WO2017104220A1 - 高速度工具鋼、工具用材料、および、工具用材料の製造方法 - Google Patents
高速度工具鋼、工具用材料、および、工具用材料の製造方法 Download PDFInfo
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- 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
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- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- 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
- C21D6/007—Heat treatment of ferrous alloys containing Co
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- 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
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- 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
- C21D6/02—Hardening by precipitation
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/24—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for saw blades
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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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
Definitions
- the present invention relates to a high-speed tool steel, a tool material using the high-speed tool steel, and a method for manufacturing the tool material.
- the saw blade is generally manufactured by the following process. First, molten steel adjusted to a predetermined component composition is cast into a material such as a steel ingot or billet, or a powder obtained from this molten steel by an atomizing method or the like is subjected to hot high pressure molding as a material, Hot working is performed, and after that, through various processing and heat treatment, a “blade material” having a shape such as a flat wire is produced. Then, the blade tip material is welded to the body using electron beam welding or laser welding, blade cutting is performed, quenching and tempering is performed, and the finished product is a saw blade.
- plastic working tools represented by dies and the like have been used for plastic working of metal materials such as steel. These plastic working tools are also manufactured from a “plastic working tool material” obtained by hot working the above-mentioned raw material. In general, the plastic working tool is obtained by machining the plastic working tool material into various tool shapes and then quenching and tempering. Manufactured by performing a surface treatment.
- High-speed tool steel of SKH59 (equivalent to AISI standard steel type M42), which is a JIS standard steel grade, is widely applied to the material of “tool material” such as the above-mentioned blade edge material and plastic working tool material.
- SKH59 is a material excellent in red heat hardness and excellent in durability at the time of cutting or plastic working, and has excellent characteristics as a material for the above-mentioned tool material.
- Patent Document 1 discloses an invention of a band saw blade that employs SKH59 as a material for a cutting edge material and a manufacturing method thereof.
- a cutting tool having a cutting edge made of SKH59 is excellent in cutting durability.
- the plastic working tool manufactured by SKH59 is also excellent in durability.
- early chipping may occur at the cutting edge of the cutting tool, and early chipping, cracking, or breakage may occur on the shape surface of the plastic processing tool (that is, the surface on which metal material is plastically processed). was there.
- the “tool material” used for the cutting tool and the plastic working tool is low in ductility of the raw material when hot working is performed on the raw material such as the steel ingot or steel slab in the manufacturing process ( In some cases, it is difficult to stretch the film to a predetermined size.
- An object of the present invention is to provide a high-speed tool steel excellent in hot workability and excellent in damage resistance when finished in various tools, a tool material using the same, and a method for producing the tool material Is to provide.
- the present invention is the above-described high-speed tool steel, and the maximum diameter of carbides contained in the cross-sectional structure is an estimated maximum predicted value ⁇ (Area max ) calculated by an extreme value statistical method, and is 32.0 ⁇ m or less. It is a tool material.
- the mass ratio is C: 0.9 to 1.2%, Si: 0.1 to 1.0%, Mn: 1.0% or less, Cr: 3.0 to 5.0% , W: 2.1 to 3.5%, Mo: 9.0 to 10.0%, V: 0.9 to 1.2%, Co: 5.0 to 10.0%, N: 0.020 % Or less, a high-speed tool steel consisting of the balance Fe and impurities is cast into a steel ingot, and a method for producing a tool material for hot working on the steel ingot, The relationship between the contents of C, Si, W, Mo, V, and Co contained in the steel ingot of the high-speed tool steel is as follows: -1.5 ⁇ M value ⁇ This is a method for producing a tool material satisfying 1.5.
- the hot workability of high-speed tool steel can be improved.
- the tool material which consists of this high-speed tool steel can be used for the cutting edge and plastic working tool of various cutting tools, and the early damage during use of these tools can be suppressed.
- One of the causes of tool damage such as chipping and cracking on the cutting edge of a cutting tool or the shape surface of a plastic working tool in use is a coarse carbide contained in the structure of the tool material. That is, if the structure of the tool material contains a large amount of extremely coarse carbides, the extremely coarse carbides remain in the product structure after quenching and tempering, and the toughness of the blade edge and the shape surface is reduced. And the stress (fracture stress) required for destruction of the cutting edge and shape surface in use falls, and the breakage which started from coarse carbide occurs. Therefore, reducing the carbide size in the structure of the tool material is effective in suppressing the tool damage.
- the component composition of SKH59 capable of realizing high hardness is an alloy design that forms a large amount of carbide in the structure.
- massive eutectic carbides that are extremely coarse are easily formed in the cast structure at the time of a raw material such as a steel ingot or steel slab.
