US20060157163A1 - Cold working die steel - Google Patents
Cold working die steel Download PDFInfo
- Publication number
- US20060157163A1 US20060157163A1 US11/332,910 US33291006A US2006157163A1 US 20060157163 A1 US20060157163 A1 US 20060157163A1 US 33291006 A US33291006 A US 33291006A US 2006157163 A1 US2006157163 A1 US 2006157163A1
- Authority
- US
- United States
- Prior art keywords
- steel
- cold working
- carbide
- working die
- hardness
- 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.)
- Abandoned
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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
Definitions
- This invention relates to a cold working die steel used for cold die and structural components processed by forging or pressing in cold working; mechanical components demanding wear resistance; punch and die for cold forging; mold die for high tensile steel sheets; bending dies; cold forging dies; swaging dies; thread rolling dies; punch components; slitter knives; punch dies for lead frames; gauges; deep-drawing punches; bender punches; shear blades; benders for stainless steel; drawing dies; tools for plastic working such as heading; punches for gears; cam components; press punch dies; progressive punch dies; seal plates for soil conveyers; screw components; rotary plates for concrete spraying machines; IC molding dies; precision press mold demanding high dimensional accuracy; and dies used for the above-described applications after being surface-treated by CVD, PVD or TD.
- SKD11, SKD12 and so forth which are representative steel types for high-alloy cold dies specified by JIS G4404 have conventionally been used as cold die steel.
- These cold die steels are subjected to cold working after being subjected to hot working (forging, rolling), and then to annealing, in which the steel is heated to a temperature range from point Ar3 to Ar3+50° C. and then slowly cooled.
- the hardness obtained after annealing under such annealing conditions falls in the range approximately from HB241 to HB255 on the Brinell hardness basis.
- Japanese Laid-Open Patent Publication “Tokkaihei” No. 6-322439 discloses that the hardness can be lowered as compared with that attained by conventional annealing, by raising the annealing temperature higher than in the conventional process.
- the document describes that the lowering of the hardness can increase the machinability, it is hardly said that the hardness of HV262 to 278 (approximately 250 to 265 on the HB basis) listed in Table 2 is small enough.
- no description is made on the hardness after quench-and-temper, despite a known problem in that annealing carried out at a temperature higher than hardening temperature results in lowering in the hardness after quench and temper than usual.
- the present invention was conceived taking the above-described problems into account, and an object thereof resides in providing a cold working die steel which can be reduced in its hardness by annealing, and is improved in readiness in the cold workability (forging, pressing and so forth) and machinability (milling, drilling, endmilling processing, grinding and turning).
- cold working die steel according to the first aspect of this invention consists essentially of, in % by mass and by both ends inclusive, 0.6% ⁇ C ⁇ 1.60%, 0.10% ⁇ Si ⁇ 1.20%, 0.10 ⁇ Mn ⁇ 0.60%, 5.5% ⁇ Cr ⁇ 13.0%, 0.80% ⁇ Mo+0.5W ⁇ 2.10%, 0.10% ⁇ V ⁇ 0.40%, 0.0002% ⁇ O ⁇ 0.0080%, 0.001% ⁇ Al ⁇ 0.10%, and the balance of Fe and inevitable impurities; having transformation point Ar3 in the range from 750° C.
- This invention has major features described below.
- Hardness after annealing is determined mainly by state of distribution of carbide having a diameter ranging from 0.1 ⁇ m to 3 ⁇ m, with both ends inclusive, on the circle-equivalent basis (referred to as secondary carbide, hereinafter), so that the hardness can be decreased by adjusting the mean circle-equivalent diameter of the carbide to the range from 0.2 ⁇ m to 0.8 ⁇ m, with both ends inclusive.
- This range of the mean circle-equivalent diameter corresponds to the enlargement of the secondary carbide.
- an absolute amount of the secondary carbide produced by the annealing is the same, so that a larger mean circle-equivalent diameter results in a smaller hardness due to scarceness of the secondary carbide having relatively large sizes.
- a smaller mean circle-equivalent diameter results in a larger hardness by virtue of the denseness of the secondary carbide having relatively small sizes. More specifically, adjustment of the mean circle-equivalent diameter of the secondary carbide in the above-described range makes it possible to obtain a Brinell hardness of as low as HB179 to HB235, with both ends inclusive (conventional steels showed a Brinell hardness of as large as HB241 to HB255 or around), and to distinctively improve the efficiency in machining and cold working.
- Size of the secondary carbide is controlled by spherodizing, or keeping the steel heated at a temperature of (Ar3+50° C.) or above and 1,050° C. or below.
- the steel is heated at a temperature (from Ar3+50° C. to a hardening temperature (1,050° C. or around)) higher than the conventional annealing temperature (from Ar3 to Ar3+50° C.) so as to allow more secondary carbides to dissolve into the matrix.
