the drawing shows the rake face, and the lower side of the drawing shows the flank face.
- Sample No. which is a comparative example. 22 is a digital microscope photograph showing a rake face and a flank face of a cutting tool used for 22 cutting operations. The upper side of the drawing shows the rake face, and the lower side of the drawing shows the flank face. Sample No. which is a comparative example. A digital microscope photograph showing the rake face and flank face of a cutting tool used for 30 cutting operations. The upper side of the drawing shows the rake face, and the lower side of the drawing shows the flank face. When deposits formed on the surface of the cutting tool in FIG. 1A (Sample No.
- FIG. 3 It is a map figure of Al, O, Mn, and S when the deposit formed on the surface of the cutting tool of Drawing 1B (sample No. 5) is analyzed by EPMA (electron beam microanalyzer), respectively. It is a map figure of Al, O, Mn, and S when the deposit formed on the surface of the cutting tool of Drawing 1C (sample No. 15) is analyzed by EPMA (electron beam microanalyzer), respectively.
- the feature of the present invention is that the machinability after tempering depends on the cutting temperature even when a large amount of undissolved carbide is formed to improve the temper hardness and control the crystal grain size.
- a good cold tool steel is realized, and the tempered cold tool steel is being cut.
- Al 2 O 3 which is a high melting point oxide and high ductility interposition are used. It is to temper cold tool steel, which is a component design of a steel material, before cutting, so that a composite lubricating protective film of MnS, which is a product, is formed on the surface of the cutting tool.
- the present inventor examined machinability improving means that can widely correspond to the component composition of cold tool steel. As a result, we focused on the effectiveness of self-lubrication. And when self-lubricating action effect using a low melting point oxide like patent document 5 was examined, it discovered that this had the subject depending on cutting temperature.
- the low melting point oxide having self-lubricating properties is a composite oxide containing Fe and Cr that are generally contained in a large amount in a steel material. It fluctuates greatly and a stable lubricating effect cannot be obtained.
- the steel material which can achieve the refining hardness of 60HRC or more as well as 58HRC or more and can form this composite lubricating protective film has an optimum component range, and this could be specified.
- the present invention has been reached.
- the component composition of the cold tool steel according to the production method of the present invention will be described.
- C 0.6 to 1.2% by mass (hereinafter simply expressed as%)
- C is an important element that forms carbides in the steel and imparts hardness to the cold tool steel. If the amount of C is too small, the amount of carbide formed is insufficient, and it is difficult to impart a hardness of 58 HRC or more, preferably 60 HRC or more. On the other hand, if the content is excessive, the toughness tends to decrease due to an increase in the amount of undissolved carbide when quenched. Therefore, the C content is set to 0.6 to 1.2%. Preferably they are 0.7% or more and / or 1.1% or less. 1.0% or less is more preferable.
- Si 0.8-2.5%
- Si is an important element that dissolves in steel and imparts hardness to cold tool steel.
- Fe and Cr it is an element that easily forms a corundum-based oxide with Al 2 O 3.
- Si is set to 0.8 to 2.5%.
- they are 1.0% or more and / or 2.0% or less. 1.2% or more is more preferable.
- Mn is an important element of the present invention, and acts as a good lubricating film on the Al 2 O 3 protective film formed on the cutting tool surface. And it is an austenite formation element, and it dissolves in steel and improves hardenability. However, if the added amount is too large, a large amount of retained austenite remains after tempering, which causes aging changes during use as a mold. Further, since the easily form a Fe and Cr and a low melting oxide, is a factor that inhibits the function of the Al 2 O 3 protective coating. Therefore, in the present invention, it was set to 0.4 to 2.0%. Preferably they are 0.6% or more and / or 1.5% or less.
- S is an important element of the present invention, and acts as a good lubricating film on the Al 2 O 3 protective film formed on the cutting tool surface. That is, a sufficient amount of S contained in the steel material forms MnS. Then, MnS is added to ductile, for compatibility with Al 2 O 3 is good, deposited on Al 2 O 3 protective coating serves these as a good composite lubricating protective coating. Addition of 0.03% or more is necessary in order to sufficiently exhibit such a lubricating action, but since S deteriorates the toughness of steel, the upper limit is made 0.1%. Preferably it is 0.04% or more and / or 0.08% or less.
- ⁇ Cr 5.0-9.0% Cr imparts hardness to the cold tool steel by forming M 7 C 3 carbide in the tempered structure.
- a part of the material is present as insoluble carbide during quenching heating, and has an effect of suppressing the growth of crystal grains.
- Cr 5.0% or more the amount of carbide
- the ability to form a VC film by a TD process or a TiC film by a CVD process is improved.
- Cr is an element effective in securing corrosion resistance.
- Cr which is a main component of cold tool steel, tends to form a low melting point oxide. That is, when Cr is excessively contained, it becomes a factor that inhibits the function of the Al 2 O 3 protective film. As a result, this becomes a factor that hinders the function of the composite lubricating protective film composed of Al 2 O 3 and MnS, which is a feature of the present invention. Therefore, it is important to adjust Cr after containing a sufficient amount of Al described later. And the function of said composite lubricating protective film is exhibited by adjusting S amount corresponding to this. For this reason, it is important that the Cr content is 5.0 to 9.0%. Preferably it is 6.0% or more, More preferably, it is 7.0% or more.
