EP2048257B1 - Free-cutting stainless steel and process for producing the same - Google Patents
Free-cutting stainless steel and process for producing the same Download PDFInfo
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- EP2048257B1 EP2048257B1 EP07791987.6A EP07791987A EP2048257B1 EP 2048257 B1 EP2048257 B1 EP 2048257B1 EP 07791987 A EP07791987 A EP 07791987A EP 2048257 B1 EP2048257 B1 EP 2048257B1
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- European Patent Office
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- stainless steel
- free
- cutting
- particles
- cutting stainless
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 80
- 239000010935 stainless steel Substances 0.000 title claims description 71
- 238000005520 cutting process Methods 0.000 title claims description 67
- 238000000034 method Methods 0.000 title description 21
- 239000002245 particle Substances 0.000 claims description 52
- 229910000831 Steel Inorganic materials 0.000 claims description 27
- 239000010959 steel Substances 0.000 claims description 27
- 238000004519 manufacturing process Methods 0.000 claims description 21
- 229910052796 boron Inorganic materials 0.000 claims description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims description 19
- 239000000654 additive Substances 0.000 claims description 15
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 13
- 230000000996 additive effect Effects 0.000 claims description 12
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 10
- 239000002244 precipitate Substances 0.000 claims description 9
- 239000011159 matrix material Substances 0.000 claims description 8
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 229910052582 BN Inorganic materials 0.000 claims description 4
- QJGQUHMNIGDVPM-UHFFFAOYSA-N nitrogen group Chemical group [N] QJGQUHMNIGDVPM-UHFFFAOYSA-N 0.000 claims description 3
- 238000010583 slow cooling Methods 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 230000007797 corrosion Effects 0.000 description 19
- 238000005260 corrosion Methods 0.000 description 19
- 238000002844 melting Methods 0.000 description 13
- 230000008018 melting Effects 0.000 description 13
- 238000010438 heat treatment Methods 0.000 description 11
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 229910052717 sulfur Inorganic materials 0.000 description 8
- 238000005496 tempering Methods 0.000 description 8
- 239000006185 dispersion Substances 0.000 description 7
- 239000011575 calcium Substances 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 238000005096 rolling process Methods 0.000 description 6
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 5
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 239000011593 sulfur Substances 0.000 description 5
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 238000010309 melting process Methods 0.000 description 4
- 230000001376 precipitating effect Effects 0.000 description 4
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 3
- CXOWYMLTGOFURZ-UHFFFAOYSA-N azanylidynechromium Chemical compound [Cr]#N CXOWYMLTGOFURZ-UHFFFAOYSA-N 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 3
- -1 nickel nitride Chemical class 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 239000002253 acid Substances 0.000 description 2
- 239000003513 alkali Substances 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000011651 chromium Substances 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 238000005339 levitation Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 239000011669 selenium Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- PAWQVTBBRAZDMG-UHFFFAOYSA-N 2-(3-bromo-2-fluorophenyl)acetic acid Chemical compound OC(=O)CC1=CC=CC(Br)=C1F PAWQVTBBRAZDMG-UHFFFAOYSA-N 0.000 description 1
- 101100008044 Caenorhabditis elegans cut-1 gene Proteins 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 229910000915 Free machining steel Inorganic materials 0.000 description 1
- 229910002651 NO3 Inorganic materials 0.000 description 1
- 229910003218 Ni3N Inorganic materials 0.000 description 1
- BUGBHKTXTAQXES-UHFFFAOYSA-N Selenium Chemical compound [Se] BUGBHKTXTAQXES-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- XSQUKJJJFZCRTK-UHFFFAOYSA-N Urea Chemical compound NC(N)=O XSQUKJJJFZCRTK-UHFFFAOYSA-N 0.000 description 1
- 229910021529 ammonia Inorganic materials 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 239000004202 carbamide Substances 0.000 description 1
- 229910052798 chalcogen Inorganic materials 0.000 description 1
- 150000001787 chalcogens Chemical class 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910017464 nitrogen compound Inorganic materials 0.000 description 1
- 150000002830 nitrogen compounds Chemical class 0.000 description 1
- 229910000069 nitrogen hydride Inorganic materials 0.000 description 1
- 150000002897 organic nitrogen compounds Chemical class 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 229910052711 selenium Inorganic materials 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 229910052714 tellurium Inorganic materials 0.000 description 1
- PORWMNRCUJJQNO-UHFFFAOYSA-N tellurium atom Chemical compound [Te] PORWMNRCUJJQNO-UHFFFAOYSA-N 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Images
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1068—Making hard metals based on borides, carbides, nitrides, oxides or silicides
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
Definitions
- the present invention relates to free-cutting stainless steel produced by adding a free-cutting additive.
- Free-cutting steels by adding free-cutting additives such as S sulfur), Pb (lead) and/or Ca (calcium) for the purpose to improve the machinability of steel are known.
- Pb can give rise to earth environmental problems, therefore, the use thereof is being suppressed.
