CN115595530A - Surface hardening material of iron-based sintered alloy material, and sprocket, gear and shaft comprising same - Google Patents
Surface hardening material of iron-based sintered alloy material, and sprocket, gear and shaft comprising same Download PDFInfo
- Publication number
- CN115595530A CN115595530A CN202211337786.7A CN202211337786A CN115595530A CN 115595530 A CN115595530 A CN 115595530A CN 202211337786 A CN202211337786 A CN 202211337786A CN 115595530 A CN115595530 A CN 115595530A
- Authority
- CN
- China
- Prior art keywords
- iron
- sintered alloy
- based sintered
- quenching
- nitriding
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 247
- 239000000956 alloy Substances 0.000 title claims abstract description 136
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 119
- 239000000463 material Substances 0.000 title claims abstract description 67
- 238000010791 quenching Methods 0.000 claims abstract description 91
- 238000005121 nitriding Methods 0.000 claims abstract description 89
- 230000000171 quenching effect Effects 0.000 claims abstract description 88
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 78
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 71
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 39
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 34
- 239000000203 mixture Substances 0.000 claims abstract description 34
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 33
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 26
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 19
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 18
- 239000011651 chromium Substances 0.000 claims abstract description 18
- 239000011733 molybdenum Substances 0.000 claims abstract description 18
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 16
- 239000010949 copper Substances 0.000 claims abstract description 16
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 15
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 14
- 238000005275 alloying Methods 0.000 claims abstract description 13
- 229910052802 copper Inorganic materials 0.000 claims abstract description 12
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 12
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 7
- 229910000640 Fe alloy Inorganic materials 0.000 claims abstract description 5
- 230000001747 exhibiting effect Effects 0.000 claims abstract description 5
- 238000005552 hardfacing Methods 0.000 claims 3
- 239000006104 solid solution Substances 0.000 abstract description 4
- 239000010410 layer Substances 0.000 description 42
- 239000000843 powder Substances 0.000 description 37
- 238000005255 carburizing Methods 0.000 description 35
- 239000007789 gas Substances 0.000 description 26
- 229910000831 Steel Inorganic materials 0.000 description 23
- 239000010959 steel Substances 0.000 description 23
- 239000000758 substrate Substances 0.000 description 18
- 239000002994 raw material Substances 0.000 description 17
- 239000012298 atmosphere Substances 0.000 description 16
- 238000000034 method Methods 0.000 description 15
- 238000005245 sintering Methods 0.000 description 15
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 13
- 229910052737 gold Inorganic materials 0.000 description 13
- 239000010931 gold Substances 0.000 description 13
- 238000010438 heat treatment Methods 0.000 description 12
- 239000000047 product Substances 0.000 description 12
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 11
- 238000005496 tempering Methods 0.000 description 11
- 238000005256 carbonitriding Methods 0.000 description 9
- 238000004519 manufacturing process Methods 0.000 description 9
- 239000011148 porous material Substances 0.000 description 9
- 239000007769 metal material Substances 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- 238000001816 cooling Methods 0.000 description 7
- 239000011572 manganese Substances 0.000 description 7
- 239000011812 mixed powder Substances 0.000 description 7
- 238000000465 moulding Methods 0.000 description 7
- 238000001878 scanning electron micrograph Methods 0.000 description 7
- 229910017112 Fe—C Inorganic materials 0.000 description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 6
- 229910001873 dinitrogen Inorganic materials 0.000 description 6
- 239000001257 hydrogen Substances 0.000 description 6
- 229910052739 hydrogen Inorganic materials 0.000 description 6
- 239000012535 impurity Substances 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 239000003921 oil Substances 0.000 description 6
- 229910000975 Carbon steel Inorganic materials 0.000 description 5
- 239000010962 carbon steel Substances 0.000 description 5
- 239000000314 lubricant Substances 0.000 description 5
- 238000005259 measurement Methods 0.000 description 5
- 150000004767 nitrides Chemical class 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 4
- 239000007788 liquid Substances 0.000 description 4
- 230000001590 oxidative effect Effects 0.000 description 4
- 239000002344 surface layer Substances 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910000851 Alloy steel Inorganic materials 0.000 description 3
- 229910001339 C alloy Inorganic materials 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 229910021529 ammonia Inorganic materials 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 150000002431 hydrogen Chemical class 0.000 description 3
- DDTIGTPWGISMKL-UHFFFAOYSA-N molybdenum nickel Chemical compound [Ni].[Mo] DDTIGTPWGISMKL-UHFFFAOYSA-N 0.000 description 3
- 238000011084 recovery Methods 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910001182 Mo alloy Inorganic materials 0.000 description 2
- 229910017263 Mo—C Inorganic materials 0.000 description 2
- PCEXQRKSUSSDFT-UHFFFAOYSA-N [Mn].[Mo] Chemical compound [Mn].[Mo] PCEXQRKSUSSDFT-UHFFFAOYSA-N 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000012768 molten material Substances 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000012466 permeate Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000007493 shaping process Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 238000007088 Archimedes method Methods 0.000 description 1
- 239000004215 Carbon black (E152) Substances 0.000 description 1
- UGFAIRIUMAVXCW-UHFFFAOYSA-N Carbon monoxide Chemical compound [O+]#[C-] UGFAIRIUMAVXCW-UHFFFAOYSA-N 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910017116 Fe—Mo Inorganic materials 0.000 description 1
- 229910000617 Mangalloy Inorganic materials 0.000 description 1
- 229910017309 Mo—Mn Inorganic materials 0.000 description 1
- 229910017318 Mo—Ni Inorganic materials 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- -1 and at the same time Substances 0.000 description 1
- CXOWYMLTGOFURZ-UHFFFAOYSA-N azanylidynechromium Chemical compound [Cr]#N CXOWYMLTGOFURZ-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000005271 boronizing Methods 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 230000003197 catalytic effect Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- VNTLIPZTSJSULJ-UHFFFAOYSA-N chromium molybdenum Chemical compound [Cr].[Mo] VNTLIPZTSJSULJ-UHFFFAOYSA-N 0.000 description 1
- OGSYQYXYGXIQFH-UHFFFAOYSA-N chromium molybdenum nickel Chemical compound [Cr].[Ni].[Mo] OGSYQYXYGXIQFH-UHFFFAOYSA-N 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000000748 compression moulding Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000000428 dust Substances 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 229930195733 hydrocarbon Natural products 0.000 description 1
- 150000002430 hydrocarbons Chemical class 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- QIQXTHQIDYTFRH-UHFFFAOYSA-N octadecanoic acid Chemical compound CCCCCCCCCCCCCCCCCC(O)=O QIQXTHQIDYTFRH-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 230000003449 preventive effect Effects 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 102200082816 rs34868397 Human genes 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F5/10—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of articles with cavities or holes, not otherwise provided for in the preceding subgroups
- B22F5/106—Tube or ring forms
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
-
- 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
- C22C38/18—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
- C22C38/40—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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/02—Pretreatment of the material to be coated
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/80—After-treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/248—Thermal after-treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/01—Reducing atmosphere
- B22F2201/016—NH3
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/02—Nitrogen
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/35—Iron
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2302/00—Metal Compound, non-Metallic compound or non-metal composition of the powder or its coating
- B22F2302/20—Nitride
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
The present invention relates to a surface hardening material of an iron-based sintered alloy material, and a sprocket, a gear, and a shaft comprising the same. The surface hardening material of the iron-based sintered alloy material is a surface hardening material of a sintered alloy base material obtained by nitriding and quenching a sintered alloy base material having a carbon-containing iron alloy composition, the iron-based sintered alloy material contains carbon, and contains 0.1 to 1.0 mass% of carbon, and one or more alloying components selected from the group consisting of 0.15 to 4.5 mass% of chromium, 0.2 to 4.5 mass% of copper, 0.1 to 2.0 mass% of molybdenum, 0.1 to 3.0 mass% of manganese, and 0.2 to 4.5 mass% of nickel, and has a hardened layer exhibiting a martensite solid solution supersaturated with nitrogen on the surface, the hardened layer has a depth of 100 [ mu ] m or more from the surface, and a Vickers hardness of 800Hv or more at a position 0.1mm from the surface.
