CN103827339A - Stainless steel for cutlery and manufacturing process therefor - Google Patents
Stainless steel for cutlery and manufacturing process therefor Download PDFInfo
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- CN103827339A CN103827339A CN201280046446.7A CN201280046446A CN103827339A CN 103827339 A CN103827339 A CN 103827339A CN 201280046446 A CN201280046446 A CN 201280046446A CN 103827339 A CN103827339 A CN 103827339A
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 87
- 239000010935 stainless steel Substances 0.000 title claims abstract description 86
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 33
- 239000000463 material Substances 0.000 claims abstract description 106
- 238000000137 annealing Methods 0.000 claims abstract description 39
- 238000002441 X-ray diffraction Methods 0.000 claims abstract description 25
- 239000010960 cold rolled steel Substances 0.000 claims abstract description 24
- 239000000203 mixture Substances 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 238000005098 hot rolling Methods 0.000 claims description 32
- 238000000034 method Methods 0.000 claims description 21
- 239000007858 starting material Substances 0.000 claims description 16
- 238000005097 cold rolling Methods 0.000 claims description 11
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 230000015572 biosynthetic process Effects 0.000 claims 1
- 230000001747 exhibiting effect Effects 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 31
- 238000005496 tempering Methods 0.000 description 28
- 238000010791 quenching Methods 0.000 description 14
- 230000000171 quenching effect Effects 0.000 description 11
- 238000011156 evaluation Methods 0.000 description 10
- 238000012545 processing Methods 0.000 description 10
- 239000013078 crystal Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000007669 thermal treatment Methods 0.000 description 7
- 239000000047 product Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 5
- 238000013001 point bending Methods 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000001816 cooling Methods 0.000 description 4
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 230000005496 eutectics Effects 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 230000033001 locomotion Effects 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000005457 optimization Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 239000007864 aqueous solution Substances 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 238000012795 verification Methods 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 244000137852 Petrea volubilis Species 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005868 electrolysis reaction Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000003116 impacting effect Effects 0.000 description 1
- 229910001105 martensitic stainless steel Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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Classifications
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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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
-
- 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
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The final purpose of the present invention is to obtain high-hardness and high-toughness cutlery having excellent characteristics. In order to achieve the final purpose, an intermediate material for a stainless steel for cutlery, an annealed material, a cold rolled steel strip, and manufacturing processes for the same are provided. This intermediate material for a stainless steel for cutlery is a hot-rolled intermediate material to be subjected to annealing, said hot-rolled intermediate material having a composition that contains, in mass%, 0.46 to 0.72% of C, 0.15 to 0.55% of Si, 0.45 to 1.00% of Mn, 12.5 to 13.9% of Cr, 0 to 1.5% of Mo, and 0 to 0.012% of B with the balance being Fe and unavoidable impurities, and exhibiting a (diffraction peak area assignable to the fcc phase)/(diffraction peak area assignable to the bcc phase) ratio of 30 or less in the X-ray diffraction of a longitudinal section. The diffraction peak area assignable to the fcc phase is a sum total of diffraction peak areas assignable to the (200), (220) and (311) planes, while the diffraction peak area assignable to the bcc phase is a sum total of diffraction peak areas assignable to the (200) and (211) planes.
Description
Technical field
The present invention relates to the Cutlery Stainless Steel and the manufacture method thereof that in such as razor, cutting knife, kitchen knife, pocket knife etc., use.
Background technology
In the past, martensitic stainless steel was widely used as the cutter material of razor, cutting knife, kitchen knife, pocket knife etc.Particularly the known high carbon martensite that contains by mass% the Cr of 13% left and right and the C of 0.65% left and right is that the material used as razor of stainless band is most suitable.The high carbon martensite using in this purposes is that stainless steel (hereinafter referred to as " Cutlery Stainless Steel ") is conventionally implemented Q-tempering and used, the characteristic such as high rigidity, high tenacity while requiring to use.
Cutlery Stainless Steel is manufactured via following manufacturing process conventionally.
First, raw material is melted, cast and manufacture starting material.Then starting material hot rolling is manufactured to intermediate materials.For starting material, also sometimes via the cogging operation of utilizing forge hot, hot rolling to carry out.
Then, intermediate materials is carried out initial annealing and manufactures annealing material.And then, repeating the cold rolling of necessary number of times only and releasing stress annealing thereupon for annealing material, manufacture has the cold-rolled steel strip of target thickness.Then, cold-rolled steel strip is implemented to Q-tempering, complete Cutlery Stainless Steel.
And then, Cutlery Stainless Steel via putting the first edge on a knife or a pair of scissors, the manufacturing procedure such as cut-out forms the finished product.It should be noted that, the transaction in the market of Cutlery Stainless Steel is carried out mainly with any one form in annealing material or cold-rolled steel strip greatly conventionally.
For above-mentioned Cutlery Stainless Steel, as the technology of reaching high rigidity, high tenacity, various motions are proposed all the time.For example, as representational example, in the Japanese kokai publication hei 5-039547 communique (patent documentation 1) that the application applicant proposes, carry out improving the motion of the carbide density of the cold-rolled steel strip of the Cutlery Stainless Steel before Q-tempering.According to this motion, the short period of time hardenability of cold-rolled steel strip is greatly improved and can improves the hardness of the Cutlery Stainless Steel after quenching, can have excellent sharp sense as razor.