- S is known as an element that affects the corrosion resistance of steels, so a very little amount of addition of S is not preferable for corrosion resistant steels such as stainless steels. S is only used ignoring improved corrosion resistance where machinability is more significant than corrosion resistance. It is very difficult to add the chemically active elements that have both low melting point and high vapor pressure at the melting point, such as Ca, into molten steel. It is hard to control the content, dispersion and precipitation of Ca containing double oxide additives for improving machinability.
- austenitic stainless steels are known as unmachinable steels as these steels have the surface hardening property at cutting.
- the stainless steels added S itself or S combined with Se (selenium) or Te (tellurium) as free-cutting additives is marketed.
- SUS303 and SUS303Se are standardized as S, Se-added austenitic free-cutting stainless steels.
- SUS430F is standardized as S- or S+Pb-added ferritic free-cutting stainless steels and SUS410F2, 416, 420F, 420F2 and 440F are standardized as martensitic free-cutting stainless steels.
- stainless steel to which titanium carbosulfide is added to improve the machinability has been manufactured.
- MnS manganese sulfide
- MnS manganese sulfide
- a large amount of needle shape MnS elongated to the rolling direction shows anisotropy of mechanical property of steel and such sulfur free-cutting stainless steels have the defects of manufactured products.
- JP-2003-129 191 A discloses a free-cutting stainless steel containing hexagonal boron nitride (R-BN) particles.
- the problem to be solved by the present invention is to provide free-cutting stainless steel that can satisfy not only of excellent machinability but also environment-friendliness, corrosion resistance and excellent mechanical property, and a method of manufacturing free-cutting stainless steel.
- the inventors of the present invention found that the above problem is solved by utilizing the properties of h-BN (hexagonal boron nitride) particles having excellent solid-lubricating property and chemically stable characteristic for either acid and alkali.
- free-cutting stainless steel that is characterized in that the free-cutting additive is spherical h-BN (hexagonal boron nitride) particles dispersed and precipitated homogeneously in the stainless steel.
- the free-cutting additive is spherical h-BN (hexagonal boron nitride) particles dispersed and precipitated homogeneously in the stainless steel.
- the free-cutting stainless steel according to Invention 1 is characterized in that the particle diameter of the h-BN particles is 0.2 to 3 ⁇ m.
- Invention 3 there is provided a method of manufacturing free-cutting stainless steel produced by adding a free-cutting additive, characterized in that free-cutting stainless steel where h-BN particles are precipitated is heated to dissolve the h-BN particles into steel matrix, quenched and subsequently tempered to disperse and precipitate h-BN particles homogeneously again as free-cutting additive.
- Invention 4 there is provided a method of manufacturing free-cutting stainless steel produced by adding a free-cutting additive, characterized in that free-cutting stainless steel where h-BN particles are precipitated is heated to dissolve the h-BN particles into steel matrix and subsequently subjected to slow cooling to disperse and precipitate h-BN particles homogeneously again as free-cutting additive.
- the method of manufacturing free-cutting stainless steel according to Invention 3 or 4 is characterized in that the addition of B (boron) is not less than 3 ⁇ 10 -3 mass% and less than 2 ⁇ 10 -1 mass% and the content of N (nitrogen) is not less than 1.5 ⁇ 10 -2 mass%, while the relation between the content of B and that of N satisfies the formula 1 shown below:
- the method of manufacturing free-cutting stainless steel according to Invention 5 is characterized in that the relation between the content of B and that of N satisfies the formula 2 below:
- the method of manufacturing free-cutting stainless steel according to Invention 5 or 6 is characterized in that the addition of B (boron) is less than 1 ⁇ 10 -1 mass%.
- the method of manufacturing free-cutting stainless steel according to any of Inventions 3 through 7 is characterized in that B is added by adding ferroboron or metallic boron and N is added by atmospheric (argon + nitrogen) or by reduced atmospheric nitrogen, to molten stainless steel.
- the method of manufacturing free-cutting stainless steel according to any of Inventions 3 through 7 is characterized in that B is added by adding ferroboron or metallic boron and N is added by adding nitrogen-containing compounds, to molten stainless steel.
- the present invention provides free-cutting stainless steel and its manufacturing method by adding h-BN particles which have acid and alkali resistant and excellent solid-lubricating properties by dispersing and precipitating h-BN particles homogeneously into steel matrix without deterioration of corrosion resistance and mechanical anisotropy.
- Invention 1 satisfies not only the excellent machinability but also environment-friendliness and corrosion resistance.
- h-BN particles are sherical, thereby enables not to give mechanical anisotropy property to this steel.
- Inventions 3 and 4 make it possible to manufacture free-cutting stainless steel without using powder metallurgy process and manufacture large size structural material not having pores remain.
- a manufacturing method according to the present invention employs a conventional melting furnace that can control the melting atmosphere for conventional stainless steel making.
- ferroboron or metallic boron is used as B source material.