- the M 2 C eutectic carbide (hereinafter referred to as “eutectic M 2 C”) in the cast structure is plate-like and can be decomposed into granular M 6 C carbide by hot working. (Hereinafter referred to as “decomposition M 6 C”).
- the carbide that cannot be made fine by the annealed structure of the tool material is difficult to make fine even by quenching and tempering in the final process.
- various tools containing a large amount of coarse carbides in the structure of the above-mentioned cutting edge and shape surface deteriorate the damage resistance necessary for suppressing chipping and cracking even though they can provide excellent wear resistance. It becomes a factor to do.
- the extremely coarse eutectic carbide formed in the cast structure at the time of the material such as the steel ingot or steel slab does not change into a granular shape even during hot working, the hot workability of this material is reduced. Inferior, it becomes difficult to stretch to a predetermined dimension by subsequent hot working.
- the present inventor reviewed the component composition of “high-speed tool steel” itself, which is the basis of the above-mentioned tool material. And the component composition advantageous to refinement
- C is an element that combines with Cr, W, Mo, and V to form carbides, increases the quenching and tempering hardness, and improves the wear resistance. However, when too much, hot workability will fall. In addition, toughness decreases. Therefore, it is set to 0.9 to 1.2% in balance with Cr, W, Mo, and V amounts described later. Preferably it is 0.95% or more. More preferably, it is 1.00% or more. Further, it is preferably 1.15% or less. More preferably, it is 1.10% or less.
- Si 0.1-1.0%
- Si is usually used as a deoxidizer in the dissolution process. And it is an element which improves the cutting workability of the material for tools. However, when the amount is too large, coarse eutectic carbides are easily formed in the cast structure, and hot workability is lowered. Also, toughness is reduced. Therefore, Si is set to 0.1 to 1.0%. Preferably it is 0.2% or more. More preferably, it is 0.25% or more. Moreover, Preferably it is 0.6% or less. More preferably, it is 0.5% or less. More preferably, it is 0.4% or less.
- Mn is used as a deoxidizer like Si.
- the toughness decreases, so 1.0% or less.
- it is 0.6% or less. More preferably, it is 0.5% or less. More preferably, it is 0.4% or less.
- Mn when it contains Mn, Preferably it is 0.1% or more. More preferably, it is 0.2% or more. More preferably, it is 0.25% or more.
- ⁇ Cr 3.0-5.0% Cr is an element effective for imparting hardenability, wear resistance, oxidation resistance, and the like. However, if the amount is too large, it is easy to promote an increase in the amount of solute C in the cast structure, and it becomes a factor in reducing the hot workability of the steel ingot. In addition, the toughness, high-temperature strength, and temper resistance softening characteristics of the tool product are lowered. Therefore, the content is set to 3.0 to 5.0%. Preferably it is 3.5% or more. More preferably, it is 3.6% or more. More preferably, it is 3.7% or more. Particularly preferably, it is 3.8% or more. Further, it is preferably 4.5% or less. More preferably, it is 4.3% or less. More preferably, it is 4.1% or less. Particularly preferably, it is 4.0% or less.
- ⁇ W 2.1-3.5% W combines with C described above to form a special carbide and imparts wear resistance and seizure resistance. Moreover, the secondary hardening action at the time of tempering is large, and the high-temperature strength is also improved. However, when too much, hot workability will be inhibited. Moreover, it becomes a factor of coarsening of carbides. Therefore, it is 2.1 to 3.5%. Preferably it is 2.2% or more. More preferably, it is 2.3% or more. More preferably, it is 2.4% or more. Moreover, it is preferably 2.9% or less. More preferably, it is 2.8% or less. More preferably, it is 2.7% or less. Particularly preferably, it is 2.6% or less.
- Mo 9.0 to 10.0% Mo, like W, combines with C to form a special carbide and imparts wear resistance and seizure resistance. Moreover, the secondary hardening action at the time of tempering is large, and the high-temperature strength is also improved. However, when too much, hot workability will be inhibited. Therefore, the content is set to 9.0 to 10.0%. Preferably it is 9.1% or more. More preferably, it is 9.2% or more. More preferably, it is 9.3% or more. Especially preferably, it is 9.4% or more. Moreover, it is preferably 9.9% or less. More preferably, it is 9.8% or less. More preferably, it is 9.7% or less. Particularly preferably, it is 9.6% or less.
- V 0.9-1.2%
- V combines with C to form a hard carbide, which contributes to improved wear resistance. However, when too much, hot workability will fall. In addition, toughness decreases. Therefore, it is set to 0.9 to 1.2%.