- Mo and W are single or composite (Mo + 1 / 2W): 0.5 to 2.0% Mo and W are elements that improve the hardness by precipitation strengthening (secondary hardening) of fine carbides during tempering during tempering. However, at the same time, since the decomposition of residual austenite that occurs during tempering is delayed, when it is excessively contained, residual austenite tends to remain in the tempered structure. Further, since Mo and W are expensive elements, the amount of addition should be reduced as much as possible for practical use. Therefore, the addition amount of these elements is 0.5 to 2.0% in the relational expression of (Mo + 1 / 2W).
- Al 0.04 to less than 0.3%
- Al is an important element of the present invention. That is, a sufficient amount of Al contained in the steel material forms Al 2 O 3 , which is a high melting point oxide, on the cutting tool surface by heat generated during the cutting process. Since the melting point of Al 2 O 3 is about 2050 ° C., which is much higher than the cutting temperature, Al 2 O 3 functions as a protective film for the cutting tool. And by containing 0.04% or more, the protective film of sufficient thickness is formed and a tool life improves. However, when a large amount of Al is added, since much Al 2 O 3 is formed as inclusions in the steel material, the machinability of the steel material is lowered. For this reason, the upper limit of the amount of Al added is less than 0.3%. Preferably they are 0.05% or more and / or 0.15% or less.
- Ni 1.0% or less
- Ni is an element which improves the toughness and weldability of steel.
- tempering during tempering precipitates as Ni 3 Al and has the effect of increasing the hardness of the steel, it is effective to add it according to the amount of Al contained in the cold tool steel according to the present invention.
- Ni is an expensive metal, and the amount to be added should be reduced as much as possible for practical use. Therefore, Ni in the present invention is preferably 1.0% or less even when added.
- Cu 1.0% or less
- Cu precipitates as (epsilon) -Cu in the tempering at the time of tempering, and has the effect of raising the hardness of steel.
- Cu is an element that causes hot brittleness of a steel material. Accordingly, Cu in the present invention is preferably 1.0% or less even when added.
- hot brittleness due to Cu can be suppressed by adding substantially the same amount of Ni, when the cold tool steel according to the present invention contains Ni, the regulation value can be relaxed according to the amount. it can.
- V 1.0% or less
- V has the effect of forming various carbides and increasing the hardness of the steel.
- the formed insoluble MC carbide has an effect of suppressing the growth of crystal grains.
- Nb which will be described later
- the MC carbide that has not been dissolved yet during quenching heating becomes fine and uniform, and has the function of effectively suppressing crystal grain growth.
- MC carbide is hard and causes a decrease in machinability. Therefore, in the present invention, the above-described composite lubricating protective film is formed on the tool surface at the time of cutting, which is important in that good machinability can be ensured even if many MC carbides are formed in the steel material. Has characteristics.
- excessive V addition excessively forms coarse MC carbides and also reduces the toughness of the cold tool steel. Therefore, V is preferably 1.0% or less even when added. More preferably, it is 0.7% or less.
- Nb 0.5% or less
- Nb has the function which forms MC carbide
- the content is preferably 0.5% or less. More preferably, it is 0.3% or less.
- the present invention is characterized in that the cold work tool steel having the above composition is tempered to a hardness of 58 to 62 HRC and then cut.
- the cold tool steel according to the present invention can stably obtain a tempered hardness of 58 HRC or higher by quenching and tempering. A hardness of 60 HRC or higher can also be achieved. And since it has excellent machinability in this high hardness state, it is not necessary to perform quenching and tempering after cutting in an annealed state. Alternatively, since it is not necessary to go through the annealing state itself, direct quenching using a cooling process after hot working the steel ingot can be applied to quenching.
- the machinability improvement effect similar to the case where the hardening after annealing is applied can be acquired. Therefore, by using the cold tool steel according to the present invention as pre-hardened steel, heat treatment deformation due to tempering is excluded, and finishing cutting and further annealing steps related to material production are omitted. Can do.
- the upper limit of the refining hardness is set to 62 HRC in order to sufficiently maintain mechanical properties other than the hardness of the cold tool steel and to perform the cutting process stably.
- die which consists of the manufacturing method of the metal mold
- the material was melted using a high frequency induction melting furnace to produce a steel ingot having the chemical components shown in Table 1. Next, hot forging was performed on these so that the forging ratio was about 10, and after cooling, annealing was performed at 860 ° C. A test for evaluating the machinability of these annealed materials after quenching by air cooling from 1030 ° C. and then tempering to a target hardness of 60 HRC by tempering twice at 500 to 540 ° C. A piece was made.
- the machinability test was carried out by plane cutting using an insert PICOmini manufactured by Hitachi Tool Co., Ltd. as a cutting edge replaceable tool corresponding to cutting of a hard material.
- the insert is made of cemented carbide as a base material and TiN coating is applied to the surface.
- Cutting conditions were a cutting speed of 70 m / min, a rotation speed of 1857 / min, a feed speed of 743 mm / min, a feed amount per blade of 0.4 mm / blade, a cutting depth of 0.15 mm, a cutting width of 6 mm, and a blade count of 1. .
