CN103827339B - Stainless steel for cutlery and manufacturing process therefor - Google Patents
Stainless steel for cutlery and manufacturing process therefor Download PDFInfo
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- CN103827339B CN103827339B CN201280046446.7A CN201280046446A CN103827339B CN 103827339 B CN103827339 B CN 103827339B CN 201280046446 A CN201280046446 A CN 201280046446A CN 103827339 B CN103827339 B CN 103827339B
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 86
- 239000010935 stainless steel Substances 0.000 title claims abstract description 86
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 31
- 239000000463 material Substances 0.000 claims abstract description 106
- 238000000137 annealing Methods 0.000 claims abstract description 40
- 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 31
- 239000007858 starting material Substances 0.000 claims description 16
- 238000005097 cold rolling Methods 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 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 14
- 238000011156 evaluation 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
- 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
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting 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
- 229910052799 carbon Inorganic materials 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 239000000155 melt Substances 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 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
- 238000001816 cooling Methods 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
- 229910001105 martensitic stainless steel Inorganic materials 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000005457 optimization 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
- 238000012790 confirmation Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 230000000875 corresponding effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 229910000734 martensite 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
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
-
- 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
-
- 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
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 manufacture method thereof that use in such as razor, cutting knife, kitchen knife, pocket knife etc.
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 stainless band of high-carbon martensitic by mass% containing the Cr of about the 13% and C of about 0.65% is most suitable as the material of razor.The high-carbon martensitic stainless steel (hereinafter referred to as " Cutlery Stainless Steel ") used in this purposes is usually implemented Q-tempering and is used, and requires the characteristic such as high rigidity, high tenacity when using.
Cutlery Stainless Steel manufactures via following manufacturing process usually.
First, raw material is melted, cast and manufacture starting material.Then starting material hot rolling is manufactured intermediate materials.For starting material, also sometimes via the cogging operation utilizing forge hot, hot rolling is carried out.
Then, initial annealing carried out to intermediate materials and manufacture annealing material.And then repeat the cold rolling of only necessary number of times and releasing stress annealing thereupon for annealing material, manufacture has the cold-rolled steel strip of target thickness.Then, Q-tempering is implemented to cold-rolled steel strip, completes 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 usually large to be carried out mainly with any one form in annealing material or cold-rolled steel strip.
For above-mentioned Cutlery Stainless Steel, as the technology reaching high rigidity, high tenacity, propose various motion all the time.Such as representatively example, in the Japanese Unexamined Patent Publication 5-039547 publication (patent documentation 1) that the application applicant proposes, has carried out the motion of the carbide density of the cold-rolled steel strip of the Cutlery Stainless Steel before improving Q-tempering.According to this motion, the short period of time hardenability of cold-rolled steel strip is greatly improved and the hardness of Cutlery Stainless Steel after can improving quenching, can have excellent sharp sense as razor.
Prior art document
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 5-039547 publication
Summary of the invention
the problem that invention will solve
As mentioned above, about the technology of feature Cutlery Stainless Steel being conceived to the cold-rolled steel strip before Q-tempering, propose various motion all the time.
But, the research of the feature of almost not carrying out the intermediate materials before being conceived to hot-roll annealing can be said, throw a flood of light on for the relation between the characteristic of annealing material of the feature of this intermediate materials and the Cutlery Stainless Steel before quenching afterwards as the annealing of half products in circulation and the characteristic of cold-rolled steel strip is hard to say.
Therefore, there is following problems: result from about aforementioned intermediate materials should have what kind of feature discovery lack, be not fully guided out the characteristic of original the had excellence of Cutlery Stainless Steel, particularly can not have high rigidity and high tenacity concurrently.In addition, when in the preamble, the feature of material changes for some reason, making that stage of aforementioned intermediate materials discovers bad problem, the bad means resulting from possible trouble of quality after preventing in operation are unknown, therefore there is following problems: if under the state of the bad problem produced in the stage not discovering aforementioned intermediate materials, operation after being reduced in of hardness, toughness is showed out first, the operation of then having carried out before this is wasted, and the cost of product increases.