Prior art document
Patent documentation
Patent documentation 1: Japanese kokai publication hei 5-039547 communique
Summary of the invention
the problem that invention will solve
As mentioned above, about the technology that Cutlery Stainless Steel is conceived to the feature of the cold-rolled steel strip before Q-tempering, various motions have been proposed all the time.
But, can say the research that is not almost conceived to the feature of the intermediate materials before hot-roll annealing, hard to say the throwing a flood of light on of relation between the characteristic of annealing material and the characteristic of cold-rolled steel strip of the Cutlery Stainless Steel before quenching afterwards for the feature of this intermediate materials and as the annealing of half products in circulation.
Therefore, there is following problems: the discovery that should have what kind of feature about aforementioned intermediate materials that results from lacks, be not fully guided out excellent characteristic that Cutlery Stainless Steel is original had, particularly can not have high rigidity and high tenacity concurrently.In addition, in the feature of aforementioned intermediate materials for some reason and variation, discover bad problem and bad means the unknown that results from possible trouble of the quality in operation after preventing in the stage of making aforementioned intermediate materials, therefore there is following problems: if under the state of the bad problem producing in the stage of not discovering aforementioned intermediate materials, the operation afterwards that is reduced in of hardness, toughness is showed out first, the operation of having carried out before this is wasted, and the cost of product increases.
Final purpose of the present invention is, the optimization of the aforementioned intermediate materials impacting by the tissue of the Cutlery Stainless Steel to before quenching, effectively obtain the cutter of high rigidity and the high tenacity with excellent characteristic, the invention provides intermediate materials, annealing material and cold-rolled steel strip and their manufacture method of Cutlery Stainless Steel for this reason.
for the scheme of dealing with problems
The inventor etc. are conceived in the feature of Cutlery Stainless Steel, be particularly studied as the form of the carbide of the factor of its hardness of domination and toughness.
First confirmed, in the tissue of the cold-rolled steel strip of Cutlery Stainless Steel, the inhomogeneous existence of carbide or the carbide with thick crystal grain mix with the carbide with thin crystal grain and in the situation pockety of carbide, compared with the equally distributed situation of carbide, hardness and toughness drop during by this cold-rolled steel strip Q-tempering.
Then thoroughly found out, in the feature of the intermediate materials of Cutlery Stainless Steel, particularly composition and the amount of fcc phase impact the distribution of the carbide in the tissue of the cold-rolled steel strip being obtained by aforementioned intermediate materials.
And find, by by the compositional optimization of the intermediate materials of Cutlery Stainless Steel and suppress the amount of fcc phase, can make being evenly distributed of carbide in cold-rolled steel strip, and then can significantly improve the characteristic as the cutter of the finished product, thereby reach the present invention.
, the present invention is a kind of intermediate materials of Cutlery Stainless Steel, it is the intermediate materials of the Cutlery Stainless Steel before hot-roll annealing, composition is C:0.46～0.72% by mass%, Si:0.15～0.55%, Mn:0.45～1.00%, Cr:12.5～13.9%, Mo:0～1.5%, B:0～0.012%, remainder is made up of Fe and impurity, the diffraction peak area that is derived from fcc phase in the X-ray diffraction of longitudinal section (is derived from (200) face, (220) summation of the diffraction peak area of face and (311) face) with the ratio (be derived from the diffraction peak area of fcc phase/be derived from the diffraction peak area of bcc phase) of the diffraction peak area (being derived from the summation of the diffraction peak area of (200) face and (211) face) that is derived from bcc phase be below 30.
Aforementioned B preferably contains with 0.0005～0.0050% scope.
In addition, the present invention is a kind of manufacture method of intermediate materials of Cutlery Stainless Steel, it is the manufacture method of the intermediate materials of aforementioned Cutlery Stainless Steel, the hot rolling starting material of adjusting to aforementioned component are heated to 1100～1250 ℃, carry out hot rolling end temp and be the hot rolling of 700～1000 ℃, make the diffraction peak area that is derived from fcc phase in the X-ray diffraction of longitudinal section (be derived from (200) face, (220) summation of the diffraction peak area of face and (311) face) with the ratio (be derived from the diffraction peak area of fcc phase/be derived from the diffraction peak area of bcc phase) of the diffraction peak area (being derived from the summation of the diffraction peak area of (200) face and (211) face) that is derived from bcc phase be below 30.
The present invention is a kind of manufacture method of annealing material of Cutlery Stainless Steel, and it carries out the annealing of 1～100 hour at 800～860 ℃ after aforementioned hot rolling.
In addition, the manufacture method of the cold-rolled steel strip that the present invention is a kind of Cutlery Stainless Steel, it uses aforementioned annealing material to carry out operation cold rolling and annealing, makes the not enough 1.0mm of thickness.
the effect of invention
Use the cutter of Cutlery Stainless Steel manufacture of the present invention owing to can having high rigidity and high tenacity concurrently, be therefore particularly suitable for most the purposes such as the razor of thin thickness.In addition, according to the present invention, can carry out qualitative control in the stage of intermediate materials rather than the finished product, therefore can suppress bad generation, reduction manufacturing cost.
Accompanying drawing explanation
Fig. 1 is the schematic diagram that represents test film collection position and the face of evaluation.