- the reason why the temperature at which the steel is heated is adjusted to a temperature lower than the hardening temperature (1,050° C. or around) is to avoid lowering of the hardness after quench-and-temper.
- the steel is gradually cooled at a cooling rate slower than 60° C./h to as low as 750° C. or below, in order to allow the dissolved secondary carbide to grow into larger grains (gradual cooling method).
- Other known treatment methods include the “repetitive heating-and-gradual-cooling method” in which heating and cooling are repeated at least twice within temperature ranges from 650° C. to transformation point Ar1, and from transformation point Ar3 to 1,050° C.; “prolonged annealing method” in which the steel is kept at a temperature lower than Ar3 for a long period of time; and “isothermal transformation method” in which the steel is kept at a constant temperature during the gradual cooling process in the gradual cooling method.
- any of these methods can successfully control the size of the secondary carbide.
- Low temperature annealing at a temperature of Ar1 or below before the spherodizing annealing makes it possible to reduce variation in the post-anneal hardness after annealing and to obtain still an even lower hardness. It is to be noted that the above-described spherodized annealing will not largely alter the size and population of the coarse carbide (primary carbide) which affects the wear resistance required for applications such as dies and tools.
- Transformation point “Ar3” herein expresses the A3 transformation point (austenization temperature), wherein “r” means cooling (refroidatorium).
- the temperature at which the steel is heated is necessarily set higher than that in the conventional process in view of thoroughly dissolving the secondary carbides into the matrix, and the transformation point of Ar3 is necessarily low enough so as to adjust the temperature to the quenching temperature or below. In other words, it is required that there is a large enough difference between the transformation point of Ar3 and the quenching temperature.
- the steel is therefore necessarily adjusted in the composition thereof so as to make transformation point Ar3 fall within the range of 750° C. to 850° C. If the Ar3 is too high only a small difference from the normal quenching temperature (1,050° C. or around) will result, and consequently fail in raising the annealing temperature thereby resulting in only an insufficient dissolution of the secondary carbide (not so different from the conventional annealing). On the other hand, if the Ar3 is too low, a vastly longer duration time for the depositing and growing of the secondary carbide.
- the annealing temperature herein is determined to a desirable level (Ar3+50° C. to quenching temperature (at around 1,050° C.)), based on results of the measurements of the transformation point Ar3 using an apparatus such as DTA (differential thermal analyzer).
- groups B and C oxide-based ones in particular inclusions (conforming to JIS G0555) are known to decrease the machinability. These inclusions have extremely high hardness of their own, which exceeds the hardness of the matrix. By coming into contact with these inclusions, tool edges can be chipped and the lifetime of tools can be considerably decreased. Both group B and C inclusions become less affective as the contents of which reduce closer to 0, so that it is necessary, for the purpose of obtaining more sufficient machinability than conventional steel, to adjust the steel cleanliness to (dB+dC)60 ⁇ 400 ⁇ 0.05%. This cleanliness level can be obtained by adjusting mainly the contents of O and Al within the range described later.
- C is an essential element for raising the hardness of martensite after quenching.
- the element forms carbide through binding with carbide-forming elements such as Cr, Mo and V, and thereby make the crystal grain more fine.
- the carbide also contributes to the improvement of the wear resistance.
- An addition to an amount of the lower limit or more is necessary in order to realize a hardness after quench and temper of HRC55 or above.
- the element is added to as much as the upper limit or less, because excessive addition results in excessive content of the carbide, which thereby decreases the toughness.
- Si is added as a deoxidizing element. Because the element contributes to the increase in hardness in the high-temperature-temper, it is added to as much as the lower limit or more, so as to obtain the effect. On the other hand, the element is added to as much as the upper limit or less, because excessive addition degrades the hot workability, and the after-quench-and-temper toughness.
- Mn is added as a deoxidizing element. Because the element contributes to the enhancement of the hardenability, and increasing in the hardness and strength, it is added to as much as 0.10% or more. On the other hand, the upper limit of the element is set to 0.60%, because excessive addition degrades the hot workability.
- Mo and W dissolve into the solid matrix to thereby raise the hardenability and to contribute to increase hardness, and forms carbides to which increase the wear resistance.
- the elements also have an effect of raising the anti-softening hardness in quench-and-temper. Addition to as much as the lower limit or more, on the Mo-equivalent basis expressed as Mo(%)+0.5W(%), is necessary for obtaining these effects. On the other hand, the element is added to as much as the upper limit or less, because excessive addition decreases the hot workability, toughness and machinability.
- V forms a stable carbide, and thereby effectively prevents the crystal grains from coarsening.
- the element forms a fine carbide, and thereby contributes to increases in the wear resistance and the hardness. Addition to as much as 0.10% or more is necessary for obtaining these effects.
