Patent Application
20140013915
The present invention relates to a steel plate for use for band-shaped die-cutting blades for cutting cardboards, paperboards, resin sheets, leathers and the like, and to such a band-shaped die-cutting blade.
The above-mentioned band-shaped die-cutting blade is also referred to as a term of Thomson blade, rule, die or the like, and is so designed as to have a tapered blade edge formed on one side edge of a band-shaped thin plate of a steel material. When such a band-shaped die-cutting blade is used, a plywood plate or the like is previously processed with a laser or the like to form thereon a groove having a predetermined cutting form, and the other side edge not having the blade edge of the band-shaped die-cutting blade is inlaid into the groove to produce a cutting die referred to as “a die mold”. In this case, the band-shaped die-cutting blade is bent in a predetermined form so as to be inlaid into the groove. The depth of the groove is smaller than the width of the band-shaped die-cutting blade, and therefore the blade chip protrudes from the surface of the plywood plate and an elastic block that is a little thicker than the protruding height of the blade chip is stuck to the periphery of the blade. With that, the material to be cut is pressed against the die mold and cut whereby the piece that has been cut in a predetermined shape is pushed back owing to the repulsive force of the elastic block and can be taken out with ease.
The band-shaped die-cutting blade is required to satisfy the characteristic of capable of being readily bent in a small bending radius in producing the die mold, or that is, required to be excellent in “bendability”, in addition to the requirement thereof that is excellent in “sharpness” and “durability” as a cutting knife.
Heretofore, in general, it is said that for realizing excellent “sharpness” the blade edge must be hard and the whole extent of the sharpened part must be highly rigid, and for securing “durability”, it is said that abrasion resistance of the blade edge and therearound must be high. Consequently, there have been employed a method of providing a hard metallographic structure that comprises mainly bainite or tempered martensite through thermal refining treatment (isothermal transformation treatment, quenching/tempering treatment), and a method of more remarkably hardening the blade edge through induction hardening treatment.
On the other hand, for securing “bendability”, there has been employed a method of decarburizing the surface layer part of a steel plate to thereby form a surface layer having a reduced C content (decarburized surface layer). The decarburized surface layer still maintains the structure condition of a ferrite single phase even after the material has been subjected to thermal refining treatment such as quenching/tempering or the like treatment, and owing to the decarburized surface layer, the steel plate can be prevented from being cracked when bent in a predetermined shape.
As the steel type capable of being hardened through such thermal refining treatment, or capable of being noticeably hardened at the blade edge through induction hardening treatment, or capable of being processed to form the decarburized surface layer thereon, for example, there may be mentioned S55C, SAE1050, SAE1055 and the like defined in Japanese Industrial Standard, JIS. Steels of those types can be given a hardness of at least 280 HV or even at least 300 HV and a suitable degree of toughness through isothermal transformation or tempering, and can further be given a hardness of at least 500 HV through induction hardening at blade edges. In addition, the decarburized surface layer can be formed through heat treatment in a suitably controlled atmosphere.
Recently for the reason of environmental concerns, cardboard is being used as a packaging/cushioning material in place of foamed polystyrene for home appliances and others, and the design of packages is being improved. Further, it has become possible to rapidly and easily design cushioning materials by computer. Consequently, it has become necessary to cut and work a large variety of and much complicated shapes than ever before, and band-shaped die-cutting blades have become used for much severer bending operation. In such a case, a band-shaped die-cutting blade having a decarburized surface layer formed thereon suffers from a problem in that the sharpened part thereof is cracked rather than the body part thereof. The sharpened part of the blade does not have a decarburized surface layer, and therefore in use for severe bending operation, the “bendability” of the sharpened part thereof is important.
So as shown in PTL 1, there has been developed a technique of providing a structure that contains a given amount of a spherical carbide to thereby significantly enhance the “bendability” of the blade edge part while securing the “durability” of the blade.
PTL 1: Japanese Patent 4152225
According to the technique of PTL 1, it has become possible to provide a band-shaped die-cutting blade capable of satisfying the recent requirement for severe bending operation. These days, however, the requirement for band-shaped die-cutting blades has become much severer, and those having high “durability” that are resistant to longer-term use than before have become desired.
The present invention is to provide a band-shaped die-cutting blade having good “bendability” and having further improved “durability”.
It has been clarified that the above-mentioned object can be attained by using, as the material for the blade, a steel plate that contains Nb and therefore has a structure with a Nb-containing carbide dispersed therein except in the surface layer part of the plate.