Final purpose of the present invention is, by the optimization of aforementioned intermediate materials impacted the tissue of Cutlery Stainless Steel before quenching, effectively obtain there is the excellent high rigidity of characteristic and the cutter of high tenacity, the invention provides the intermediate materials of Cutlery Stainless Steel, annealing material and cold-rolled steel strip and their manufacture method for this reason.
for the scheme of dealing with problems
The present 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 confirm, in the tissue of the cold-rolled steel strip of Cutlery Stainless Steel, the uneven 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 during this cold-rolled steel strip Q-tempering and toughness are reduced.
Then thoroughly found out, in the feature of the intermediate materials of Cutlery Stainless Steel, particularly the distribution of amount to the carbide in the tissue of the cold-rolled steel strip obtained by aforementioned intermediate materials of composition and fcc phase impacts.
And find, suppressed the amount of fcc phase by the compositional optimization of the intermediate materials by Cutlery Stainless Steel, being evenly distributed of the carbide in cold-rolled steel strip can be made, and then significantly can improve the characteristic of the cutter as the finished product, thus reach the present invention.
Namely, 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 areas being derived from fcc phase in the X-ray diffraction of longitudinal section (is derived from (200) face, (220) summation of the diffraction peak areas in face and (311) face) be less than 30 with the ratio (being derived from the diffraction peak areas of the diffraction peak areas of fcc phase/be derived from bcc phase) of the diffraction peak areas (being derived from the summation of (200) face and the diffraction peak areas in (211) face) being derived from bcc phase.
Aforementioned B preferably contains with the scope of 0.0005 ~ 0.0050%.
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 adjusting to aforementioned component are heated to 1100 ~ 1250 DEG C, carry out the hot rolling that hot rolling end temp is 700 ~ 1000 DEG C, the diffraction peak areas being derived from fcc phase in the X-ray diffraction of longitudinal section is made (to be derived from (200) face, (220) summation of the diffraction peak areas in face and (311) face) be less than 30 with the ratio (being derived from the diffraction peak areas of the diffraction peak areas of fcc phase/be derived from bcc phase) of the diffraction peak areas (being derived from the summation of (200) face and the diffraction peak areas in (211) face) being derived from bcc phase.
The present invention is a kind of manufacture method of annealing material of Cutlery Stainless Steel, and it is after aforementioned hot rolling, carries out the annealing of 1 ~ 100 hour at 800 ~ 860 DEG C.
In addition, the present invention is a kind of manufacture method of cold-rolled steel strip of Cutlery Stainless Steel, and it uses aforementioned annealing material to carry out operation that is cold rolling and annealing, makes thickness less than 1.0mm.
the effect of invention
Use the cutter of Cutlery Stainless Steel manufacture of the present invention due to high rigidity and high tenacity can be had concurrently, be therefore particularly most suitable for the purposes such as the thin razor of thickness.In addition, according to the present invention, qualitative control can be carried out in the stage of intermediate materials instead of the finished product, therefore, it is possible to suppress bad generation, reduce manufacturing cost.
Accompanying drawing explanation
Fig. 1 is the schematic diagram representing test film collection position and the face of evaluation.
Fig. 2 is the alternative accompanying drawing photo of an example of the metallographic structure of the intermediate materials representing Cutlery Stainless Steel of the present invention.
Fig. 3 is the alternative accompanying drawing photo of an example of the metallographic structure of the intermediate materials of the Cutlery Stainless Steel representing comparative example.
Fig. 4 is the alternative accompanying drawing photo of an example of the metallographic structure of the intermediate materials representing Cutlery Stainless Steel of the present invention.
Fig. 5 is the alternative accompanying drawing photo of an example of the metallographic structure of the intermediate materials of the Cutlery Stainless Steel representing comparative example.
Fig. 6 is the alternative accompanying drawing photo of an example of the metallographic structure of the intermediate materials representing Cutlery Stainless Steel of the present invention.
Fig. 7 is the alternative accompanying drawing photo of an example of the metallographic structure of the intermediate materials representing Cutlery Stainless Steel of the present invention.