- the machinability was evaluated based on the following two points. First, the formation amount of the composite lubricating protective film composed of Al 2 O 3 and MnS on the cutting tool surface was evaluated. This amount of formation was analyzed using EPMA from the rake face side at a cutting distance of 0.8 m immediately after the start of cutting, and was used as the average count number of Al and S at this time. Then, the cutting distance was extended to 8 m, and the amount of tool wear at this time was measured using an optical microscope. These evaluation results are shown in Table 2.
- a composite lubricating protective film is formed on the surface of the cutting tool, and tool wear is suppressed. And even when Nb and V which form insoluble carbides are added, good machinability is maintained. On the other hand, the cutting of cold tool steel that does not satisfy the present invention has a larger amount of tool wear than the present invention.
- FIGS. 2A to 2E are digital microscope photographs showing the flank and rake face of the cutting tool used in 3, 5, 15, 22, and 30, and FIGS. 2A to 2E show EPMA of the deposit formed on the surface of FIGS. (The high concentration part of each element is shown in white).
- Table 2 sample Nos. With high average counts of Al and S were obtained. 3, 5 and 15, it was also confirmed in the EPMA analysis of FIGS. 2A to 2C that a large amount of Al and S was adhered over a wide range of the tool. In comparison with this, sample No. Sample No. 22 The average count numbers of Al and S were lower than 3, 5, and 15, and the adhesion range of Al and S was narrow.
- sample No. 1 with a low Al and S content in the steel. No. 30 also had a low average count of these elements, and Al and S were hardly detected by EPMA analysis (most of the Fe and Cr that seemed to be transferred from the test piece were detected).
- FIGS. 1A to 1C showing the wear state of the cutting tool
- sample No It can be seen that deposits are remarkably adhered to the 3, 5 and 15 tool rake faces, and that tool wear is suppressed on both the flank face and the rake face. Moreover, tool wear is progressing uniformly and stably.
- sample no. The tool wear amount of No. 22 is the sample No. The tool was close to 3 times, and chipping occurred in the tool. And sample no. The tool surface of 30 is also sample No. Like 22 the damage was severe.
- FIGS. It is the cross-sectional TEM image which showed the deposit confirmed by the tool surface in 3, 22, and 30 with the TiN coating under it.
- reference numeral 1 is a protective film for sample preparation
- 2 is a deposit on cutting
- 3 is a TiN plastic deformation region
- 4 is a TiN undeformed region.
- the sample Nos. The deposit of No. 3 is thicker, and as the count number decreases, the sample No. 3 increases. In 22, the deposit was thinly transferred. Sample No. At 30, almost no deposits were observed. And sample no. Like sample 3, sample no. Al 2 O 3 and MnS were also attached to the surface of the tool No. 22, but the thickness was thin and chipping occurred as described above.
- Sample No. 3 exhibits a high lubrication protection function because the TiN coating on the tool surface, which is usually plastically deformed by frictional stress during cutting, has a thick deposit. 3 is suppressed (the plastic deformation region is the narrowest).
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
C:0.6~1.2%、
Si:0.8~2.5%、
Mn:0.4~2.0%、
S:0.03~0.1%、
Cr:5.0~9.0%、
MoおよびWは単独または複合で(Mo+1/2W):0.5~2.0%、
Al:0.04~0.3%未満、
残部Feおよび不可避的不純物からなる冷間工具鋼の鋼塊に熱間加工を行って素材とし、該素材に焼入れ焼戻しを行って硬さを58~62HRCに調質した後に、切削加工を行って金型の形状に仕上げることを特徴とする冷間加工用金型の製造方法である。一具体例としては、熱間加工を行った素材に、焼鈍を行った後、焼入れ焼戻しを行う冷間加工用金型の製造方法である。そして、別の一具体例としては、焼入れは、前記熱間加工後の冷却過程で行う直接焼入れである冷間加工用金型の製造方法である。好ましくは、調質後の硬さが60HRC以上である。 That is, the present invention is mass%,
C: 0.6 to 1.2%
Si: 0.8 to 2.5%,
Mn: 0.4 to 2.0%,
S: 0.03-0.1%,
Cr: 5.0 to 9.0%,
Mo and W are used alone or in combination (Mo + 1 / 2W): 0.5 to 2.0%,
Al: 0.04 to less than 0.3%,
The steel ingot of the cold tool steel composed of the remaining Fe and inevitable impurities is hot-worked into a raw material, and the material is quenched and tempered to adjust the hardness to 58 to 62 HRC, and then cut. A method for manufacturing a cold working mold, wherein the mold is finished in the shape of a mold. As a specific example, there is a method of manufacturing a cold working mold in which a material subjected to hot working is annealed and then quenched and tempered. As another specific example, quenching is a method for manufacturing a cold working mold, which is direct quenching performed in the cooling process after the hot working. Preferably, the hardness after tempering is 60 HRC or more.