Description
The application is a divisional application of Chinese patent application with the application date of 2018, 11 and 9, the application number of 201880072656.0, and the name of the invention being "iron-based sintered alloy material and manufacturing method thereof".
Technical Field
The present invention relates to an iron-based sintered alloy material having improved strength by hardening the surface thereof, and a method for producing the same.
Background
Conventionally, a metal material has been surface-treated by a chemical hardening method in order to impart material characteristics such as wear resistance and fatigue resistance required for machine parts and the like. The chemical hardening method is a method of forming a hardened layer on the surface of a material by allowing a hardening component to act on the surface, and there are various treatment methods such as carburizing treatment, nitriding treatment, carbonitriding treatment, sulfurizing-nitriding treatment, and boronizing treatment. Carburizing treatment is a hardening method that has been carried out since a long time ago and is widely used, but has a problem of large strain due to quenching carried out as heat treatment after carburizing.
On the other hand, the nitriding treatment by precipitation hardening with nitride can be performed at a lower heating temperature than the carburizing treatment, and can reduce thermal strain, but has a problem that the treatment time is long and the hardened layer is thin. In addition, since nitrides are brittle even if they are hard, they have a problem in strength. On the other hand, nitriding treatment by solid solution diffusion of nitrogen does not depend on the formation of nitrides, and therefore, the problem caused by brittleness can be avoided, and thermal strain is reduced as compared with carburizing treatment. However, nitriding still has the disadvantages of long treatment time, shallow hardened layer, and the like. For example, patent document 1 below describes a surface layer hardening treatment method for hardening the surface of a metal material, and discloses that the vickers hardness of the metal material from the surface to a depth of 78 μm is increased by 5% or more by nitriding the metal material. The hardened layer of this depth was obtained by a treatment for 12 hours.
Documents of the prior art
Patent document
Patent document 1: japanese re-publication of patent No. WO2014/104085
Disclosure of Invention
Problems to be solved by the invention
Austenite into which nitrogen has been diffused by infiltration undergoes martensitic transformation when quenching is performed, and the hardness is significantly improved. That is, the hardened layer on the surface is formed by performing such a rapid cooling heat treatment. The austenitizing temperature of Fe-N system is lower than that of Fe-C system, and the strain due to heat treatment can be reduced by nitriding treatment as compared with carburizing treatment. However, as described above, in the conventional nitriding treatment, it is difficult to form a sufficiently thick hardened layer on the surface. In order to efficiently and inexpensively provide a machine component or the like excellent in wear resistance and the like, it is necessary to achieve surface hardening which is small in strain due to heat treatment and capable of forming a thick hardened layer in a short time, and to improve material characteristics of a metal material constituting the machine component or the like.
The present invention has been made to solve the above problems, and an object of the present invention is to provide a metal material having an improved strength by a hardened layer at an effective and low cost, and to provide a high-quality product with high accuracy.
Means for solving the problems
The present inventors have studied a chemical hardening method of a metal material in order to solve the above problems, and have found that a metal material having a hardened layer formed on the surface thereof suitably can be obtained by nitriding and quenching an iron-based sintered alloy, and have realized a technique capable of providing a mechanical component such as a sprocket and various members excellent in wear resistance and fatigue strength.
According to one embodiment of the present invention, an iron-based sintered alloy material has a hardened layer exhibiting a martensite phase in which nitrogen is supersaturated and solid-dissolved on the surface.
The iron-based sintered alloy material may contain 0.1 to 1.0 mass% of carbon. Further, the alloy may contain one or more alloying components selected from the group consisting of chromium, copper, molybdenum, manganese, and nickel. The alloying component is any one of 0.15-4.5 mass% of chromium, 0.2-4.5 mass% of copper, 0.1-2.0 mass% of molybdenum, 0.1-3.0 mass% of manganese and 0.2-4.5 mass% of nickel. The hardened layer contributes to an increase in the surface fatigue strength by increasing the depth from the surface to 100 μm or more.
In addition, according to one embodiment of the present invention, a method for producing an iron-based sintered alloy material includes: an iron-based powder mixture containing carbon powder is formed into a green compact having a desired shape, the green compact is heated to 1000 to 1300 ℃ in a non-oxidizing atmosphere and sintered to obtain an iron-based sintered bond base material, the iron-based sintered bond base material is heated to a nitriding temperature of 590 ℃ or higher in an atmosphere containing ammonia gas to be nitrided, and the nitrided iron-based sintered bond base material is quenched by rapid cooling.
The quenching is effective for suppressing thermal strain if it is performed at a quenching temperature lower than the nitriding temperature. After the quenching, the steel sheet is further heated to 100 to 200 ℃ and tempered, and is effective in eliminating stress and martensitic transformation of retained austenite. The carbon powder contained in the iron-based mixed powder may be 0.1 to 1.2 mass% of graphite powder. The iron-based mixed powder may further contain one or more alloying components selected from the group consisting of chromium, copper, molybdenum, manganese, and nickel. The iron-based mixed powder preferably contains at least one alloying component selected from the group consisting of 0.15 to 4.5 mass% of chromium, 0.2 to 4.5 mass% of copper, 0.1 to 2.0 mass% of molybdenum, 0.1 to 3.0 mass% of manganese, and 0.2 to 4.5 mass% of nickel.
Effects of the invention
According to the present invention, the characteristics such as fatigue strength and wear resistance of the iron-based sintered alloy material having the hardened layer formed on the surface thereof are improved, and various products such as machine parts can be provided with high accuracy and at low cost by reducing thermal strain.
Drawings
Fig. 1 is an SEM image of a metal structure of a cross section of a surface-hardened iron-based sintered alloy material, wherein (a) shows an SEM image of hardening by carburizing and quenching, (b) shows an SEM image of hardening by carburizing and nitriding and quenching, and (c) shows an SEM image of hardening by nitriding and quenching.