Fig. 8 be represent to the annealing material of Cutlery Stainless Steel of the present invention quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Fig. 9 be represent to the annealing material of the Cutlery Stainless Steel of comparative example quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Figure 10 be represent to the annealing material of Cutlery Stainless Steel of the present invention quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Figure 11 be represent to the annealing material of the Cutlery Stainless Steel of comparative example quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Figure 12 be represent to the annealing material of Cutlery Stainless Steel of the present invention quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Figure 13 be represent to the annealing material of Cutlery Stainless Steel of the present invention quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Figure 14 is the alternative accompanying drawing photo of an example of the metallographic structure of the cold-rolled steel strip representing Cutlery Stainless Steel of the present invention.
Figure 15 be represent to the cold-rolled steel strip of Cutlery Stainless Steel of the present invention quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Figure 16 is the alternative accompanying drawing photo of an example of the metallographic structure of the cold-rolled steel strip representing Cutlery Stainless Steel of the present invention.
Figure 17 be represent to the cold-rolled steel strip of Cutlery Stainless Steel of the present invention quench-subzero-tempering after the alternative accompanying drawing photo of an example of metallographic structure.
Embodiment
As mentioned above, key character of the present invention is, except making except the alloy composition of the form having influence on carbide optimizes, to control the amount of fcc phase in the intermediate materials before annealing, reaches having concurrently of high rigidity and high tenacity thus for the cutter as the finished product.
First the alloy composition giving the fundamental characteristics specified 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 be 0.46 ~ 0.72% is to reach sufficient hardness as cutter and suppressing the crystallization of eutectic carbides when casting, solidify at bottom line.If C is less than 0.46%, can not get sufficient hardness as cutter.In addition, if more than 0.72%, then due to the balance measured with Cr and the crystallization content of eutectic carbides increase, become the reason of sword breach when putting the first edge on a knife or a pair of scissors.The lower limit of preferred C amount is 0.50%, more preferably 0.65%.In addition, the upper limit of preferred C amount is 0.70%.
Si：0.15～0.55%
Si adds as reductor during refining.If wish to get sufficient deoxidation effect, Si residual more than 0.15%.On the other hand, if more than 0.55%, then inclusion amount increases, and becomes the reason of sword breach when 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 improving anti-temper softening.Si more than 0.20% add when, sufficient hardness can be obtained as cutter.Therefore, the lower limit of preferred Si amount is 0.20%.In addition, the upper limit of preferred Si amount is 0.35%.
Mn：0.45～1.00%
Mn and Si similarly also adds as reductor during refining.If wish to get sufficient deoxidation effect, Mn residual more than 0.45%.On the other hand, if more than 1.00%, hot workability reduces.Therefore, Mn is 0.45 ~ 1.00%.The lower limit of preferred Mn amount is 0.65%.In addition, the upper limit of preferred Mn amount is 0.85%.
Cr：12.5～13.9%
Making Cr be 12.5 ~ 13.9% is to reach sufficient solidity to corrosion and suppressing the crystallization of eutectic carbides when casting, solidify at bottom line.If Cr is less than 12.5%, can not get sufficient solidity to corrosion as stainless steel, if more than 13.9%, then the crystallization content of eutectic carbides increases, and becomes the reason of sword breach when putting the first edge on a knife or a pair of scissors.The lower limit of preferred Cr amount is 13.0%.In addition, the upper limit of preferred Cr amount is 13.6%.
Mo：0～1.5%
Mo, owing to being improve corrosion proof element, can add using 1.5% as the upper limit as required.If but Mo is more than 1.5%, then 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 raising 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 B in advance, the effect that toughness improves can be obtained effectively.Therefore, for B, can add using 0.012% as the upper limit.If but B ultrasonic crosses 0.012%, then as hot workability, ductility significantly reduces.Therefore the upper limit of B is 0.012%.It should be noted that, for obtain more effectively by B add the hardness that realizes and toughness improve effect when, if the effect of adding less than 0.0005%, B is insufficient, be advisable in the scope therefore making B be in 0.0005 ~ 0.0050%.
Be Fe and impurity except above-described element.
Representatively impurity element, has P, S, Ni, W, V, Cu, Al, Ti, N and O, and 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%.