Fig. 2 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the intermediate materials of Cutlery Stainless Steel of the present invention.
Fig. 3 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the intermediate materials of the Cutlery Stainless Steel of comparative example.
Fig. 4 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the intermediate materials of Cutlery Stainless Steel of the present invention.
Fig. 5 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the intermediate materials of the Cutlery Stainless Steel of comparative example.
Fig. 6 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the intermediate materials of Cutlery Stainless Steel of the present invention.
Fig. 7 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the intermediate materials of Cutlery Stainless Steel of the present invention.
Fig. 8 is the alternative accompanying drawing photo that represents the example to the metallographic structure after the quench-subzero-tempering of the annealing material of Cutlery Stainless Steel of the present invention.
Fig. 9 is the alternative accompanying drawing photo that represents an example of the metallographic structure after the quench-subzero-tempering of annealing material of Cutlery Stainless Steel to comparative example.
Figure 10 is the alternative accompanying drawing photo that represents the example to the metallographic structure after the quench-subzero-tempering of the annealing material of Cutlery Stainless Steel of the present invention.
Figure 11 is the alternative accompanying drawing photo that represents an example of the metallographic structure after the quench-subzero-tempering of annealing material of Cutlery Stainless Steel to comparative example.
Figure 12 is the alternative accompanying drawing photo that represents the example to the metallographic structure after the quench-subzero-tempering of the annealing material of Cutlery Stainless Steel of the present invention.
Figure 13 is the alternative accompanying drawing photo that represents the example to the metallographic structure after the quench-subzero-tempering of the annealing material of Cutlery Stainless Steel of the present invention.
Figure 14 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the cold-rolled steel strip of Cutlery Stainless Steel of the present invention.
Figure 15 is the alternative accompanying drawing photo that represents the example to the metallographic structure after the quench-subzero-tempering of the cold-rolled steel strip of Cutlery Stainless Steel of the present invention.
Figure 16 is the alternative accompanying drawing photo that represents an example of the metallographic structure of the cold-rolled steel strip of Cutlery Stainless Steel of the present invention.
Figure 17 is the alternative accompanying drawing photo that represents the example to the metallographic structure after the quench-subzero-tempering of the cold-rolled steel strip of Cutlery Stainless Steel of the present invention.
Embodiment
As mentioned above, key character of the present invention is, except making the alloy composition optimization of the form that has influence on carbide, controls the amount of the fcc phase in the intermediate materials before annealing, thus for reaching having concurrently of high rigidity and high tenacity as the cutter of the finished product.
First the alloy composition of giving the fundamental characteristics stipulating in the present invention is described.It should be noted that, the content of each element is quality %.
C：0.46～0.72%
Making C is 0.46～0.72%, in order to reach sufficient hardness as cutter and the crystallization of casting, eutectic carbides while solidifying to be suppressed to bottom line.If 0.46% of C less than can not get sufficient hardness as cutter.In addition, if exceed 0.72%,, because the crystallization content of eutectic carbides increases with the balance of Cr amount, become the reason of the sword breach while putting the first edge on a knife or a pair of scissors.Under preferred C amount, be limited to 0.50%, more preferably 0.65%.In addition, preferred C amount on be limited to 0.70%.
Si：0.15～0.55%
The reductor of Si during as refining adds.If Si is residual more than 0.15% to wish to get sufficient deoxidation effect.On the other hand, if exceed 0.55%, inclusion amount increases, and becomes the reason of the sword breach while putting the first edge on a knife or a pair of scissors.Therefore, Si is 0.15～0.55%.In addition, Si has the effect that improves anti-temper softening.In the situation of more than 0.20% adding of Si, can obtain sufficient hardness as cutter.Therefore, preferred Si amount under be limited to 0.20%.In addition, preferred Si amount on be limited to 0.35%.
Mn：0.45～1.00%
Mn and the Si reductor during similarly also as refining adds.If Mn is residual more than 0.45% to wish to get sufficient deoxidation effect.On the other hand, reduce if exceed 1.00% hot workability.Therefore, Mn is 0.45～1.00%.Under preferred Mn amount, be limited to 0.65%.In addition, preferred Mn amount on be limited to 0.85%.
Cr：12.5～13.9%
Making Cr is 12.5～13.9%, in order to reach sufficient solidity to corrosion and the crystallization of casting, eutectic carbides while solidifying to be suppressed to bottom line.If 12.5% of Cr less than can not get sufficient solidity to corrosion as stainless steel, if exceed 13.9%, the crystallization content of eutectic carbides increases, and becomes the reason of the sword breach while putting the first edge on a knife or a pair of scissors.Under preferred Cr amount, be limited to 13.0%.In addition, preferred Cr amount on be limited to 13.6%.
Mo：0～1.5%
Mo, owing to being to improve corrosion proof element, can add using 1.5% as the upper limit as required.If but Mo exceedes 1.5%, solution strengthening grow, resistance to deformation rising and hot workability is deteriorated, therefore the content of Mo is 0～1.5%.
