EP2679697A1 - Procédé de fabrication de matrice pour formage à froid - Google Patents
Procédé de fabrication de matrice pour formage à froid Download PDFInfo
- Publication number
- EP2679697A1 EP2679697A1 EP12749111.6A EP12749111A EP2679697A1 EP 2679697 A1 EP2679697 A1 EP 2679697A1 EP 12749111 A EP12749111 A EP 12749111A EP 2679697 A1 EP2679697 A1 EP 2679697A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- cold
- steel
- machining
- hardness
- work tool
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 7
- 238000005482 strain hardening Methods 0.000 title abstract 2
- 229910000822 Cold-work tool steel Inorganic materials 0.000 claims abstract description 37
- 239000000463 material Substances 0.000 claims abstract description 32
- 238000005496 tempering Methods 0.000 claims abstract description 13
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 238000003754 machining Methods 0.000 claims description 47
- 238000000034 method Methods 0.000 claims description 33
- 230000000171 quenching effect Effects 0.000 claims description 21
- 238000010791 quenching Methods 0.000 claims description 19
- 238000000137 annealing Methods 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 4
- 229910000831 Steel Inorganic materials 0.000 abstract description 42
- 239000010959 steel Substances 0.000 abstract description 42
- 229910052742 iron Inorganic materials 0.000 abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract 2
- 239000000523 sample Substances 0.000 description 29
- 150000001247 metal acetylides Chemical class 0.000 description 25
- 230000008569 process Effects 0.000 description 21
- 230000001681 protective effect Effects 0.000 description 21
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 20
- 229910052593 corundum Inorganic materials 0.000 description 20
- 229910052717 sulfur Inorganic materials 0.000 description 20
- 229910001845 yogo sapphire Inorganic materials 0.000 description 20
- 230000001050 lubricating effect Effects 0.000 description 19
- 238000005520 cutting process Methods 0.000 description 18
- 238000002844 melting Methods 0.000 description 15
- 230000008018 melting Effects 0.000 description 15
- 229910052782 aluminium Inorganic materials 0.000 description 13
- 229910052720 vanadium Inorganic materials 0.000 description 10
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 9
- 239000000203 mixture Substances 0.000 description 9
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 8
- 230000000694 effects Effects 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 8
- 239000011593 sulfur Substances 0.000 description 8
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 8
- 239000011248 coating agent Substances 0.000 description 7
- 238000000576 coating method Methods 0.000 description 7
- 230000006870 function Effects 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 238000013507 mapping Methods 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 238000011282 treatment Methods 0.000 description 4
- 229910000760 Hardened steel Inorganic materials 0.000 description 3
- 238000004458 analytical method Methods 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 230000002401 inhibitory effect Effects 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- 230000000717 retained effect Effects 0.000 description 3
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910005347 FeSi Inorganic materials 0.000 description 1
- -1 Nb and V Chemical class 0.000 description 1
- 229910001005 Ni3Al Inorganic materials 0.000 description 1
- 238000003917 TEM image Methods 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 208000037998 chronic venous disease Diseases 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 229910052840 fayalite Inorganic materials 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000009993 protective function Effects 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
Images
Classifications
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- 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 of manufacturing a cold-work, for example, for forming parts of home electric appliances, mobile phones or automobiles.
- a steel material In a field of cold-work tools for use in press forming such as bending, squeezing or punching of a plate material at a room temperature, a steel material has been proposed that can obtain a hardness of not lower than 55 HRC by quenching and tempering (hereinafter, quenching and tempering are referred to as "hardening process") in order to improve wear resistance (see Patent Literatures 1 to 3). Since it is difficult to machine the steel material having such a high hardness into a die shape after the hardening process, the steel material is usually roughly worked in an annealed state after hot worked where the hardness is low, and then is subjected to the hardening process to a hardness of not lower than 55 HRC for use.
- the die since the die is deformed due to the heat treatment of the hardening process, the die is again subjected to finish machining to correct the deformed portion after the hardening process, and finished in a final tool shape.
- the main reason for the heat treatment deformation of the tool due to the hardening process is because the steel material transforms from a ferritic structure in the annealed state to a martensitic structure and thus volume expansion generates.
