CN114703345A - Cutter and heat treatment nose tip cooling preparation method thereof - Google Patents
Cutter and heat treatment nose tip cooling preparation method thereof Download PDFInfo
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- CN114703345A CN114703345A CN202210401697.8A CN202210401697A CN114703345A CN 114703345 A CN114703345 A CN 114703345A CN 202210401697 A CN202210401697 A CN 202210401697A CN 114703345 A CN114703345 A CN 114703345A
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B26—HAND CUTTING TOOLS; CUTTING; SEVERING
- B26B—HAND-HELD CUTTING TOOLS NOT OTHERWISE PROVIDED FOR
- B26B9/00—Blades for hand knives
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
- C21D1/44—Methods of heating in heat-treatment baths
- C21D1/46—Salt baths
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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
- C21D9/18—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for knives, scythes, scissors, or like hand 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Crystallography & Structural Chemistry (AREA)
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- Metallurgy (AREA)
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- Forests & Forestry (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The invention provides a method for controlling an endoplasmic structure required by the preparation of a martensitic stainless steel cutter, belonging to the technical field of metal heat treatment. The heat treatment of the martensitic stainless steel is divided into a range of hypoeutectoid steel according to the carbon content, and the control method of the process technology aims to change the structure of a product in the heat treatment phase change of a cutter blank and improve the use adaptability of a civil cutter taking the martensitic stainless steel as a main body. The method comprises the following steps: and slowly cooling the cutter blank which is just quenched at room temperature until the temperature is reduced to 600-500 ℃, quickly cooling the cutter blank, taking out the cutter blank when the temperature is reduced to about 230-140 ℃, and naturally cooling to room temperature to obtain the cutter blank tissue. The method can improve the toughness of the cutter under the condition of the same hardness, reduce the 'sliding edge' feeling and brittleness of the cutter, and the cutter is easier to grind than a quick cooling process when being sharpened after being blunt.
Description
Technical Field
The invention relates to the technical field of metallurgy, in particular to a cutter and a preparation method thereof.
Background
The prior art tools are typically made via rapid cooling of finer grain, typically ferrite + carbon compound + cryptocrystalline or fine crystalline tempered martensite structure. The cutting edge of this tissue often gives a "sliding edge" sensation when the knife hardness is above 54HRC, cutting or peeling.
Disclosure of Invention
In view of the above, the present invention provides a cutting tool and a method for manufacturing the same, which can reduce the "sliding edge" feeling of the cutting tool under the same hardness condition, and the cutting tool is more practical because the cutting edge of the cutting tool is easier to grind than the cutting tool which is rapidly cooled when the cutting tool is ground after being blunt.
In order to achieve the first object, the technical scheme of the cutter provided by the invention is as follows:
the cutter provided by the invention is made of martensitic stainless steel, and the carbon content of the martensitic stainless steel is in the range of hypoeutectoid steel.
The cutter provided by the invention can be further realized by adopting the following technical measures.
Preferably, the metallographic structure of the tool is: ferrite, granular carbon compound, and tempered martensite grain structure with partial newspaper board strip shape or fine root strip shape.
In order to achieve the second object, the technical scheme of the preparation method of the cutter provided by the invention is as follows:
the preparation method of the cutter provided by the invention comprises the following steps;
quenching the cutter blank to obtain a quenched cutter blank;
cooling the quenched cutter blank to 600-500 ℃ to obtain a cooled cutter blank;
rapidly cooling the cooled cutter blank to 230-140 ℃ to obtain an intermediate product;
and taking out the intermediate product and naturally cooling to room temperature to obtain the cutter.
The preparation method of the cutter provided by the invention can be further realized by adopting the following technical measures.
Preferably, in the step process of obtaining the intermediate product by rapidly cooling the cooled knife blank to 230-140 ℃, the rapid cooling is adopted at the tip of a C curve, wherein,
the C curve is a relation curve among time, temperature and structure of super-cooled austenite isothermal transformation.