- Co dissolves in the matrix, improves the hardness of the tempered martensite, and contributes to the improvement of wear resistance. It also improves the strength and heat resistance of the tool. However, when too much, hot workability will fall. In addition, toughness decreases. Therefore, the content is set to 5.0 to 10.0%. Preferably it is 6.0% or more. More preferably, it is 6.5% or more. More preferably, it is 7.0% or more. Moreover, Preferably it is 9.3% or less. More preferably, it is 9.2% or less. More preferably, it is 9.0% or less. Particularly preferably, it is 8.5% or less.
- N 0.020% or less
- N has an effect of suppressing agglomeration of eutectic carbide in the cast structure of the high-speed tool steel having the above-described component composition.
- vanadium nitride is formed in the cast structure, and the hot workability of the material is hindered.
- N is set to 0.020% or less.
- it is 0.019% or less. More preferably, it is 0.018% or less. More preferably, it is 0.017% or less.
- it when it contains N, in order to acquire said effect, it is 0.005% or more preferably. More preferably, it is 0.008% or more. More preferably, it is 0.012% or more. Particularly preferably, it is 0.015% or more.
- M value ⁇ 9.500 + 9.334 [% C] ⁇ 0.275 [% Si] ⁇ 0.566 [% W] ⁇ 0.404 [% Mo] +3.980 [% V] +0.166 [%] % Co] []
- the content in parentheses indicates the content (% by mass) of each element.
- the above formula is an index value indicating the amount (frequency) of eutectic carbide that can exist “stablely” in the structure of the high-speed tool steel having the component composition of the present invention.
- the eutectic M 2 C is not decomposed into M 6 C by hot working, The frequency which can remain in the structure
- the eutectic M 6 C it shows the frequency of its own (i.e., frequency in the tool material after hot working).
- C, Si, W, Mo, V, and Co can be cited as elements that affect the stabilization of the eutectic carbide.
- the present inventors have found that C, V, and Co promote stabilization of the eutectic M 2 C, and Si, W, and Mo promote stabilization of the eutectic M 6 C. .
- the present inventor assigns “plus” coefficients to C, V, and Co that promote stabilization of the eutectic M 2 C, and “minus” to Si, W, and Mo that promotes stabilization of the eutectic M 6 C.
- Making the M value according to the above equation close to “zero” by the above-described determination of the coefficient means that eutectic carbides that cause coarsening of carbides are reduced in the structure of the tool material. That is, by bringing the M value close to “zero”, the eutectic M 2 C in the cast structure can be easily changed to fine decomposition M 6 C by hot working. Then, as well, hot hard eutectic M 6 C to be fine in processing can reduce the abundance itself. And in this invention, said M value shall be "1.5 or less.” Thereby, the stable eutectic M 2 C is reduced, and the eutectic M 2 C can be changed into fine decomposition M 6 C by hot working. Preferably, it is “1.0 or less”.
- the M value is set to “ ⁇ 1.5 or more”. This can reduce eutectic M 6 C itself, which is difficult to make fine by hot working.
- S and P can be included as inevitable impurity elements in the high-speed tool steel of the present invention. If the amount of S is too large, the hot workability of the material is hindered. More preferably, it is 0.005% or less. More preferably, it is 0.001% or less. If P is too large, the toughness deteriorates, so it is preferable to regulate it to 0.05% or less. More preferably, it is 0.03% or less. More preferably, it is 0.025% or less.
- the carbide size described above is an estimated maximum predicted value ⁇ (Area max ) calculated by an extreme value statistical method in which the maximum diameter of the carbide contained in the cross-sectional structure of the tool material is 32.0 ⁇ m or less. Preferably there is.
- the damage resistance of various tools can be further improved. More preferably, it is 30.0 ⁇ m or less. More preferably, it is 28.0 ⁇ m or less.
- a molten steel adjusted to a predetermined composition was prepared. Then, this molten steel was cast at a cooling rate of about 10 ° C./min corresponding to the actual operation level to produce a steel ingot of high-speed tool steel having the component composition shown in Table 1.
- Ingot No. 13 corresponds to SKH59.
- Table 1 the order of the steel ingots is arranged in order from the smallest M value so that the effect of the present invention can be easily evaluated.
- the above steel ingot No. 1 to 21 are forged by hot working, and the tool material No. 1 corresponding to the above ingot number order in the annealing state made of a rectangular bar having a cross-sectional shape of 20 mm ⁇ 20 mm. 1-21 were obtained.
- the cross-sectional shape is forged from the end of the steel ingot, about the one that wrinkles occurred on the surface of the bar (or steel ingot) during the forging.