Detailed Description
An iron-based sintered alloy material is a sintered material having an alloy composition containing iron as a main component, and is obtained by compression-molding a powder containing iron as a main component into a desired shape to obtain a green compact, and heat-sintering the obtained green compact. The final sintered body is formed into a product made of an iron-based sintered alloy by, for example, forming the product into a net shape or a near net shape of the target product during the forming. The sintered material is a porous material having pores, and the iron-based sintered alloy material of the present invention is also a porous material having pores at a porosity corresponding to the powder compact density at the time of molding. Since the sintered material is used as a product by performing processes such as shaping (サイジング) and coining (コイニング) on the sintered material as necessary, the surface of the sintered material is densified in this case. Iron and steel materials provided in the form of molten materials, cast materials, forged materials, and the like are widely used as raw materials for constituting machine parts, structural members, and the like, and iron-based sintered alloy materials having the same alloy composition are also suitable for various parts and members. Therefore, it is very useful to produce an iron-based sintered alloy material exhibiting excellent material characteristics at low cost and efficiently, and by realizing an iron-based sintered alloy material in which the material characteristics are improved by surface hardening treatment, it is possible to provide a power transmission component, a mechanical device component, and the like with high quality.
The iron-based sintered alloy material in the present invention is a case hardened material obtained by nitriding and quenching a sintered alloy base material having the same alloy composition as that of a steel material, that is, a carbon-containing iron alloy composition. By nitriding, nitrogen permeates and diffuses from the alloy surface, and austenite in which nitrogen is dissolved is generated. The steel sheet is quenched to cause martensitic transformation, thereby forming a hardened layer of martensite in which nitrogen is supersaturated and solid-dissolved. The nitrogen-diffused layer can be formed at a depth of about 100 μm or more from the outermost surface in a short period of time, and the hardened layer thus formed is effective for improving the surface fatigue strength. By extending the nitriding treatment time, the hardened layer can be formed more deeply. The increase in hardness of the surface portion by the hardened layer contributes to improvement in strength and wear resistance. Since the iron-based sintered bond base material is a porous material, the nitrogen permeation and diffusion can be performed not only on the outer surface of the sintered bond base material but also in the pores. Therefore, the hardened layer formed by nitriding quenching reaches the inner surface of the pore, that is, the deep part of the sintered alloy, and an effect similar to the formation of a deep hardened layer can be obtained. The depth of the hardened layer formed by nitriding quenching of the molten material is usually about 50 μm, whereas the depth of the hardened layer in the sintered alloy material is likely to reach about 200 μm. In the present invention, depending on the content of nitrogen, the nitride may be dispersed in the martensite phase, but the dispersion of the nitride to a certain extent is allowable, and the function as the hardened layer is not impaired.
The austenitizing temperature of Fe-C is about 727 ℃ and the austenitizing temperature of Fe-N is about 590 ℃ lower than that of 130 ℃ or higher, so that the nitriding treatment can be performed at a temperature lower than that of the carburizing treatment by 100 ℃. Therefore, the quenching temperature after the nitriding treatment may be set to a temperature lower than the carburizing and quenching temperature. Therefore, the thermal strain can be significantly reduced as compared to carburizing and quenching. Further, since the eutectoid point (2.35 mass% N) of Fe-N system is higher in element content than the eutectoid point (0.77 mass% C) of Fe-C system, the austenitizing temperature increases in the range (0.77 mass% or more) where the carbon amount increases from the eutectoid point in Fe-C system, whereas the austenitizing temperature decreases as the nitrogen amount increases (but up to 2.35 mass%) in the same range of Fe-N system. That is, in the nitriding treatment, not only nitrogen can be solid-dissolved at a low temperature, but also the amount of solid-dissolved nitrogen can be increased as compared with the carburizing treatment.
The iron-based sintered alloy material of the present invention is explained below. The iron-based sintered alloy material of the present invention is an iron-based sintered alloy material in which a hardened layer, that is, a surface hardened layer, is formed on the surface of a sintered alloy base material composed of an iron-based alloy containing carbon. Therefore, the main part thereof is composed of an iron-based sintered alloy containing carbon, and the surface hardened layer produced by nitriding quenching exhibits a martensite phase in which nitrogen is supersaturated and dissolved. The iron-based sintered alloy substrate is composed of an iron-based sintered alloy as follows.
< iron-based sintered alloy containing carbon >
The iron-based sintered alloy material before surface hardening is made of an iron-based sintered alloy containing carbon, and the iron-based sintered alloy material after surface hardening has the same alloy composition for the portions other than the hardened layer. The alloy composition is a carbon-containing iron alloy composition and comprises steel compositions such as carbon steel, low alloy steel and high alloy steel. Examples of the composition include alloy steels such as chromium steel, nickel-chromium-molybdenum steel, nickel-molybdenum steel, manganese steel, and manganese-molybdenum steel, but the composition is not limited thereto, and Fe — Cu — C alloys and other carbon-containing iron alloy compositions are also included in the category. An iron-based sintered alloy having a hardened surface can be obtained by nitriding and quenching the iron-based sintered alloy substrate having the above composition to form a hardened layer.
The production of the iron-based sintered alloy base material before hardening is described below, but it is needless to say that an iron-based sintered alloy product having such a composition is commercially available and subjected to nitriding quenching to harden the surface thereof. Nitriding quenching of the iron-based sintered gold base material will be described later.
< production of iron-based sintered alloy substrate >
The raw material powder used for producing the iron-based sintered gold base material is a mixed powder containing carbon powder and iron as a main component (iron-based mixed powder), and depending on the target alloy composition, for example, an alloying component such as chromium (Cr), copper (Cu), molybdenum (Mo), manganese (Mn), nickel (Ni), aluminum (Al), vanadium (V), titanium (Ti), or silicon (Si) may be optionally blended. The alloying components may be blended in the raw material powder in the form of an alloy powder with iron, or may be blended in the form of a single powder. Chromium and molybdenum are particularly effective ingredients for improving the hardness and mechanical properties of the material. An iron-based sintered alloy having the same composition as the alloy steel such as the chromium steel and the nickel-molybdenum steel can be obtained from a raw material powder containing one or more of chromium, copper, molybdenum, manganese, and nickel. When any or all of the above alloying components are blended, the contents of the alloying components in the iron-based sintered alloy are preferably, respectively, chromium: 0.15 to 4.5 mass%, copper: 0.2 to 4.5 mass%, molybdenum: 0.1 to 2.0 mass%, manganese: 0.1 to 3.0 mass%, nickel: 0.2 to 4.5 mass%.
When a graphite powder having an average particle diameter of about 1 to 40 μm is used as the carbon powder used for preparing the raw material powder, the graphite powder is favorably diffused into the matrix. When the single powder or alloy powder for iron and alloying components has an average particle diameter of about 1 to 300 μm, preferably about 45 to 150 μm, the powder is preferably excellent in compactibility in molding and easy to produce and handle. Powders for the respective components are blended in a ratio corresponding to the composition of the target iron-based sintered alloy and uniformly mixed, and the obtained mixed powder is used as a raw material powder for molding a green compact. In consideration of the scattering portion (emanation), the ratio of the graphite powder in the raw material powder for preparing the iron-based sintered gold substrate having a carbon content of 0.1 to 1.0 mass% may be about 0.1 to 1.2 mass%. If a powder lubricant such as a stearate is appropriately added as necessary, the compressibility of the raw material powder is improved.