- the upper limit is set to 0.40%, because excessive addition increases the carbide content, and thereby decreases the machinability and hot workability.
- the elements are constituent elements of group B and C inclusions, and large contents of which can decrease the toughness, so that it is necessary to suppress the contents to as much as the upper limit or less.
- Positive efforts of reducing these elements although depending on balance with the production cost, makes it possible to maintain a high, stable toughness. Excessive lowering of the contents only results in an increase in the production cost and a saturation of influences exerted on the toughness, so that the elements are added to as much as the lower limit or more.
- Transformation Point Ar3 Adjusted to 750° C. to 850° C.
- Transformation point Ar3 adjusted in the above-described range can expand the temperature range ranging from Ar3+50° C., at which spherodizing is effected.
- the quenching temperature (about 1,050° C.), ensures a sufficient range of annealing temperature allowing the secondary carbides to thoroughly dissolve.
- Ar3 can be measured typically by DTA, and defined as being obtained at a cooling rate of 5° C./h or more to 60° C./h, because Ar3 varies depending on conditions of the measurement.
- the mean circle-equivalent diameter of the carbide which belongs to the circle-equivalent diameter range of 0.1 ⁇ m to 3 ⁇ m was observed in the section of the structure obtained after spherodizing a sample that was heated at a temperature of (Ar3+50° C.) or above and 1,050° C. or below, adjusted to 0.25 ⁇ m or more and 0.8 ⁇ m or less.
- the mean circle-equivalent diameter of the carbide is calculated by an image analysis of a polished section of the steel structure. More specifically, a circle-equivalent diameter is calculated for every carbide grain having a circle-equivalent diameter ranging from 0.1 ⁇ m to 3 ⁇ m which can be seen in a magnified field of view under a scanning electron microscope or an optical microscope, and a mean value of which is determined as the mean circle-equivalent diameter. It is necessary that the observation in the magnified field of view is carried out at least in an area of 1 mm 2 or larger, at randomly selected positions excluding the surface and center portions of the material.
- each field contains 20 to 50 carbide grains having a circle-equivalent diameter ranging from 0.1 ⁇ m to 3 ⁇ m.
- the carbide having a diameter ranging from 0.1 ⁇ m to 3 ⁇ m means a carbide (secondary carbide) contributive to the hardness.
- a mean grain size of the carbide belonging this range of less than 0.25 ⁇ m results in a high hardness, and fails in obtaining the effect of increasing the machinability (this applies to the case where the conventional style of annealing was carried out).
- an excessively large mean grain size results in an extremely small number of carbide grains grown during the process of gradual cooling in the annealing, and this makes the regenerative perlite more likely to deposit in the cooling process, and conversely increases the hardness. It is therefore necessary to set the upper limit of the mean circle-equivalent diameter of carbide to 0.8 ⁇ m.
- Adjustment of the Brinell hardness after the spherodizing to HB179 to HB235 makes it possible to obtain the machinability and cold workability superior to those in the prior art. Excessive lowering of the hardness results in a high cost from the industrial point of view, so that a hardness of HB179 or more is enough for the purpose.
- the class B inclusion (mainly alumina and so forth) refers to grains forming an agglomerate discontinuously arrayed in the working direction
- the group C inclusion (such as granular oxide) refers to grains irregularly dispersed without causing viscous deformation. Excessive amounts of these inclusions decreases the machinability, and a desirable level of machinability can be obtained by adjusting the cleanliness (dB+dC)60 ⁇ 400 of the steel with respect to group B and C inclusions, determined by the test method as specified in JIS G0555, of 0.05% or less.
- K value expresses the amount of Cr solubilized in the matrix at an appropriate quenching temperature. Adjustment within the above range results in the hardness obtained after quench-and-temper almost equivalent to the previous, and therefore makes it possible to adjust the amount of deposition of carbides depending on the wear resistance, toughness and machinability required for the cold working die steel. In contrast, if the K value is out of the above range, it results in only an insufficient amount of the secondary carbide which deposits during tempering and contributes to the hardness, and consequently fails in maintaining the hardness necessary for the cold working die steel.
- FIG. 1 shows a relation between the C content and the Cr content. The straight lines ascending from the lower left towards the upper right in the drawing relate to the K value, and the straight lines descending from the upper left towards the lower right in the drawing relate to the L value described later.
- the cold working die steel of this invention can further contain, as steel components, either one of or both of 0.0030% ⁇ N ⁇ 0.0500% and 0.001% ⁇ P ⁇ 0.040%.
- the cold working die steel of this invention can further contain, as steel components, any one of, or two or more of steel components selected from 0.01% ⁇ Cu ⁇ 1.0%, 0.01% ⁇ Ni ⁇ 1.0%, 0.2% ⁇ Co ⁇ 1.0% and 0.0003% ⁇ B ⁇ 0.010%.