B：0～0.012%
B is effective element for improving hardness and toughness.In the present invention, also can improve toughness by the adjustment of the strength ratio of X ray described later, but by adding in advance B, can obtain effectively the effect that toughness improves.Therefore,, for B, can add using 0.012% as the upper limit.If but B ultrasonic crosses 0.012%, as hot workability, ductility significantly reduces.Therefore B on be limited to 0.012%.It should be noted that, want to obtain more effectively to add by B the hardness and the toughness that realize and improve in the situation of effect, if the effect that 0.0005% B of less than adds is insufficient, therefore make B be advisable in 0.0005～0.0050% scope.
Except above-described element, be Fe and impurity.
As representational impurity element, there are P, S, Ni, W, V, Cu, Al, Ti, N and O, these elements are preferably limited in following scope.
P≤0.03%, S≤0.005%, Ni≤0.15%, W≤0.05%, V≤0.2%, Cu≤0.1%, Al≤0.01%, Ti≤0.01%, N≤0.05% and O≤0.05%.
Find according to the inventor's etc. research, (be derived from (200) face about the diffraction peak area that is derived from fcc phase having in the X-ray diffraction of intermediate materials of Cutlery Stainless Steel of above-mentioned composition, (220) summation of the diffraction peak area of face and (311) face) with the ratio (be derived from the diffraction peak area of fcc phase/be derived from the diffraction peak area of bcc phase) of diffraction peak area (being derived from the summation of the diffraction peak area of (200) face and (211) face) that is derived from bcc phase, with the aforementioned intermediate materials of use, via annealing, cold rolling, quench, the toughness of the Cutlery Stainless Steel that the manufacturing processes such as tempering obtain is relevant.
Particularly, if the diffraction peak area that is derived from fcc phase in the X-ray diffraction of Cutlery Stainless Steel intermediate materials exceedes 30 with the ratio of the diffraction peak area that is derived from bcc phase, form the too much state of amount of fcc phase.If so, while annealing, easily separate out at crystal boundary the carbide that aspect ratio is high after hot-work.Its result, after the Q-tempering carrying out for example, during for cutter, toughness significantly reduces.The ratio that therefore, need to make to be derived from the diffraction peak area of fcc phase/the be derived from diffraction peak area of bcc phase is below 30.Be preferably below 20, more preferably below 5.Lower limit can be 0.
It should be noted that, in the present invention, select (200) face, (220) face and (311) face of fcc phase and (200) face of bcc phase and (211) face be due to, for the alloy system of the composition stipulating in the present invention, aforementioned orientation is the main peak in X-ray diffraction.Beyond aforementioned main peaks, because peak intensity is low, the impact of ratio that is therefore derived from the diffraction peak area of fcc phase/the be derived from diffraction peak area of bcc phase is little.Therefore be exactly, sufficient by the mensuration of aforementioned main peaks.
It should be noted that, the ratio of diffraction peak area of the diffraction peak area of the above-mentioned fcc of being derived from phase/be derived from bcc phase is relevant with the actual volume ratio of each phase, therefore can be used as corresponding to the value of the ratio that forms phase and evaluates.
While carrying out above-mentioned X-ray diffraction, the longitudinal section X-ray irradiation of intermediate materials is carried out.In the application, " longitudinal section " refers to as shown in Figure 1, is equivalent to the section of the evaluation face shown in Fig. 12, perpendicular to the section of the width of intermediate materials near the surface of the test film gathering the center by the width of the intermediate materials 1 of Cutlery Stainless Steel.Longitudinal section is for the reason of evaluating, and rolled stock has the anisotropy of the rolling direction of depending on, and therefore, by fixing evaluation face, can under identical conditions, evaluate.Be in addition due to, in the situation as cutter, longitudinal section is mostly corresponding to the point of a knife having concurrently that requires most high strength and toughness.
For the test film using in X-ray diffraction, by longitudinal section mirror ultrafinish, and then carry out electrolytic polishing, thereby be adjusted into X-ray diffraction test film.Then aforementioned electrolysis abrasive surface is carried out to X-ray diffraction as mensuration face, then, calculate the summation and the ratio of summation of diffraction peak area of (200) face, (211) face that is derived from bcc phase of the diffraction peak area of (200) face, (220) face and (311) face of being derived from fcc phase.While obtaining the area of each diffraction peak, obtain the area of the diffraction peak that has deducted the intensity of background and obtain.
Then the manufacture method of the intermediate materials to Cutlery Stainless Steel of the present invention, annealing material and cold-rolled steel strip describes.
First, by the starting material that melt, Cutlery Stainless Steel is manufactured in casting.Melting can be suitable for the methods such as vacuum melting, atmosphere melt, vacuum arc melts again, electroslag melts again.Casting can obtain starting material by casting, continuous casting etc. to mold.Also can carry out homogenizing thermal treatment to obtained starting material as required.And then can add the cogging operation of utilizing forge hot, hot rolling to carry out.
Then,, by aforementioned starting material hot rolling, manufacture thus the intermediate materials of Cutlery Stainless Steel.For hot rolling, be heated to 1100～1250 ℃, carry out hot rolling, the end temp that makes hot rolling is 700～1000 ℃ of intermediate materials of manufacturing Cutlery Stainless Steel.
Make Heating temperature be 1100～1250 ℃ be due to, under this temperature province, resistance to deformation is lower, have excellent hot workability.If exceed 1250 ℃, become the extreme temperature province reducing of ductility, in the time of hot-work, easily crack.On the other hand, during lower than 1100 ℃, the resistance to deformation of the material in hot rolling is large, be difficult to process with large working modulus, needs to repeat to reheat in hot-work.The preferred lower limit of Heating temperature is 1150 ℃.