- a cold-work tool steel has been proposed for suppressing tool wear caused by a friction between a cutting tool and a steel material at a time of machining.
- the steel has self-lubricating properties by adding an element forming an oxide having a melting point of 1200°C or lower ((FeO) 2 ⁇ SiO 2 , Fe 2 SiO 4 or (FeSi)Cr 2 O 2 ) to form the oxide on a surface of a die by heat generated at the time of machining (Patent Literature 5).
- a cold-work tool steel has a hardness after quenched and tempered of not lower than 58HRC, further not lower than 60HRC. Therefore, it is preferable that a pre-hardened steel stably achieves the hardness of not lower than 60HRC, as a matter of course not lower than 58HRC, as well as superior machinability in the state having such a high hardness.
- the cold-work tool steel disclosed in Patent Literature 4 is a superior pre-hardened steel simultaneously satisfying machinability at the time of machining and wear resistance as a die.
- Patent Literature 4 discloses that Nb and V are preferably added for suppressing grain growth at a time of heating for quenching. However, the elements are likely to form insoluble MC carbides at the above quenching temperature. Since the MC carbides are hard, there is a problem that machinability after the hardening process is deteriorated in the composition disclosed in Patent Literature 4.
- the cold-work tool steel disclosed in Patent Literature 5 utilizes a low melting point oxide as a self-lubricating film.
- the lubricating effect is not obtained when the machining temperature is below the melting point of the oxide.
- the machining temperature rises too high, there is a problem that a viscosity of the oxide is remarkably reduced and the oxide will not serve as the lubricating film.
- An object of the present invention is to provide a method of manufacturing a cold-work die, including machining a cold-work tool steel having a composition for stably achieving a high hardness of not lower than 60 HRC, as a matter of course of not lower than 58 HRC, and also preferably having remarkably improved machinability after the hardening process without depending on a machining temperature even if an amount of insoluble carbides are further increased.
- the present inventors have studied to improve machinability of a cold-work tool steel. As a result, the inventors have found that Al 2 O 3 which is an oxide having a high melting point is positively introduced to form a complex lubricating protective film including Al 2 O 3 and MnS, which is a high ductility inclusion, on a surface of a cutting tool by heat generated at a time of machining.
- the inventors has found a compositional range for the steel material that is capable of forming the complex lubricating protective film as well as having a hardness of not lower than 60 HRC, as a matter of course not lower than 58HRC, thereby reaching the present invention.
- the present invention provides a method of manufacturing a cold-work die, including:
- the cold-work tool steel may include not greater than 1.0% of Ni, or may further include not greater than 1.0% of Cu.
- the cold-work tool steel may further include not greater than 1.0% of V, or may further include not greater than 0.5% of Nb.
- the present invention uses a mechanism for improving machinability, which can be widely applied to a number of steel compositions.
- machinability machinability
- the cold-work tool steel can have remarkably improved machinability after the hardening process without depending on a machining temperature. Therefore, the hardness of the cold-work tool steel and the amount of the insoluble carbides can be widely selected depending on various functions.
- the steel is thermally refined to have a hardness of 58-62HRC and then machined, a die can be manufactured without the problems of the deformation during heat-treatment and the finishing machining.
- the invention provides an essential technique for practical use of a cold work die, in particular made of the pre-hardened cold-work tool steels.
- the present invention realizes a cold-work tool steel having not only an improved hardness but also good machinability after the hardening process without depending on a machining temperature even if a large amount of insoluble carbides are formed to, for example, control a grain size, and the invention has characterization of machining the steel after hardening.
- the hardening is conducted before the machining of the steel material designed so that a hardness of not lower than 58HRC, preferably not lower than 60 HRC, is achieved, as well as a complex lubricating protective film of Al 2 O 3 as a high melting point oxide and MnS as a high ductility inclusion are formed on a surface of a cutting tool in order to suppress wear of the cutting tool.
- the present inventors have studied to improve machinability, which can be widely applied to a composition of a cold-work tool steel. As a result, the inventors have noticed on effectiveness of self-lubricating properties. Then, the inventors have studied the effect of self-lubricating properties of the oxide having a low melting point as Patent Literature 5, and consequently have found a problem that the low melting point oxide depends on a machining temperature.