Specifically, the present invention provides a steel plate for band-shaped die-cutting blades having excellent durability, wherein the region having a depth of not more than 200 μm from the surface on both sides of the steel plate is referred to as “surface layer part” and the region inner than the surface layer part in the plate thickness direction is referred to as “base part”, and wherein:
The base part may have a metallographic structure which comprises bainite or tempered martensite and in which a spherical carbide constituted of cementite is present in the bainite or tempered martensite in an amount of 1.0 vol % or more and a Nb-containing carbide having an equivalent-circle diameter of 0.5 μm or more is present at an existential density of 10.0 or more grains per 900 μm2, and the hardness thereof may be controlled to be from 265 to 450 HV. In this case, in the 15-μm-thick surface layer region, the existential density of the Nb-containing carbide having an equivalent-circle diameter of 0.5 μm or more may be reduced to from 0 to 5.0 grains per 900 μm2.
Here, the Nb-containing carbide mainly comprises a Nb carbide and can be differentiated from cementite through EDX or the like analysis. The amount of the spherical carbide constituted of cementite and the existential density of the Nb-containing carbide can be determined through image analysis of microscopic image of the cross section parallel to the plate thickness direction of the steel plate. The equivalent-circle diameter corresponds to the diameter of the circle that is presumed to have the same area as the grain appearing in the cross section being analyzed. The existential density of the Nb-containing carbide is determined as follows: A region of 4500 μm2 (900 μm2×5 fields of view) or more is observed, and of the Nb-containing carbide grains existing in the region, the total number of the grains each having the above-mentioned predetermined equivalent-circle diameter (0.5 μm or more, or 1.0 μm or more) is counted, and the value is converted into the density of the grains per 900 μm2. In the 15-μm-thick surface layer region, a rectangular region having a length of 15 μm as one side in the plate thickness direction and having an area of 15×60 μm (=900 μm2) may be observed and analyzed in at least 5 fields of view. Regarding the Nb-containing carbide lying across the boundaries of the observing regions, the grain of which a half or more of the area exists in the observing region is counted to be one grain.
“Ferrite single-phase structure” of the surface layer part means a structure in which no metallographic phase to be formed through transformation of bainite, martensite or the like exists and in which the matrix (metal base) is a ferrite single phase.
One specific example of the chemical composition of the base part comprises, as % by mass, 0.40 to 0.80% C, 0.05 to 0.50% Si, 0.14 to 2.0% Mn, 0.002 to 0.020% P, 0.0005 to 0.020% S, 0.01 to 1.00% Cr, 0.10 to 0.50% Nb, 0 to 0.50% Mo, 0 to 0.50% V, 0 to 2.0% Ni, 0 to 0.005%B, and a balance of Fe and inevitable impurities.
The thickness of the steel plate is, for example, from 0.4 to 1.5 mm.
Also in the invention, there is provided a band-shaped die-cutting blade having, at the side edge part of a band-shaped material constituted of the above-mentioned steel plate, a sharpened part having a tapered form. The blade edge may be constituted of a base part controlled to have a hardness of from 265 to 450 HV or from 300 to 450 HV, but the cutting blade having a quenched blade edge part to be formed by quenching the base part so as to have a hardness of at least 500 HV is more effective in point of the sharpness thereof.
According to the invention, it has become possible to provide a band-shaped die-cutting blade having good bendability and especially having high durability. The die-cutting blade has a Nb-containing carbide at a suitable density in the base part thereof and therefore the sharpened part thereof is excellent in abrasion resistance, and consequently, the die-cutting blade maintains the original sharpness and cutting accuracy thereof for a long period of time. The life of the die-cutting blade having a induction hardening blade edge is about 2 times that of a conventional ordinary high-frequency quenched die-cutting blade not utilizing the abrasion resistance-improving effect of a Nb-containing carbide. Even though not quenched at high frequency, the die-cutting blade of the invention has a life of about 1.5 times that of the conventional one, and therefore by omitting the high-frequency quenching step, the production cost in the invention can be reduced.
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The chemical composition of the base part is directly reflected by the chemical composition of steel in production thereof by smelting. Unless otherwise specifically indicated hereinunder, “%” in expressing chemical composition means “% by mass”.
