NO153838B - DEVICE FOR REGULATION OF THE KATA VALUE. - Google Patents
DEVICE FOR REGULATION OF THE KATA VALUE. Download PDFInfo
- Publication number
- NO153838B NO153838B NO794210A NO794210A NO153838B NO 153838 B NO153838 B NO 153838B NO 794210 A NO794210 A NO 794210A NO 794210 A NO794210 A NO 794210A NO 153838 B NO153838 B NO 153838B
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- Prior art keywords
- percent
- phase
- alloy
- iron
- sintered
- Prior art date
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- 229910045601 alloy Inorganic materials 0.000 claims description 50
- 239000000956 alloy Substances 0.000 claims description 50
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 35
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 30
- 239000010941 cobalt Substances 0.000 claims description 18
- 229910017052 cobalt Inorganic materials 0.000 claims description 18
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 18
- 229910052742 iron Inorganic materials 0.000 claims description 17
- 229910052759 nickel Inorganic materials 0.000 claims description 15
- 229910052751 metal Inorganic materials 0.000 claims description 13
- 239000002184 metal Substances 0.000 claims description 13
- 239000011230 binding agent Substances 0.000 claims description 8
- 229910001018 Cast iron Inorganic materials 0.000 claims description 7
- 239000010959 steel Substances 0.000 claims description 7
- 229910001208 Crucible steel Inorganic materials 0.000 claims description 5
- 229910039444 MoC Inorganic materials 0.000 claims description 5
- QIJNJJZPYXGIQM-UHFFFAOYSA-N 1lambda4,2lambda4-dimolybdacyclopropa-1,2,3-triene Chemical compound [Mo]=C=[Mo] QIJNJJZPYXGIQM-UHFFFAOYSA-N 0.000 claims description 4
- 238000005520 cutting process Methods 0.000 claims description 4
- 239000000203 mixture Substances 0.000 description 8
- 229910003468 tantalcarbide Inorganic materials 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 238000005245 sintering Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 229910003178 Mo2C Inorganic materials 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 1
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60H—ARRANGEMENTS OF HEATING, COOLING, VENTILATING OR OTHER AIR-TREATING DEVICES SPECIALLY ADAPTED FOR PASSENGER OR GOODS SPACES OF VEHICLES
- B60H1/00—Heating, cooling or ventilating [HVAC] devices
- B60H1/00357—Air-conditioning arrangements specially adapted for particular vehicles
- B60H1/00371—Air-conditioning arrangements specially adapted for particular vehicles for vehicles carrying large numbers of passengers, e.g. buses
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60H—ARRANGEMENTS OF HEATING, COOLING, VENTILATING OR OTHER AIR-TREATING DEVICES SPECIALLY ADAPTED FOR PASSENGER OR GOODS SPACES OF VEHICLES
- B60H1/00—Heating, cooling or ventilating [HVAC] devices
- B60H1/00642—Control systems or circuits; Control members or indication devices for heating, cooling or ventilating devices
- B60H1/00814—Control systems or circuits characterised by their output, for controlling particular components of the heating, cooling or ventilating installation
- B60H1/00821—Control systems or circuits characterised by their output, for controlling particular components of the heating, cooling or ventilating installation the components being ventilating, air admitting or air distributing devices
- B60H1/00828—Ventilators, e.g. speed control
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F24—HEATING; RANGES; VENTILATING
- F24F—AIR-CONDITIONING; AIR-HUMIDIFICATION; VENTILATION; USE OF AIR CURRENTS FOR SCREENING
- F24F11/00—Control or safety arrangements
- F24F11/0001—Control or safety arrangements for ventilation
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F24—HEATING; RANGES; VENTILATING
- F24F—AIR-CONDITIONING; AIR-HUMIDIFICATION; VENTILATION; USE OF AIR CURRENTS FOR SCREENING
- F24F11/00—Control or safety arrangements