- the low melting point oxide having self-lubricating properties is generally a complex oxide including Fe and Cr which are included in a steel material in a large amount. Thus, when the machining temperature changes, a composition and an amount of the complex oxide change and a stable lubricating effect is not obtained.
- Carbon is an important element for forming carbides in a steel to make a cold-work tool steel hard. If the carbon content is too small, an amount of the carbides is insufficient, and it is difficult to provide a hardness of not lower than 58HRC, preferably not lower than 60 HRC. On the other hand, if an excessive amount of carbon is included, an amount of insoluble carbides increases in quenching, and toughness is likely to be decreased. Therefore, the carbon content is defined as 0.6 to 1.2%. Preferably, the content is not less than 0.7% and/or not greater than 1.1 %. Not greater than 1.0% is further preferable.
- Si solid-solutes in a steel, and is an important element for making the cold-work tool steel hard.
- Si since Si has a stronger tendency to be oxidized than Fe and Cr and is also likely to form corundum-type oxides with Al 2 O 3 , Si has an important function to suppress a formation of Fe-based and Cr-based oxides which reduce a melting point of oxides, and to promote formation of an Al 2 O 3 protective film.
- the Si content is defined as 0.8 to 2.5%.
- the content is not less than 1.0% and/or not greater than 2.0%. Not less than 1.2% is further preferable.
- Mn is an important element in the present invention. Mn acts as a good lubricating film on the Al 2 O 3 protective film formed on a surface of a cutting tool. Mn forms austenitic phase and solid-solutes in the steel to enhance quenching properties. However, if the Mn content is too large, a large amount of retained austenite remains after the hardening process, which causes secular deformation during use of a die. In addition, since Mn is likely to form low melting point oxides with Fe and Cr, it becomes a factor of inhibiting the function of the Al 2 O 3 protective film. Therefore, the Mn content is defined as 0.4 to 2.0% in the present invention. Preferably, the content is not less than 0.6% and/or not greater than 1.5%.
- Sulfur is an important element in the present invention. Sulfur acts as a good lubricating film on the Al 2 O 3 protective film formed on a surface of a cutting tool. When sufficient sulfur is included in the steel material, MnS is formed. Since MnS has good ductility we well as is compatible with Al 2 O 3 , it deposits on the Al 2 O 3 protective film and acts as a good lubricating protective complex film. In order to sufficiently exert such a lubricating action, sulfur is required to be added in an amount of not less than 0.03%. However, sulfur deteriorates toughness of the steel, and therefore an upper limit thereof is defined as 0.1 %. Preferably, the sulfur content is not less than 0.04% and/or not greater than 0.08%.
- Cr forms an M 7 C 3 carbide in a structure after the hardening process, thereby it makes a cold-work tool steel hard.
- Cr has an effect of suppressing grain growth since a part of Cr forms insoluble carbides at a time of quenching heating.
- a Cr content is not less than 5.0%, a large amount of carbides is formed, and a hardness of not lower than 58HRC, preferably not lower than 60HRC, is obtained.
- a surface of a cold-work die is subjected to various coating treatments, forming ability of a VC film with a TD treatment or a TiC film with a CVD treatment is enhanced. Cr is effective in ensuring corrosion resistance.
- Cr a main component of the cold-work tool steel, is likely to form an oxide having a low melting point.
- Cr a main component of the cold-work tool steel
- Cr is likely to form an oxide having a low melting point.
- Cr is important to adjust the Cr content provided that a sufficient amount of Al described below is included.
- the function of the above lubricating complex protective film is exerted by adjusting the corresponding sulfur content. Therefore, it is important that the Cr content is 5.0 to 9.0%.
- the content is preferably not less than 6.0%, and more preferably not less than 7.0%.
- Mo and W increase hardness by precipitation strengthening (secondary hardening) of fine carbides during tempering of the hardening process.
- Mo and W make the decomposition of retained austenite retard during the tempering.
- Mo and W are expensive, their addition should be reduced as much as possible in terms of practical use. Therefore, the amounts of the elements are defined as 0.5 to 2.0% in a form of relational expression (Mo + 1/2W).
- Al is an important element in the present invention.
- Al 2 O 3 that is an oxide having a high melting point
- Al 2 O 3 serves as the protective film of the machining tool.