- the use of ferroboron for the source of melting charge is technically advantageous for its low melting point as source material to be molten and also economic because the cost per unit weight of B is lower than metallic B.
- Standard B concentration in stainless steel is not less than 3 ⁇ 10 -3 mass% and less than 2 ⁇ 10 -1 mass%, preferably not less than 0.003 mass% and less than 0.1 mass%, more preferably not less than 0.003 mass% and less than 0.05 mass%.
- N source material N in the melting atmosphere may be absorbed or N-containing compounds such as chromium nitride may be added.
- the N concentration in the molten stainless steel at 1,600°C in accordance with Sievert's low is proportional to the 1/2-th power of the N partial pressure in the atmosphere and is about 0.25 mass% in N atmosphere at the atmospheric pressure for SUS304 that is a typical austenitic stainless steel.
- Standard N concentration in stainless steel is not less than 1.5 ⁇ 10 -2 mass%, preferably not less than 5 ⁇ 10 -2 mass%.
- concentration ratio of N to B (N/B) in stainless steel is low, solid-soluted B in stainless steel increases and precipitated h-BN particles that are effective for machinability decrease. Therefore, the value of N/B is preferably as large as possible.
- Molten stainless steel manufactured in a process as described above so as to contain B and N is poured into molds to become ingots or is made into billets or slabs in the case of a continuous molding facility.
- the cast products are then heated to the forging temperature in an ordinary soaking furnace and then subjected to an ordinary forging/rolling process so as to produce rods, pipes and/or sheets.
- the forging temperature is 1,200 to 1,250°C for ordinary stainless steel.
- h-BN particles While 0.2 to 3 ⁇ m h-BN particles are preferable to be precipitated homogeneously in the stainless steel products, h-BN particles coarsely grown to about 20 to 30 ⁇ m can be dispersed irregularly in part of the product depending on the cooling rate after the forging/rolling process in the case of stainless steel rods, pipes and/or sheets. It is desirable to execute a heat treatment process as described below to avoid such a problem.
- the h-BN particles precipitated in stainless steel are decomposed to B and N in the stainless steel in a relatively short time (e.g., from 0.5 to 1 hour at 1,250°C) and dissolved in the matrix of stainless steel at temperature not lower than 1,250°C.
- the above-described condition can be obtained by quenching the stainless steel that contains supersaturated B and N.
- the stainless steel containing supersaturated B and N is tempered at 800°C to 1,150°C, h-BN is precipitated again.
- the stainless steel is tempered at or around 800°C, very fine h-BN particles are precipitated and dispersed homogeneously throughout the stainless steel product because the difference between the equilibrium solubility of B and N at this temperature and the supersaturated solubility thereof is large, the diffusion rate of B and N is low and the diffusion distance of these elements is so short, the precipitation of h-BN nuclei takes place prior to the growth of h-BN nuclei for these two reasons.
- tempering temperature is important for precipitation of h-BN particles with a preferable particle diameter and a preferable dispersion state.
- range of tempering temperature that provides a preferable particle diameter and a preferable dispersion state is from 950 to 1,100°C, preferably from 1,000 to 1,050°C.
- This tempering heat treatment temperature is very advantageous because the tempering heat treatment temperature is within the temperature range of heat treatment for solid solution that takes place after the hot working process and hence the solution heat treatment of stainless steel after the hot working process can be replaced by a heat treatment process for precipitating h-BN particles.
- the tempering holding time it can be very short when the temperature is high enough so the diffusion rates of B and N are high.
- the range of the tempering holding time is from 0.5 to 3 hours, preferably from 1 to 2 hours.
- the steel material is then quenched to stop any further growth of h-BN particles.
- h-BN can be re-precipitated for Inventions 1 and 2 by this method.
- the cooling rate necessary for re-precipitating h-BN particles is between 1 ⁇ 10 1 and 1 ⁇ 10 4 °C/hour, preferably between 1 ⁇ 10 2 and 1 ⁇ 10 3 °C/hour.
- the composition (mass%) of the source material was 0.07 %C, 0.33 %Si, 1.15 %Mn, 0.036 %P, 0.022 %S, 8.07 %Ni and 18.03 %Cr.
- N was introduced into the vacuum induction melting furnace to 0.07 MPa to adjust the N concentration.
- the ingot was cut to upper and lower halves, one of which was hot-worked to produce a rod and the other was hot-worked to sheet.
- the hot-working temperature was 1,250°C for both of them.
- the rod was forged to 55 mm diameter, and the sheet was forged to a rectangular bar of 50 mm ⁇ 90 mm and then rolled to 15 mm thickness and 100 mm width by a hot rolling mill.
- N Since the atmosphere of N maintained at the same pressure level, N was added to a constant quantity ratio.
- FIG. 1 is picture of a fracture surface of a sample taken through SEM (scanning electron microscope), showing the precipitating behavior of dispersion of particles in the sample after the tempering process.