C is an important element for securing the strength of a steel material. In use for band-shaped die-cutting blades, the hardness of the base part must be at least 265 HV, and in some uses, the hardness may be required to be at least 300 HV. In case where the blade edge is quenched, the hardness thereof may be required to be at least 500 HV. Taking these into consideration, steel that contains at least 0.4% C is used here. However, when the C content is more than 0.8%, then the toughness of bainite or tempered martensite may lower and the bendability may degrade; and therefore in the invention, steel having 0.4 to 0.8% C is used.
Nb is an important element for forming a hard Nb-containing carbide that comprises mainly NbC. The Nb-containing carbide dispersed in the base part at a suitable density therein is extremely effective for improving the abrasion resistance of the part. In addition, Nb has an effect of refining the prior austenite grain size in the bainite structure or the tempered martensite structure and is therefore effective for preventing the sharpened part from being cracked in bending. As a result of various investigations, the Nb content must be at least 0.10% for sufficiently exhibiting the above-mentioned effects. However, the existence of too much Nb may be a cause of lowering the bendability, and therefore the Nb content is at most 0.50%.
The other steel components than C and Nb may be controlled within the range to provide the metallographic structure to be mentioned below without detracting the bendability of the steel plate. For example, there are exemplified the following steel components.
Si is an element effective for deoxidization of steel, and the content thereof is preferably from 0.05 to 0.50%.
Mn and Cr are effective for improving the quenchability of steel, and are effective for forming a uniform bainite structure or tempered martensite structure. Preferably, the Mn content is from 0.14 to 2.0%, and the Cr content is from 0.01 to 1.00%. More preferably, the Mn content is at least 0.20%.
P and S may lower the toughness of steel and their content is preferably smaller; however, too excessive dephosphorization and desulfurization is unfavorable as increasing the load in steel making. The P content may be from 0.002 to 0.020%, and the S content may be from 0.0005 to 0.020%.
In addition, if desired, one or more of at most 0.50% of Mo, at most 0.50% of V, at most 2.0% of Ni and at most 0.005% of B may be incorporated in the steel plate.
The metallographic structure of the base part to be employed here mainly comprises bainite or tempered martensite for securing the basic characteristics of hardness and abrasion resistance of blades. Preferably, ferrite or pearlite structure does not exist in the part. Whether the part could have a bainite structure or a tempered martensite structure may be determined by the history of thermal treatment. In other words, the former is formed through isothermal transformation treatment in the cooling step from an austenite region; while the latter is formed through quenching treatment from an austenite region to give a martensite structure followed by tempering treatment of the martensite structure. For use for band-shaped die-cutting blades, the hardness of the base part is preferably controlled to be from 265 to 450 HV, more preferably from 300 to 450 HV.
For improving the bendability of the sharpened part in which the base part is exposed out, herein provided is a structure state in which the above-mentioned bainite structure or tempered martensite structure is the base and in which a spherical carbide constituted of cementite is dispersed in the base. As a result of various investigations, when such a spherical carbide exists in the base part in an amount of at least 1.0 vol %, then the bendability of the part is significantly improved. It is considered that the spherical carbide distributed in the base part would cause, when undergone bending deformation, a microscopic yielding by which the local stress concentration of the matrix to lead to cracking could be evaded and the bendability could be thereby improved. Preferably, the grain size (equivalent-circle diameter) of the spherical carbide is from 0.2 to 4.0 μm.
The base part is exposed out of the surface in the sharpened part of the blade, and is readily damaged by abrasion (see
A decarburized surface layer is formed on the surface on both sides of the steel plate. The decarburized surface layer is a region in which the carbon concentration is reduced through decarburization annealing and in which there is formed no transformed phase of bainite or martensite after thermal refining treatment but the matrix is a ferrite single phase. The decarburized surface layer is soft and ductile, and therefore, when bent after the steel plate is worked into a band-shaped die-cutting blade, the layer exhibits the function of preventing the surface cracking in the body part. The body part is thick and therefore can hardly secure sufficient bendability according to the bendability improving method of dispersing a spherical carbide therein, and consequently, the formation of the decarburized layer is necessary. As a result of various investigations, the thickness of the decarburized layer must be at least 5 μm. In general, the thickness may fall within a range of from 5 to 20 μm.