- An amount of not less than 0.04% Al forms the protective film having a sufficient thickness, and improves tool lifetime.
- the upper limit of the Al content is defined as less than 0.3%.
- the Al content is not less than 0.05% and/or not greater than 0.15%.
- Ni not greater than 1.0%
- Ni improves toughness and weldability of the steel.
- Ni precipitates as Ni 3 Al in tempering of the hardening process and effects to increase hardness of the steel.
- it is effective to add Ni depending on the Al content in the cold-work tool steel of the present invention.
- Ni since Ni is an expensive metal, it should be reduced as much as possible in terms of practical use. Therefore, not greater than 1.0% Ni is preferable even if it is added.
- Cu precipitates as ⁇ -Cu during tempering of the hardening process and effects to increase a hardness of the steel.
- Cu causes hot-shortness of the steel material. Therefore, in the present invention, not greater than 1.0% Cu is preferable even if it is added.
- the hot-shortness by Cu is suppressed by adding substantially same amount of Ni. Thus, when the steel according to the invention includes Ni, the limitation of the content may be extended.
- Vanadium forms various carbides and effects to increase hardness of the steel.
- the formed insoluble MC carbides effect to suppress grain growth.
- vanadium is added in combination with Nb described later to make the insoluble MC carbides fine and uniform at the time of quenching heating, and vanadium acts to effectively suppress grain growth.
- the MC carbides are hard and deteriorate machinability.
- the present invention forms the above-described complex lubricating protective film on the surface of the tool at the time of machining to make it possible to ensure good machinability even if a large amount of MC carbides are formed in the steel material.
- the vanadium content is preferably not greater than 1.0%. More preferably, the vanadium content is not greater than 0.7%
- Nb not greater than 0.5%
- Nb forms MC carbides and effects to prevent coarse grains.
- coarse MC carbides are excessively formed to deteriorate toughness and machinability of the steel.
- the Nb content is preferably not greater than 0.5%. More preferably, the Nb content is not greater than 0.3%.
- the present invention resides in the machining of the cool tool steel having the above composition after the hardening of the steel so as to have a hardness of 58-62HRC.
- the cold-work tool steel according to the present invention can achieve a hardness of not lower than 58HRC by quenching and tempering. It is also possible to achieve a hardness of not lower than 60HRC. Since the steel has superior machinability while it has such a high hardness, there is no need to machine the steel in an annealed state followed by quenching and tempering. Since there is no need to undergo the annealed state, the steel can be directly quenched in the course of the cooling from hot working of the ingot.
- the cold-work tool steel of the present invention is used as a pre-hardened steel, it is possible to eliminate heat treatment deformation due to the hardening process and to omit finish machining, and may further omit the annealing step etc. for manufacturing the base material.
- the present invention defines an upper limit of the hardness is 62HRC in order to maintain sufficient mechanical properties other than the hardness of the steel and to stably conduct the machining.
- a die produced through the method according to the present invention has a superior dimensional accuracy and wear resistance. When it is subjected to PVD treatment, the wear resistance is further improved while maintaining a high dimensional accuracy.
- a machinability test was conducted by surface-grinding with an insert PICOmini manufactured by Hitachi Tool Engineering Ltd. as a cutting edge replaceable tool that can machine a high hardness material.
- the insert is made of a cemented carbide alloy as a base material coated with TiN. Machining conditions were as follows:
- Machinability was evaluated based on the following two points. First, an amount of the complex lubricating protective film including Al 2 O 3 and MnS on the surface of the cutting tool was evaluated. The amount was determined as follows. When a machining length is 0.8m after the beginning of the machining, the insert was analysed from a rake face side with EPMA, and the amount was evaluated by average counts of Al and S. Then, the machining length was extended to 8 m and the tool wear at this time was measured using an optical microscope. These evaluation results are shown in Table 2.
- the complex lubricating protective film is formed on the surface of the cutting tool to suppress the tool wear. Even in a case where Nb and V are added for forming insoluble carbides, good machinability is maintained. On the contrary, in the machining for the cold-work tool steels that do not satisfy the requirements of the present invention, the tool wear is larger than the steels of the present invention.