In addition, in the present invention, it is in order to consider the hot workability while forming the intermediate materials of Cutlery Stainless Steel and to carry out phase control, metallographic structure control that the end temp that makes hot rolling is 700～1000 ℃.If the end temp of hot rolling exceedes 1000 ℃, the diffraction peak area that is derived from fcc phase in X-ray diffraction increases with the amount that the ratio of diffraction peak area that is derived from bcc phase exceedes 30, fcc phase.If the amount of fcc phase is too much, after implement annealing in, easily at fcc phase crystal boundary carbide precipitate.In addition, if process finishing temperature is high, unrelieved stress is few, and also easily increase of crystal grain diameter, in annealing, separates out in the carbide of fcc phase crystal boundary and easily forms network thus.
Be due to, the end temp of hot rolling during lower than 700 ℃ on the other hand, resistance to deformation increases, is difficult to carry out hot rolling.Therefore, making the Heating temperature of hot-rolled process is that 1100～1250 ℃, the end temp of hot rolling are 700～1000 ℃.Under preferred Heating temperature, be limited to 1150 ℃, preferred end temp on be limited to 950 ℃, preferred end temp on be limited to 900 ℃, preferred end temp under be limited to 750 ℃.
Utilizing above-mentioned hot rolling, making hot worked end temp is the intermediate materials of 700～1000 ℃ of Cutlery Stainless Steels that obtain, and in the threading on runoff table or/and then in batching with take-up mechanism, water is cooled to suitable.With lighting in 5 minutes in the time that the final passage of hot rolling finishes, to obtain being cooled to the water yield of the degree of the speed of cooling below 600 ℃ to be cooled to the coiled material being batched suitable.
This be due to, for batched coiled material, although it is cooling that the face contacting with atmosphere at coiled material temporarily carries out, but the potentiality heat having due to coiled material self, exist and temporarily carried out cooling coiled material surface and again heat up, result is near the front end area of coiled material, central authorities and the mutually different possibility of back-end region metallographic structure.If exceed 600 ℃ in a part of lighting the coiled material batching in 5 minutes in the time that the final passage of hot rolling finishes, likely reduce as the toughness of cutter.
Therefore preferably lighting in 5 minutes in the time that the final passage of hot rolling finishes, undertaken cooling so that the coiled material batching is below 600 ℃ by water.
While finishing above hot-rolled process, can obtain the intermediate materials of the Cutlery Stainless Steel with the tissue stipulating in the present invention.
The intermediate materials of the Cutlery Stainless Steel of manufacturing by above-mentioned manufacture method is carried out at 700 ℃～860 ℃ to the initial annealing of 1～100 hour, manufacture thus the annealing material of the Cutlery Stainless Steel of having separated out carbide.
And then the annealing material that uses above-mentioned Cutlery Stainless Steel is while obtaining cold-rolled steel strip that thickness is the Cutlery Stainless Steel below 1.0mm, can manufacture by repeating cold rolling and annealing.
About the cold-rolled steel strip of above-mentioned Cutlery Stainless Steel, quench, tempering, putting the first edge on a knife or a pair of scissors forms when cutter, sometimes after quenching, carry out as required applying on surface after subzero processing, tempering.
Embodiment
By following embodiment, the present invention will be described in more detail.
Make 6 10kg steel ingots (starting material) of A～F by vacuum melting.The steel ingot chemical composition of A～F is as shown in table 1.
[table 1]
(quality %)
| Steel ingot | C | Si | Mn | Cr | Mo | B |
| A | 0.69 | 0.28 | 0.68 | 13.39 | 0.01 | 0.0001 |
| B | 0.70 | 0.29 | 0.73 | 13.29 | 0.01 | 0.0018 |
| C | 0.70 | 0.29 | 0.73 | 13.25 | 0.01 | 0.0102 |
| D | 0.58 | 0.39 | 0.85 | 13.29 | 0.89 | 0.0002 |
| E | 0.70 | 0,29 | 0.74 | 13.19 | 0.02 | 00005 |
| F | 0.50 | 0.45 | 0.82 | 13.42 | 1.27 | 0.0004 |
| Steel ingot | P | S | Ni | W | V | Cu | AI | Ti | ［N］ | ［Ｏ］ |
| A | 0.024 | 0.0012 | 0.01 | <0.01 | O.０２ | <0.01 | 0.002 | 0.001 | 13 | 61 |
| B | 0.024 | 0.0015 | 0.01 | <0,01 | 0.02 | <0.01 | 0.002 | 0.001 | 12 | 34 |
| C | 0.022 | 0.0015 | 0.01 | <0.01 | 0.02 | <0.01 | 0.003 | 0.001 | 12 | ３０ |
| D | 0.023 | 0.0016 | 0.01 | <0.01 | 0.02 | <0.01 | 0.005 | 0.001 | 13 | ２８ |
| E | 0.021 | 0,0029 | 0.01 | 0.01 | 0.02 | 0.01 | 0.0(36 | 0.003 | 11 | 31 |
| F | 0.G36 | 0.0029 | 0.01 | 0.01 | 0.01 | <0,01 | 0.009 | 0.002 | 10 | 33 |
※ 1.[] shown in the numerical value of element be ppm.