Cは、鋼中で炭化物を形成し、冷間工具鋼に硬さを付与する重要な元素である。Cが少なすぎると形成される炭化物量が不足し、58HRC以上、好ましくは60HRC以上の硬さを付与することが困難である。一方、過多の含有は、焼入れしたときの未固溶炭化物量の増加により靱性が低下しやすい。よって、Cの含有量は0.6~1.2%とした。好ましくは0.7%以上および/または1.1%以下である。1.0%以下がさらに好ましい。 C: 0.6 to 1.2% by mass (hereinafter simply expressed as%)
C is an important element that forms carbides in the steel and imparts hardness to the cold tool steel. If the amount of C is too small, the amount of carbide formed is insufficient, and it is difficult to impart a hardness of 58 HRC or more, preferably 60 HRC or more. On the other hand, if the content is excessive, the toughness tends to decrease due to an increase in the amount of undissolved carbide when quenched. Therefore, the C content is set to 0.6 to 1.2%. Preferably they are 0.7% or more and / or 1.1% or less. 1.0% or less is more preferable.
Siは、鋼中に固溶して、冷間工具鋼に硬さを付与する重要な元素である。また、FeやCrよりも酸化傾向が強いことに加えて、Al2O3とコランダム系の酸化物を形成しやすい元素であるため、本発明では酸化物を低融点化するFe系酸化物やCr系酸化物の形成を抑制し、Al2O3保護皮膜の形成を促進する重要な作用がある。しかし、多すぎると焼入れ性や靱性が著しく低下する。よって、Siは0.8~2.5%とした。好ましくは1.0%以上および/または2.0%以下である。1.2%以上がさらに好ましい。 ・ Si: 0.8-2.5%
Si is an important element that dissolves in steel and imparts hardness to cold tool steel. In addition to being stronger in oxidation tendency than Fe and Cr, it is an element that easily forms a corundum-based oxide with Al 2 O 3. There is an important effect of suppressing the formation of Cr-based oxides and promoting the formation of an Al 2 O 3 protective film. However, if it is too much, hardenability and toughness are significantly reduced. Therefore, Si is set to 0.8 to 2.5%. Preferably they are 1.0% or more and / or 2.0% or less. 1.2% or more is more preferable.
Mnは、本発明の重要な元素であり、切削工具表面に形成されたAl2O3保護皮膜上で良好な潤滑皮膜として作用する。そして、オーステナイト形成元素であり、鋼中に固溶して焼入れ性を向上する。しかし、添加量が多すぎると調質後に残留オーステナイトが多く残り、金型として使用時の経年変寸の原因となる。また、FeやCrと低融点酸化物を形成しやすいため、Al2O3保護皮膜の機能を阻害する要因となる。よって、本発明では0.4~2.0%とした。好ましくは0.6%以上および/または1.5%以下である。 ・ Mn: 0.4-2.0%
Mn is an important element of the present invention, and acts as a good lubricating film on the Al 2 O 3 protective film formed on the cutting tool surface. And it is an austenite formation element, and it dissolves in steel and improves hardenability. However, if the added amount is too large, a large amount of retained austenite remains after tempering, which causes aging changes during use as a mold. Further, since the easily form a Fe and Cr and a low melting oxide, is a factor that inhibits the function of the Al 2 O 3 protective coating. Therefore, in the present invention, it was set to 0.4 to 2.0%. Preferably they are 0.6% or more and / or 1.5% or less.
Sは、本発明の重要な元素であり、切削工具表面に形成されたAl2O3保護皮膜上で良好な潤滑皮膜として作用する。つまり、鋼素材中に含まれる十分量のSは、MnSを形成する。そして、MnSは延性に富むことに加え、Al2O3との馴染みが良いため、Al2O3保護皮膜上に堆積して、これらが良好な複合潤滑保護皮膜としての役割を果たす。このような潤滑作用が十分に発揮されるためには0.03%以上の添加が必要であるが、Sは鋼の靱性を劣化させるため、上限は0.1%とする。好ましくは0.04%以上および/または0.08%以下である。 ・ S: 0.03-0.1%
S is an important element of the present invention, and acts as a good lubricating film on the Al 2 O 3 protective film formed on the cutting tool surface. That is, a sufficient amount of S contained in the steel material forms MnS. Then, MnS is added to ductile, for compatibility with Al 2 O 3 is good, deposited on Al 2 O 3 protective coating serves these as a good composite lubricating protective coating. Addition of 0.03% or more is necessary in order to sufficiently exhibit such a lubricating action, but since S deteriorates the toughness of steel, the upper limit is made 0.1%. Preferably it is 0.04% or more and / or 0.08% or less.
Crは、調質後の組織中にM7C3炭化物を形成することで、冷間工具鋼に硬さを付与する。また、焼入加熱時に一部は未固溶炭化物として存在して、結晶粒の成長を抑制する効果がある。そして、Crを5.0%以上とすることで、形成される炭化物量が多くなり、58HRC以上、好ましくは60HRC以上の硬さを十分に達成することができる。さらに、冷間加工用金型としたときの表面には、各種の被覆処理を行う場合、TD処理によるVC皮膜やCVD処理によるTiC皮膜の形成能が向上する。また、Crは耐食性を確保する上で有効な元素である。 ・ Cr: 5.0-9.0%
Cr imparts hardness to the cold tool steel by forming M 7 C 3 carbide in the tempered structure. In addition, a part of the material is present as insoluble carbide during quenching heating, and has an effect of suppressing the growth of crystal grains. And by making Cr 5.0% or more, the amount of carbide | carbonized_material formed increases and the hardness of 58 HRC or more, Preferably 60 HRC or more can fully be achieved. Furthermore, when various coating processes are performed on the surface of the cold working mold, the ability to form a VC film by a TD process or a TiC film by a CVD process is improved. Cr is an element effective in securing corrosion resistance.