- the length of the bar (forge elongation) at that time was also measured.
- Table 2 shows the forge elongation of each tool material after hot working together with its M value.
- the forge elongation is SKH59 tool material No. so that the hot workability of the high-speed tool steel can be easily evaluated. It was shown as a comparative value when that of 13 was set to “100”.
- Table 2 shows that the amount of each element contained in the high-speed tool steel satisfies the present invention, and the M-value is adjusted within the range of “ ⁇ 1.5 to 1.5”.
- the forging elongation of 8 to 11 is “over 100”.
- the forging elongation of 9 and 11 was “120 or more”, and substantially all of the steel ingot could be forged. And hot workability was favorable compared with SKH59 (tool material No. 13).
- the tool material no. Nos. 1 to 5 indicate that the amount of each element contained does not satisfy the present invention, and a large amount of coarse eutectic M 6 C is present in the cast structure of the steel ingot.
- the hot workability was inferior to that of SKH59 (tool material No. 13).
- the tool material No. 2 In addition to the above factors, due to the high content of Si and Cr, remarkable flaws occurred on the surface of the steel ingot from the beginning of forging, and hot working was stopped. did.
- a tool material No. having an M value in the range of “ ⁇ 1.5 to 1.5” is shown. 6 and 7, the tool material No. In No. 6, the W content was higher than the range of the present invention, but the forge elongation exceeded 100. However, the tool material No. In No. 7, since the W content was higher and the Mo content was higher, the hot workability was lowered.
- Tool material No. with M value larger than “1.5” Nos. 12 to 21 showed hot workability substantially equivalent to that of SKH59 (tool material No. 13) except for a part, regardless of the amount of each element contained in the present invention. And about said one part, tool material No. No. 15 had a high content of C, W and V, so that hot workability was greatly deteriorated. In addition, the tool material No. In No. 19, the hot workability was greatly deteriorated due to the fact that in addition to the high contents of C and V, the Co content was also high. Tool material No. with high content of C and V In No. 21, hot workability decreased. In FIG. The relationship between the M value in 1 to 21 and the above-described forge elongation is shown (however, for No. 2 in which hot working is stopped, the forge elongation is indicated as “0”).
- the distribution of carbides in the 1 to 21 annealed structures was observed.
- a scanning electron microscope (SEM) with a magnification of 150 times was used.
- the observation surface is a cross section (longitudinal cross section) in the length direction including the center line of the bar, and includes one side (20 mm) of the cross section of the bar and one side (20 mm) in the length direction of the bar.
- a rectangular area of 20 mm ⁇ 20 mm is obtained.
- 64 fields were observed with the above SEM, and carbides having a maximum diameter of 9 ⁇ m or more for each field were measured.
- the above carbide was measured according to the following procedure. First, by performing a binarization process on the reflected electron image by SEM based on the maximum diameter of carbides confirmed in this image, the maximum diameter of “9 ⁇ m” is set as a threshold value. A binarized image showing a carbide having a “maximum diameter of 9 ⁇ m or more” distributed on the observation surface was obtained. 3 and 4 respectively show tool material Nos. Which are examples of the present invention. 11 and the comparative tool material No. 19 is the above binarized image (the carbide is shown by the distribution of black spots). And the carbide
- the size of the “largest carbide” is read for each field of view, and the “largest carbide for each field of view” is read.
- the extreme value statistical graph based on the size of " Then, the maximum diameter of carbides contained in the cross-sectional structure of the tool material (that is, the estimated maximum predicted value ⁇ (Area max )) was predicted by the extreme value statistical method. The estimated maximum predicted value was obtained by setting the recursion period to 100 based on the above extreme value statistical graph (described later). Table 3 shows the maximum diameter of carbide (estimated maximum predicted value ⁇ (Area max )).
- the tool material No. of the present invention example.
- the maximum diameter of the carbide contained in the cross-sectional structure was 32.0 ⁇ m or less as an estimated maximum predicted value ⁇ (Area max ).
- the tool material No. ⁇ (Area max ) of 8, 10, 11 was 30.0 ⁇ m or less. Therefore, the tool produced using the tool material of the present invention can be expected to have improved damage resistance.
- the tool material No. The estimated maximum predicted value ⁇ (Area max ) of 1, 3, 5, 7, 14, and 15 was 32.0 ⁇ m or less.
- these tool materials were inferior in hot workability to SKH59 (tool material No. 13) as described above.
- the M value satisfies the range of “ ⁇ 1.5 to 1.5” of the present invention, but the W content is higher than the range of the present invention, and the estimated maximum predicted value ⁇ (Area max ) Was over 32.0 ⁇ m.