Preferably, the method for acquiring the C curve includes the following steps:
the eutectoid steel with the same material as the cutter is made into a rod-shaped object with the same size;
dividing the sticks into a plurality of groups, including 1 st group of sticks, 2 nd group of sticks and up to nth group of sticks, wherein n is a natural number greater than or equal to 2;
austenitizing the 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects till the n th group of rod-shaped objects to obtain the 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects till the n th group of rod-shaped objects after austenitizing;
the rod-shaped objects of the 1 st group, the 2 nd group and the rod-shaped objects of the n group after austenitizing are subjected to isothermal transformation under different set temperature conditions respectively, wherein the different set temperatures are below the temperature point of transformation from austenite to pearlite during cooling;
measuring the structure performance of the austenitized 1 st group of rod-shaped objects and 2 nd group of rod-shaped objects until the start time and the end time of the structure transformation of the n th group of rod-shaped objects and the end time of the transformation;
in a coordinate system with temperature data on the ordinate and time data on the abscissa,
the austenitized 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects and the transformation starting point of the tissue structure performance of the n th group of rod-shaped objects are connected to form a transformation starting line,
connecting the austenitized 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects to the transformation end point of the tissue structure performance of the n th group of rod-shaped objects to form a transformation end line,
the transition start line and the transition end line constitute the C curve.
Preferably, the rod-like objects of the same size are in the shape of a cylinder.
Preferably, n is 5, and the isothermal transformation temperature of the group 1 rods is 650 ℃; the isothermal transformation temperature of the rods in the group 2 was 600 ℃; the isothermal transformation temperature of the group 3 rods was 500 ℃; the isothermal transformation temperature of the rods of group 4 was 350 ℃; the isothermal transformation temperature of the rods of group 5 was 230 ℃.
Preferably, the step of measuring the structural properties of the group 1 rods, the group 2 rods, and the group n rods after austenitizing up to the start time and the end time of the transformation is performed by a batch measurement.
Preferably, the austenitized group 1 rods, group 2 rods, and up to group n rods are subjected to isothermal transformation in a salt bath furnace under different set temperature conditions.
Preferably, in the step of measuring the structure properties of the austenitized rods of group 1 and group 2 up to the start time and the end time of the transformation of the rod of group n, the measuring step is performed under a microscope.
According to the cutter prepared by the preparation method provided by the embodiment of the invention, through sensory evaluation, the cutter can reduce the 'sliding edge' feeling of the cutter under the same hardness condition, and the cutting edge of the cutter is easier to grind when being sharpened after being blunted than the cutting edge of the cutter which is rapidly cooled.
Drawings
Various additional advantages and benefits will become apparent to those of ordinary skill in the art upon reading the following detailed description of the preferred embodiments. The drawings are only for purposes of illustrating the preferred embodiments and are not to be construed as limiting the invention. Also, like reference numerals are used to refer to like parts throughout the drawings. In the drawings:
FIG. 1 is a schematic diagram of a curve C according to an embodiment of the present invention;
FIG. 2 is a graph showing a descending cutting depth curve of a kitchen knife and a comparison graph of regrinding according to an embodiment of the present invention.
Detailed Description
In view of the above, the present invention provides a communication method and a communication terminal, which compare an incoming call number with an outgoing call number, and enable a conditional or unconditional connection when the incoming call number is the same as the outgoing call number, thereby being more practical.
To further illustrate the technical means and effects of the present invention adopted to achieve the predetermined objects, the following detailed description of a communication method and a communication terminal according to the present invention with reference to the accompanying drawings and preferred embodiments will be made in detail. In the following description, different "one embodiment" or "an embodiment" refers to not necessarily the same embodiment. Furthermore, the particular features, structures, or characteristics may be combined in any suitable manner in one or more embodiments.
The term "and/or" herein is merely an association describing an associated object, meaning that three relationships may exist, e.g., a and/or B, with the specific understanding that: both a and B may be included, a may be present alone, or B may be present alone, and any of the three cases can be provided.
Cutting tool embodiments
The cutter provided by the invention is made of martensitic stainless steel, and the carbon content of the martensitic stainless steel is in the range of hypoeutectoid steel.
Wherein, the metallographic structure of the cutter is as follows: ferrite, granular carbon compound, and a part of lath or thin lath tempered martensite grain structure.
Method for producing cutting tool
The preparation method of the cutter provided by the invention comprises the following steps;
step S1: quenching the cutter blank to obtain a quenched cutter blank;
step S2: cooling the quenched cutter blank to 600-500 ℃ to obtain a cooled cutter blank; wherein, at 650 ℃ -500 ℃, the alloy material (hypoeutectoid steel) super-cooled austenite in the temperature period has poor stability, and the stability is improved by rapid cooling, which is because the super-cooled austenite at the temperature has large super-cooling degree, more nucleation and instability. The transformation product is a mechanical mixture of ferrite and cementite, and the atomic expansion force is strong. The interlamellar distance of the mixture is smaller than that of critical quenching, so that certain process support is provided for obtaining the lath-shaped martensite structure. Such a cooling method is effective only for stainless steel alloys. Because the alloy elements increase the stability of the undercooled austenite, the transformation of austenite nucleation is delayed, and the hardenability is strong. Even if natural air cooling is carried out, a martensite structure can be obtained, which is different from carbon steel quenching. The super-cooled austenite of carbon steel is extremely unstable and must be rapidly cooled at 840-860 ℃ on A1 to obtain the corresponding martensite structure.
Step S3: rapidly cooling the cooled cutter blank to 230-140 ℃ to obtain an intermediate product; wherein the martensite transformation temperature is 230 ℃, and the martensite structure mainly comprises two basic forms of lath martensite and lamellar martensite. The lath-shaped structure with low carbon content is easy to obtain. The lamellar structure is easy to obtain due to high carbon content. Because the lamellar of the sheet is fine, the sheet is also called cryptocrystal martensite, the strength is high and the brittleness is high. When the martensite is quenched, the transformation starting temperature is 230 ℃, the transformation ending temperature is-50 ℃, the supercooling degree at the temperature is extremely high, the kinetic energy of carbon atoms and iron atoms is small, the carbon atoms and the iron atoms cannot be diffused and only move in a short distance, and all the carbon atoms and the iron atoms are forced to be dissolved in alpha-Fe crystal lattices. At the moment, the cutter blank is taken out for air cooling, thus being beneficial to the formation of lath-shaped martensite structure and being helpful for improving the toughness of the cutter.
Step S4: and taking out the intermediate product and naturally cooling to room temperature to obtain the needed unprocessed cutter blank.
Wherein, in the step process of rapidly cooling the cooled knife blank to 230-140 ℃ to obtain an intermediate product, the rapid cooling is adopted at the tip of a C curve, wherein,
the C curve is a relation curve among time, temperature and structure of the super-cooled austenite isothermal transformation.
The method for acquiring the C curve comprises the following steps:
eutectoid steel which is the same as the cutter in material is made into a rod-shaped object with the same size;
dividing the rods into a plurality of groups, including the 1 st group of rods, the 2 nd group of rods and the nth group of rods, wherein n is a natural number which is greater than or equal to 2;
austenitizing the 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects till the nth group of rod-shaped objects to obtain the 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects till the nth group of rod-shaped objects after austenitizing;
respectively carrying out isothermal transformation on the austenitized group 1 rod-shaped objects, the group 2 rod-shaped objects and the group n rod-shaped objects under different set temperature conditions, wherein the different set temperatures are below the temperature point of transformation from austenite to pearlite during cooling;
measuring the structure performance of the austenitized 1 st group of rod-shaped objects and 2 nd group of rod-shaped objects until the start time and the end time of the structure transformation of the nth group of rod-shaped objects and the end time of the transformation;
in a coordinate system with temperature data on the ordinate and time data on the abscissa,
the rod-shaped objects of the 1 st group and the rod-shaped objects of the 2 nd group after being austenitized are connected to the transformation starting point of the tissue structure performance of the rod-shaped objects of the n th group to form a transformation starting line,
connecting the austenitized 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects to the transformation end point of the tissue structure performance of the n th group of rod-shaped objects to form a transformation end line,
the transition start line and the transition end line constitute a C curve.
Wherein, the rod-shaped objects with the same size are in the shape of a cylinder.
Wherein n is 5, and the isothermal transformation temperature of the group 1 rods is 650 ℃; the isothermal transformation temperature of the rods in the group 2 was 600 ℃; the isothermal transformation temperature of the group 3 rods was 500 ℃; the isothermal transformation temperature of the rods of group 4 was 350 ℃; the isothermal transformation temperature of the rods of group 5 was 230 ℃.