Research according to the present inventor etc. finds, about have above-mentioned composition Cutlery Stainless Steel intermediate materials X-ray diffraction in the diffraction peak areas being derived from fcc phase (be derived from (200) face, (220) summation of the diffraction peak areas in face and (311) face) with the ratio (being derived from the diffraction peak areas of the diffraction peak areas of fcc phase/be derived from bcc phase) of diffraction peak areas (being derived from the summation of (200) face and the diffraction peak areas in (211) face) being derived from bcc phase, with the aforementioned intermediate materials of use, via annealing, cold rolling, quenching, the toughness of the Cutlery Stainless Steel that the manufacturing processes such as tempering obtain is correlated with.
Specifically, if the diffraction peak areas being derived from fcc phase in the X-ray diffraction of Cutlery Stainless Steel intermediate materials be derived from the ratio of diffraction peak areas of bcc phase more than 30, then form the state that the amount of fcc phase is too much.If so, then when annealing after hot working, easily separate out the high carbide of aspect ratio at crystal boundary.Its result, such as, for after the Q-tempering that carries out during cutter, toughness significantly reduces.Therefore, the ratio needing to make to be derived from the diffraction peak areas of fcc phase/the be derived from diffraction peak areas of bcc phase is less than 30.Be preferably less than 20, more preferably less than 5.Lower limit can be 0.
It should be noted that, select in the present invention (200) face of fcc phase, (200) face of (220) face and (311) face and bcc phase and (211) face be due to, for the alloy system of the composition specified 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 being therefore derived from the diffraction peak areas of fcc phase/the be derived from ratio of the diffraction peak areas of bcc phase is little.Therefore, be exactly sufficient by the mensuration of aforementioned main peaks.
It should be noted that, the ratio of the diffraction peak areas of the above-mentioned fcc of being derived from phase/the be derived from diffraction peak areas of bcc phase is relevant to the volume ratio of the reality of each phase, therefore can evaluate as the value corresponding to the ratio forming phase.
When 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 in the evaluation face shown in Fig. 12, namely perpendicular to the section of the width of intermediate materials in the surface by the test film of the immediate vicinity collection of the width of the intermediate materials 1 of Cutlery Stainless Steel.The reason being used for evaluating by longitudinal section is, rolled stock has the anisotropy depending on rolling direction, therefore by fixing evaluation face, can evaluate under identical conditions.Be in addition due to, when as cutter, longitudinal section mostly corresponds to and requires the point of a knife had concurrently of high strength and toughness most.
For the test film used in X-ray diffraction, by longitudinal section mirror ultrafinish, and then carry out electrolytic polishing, thus be adjusted to X-ray diffraction test film.Then X-ray diffraction is carried out as mensuration face in aforementioned electrolytic polishing face, then, calculate be derived from fcc phase (200) face, the summation of diffraction peak areas in (220) face and (311) face and the ratio of summation being derived from (200) face of bcc phase, the diffraction peak areas in (211) face.When obtaining the area of each diffraction peak, obtain the area of the intensity having deducted background and the diffraction peak obtained.
Then the intermediate materials of Cutlery Stainless Steel of the present invention, the manufacture method of anneal material and cold-rolled steel strip are described.
First, by melting, casting the starting material manufacturing Cutlery Stainless Steel.Melting can be suitable for the methods such as vacuum melting, air melts, vacuum arc melts again, electroslag melts again.Casting can obtain starting material by the casting to mold, continuous casting etc.Also homogenizing thermal treatment can be carried out to obtained starting material as required.And then can add utilize forge hot, cogging operation that hot rolling is carried out.
Then, by aforementioned starting material hot rolling, the intermediate materials of Cutlery Stainless Steel is manufactured thus.For hot rolling, be heated to 1100 ~ 1250 DEG C, carry out hot rolling, make the end temp of hot rolling be 700 ~ 1000 DEG C of intermediate materials manufacturing Cutlery Stainless Steel.
Make Heating temperature be 1100 ~ 1250 DEG C to be due to, under this temperature province, resistance to deformation is lower, have excellent hot workability.If more than 1250 DEG C, then become the temperature province that ductility extremely reduces, easily crack when hot-work.On the other hand, during lower than 1100 DEG C, 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 DEG C.