MoおよびWは、調質時の焼戻しにおいて、微細炭化物の析出強化(二次硬化)により硬さを向上させる元素である。しかし同時には、焼戻しで起こる残留オーステナイトの分解を遅滞させるため、過多に含有すると、調質後の組織に残留オーステナイトが残りやすい。また、MoやWは高価な元素であるため、実用化する上では添加量を極力低減すべきである。よって、これら元素の添加量は(Mo+1/2W)の関係式で0.5~2.0%とする。 Mo and W are single or composite (Mo + 1 / 2W): 0.5 to 2.0%
Mo and W are elements that improve the hardness by precipitation strengthening (secondary hardening) of fine carbides during tempering during tempering. However, at the same time, since the decomposition of residual austenite that occurs during tempering is delayed, when it is excessively contained, residual austenite tends to remain in the tempered structure. Further, since Mo and W are expensive elements, the amount of addition should be reduced as much as possible for practical use. Therefore, the addition amount of these elements is 0.5 to 2.0% in the relational expression of (Mo + 1 / 2W).
Alは、本発明の重要な元素である。つまり、鋼素材中に含まれる十分量のAlは、切削加工時に発生する熱によって高融点酸化物であるAl2O3を切削工具表面に形成する。Al2O3の融点は約2050℃であり、これは切削温度よりも遥かに高いため、Al2O3は切削工具の保護皮膜として機能する。そして、0.04%以上を含有することで、十分な厚さの保護皮膜が形成され、工具寿命が改善する。しかし、Alを多量に添加した場合は、鋼素材中にAl2O3が介在物として多く形成されるため、鋼素材の被削性がかえって低下する。このため、Al添加量の上限は0.3%未満とする。好ましくは0.05%以上および/または0.15%以下である。 Al: 0.04 to less than 0.3% Al is an important element of the present invention. That is, a sufficient amount of Al contained in the steel material forms Al 2 O 3 , which is a high melting point oxide, on the cutting tool surface by heat generated during the cutting process. Since the melting point of Al 2 O 3 is about 2050 ° C., which is much higher than the cutting temperature, Al 2 O 3 functions as a protective film for the cutting tool. And by containing 0.04% or more, the protective film of sufficient thickness is formed and a tool life improves. However, when a large amount of Al is added, since much Al 2 O 3 is formed as inclusions in the steel material, the machinability of the steel material is lowered. For this reason, the upper limit of the amount of Al added is less than 0.3%. Preferably they are 0.05% or more and / or 0.15% or less.
Niは、鋼の靱性や溶接性を改善する元素である。また、調質時の焼戻しではNi3Alとして析出し、鋼の硬さを高める効果があるので、本発明に係る冷間工具鋼が含有するAl量に応じて添加することは有効である。ただし、Niは高価な金属であり、実用化する上では添加量を極力低減すべきである。そのため、本発明におけるNiは、添加する場合でも1.0%以下が好ましい。 -Preferably, Ni: 1.0% or less Ni is an element which improves the toughness and weldability of steel. Further, since tempering during tempering precipitates as Ni 3 Al and has the effect of increasing the hardness of the steel, it is effective to add it according to the amount of Al contained in the cold tool steel according to the present invention. However, Ni is an expensive metal, and the amount to be added should be reduced as much as possible for practical use. Therefore, Ni in the present invention is preferably 1.0% or less even when added.
Cuは、調質時の焼戻しにおいてε-Cuとして析出し、鋼の硬さを高める効果がある。ただし、Cuは鋼素材の熱間脆性を引き起こす元素である。よって、本発明におけるCuは、添加する場合でも1.0%以下が好ましい。なお、Cuによる熱間脆性は、ほぼ同量のNiを添加することで抑制できるため、本発明に係る冷間工具鋼がNiを含む場合は、該量に応じて規制値を緩和することができる。 -Preferably, Cu: 1.0% or less Cu precipitates as (epsilon) -Cu in the tempering at the time of tempering, and has the effect of raising the hardness of steel. However, Cu is an element that causes hot brittleness of a steel material. Accordingly, Cu in the present invention is preferably 1.0% or less even when added. In addition, since hot brittleness due to Cu can be suppressed by adding substantially the same amount of Ni, when the cold tool steel according to the present invention contains Ni, the regulation value can be relaxed according to the amount. it can.
Vは、種々の炭化物を形成して、鋼の硬さを高める効果がある。また、形成された未固溶のMC炭化物は、結晶粒の成長を抑制する効果がある。そして特に、後述のNbと複合添加することで、焼入加熱時に未固溶のMC炭化物が微細かつ均一となり、結晶粒成長を効果的に抑制する働きがある。一方、MC炭化物は硬質であり、被削性を低下させる原因となる。そこで本発明では、上述した複合潤滑保護皮膜を切削加工時の工具表面に形成させたことで、鋼素材中に多くのMC炭化物を形成しても良好な被削性を確保できる点に重要な特徴を有する。ただし、過多のV添加は、粗大なMC炭化物を過剰に形成して、冷間工具鋼の靱性も低下させる。そのため、Vは添加する場合でも1.0%以下とすることが好ましい。より好ましくは0.7%以下である。 -Preferably, V: 1.0% or less V has the effect of forming various carbides and increasing the hardness of the steel. In addition, the formed insoluble MC carbide has an effect of suppressing the growth of crystal grains. In particular, by adding it in combination with Nb, which will be described later, the MC carbide that has not been dissolved yet during quenching heating becomes fine and uniform, and has the function of effectively suppressing crystal grain growth. On the other hand, MC carbide is hard and causes a decrease in machinability. Therefore, in the present invention, the above-described composite lubricating protective film is formed on the tool surface at the time of cutting, which is important in that good machinability can be ensured even if many MC carbides are formed in the steel material. Has characteristics. However, excessive V addition excessively forms coarse MC carbides and also reduces the toughness of the cold tool steel. Therefore, V is preferably 1.0% or less even when added. More preferably, it is 0.7% or less.