- Figs. 1A to 1E are digital microscope photographs showing flank faces and rake faces of cutting tools used for, respectively, Samples Nos. 3, 5, 15, 22 and 30.
- Figs. 2A to 2E are analysis results of belag on the surfaces in, respectively, Figs. 1A to 1E with use of EPMA, in which a high concentration portion of each element is represented in white colour.
- Samples Nos. 3, 5 and 15 exhibit large average counts of Al and S in Table 2, and it has been confirmed that much Al and S are attached over a wide region in the EPMA analysis of Figs. 2A to 2C .
- Sample No. 22 having smaller amount of Al has smaller average counts of Al and S and smaller attached Al and S than Samples Nos. 3, 5 and 15. Since Sample No. 30 originally has small Al and S contents in the steel, the average counts of these elements are small and Al and S are hardly detected in the EPMA analysis (detected elements were mostly Fe and Cr which were likely transferred from the test piece).
- Figs. 3A to 3C are cross sectional TEM images showing belag confirmed on the surfaces of the tools of respectively Samples No. 3, 22 and 30, together with an underlying TiN coating.
- reference number 1 denotes a protective film for preparing a sample
- reference number 2 denotes a belag at the time of machining
- reference number 3 denotes a plastically deformed TiN region
- reference number 4 denotes an undeformed TiN region.
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- 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)
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Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2011034188 | 2011-02-21 | ||
| PCT/JP2012/053929 WO2012115025A1 (fr) | 2011-02-21 | 2012-02-20 | Procédé de fabrication de matrice pour formage à froid |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| EP2679697A1 true EP2679697A1 (fr) | 2014-01-01 |
| EP2679697A4 EP2679697A4 (fr) | 2016-11-23 |
| EP2679697B1 EP2679697B1 (fr) | 2018-06-27 |
Family
ID=46720802
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP12749111.6A Active EP2679697B1 (fr) | 2011-02-21 | 2012-02-20 | Procédé de fabrication de matrice pour formage à froid |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP2679697B1 (fr) |
| JP (1) | JP5843173B2 (fr) |
| CN (1) | CN103403207B (fr) |
| TW (1) | TWI440726B (fr) |
| WO (1) | WO2012115025A1 (fr) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3199656A4 (fr) * | 2014-09-26 | 2017-09-20 | Hitachi Metals, Ltd. | Matériau d'outil froid et procédé de fabrication d'outil froid |
| US10407747B2 (en) | 2016-03-18 | 2019-09-10 | Hitachi Metals, Ltd. | Cold working tool material and cold working tool manufacturing method |
| EP4059638A1 (fr) * | 2021-03-19 | 2022-09-21 | Daido Steel Co., Ltd. | Alliage à base de fe et poudre métallique |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6416624B2 (ja) * | 2012-08-20 | 2018-10-31 | 日立金属株式会社 | 冷間工具鋼の切削方法及び冷間金型材料の製造方法 |
| CN103834872A (zh) * | 2012-11-26 | 2014-06-04 | 天工爱和特钢有限公司 | 高耐磨性模具钢 |
| WO2014156487A1 (fr) | 2013-03-29 | 2014-10-02 | 日立金属株式会社 | Matériau d'acier pour matrice et procédé de production de celui-ci, procédé de production de produit d'acier prédurci pour matrice, et procédé de production de matrice de formage à froid |
| JP6519226B2 (ja) * | 2015-02-26 | 2019-05-29 | 大同特殊鋼株式会社 | 合金工具鋼 |