Remainder beyond ※ 2. is above-mentioned is Fe and inevitable impurity.
Made the hot rolling starting material of width 45minx length 1000mmx thickness 20mm by the steel ingot of above-mentioned A～D.Use these hot rollings starting material to carry out hot rolling under following three kinds of conditions, obtain the intermediate materials of Cutlery Stainless Steel.
(1) A～D starting material: be heated to 1180 ℃, finish the operation of hot rolling at 8.50 ℃.
(2) A～C starting material: be heated to 1200 ℃, finish the operation of hot rolling at 10.50 ℃.
(3) E, F starting material: be heated to 1180 ℃, finish the operation of hot rolling at 900 ℃.
It should be noted that, carried out C alloy that the hot rolling of above-mentioned (2) obtains owing to cracking and interruption operation in hot rolling.
In addition, this time, in test, do not obtain only batching the length into coiled material, but confirm lighting in 5 minutes in the time that the final passage of hot rolling finishes, the intermediate materials of Cutlery Stainless Steel is cooled to below 600 ℃.
By near the acquisition test sheet center of the width of the intermediate materials of above-mentioned Cutlery Stainless Steel.It should be noted that, the collection position of test film is the position shown in Fig. 1, is recited as the longitudinal section of evaluation face 2 as the evaluation face of metallographic structure observation, X-ray diffraction and hardness.
Carry out the diffraction peak area that is derived from fcc phase in metallographic structure observation and X-ray diffraction and be derived from the ratio of diffraction peak area of bcc phase and the mensuration of hardness at the longitudinal section of gathered test film.It should be noted that, the test film using in X-ray diffraction is by by longitudinal section mirror ultrafinish and then carry out electrolytic polishing and be adjusted into X-ray diffraction test film.
The alternative accompanying drawing that has represented to carry out the metallographic structure of the material N o.1～6 of metallographic structure observation uses photo as shown in Fig. 2～7.In addition, the diffraction peak area that is derived from fcc phase in X-ray diffraction is as shown in table 2 with ratio and the hardness of diffraction peak area that is derived from bcc phase.In addition, table 3 illustrates the diffraction peak area that is derived from fcc phase and bcc phase for each crystal indices.
For aforementioned metallographic structure is observed, the longitudinal section of test film is being ground to after minute surface, corrode with ferric chloride in aqueous solution, use scanning electronic microscope to observe.
About the diffraction peak area that is derived from fcc phase in X-ray diffraction and the ratio of diffraction peak area that is derived from bcc phase, try to achieve by the diffraction peak area that is derived from fcc phase in X-ray diffraction (being derived from the summation of the diffraction peak area of (200) face, (220) face and (311) face) and the ratio (be derived from the diffraction peak area of fcc phase/be derived from the diffraction peak area of bcc phase) of the diffraction peak area (being derived from the summation of the diffraction peak area of (200) face and (211) face) that is derived from bcc phase.It should be noted that, X-ray diffraction is measured and is used Rigaku Corporation RINT2500V processed, and source of radiation uses Co.
For hardness, cut out test film is carried out after paper grinding with #1200 sand paper, use Vickers hardness tester, measure with 98.1 (N) load.It should be noted that, hardness is 5 average data.
[table 2]
[table 3]
Then, use the intermediate materials of the Cutlery Stainless Steel shown in aforementioned table 2, applicable quenching, subzero processing, tempering while carrying out using as cutter.
Cut out the test film collection intermediate materials of width 40mm × length 100mm × thickness 1mm by the intermediate materials of Cutlery Stainless Steel.Now, cut out test film collection intermediate materials near the mode center of the width that comprises the rolled stock shown in Fig. 1.
The collection of afore-mentioned test sheet is carried out to the annealing of 840 ℃ × 5 hours with intermediate materials, formed after annealing material, as quenching, keep carrying out water-cooled after 1100 ℃ × 3 minutes.And then, after aforementioned quenching, carry out keeping at-75 ℃ the subzero processing of 30 minutes, after aforementioned subzero processing, carry out keeping at 150 ℃ the tempering of 3 minutes.
By 5 of the test films of three point bending test that carried out aforementioned heat treated each test film collection intermediate materials making width 5mm × length 70mm × thickness 0.5mm.
In addition, gathered other test film by near the position (center of the width of rolled stock) that is equivalent to position shown in Fig. 1, become the mode acquisition test sheet of the evaluation face of metallographic structure observation and hardness to be recited as the longitudinal section of evaluation face 2.Metallographic structure photo (No.1～6) is as shown in Fig. 8～13, and hardness, absorption energy, bending strength and the amount of deflection of utilizing three point bending test to obtain are as shown in table 4.
For metallographic structure is observed, evaluation face is ground to after minute surface, corrode with ferric chloride in aqueous solution, use scanning electronic microscope to observe.In three point bending test, measure the test film of width 5mm × length 70mm × thickness 0.5mm with 50mm span (span).It should be noted that, hardness and three point bending test are 5 average data.