Nbは、MC炭化物を形成して、結晶粒の粗大化を抑える働きがある。ただし、過多に添加すると、粗大なMC炭化物が過剰に形成されて、鋼の靱性が低下する。そのため、添加する場合でも0.5%以下とすることが好ましい。より好ましくは0.3%以下である。 -Preferably, Nb: 0.5% or less Nb has the function which forms MC carbide | carbonized_material and suppresses the coarsening of a crystal grain. However, if added excessively, coarse MC carbides are excessively formed, and the toughness of the steel decreases. Therefore, even when added, the content is preferably 0.5% or less. More preferably, it is 0.3% or less.
Claims (8)
- 質量%で、
C:0.6~1.2%、
Si:0.8~2.5%、
Mn:0.4~2.0%、
S:0.03~0.1%、
Cr:5.0~9.0%、
MoおよびWは単独または複合で(Mo+1/2W):0.5~2.0%、
Al:0.04~0.3%未満、
残部Feおよび不可避的不純物からなる冷間工具鋼の鋼塊に熱間加工を行って素材とし、
前記素材に焼入れ焼戻しを行って硬さを58~62HRCに調質した後に、
切削加工を行って金型の形状に仕上げることを特徴とする冷間加工用金型の製造方法。 % By mass
C: 0.6 to 1.2%
Si: 0.8 to 2.5%,
Mn: 0.4 to 2.0%,
S: 0.03-0.1%,
Cr: 5.0 to 9.0%,
Mo and W are used alone or in combination (Mo + 1 / 2W): 0.5 to 2.0%,
Al: 0.04 to less than 0.3%,
Hot working on the steel ingot of the cold tool steel consisting of the balance Fe and inevitable impurities,
After quenching and tempering the material to adjust the hardness to 58-62 HRC,
A method for producing a cold working mold, wherein the mold is finished by cutting. - 前記熱間加工を行った素材に、焼鈍を行った後、前記焼入れ焼戻しを行うことを特徴とする請求項1に記載の冷間加工用金型の製造方法。 The method for manufacturing a cold working mold according to claim 1, wherein the quenching and tempering is performed after annealing the hot-worked material.
- 前記焼入れは、前記熱間加工後の冷却過程で行う直接焼入れであることを特徴とする請求項1に記載の冷間加工用金型の製造方法。 The method for manufacturing a cold working die according to claim 1, wherein the quenching is a direct quenching performed in a cooling process after the hot working.
- 前記冷間工具鋼は、質量%で、Ni:1.0%以下をさらに含有することを特徴とする請求項1ないし3のいずれかに記載の冷間加工用金型の製造方法。 The method for producing a cold working die according to any one of claims 1 to 3, wherein the cold tool steel further contains Ni: 1.0% or less in mass%.
- 前記冷間工具鋼は、質量%で、Cu:1.0%以下をさらに含有することを特徴とする請求項1ないし4のいずれかに記載の冷間加工用金型の製造方法。 The method for manufacturing a cold working die according to any one of claims 1 to 4, wherein the cold tool steel further contains Cu: 1.0% or less in terms of mass%.
- 前記冷間工具鋼は、質量%で、V:1.0%以下をさらに含有することを特徴とする請求項1ないし5のいずれかに記載の冷間加工用金型の製造方法。 The method for manufacturing a cold working die according to any one of claims 1 to 5, wherein the cold tool steel further contains, by mass%, V: 1.0% or less.
- 前記冷間工具鋼は、質量%で、Nb:0.5%以下をさらに含有することを特徴とする請求項1ないし6のいずれかに記載の冷間加工用金型の製造方法。 The method for producing a cold working die according to any one of claims 1 to 6, wherein the cold tool steel further contains, by mass%, Nb: 0.5% or less.
- 調質後の硬さが60HRC以上であることを特徴とする請求項1ないし7のいずれかに記載の冷間加工用金型の製造方法。 The method for producing a cold working mold according to any one of claims 1 to 7, wherein the hardness after tempering is 60 HRC or more.