- These elements have an effect of increasing the hardenability by dissolving themselves into the matrix. They have also an effect of increasing the toughness by lowering the impact transition temperature, and by consequently preventing the weldability from degrading. Co has an effect of increasing the high temperature strength. Addition to as much as the lower limit or above is preferable in view of obtaining these effects. The elements are added to as much as the upper limit or less, because excessive addition only results in a saturated effect.
- the cold working die steel of this invention can further contain, as steel components, any one of, or two or more of 0.001% ⁇ S ⁇ 0.20%, 0.005% ⁇ Se ⁇ 0.10%, 0.005% ⁇ Te ⁇ 0.10%, 0.0002% ⁇ Ca ⁇ 0.010%, 0.005% ⁇ Pb ⁇ 0.10% and 0.005% ⁇ Bi ⁇ 0.10%.
- S can be added as an element increasing the free cutting property.
- carbide-forming elements such as Cr, Mo and V
- addition to as much as 0.04% or more is preferable in view of obtaining the effect of increasing the free cutting property.
- Excessive addition of the element considerably decreases the toughness, or mechanical properties including surface roughness after discharge processing and cutting, so that the upper limit is preferably adjusted to 0.20%.
- the element is added considering the balance with the mechanical properties.
- the amount of addition of S is set to 0.02% or less, and more preferably to 0.01% or less, considering the balance with the cost for manufacturing.
- the mechanical properties can be satisfied by adjusting the amount of the addition to 0.01% or more and 0.02% or less for the practical operation. This makes it possible to obtain the S content described in the above.
- Se and Te can be added for the purpose of increasing machinability.
- Se and Te can be used as substitutive elements of S in Mn sulfide.
- Ca improves the machinability by forming a protective film on the surface of a tool during cutting, by forming an oxide or by dissolving itself into Mn sulfide.
- Pb and Bi segregate in the grain boundary, to thereby lower the grain boundary strength and to improve the machinability.
- the elements are necessarily added to as much as the lower limits or more in view of obtaining these effects. On the other hand, excessive addition results in degraded mechanical properties, so that the upper limits should be met.
- the cold working die steel of this invention can further contain, as the steel components, any one of, or two or more of 0.01% ⁇ Nb ⁇ 0.12%, 0.005% ⁇ Ta ⁇ 0.10%, 0.005% ⁇ Ti ⁇ 0.10%, 0.005% ⁇ Zr ⁇ 0.10%, 0.005% ⁇ Mg ⁇ 0.10% and 0.005% ⁇ REM ⁇ 0.10%.
- Mg and REM have an effect of increasing the toughness and machinability, through formation of oxides, which contribute to the reduction of the O content and consequently in coarse oxide grains. Addition to as much as the lower limit or above is preferable in view of obtaining these effects. On the other hand, excessive addition results in decreasing in the toughness and weldability, so that the amount of addition is preferably set to the upper limit or less.
- a single species or two or more species of rare earth metals may be used as REM.
- the cold working die steel according to the second aspect may contain, as the steel components, 0.60% ⁇ C ⁇ 0.80%, 0.10% ⁇ Si ⁇ 1.20%, 0.10% ⁇ Mn ⁇ 0.60%, 5.5% ⁇ Cr ⁇ 8.5%, 0.80% ⁇ Mo+0.5W ⁇ 2.10%, 0.10% ⁇ V ⁇ 0.40%, 0.0002% ⁇ Al ⁇ 0.0080%.
- further limitations are added to C, Si, Cr and Mo, out of the steel components according to the first aspect.
- the toughness and fine machining are particularly required to decrease the coarse carbide. More specifically, it is necessary to avoid as much as possible, the formation of coarse carbides mainly composed of M 7 C 3 (where, M represents Cr, Mo or V), by adjusting the contents of C, Si, Cr and Mo within the above-described ranges.
- the amount of coarse carbide corresponds to 0.01 to 5% in % by mass. Assuming now L value as an index expressing the amount of coarse carbide as Cr(mass %)+15.5 ⁇ C(mass %), the amount of coarse carbide corresponds to 14.9 ⁇ (L value) ⁇ 21.0 (see FIG. 1 ).
- the cold working die steel according to the third aspect may contain, as the steel components, 0.90% ⁇ C ⁇ 1.10%, 0.8% ⁇ Si ⁇ 1.20%, 0.10% ⁇ Mn ⁇ 0.60%, 7.0% ⁇ Cr ⁇ 9.0%, 1.50% ⁇ Mo+0.5W ⁇ 2.10%, 0.10% ⁇ V ⁇ 0.40%, 0.0002% ⁇ Al ⁇ 0.0080%.
- further limitations are added to C, Si, Cr and Mo, out of the steel components according to the first aspect.