- Tool material No. 12 and 16 to 21 the M value did not satisfy the range of “ ⁇ 1.5 to 1.5” of the present invention, and the estimated maximum predicted value ⁇ (Area max ) exceeded 32.0 ⁇ m.
- FIG. The relationship between the M value of 1 to 21 (excluding No. 2) and the above-mentioned ⁇ (Area max ) will be shown.
- tool material No. for 1 to 21 (excluding No. 2), quenching was performed by heating to 1190 ° C. and quenching, followed by tempering by holding at 560 ° C. for 1 hour three times. The hardness of the tool material after quenching and tempering was measured. The results are shown in Table 4.
- a molten steel adjusted to a predetermined composition was prepared.
- the molten steel was cast at a cooling rate of about 10 ° C./min. 22 to 24 were produced.
- Ingot No. 24 corresponds to SKH59.
- the above steel ingot No. 22 to 24, which are hot-worked and made of an annealed coil wire having a diameter of 5 mm, the tool material No. 22-24 were obtained.
- the tool material No. The distribution of carbides in the 22-24 annealed structures was observed.
- the observation surface was the position of the center line of the longitudinal section including the center line of the coil wire.
- carbides having a maximum diameter of 9 ⁇ m or more for each visual field were measured in the same manner as in Example 1 for 64 visual fields in which the visual field of 34080 ⁇ m 2 on this observation surface was one visual field.
- the tool material No. of the present invention example.
- the maximum diameter of the carbide contained in the cross-sectional structure was 32.0 ⁇ m or less as an estimated maximum predicted value ⁇ (Area max ). Therefore, a cutting tool and a plastic working tool produced using the tool material of the present invention can be expected to have improved damage resistance.
- the above-mentioned coil wire rod tool material No. No. 22-24 were tempered by repeating quenching from 1190 ° C. and holding at 560 ° C. for 1 hour three times, assuming the quenching and tempering conditions of the actual tool.
- the test piece after quenching and tempering was subjected to a three-point bending test, and the maximum bending stress (that is, the bending force) until the test piece was broken was measured.
- the bending test the dimensions of the test piece were 4 mm diameter ⁇ 60 mm length, and the span during the test was 50 mm. Further, the bending strength was the average value of the maximum bending stress by performing the bending test four times. The results are shown in Table 7 together with the quenching and tempering hardness.