In addition, in the present invention, make the end temp of hot rolling be 700 ~ 1000 DEG C to be in order to hot workability when considering the intermediate materials forming Cutlery Stainless Steel and carry out phase control, metallographic structure controls.If the end temp of hot rolling is more than 1000 DEG C, then the diffraction peak areas being derived from fcc phase in X-ray diffraction increases more than the amount of 30, fcc phase with the ratio of the diffraction peak areas being derived from bcc phase.If the amount of fcc phase is too much, then in the annealing implemented afterwards, easily at fcc phase crystal boundary carbide precipitate.In addition, if process finishing temperature is high, then unrelieved stress is few, and crystal grain diameter also easily increases, and thus in annealing, the carbide of separating out in fcc phase crystal boundary easily forms network.
Be on the other hand due to, when the end temp of hot rolling is lower than 700 DEG C, resistance to deformation increases, is difficult to carry out hot rolling.Therefore, make that the Heating temperature of hot-rolled process is 1100 ~ 1250 DEG C, the end temp of hot rolling is 700 ~ 1000 DEG C.The lower limit of preferred Heating temperature is 1150 DEG C, the upper limit of preferred end temp is 950 DEG C, the upper limit of preferred end temp is 900 DEG C, the lower limit of preferred end temp is 750 DEG C.
The intermediate materials utilizing above-mentioned hot rolling, make hot worked end temp be the Cutlery Stainless Steel that 700 ~ 1000 DEG C obtain, in threading on the run-out table or/and then during proper take-up mechanism batches, uses water to carry out being cooled to suitable.Lighting within 5 minutes at the end of the final passage from hot rolling, obtain batched coiled material can being cooled to the water yield of the degree of the speed of cooling of less than 600 DEG C to carry out being cooled to suitable.
This be due to, for batched coiled material, although temporarily cool in the face of coiled material and atmosphere, but due to the potentiality heat that coiled material self has, there is the coiled material surface that temporarily cool again to heat up, result coiled material front end area, central near and the mutually different possibility of back-end region metallographic structure.If light a part for the coiled material batched within 5 minutes more than 600 DEG C at the end of the final passage from hot rolling, then the toughness as cutter likely reduces.
Therefore preferably light within 5 minutes at the end of the final passage from hot rolling, undertaken cooling to make batched coiled material be less than 600 DEG C by water.
When terminating above hot-rolled process, the intermediate materials of the Cutlery Stainless Steel with the tissue specified in the present invention can be obtained.
The intermediate materials of the Cutlery Stainless Steel manufactured by above-mentioned manufacture method is carried out at 700 DEG C ~ 860 DEG C to the initial annealing of 1 ~ 100 hour, manufacture the annealing material of having separated out the Cutlery Stainless Steel of carbide thus.
And then when using the annealing material of above-mentioned Cutlery Stainless Steel to obtain the cold-rolled steel strip of the Cutlery Stainless Steel that thickness is below 1.0mm, by repeating cold rolling and annealing and can manufacture.
About the cold-rolled steel strip of above-mentioned Cutlery Stainless Steel, carry out quenching, tempering, put the first edge on a knife or a pair of scissors when forming cutter, apply on surface after sometimes carrying out subzero process, tempering after quenching as required.
Embodiment
By following embodiment, the present invention will be described in more detail.
6 10kg steel ingots (starting material) of A ~ F are made 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 |
The numerical value of the element shown in ※ 1. [] is ppm.
※ 2. remainder other than the above is Fe and inevitable impurity.
The hot rolling starting material of width 45minx length 1000mmx thickness 20mm are made by the steel ingot of above-mentioned A ~ D.Use these hot rolling 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 DEG C, terminate the operation of hot rolling at 8.50 DEG C.
(2) A ~ C starting material: be heated to 1200 DEG C, terminate the operation of hot rolling at 10.50 DEG C.
(3) E, F starting material: be heated to 1180 DEG C, terminate the operation of hot rolling at 900 DEG C.
It should be noted that, the C alloy that the hot rolling having carried out above-mentioned (2) obtains owing to cracking and interruption operation in hot rolling.
In addition, this time in test, only batched the length into coiled material, but confirmation is lighted at the end of the final passage from hot rolling within 5 minutes, the intermediate materials of Cutlery Stainless Steel is cooled to less than 600 DEG C.
By the immediate vicinity acquisition test sheet 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, and the longitudinal section being recited as evaluation face 2 is as the evaluation face of metallographic structure observation, X-ray diffraction and hardness.