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201280009869.1A CN103403207B (en) | 2011-02-21 | 2012-02-20 | The manufacture method of cold working mould |
EP12749111.6A EP2679697B1 (en) | 2011-02-21 | 2012-02-20 | Manufacturing method for cold-working die |
JP2013501016A JP5843173B2 (en) | 2011-02-21 | 2012-02-20 | Manufacturing method of cold working mold |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2011034188 | 2011-02-21 | ||
JP2011-034188 | 2011-02-21 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2012115025A1 true WO2012115025A1 (en) | 2012-08-30 |
Family
ID=46720802
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2012/053929 WO2012115025A1 (en) | 2011-02-21 | 2012-02-20 | Manufacturing method for cold-working die |
Country Status (5)
Country | Link |
---|---|
EP (1) | EP2679697B1 (en) |
JP (1) | JP5843173B2 (en) |
CN (1) | CN103403207B (en) |
TW (1) | TWI440726B (en) |
WO (1) | WO2012115025A1 (en) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103834872A (en) * | 2012-11-26 | 2014-06-04 | 天工爱和特钢有限公司 | Die steel with high-wearing resistance |
WO2014156487A1 (en) | 2013-03-29 | 2014-10-02 | 日立金属株式会社 | Steel material for die and process for producing same, process for producing prehardened steel product for die, and process for producing cold working die |
JPWO2014030619A1 (en) * | 2012-08-20 | 2016-07-28 | 日立金属株式会社 | Method for cutting cold tool steel and method for producing cold mold material |
JP2016156081A (en) * | 2015-02-26 | 2016-09-01 | 大同特殊鋼株式会社 | Alloy tool steel |
KR101828228B1 (en) * | 2014-09-26 | 2018-02-09 | 히타치 긴조쿠 가부시키가이샤 | Cold tool material and method for manufacturing cold tool |
KR101852316B1 (en) | 2016-03-18 | 2018-04-25 | 히타치 긴조쿠 가부시키가이샤 | Method for manufacturing cold tool material and cold tool |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016152406A1 (en) * | 2015-03-26 | 2016-09-29 | 日立金属株式会社 | Cold work tool and method for manufacturing same |
CN105945160A (en) * | 2016-05-25 | 2016-09-21 | 南京工业职业技术学院 | Round hole plunger chip processing technology |
CN107937819A (en) * | 2017-11-18 | 2018-04-20 | 蚌埠市宏大制药机械有限公司 | A kind of high-quality feedstocks for mold manufacturing |
CN107937837A (en) * | 2017-11-18 | 2018-04-20 | 蚌埠市宏大制药机械有限公司 | A kind of manufacture method of high-performance Pharmic die |
CN110656281A (en) * | 2018-06-29 | 2020-01-07 | 宝钢特钢有限公司 | High-hardness die steel and preparation method thereof |
CN109913751B (en) * | 2019-03-13 | 2020-11-06 | 江西耐普矿机股份有限公司 | High-strength and high-toughness bainite wear-resistant steel suitable for large-scale semi-autogenous mill lining plate and preparation method thereof |
CN110016617B (en) * | 2019-05-08 | 2021-05-04 | 上海大学 | Cold-work die steel and preparation method thereof |
JP2022144437A (en) * | 2021-03-19 | 2022-10-03 | 大同特殊鋼株式会社 | Fe-based alloy and metal powder |
CN117660734B (en) * | 2024-01-31 | 2024-06-04 | 成都先进金属材料产业技术研究院股份有限公司 | Cold work die steel surface strengthening treatment method and cold work die steel |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2001316769A (en) | 2000-05-10 | 2001-11-16 | Daido Steel Co Ltd | Cold tool steel |
JP2005272899A (en) | 2004-03-23 | 2005-10-06 | Nippon Koshuha Steel Co Ltd | Tool steel having self-lubricity |
JP2006169624A (en) * | 2004-11-18 | 2006-06-29 | Hitachi Metals Ltd | Cold die steel having excellent dimensional change suppression property and galling resistance |
JP2006193790A (en) | 2005-01-14 | 2006-07-27 | Daido Steel Co Ltd | Cold working tool steel |
JP2007002333A (en) * | 2005-05-26 | 2007-01-11 | Hitachi Metals Ltd | Press die with excellent self-lubricating property |
JP2008189982A (en) | 2007-02-02 | 2008-08-21 | Daido Steel Co Ltd | Tool steel |
JP2009132990A (en) | 2007-10-31 | 2009-06-18 | Daido Steel Co Ltd | Alloy tool steel and manufacturing method thereof |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000212700A (en) * | 1998-11-20 | 2000-08-02 | Hitachi Metals Ltd | Die excellent in weldability |
JP4487257B2 (en) * | 2004-11-29 | 2010-06-23 | 日立金属株式会社 | Cold die steel with excellent size reduction characteristics |
CN101528962A (en) * | 2006-10-17 | 2009-09-09 | 株式会社神户制钢所 | Cold work die steel, die, and method for production of cold work die steel |
WO2008047806A1 (en) * | 2006-10-17 | 2008-04-24 | Kabushiki Kaisha Kobe Seiko Sho | Cold work die steel, die, and method for production of cold work die steel |
JP5143531B2 (en) * | 2007-11-13 | 2013-02-13 | 株式会社神戸製鋼所 | Cold mold steel and molds |
CN102209798B (en) * | 2009-05-22 | 2013-10-30 | 新日铁住金株式会社 | Steel for machine structure use attaining excellent cutting-tool life and method for cutting same |
-
2012
- 2012-02-20 CN CN201280009869.1A patent/CN103403207B/en active Active
- 2012-02-20 WO PCT/JP2012/053929 patent/WO2012115025A1/en active Application Filing