In the molding of the raw material powder, the raw material powder is put into a cavity having a desired shape, and the raw material powder is compressed by a press machine to be molded into a green compact. The molding pressure may be appropriately set in accordance with the density required for the target product, and may be generally set in the range of about 250 to 800 MPa.
The green compact obtained by the molding is heated and sintered to obtain a green compact having a density of 6.0 to 7.6Mg/m 3 A sintered body, i.e., an iron-based sintered gold substrate. The sintering temperature is set to an appropriate temperature according to the composition of the iron-based sintered alloy, and generally, may be set to a temperature range of about 1000 to 1300 ℃. If the sintering environment is oxidizingSince the sintering alloy is oxidized, the sintering is performed in an "environment non-oxidizing to the green compact", that is, an environment in which the green compact is not oxidized. Specifically, the sintering may be performed under reduced pressure or in a non-oxidizing atmosphere of an inert gas such as argon or nitrogen. In the case of a green compact containing neither chromium nor molybdenum, an endothermic transition gas (ガス) may be used in the sintering atmosphere since it does not cause oxidation of the green compact. That is, depending on the composition of the green compact, the endothermic conversion gas may be "an environment that is non-oxidizing to the green compact". The atmosphere gas containing hydrogen has an advantage of reducing oxygen on the surface of the powder and promoting sintering. It is preferable to use an atmosphere having a low dew point. The iron-based sintered alloy base material is obtained by such heating and sintering, and the iron-based sintered alloy base material is recovered by cooling the furnace.
< quenching by nitriding >
Nitriding quenching is performed by bringing an iron-based sintered gold base material into contact with a gas for nitriding, and therefore, it is necessary to adjust the atmosphere conditions of the iron-based sintered gold base material. Therefore, before and after the iron-based sintered alloy base material recovered from the sintering furnace is introduced into the quenching furnace, the atmosphere conditions in the quenching furnace are adjusted as follows.
As the atmosphere adjustment before nitriding quenching, the inside of the furnace was evacuated and pressure recovery (nitrogen substitution) was performed with nitrogen gas to sufficiently remove oxygen. The iron-based sintered alloy substrate was placed in a furnace whose atmosphere was adjusted in this manner. Then, vacuum is again applied, and a low pressure of about 50Pa is maintained for about 10 to 30 minutes, preferably about 20 minutes. Thereby, the residual gas in the pores of the iron-based sintered gold base material was removed. Further, the pressure is recovered by nitrogen gas, and heating is started to raise the temperature in the furnace to the nitriding temperature. The nitriding temperature is a temperature greater than or equal to the austenitizing temperature, i.e., greater than or equal to 590 ℃, and nitriding is carried out at a temperature of 590-900 ℃. In view of nitriding speed and thermal strain, a temperature range of the order of 650 to 800 ℃ is preferable. The time for carrying the iron-based sintered alloy substrate into the furnace and performing the evacuation and the temperature rise may be less than or equal to about 1 hour.
After the temperature in the furnace reaches the nitriding temperature, the temperature is maintained and left to stand for about 10 to 30 minutes, preferably about 20 minutes, so that the temperature of the iron-based sintered alloy substrate is equalized as a whole. Then, a nitriding gas is supplied into the furnace to start a nitriding treatment.
The nitriding treatment is performed by bringing a nitriding gas into contact with the iron-based sintered alloy base material. As the gas for nitriding, nitriding is performed in an atmosphere containing ammonia and nitrogen using a gas containing ammonia. Nitriding can also be performed using a mixed gas of ammonia and hydrogen, and such a gas can also be used. Ammonia gas becomes unstable when heated and thermally decomposes into nitrogen molecules and hydrogen molecules. If steel is present, atomic nitrogen and hydrogen are generated only on the surface of hot steel due to the catalytic action thereof, and active atomic nitrogen permeates and diffuses into the steel. On the surface of the iron-based sintered gold base material heated to an austenitizing temperature (about 590 ℃) or higher, active atomic nitrogen penetrates into the alloy, and at the same time, nitrogen is dissolved to cause diffusion (nitriding), and the surface layer portion assumes an Fe — N austenite phase. Since nitriding proceeds with the decomposition reaction as described above, it is preferable to use a mixed gas of ammonia gas and nitrogen gas 1:2 as the nitriding gas. The nitriding proceeds at a rate depending on the nitrogen concentration, and the solid solubility limit of nitrogen in the Fe-N system is about 2.8 mass% N, which is larger than the solid solubility limit of carbon (2.1 mass% C) in the Fe-C system. The nitriding treatment may be performed for about 30 to 180 minutes, preferably about 120 to 180 minutes, whereby a hardened layer having a depth of about 100 μm or more can be formed. The depth of nitrogen solid solution varies depending on the treatment conditions, and by extending the nitriding treatment time, nitrogen can be diffused more deeply, and the depth of the hardened layer obtained after quenching increases. The nitriding time is preferably set so that a hardened layer having a depth of about 200 μm or more can be formed.
The Fe — N austenite phase is transformed into martensite (nitrogen martensite) supersaturated with nitrogen and solid-dissolved by rapid cooling, forming a hardened layer having high hardness and fatigue strength. Therefore, the hardened layer can be formed on the surface by quenching the nitrided iron-based sintered gold base material. The quenching temperature may be 640 to 800 ℃ as long as it is equal to or higher than the austenitizing temperature, but the quenching temperature may be set to a temperature lower than the nitriding temperature in order to reduce the thermal strain. Therefore, the quenching temperature is preferably set to about 640 to 720 ℃ and more preferably to 660 to 700 ℃, and the temperature in the furnace can be lowered to the quenching temperature after the nitriding treatment. In this case, it is desirable to avoid a rapid temperature drop from the viewpoint of suppressing thermal strain, and the rate of temperature drop may be set to about 0.6 to 1.0 ℃/min, preferably about 0.8 ℃/min.
After the temperature in the furnace reaches the quenching temperature, the temperature is maintained at the quenching temperature for about 10 to 30 minutes, preferably about 20 minutes, so that the temperature of the iron-based sintered alloy substrate is equalized as a whole. Then, the supply of the nitriding gas is stopped, and quenching is performed using a quenching liquid or gas, whereby the surface layer portion is hardened by martensitic transformation of the austenite phase, and quenching is performed. The quenching liquid may be oil or water, and is preferably oil quenched with oil at about 40 to 150 ℃. As the gas, an inert gas such as nitrogen or argon is preferably used. Cooling is carried out until the temperature of the iron-based sintered alloy substrate is less than or equal to 50 ℃.
The iron-based sintered alloy material obtained by quenching has a hardened layer exhibiting a martensite phase in which nitrogen is supersaturated and solid-dissolved on the surface. In the hardened layer on the surface, nitrogen is dissolved in solid solution and the concentration increases. Since the iron-based sintered alloy material is cooled from a quenching temperature lower than the carburizing and quenching temperature, the thermal strain is smaller than that of the carburizing and quenching material. When the iron-based sintered alloy material is tempered, the residual austenite can be transformed into martensite to stabilize the structure and impart flexibility while further removing stress. The tempering is suitably low-temperature tempering capable of preventing embrittlement, and the tempering temperature may be set to about 100 to 200 ℃, preferably about 150 to 200 ℃. The heating time for tempering may be about 1 hour, and the tempering may be performed in any of an air (air) atmosphere, a nitrogen atmosphere, and a reducing atmosphere.
The iron-based sintered alloy material obtained as described above has increased hardness by forming a hardened layer on the surface by nitriding quenching, and contributes to improvement of the surface fatigue strength by forming the hardened layer to a depth of 100 μm or more. Specifically, by nitriding and quenching an iron-based sintered alloy base material having a hardness (Vickers hardness) of about 100 to 350Hv, the hardness at a distance of 0.1mm from the surface is increased to about 800Hv or more. By such case hardening, an iron-based sintered alloy material having improved wear resistance and reduced wear amount can be provided.
In the present invention, depending on the austenitizing temperature, the nitriding temperature is lower than the carburizing temperature, and the quenching may be performed at a low temperature. In the above-described manufacturing method, the thermal strain after quenching is further reduced by setting the quenching temperature to be lower than the nitriding temperature. Therefore, the thermal strain in the obtained iron-based sintered alloy material is halved as compared with the thermal strain at the time of carburizing and quenching, and therefore, the dimensional accuracy of the product can be significantly improved.
As described above, the surface-hardened iron-based sintered alloy material can be produced with high dimensional accuracy by nitriding quenching, and an iron-based sintered alloy product excellent in surface fatigue strength and wear resistance suitable for machine parts and structural members can be provided. In machine parts and the like, depending on the application field, the required accuracy and quality may vary, and the iron-based sintered alloy material may be subjected to nitriding quenching after being subjected to machining such as shaping, coining, rolling, and the like as appropriate. Even if such processing is performed, pores remain in the densified surface layer, and nitriding proceeds. In this case, the porous iron-based sintered alloy material can be provided as a product in which the surface is densified. Alloy compositions (numerical values representing composition ratios are mass%) of excellent materials which can be provided by carrying out the present invention are exemplified below.
(Fe-C series sintered alloy)
Iron materials contain a small amount of unavoidable impurities due to the production method, and carbon steel also contains a small amount (less than 1%) of manganese and the like. Carbon steel, which is an iron-carbon alloy containing carbon in an amount of about 0.02 to 2%, has toughness and can be used for the production of automobile parts, structural parts for mechanical devices, and the like, but because of its low hardness, various parts having improved durability can be provided by performing surface hardening by nitriding quenching. The durability of Fe — C sintered alloys having the same alloy composition as carbon steel can also be improved by case hardening by nitriding quenching, and for example, by applying the technique of the present invention to sintered alloy materials having the same alloy composition as carbon steel for machine structures (S45C in JIS standard) having a carbon content of 0.45%, carbon tool steel (SK 95 in JIS standard) having a carbon content of 0.9 to 1.0%, and the like, mechanical parts, tools, and the like of Fe — C sintered alloys having excellent durability can be provided.
(Fe-Cr-C series sintered alloy)
Chromium steels (SCr 435, SCr440, SCr445, etc. in JIS standard), stainless steels (SUS 420, etc. in JIS standard), high-carbon chromium bearing steels (SUJ 2 in JIS standard), etc. contain chromium in the range of 0.15 to 4.5%, carbon in the range of 0.2 to 1.0%, and manganese as an unavoidable impurity. Further, chromium molybdenum steel (SCM 435, SCM440, etc. of JIS standard) contains chromium of about 0.9 to 1.2%, molybdenum of about 0.1 to 0.2%, carbon of about 0.35 to 0.5%, and inevitable impurities, and is a material having high strength, and thus can be used as a structural material. The effectiveness of nitriding and quenching of Fe-Cr-C alloys is high, and the effect is enhanced if chromium nitride is dispersed in the hardened layer. Therefore, the durability of the Fe-Cr-C sintered alloy can be improved by surface hardening by nitriding quenching, and the technique of the present invention can be applied to a sintered alloy material having the same alloy composition as the steel material, thereby providing a machine part, a tool, or the like of the Fe-Cr-C sintered alloy having excellent durability.
(Fe-Cu-C sintered alloy)
The copper steel contains about 0.2 to 4.5% of copper, about 0.4 to 1.0% of carbon, and inevitable impurities. Can be used as general structural material. When the technique of the present invention is applied to a sintered alloy material having the same alloy composition as that of such a steel material, it is possible to provide a Fe — Cu — C-based sintered alloy having excellent durability as a general structural material or the like.
(Fe-Ni-Mo-C series sintered alloy)
The nickel-molybdenum steel contains about 0.2 to 5.0% of nickel, about 0.1 to 2.0% of molybdenum, about 0.2 to 1.0% of carbon, and inevitable impurities. The composition is a composition to which toughness and wear resistance are imparted by nickel and wear resistance is imparted by molybdenum. Since nickel and molybdenum improve hardenability and suppress softening during tempering, when the technique of the present invention is applied to a sintered alloy material having the same alloy composition as the steel material, the iron-based sintered alloy material having a hardened layer formed thereon exhibits very high hardness.
(Fe-Mn-Mo-C type sintered alloy)
The manganese-molybdenum steel contains 0.1 to 3.0% manganese, 0.1 to 2.0% molybdenum, and 0.2 to 1.0% carbon, and has a high tensile strength.
The composition is one in which toughness and wear resistance are imparted by manganese and wear resistance is imparted by molybdenum. Since molybdenum suppresses softening during tempering, when the technique of the present invention is applied to a sintered alloy material having the same alloy composition as the steel material, the iron-based sintered alloy material having a hardened layer formed thereon exhibits a very high hardness.
Example 1
(sample 1)
Graphite powder was mixed with Fe-Cr-Mo-Mn alloy powder and uniformly mixed to prepare a powder having an overall composition (mass%) of Cr:0.5%, mo:0.2%, mn:0.2%, C:0.5% and the balance iron. Using this raw material powder, the following molding and sintering were performed.
A mold having a circular cavity with an outer diameter of 50mm, an inner diameter of 30mm and a length of 6mm was prepared, and a raw material powder was put into the cavity and compressed by a press to form a green compact with a density of 7.2Mg/m 3 To a degree of dust compaction. The compact was placed in a sintering furnace, heated to 1200 ℃ in a mixed gas atmosphere of 90% nitrogen and 10% hydrogen, and the temperature in the furnace was reduced after sintering for 60 minutes, to obtain an iron-based sintered gold substrate of sample 1. In addition, as for the density, the powder compact was immersed in the liquid rust preventive oil according to the archimedes method to measure the weight change at room temperature, and determined based on the obtained weight change.
(sample 2)
Copper powder, graphite powder and a forming lubricant were mixed with iron powder to prepare a powder composed of Cu:1.5%, C:0.6% and the balance iron, and using this raw material powder, a green compact was produced in the same manner as in sample 1, and this green compact was placed in a sintering furnace, heated to 1130 ℃ in a mixed gas atmosphere of 90% nitrogen and 10% hydrogen, and after sintering for 60 minutes, the furnace temperature was lowered to obtain an iron-based sintered gold substrate of sample 2.
(sample 3)
Nickel powder, graphite powder and a forming lubricant were mixed with Fe — Mo alloy powder to prepare a Fe — Mo alloy powder containing Mo:1.5%, ni:2.0%, C: the same operation as in sample 1 was repeated except that 0.5% and the balance of raw material powder made of iron were used, and the iron-based sintered gold base material of sample 3 was obtained.
(sample 4)
Fe-Mn alloy powder, copper powder, graphite powder and a forming lubricant are mixed into Fe-Mo alloy powder, and the mixture is prepared by mixing the following components in percentage by weight: 1.3%, mo:0.5%, cu:1.0%, C: the same operation as in sample 1 was repeated except that 0.5% and the balance of raw material powder made of iron were used, and the iron-based sintered gold substrate of sample 4 was obtained.
(nitriding quenching)
Each of the iron-based sintered alloy base materials of samples 1 to 4 was subjected to size matching (sample length after machining: 5.6 mm), and then subjected to nitriding quenching and tempering as follows. In the following operations, the nitriding temperature was 780 ℃ (samples 1 to 3) or 740 ℃ (sample 4), the quenching temperature was 700 ℃, and the tempering temperature was 180 ℃.
After evacuation of the inside of the furnace of the hot wall type nitriding quenching furnace, nitrogen gas was supplied for pressure recovery, and the iron-based sintered alloy substrate was placed in the furnace, and after 20 minutes of evacuation, nitrogen gas was supplied for pressure recovery. The furnace is heated and the temperature is raised to the nitriding temperature for about 40 minutes. After reaching the nitriding temperature, the temperature was maintained and left for 20 minutes. Then, a mixed gas of ammonia gas and nitrogen gas (flow ratio = 1/2) was used as a nitriding gas, and the nitriding gas was started to be supplied and brought into contact with the iron-based sintered alloy substrate to carry out nitriding treatment. After nitriding treatment was continued for 180 minutes, the furnace temperature was lowered to the quenching temperature at a cooling rate of 0.8 ℃/minute, and the temperature was maintained for 20 minutes. Then, the supply of the nitriding gas was stopped, and the iron-based sintered alloy substrate was quenched using oil of 65 ℃ as a quenching liquid, thereby quenching the substrate.
Further, the iron-based sintered alloy material surface-hardened by quenching was tempered by heating at a tempering temperature for 60 minutes in a furnace in an atmospheric atmosphere, and then, the heating was stopped and the iron-based sintered alloy material was recovered by natural cooling.
(carburizing and quenching)
The same procedure as nitriding quenching was repeated except that a gas carburizing agent (gas containing carbon monoxide and hydrocarbon) was used instead of the gas for nitriding, the heating temperature was changed from the nitriding temperature to the carburizing temperature, and quenching was performed at the carburizing temperature without lowering the temperature after the carburizing treatment. The same tempering was performed to obtain an iron-based sintered alloy material obtained by carburizing and quenching the iron-based sintered alloy base materials of samples 1 to 4. Note that the carburizing temperature was set to 850 ℃ (samples 1, 3, and 4) or 900 ℃ (sample 2).
(measurement of hardness)
For each of samples 1 to 4, the hardness (H) of the iron-based sintered alloy material after surface hardening was measured using a Rockwell hardness tester (ARK-F1000, manufactured by AKASHI Co., ltd.) R A) In that respect The measurement was performed at room temperature using a conical diamond indenter under a load of 60kgf (588N), and the value was obtained as an average value of 5-point measurements. Further, the hardness (Vickers hardness H) at a depth of 0.1mm from the surface of the cross section of the iron-based sintered alloy material subjected to the etching treatment with a 5% nital etchant was measured (load: 0.98N) using a micro hardness measuring apparatus (HM-200, manufactured by Sanfeng Co., ltd.) v ) A value was obtained as an average of the 5-point measurement values. The results are shown in Table 1.
[ Table 1]
As is clear from table 1, in any of samples 1 to 4, the hardness at a depth of 0.1mm in the iron-based sintered alloy material obtained by nitriding quenching was significantly improved as compared with the case of carburizing quenching, and the case hardening was appropriately completed.
Further, in sample 2, the hardness at a depth of 1.0mm from the surface was measured in the cross section of the iron-based sintered alloy material, and the result was 700H at the time of nitriding quenching v 610H in carburizing and quenching v . From this, it is considered that the penetration diffusion of nitrogen upon nitriding quenching reaches a depth of approximately 1 mm.
Example 2
A mold having a cavity for forming sprocket teeth for a variable phase system having a roller outer bus bar diameter of 94.425mm was prepared. The alloy powder is mixed with Fe-Mo-Ni alloy powder, graphite powder and a forming lubricant to prepare a composite material (mass percent) consisting of Mo:0.55%, ni:0.55%, C: a mixed powder of 0.25% and the balance of iron and unavoidable impurities was used as a raw material powder, and an iron-based sintered alloy substrate having a sprocket tooth shape was produced in the same manner as in example 1. Then, the teeth are subjected to rolling treatment to densify the outermost surface of the teeth.
Using the above base material, nitriding quenching or carburizing quenching was performed in the same manner as in example 1 to obtain an iron-based sintered alloy material having a sprocket tooth shape with a hardened layer formed on the surface. Wherein the nitriding temperature is set to 700 ℃ and the carburizing temperature is set to 900 ℃.
Further, the above base material was subjected to carbonitriding quenching to obtain an iron-based sintered alloy material having a sprocket tooth shape with a hardened layer formed on the surface thereof. Carbonitriding quenching is performed by repeating the same operation as the above-described carbonitriding quenching except that a gaseous carburizing agent containing ammonia gas is used as an atmospheric gas for carbonitriding instead of the gaseous carburizing agent in the above-described carbonitriding quenching, and the heating temperature is changed from the carburizing temperature to the carbonitriding temperature (780 ℃).
The metal structures of the cross sections of the 3 alloy materials obtained above were photographed, and the obtained SEM images are shown in fig. 1. In FIG. 1, (a) is an SEM image obtained by carburizing and quenching, and (b) isSEM image obtained by carbonitriding quenching, and (c) SEM image obtained by nitriding quenching. Further, the hardness at 0.1mm from the surface of the cross section of the alloy material was measured, and the hardness at 0.1mm from the surface was 680H v (carburizing and quenching) 680H v (carbonitriding quenching) 700H v (nitriding quenching). Further, 7.0g/cm was measured by a three-ball pitting test 3 Fatigue strength of face pressure (temperature: room temperature, rotation speed: 600 min) -1 And (3) using oil: MTF-III, ball material: SUJ-2), the results showed that the surface fatigue strength was 2.35GPa (carburizing-quenching), 2.35GPa (carburizing-nitriding-quenching) or 2.40GPa (nitriding-quenching).
Further, the strain of the sprocket tooth shape was evaluated based on the strain measurement as the ellipse amount obtained by the strain analysis, and the average values of the ellipse amounts were 156 μm (carburizing and quenching), 119 μm (carburizing and nitriding and quenching), and 60 μm (nitriding and quenching). It is understood that the strain due to nitriding quenching is reduced to about 40% of the strain at the time of carburizing and quenching.
The disclosure of the present application is related to the subject matter described in japanese patent application No. 2017-217064, filed on 11/10/2017, the entire disclosure of which is incorporated herein by reference.
It should be noted that various modifications and changes may be made to the above-described embodiments in addition to those already described without departing from the novel and advantageous features of the present invention. Accordingly, all such modifications and changes are intended to be included within the scope of the appended claims.
Industrial applicability of the invention
Since a hardened layer obtained by nitriding can be formed at an appropriate depth on the surface of an iron-based sintered alloy, and a sintered member having excellent hardness, wear resistance, and surface fatigue strength can be provided with high dimensional accuracy, the sintered alloy is suitable for various machine parts requiring durability, such as sprockets, gears, rollers, and shafts of motors, and can contribute to the spread of products by improving quality and reducing manufacturing cost.
Claims (7)
1. A surface hardening material for a sintered alloy base material obtained by nitriding and quenching a sintered alloy base material having a carbon-containing iron alloy composition,
the iron-based sintered alloy material contains carbon, 0.1 to 1.0 mass% of carbon, and at least one alloying component selected from the group consisting of 0.15 to 4.5 mass% of chromium, 0.2 to 4.5 mass% of copper, 0.1 to 2.0 mass% of molybdenum, 0.1 to 3.0 mass% of manganese, and 0.2 to 4.5 mass% of nickel, and has a hardened layer exhibiting a martensite phase in which nitrogen is supersaturated and solid-dissolved on the surface,
the depth of the hardened layer from the surface is greater than or equal to 100 μm,
the Vickers hardness at 0.1mm from the surface is greater than or equal to 800Hv.
2. The surface-hardening iron-based sintered alloy material according to claim 1, wherein the alloying component contains 0.15 to 4.5 mass% of chromium.
3. The surface-hardening iron-based sintered alloy material according to claim 1, wherein the alloying component contains 0.2 to 4.5 mass% of copper.
4. The surface-hardened material of an iron-based sintered alloy material according to any one of claims 1 to 3, wherein the depth of the hardened layer from the surface is 200 μm or more.
5. A sprocket comprising the hardfacing material of the iron-based sintered alloy material of claim 1.
6. A gear comprising a hardfacing material of the iron-based sintered alloy material of claim 1.
7. A shaft comprising a hardfacing material of the iron-based sintered alloy material of claim 1.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2017217064A JP7167428B2 (en) | 2017-11-10 | 2017-11-10 | Iron-based sintered alloy material and its manufacturing method |
| JP2017-217064 | 2017-11-10 | ||
| PCT/JP2018/041670 WO2019093480A1 (en) | 2017-11-10 | 2018-11-09 | Iron-based sintered alloy material and production method therefor |
| CN201880072656.0A CN111344429B (en) | 2017-11-10 | 2018-11-09 | Iron-based sintered alloy material and method for producing same |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201880072656.0A Division CN111344429B (en) | 2017-11-10 | 2018-11-09 | Iron-based sintered alloy material and method for producing same |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN115595530A true CN115595530A (en) | 2023-01-13 |
Family
ID=66437899
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211337786.7A Pending CN115595530A (en) | 2017-11-10 | 2018-11-09 | Surface hardening material of iron-based sintered alloy material, and sprocket, gear and shaft comprising same |
| CN201880072656.0A Active CN111344429B (en) | 2017-11-10 | 2018-11-09 | Iron-based sintered alloy material and method for producing same |
Family Applications After (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201880072656.0A Active CN111344429B (en) | 2017-11-10 | 2018-11-09 | Iron-based sintered alloy material and method for producing same |
Country Status (4)
| Country | Link |
|---|---|
| US (2) | US20200331068A1 (en) |
| JP (1) | JP7167428B2 (en) |
| CN (2) | CN115595530A (en) |
| WO (1) | WO2019093480A1 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| TWI726451B (en) * | 2019-10-21 | 2021-05-01 | 晟銘電子科技股份有限公司 | Preparing method of molded article having nitrided layer and molded article thereof |
| CN112475304B (en) * | 2020-12-09 | 2021-09-28 | 福州大学 | 12Cr stainless steel surface strengthening method based on spark plasma sintering |
| JP2022126017A (en) * | 2021-02-18 | 2022-08-30 | 株式会社日立製作所 | Sliding member, method for producing the same, and apparatus for producing the same |
| KR102586490B1 (en) * | 2021-08-13 | 2023-10-06 | 현대자동차주식회사 | Outer ring for oil pump and methods for producing the same |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03219040A (en) * | 1990-01-24 | 1991-09-26 | Komatsu Ltd | High strength sintered steel and its manufacture |
| JPH05247580A (en) * | 1992-03-03 | 1993-09-24 | Sintokogio Ltd | Production of permeable metal mold material |
| JPH09125211A (en) * | 1995-10-31 | 1997-05-13 | Tokyo Shiyouketsu Kinzoku Kk | Ferrous sintered soft-magnetic material excellent in wear resistance and its production |
| US5782953A (en) * | 1997-01-23 | 1998-07-21 | Capstan Inland | Surface hardened powdered metal stainless steel parts |
| CN1946865A (en) * | 2004-04-23 | 2007-04-11 | 株式会社丰田中央研究所 | Iron-based sintered alloy, iron-based sintered alloy member and method for producing those |
| US20120018050A1 (en) * | 2010-03-19 | 2012-01-26 | Jx Nippon Mining & Metals Corporation | Steel for surface layer hardening treatment, surface layer-hardened steel part, and method of manufacturing the same |
| CN102605273A (en) * | 2012-04-11 | 2012-07-25 | 长沙威斯坦冶金制品有限公司 | Steel bonded hard alloy and preparation method thereof |
| CN102933338A (en) * | 2010-06-04 | 2013-02-13 | 霍加纳斯股份有限公司 | Nitrided sintered steels |
| US20130313405A1 (en) * | 2011-02-14 | 2013-11-28 | Shintokogio, Ltd. | Mold and die metallic material, air-permeable member for mold and die use, and method for manufacturing the same |