- the bending strength is an index for evaluating the toughness of the tool, and the larger this value, the higher the toughness. Since the value of the bending strength is large, in the cutting tool, early chipping generated at the cutting edge can be suppressed. In addition, in a plastic working tool, early chipping, cracking, breakage, etc. occurring on the shape surface can be suppressed. And as shown in Table 7, the tool material No. of the present invention example. Nos. 22 and 23 are tool product states after quenching and tempering. Compared with 24 (SKH59), it showed high bending strength.
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Abstract
Description
また、上記の切断工具や塑性加工工具に用いる「工具用材料」についても、その製造工程で、上記の鋼塊や鋼片等の素材に熱間加工を行なったときには、素材の延性が低い(熱間加工性に劣る)ことに起因して、所定の寸法にまで延伸し難い場合があった。
この高速度工具鋼が含有する上記のC、Si、W、Mo、V、Coの含有量の関係が、下記の式で算出されるM値において、-1.5≦M値≦1.5を満たす高速度工具鋼である。
式:M値=-9.500+9.334[%C]-0.275[%Si]-0.566[%W]-0.404[%Mo]+3.980[%V]+0.166[%Co]
[]括弧内は各元素の含有量(質量%)を示す。
この高速度工具鋼の鋼塊が含有する上記のC、Si、W、Mo、V、Coの含有量の関係が、下記の式で算出されるM値において、-1.5≦M値≦1.5を満たす工具用材料の製造方法である。
式:M値=-9.500+9.334[%C]-0.275[%Si]-0.566[%W]-0.404[%Mo]+3.980[%V]+0.166[%Co]
[]括弧内は各元素の含有量(質量%)を示す。
また、SKH59のような成分組成の高速度工具鋼の鋳造組織中には、M6C共晶炭化物(以下、「共晶M6C」と言う。)も形成される。一般的に、この共晶M6Cは、魚骨状である。そして、熱間加工によって粒状化することが難しい。よって、上記の共晶M6Cが著しく粗大であると、熱間加工後において、これが“そのまま”の著しく粗大な状態で残って、工具用材料の焼鈍組織に著しく粗大な炭化物が多く存在する結果となる。
また、上記の鋼塊や鋼片等の素材の時点で、その鋳造組織中に形成された著しく粗大な共晶炭化物が、熱間加工でも粒状に変化しないと、この素材の熱間加工性が劣って、続く熱間加工で所定の寸法にまで延伸することが難しくなる。
Cは、Cr、W、Mo、Vと結合して炭化物を形成し、焼入れ焼戻し硬さを高め、耐摩耗性を向上する元素である。しかし、多すぎると、熱間加工性が低下する。また、靭性が低下する。よって、後述するCr、W、Mo、V量とバランスさせた上で、0.9~1.2%とする。好ましくは0.95%以上である。より好ましくは1.00%以上である。また、好ましくは1.15%以下である。より好ましくは、1.10%以下である。
Siは、通常、溶解工程における脱酸剤として使用される。そして、工具用材料の切削加工性を向上させる元素である。しかし、多すぎると、鋳造組織中に粗大な共晶炭化物を形成しやすく、熱間加工性が低下する。また、靭性も低下する。よって、Siは、0.1~1.0%とする。好ましくは0.2%以上である。より好ましくは0.25%以上である。また、好ましくは0.6%以下である。より好ましくは0.5%以下である。更に好ましくは0.4%以下である。
Mnは、Siと同様、脱酸剤として使用される。しかし、多すぎると靭性が低下するので、1.0%以下とする。好ましくは0.6%以下である。より好ましくは0.5%以下である。更に好ましくは0.4%以下である。また、Mnを含有する場合、好ましくは0.1%以上である。より好ましくは0.2%以上である。さらに好ましくは0.25%以上である。
Crは、焼入性、耐摩耗性、耐酸化性等を付与するのに有効な元素である。しかし、多すぎると、鋳造組織中における固溶C量の増加を助長しやすく、少なからず、鋼塊の熱間加工性の低下の要因となる。また、工具製品の靭性、高温強度、耐焼戻し軟化特性を低下させる。よって、3.0~5.0%とする。好ましくは3.5%以上である。より好ましくは3.6%以上である。更に好ましくは3.7%以上である。特に好ましくは3.8%以上である。また、好ましくは4.5%以下である。より好ましくは4.3%以下である。更に好ましくは4.1%以下である。特に好ましくは4.0%以下である。
Wは、上述したCと結合して特殊な炭化物を形成して、耐摩耗性や耐焼付き性を付与する。また、焼戻し時の二次硬化作用が大きく、高温強度も向上する。しかし、多すぎると、熱間加工性を阻害する。また、少なからず、炭化物の粗大化の要因となる。よって、2.1~3.5%とする。好ましくは2.2%以上である。より好ましくは2.3%以上である。更に好ましくは2.4%以上である。また、好ましくは2.9%以下である。より好ましくは2.8%以下である。更に好ましくは2.7%以下である。特に好ましくは2.6%以下である。
Moは、Wと同様にCと結合して特殊な炭化物を形成して、耐摩耗性や耐焼付き性を付与する。また、焼戻し時の二次硬化作用が大きく、高温強度も向上する。しかし、多すぎると、熱間加工性を阻害する。よって、9.0~10.0%とする。好ましくは9.1%以上である。より好ましくは9.2%以上である。更に好ましくは9.3%以上である。特に好ましくは9.4%以上である。また、好ましくは9.9%以下である。より好ましくは9.8%以下である。更に好ましくは9.7%以下である。特に好ましくは9.6%以下である。