[Nb-Containing Carbide in 15-μm-thick Surface Layer Region]
On the other hand, it has been known that the Nb-containing carbide existing in the surface layer part causes degradation of the bendability of the part. Though not always clear, the reason behind it would be because of the extremely large hardness difference between the decarburized surface layer and the Nb-containing carbide. It is important that, in the surface layer part, especially in the region thereof nearer to the surface, a Nb-containing carbide exists as little as possible for keeping good bendability of the decarburized surface layer. As a result of detailed investigations, in case where the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 1.0 μm in the base part is controlled to be at least 10.0 grains per 900 μm2, good bendability can be secured so far as the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 1.0 μm in the 15-μm-thick surface layer region is controlled to be from 0 to 5.0 grains per 900 μm2. The Nb-containing carbide existing in the region nearer to the center part of the plate thickness than that 15-μm-thick surface layer region does not have any significant influence on the bendability of the body part. In case where the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 0.5 μm in the base part is controlled to be at least 10.0 grains per 900 μm2, good bendability can be secured so far as the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 0.5 μm in the 15-μm-thick surface layer region is controlled to be from 0 to 5.0 grains per 900 μm2.
For reducing the existential density of the Nb-containing carbide in the 15-μm-thick surface layer region, it is effective that the surface layer part of the steel plate is derived from the surface layer part to a depth of around 20 mm of a slab (for example, continuously-cast slab) (the part solidified at a high solidification rate). The cooling rate in solidification is large in the area around the surface layer part of a slab, and therefore the network of the eutectic carbide in the solidified structure is smaller than in the internal region of the slab. By utilizing the difference in the carbide distribution between the regions in the slab, the existential density of the Nb-containing carbide in the 15-μm-thick surface layer region can be made smaller than in the base part. On the contrary, in case where the surface layer part of the steel plate is derived from the part having a large eutectic carbide network inside the slab, a structure state where the coarse eutectic carbide network may be broken or cut through hot rolling or cold rolling is formed in the surface layer part of the steel plate and, as a result, the existential density of the Nb-containing carbide in the 15-μm-thick surface layer region could not be sufficiently reduced.
For obtaining the steel plate of the invention, a decarburization annealing step and a thermal refining treatment step are necessary. Concretely, the following process is exemplified.
Steelmaking→hot rolling→cold rolling→decarburization annealing→cold rolling→thermal refining treatment
Here the steel material to be hot-rolled is preferably one in which the 20-mm-thick surface layer region of a slab appears on the surface thereof. When a slab from which the surface layer part was removed excessively is used, then the slab shall be hot-rolled in a state where the above-mentioned coarse eutectic carbide network is kept appearing around the surface of the slab, and if so, it would be difficult to reduce the existential density of the Nb-containing carbide in the 15-μm-thick surface layer region.
Preferably, the final plate thickness is from 0.4 to 1.5 mm.
The decarburization annealing may be attained through thermal treatment of, for example, exposing the surface of the steel plate to a gaseous atmosphere of 75% H2+25% N2+H2O at 700° C. having a controlled dew point, for from 3 to 10 hours.
For the thermal refining treatment, for example, the following condition may be exemplified.
In a case of giving a bainite structure:
860° C.×120 sec→rapid cooling→400° C.×480 sec→air cooling to room temperature
In a case of giving a tempered martensite structure:
860° C.×120 sec→rapid cooling to about 60° C.→500° C.×180 sec→air cooling to room temperature
In the thermal refining treatment of these cases, when the austenization temperature is too high or when the austenization time is too long, then it would be difficult to disperse a spherical carbide in an amount of 1.0 vol % or more.
After the thermal refining treatment, the steel plate having the above-mentioned controlled structure state is slit into a predetermined width, and the side edge thereof is sharpened to be a sharpened part having a tapered form, thereby giving a band-shaped die-cutting blade. If desired, the blade edge is quenched at high frequency thereby giving a band-shaped die-cutting blade having much more excellent durability.
Steel shown in Table 1 was produced, and the obtained slab was heated at 1250° C. for 1 hour, and then hot-rolled at a finishing rolling temperature of 850° C. and a coiling temperature 550° C. to give a hot-rolled steel plate having a thickness of 3 mm. Some samples (No. 4 in Table 2) were hot-rolled in a state with a part, in which the network of the eutectic carbide in the solidified structure was large, kept appearing on the surface thereof, and therefore of those samples, the 20-mm-thick surface layer part of the slab was cut off and the resulting steel material was hot-rolled. Thus obtained, the hot-rolled steel plate was cold-rolled to have a thickness of 2.2 mm, then decarburized and annealed, further cold-rolled to have a thickness of 0.7 mm, and thereafter treated for quenching/tempering or isothermal transformation in a continuous annealing furnace to give a sample material.
The heat treatment condition was as follows.