Wherein, in the step of measuring the structure property of the group 1 rod-like object and the group 2 rod-like object after austenitizing to the start time and the end time of the transformation of the n group rod-like object, the measuring method is intermittent measuring.
Wherein, in the step process that the austenitized 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects and the nth group of rod-shaped objects respectively carry out isothermal transformation under different set temperature conditions, the isothermal transformation is finished in a salt bath furnace.
Wherein, in the step of measuring the structure property of the group 1 rod-like object and the group 2 rod-like object after austenitizing to the start time and the end time of the transformation of the nth group rod-like object, the measuring step is carried out under a microscope.
Example 1
Quenching the cutter blank to obtain a quenched cutter blank;
cooling the quenched cutter blank to 600 ℃ to obtain a cooled cutter blank;
rapidly cooling the cooled cutter blank to 230 ℃ to obtain an intermediate product;
and taking out the intermediate product and naturally cooling to room temperature to obtain the cutter.
Wherein, in the step process of rapidly cooling the cooled cutter blank to 230 ℃ to obtain an intermediate product, the rapid cooling is adopted at the tip of a C curve, the group number n of the rodlike objects is 5, and the isothermal transformation temperature of the 1 st group of rodlike objects is 650 ℃; the isothermal transformation temperature of the rods in the group 2 was 600 ℃; the isothermal transformation temperature of the group 3 rods was 500 ℃; the isothermal transformation temperature of the rods of group 4 was 350 ℃; the isothermal transformation temperature of the rods of group 5 was 230 ℃ and the rods were cylindrical in shape.
Examples 2 to 10
The cutting tools obtained according to examples 1 to 10 were able to reduce the "sliding edge" feeling of the cutting tools under the same hardness conditions by sensory evaluation, and were easier to grind with blunt sharpening than the cutting edges of the cutting tools cooled rapidly. Specifically, as shown in fig. 2, the circle in fig. 2 shows a graph of the kitchen knife manufactured by the nose tip cooling heat treatment method according to the embodiment of the present invention, the triangle shows a graph of the kitchen knife manufactured by the rapid cooling heat treatment method, and the schematic diagram of the sliding edge and the regrinding difficulty is formed by combining two graphs, wherein the "sliding edge" is shown by a curve of the descending cutting depth of the kitchen knife, and the regrinding frequency of the cutting edge of the knife to the initial maximum single cutting depth after regrinding is shown. According to a graph of the cutting depth decline of the kitchen knife, the graph is obtained by detecting the sharpness durability according to the national standard of the kitchen knife and using a sharpness durability tester. The X axis is the cutting times n, and the standard period is 30 times; the Y-axis is the single cut depth in mm. According to this standard test, the initial maximum single cut depth of a knife, i.e. the initial maximum sharpness value, can be measured and the sum of the previous three cut values is called ACC sharpness. After 30 cycles of cutting tests, the tool edge became very dull, at which point the edge needed to be reground to return to the original maximum sharpness. From the comparison of the regrinding, it can be seen that the X-axis represents the regrinding times m, and the Y-axis represents the single cutting depth in mm. The stainless steel kitchen knife tool subjected to the sharpness durability test is reground by using the same regrinding equipment and processing method, and the regrinding processing frequency required by the kitchen knife tool obtained by nose tip cooling heat treatment is obviously less than that of the kitchen knife tool obtained by rapid cooling heat treatment on the basis of reaching the initial maximum sharpness value. The brief points obtained by combining two schematic diagrams:
two kinds of kitchen knife tools with different heat removal treatment processes (nose tip cooling and rapid cooling) and the same other elements.
"sliding edge": although the sharp degree ACC value (sum of the cutting depths of the first three times) of the rapid cooling is higher than that of the nose tip cooling heat treatment, after 3 times of cutting, the cutting depth drop value of the kitchen knife cutter of the nose tip cooling heat treatment is slower than that of the rapid cooling, and the sharp value maintaining capability is better than that of the rapid cooling treatment, namely the 'sliding edge' feeling during the use is reduced.
2. The standard sharpness and durability detection method tests two heat removal treatment processes (nose tip cooling and rapid cooling) and other kitchen knife cutters with consistent elements, so that the cutting edge of the kitchen knife cutter is dull and needs to be subjected to regrinding processing. The same regrinding equipment and the same regrinding method are used for regrinding, the regrinding frequency of the kitchen knife tool obtained by nose tip cooling heat treatment is obviously less than that of the kitchen knife tool obtained by quick cooling heat treatment by taking the maximum initial sharpness value as a reference, and the kitchen knife tool product obtained by the nose tip cooling heat treatment is easier to regrind.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (10)
1. A cutting tool, characterized in that the cutting tool is made of a martensitic stainless steel, the carbon content of which is in the range of hypoeutectoid steels.
2. The tool according to claim 1, wherein the metallographic structure of the tool is: ferrite, granular carbon compound, and a part of lath or thin lath tempered martensite grain structure.
3. A method of manufacturing a cutting tool according to claim 1 or 2, characterized by the steps of:
quenching the cutter blank to obtain a quenched cutter blank;
cooling the quenched cutter blank to 600-500 ℃ to obtain a cooled cutter blank;
rapidly cooling the cooled cutter blank to 230-140 ℃ to obtain an intermediate product;
and taking out the intermediate product and naturally cooling to room temperature to obtain the cutter.
4. The method for preparing a cutting tool according to claim 3, wherein during the step of rapidly cooling the cooled tool blank to 230 ℃ -140 ℃ to obtain an intermediate product, the rapid cooling is taken at the tip of the C curve, wherein,
the C curve is a relation curve among time, temperature and structure of super-cooled austenite isothermal transformation.
5. The method for preparing a cutting tool according to claim 4, wherein the method for obtaining the C-curve comprises the following steps:
the eutectoid steel with the same material as the cutter is made into a rod-shaped object with the same size;
dividing the sticks into a plurality of groups, including 1 st group of sticks, 2 nd group of sticks and up to nth group of sticks, wherein n is a natural number greater than or equal to 2;
austenitizing the 1 st group of rod-shaped objects and the 2 nd group of rod-shaped objects till the nth group of rod-shaped objects to obtain the 1 st group of rod-shaped objects, the 2 nd group of rod-shaped objects till the nth group of rod-shaped objects after austenitizing;
the rod-shaped objects of the 1 st group, the 2 nd group and the rod-shaped objects of the n group after austenitizing are subjected to isothermal transformation under different set temperature conditions respectively, wherein the different set temperatures are below the temperature point of transformation from austenite to pearlite during cooling;
measuring the tissue performance of the rod-shaped objects of the 1 st group and the rod-shaped objects of the 2 nd group after the austenitization till the start time and the end time of the tissue transformation of the rod-shaped objects of the n th group and the end time of the tissue transformation;
in a coordinate system with temperature data on the ordinate and time data on the abscissa,
the austenitized rods of group 1 and group 2 were connected to the transformation starting point of the structural properties of the rod of group n and the n point of the final transformation by a wire.
The line from the starting point to the end point of the transformation in the coordinate system is formed into a geometric figure C, so that the line is called a C curve, and some lines are like the nose of a person, so that the line is called a 'nose tip' line.
6. The method for manufacturing a cutting tool according to claim 5, wherein the rod-like objects of the same size are shaped as a cylinder.
7. The method of claim 5, wherein the isothermal transformation temperature of the group 1 rods is 650 ℃; the isothermal transformation temperature of the rods in the group 2 was 600 ℃; the isothermal transformation temperature of the group 3 rods was 500 ℃; the isothermal transformation temperature of the rods of group 4 was 350 ℃; the isothermal transformation temperature of the rods of group 5 was 230 ℃.
8. The method for manufacturing a cutting tool according to claim 5, wherein the step of measuring the properties of the structure of the rods of the group 1 and the rods of the group 2 after austenitizing up to the start time and the end time of the transformation of the rod of the group n is a batch measurement.
9. The method for preparing a cutting tool according to claim 5, wherein the austenitized rods of group 1, group 2 and up to group n are isothermally transformed in a salt bath furnace under different set temperature conditions.
10. The method for manufacturing a cutting tool according to claim 5, wherein the step of measuring the properties of the structure of the austenitized rods of group 1, group 2, and group n up to the start point, the end point, and the end point of the transformation is performed under a microscope.
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| 张浩等: "《钢材轧制及热处理技术》", 北京理工大学出版社, pages: 186 - 123 * |
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