- the wear resistance and the toughness must be well-balanced, to ensure a certain amount of coarse carbides.
- the coarse carbides mainly composed of M 7 C 3 are formed by adjusting the contents of C, Si, Cr and Mo within the above-described ranges.
- the amount of coarse carbides corresponds from 5 to 10% in % by mass, and to 21.0 ⁇ (L value) ⁇ 27.0 (see FIG. 1 ).
- the cold working die steel according to the fourth aspect may contain, as the steel components, 1.40% ⁇ C ⁇ 1.60%, 0.10% ⁇ Si ⁇ 0.40%, 0.10% ⁇ Mn ⁇ 0.60%, 11.0% ⁇ Cr ⁇ 13.0%, 0.80% ⁇ Mo+0.5W ⁇ 1.20%, 0.10% ⁇ V ⁇ 0.40%, 0.0002% ⁇ Al ⁇ 0.0080%
- further limitations are added to C, Si, Cr and Mo, out of the steel components according to the first aspect.
- FIG. 1 is a drawing expressing relations between C content and Cr content (K value, L value).
- compositions of comparative steels listed in Table 1 those departing from the compositional ranges specified by this invention are indicated by a downward arrow ( ⁇ ) if they came short of the lower limits, by an upward arrow ( ⁇ ) if they exceeded the upper limits.
- the polished surface of each steel was subjected to image analysis and the mean grain size of the carbide was measured.
- the image analysis was made on an image observed under a SEM, wherein a total of 1 mm 2 area was observed at an appropriate magnification ranging from 500 ⁇ to 5,000 ⁇ .
- the circle-equivalent diameters were calculated for all carbide grains having a diameter ranging from 0.1 ⁇ m to 3.0 ⁇ m seen in the field of view, and thereby obtained an average mean value.
- the polished surface herein was etched with a picric acid-ethanol solution to a depth allowing observation of the carbide grains having a diameter of about 0.1 ⁇ m, without causing dropping of the carbide grains.
- a test piece was cut out from each of the manufactured inventive steels and comparative steels, and subjected to the machinability test.
- Cutting width 0.5 mm, 10 mm in height
- Judgment marked with ⁇ if the tool caused no breakage, and marked with x if the tool caused breakage or sparking during the cutting.
- Test pieces measuring 12 ⁇ 18 mm were cut out from each of the inventive steels and the comparative steels, and pressed by a single stroke to 60% height of the test piece using a 600-t hydraulic press machine. Ten pressed test pieces of the individual steels were observed, and the number of test pieces causing breakage was found.
- Hardness was measured using a Rockwell C scale, under varied annealing conditions in the quench-and-temper.
- a 10R-notched Charpy test piece was cut out from each of the manufactured inventive steels and the comparative steels.
- the direction of the test pieces was aligned to the longitudinal direction of the material.
- the test was carried out according to the method described in JIS Z2242. The test was carried out under room temperature.
- comparative steel 1 having a composition departing from the compositional ranges specified by this invention, showed an extremely lowered Ar3 temperature.
- the steel annealed under conventional annealing conditions failed to fully solubilize the carbide into solid, and failed in allowing the carbide to grow larger under gradual cooling, so that the carbide became smaller in size, and the steel became harder.
- the steel was consequently poor in the cold workability, showing cracks in 8 out of ten test pieces.
- Comparative steel 3 having a composition departing from the compositional ranges specified by this invention, showed an extremely lowered Ar3 temperature. Too high a temperature in the quench-and-temper resulted in an extremely lowered hardness, increased ductility of the material, and conversely degraded machinability, although the cold workability was judged as desirable by virtue of a large carbide size and a considerably lowered hardness.
- Comparative steel 4 showed a K value largely departing from the inventive range, despite having a composition within the compositional ranges specified by this invention.
- the steel therefore failed in achieving a maximum hardness of as large as HRC60 or above after annealing by the quench-and-temper, and failed in obtaining a level of hardness required for cold working die steel.