- 2012-02-20 JP JP2013501016A patent/JP5843173B2/en active Active
- 2012-02-20 TW TW101105391A patent/TWI440726B/en active
- 2012-02-20 EP EP12749111.6A patent/EP2679697B1/en active Active
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2001316769A (en) | 2000-05-10 | 2001-11-16 | Daido Steel Co Ltd | Cold tool steel |
JP2005272899A (en) | 2004-03-23 | 2005-10-06 | Nippon Koshuha Steel Co Ltd | Tool steel having self-lubricity |
JP2006169624A (en) * | 2004-11-18 | 2006-06-29 | Hitachi Metals Ltd | Cold die steel having excellent dimensional change suppression property and galling resistance |
JP2006193790A (en) | 2005-01-14 | 2006-07-27 | Daido Steel Co Ltd | Cold working tool steel |
JP2007002333A (en) * | 2005-05-26 | 2007-01-11 | Hitachi Metals Ltd | Press die with excellent self-lubricating property |
JP2008189982A (en) | 2007-02-02 | 2008-08-21 | Daido Steel Co Ltd | Tool steel |
JP2009132990A (en) | 2007-10-31 | 2009-06-18 | Daido Steel Co Ltd | Alloy tool steel and manufacturing method thereof |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPWO2014030619A1 (en) * | 2012-08-20 | 2016-07-28 | 日立金属株式会社 | Method for cutting cold tool steel and method for producing cold mold material |
CN103834872A (en) * | 2012-11-26 | 2014-06-04 | 天工爱和特钢有限公司 | Die steel with high-wearing resistance |
WO2014156487A1 (en) | 2013-03-29 | 2014-10-02 | 日立金属株式会社 | Steel material for die and process for producing same, process for producing prehardened steel product for die, and process for producing cold working die |
JP2016106176A (en) * | 2013-03-29 | 2016-06-16 | 日立金属株式会社 | Method for manufacturing prehardened steel material for use in die, and method for manufacturing die for cold working |
EP2979772A4 (en) * | 2013-03-29 | 2016-10-12 | Hitachi Metals Ltd | Steel material for die and process for producing same, process for producing prehardened steel product for die, and process for producing cold working die |
JP6032582B2 (en) * | 2013-03-29 | 2016-11-30 | 日立金属株式会社 | Manufacturing method of steel material for mold |
KR101828228B1 (en) * | 2014-09-26 | 2018-02-09 | 히타치 긴조쿠 가부시키가이샤 | Cold tool material and method for manufacturing cold tool |
JP2016156081A (en) * | 2015-02-26 | 2016-09-01 | 大同特殊鋼株式会社 | Alloy tool steel |
KR101852316B1 (en) | 2016-03-18 | 2018-04-25 | 히타치 긴조쿠 가부시키가이샤 | Method for manufacturing cold tool material and cold tool |
US10407747B2 (en) | 2016-03-18 | 2019-09-10 | Hitachi Metals, Ltd. | Cold working tool material and cold working tool manufacturing method |
Also Published As
Publication number | Publication date |
---|---|
JP5843173B2 (en) | 2016-01-13 |
EP2679697A4 (en) | 2016-11-23 |
CN103403207B (en) | 2016-06-15 |
TW201250010A (en) | 2012-12-16 |
CN103403207A (en) | 2013-11-20 |
EP2679697A1 (en) | 2014-01-01 |
TWI440726B (en) | 2014-06-11 |
JPWO2012115025A1 (en) | 2014-07-07 |
EP2679697B1 (en) | 2018-06-27 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5843173B2 (en) | Manufacturing method of cold working mold | |
US6884388B2 (en) | Low carbon martensitic stainless steel and method for production thereof | |
JP5276330B2 (en) | Cold mold steel and cold press mold | |
JP5143531B2 (en) | Cold mold steel and molds | |
JP2014177710A (en) | Hardening method for steel | |
JP5672466B2 (en) | Cold work tool steel with excellent machinability | |
JP4860774B1 (en) | Cold work tool steel | |
JP4269293B2 (en) | Steel for mold | |
EP3006601B1 (en) | Method for manufacturing mold for cold working use | |
JP2014031575A (en) | Steel for high hardness cold die and manufacturing method thereof | |
JP5351528B2 (en) | Cold mold steel and molds | |
JP6416624B2 (en) | Method for cutting cold tool steel and method for producing cold mold material | |
KR102550394B1 (en) | Hot work tool steels and hot work tools | |
JP4411594B2 (en) | Cold working mold | |
JP6583484B2 (en) | Nitriding steel | |
JP3191008B2 (en) | Hot tool steel | |
JP2008038219A (en) | Prehardened steel with excellent machinability and toughness | |
JP6716156B2 (en) | Resource-saving cold press die steel with excellent surface treatment | |
JP2021091954A (en) | Steel for mold and mold | |
JP2004315840A (en) | Cold working tool steel superior in machinability, and manufacturing method therefor | |
JP2006249494A (en) | Material for nitriding part excellent in suitability to broaching and method for manufacturing the same | |
JPH03199341A (en) | High-hardness prehardened free cutting steel |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 12749111 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2013501016 Country of ref document: JP Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2012749111 Country of ref document: EP |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 1301004601 Country of ref document: TH |