The diffraction peak areas being derived from fcc phase in metallographic structure observation and X-ray diffraction and the ratio of diffraction peak areas and the mensuration of hardness that are derived from bcc phase is carried out at the longitudinal section of gathered test film.It should be noted that, the test film used in X-ray diffraction passes through longitudinal section mirror ultrafinish and then carries out electrolytic polishing and be adjusted to X-ray diffraction test film.
Represent that the alternative accompanying drawing photo of the metallographic structure having carried out the material N o.1 ~ 6 that metallographic structure is observed is as shown in Fig. 2 ~ 7.In addition, the diffraction peak areas being derived from fcc phase in X-ray diffraction is as shown in table 2 with the ratio of diffraction peak areas and hardness being derived from bcc phase.In addition, table 3 illustrates the diffraction peak areas being derived from fcc phase and bcc phase for each crystal indices.
For aforementioned metallographic structure is observed, after the longitudinal section of test film is ground to minute surface, corrode with ferric chloride in aqueous solution, use scanning electronic microscope to observe.
About the diffraction peak areas being derived from fcc phase in X-ray diffraction and the ratio of diffraction peak areas being derived from bcc phase, tried to achieve by the ratio (being derived from the diffraction peak areas of the diffraction peak areas of fcc phase/be derived from bcc phase) of the diffraction peak areas (being derived from the summation of diffraction peak areas in (200) face, (220) face and (311) face) being derived from fcc phase in X-ray diffraction with the diffraction peak areas (being derived from the summation of (200) face and the diffraction peak areas in (211) face) being derived from bcc phase.It should be noted that, X-ray diffraction measures and uses Rigaku Corporation RINT2500V, and source of radiation uses Co.
For hardness, after paper grinding is carried out to cut out test film #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, the intermediate materials of the Cutlery Stainless Steel shown in aforementioned table 2 is used, the quenching be suitable for when carrying out using as cutter, subzero process, tempering.
The test film collection intermediate materials of width 40mm × length 100mm × thickness 1mm is cut out by the intermediate materials of Cutlery Stainless Steel.Now, test film collection intermediate materials is cut out in the mode of the immediate vicinity comprising the width of the rolled stock shown in Fig. 1.
Afore-mentioned test sheet collection intermediate materials is carried out to the annealing of 840 DEG C × 5 hours, after forming annealing material, as quenching, keep carrying out water-cooled after 1100 DEG C × 3 minutes.And then, after aforementioned quenching, at carrying out-75 DEG C, keep the subzero process of 30 minutes, after aforementioned subzero process, carry out the tempering keeping 3 minutes at 150 DEG C.
By the three point bending test test film 5 having 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 the position (immediate vicinity of the width of rolled stock) being equivalent to position shown in Fig. 1, become the mode acquisition test sheet in the evaluation face of metallographic structure observation and hardness with the longitudinal section being recited as evaluation face 2.As depicted in figures 8-13, hardness, the absorption energy, bending strength and the amount of deflection that utilize three point bending test to obtain are as shown in table 4 for metallographic structure photo (No.1 ~ 6).
For metallographic structure is observed, after evaluation face is ground to 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, when annealing to Cutlery Stainless Steel intermediate materials-quench-the heat treated X-ray diffraction of subzero process-tempering in the diffraction peak areas being derived from fcc phase when being less than 30 with the ratio of the diffraction peak areas being derived from bcc phase, even if annealing-quench-thermal treatment of subzero process-tempering after, also high hardness is maintained, and with the tenacity excellent that the absorption of three point bending test can be evaluated.
This can think owing to annealing-quenching-thermal treatment of subzero process-tempering after the difference of metallographic structure.Specifically this be due to, the diffraction peak areas being derived from fcc phase in the X-ray diffraction of Cutlery Stainless Steel rolled stock with the ratio of diffraction peak areas being derived from bcc phase more than 30 time, 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 to reduce.
On the other hand, when the diffraction peak areas being derived from fcc phase in X-ray diffraction is less than 30 with the ratio of the diffraction peak areas being derived from bcc phase, think as confirmed by Fig. 8, Figure 10, Figure 12 and Figure 13, carbide after thermal treatment can more uniformly disperse, and is formed in the preferred tissue in toughness aspect.