- the low hardness also resulted in a large specific wear.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2005007198A JP2006193790A (ja) | 2005-01-14 | 2005-01-14 | 冷間工具鋼 |
JP2005-007198 | 2005-01-14 |
Publications (1)
Publication Number | Publication Date |
---|---|
US20060157163A1 true US20060157163A1 (en) | 2006-07-20 |
Family
ID=36682651
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US11/332,910 Abandoned US20060157163A1 (en) | 2005-01-14 | 2006-01-17 | Cold working die steel |
Country Status (5)
Country | Link |
---|---|
US (1) | US20060157163A1 (ko) |
JP (1) | JP2006193790A (ko) |
KR (1) | KR20060083142A (ko) |
CN (1) | CN100564569C (ko) |
TW (1) | TW200624570A (ko) |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20100132429A1 (en) * | 2008-01-10 | 2010-06-03 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel Ltd) | Cold-work die steel and dies for cold pressing |
CN101153374B (zh) * | 2006-09-27 | 2010-09-08 | 宝山钢铁股份有限公司 | 一种切纸机刀片用钢及其制造方法 |
US8968495B2 (en) | 2007-03-23 | 2015-03-03 | Dayton Progress Corporation | Methods of thermo-mechanically processing tool steel and tools made from thermo-mechanically processed tool steels |
US9132567B2 (en) | 2007-03-23 | 2015-09-15 | Dayton Progress Corporation | Tools with a thermo-mechanically modified working region and methods of forming such tools |
EP3006601A4 (en) * | 2013-05-30 | 2016-11-02 | Hitachi Metals Ltd | METHOD FOR MANUFACTURING MOLD FOR COLD FORMING USE |
EP2679697A4 (en) * | 2011-02-21 | 2016-11-23 | Hitachi Metals Ltd | METHOD FOR MANUFACTURING COLD FORMING MATRIX |
US9994925B2 (en) | 2015-02-04 | 2018-06-12 | Hitachi Metals, Ltd. | Cold work tool material, cold work tool and method for manufacturing same |
US10407747B2 (en) | 2016-03-18 | 2019-09-10 | Hitachi Metals, Ltd. | Cold working tool material and cold working tool manufacturing method |
CN110938774A (zh) * | 2019-12-17 | 2020-03-31 | 贾宁 | 一种环保炼钢炉炼钢工艺 |
CN114381657A (zh) * | 2020-10-22 | 2022-04-22 | 浙江叶晓针织机械有限公司 | 一种skd11合金材料的制备方法 |
CN115627419A (zh) * | 2022-10-25 | 2023-01-20 | 攀钢集团江油长城特殊钢有限公司 | 一种高强高韧Cr8冷作模具钢及其制备方法 |
Families Citing this family (33)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101563470B (zh) * | 2006-12-27 | 2011-05-11 | 日立金属株式会社 | 工具钢的制造方法 |
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 |
CN101538685B (zh) * | 2008-03-21 | 2011-11-23 | 宝山钢铁股份有限公司 | 一种高强韧性刀片钢及其冶金制造方法 |
CN103403206B (zh) * | 2011-02-21 | 2015-11-25 | 日立金属株式会社 | 切削性优异的冷作工具钢 |
CN102251190B (zh) * | 2011-03-26 | 2013-04-17 | 萍乡市德博科技发展有限公司 | 铬钼镍钛钒涡轮增压器密封环 |
WO2014030619A1 (ja) * | 2012-08-20 | 2014-02-27 | 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 |
KR20140039416A (ko) * | 2012-09-21 | 2014-04-02 | 한국기계연구원 | 뜨임저항성이 우수한 냉간공구강 |
CN102978517B (zh) * | 2012-12-14 | 2015-04-22 | 江苏天工工具有限公司 | 一种冷作模具钢的制备方法 |
CN103173681B (zh) * | 2013-03-16 | 2015-01-07 | 江阴润源机械有限公司 | 一种用skd-11钢材的冷轧钢工作辊及其生产工艺 |
WO2014156487A1 (ja) | 2013-03-29 | 2014-10-02 | 日立金属株式会社 | 金型用鋼素材およびその製造方法、金型用プリハードン鋼材の製造方法、冷間加工用金型の製造方法 |
CN103233187B (zh) * | 2013-05-28 | 2015-02-18 | 滁州迪蒙德模具制造有限公司 | 冷作模具用钢及其生产方法 |
CN103774049B (zh) * | 2014-01-18 | 2015-12-09 | 山西百一机械设备制造有限公司 | 高韧性高耐磨高铬莱氏体冷作模具钢及其制备方法 |
CN103820716B (zh) * | 2014-02-26 | 2016-06-01 | 常熟市长江不锈钢材料有限公司 | 一种9Cr13MoVCo不锈钢带钢及制备方法 |
JP6337524B2 (ja) * | 2014-03-07 | 2018-06-06 | 大同特殊鋼株式会社 | 金型用鋼 |
JP6472174B2 (ja) * | 2014-05-27 | 2019-02-20 | 山陽特殊製鋼株式会社 | 低温焼入れ可能な高硬度高靭性の冷間工具鋼 |