| WO2014037627A1 (en) * | 2012-09-06 | 2014-03-13 | Arcelormittal Investigación Y Desarrollo Sl | Process for manufacturing press-hardened coated steel parts and precoated sheets allowing these parts to be manufactured |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6040505B2 (en) * | 1980-04-07 | 1985-09-11 | 三菱製鋼株式会社 | Manufacturing method of nitrided sintered alloy |
| JPH04218607A (en) * | 1990-12-18 | 1992-08-10 | Nkk Corp | Sintered compact having pore in surface |
| KR100398563B1 (en) * | 1999-11-15 | 2003-09-19 | 마츠시타 덴끼 산교 가부시키가이샤 | Rotary compressor and method for manufacturing same |
| JP2004132370A (en) * | 2002-09-20 | 2004-04-30 | Mitsubishi Materials Corp | Sprocket integrated housing and its manufacturing method |
| SE526249C2 (en) * | 2003-12-05 | 2005-08-02 | Erasteel Kloster Ab | Steel material and use of this material |
| BR112016007332B1 (en) * | 2013-10-02 | 2020-03-10 | Uddeholms Ab | STEEL MADE BY POWDER METALLURGY AND METHOD FOR MANUFACTURING THE SAME |
| CN105177397B (en) * | 2015-10-08 | 2017-03-22 | 东睦新材料集团股份有限公司 | Preparation method for powder metallurgy wear-resisting stainless steel |
-
2017
- 2017-11-10 JP JP2017217064A patent/JP7167428B2/en active Active
-
2018
- 2018-11-09 US US16/762,737 patent/US20200331068A1/en not_active Abandoned
- 2018-11-09 WO PCT/JP2018/041670 patent/WO2019093480A1/en active Application Filing
- 2018-11-09 CN CN202211337786.7A patent/CN115595530A/en active Pending
- 2018-11-09 CN CN201880072656.0A patent/CN111344429B/en active Active
-
2023
- 2023-02-24 US US18/173,929 patent/US20230211413A1/en active Pending
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03219040A (en) * | 1990-01-24 | 1991-09-26 | Komatsu Ltd | High strength sintered steel and its manufacture |
| JPH05247580A (en) * | 1992-03-03 | 1993-09-24 | Sintokogio Ltd | Production of permeable metal mold material |
| JPH09125211A (en) * | 1995-10-31 | 1997-05-13 | Tokyo Shiyouketsu Kinzoku Kk | Ferrous sintered soft-magnetic material excellent in wear resistance and its production |
| US5782953A (en) * | 1997-01-23 | 1998-07-21 | Capstan Inland | Surface hardened powdered metal stainless steel parts |
| CN1946865A (en) * | 2004-04-23 | 2007-04-11 | 株式会社丰田中央研究所 | Iron-based sintered alloy, iron-based sintered alloy member and method for producing those |
| US20120018050A1 (en) * | 2010-03-19 | 2012-01-26 | Jx Nippon Mining & Metals Corporation | Steel for surface layer hardening treatment, surface layer-hardened steel part, and method of manufacturing the same |
| CN102933338A (en) * | 2010-06-04 | 2013-02-13 | 霍加纳斯股份有限公司 | Nitrided sintered steels |
| US20130313405A1 (en) * | 2011-02-14 | 2013-11-28 | Shintokogio, Ltd. | Mold and die metallic material, air-permeable member for mold and die use, and method for manufacturing the same |
| CN102605273A (en) * | 2012-04-11 | 2012-07-25 | 长沙威斯坦冶金制品有限公司 | Steel bonded hard alloy and preparation method thereof |
| WO2014037627A1 (en) * | 2012-09-06 | 2014-03-13 | Arcelormittal Investigación Y Desarrollo Sl | Process for manufacturing press-hardened coated steel parts and precoated sheets allowing these parts to be manufactured |
Non-Patent Citations (3)
| Title |
|---|
| 夏立芳等: "《钢的渗氮》", 30 June 1989, 机械工业出版社, pages: 38 - 41 * |
| 管鄂编: "《淬火新技术》", 30 November 1987, 上海科学技术出版社, pages: 132 - 139 * |
| 韩福海等: "《热处理工现场操作技能》", 31 July 2008, 国防工业出版社, pages: 196 - 198 * |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2019085634A (en) | 2019-06-06 |
| CN111344429A (en) | 2020-06-26 |
| WO2019093480A1 (en) | 2019-05-16 |
| US20230211413A1 (en) | 2023-07-06 |
| CN111344429B (en) | 2022-11-15 |
| JP7167428B2 (en) | 2022-11-09 |
| US20200331068A1 (en) | 2020-10-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111344429B (en) | Iron-based sintered alloy material and method for producing same | |
| JP5671526B2 (en) | High strength low alloy sintered steel | |
| Akhtar et al. | Evaluation of gas nitriding process with in-process variation of nitriding potential for AISI H13 tool steel | |
| RU2271263C2 (en) | Metal powder articles with compacted surface manufacturing method | |
| US10213832B2 (en) | Sintered member, pinion gear for starters, and production method therefor | |
| RU2699882C2 (en) | Pre-alloyed iron-based powder, iron-based powder mixture containing pre-alloyed iron-based powder, and method of making pressed and sintered parts from iron-based powder mixture | |
| CN107406959B (en) | Nitrided component and soft nitrided component having excellent wear resistance and pitting resistance, and nitriding method and soft nitriding method | |
| JP5477111B2 (en) | Nitriding induction hardening steel and nitriding induction hardening parts | |
| EP2200769B1 (en) | Method of producing a sinter-hardened component | |
| US20100196188A1 (en) | Method of producing a steel moulding | |
| US7722803B2 (en) | High carbon surface densified sintered steel products and method of production therefor | |
| JP4301507B2 (en) | Sintered sprocket for silent chain and manufacturing method thereof | |
| JP7364895B2 (en) | Steel parts and their manufacturing method | |
| JP4821810B2 (en) | Carburizing heat treatment method and carburizing source material | |
| Dahlström et al. | High performance PM components heat treated by low pressure carburizing and gas quenching | |
| Kremel et al. | Low-pressure carburizing of sintered alloy steels with varying porosity | |
| JP2004107709A (en) | Rolling member and manufacturing method thereof | |
| Engstrom et al. | Efficient Low-Alloy Steels for High-Performance Structural Applications | |
| Bengtsson et al. | Carburizing of Low-Alloyed Chromium Materials–An Overview | |
| JP2012219317A (en) | Iron-based material and method for producing the same | |
| Pauty et al. | ECM Technologies, Large Scale Production Equipment for Heat Treating PM Parts, Improvement and Innovation | |
| Dahlström | Influence of Alloying Content on Low Pressure Carburized and Gas Quenched PM Components | |
| Santos et al. | Influence of repeated quenching on the rolling contact fatigue of bearing steel | |
| Dlapka et al. | Heat Treatment: Porosity Effects in Low Pressure Carburizing of Sintered Steels | |
| Dahlström et al. | Heat Treatment/Steam Treatment/Properties: High Performance PM Components Heat Treated by Low Pressure Carburizing and Gas Quenching |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| CB02 | Change of applicant information | ||
| CB02 | Change of applicant information |
Address after: Tokyo, Japan Applicant after: Lishennoco Co.,Ltd. Address before: Tokyo, Japan Applicant before: Showa electrical materials Co.,Ltd. |