By these results verifications, Cutlery Stainless Steel intermediate materials of the present invention by carrying out annealing-quench-thermal treatment of subzero process-tempering, as cutter hardness is high and toughness is high.
In addition we know, except the diffraction peak areas being derived from fcc phase in X-ray diffraction and the ratio of diffraction peak areas being derived from bcc phase, also containing less than 0.0050% B, make the balance of Hardness and toughness more excellent thus.
Then, the test film collection intermediate materials of width 40mm × length 100mm × thickness 1.5mm is cut out by the intermediate materials of the Cutlery Stainless Steel shown in aforementioned No.1 and No.3.Now, test film collection intermediate materials is cut out in the mode of the immediate vicinity comprising the width of the intermediate materials shown in Fig. 1.
After carrying out the anneal of 10 hours to afore-mentioned test sheet collection intermediate materials at 840 DEG C, implement cold rolling with small-sized cold-rolling mill, result can make thickness until 0.075mm and can not obtain cold rolling material with rupturing.Confirm thus also can form cold-rolled steel strip.
Then, for aforementioned cold rolling material, as quenching, keep carrying out water-cooled after 1100 DEG C × 40 seconds.And then, after aforementioned quenching, at carrying out-75 DEG C, keep the subzero process of 30 minutes, after aforementioned subzero process, carry out the tempering keeping 30 seconds at 150 DEG C.
Use aforementioned cold rolling material and anneal-quench-thermal treatment of subzero process-tempering after test film collection starting material, by position (immediate vicinity of the width of rolled stock) the acquisition test sheet being equivalent to position shown in Fig. 1, become the mode acquisition test sheet in the evaluation face of metallographic structure observation and hardness with the longitudinal section being recited as evaluation face 2.Represent that the alternative accompanying drawing photo of the metallographic structure (No.1 and 3) before and after aforementioned hot process is as shown in Figure 14 ~ 17, 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 process and tempering, do not find the carbide making the aspect ratio of toughness deterioration high, the spherical carbide that can obtain good toughness disperses imperceptibly.In addition, the hardness after quenching, subzero process and tempering also can obtain the high rigidity of more than 790HV.
By above results verification, the intermediate materials of the Cutlery Stainless Steel of the application of the invention carries out annealing, cold rolling, so carry out quenching, subzero process and tempering, the metallographic structure and the hardness that are suitable for cutter can be realized.
utilizability in industry
Use cutter that the intermediate materials of Cutlery Stainless Steel of the present invention and 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, namely the diffraction peak areas being derived from fcc phase in the X-ray diffraction of longitudinal section is derived from (200) face, (220) namely summation and the diffraction peak areas being derived from bcc phase of the diffraction peak areas in face and (311) face are derived from the diffraction peak areas that namely (200) face and the ratio of the summation of the diffraction peak areas in (211) face be derived from the diffraction peak areas of fcc phase/be derived from bcc phase is less than 30.
2. the intermediate materials of Cutlery Stainless Steel according to claim 1, is characterized in that, contains B with the scope of 0.0005 ~ 0.0050%.
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 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 DEG C, carry out the hot rolling that hot rolling end temp is 700 ~ 1000 DEG C, namely the diffraction peak areas being derived from fcc phase formed in the X-ray diffraction of longitudinal section is derived from (200) face, (220) namely summation and the diffraction peak areas being derived from bcc phase of the diffraction peak areas in face and (311) face are derived from the diffraction peak areas that namely (200) face and the ratio of the summation of the diffraction peak areas in (211) face be derived from the diffraction peak areas of fcc phase/be derived from bcc phase is the intermediate materials of less than 30.
4. the manufacture method of the intermediate materials of Cutlery Stainless Steel according to claim 3, is characterized in that, described intermediate materials contains B with the scope of 0.0005 ~ 0.0050%.
5. a manufacture method for the annealing material of Cutlery Stainless Steel, is characterized in that, it, for the intermediate materials of the Cutlery Stainless Steel manufactured by the manufacture method described in claim 3 or 4, carries out the annealing of 1 ~ 100 hour at 800 ~ 860 DEG C.
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 manufactured by manufacture method according to claim 5 carries out cold rolling and annealing, makes thickness less than 1.0mm.