CN105637108B (zh) * | 2014-09-26 | 2017-08-11 | 日立金属株式会社 | 冷作工具材料及冷作工具的制造方法 |
CN104480400B (zh) * | 2014-12-18 | 2016-08-24 | 钢铁研究总院 | 一种c-n-b复合硬化高耐磨冷作模具钢 |
JP6484086B2 (ja) * | 2015-03-31 | 2019-03-13 | 株式会社木村鋳造所 | 工具鋼鋳鋼品の製造方法 |
CN104942879B (zh) * | 2015-07-08 | 2017-03-01 | 安徽华天机械股份有限公司 | 一种平圆刀及其制造方法 |
CN105112791A (zh) * | 2015-09-21 | 2015-12-02 | 无锡清杨机械制造有限公司 | 一种新型金属材料及其制备方法 |
CN106191703A (zh) * | 2016-08-16 | 2016-12-07 | 安徽瑞泰新材料科技有限公司 | 一种高铬耐磨钢球及其制备方法 |
JP6772915B2 (ja) * | 2017-03-20 | 2020-10-21 | 愛知製鋼株式会社 | 冷間工具鋼 |
CN108220808A (zh) * | 2017-11-28 | 2018-06-29 | 昆山邦泰汽车零部件制造有限公司 | 一种制造冲压加工设备冲头的钢 |
CN108251758A (zh) * | 2018-01-15 | 2018-07-06 | 苏州健雄职业技术学院 | 一种高硬高韧耐久刀具钢 |
CN110029283A (zh) * | 2018-06-08 | 2019-07-19 | 中南大学 | 一种Co韧化铸铁及其制造与热处理方法 |
JP7343738B2 (ja) * | 2018-11-15 | 2023-09-13 | 株式会社シザーストリート | 毛髪仕上げコーム及びコーミング方法 |
CN110184540A (zh) * | 2019-06-06 | 2019-08-30 | 南通聚星铸锻有限公司 | 一种电渣锭及其冶炼方法 |
CN110306122B (zh) * | 2019-08-06 | 2021-05-11 | 鄱阳县黑金刚钓具有限责任公司 | 一种新型高强度材料鱼钩 |
CN111235490B (zh) * | 2020-03-12 | 2021-06-11 | 梵肯金属材料(上海)有限公司 | 一种高品质刀具用高合金钢材料 |
CN112011740B (zh) * | 2020-08-31 | 2021-11-02 | 天津钢研海德科技有限公司 | 一种高韧性高硬度模具钢及其制备方法 |
CN113215482B (zh) * | 2021-03-22 | 2022-05-20 | 武汉钜能科技有限责任公司 | 耐磨冷作工具钢 |
JP2023124892A (ja) * | 2022-02-26 | 2023-09-07 | 株式会社シザーストリート | 皮膚炎対処用具及びその使用方法 |
CN116043106B (zh) * | 2022-11-08 | 2023-12-15 | 湖北楠田工模具科技有限公司 | 一种高纯净度高韧性长服役周期冷作模具钢及其制备方法 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4604145A (en) * | 1984-01-13 | 1986-08-05 | Sumitomo Metal Industries, Ltd. | Process for production of steel bar or steel wire having an improved spheroidal structure of cementite |
US6053991A (en) * | 1998-01-06 | 2000-04-25 | Sanyo Special Steel Co., Ltd. | Production of cold working tool steel |
US20030066577A1 (en) * | 2001-03-05 | 2003-04-10 | Kiyohito Ishida, Dokuritsu Gyousei Houjin Sangyo Gijutsu Sougo, Kenkyusho, Katsunari Oikawa | Free-cutting tool steel |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60224754A (ja) * | 1984-04-19 | 1985-11-09 | Daido Steel Co Ltd | 合金工具鋼 |
JPH0717986B2 (ja) * | 1985-03-16 | 1995-03-01 | 大同特殊鋼株式会社 | 合金工具鋼 |
JP2003055743A (ja) * | 2001-08-17 | 2003-02-26 | Daido Steel Co Ltd | 被削性にすぐれた冷間ダイス金型用鋼 |
JP2004169177A (ja) * | 2002-11-06 | 2004-06-17 | Daido Steel Co Ltd | 合金工具鋼及びその製造方法、並びにそれを用いた金型 |
-
2005
- 2005-01-14 JP JP2005007198A patent/JP2006193790A/ja active Pending
- 2005-12-19 TW TW094145049A patent/TW200624570A/zh unknown
-
2006
- 2006-01-11 KR KR1020060003210A patent/KR20060083142A/ko not_active Application Discontinuation
- 2006-01-13 CN CNB2006100008511A patent/CN100564569C/zh not_active Expired - Fee Related
- 2006-01-17 US US11/332,910 patent/US20060157163A1/en not_active Abandoned
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4604145A (en) * | 1984-01-13 | 1986-08-05 | Sumitomo Metal Industries, Ltd. | Process for production of steel bar or steel wire having an improved spheroidal structure of cementite |
US6053991A (en) * | 1998-01-06 | 2000-04-25 | Sanyo Special Steel Co., Ltd. | Production of cold working tool steel |
US20030066577A1 (en) * | 2001-03-05 | 2003-04-10 | Kiyohito Ishida, Dokuritsu Gyousei Houjin Sangyo Gijutsu Sougo, Kenkyusho, Katsunari Oikawa | Free-cutting tool steel |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101153374B (zh) * | 2006-09-27 | 2010-09-08 | 宝山钢铁股份有限公司 | 一种切纸机刀片用钢及其制造方法 |