[table 4]
Confirmed by table 2 and table 4, in the case of Cutlery Stainless Steel intermediate materials is annealed-is quenched-the diffraction peak area that is derived from fcc phase in the heat treated X-ray diffraction of subzero processing-tempering and the ratio of diffraction peak area that is derived from bcc phase be below 30, even annealing-quench-thermal treatment of subzero processing-tempering after, also maintain high hardness, and the tenacity excellent that can evaluate with the absorption of three point bending test.
The difference of the metallographic structure after the thermal treatment of this can think owing to annealing-quenching-subzero processing-tempering.Particularly this be due to, the diffraction peak area that is derived from fcc phase in the X-ray diffraction of Cutlery Stainless Steel rolled stock exceedes at 30 o'clock with the ratio of the diffraction peak area that is derived from bcc phase, think as confirmed by Fig. 9 and Figure 11, the carbide that the aspect ratio of the Cutlery Stainless Steel rolled stock after thermal treatment is high is connected with crystal boundary and causes toughness drop.
On the other hand, the diffraction peak area that is derived from fcc phase in X-ray diffraction is in the situation below 30 with the ratio of the diffraction peak area that is derived from bcc phase, think as confirmed by Fig. 8, Figure 10, Figure 12 and Figure 13, carbide after thermal treatment can disperse more equably, is formed on the preferred tissue in toughness aspect.
By these results verifications, Cutlery Stainless Steel intermediate materials of the present invention by annealing-quench-thermal treatment of subzero processing-tempering, high and toughness is high as cutter hardness.
In addition we know, the diffraction peak area that is derived from fcc phase in X-ray diffraction be derived from the ratio of diffraction peak area of bcc phase, also contain the B below 0.0050%, make thus the balance of Hardness and toughness more excellent.
Then, cut out the test film collection intermediate materials of width 40mm × length 100mm × thickness 1.5mm by the intermediate materials of the Cutlery Stainless Steel shown in aforementioned No.1 and No.3.Now, cut out test film collection intermediate materials near the mode center of the width that comprises the intermediate materials shown in Fig. 1.
The collection of afore-mentioned test sheet is carried out at 840 ℃ with intermediate materials after the anneal of 10 hours, implemented cold rollingly with small-sized cold-rolling mill, result can make thickness until 0.075mm and can not rupture and obtain cold rolling material.Confirm also can form thus cold-rolled steel strip.
Then,, for aforementioned cold rolling material, as quenching, keep carrying out water-cooled after 1100 ℃ × 40 seconds.And then, after aforementioned quenching, carry out keeping at-75 ℃ the subzero processing of 30 minutes, after aforementioned subzero processing, carry out keeping at 150 ℃ the tempering of 30 seconds.
Use aforementioned cold rolling material and anneal-quench-test film collection starting material after the thermal treatment of subzero processing-tempering, by near position (center of the width of rolled stock) the acquisition test sheet that is equivalent to position shown in Fig. 1, become the mode acquisition test sheet of the evaluation face of metallographic structure observation and hardness to be recited as the longitudinal section of evaluation face 2.The alternative accompanying drawing that represents the metallographic structure (No.1 and 3) of aforementioned hot processing front and back uses photo as shown in Figure 14～17, and hardness is as shown in table 5.
[table 5]
From the result of Figure 14～17 and table 5, for the Cutlery Stainless Steel after cold rolling material of the present invention and quenching, subzero processing and tempering, do not find to make the high carbide of the deteriorated aspect ratio of toughness, the spherical carbide that can obtain good toughness disperses imperceptibly.In addition, the hardness after quenching, subzero processing and tempering also can obtain high rigidity more than 790HV.
By above results verification, the intermediate materials of the Cutlery Stainless Steel of the application of the invention anneals, cold rolling, so quench, subzero processing and tempering, can realize the metallographic structure and the hardness that are suitable for cutter.
utilizability in industry
Use the intermediate materials of Cutlery Stainless Steel of the present invention and the cutter of cold-rolled steel strip manufacture due to hardness and tenacity excellent, therefore can expect to be applicable to razor etc.
description of reference numerals
The intermediate materials of 1 Cutlery Stainless Steel
2 longitudinal sections
Claims (6)
1. the intermediate materials of a Cutlery Stainless Steel, it is characterized in that, it is the intermediate materials of the Cutlery Stainless Steel before hot-roll annealing, composition is C:0.46～0.72% by mass%, Si:0.15～0.55%, Mn:0.45～1.00%, Cr:12.5～13.9%, Mo:0～1.5%, B:0～0.012%, remainder is made up of Fe and impurity, the diffraction peak area that is derived from fcc phase in the X-ray diffraction of longitudinal section is derived from (200) face, (220) the diffraction peak area that ratio that summation of the diffraction peak area of face and (311) face and the diffraction peak area that is derived from bcc phase be derived from the summation of the diffraction peak area of (200) face and (211) face is derived from the diffraction peak area of fcc phase/be derived from bcc phase is below 30.
2. the intermediate materials of Cutlery Stainless Steel according to claim 1, is characterized in that, contains B with 0.0005～0.0050% scope.