- the sample of the picture is Sample A33 listed in Table 1.
- the rod of 3 mm diameter was cut out from the sample and then the rod sample was bent and fractured.
- the fracture surface of the rod sample was observed through an SEM.
- the observed precipitates were analyzed EDS (energy dispersive X-ray spectroscopic analyzer) annexed to the SEM to identify the type of the precipitates.
- Ten of h-BN particles at the size of 1 to 3 ⁇ m were dispersed throughout at the 1,000 magnification sight.
- MnS that is known as free-cutting element and exist in sulfur free-cutting stainless steel such as commercially available SUS303
- six localized MnS particles were observed at the center part of this figure. Two MnS particles about 10 ⁇ m were observed coexisting with a BN particle. It seems that needle shape MnS particles at the length at about 20 ⁇ m elongated at hot working are destroyed into three pieces.
- MnS crystallizes during solidification process of ingot MnS particles are apt to be segregate and to be elongated toward the rolling direction easily, the steels containing MnS have the anisotropy characteristics.
- h-BN precipitates from supersaturated state of B and N h-BN particles precipitate and comparatively distribute homogeneously, therefore, the feature of anisotropy of steel cannot be observed.
- FIG. 2 shows the results of machinability test cutting by lathe conducted on round rod. This figure shows the relation between cutting speed and combined cutting force of the sample of different boron contents. The conditions of this test were depth of cut 1. 0 mm, feed of tool 0.1 mm/rev and tool material M30 without chip breaker.
- FIG. 3 shows the results of corrosion resistance test for B bearing stainless steel sheets.
- FIG. 3 shows the results of a corrosion test of the samples of different B contents by sulfuric acid solution test standardized by JIS G 0591. The condition of this test is continuous immersion into boiling 5% H 2 SO 4 solution continuously for 6 hours. The corrosion ratio of the samples is indicated as the ratio of weight loss by corrosion divided the samples obtained by dividing the quantity reduced by the initial surface area of the sample. There is scarcely increase of corrosion rate and addition of B has almost no influence on the corrosion.
- N may be added not only nitrogen gas but also nitrogen containing compounds selected from metal nitrides such as CrN (chromium nitride) and Ni 3 N (nickel nitride), inorganic nitrogen compounds such as NH 3 (ammonia), (NH 4 )NO 3 (ammonium nitrate) and Ca 3 N 2 (calcium nitride) and organic nitrogen compounds such as CO (NH 2 ) 2 (urea).
- metal nitrides such as CrN (chromium nitride) and Ni 3 N (nickel nitride)
- inorganic nitrogen compounds such as NH 3 (ammonia), (NH 4 )NO 3 (ammonium nitrate) and Ca 3 N 2 (calcium nitride) and organic nitrogen compounds such as CO (NH 2 ) 2 (urea).
- the composition (mass%) of the source material was 0.06 %C, 0.28 %Si, 1.33 %Mn, 0.035 %P, 0.025 %S, 8.05 %Ni and 18.39 %Cr.
- N was introduced into the levitation melting furnace to 0.075 MPa to adjust the N concentration.
- 0.73 g of commercially available ferroboton (19.2 mass%B) was added to the molten steel and the molten steel was held in a little reduced pressure N atmosphere for 1/6 hours. Then, the molten steel was solidified in the furnace to produce an ingot.
- FIG. 4 is an image of SEM (scanning electron microscope), showing the behavior of precipitation and dispersion of particles in the sample held to 1,250°C for 1/2 hours and subsequently cooled to the room temperature at a cooling rate of 100°C/hour. Comparing to Example 1, it was observed that spherical h-BN particles about 3 ⁇ m particle diameter had been dispersed and re-precipitated throughout the sample.
- the present invention can provide stainless steel which improve machinability without being inferior to corrosion resistance and environmental problems.
- Such stainless steels can be advantageous for applications in various fields of industry.
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Description
- The present invention relates to free-cutting stainless steel produced by adding a free-cutting additive.
- Free-cutting steels by adding free-cutting additives such as S sulfur), Pb (lead) and/or Ca (calcium) for the purpose to improve the machinability of steel are known. As Pb can give rise to earth environmental problems, therefore, the use thereof is being suppressed. S is known as an element that affects the corrosion resistance of steels, so a very little amount of addition of S is not preferable for corrosion resistant steels such as stainless steels. S is only used ignoring improved corrosion resistance where machinability is more significant than corrosion resistance. It is very difficult to add the chemically active elements that have both low melting point and high vapor pressure at the melting point, such as Ca, into molten steel. It is hard to control the content, dispersion and precipitation of Ca containing double oxide additives for improving machinability.
- On the other hand, austenitic stainless steels are known as unmachinable steels as these steels have the surface hardening property at cutting. For the purpose to improve machinability, the stainless steels added S itself or S combined with Se (selenium) or Te (tellurium) as free-cutting additives is marketed. As for Japanese Industrial Standards, two kinds of stainless steel, SUS303 and SUS303Se, are standardized as S, Se-added austenitic free-cutting stainless steels. Additionally, SUS430F is standardized as S- or S+Pb-added ferritic free-cutting stainless steels and SUS410F2, 416, 420F, 420F2 and 440F are standardized as martensitic free-cutting stainless steels. Recently, stainless steel to which titanium carbosulfide is added to improve the machinability has been manufactured.
- Even a very small addition of chalcogen such as S or its compounds makes the corrosion resistance inferior, which is the most advantageous property of austenitic stainless steels. Therefore, these free-cutting stainless steel are only used under corrosiveless atmospheres or are used for the products for not requiring corrosion resistance. For these reasons, no free-cutting stainless steel that satisfies both excellent machinability and that of corrosion resistance is currently available.
- Furthermore, in the case of sulfur free-cutting stainless steel that is currently being manufactured, the added S forms MnS (manganese sulfide), MnS that improves the machinability is plastically deformed easily so that it is elongated to needle shape in accordance with the rolling direction while the hot working of steel rods or sheets. A large amount of needle shape MnS elongated to the rolling direction shows anisotropy of mechanical property of steel and such sulfur free-cutting stainless steels have the defects of manufactured products.
JP-2003-129 191 A - In view of the above-mentioned background art, the problem to be solved by the present invention is to provide free-cutting stainless steel that can satisfy not only of excellent machinability but also environment-friendliness, corrosion resistance and excellent mechanical property, and a method of manufacturing free-cutting stainless steel.
- The inventors of the present invention found that the above problem is solved by utilizing the properties of h-BN (hexagonal boron nitride) particles having excellent solid-lubricating property and chemically stable characteristic for either acid and alkali.
- According to Invention 1, there is provided free-cutting stainless steel that is characterized in that the free-cutting additive is spherical h-BN (hexagonal boron nitride) particles dispersed and precipitated homogeneously in the stainless steel.
- According to Invention 2, the free-cutting stainless steel according to Invention 1 is characterized in that the particle diameter of the h-BN particles is 0.2 to 3 µm.
- According to Invention 3, there is provided a method of manufacturing free-cutting stainless steel produced by adding a free-cutting additive, characterized in that free-cutting stainless steel where h-BN particles are precipitated is heated to dissolve the h-BN particles into steel matrix, quenched and subsequently tempered to disperse and precipitate h-BN particles homogeneously again as free-cutting additive.
- According to Invention 4, there is provided a method of manufacturing free-cutting stainless steel produced by adding a free-cutting additive, characterized in that free-cutting stainless steel where h-BN particles are precipitated is heated to dissolve the h-BN particles into steel matrix and subsequently subjected to slow cooling to disperse and precipitate h-BN particles homogeneously again as free-cutting additive.
- According to Invention 5, the method of manufacturing free-cutting stainless steel according to Invention 3 or 4 is characterized in that the addition of B (boron) is not less than 3 × 10-3 mass% and less than 2 × 10-1 mass% and the content of N (nitrogen) is not less than 1.5 × 10-2 mass%, while the relation between the content of B and that of N satisfies the formula 1 shown below:
- (formula 1)
- According to Invention 6, the method of manufacturing free-cutting stainless steel according to Invention 5 is characterized in that the relation between the content of B and that of N satisfies the formula 2 below:
- (formula 2)
- According to Invention 7, the method of manufacturing free-cutting stainless steel according to Invention 5 or 6 is characterized in that the addition of B (boron) is less than 1 × 10-1 mass%.
- According to Invention 8, the method of manufacturing free-cutting stainless steel according to any of Inventions 3 through 7 is characterized in that B is added by adding ferroboron or metallic boron and N is added by atmospheric (argon + nitrogen) or by reduced atmospheric nitrogen, to molten stainless steel.
- According to Invention 9, the method of manufacturing free-cutting stainless steel according to any of Inventions 3 through 7 is characterized in that B is added by adding ferroboron or metallic boron and N is added by adding nitrogen-containing compounds, to molten stainless steel.
- The present invention provides free-cutting stainless steel and its manufacturing method by adding h-BN particles which have acid and alkali resistant and excellent solid-lubricating properties by dispersing and precipitating h-BN particles homogeneously into steel matrix without deterioration of corrosion resistance and mechanical anisotropy.
- Invention 1 satisfies not only the excellent machinability but also environment-friendliness and corrosion resistance.
- As h-BN particles have higher heat resistant property compared to lead, the stainless steel which has both free-cutting and heat resistant properties can be obtained.
- Furthermore, h-BN particles are sherical, thereby enables not to give mechanical anisotropy property to this steel.
- These advantages are performed by utilizing h-BN particles which have solid-lubricant property, therefore, stainless steel with excellent machinability and environment-friendliness are manufactured without deterioration of corrosion resistance and mechanical anisotropy which are shown in available sulfur free-cutting stainless steel.
- Although another way to manufacture free-cutting stainless steel by powder metallurgy process by dispersing h-BN particles is to be thought, there is the worst disadvantage of this process that a large number of voids remain in steel and large size structural material can never manufacture.
- On the contrary, Inventions 3 and 4 make it possible to manufacture free-cutting stainless steel without using powder metallurgy process and manufacture large size structural material not having pores remain.
-
-
FIG. 1 is a picture of fractured surface of a sample taken through SEM, showing the precipitation and dispersion behavior of particles in the sample and identifying the kind of particles by means of EDS analysis. -
FIG. 2 is a graph illustrating the relationship between the cutting speed and the combined cutting force of each of the samples of varying the addition of B. -
FIG. 3 is a graph illustrating the results of a corrosion test on each of the samples of varying the addition of B conducted by the method of sulfuric acid test (JIS G 0591). -
FIG. 4 is a picture of a sample taken through SEM (scanning electron microscope), showing the dispersion behavior of precipitated particles in the sample held at 1,250°C for 1/2 hours and subsequently cooled to the room temperature at a cooling rate of 100°C/hour. - The present invention, which is characterized as described above, will now be described below by way of embodiments.
- A manufacturing method according to the present invention employs a conventional melting furnace that can control the melting atmosphere for conventional stainless steel making. In the melting process, ferroboron or metallic boron is used as B source material. The use of ferroboron for the source of melting charge is technically advantageous for its low melting point as source material to be molten and also economic because the cost per unit weight of B is lower than metallic B.
- Standard B concentration in stainless steel is not less than 3 × 10-3 mass% and less than 2 × 10-1 mass%, preferably not less than 0.003 mass% and less than 0.1 mass%, more preferably not less than 0.003 mass% and less than 0.05 mass%. As N source material, N in the melting atmosphere may be absorbed or N-containing compounds such as chromium nitride may be added.
- Note that, when N is adsorbed from the melting atmosphere, the N concentration in the molten stainless steel at 1,600°C in accordance with Sievert's low is proportional to the 1/2-th power of the N partial pressure in the atmosphere and is about 0.25 mass% in N atmosphere at the atmospheric pressure for SUS304 that is a typical austenitic stainless steel.
- Standard N concentration in stainless steel is not less than 1.5 × 10-2 mass%, preferably not less than 5 × 10-2 mass%. When the concentration ratio of N to B (N/B) in stainless steel is low, solid-soluted B in stainless steel increases and precipitated h-BN particles that are effective for machinability decrease. Therefore, the value of N/B is preferably as large as possible.
- The above relationship can be expressed by formula 1 shown below:
- (formula 1)
and preferably expressed by formula 2 shown below: - (formula 2)
- Molten stainless steel manufactured in a process as described above so as to contain B and N is poured into molds to become ingots or is made into billets or slabs in the case of a continuous molding facility. The cast products are then heated to the forging temperature in an ordinary soaking furnace and then subjected to an ordinary forging/rolling process so as to produce rods, pipes and/or sheets. The forging temperature is 1,200 to 1,250°C for ordinary stainless steel.
- While 0.2 to 3 µm h-BN particles are preferable to be precipitated homogeneously in the stainless steel products, h-BN particles coarsely grown to about 20 to 30 µm can be dispersed irregularly in part of the product depending on the cooling rate after the forging/rolling process in the case of stainless steel rods, pipes and/or sheets. It is desirable to execute a heat treatment process as described below to avoid such a problem.
- The h-BN particles precipitated in stainless steel are decomposed to B and N in the stainless steel in a relatively short time (e.g., from 0.5 to 1 hour at 1,250°C) and dissolved in the matrix of stainless steel at temperature not lower than 1,250°C.
- Such a process is not feasible when stainless steel is molted. Therefore, the process needs to be executed at the temperature lower than the melting temperature of the stainless steel.
- The above-described condition can be obtained by quenching the stainless steel that contains supersaturated B and N. When the stainless steel containing supersaturated B and N, is tempered at 800°C to 1,150°C, h-BN is precipitated again. When the stainless steel is tempered at or around 800°C, very fine h-BN particles are precipitated and dispersed homogeneously throughout the stainless steel product because the difference between the equilibrium solubility of B and N at this temperature and the supersaturated solubility thereof is large, the diffusion rate of B and N is low and the diffusion distance of these elements is so short, the precipitation of h-BN nuclei takes place prior to the growth of h-BN nuclei for these two reasons. Contrarily, when the stainless steel is tempered at or around 1,150°C, h-BN particles grow considerably coarse are precipitated because the growth of h-BN nuclei takes place prior to the precipitation of h-BN nuclei conversely relative to the tempering at or around 800°C.
- Therefore, selection of tempering temperature is important for precipitation of h-BN particles with a preferable particle diameter and a preferable dispersion state. As a result of a trial experiment, it was found that the range of tempering temperature that provides a preferable particle diameter and a preferable dispersion state is from 950 to 1,100°C, preferably from 1,000 to 1,050°C. This tempering heat treatment temperature is very advantageous because the tempering heat treatment temperature is within the temperature range of heat treatment for solid solution that takes place after the hot working process and hence the solution heat treatment of stainless steel after the hot working process can be replaced by a heat treatment process for precipitating h-BN particles.
- Additionally, as for the tempering holding time, it can be very short when the temperature is high enough so the diffusion rates of B and N are high. The range of the tempering holding time is from 0.5 to 3 hours, preferably from 1 to 2 hours. The steel material is then quenched to stop any further growth of h-BN particles.
- On the other hand, dissolved h-BN by heating re-precipitate by slow cooling rate to the amount of its corresponding saturated concentration level, as solubility limit of the both B and N that are dissolved in steel matrix decreases. h-BN can be re-precipitated for Inventions 1 and 2 by this method. The cooling rate necessary for re-precipitating h-BN particles is between 1 × 101 and 1 × 104 °C/hour, preferably between 1 × 102 and 1 × 103 °C/hour.
- A round rod of commercially available austenitic stainless steel (SUS304) (weight: 18 kg) was melted as a molten source material by using a vacuum induction melting furnace. The composition (mass%) of the source material was 0.07 %C, 0.33 %Si, 1.15 %Mn, 0.036 %P, 0.022 %S, 8.07 %Ni and 18.03 %Cr. During the melting process, N was introduced into the vacuum induction melting furnace to 0.07 MPa to adjust the N concentration. After the melting process, predetermined amount of commercially available ferroboron (19.2 mass %B) as listed in Table 1 was added into the molten steel to adjust the B concentration and the molten steel was held in a little reduced pressure N atmosphere for 1/3 hours. Then, themolten steel was cast at 1,600°C to produce an ingot.
- The ingot was cut to upper and lower halves, one of which was hot-worked to produce a rod and the other was hot-worked to sheet. The hot-working temperature was 1,250°C for both of them. The rod was forged to 55 mm diameter, and the sheet was forged to a rectangular bar of 50 mm × 90 mm and then rolled to 15 mm thickness and 100 mm width by a hot rolling mill.
- Both the rod and the sheet that had been hot-worked were then held to 1,250°C for 0.5 hours and water-cooled with water for the purpose to dissolve h-BN. Subsequently, they were held to 1, 050°C for 1 hour and water-cooled for the purpose to precipitate h-BN. Table 1 shows the chemical analysis of B and N (unit: mass%) in the stainless steel obtained after the above processes.
Table 1 Sample No. Added ferroboron g Total B Soluble B N A31 0 0.000 0.000 0.20 A32 9.4 0.007 0.002 0.20 A33 18.8 0.016 0.003 0.18 Chemical analysis of B and N in samples (unit: mass%) - As shown in Table 1, about 80% of the added B remained after the processes. The soluble B was not more than 0.005% and hence the added B mostly formed h-BN.
- Since the atmosphere of N maintained at the same pressure level, N was added to a constant quantity ratio.
-
FIG. 1 is picture of a fracture surface of a sample taken through SEM (scanning electron microscope), showing the precipitating behavior of dispersion of particles in the sample after the tempering process. The sample of the picture is Sample A33 listed in Table 1. The rod of 3 mm diameter was cut out from the sample and then the rod sample was bent and fractured. The fracture surface of the rod sample (parallel section for the rolling direction) was observed through an SEM. - Additionally, the observed precipitates were analyzed EDS (energy dispersive X-ray spectroscopic analyzer) annexed to the SEM to identify the type of the precipitates. Ten of h-BN particles at the size of 1 to 3 µm were dispersed throughout at the 1,000 magnification sight. As for MnS, that is known as free-cutting element and exist in sulfur free-cutting stainless steel such as commercially available SUS303, six localized MnS particles were observed at the center part of this figure. Two MnS particles about 10 µm were observed coexisting with a BN particle. It seems that needle shape MnS particles at the length at about 20 µm elongated at hot working are destroyed into three pieces. Since MnS crystallizes during solidification process of ingot, MnS particles are apt to be segregate and to be elongated toward the rolling direction easily, the steels containing MnS have the anisotropy characteristics. On the contrary, as h-BN precipitates from supersaturated state of B and N, h-BN particles precipitate and comparatively distribute homogeneously, therefore, the feature of anisotropy of steel cannot be observed.
-
FIG. 2 shows the results of machinability test cutting by lathe conducted on round rod. This figure shows the relation between cutting speed and combined cutting force of the sample of different boron contents. The conditions of this test were depth of cut 1. 0 mm, feed of tool 0.1 mm/rev and tool material M30 without chip breaker. - Comparing the case of precipitating BN with congruent distribution and without BN, combined cutting force are reduced to 20 to 25% at high cutting speed, and it was shown that the machinability of BN stainless steel was improved, unless at the low cutting speed combined cutting forces were almost the same. This means that easy cutting by lathe at high cutting speed makes the improvement of productivity and energy saving.