Vは、Cと結合して硬質の炭化物を形成し、耐摩耗性の向上に寄与する。しかし、多すぎると、熱間加工性が低下する。また、靭性が低下する。よって、0.9~1.2%とする。好ましくは0.93%以上である。より好ましくは0.95%以上である。また、好ましくは1.15%以下である。より好ましくは1.10%以下である。
Coは、基地中に固溶して、焼戻しマルテンサイトの硬さを向上させ、耐摩耗性の向上に寄与する。また、工具の強度や耐熱性を向上させる。しかし、多すぎると、熱間加工性が低下する。また、靭性が低下する。よって、5.0~10.0%とする。好ましくは6.0%以上である。より好ましくは6.5%以上である。更に好ましくは7.0%以上である。また、好ましくは9.3%以下である。より好ましくは9.2%以下である。更に好ましくは9.0%以下である。特に好ましくは8.5%以下である。
Nは、上述した成分組成を有する高速度工具鋼の鋳造組織において、共晶炭化物の塊状化を抑制する効果を有する。しかし、多すぎると、鋳造組織中にバナジウム窒化物を形成して、素材の熱間加工性を阻害する。また、かえって、上記の共晶炭化物の塊状化を助長する作用がある。よって、Nは、0.020%以下とする。好ましくは0.019%以下である。より好ましくは0.018%以下である。更に好ましくは0.017%以下である。なお、Nを含有する場合、上記の効果を得るのに好ましくは0.005%以上である。より好ましくは0.008%以上である。更に好ましくは0.012%以上である。特に好ましくは0.015%以上である。
式:M値=-9.500+9.334[%C]-0.275[%Si]-0.566[%W]-0.404[%Mo]+3.980[%V]+0.166[%Co]
[]括弧内は各元素の含有量(質量%)を示す。
そして、本発明においては、上記のM値を「1.5以下」とする。これによって、安定的な共晶M2Cが減り、共晶M2Cを熱間加工で微細な分解M6Cに変化させることができる。好ましくは「1.0以下」である。より好ましくは「0.8以下」である。更に好ましくは「0.7以下」である。また、本発明においては、上記のM値を「-1.5以上」とする。これによって、熱間加工で微細にすることが困難な共晶M6C自体を低減することができる。好ましくは「-1.0以上」である。より好ましくは「-0.8以上」である。更に好ましくは「-0.7以上」である。M値をこれら範囲に調整することよって、高速度工具鋼の熱間加工性の向上、および、各種工具の耐損傷性の向上を達成することができる。
また、M値が「-1.5~1.5」の範囲内にある工具用材料No.6,7のうち、工具用材料No.6は、Wの含有量が本発明の範囲より高いが、鍛伸長さは100を超えた。しかし、工具用材料No.7は、Wの含有量が更に高いことに加えて、Moの含有量も高めであることから、熱間加工性が低下した。
図2に、工具用材料No.1~21における、M値と、上記の鍛伸長さとの関係を示しておく(但し、熱間加工を中止したNo.2については、鍛伸長さを「0」として示している)。
上記の炭化物の計測は、次の要領によった。まず、SEMによる反射電子像に対し、この像中に確認される炭化物の最大径に基づいて、「9μm」の最大径を閾(しきい)値とした二値化処理を行うことで、上記の観察面に分布する「最大径が9μm以上」の炭化物を示した二値化画像を得た。図3および図4は、それぞれ、本発明例である工具用材料No.11および比較例である工具用材料No.19における上記の二値化画像である(炭化物は、黒点の分布で示されている)。そして、この二値化画像から、最大径が9μm以上の炭化物の計測を行った。
上記の極値統計処理には、マイクロソフト社の表計算ソフトウェア「エクセル」を用いた。このとき、極値統計処理に必要な再帰期間について、予測体積は31.4mm3とした。これは、通常、各種工具の耐チッピング性等を評価するのに用いられている、直径4mm、スパン50mmの試験片による3点曲げ試験において、その破壊の起点となり得る危険部分が、この試験片の表面から中心に向かって直径の5%入った体積の部分にあることに基づいたものである。そして、表3に示した炭化物の最大径(推定最大予測値√(Areamax))は、上記した3点曲げ試験片100本当たりでの推定値である。
これに対して、工具用材料No.1、3、5、7、14、15も、上記の推定最大予測値√(Areamax)が32.0μm以下であった。しかし、これらの工具用材料は、上述の通り、SKH59(工具用材料No.13)より熱間加工性が劣っていた。
工具用材料No.6は、M値が本発明の「-1.5~1.5」の範囲を満たしているが、Wの含有量が本発明の範囲より高く、上記の推定最大予測値√(Areamax)が32.0μmを超えていた。
工具用材料No.12、16~21は、M値が本発明の「-1.5~1.5」の範囲を満たさず、推定最大予測値√(Areamax)が32.0μmを超えていた。
図1に、工具用材料No.1~21(但し、No.2を除く)のM値と、上記の√(Areamax)との関係を示しておく。
Claims (3)
- 質量%で、C:0.9~1.2%、Si:0.1~1.0%、Mn:1.0%以下、Cr:3.0~5.0%、W:2.1~3.5%、Mo:9.0~10.0%、V:0.9~1.2%、Co:5.0~10.0%、N:0.020%以下、残部Feおよび不純物でなる高速度工具鋼であり、
前記高速度工具鋼が含有する前記C、Si、W、Mo、V、Coの含有量の関係が、下記式で算出されるM値において、-1.5≦M値≦1.5を満たすことを特徴とする高速度工具鋼。
式:M値=-9.500+9.334[%C]-0.275[%Si]-0.566[%W]-0.404[%Mo]+3.980[%V]+0.166[%Co]
[]括弧内は各元素の含有量(質量%)を示す。 - 請求項1に記載の高速度工具鋼でなり、
断面組織中に含まれる炭化物の最大径が、極値統計法によって算出される推定最大予測値√(Areamax)で、32.0μm以下であることを特徴とする工具用材料。 - 質量%で、C:0.9~1.2%、Si:0.1~1.0%、Mn:1.0%以下、Cr:3.0~5.0%、W:2.1~3.5%、Mo:9.0~10.0%、V:0.9~1.2%、Co:5.0~10.0%、N:0.020%以下、残部Feおよび不純物でなる高速度工具鋼を鋼塊に鋳造し、前記鋼塊に熱間加工を行う工具用材料の製造方法であって、
前記高速度工具鋼の鋼塊が含有する前記C、Si、W、Mo、V、Coの含有量の関係が、下記式で算出されるM値において、-1.5≦M値≦1.5を満たすことを特徴とする工具用材料の製造方法。
式:M値=-9.500+9.334[%C]-0.275[%Si]-0.566[%W]-0.404[%Mo]+3.980[%V]+0.166[%Co]
[]括弧内は各元素の含有量(質量%)を示す。
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Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0941091A (ja) * | 1995-07-26 | 1997-02-10 | Hitachi Ltd | 冷間圧延用ロール材 |
JPH0966305A (ja) * | 1995-09-04 | 1997-03-11 | Kanto Special Steel Works Ltd | 冷間圧延用ワークロールとその製造方法 |
JP2000219935A (ja) * | 1999-01-28 | 2000-08-08 | Hitachi Metals Ltd | メタルバンドソー用刃材 |
JP2014208870A (ja) * | 2012-09-20 | 2014-11-06 | 日立金属株式会社 | 高速度工具鋼、刃先用材料および切断工具、ならびに、刃先用材料の製造方法 |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5453614A (en) | 1977-10-07 | 1979-04-27 | Hitachi Metals Ltd | Highhspeed toollsteel having good heattresistivity and highhtoughness |
JPS579622A (en) | 1980-06-17 | 1982-01-19 | Matsushita Electric Ind Co Ltd | Buffer for pallet |
JPS6115143A (ja) | 1984-07-02 | 1986-01-23 | Fuji Photo Film Co Ltd | 自動現像装置 |
FI69270C (fi) * | 1984-09-21 | 1986-01-10 | Metsaeliiton Teollisuus Oy | Brandbestaendiga traekompositer speciellt inredningsskivor ochfoerfarande foer framstaellning av dessa |
JPH04180540A (ja) | 1990-11-14 | 1992-06-26 | Hitachi Metals Ltd | 高速度工具鋼 |
JPH06115143A (ja) * | 1992-10-06 | 1994-04-26 | Fujitsu Ltd | サーマルプリンタ制御方法 |
JPH093604A (ja) | 1995-06-23 | 1997-01-07 | Daido Steel Co Ltd | 精密鋳造用高速度工具鋼 |
JP2000144333A (ja) | 1998-11-05 | 2000-05-26 | Hitachi Metals Ltd | 溶解法による高硬度高速度工具鋼 |
GB0025113D0 (en) | 2000-10-13 | 2000-11-29 | Carrott Andrew J | Improvements in tabletting dies |
JP4180540B2 (ja) * | 2004-03-29 | 2008-11-12 | 三菱電機インフォメーションシステムズ株式会社 | データマイニングシステム |
AT507956B1 (de) | 2009-02-16 | 2011-01-15 | Boehler Edelstahl Gmbh & Co Kg | Bimetallsäge |
JP5328494B2 (ja) | 2009-06-03 | 2013-10-30 | 株式会社アマダ | 帯鋸刃及びその製造方法 |
CN103695789B (zh) | 2014-01-02 | 2016-03-30 | 大连远东工具有限公司 | 一种高性能超硬高速钢 |
CN114086063A (zh) * | 2015-06-22 | 2022-02-25 | 日立金属株式会社 | 高速工具钢钢材的制造方法、高速工具钢制品的制造方法及高速工具钢制品 |
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Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0941091A (ja) * | 1995-07-26 | 1997-02-10 | Hitachi Ltd | 冷間圧延用ロール材 |
JPH0966305A (ja) * | 1995-09-04 | 1997-03-11 | Kanto Special Steel Works Ltd | 冷間圧延用ワークロールとその製造方法 |
JP2000219935A (ja) * | 1999-01-28 | 2000-08-08 | Hitachi Metals Ltd | メタルバンドソー用刃材 |
JP2014208870A (ja) * | 2012-09-20 | 2014-11-06 | 日立金属株式会社 | 高速度工具鋼、刃先用材料および切断工具、ならびに、刃先用材料の製造方法 |
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