US8968495B2 (en) | 2007-03-23 | 2015-03-03 | Dayton Progress Corporation | Methods of thermo-mechanically processing tool steel and tools made from thermo-mechanically processed tool steels |
US9132567B2 (en) | 2007-03-23 | 2015-09-15 | Dayton Progress Corporation | Tools with a thermo-mechanically modified working region and methods of forming such tools |
US20100132429A1 (en) * | 2008-01-10 | 2010-06-03 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel Ltd) | Cold-work die steel and dies for cold pressing |
EP2679697A4 (en) * | 2011-02-21 | 2016-11-23 | Hitachi Metals Ltd | METHOD FOR MANUFACTURING COLD FORMING MATRIX |
EP3006601A4 (en) * | 2013-05-30 | 2016-11-02 | Hitachi Metals Ltd | METHOD FOR MANUFACTURING MOLD FOR COLD FORMING USE |
US9994925B2 (en) | 2015-02-04 | 2018-06-12 | Hitachi Metals, Ltd. | Cold work tool material, cold work tool and method for manufacturing same |
US10407747B2 (en) | 2016-03-18 | 2019-09-10 | Hitachi Metals, Ltd. | Cold working tool material and cold working tool manufacturing method |
CN110938774A (zh) * | 2019-12-17 | 2020-03-31 | 贾宁 | 一种环保炼钢炉炼钢工艺 |
CN114381657A (zh) * | 2020-10-22 | 2022-04-22 | 浙江叶晓针织机械有限公司 | 一种skd11合金材料的制备方法 |
CN115627419A (zh) * | 2022-10-25 | 2023-01-20 | 攀钢集团江油长城特殊钢有限公司 | 一种高强高韧Cr8冷作模具钢及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
KR20060083142A (ko) | 2006-07-20 |
CN1811004A (zh) | 2006-08-02 |
CN100564569C (zh) | 2009-12-02 |
TW200624570A (en) | 2006-07-16 |
JP2006193790A (ja) | 2006-07-27 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US20060157163A1 (en) | Cold working die steel | |
US20050252580A1 (en) | Cold work tool steel | |
EP2003220B1 (en) | Steel plate having excellent fine blanking processability and method for manufacture thereof | |
KR20100135206A (ko) | 열간가공 공구강 및 이를 이용한 철강제품 | |
EP1783238A2 (en) | High strength steel for dies with excellent machinability | |
KR20100135205A (ko) | 열간가공 공구강 및 이를 이용한 철강제품 | |
JP2007009321A (ja) | プラスチック成形金型用鋼 | |
US20080035296A1 (en) | Process for producing cast steel billet or steel ingot of titanium-added case hardening steel | |
JP2007197746A (ja) | 工具鋼 | |
JP4964063B2 (ja) | 冷間鍛造性および結晶粒粗大化防止特性に優れた肌焼鋼およびそれから得られる機械部品 | |
JP2009013439A (ja) | 高靭性高速度工具鋼 | |
JP2008189982A (ja) | 工具鋼 | |
US6663726B2 (en) | High-hardness prehardened steel for cold working with excellent machinability, die made of the same for cold working, and method of working the same | |
EP2154260B1 (en) | Free-cutting alloy tool steel | |
KR100511652B1 (ko) | 단조성과 피삭성이 우수한 강 | |
JP2005226150A (ja) | 工具鋼の焼きなまし方法、及び工具鋼の焼きなまし材の製造方法、工具鋼の焼きなまし材、並びにそれを用いた工具鋼、工具 | |
EP0930374A1 (en) | Production of cold working tool steel | |
EP3199656B1 (en) | Cold work tool material and method for manufacturing cold work tool | |
JP2014025103A (ja) | 熱間工具鋼 | |
EP1072691B1 (en) | Tool steel with excellent workability, machinability and heat treatment characteristics, and die using same | |
JP2005336553A (ja) | 熱間工具鋼 | |
EP1381702B1 (en) | Steel article | |
JP5597999B2 (ja) | 被削性に優れた冷間工具鋼 | |
JP4322239B2 (ja) | 冷間工具鋼及びその製造方法 | |
JP7214313B2 (ja) | 高い耐摩耗性を有する高靭性の冷間工具鋼 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: DAIDO STEEL CO., LTD., JAPAN Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:SHIMIZU, TAKAYUKI;IKEUCHI, YASUTAKA;FUJII, TOSHIMITSU;REEL/FRAME:017483/0410;SIGNING DATES FROM 20051201 TO 20051208 |
|
STCB | Information on status: application discontinuation |
Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION |