阅读说明：本技术 刀具用钢带的制造方法及刀具用钢带 (Method for manufacturing steel strip for cutting tool and steel strip for cutting tool ) 是由 妹尾亘 于 2018-05-15 设计创作，主要内容包括：本发明提供一种可不添加昂贵的Mo而将碳化物密度控制在适当的范围内、具有良好的生产性的刀具用钢带的制造方法及刀具用钢带。一种刀具用钢带的制造方法及刀具用钢带,所述刀具用钢带的制造方法制造以质量％计包含C：0.55％～0.80％、Si：1.0％以下、Mn：1.0％以下、Cr：12.0％～14.0％、且剩余部分由Fe及不可避免的杂质构成的刀具用钢带,并且包括：分批退火步骤,在分批式的退火炉内对具有所述金属组成的冷轧用原材料进行退火；以及冷轧步骤,对分批退火后的冷轧用原材料实施一次以上的冷轧而制成钢带,所述分批退火步骤包括：第一均热步骤,在炉内温度超过450℃且小于770℃下加热保持1小时～12小时；以及第二均热步骤,在第一均热步骤之后进行,在炉内温度超过770℃且小于900℃下加热保持1小时～16小时。(The invention provides a method for manufacturing a steel strip for a cutting tool and the steel strip for the cutting tool, which can control the carbide density in a proper range without adding expensive Mo and has good productivity. A method for manufacturing a steel strip for a cutting tool, which includes, in mass%, C: 0.55-0.80%, Si: 1.0% or less, Mn: 1.0% or less, Cr: 12.0% to 14.0%, with the remainder comprising Fe and unavoidable impurities, and comprising: a batch annealing step of annealing a cold rolling material having the metal composition in a batch-type annealing furnace; and a cold rolling step of cold-rolling the batch-annealed cold-rolled material at least once to produce a steel strip, the batch annealing step including: a first soaking step of heating and maintaining for 1-12 hours at a temperature in the furnace of more than 450 ℃ and less than 770 ℃; and a second soaking step, which is performed after the first soaking step, and is heated and maintained for 1 to 16 hours at a temperature in the furnace of more than 770 ℃ and less than 900 ℃.)

1. A method for producing a steel strip for a cutting tool, comprising the steps of: 0.55-0.80%, Si: 1.0% or less, Mn: 1.0% or less, Cr: 12.0% to 14.0%, and the balance of Fe and inevitable impurities, and a method for producing the steel strip for cutting tools, comprising:

a batch annealing step of annealing a cold rolling material having the composition in a batch-type annealing furnace; and

a cold rolling step of cold rolling the cold-rolled material after the batch annealing step at least once to produce a steel strip,

the batch annealing step includes: a first soaking step of heating and maintaining for 1-12 hours at a temperature in the furnace of more than 450 ℃ and less than 770 ℃; and a second soaking step, which is carried out after the first soaking step, and is heated and kept for 1-16 h at the temperature in the furnace which exceeds 770 ℃ and is less than 900 ℃.

2. The method for manufacturing a steel strip for cutting tools as claimed in claim 1, wherein the metal structure of the steel strip for cutting tools is a ferrite structure in which carbides are dispersed,

the density of the carbide is 100/100 mu m²200 pieces/100 mu m²。

3. The method for producing a steel strip for tools as claimed in claim 2, wherein the average diameter of carbides of the steel strip for tools is 0.30 to 0.45 μm.

4. A steel strip for a cutting tool, comprising, in mass%, C: 0.55-0.80%, Si: 1.0% or less, Mn: 1.0% or less, Cr: 12.0 to 14.0%, and the balance of Fe and inevitable impurities,

the metal structure of the steel strip for a cutter is a ferrite structure in which carbide is dispersed,

the density of the carbide is 100/100 mu m²200 pieces/100 mu m²。

5. The steel strip for tools as claimed in claim 4, wherein the average diameter of carbides of the steel strip for tools is 0.30 to 0.45 μm.

Technical Field

The present invention relates to a method for manufacturing a steel strip for a cutter, and a steel strip for a cutter.

Background

A martensitic stainless steel (martentite) having high hardness, excellent wear resistance and corrosion resistance and containing, by mass%, C1.0% or less and Cr 12.0% to 14.0% or so is used for a steel strip for a tool used for a tool such as a cutter. The martensitic stainless steel strip can be generally processed into a desired product shape by cold rolling and softening annealing, and then quenched and tempered to obtain a high-hardness structure.

The structure of the steel strip for a cutting tool before quenching and tempering shows a state in which carbides are dispersed in a ferrite structure, and characteristics such as hardness vary depending on the distribution state of the carbides. For example, in patent document 1 previously proposed by the present applicant, in order to provide a stainless steel for a shaver which can obtain excellent hardness by a short-time heat treatment, there is an invention of the following stainless steel for a shaver: c in weight percent: more than 0.55% and 0.73% or less, Si: 1.0% or less, Mn: 1.0% or less, Cr: 12% to 14% inclusive, Mo: 0.2% to 1.0%, Ni: no addition of 1.0%, and the balance of Fe and impurities, and the carbide density in the annealed state was 140 particles/100 μm²200 pieces/100 mu m²The hardenability of (2) is excellent.

Disclosure of Invention

Problems to be solved by the invention

The stainless steel for a shaver described in patent document 1 is an invention excellent in hardenability and cold rolling property, but Mo, which is an expensive raw material, must be added in order to increase the carbide density, and there is no description about increasing the carbide density without adding Mo, and there is room for study. Accordingly, an object of the present invention is to provide a method for producing a steel strip for a cutter, and a steel strip for a cutter: the carbide density can be controlled within an appropriate range without adding Mo, and the productivity can be expected to be improved.

Means for solving the problems

The present inventors have intensively studied the heating conditions of a batch annealing furnace in order to obtain a steel strip containing no Mo and having an appropriate carbide density. As a result, the inventors have found that characteristics equivalent to those of the steel strip of patent document 1 containing Mo can be obtained by adjusting the temperature rise rate, the heating holding time, and the temperature of the batch annealing furnace to appropriate ranges, and have arrived at the present invention.

That is, one embodiment of the present invention is a method for manufacturing a steel strip for a cutting tool, which includes, in mass%, C: 0.55-0.80%, Si: 1.0% or less, Mn: 1.0% or less, Cr: 12.0% to 14.0%, with the remainder comprising Fe and unavoidable impurities, and comprising: a batch annealing step of annealing a cold rolling material having the composition in a batch-type annealing furnace; and a cold rolling step of performing cold rolling on the cold-rolled material after the batch annealing step at least once to produce a steel strip, the batch annealing step including: a first soaking step of heating and maintaining for 1-12 hours at a temperature in the furnace of more than 450 ℃ and less than 770 ℃; and a second soaking step, which is performed after the first soaking step, and is heated and maintained for 1 to 16 hours at a temperature in the furnace of more than 770 ℃ and less than 900 ℃.

Preferably the aboveThe metal structure of the steel strip for cutting tools is a ferrite structure in which carbides are dispersed, the density of the carbides being 100 particles/100 [ mu ] m²200 pieces/100 mu m²。

Preferably, the average carbide diameter of the steel strip for cutting tools is 0.30 to 0.45. mu.m.

Another embodiment of the present invention is a steel strip for a cutter tool, having a composition comprising, in mass%, C: 0.55-0.80%, Si: 1.0% or less, Mn: 1.0% or less, Cr: 12.0 to 14.0%, and the balance of Fe and inevitable impurities,

the metal structure of the steel strip for a cutter is a ferrite structure in which carbide is dispersed,

the density of the carbide is 100/100 mu m²200 pieces/100 mu m²。

Preferably, the average carbide diameter of the steel strip for cutting tools is 0.30 to 0.45. mu.m.

ADVANTAGEOUS EFFECTS OF INVENTION

According to the present invention, the carbide density can be controlled within an appropriate range without adding expensive Mo, and a steel strip for a tool having a productivity better than that of the conventional continuous annealing method can be obtained.

Drawings

FIG. 1 is an electron micrograph showing a surface portion of a steel strip for a cutting tool of the present invention.

Detailed Description

Hereinafter, an embodiment of the present invention will be described. However, the present invention is not limited to the embodiments described herein, and can be combined or modified as appropriate within a range not departing from the technical spirit of the present invention. First, the reasons for limitations will be described with respect to the composition of the steel strip for a cutter according to the present invention.

C：0.55％～0.80％

C is an important element which is adjusted to a carbide density suitable for the present invention, is solid-dissolved from the carbide to the matrix (matrix) at an austenitizing temperature during quenching, and determines the hardness of martensite generated during quenching. In order to obtain a carbide density suitable for the present invention, the content of C is set to 0.55% or more. The lower limit of C is preferably 0.60%, and more preferably 0.63%. In addition, since the excessive content of C may cause formation of large eutectic carbides or decrease in corrosion resistance, the upper limit is set to 0.80%. The upper limit of C is preferably 0.78%, and more preferably 0.75%.

Si: 1.0% or less

Si is an element that is used as a deoxidizer in the refining of a steel strip for cutting tools, and that is dissolved in steel to suppress softening in low-temperature tempering. However, the excessive content is as SiO₂The content is set to 1.0% or less because hard inclusions are highly likely to remain in the steel for cutting tools and cause chipping or spot rusting. In order to ensure the effect of softening resistance of low-temperature tempering by Si and to prevent the formation of hard inclusions, the content of Si is preferably in the range of 0.1% to 0.7%. The lower limit of Si is preferably 0.15%, and the upper limit of Si is preferably 0.5%.

Mn: 1.0% or less

Mn can be used as a deoxidizer in refining, similarly to Si. However, if Mn exceeds 1.0%, the hot workability is degraded, so the Mn content is set to 1.0% or less. Further, in the case of using Mn as a deoxidizer, not much Mn remains in the tool steel. Therefore, the lower limit of Mn is not particularly limited, but exceeds 0%. The preferable range of Mn is 0.1% to 0.9%.

Cr：12.0％～14.0％

Cr is an important element for forming Cr-based carbide necessary for obtaining carbide density suitable for the present invention while maintaining excellent corrosion resistance of the steel strip for cutting tools. In order to obtain the effect of Cr, at least 12.0% Cr is required. On the other hand, if Cr exceeds 14.0%, the amount of crystals of eutectic carbides increases, which causes edge chipping of the tool. Therefore, the content of Cr is set to a range of 12.0% to 14.0%. In order to more reliably obtain the effect of Cr, the lower limit of Cr is preferably 12.5%, and the upper limit of Cr is preferably 13.5%.

In the present invention, the other components are Fe and inevitable impurities. In particular, Mo has been added in the past to increase the carbide density, but is not added in order to reduce the raw material cost and obtain a carbide density suitable for the present invention. Examples of the other inevitable impurity elements include P, S, Cu, Al, Ti, N, and O, and they may be contained within the following ranges that do not inhibit the effects of the present invention.

P is less than or equal to 0.03%, S is less than or equal to 0.005%, Cu is less than or equal to 0.5%, Al is less than or equal to 0.1%, Ti is less than or equal to 0.1%, N is less than or equal to 0.05%, and O is less than or equal to 0.05%.

Next, the manufacturing method of the present embodiment will be described.

In the present embodiment, the following is made: the hot-rolled material having the above composition is used as a cold-rolling material, the cold-rolling material is subjected to batch annealing (batch annealing step), and the batch annealed cold-rolling material is subjected to cold-rolling at least once (cold-rolling step). Here, the surface of the hot-rolled material may be polished in order to remove scale or rolling defects present on the surface of the material after hot rolling before the batch annealing step.

[ batch annealing step ]

In the present embodiment, prior to the cold rolling step, a cold rolling material (hereinafter, also referred to as a coil) wound in a coil shape is batch-annealed in vacuum using a batch annealing furnace. By applying the batch annealing, a plurality of coils can be annealed at a time, and thus annealing can be performed with productivity better than continuous annealing. In the present embodiment, the batch annealing includes: a first soaking step of heating at a temperature lower than the transformation point of the raw material as a preceding stage heating to precipitate fine carbides; and a second soaking step of heating the raw material at a temperature equal to or higher than the transformation point of the raw material to spheroidize the carbide, after the first soaking step. In the first soaking step in the present embodiment, the furnace is heated at a temperature exceeding 450 ℃ and less than 770 ℃ for 1 to 12 hours. By this procedure, fine carbides having a uniform size can be precipitated. When the furnace temperature is 450 ℃ or less or the heating holding time is less than 1 hour, the carbide is not sufficiently precipitated, which is not preferable. When the temperature is 770 ℃ or higher or the heating holding time exceeds 12 hours, excessively grown carbide particles aggregate together, and the number of final carbide particles decreases, which is not preferable. The lower limit of the more preferable temperature is 470 ℃. Further, the lower limit of the temperature is preferably 600 ℃. More preferably, the upper limit of the temperature is less than 750 ℃. The lower limit of the heating retention time is more preferably 3 hours, and the upper limit of the heating retention time is more preferably 9 hours. Further, the upper limit of the heating holding time is preferably 8 hours, and the most preferable upper limit of the heating holding time is 7 hours. Unless otherwise specified, the "transformation point" in the present embodiment indicates the Ac1 point (the temperature at which austenite starts to be generated).

In the present embodiment, as described above, the second soaking step is included after the first soaking step, in which the heat is maintained at the furnace temperature of more than 770 ℃ and less than 900 ℃ for 1 to 16 hours. By setting the temperature in the second soaking step to a temperature equal to or higher than the transformation point of the material, that is, higher than 770 ℃ and lower than 900 ℃, the spheroidizing heat treatment can be performed while reducing the carbide dissolved in the material, and the carbide density can be increased. When the furnace temperature is 770 ℃ or lower, the structure is not austenitized, carbide is coarsened, and spheroidizing may not sufficiently proceed, which is not preferable. When the temperature is 900 ℃ or higher, the carbide is excessively dissolved in solid solution, and therefore the carbide re-precipitated in the subsequent slow cooling step tends to be coarse, which is not preferable. The lower limit of the more preferable temperature is 800 ℃ and the upper limit of the more preferable temperature is 860 ℃. The upper limit of the holding time in the second soaking step is more preferably 13 hours, and still more preferably 11 hours. When the holding time in the second soaking step is less than 1 hour, the holding time is too short, and therefore, dimensional defects and breakage of the steel strip tend to occur, which is not preferable. In the present embodiment, since a batch furnace is used, a plurality of coils can be put in one annealing (for example, 10 coils having a maximum outer diameter of phi 1000mm are put in the furnace), and thus the productivity is high. After the second soaking step, in order to sufficiently precipitate carbide in the raw material, it is preferable to perform a slow cooling step of slowly cooling the raw material until the temperature of the raw material reaches 600 to 800 ℃ (of these, a temperature lower than the temperature in the furnace in the second soaking step).

[ Cold Rolling step ]

In the present embodiment, a steel strip adjusted to a desired thickness can be obtained by performing cold rolling at least once on a cold rolling material having completed a batch annealing step. Further, the cold rolling may be performed a plurality of times, and intermediate annealing for softening the steel strip may be performed during the cold rolling. Further, after the final cold rolling, strain relief annealing for the purpose of strain relief may be performed.

[ metallic Structure ]

The metal structure of the steel strip for cutting tools obtained by the method of the present invention before quenching and tempering is a ferrite structure in which carbides are dispersed, and the density of the carbides is adjusted to 100 particles/100 μm²200 pieces/100 mu m². By controlling within the above range, a steel strip excellent in hardenability can be obtained. The density of carbide is less than 100 pieces/100 mu m²In the case of (3), the amount of solid solution of carbide during quenching tends to be small, and the desired hardness tends not to be obtained. The density of carbide exceeds 200/100 mu m²In the case of (2), the hardness of the steel strip tends to be high, and the productivity tends to be low. The lower limit of the carbide density is more preferably 120 particles/100. mu.m²Further, the lower limit of the carbide density is preferably 130 particles/100. mu.m²The most preferred lower limit of the carbide density is 140/100. mu.m². Further, the upper limit of the carbide density is preferably 190 particles/100. mu.m²More preferably, the upper limit of the carbide density is 180 particles/100. mu.m²。

The average carbide diameter of the steel strip for cutting tools of the present invention before quenching and tempering is preferably 0.30 to 0.45. mu.m. By controlling the carbide size within the above range, the carbide tends to be easily dissolved in the solution during quenching. More preferably, the amount of fine carbides having an average diameter of 0.30 to 0.40 μm is large. In this way, fine carbides having a size of 0.40 μm or less are mainly precipitated, whereby further excellent hardenability can be obtained. The method of measuring carbide in the present embodiment can be measured, for example, as follows: the surface (rolled surface) of the steel strip was etched, the developed structure was observed at 10000 times with an electron microscope, and the obtained image was subjected to image analysis to calculate the number of carbides and the average diameter (area circle equivalent diameter).