The surface of the steel plate was exposed to a gaseous atmosphere of 75% H2+25% N2+H2O at 700° C. having a controlled dew point, for 5 hours.
Kept at 780 to 980° C. for 30 to 600 seconds→rapidly cooled in a molten bismuth bath kept at 320 to 480° C.→kept at 320 to 480° C. for 60 to 600 seconds→air-cooled to room temperature.
Kept at 780 to 980° C. for 30 to 600 seconds→rapidly cooled in a quenching liquid at 60° C.→kept at 400° C. for 300 seconds→air-cooled to room temperature.
0.21
—
—
0.87
0.56
The cross section of each sample material, cut in the plate thickness direction thereof, was observed to determine the thickness of the decarburized surface layer (mean thickness of the area of which the matrix is a ferrite single phase), the metallographic structure of the base part, the areal ratio (vol %) of the spherical carbide constituted of cementite in the base part, and the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 1.0 μm in the base part and in the 15-μm-thick surface layer region. Whether the carbide could be a Nb-containing carbide was confirmed through EDX analysis. The amount of the spherical carbide and the equivalent-circle diameter of the Nb-containing carbide were determined through image analysis. The existential ratio of the Nb-containing carbide was computed by analyzing a region of 4500 μm2 both in the base part and in the 15-μm-thick surface layer region to thereby determine the density thereof per 900 μm2. In the 15-μm-thick surface layer region of those, five rectangular visual fields of 15×60 μm (=900 μm2) each having a 15-μm-long side in the thickness direction were analyzed.
Here, the steel d in Table 1 has a small C content and therefore could not have a sufficient hardness suitable to die-cutting blades, and consequently, this was excluded from investigation objects except for the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 1.0 μm in the base part and in the 15-μm-thick surface layer region.
The surface part to a depth of at least 200 μm was cut off to leave the base part alone. From this, an analysis sample was collected and analyzed for the e chemical composition of the base part. As a result, the data of every steel well corresponded to the analysis values of the ingot sample shown in Table 1. Accordingly, it may be said that the analysis values in Table 1 can be taken as the chemical composition of the base part, directly as they are.
A rectangular test piece having a length of 100 mm and a width of 25 mm was cut out of each sample material in such a manner that the rolling direction could be the lengthwise direction thereof. One side edge of the test piece was sharpened to be a sharpened part, thereby producing a die-cutting blade sample having a tool angle of 45°. The thickness of the body part was 0.7 mm.
The sharpened sample was bent at a bending angle of 120° with a punch having a tip radius of 0.25 mm, whereupon the bendability of both the body part and the sharpened part was evaluated. The evaluation criteria for both the body part and the sharpened part are as follows, and the samples given an evaluation score of 4 or more were approved as good.
Evaluation score 5: Neither cracking nor surface roughening was seen.
Evaluation score 4: Cracking was not seen, but surface roughening was seen.
Evaluation score 3: Fine cracks were seen.
Evaluation score 2: Fine cracks connecting in the width direction were seen.
Evaluation score 1: The sample was broken.
From the samples that had been approved as good in point of the bendability thereof, a band-shaped die-cutting blade having the same blade edge shape as in the above was produced and the blade edge thereof was quenched at high frequency, then bent to a square die-cutting shape, and this was inlaid into a die mold formed of a plywood plate thereby producing a die-cutting blade. Using the square die-cutting blade, papers for cutting test were cut under a predetermined load and at a predetermined pushing rate, whereupon the number of the papers cut under the condition under which a practicably sufficient cutting accuracy and a good operability level could be maintained was counted under predetermined standards. The results were compared with the same test results with a conventional band-shaped die-cutting blade formed of S55C-corresponding steel (no Nb added) defined in JIS. The samples of which the durability was considered to be obviously higher than that of the S55C-corresponding steel were evaluated as “O” (durability: good), while the samples of which the durability was considered to be comparable to that of the S55C-corresponding steel were evaluated as “X” (durability: average). The samples with the evaluation of “O” were approved as good.
The results are shown in Table 2.
As known from Table 2, the steel plates of the present invention had a predetermined metallographic structure state both in the surface layer part and in the base part; and when these are used, it is possible to realize band-shaped die-cutting blades excellent in bendability and durability.
As opposed to these, for the comparative sample of No. 4, a steel plate in which the part having a large eutectic carbide network in the solidified structure appeared on the surface thereof was hot rolled. Therefore in this, a large quantity of the Nb-containing carbide that would be derived from the coarse eutectic carbide network as broken and cut through hot-rolling and cold-rolling existed in the surface layer part of the obtained steel plate, and the bendability of the comparative sample was poor. In No. 5, the C content was low and therefore the blade edge could not be given a hardness of 500 HV through induction hardening. For Nos. 6 and 8, used was a Nb-free steel, and in these, the sharpened part could not enjoy the abrasion resistance-improving effect to be given by a Nb-containing carbide, or that is, the durability of these samples was not improved. For No. 12, used was a steel having a too high C content, and therefore the bendability of the sample was poor. For No. 13, used was a steel having a too high Nb content, and in this therefore, the amount of the Nb-containing carbide was large and the bendability of the sample was poor.
Here the existential density of the Nb-containing carbide in the base part was determined by counting the number of the grains having an equivalent-circle diameter of at least 0.5 μm, and the samples were tested in the same manner as in Example 1. The steel shown in Table 1 and Table 3 was produced, then cold-rolled to have a thickness of 0.7 mm under the same condition as in Example 1, and thereafter treated for quenching/tempering or isothermal transformation in a continuous annealing furnace to give a sample material. The condition for the quenching/tempering treatment or the isothermal transformation treatment was the same as in Example 1.
The cross section of each sample material, cut in the plate thickness direction thereof, was observed to determine the thickness of the decarburized surface layer (mean thickness of the area of which the matrix is a ferrite single phase), the metallographic structure of the base part, the areal ratio (vol %) of the spherical carbide constituted of cementite in the base part, and the existential density of the Nb-containing carbide in the base part and in the 15-μm-thick surface layer region. For the existential density of the Nb-containing carbide, the number of the grains having an equivalent-circle diameter of at least 0.5 μm was counted in the base part, while the number of the grains having an equivalent-circle diameter of at least 1.0 μm was counted in the 15-μm-thick surface layer region. The measurement method is the same as in Example 1.
The bendability was evaluated according to the same method as in Example 1.
From the samples that had been approved as good in point of the bendability thereof, a band-shaped die-cutting blade having the same blade edge shape as in the above was produced. Here, some samples were quenched at high frequency but some others were not. All these samples were tested according to the same test method as in Example 1. Thus tested, the data of the samples were compared with the same test results with a conventional band-shaped die-cutting blade formed of S55C-corresponding steel (no Nb added) defined in JIS.
The samples of which the durability was considered to be at least about 2 times that of the S55C-corresponding steel were evaluated as “OO” (durability: excellent); the samples of which the durability was considered to be at least about 1.5 times that of the S55C-corresponding steel were evaluated as “O” (durability: good); and the samples of which the durability was considered to be comparable to that of the S55C-corresponding steel were evaluated as “X” (durability: average). Of those that had been quenched at high frequency, the samples with the evaluation of “OO” were approved as good, while of those that had not been quenched at high frequency, the samples with the evaluation of “O” were approved as good.
The results are shown in Table 4.
As known from Table 4, using the steel plate of the invention in which the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 0.5 μm in the surface layer part was reduced to from 0 to 5.0 grains per 900 μm2 and the existential density of the Nb-containing carbide having an equivalent-circle diameter of at least 0.5 μm in the base part is from at least 10.0 grains per 900μm2, it is possible to realize a band-shaped die-cutting blade having good bendability and durability. Regarding the durability, the invention realizes better durability than that of conventional materials even in the absence of induction hardening at the blade edge.
As opposed to these, for the comparative sample of No. 34, a steel plate in which the part having a large eutectic carbide network in the solidified structure appeared on the surface thereof was hot rolled. Therefore in this, a large quantity of the Nb-containing carbide that would be derived from the coarse eutectic carbide network as broken and cut through hot-rolling and cold-rolling existed in the surface layer part of the obtained steel plate, and the bendability of the comparative sample was poor. In No. 35, the C content was low and therefore the sample could not realize good durability irrespective of the presence or absence of induction hardening at the blade edge. For Nos. 36 and 38, used was a Nb-free steel, and in these, the sharpened part could not enjoy the abrasion resistance-improving effect to be given by a Nb-containing carbide, or that is, the durability of these samples was not improved. For No. 42, used was a steel having a too high C content, and therefore the bendability of the sample was poor. For No. 43, used was a steel having a too high Nb content, and in this therefore, the amount of the Nb-containing carbide was large and the bendability of the sample was poor.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-068990 | Mar 2011 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2012/057631 | 3/23/2012 | WO | 00 | 9/25/2013 |