3. the manufacture method of the intermediate materials of a Cutlery Stainless Steel, it is characterized in that, it is the manufacture method of the intermediate materials of the Cutlery Stainless Steel before hot-roll annealing, to form is C:0.46～0.72% by mass%, Si:0.15～0.55%, Mn:0.45～1.00%, Cr:12.5～13.9%, Mo:0～1.5%, B:0～0.012%, the starting material that remainder is made up of Fe and impurity are heated to 1100～1250 ℃, carry out hot rolling end temp and be the hot rolling of 700～1000 ℃, the diffraction peak area that is derived from fcc phase in the X-ray diffraction of formation longitudinal section is derived from (200) face, (220) the diffraction peak area that ratio that summation of the diffraction peak area of face and (311) face and the diffraction peak area that is derived from bcc phase be derived from the summation of the diffraction peak area of (200) face and (211) face is derived from the diffraction peak area of fcc phase/be derived from bcc phase is the intermediate materials below 30.
4. the manufacture method of the intermediate materials of Cutlery Stainless Steel according to claim 3, is characterized in that, contains B with 0.0005～0.0050% scope.
5. a manufacture method for the annealing material of Cutlery Stainless Steel, is characterized in that, the intermediate materials of its Cutlery Stainless Steel of manufacturing for the manufacture method by described in claim 3 or 4 carries out the annealing of 1～100 hour at 800～860 ℃.
6. a manufacture method for the cold-rolled steel strip of Cutlery Stainless Steel, is characterized in that, its annealing material for the Cutlery Stainless Steel of manufacturing by manufacture method claimed in claim 5 carries out cold rolling and annealing, makes the not enough 1.0mm of thickness.
Applications Claiming Priority (3)
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| JP2011208430 | 2011-09-26 | ||
| JP2011-208430 | 2011-09-26 | ||
| PCT/JP2012/073621 WO2013047237A1 (en) | 2011-09-26 | 2012-09-14 | Stainless steel for cutlery and manufacturing process therefor |
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| CN103827339A true CN103827339A (en) | 2014-05-28 |
| CN103827339B CN103827339B (en) | 2015-04-01 |
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| Country | Link |
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| US (1) | US20140294662A1 (en) |
| EP (1) | EP2762595B1 (en) |
| JP (1) | JP5333695B1 (en) |
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| CN105568169A (en) * | 2016-01-19 | 2016-05-11 | 溧阳市金昆锻压有限公司 | Martensitic stainless steel circular mould |
| CN107130186A (en) * | 2017-05-25 | 2017-09-05 | 湖北东舟重工科技股份有限公司 | A kind of high-hardenability die steel and its preparation technology |
| CN107699815A (en) * | 2017-11-27 | 2018-02-16 | 上海大学 | High hardness high toughness cutlery stainless steel and preparation method thereof |
| CN110004380A (en) * | 2019-04-04 | 2019-07-12 | 山东泰山钢铁集团有限公司 | A kind of shear steel containing molybdenum |
| TWI774333B (en) * | 2020-04-30 | 2022-08-11 | 日商杰富意鋼鐵股份有限公司 | Stainless steel sheet and its manufacturing method, cutting tools and cutting tools |
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| CN104838031B (en) * | 2013-03-25 | 2017-05-10 | 日立金属株式会社 | Intermediate material for stainless steel for knives |
| JP6635890B2 (en) * | 2016-07-15 | 2020-01-29 | 日鉄ステンレス株式会社 | Martensitic stainless steel sheet for cutting tools with excellent manufacturability and corrosion resistance |
| WO2018051854A1 (en) * | 2016-09-16 | 2018-03-22 | 日立金属株式会社 | Blade material |
| DE102017003965B4 (en) * | 2017-04-25 | 2019-12-12 | Zapp Precision Metals Gmbh | Martensitic chrome steel, steel foil, perforated and / or perforated steel foil component, process for producing a steel foil |
| KR102282041B1 (en) * | 2019-03-12 | 2021-07-28 | 한국과학기술연구원 | Ferritic stainless steels with high strength and toughness and method of manufacturing the same |
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| CN107130186A (en) * | 2017-05-25 | 2017-09-05 | 湖北东舟重工科技股份有限公司 | A kind of high-hardenability die steel and its preparation technology |
| CN107130186B (en) * | 2017-05-25 | 2019-06-18 | 湖北东舟重工科技股份有限公司 | A kind of high-hardenability die steel and its preparation process |
| CN107699815A (en) * | 2017-11-27 | 2018-02-16 | 上海大学 | High hardness high toughness cutlery stainless steel and preparation method thereof |
| CN107699815B (en) * | 2017-11-27 | 2019-08-30 | 上海大学 | High hardness high toughness cutlery stainless steel and preparation method thereof |
| CN110004380A (en) * | 2019-04-04 | 2019-07-12 | 山东泰山钢铁集团有限公司 | A kind of shear steel containing molybdenum |
| TWI774333B (en) * | 2020-04-30 | 2022-08-11 | 日商杰富意鋼鐵股份有限公司 | Stainless steel sheet and its manufacturing method, cutting tools and cutting tools |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2762595A1 (en) | 2014-08-06 |
| WO2013047237A1 (en) | 2013-04-04 |
| CN103827339B (en) | 2015-04-01 |
| EP2762595A4 (en) | 2015-02-25 |
| US20140294662A1 (en) | 2014-10-02 |
| JP5333695B1 (en) | 2013-11-06 |
| EP2762595B1 (en) | 2018-07-04 |
| JPWO2013047237A1 (en) | 2015-03-26 |
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