-
FIG. 3 shows the results of corrosion resistance test for B bearing stainless steel sheets.FIG. 3 shows the results of a corrosion test of the samples of different B contents by sulfuric acid solution test standardized by JIS G 0591. The condition of this test is continuous immersion into boiling 5% H2SO4 solution continuously for 6 hours. The corrosion ratio of the samples is indicated as the ratio of weight loss by corrosion divided the samples obtained by dividing the quantity reduced by the initial surface area of the sample. There is scarcely increase of corrosion rate and addition of B has almost no influence on the corrosion. - The present invention is not limited to the above-described examples and any of the details of the samples may be modified in various different ways.
- N may be added not only nitrogen gas but also nitrogen containing compounds selected from metal nitrides such as CrN (chromium nitride) and Ni3N (nickel nitride), inorganic nitrogen compounds such as NH3 (ammonia), (NH4)NO3 (ammonium nitrate) and Ca3N2 (calcium nitride) and organic nitrogen compounds such as CO (NH2)2 (urea).
- A round rod of commercially available austenitic stainless steel (SUS304) (weight: 2 kg) was melted by using a cold crucible levitation melting furnace. The composition (mass%) of the source material was 0.06 %C, 0.28 %Si, 1.33 %Mn, 0.035 %P, 0.025 %S, 8.05 %Ni and 18.39 %Cr. N was introduced into the levitation melting furnace to 0.075 MPa to adjust the N concentration. After the melting process at 1,600°c, 0.73 g of commercially available ferroboton (19.2 mass%B) was added to the molten steel and the molten steel was held in a little reduced pressure N atmosphere for 1/6 hours. Then, the molten steel was solidified in the furnace to produce an ingot.
- The ingot was heated to 1,200°C and hot worked to 14.3 mm square rod at that temperature. The rod was held to 1,250°C for 1/2 hours ana cooled from this temperature at cooling rate of 100°C/hour for the purpose of dissolving h-BN into steel matrix and re-precipitating h-BN. Table 2 shows the content of B and N (unit: mass%) in the stainless steel and made after above heat treatment processes.
Table 2 total B% sol. B% N% Ingot 0.0070 0.0058 022 After heat treatment processes 0.0049 0.0006 022 - The difference between total B% and sol. B% in Table 2 corresponds to the amount of h-BN in steel. As the amount of h-BN remarkably increased after the heat treatment processes, this shows that h-BN was re-precipitated by this heat treatment processes.
-
FIG. 4 is an image of SEM (scanning electron microscope), showing the behavior of precipitation and dispersion of particles in the sample held to 1,250°C for 1/2 hours and subsequently cooled to the room temperature at a cooling rate of 100°C/hour. Comparing to Example 1, it was observed that spherical h-BN particles about 3 µm particle diameter had been dispersed and re-precipitated throughout the sample. - As described above in detail, the present invention can provide stainless steel which improve machinability without being inferior to corrosion resistance and environmental problems. Such stainless steels can be advantageous for applications in various fields of industry.
Claims (9)
- Free-cutting stainless steel produced by adding a free-cutting additive, characterized in that the free-cutting additive thereof is spherical h-BN (hexagonal boron nitride) particles dispersed and precipitated homogeneously in the stainless steel.
- The free-cutting stainless steel according to claim 1, characterized in that the particle diameter of the h-BN particles is 0.2 to 3 µm.
- A method of manufacturing free-cutting stainless steel produced by adding a free-cutting additive, characterized in that free-cutting stainless steel where h-BN particles are precipitated is heated to dissolve the h-BN particles into steel matrix, quenched and subsequently tempered to disperse and precipitate spherical h-BN particles homogeneously again as free-cutting additive.
- A method of manufacturing free-cutting stainless steel produced by adding a free-cutting additive, characterized in that free-cutting stainless steel where h-BN particles are precipitated is heated to dissolve the h-BN particles into steel matrix and subsequently subjected to slow cooling to disperse and precipitate spherical h-BN particles homogeneously again as free-cutting additive.
- The method of manufacturing free-cutting stainless steel according to claim 3 or 4, characterized in that the addition of B (boron) is not less than 3 × 10-3 mass% and less than 2 × 10-1 mass% and the content of N (nitrogen) is not less than 1.5 × 10-2 mass%, while the relation between the content of B and that of N satisfies the formula 1 shown below:
- The method of manufacturing free-cutting stainless steel according to claim 5, characterized in that the addition of B (boron) is less than 1 × 10-1 mass%.
- The method of manufacturing free-cutting stainless steel according to claim 3 or 4, characterized in that B is added by adding ferroboron or metallic boron and N is added by atmospheric (argon + nitrogen) or by reduced atmospheric nitrogen, to molten stainless steel.
- The method of manufacturing free-cutting stainless steel according to claim 3 or 4, characterized in that B is added by adding ferroboron or metallic boron and N is added by adding nitrogen-containing compounds, to molten stainless steel.
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