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| JP2011-208430 | 2011-09-26 | ||
| JP2011208430 | 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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| CN103827339B true CN103827339B (en) | 2015-04-01 |
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| US (1) | US20140294662A1 (en) |
| EP (1) | EP2762595B1 (en) |
| JP (1) | JP5333695B1 (en) |
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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 |
| CN105568169A (en) * | 2016-01-19 | 2016-05-11 | 溧阳市金昆锻压有限公司 | Martensitic stainless steel circular mould |
| 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 |
| CN109563584A (en) * | 2016-09-16 | 2019-04-02 | 日立金属株式会社 | Cutter raw 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 |
| 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 |
| CN107699815B (en) * | 2017-11-27 | 2019-08-30 | 上海大学 | High hardness high toughness cutlery stainless steel and preparation method thereof |
| KR102282041B1 (en) * | 2019-03-12 | 2021-07-28 | 한국과학기술연구원 | Ferritic stainless steels with high strength and toughness and method of manufacturing the same |
| 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 |
| MX2022013630A (en) * | 2020-04-30 | 2023-01-24 | Jfe Steel Corp | Stainless steel sheet, method for producing same, edged tools and cutlery. |
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| JPH0920923A (en) * | 1995-07-05 | 1997-01-21 | Sumitomo Metal Ind Ltd | Production of high carbon stainless steel plate |
| JP2007224405A (en) * | 2006-02-27 | 2007-09-06 | Jfe Steel Kk | Steel for blade |
| JP2009270196A (en) * | 2008-04-09 | 2009-11-19 | Hitachi Metals Ltd | Manufacturing method of band steel for blade |
| CN101643886A (en) * | 2009-08-31 | 2010-02-10 | 武汉钢铁(集团)公司 | Stainless steel for cutter and manufacture method thereof |
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| EP0485641B1 (en) * | 1990-11-10 | 1994-07-27 | Wilkinson Sword Gesellschaft mit beschränkter Haftung | Razor blade steel having high corrosion resistance, razor blades and a process for manufacturing razor blades |
| JP3354163B2 (en) | 1991-08-05 | 2002-12-09 | 日立金属株式会社 | Stainless steel for razor and method for producing the same |
| TW338729B (en) * | 1996-09-30 | 1998-08-21 | Kawasaki Steel Co | Hot roll stainless steel tape and the manufacturing method |
| US6733601B2 (en) * | 2001-01-18 | 2004-05-11 | Jfe Steel Corporation | Ferritic stainless steel sheet with excellent workability |
| EP1591547B1 (en) * | 2004-04-27 | 2007-12-26 | Hitachi Metals, Ltd. | Steel strip for a replacement blade and manufacturing method therefor |
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2012
- 2012-09-14 CN CN201280046446.7A patent/CN103827339B/en active Active
- 2012-09-14 JP JP2013513470A patent/JP5333695B1/en active Active
- 2012-09-14 WO PCT/JP2012/073621 patent/WO2013047237A1/en active Application Filing
- 2012-09-14 US US14/346,740 patent/US20140294662A1/en not_active Abandoned
- 2012-09-14 EP EP12836077.3A patent/EP2762595B1/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0920923A (en) * | 1995-07-05 | 1997-01-21 | Sumitomo Metal Ind Ltd | Production of high carbon stainless steel plate |
| JP2007224405A (en) * | 2006-02-27 | 2007-09-06 | Jfe Steel Kk | Steel for blade |
| JP2009270196A (en) * | 2008-04-09 | 2009-11-19 | Hitachi Metals Ltd | Manufacturing method of band steel for blade |
| CN101643886A (en) * | 2009-08-31 | 2010-02-10 | 武汉钢铁(集团)公司 | Stainless steel for cutter and manufacture method thereof |
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| EP2762595A1 (en) | 2014-08-06 |
| WO2013047237A1 (en) | 2013-04-04 |
| JPWO2013047237A1 (en) | 2015-03-26 |
| JP5333695B1 (en) | 2013-11-06 |
| EP2762595A4 (en) | 2015-02-25 |
| CN103827339A (en) | 2014-05-28 |
| US20140294662A1 (en) | 2014-10-02 |
| EP2762595B1 (en) | 2018-07-04 |
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