| TR201901455T4 (tr) * | 2015-03-26 | 2019-02-21 | Hitachi Metals Ltd | Soğuk iş takımı ve aynısının üretim yöntemi. |
| CN105945160A (zh) * | 2016-05-25 | 2016-09-21 | 南京工业职业技术学院 | 一种圆孔冲头加工工艺 |
| CN107937837A (zh) * | 2017-11-18 | 2018-04-20 | 蚌埠市宏大制药机械有限公司 | 一种高性能制药模具的制造方法 |
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| CN110656281A (zh) * | 2018-06-29 | 2020-01-07 | 宝钢特钢有限公司 | 一种高硬模具钢及其制备方法 |
| CN109913751B (zh) * | 2019-03-13 | 2020-11-06 | 江西耐普矿机股份有限公司 | 适用于大型半自磨机衬板的高强韧性贝氏体耐磨钢及其制备方法 |
| CN110016617B (zh) * | 2019-05-08 | 2021-05-04 | 上海大学 | 一种冷作模具钢及其制备方法 |
| CN117660734B (zh) * | 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 | 一种冷作模具钢表面强化处理方法及冷作模具钢 |
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| JP2000212700A (ja) * | 1998-11-20 | 2000-08-02 | Hitachi Metals Ltd | 溶接性に優れた金型 |
| JP2001316769A (ja) | 2000-05-10 | 2001-11-16 | Daido Steel Co Ltd | 冷間工具鋼 |
| JP4093978B2 (ja) * | 2004-03-23 | 2008-06-04 | 日本高周波鋼業株式会社 | 自己潤滑性を有する工具鋼 |
| JP4737606B2 (ja) * | 2004-11-18 | 2011-08-03 | 日立金属株式会社 | 変寸抑制特性および耐カジリ性に優れた冷間ダイス鋼 |
| JP4487257B2 (ja) * | 2004-11-29 | 2010-06-23 | 日立金属株式会社 | 変寸抑制特性に優れた冷間ダイス鋼 |
| JP2006193790A (ja) * | 2005-01-14 | 2006-07-27 | Daido Steel Co Ltd | 冷間工具鋼 |
| JP4844874B2 (ja) * | 2005-05-26 | 2011-12-28 | 日立金属株式会社 | プレス成形品の製造方法 |
| CN101528962A (zh) * | 2006-10-17 | 2009-09-09 | 株式会社神户制钢所 | 冷加工模具钢、模具和用于制造冷加工模具钢的方法 |
| US20100074792A1 (en) * | 2006-10-17 | 2010-03-25 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Cold work die steel, die, and method for production of cold work die steel |
| JP2008189982A (ja) | 2007-02-02 | 2008-08-21 | Daido Steel Co Ltd | 工具鋼 |
| JP5338188B2 (ja) * | 2007-10-31 | 2013-11-13 | 大同特殊鋼株式会社 | 合金工具鋼及びその製造方法 |
| JP5143531B2 (ja) * | 2007-11-13 | 2013-02-13 | 株式会社神戸製鋼所 | 冷間金型用鋼および金型 |
| BRPI1012814B1 (pt) * | 2009-05-22 | 2019-02-19 | Nippon Steel & Sumitomo Metal Corporation | Método para usinar aço para uso em estruturas de máquinas |
-
2012
- 2012-02-20 CN CN201280009869.1A patent/CN103403207B/zh active Active
- 2012-02-20 TW TW101105391A patent/TWI440726B/zh active
- 2012-02-20 JP JP2013501016A patent/JP5843173B2/ja active Active
- 2012-02-20 WO PCT/JP2012/053929 patent/WO2012115025A1/fr active Application Filing
- 2012-02-20 EP EP12749111.6A patent/EP2679697B1/fr active Active
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3199656A4 (fr) * | 2014-09-26 | 2017-09-20 | Hitachi Metals, Ltd. | Matériau d'outil froid et procédé de fabrication d'outil froid |
| US9890435B2 (en) | 2014-09-26 | 2018-02-13 | Hitachi Metals, Ltd. | Cold work tool material and method of manufacturing cold work tool |
| US10407747B2 (en) | 2016-03-18 | 2019-09-10 | Hitachi Metals, Ltd. | Cold working tool material and cold working tool manufacturing method |
| EP4059638A1 (fr) * | 2021-03-19 | 2022-09-21 | Daido Steel Co., Ltd. | Alliage à base de fe et poudre métallique |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103403207A (zh) | 2013-11-20 |
| TWI440726B (zh) | 2014-06-11 |
| JPWO2012115025A1 (ja) | 2014-07-07 |
| JP5843173B2 (ja) | 2016-01-13 |
| CN103403207B (zh) | 2016-06-15 |
| TW201250010A (en) | 2012-12-16 |
| EP2679697A4 (fr) | 2016-11-23 |
| EP2679697B1 (fr) | 2018-06-27 |
| WO2012115025A1 (fr) | 2012-08-30 |
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