- F24F11/70—Control systems characterised by their outputs; Constructional details thereof
- F24F11/72—Control systems characterised by their outputs; Constructional details thereof for controlling the supply of treated air, e.g. its pressure
-
- G—PHYSICS
- G05—CONTROLLING; REGULATING
- G05D—SYSTEMS FOR CONTROLLING OR REGULATING NON-ELECTRIC VARIABLES
- G05D16/00—Control of fluid pressure
- G05D16/20—Control of fluid pressure characterised by the use of electric means
- G05D16/2006—Control of fluid pressure characterised by the use of electric means with direct action of electric energy on controlling means
- G05D16/2066—Control of fluid pressure characterised by the use of electric means with direct action of electric energy on controlling means using controlling means acting on the pressure source
-
- G—PHYSICS
- G05—CONTROLLING; REGULATING
- G05D—SYSTEMS FOR CONTROLLING OR REGULATING NON-ELECTRIC VARIABLES
- G05D7/00—Control of flow
- G05D7/06—Control of flow characterised by the use of electric means
- G05D7/0617—Control of flow characterised by the use of electric means specially adapted for fluid materials
- G05D7/0629—Control of flow characterised by the use of electric means specially adapted for fluid materials characterised by the type of regulator means
- G05D7/0676—Control of flow characterised by the use of electric means specially adapted for fluid materials characterised by the type of regulator means by action on flow sources
Description
Sintret hårdmetallegering for bearbeidelse av støpejern og stål. Sintered hard metal alloy for machining cast iron and steel.
Foreliggende oppfinnelse angår en The present invention relates to a
sintret, finkornet hårdmetallegering med utmerkede skjæreegenskaper for bearbeidelse av såvel støpejern som stål. Sammenlignet med tidligere kjente sintrede hård-metallkvaliteter for dette formål har legeringen ifølge foreliggende oppfinnelse en sintered, fine-grained hard metal alloy with excellent cutting properties for processing both cast iron and steel. Compared to previously known sintered cemented carbide grades for this purpose, the alloy according to the present invention has a
bedre slitestyrke forenet med en meget stor seighet. Legeringen har en sammensetning av en i og for seg kjent type og inneholder wolframcarbid som hovedbestanddel, sam-men med titancarbid og fortrinnsvis ett eller flere ytterligere carbider, som tantal-carbid og/eller niobcarbid og et bindemetall som kobolt og/eller nikkel. Det har vist seg at en nødvendig betingelse ved foreliggende legering er at den inneholder i volumprosent: 60—80 pst. WC, 10—25 pst. TiC, 0—20 pst. TaC, NbC og/eller VC, 0—10 pst. Cr2C3, ZrC og/eller HfC, 0—5 pst. Mo og/eller molybdencarbid, idet resten hovedsakelig er kobolt og/eller nikkel og eventuelt også jern. Den samlede mengde av kobolt, nikkel og jern bør ikke overstige 9,5 pst. og innholdet av jern bør ikke overstige 6 pst. better wear resistance combined with a very high toughness. The alloy has a composition of a type known per se and contains tungsten carbide as the main component, together with titanium carbide and preferably one or more additional carbides, such as tantalum carbide and/or niobium carbide and a binder metal such as cobalt and/or nickel. It has been shown that a necessary condition for the present alloy is that it contains in volume percentage: 60-80 percent WC, 10-25 percent TiC, 0-20 percent TaC, NbC and/or VC, 0-10 percent Cr2C3, ZrC and/or HfC, 0-5% Mo and/or molybdenum carbide, the rest being mainly cobalt and/or nickel and possibly also iron. The total amount of cobalt, nickel and iron should not exceed 9.5 per cent and the content of iron should not exceed 6 per cent.
Det er av avgjørende betydning at legeringen har en viss struktur med hensyn til legeringsfasene og kornstørrelsen av carbidene for å oppnå den uventede forbedring av egenskapene som er karakteristisk for foreliggende legering. Den gjennomsnittlige kornstørrelse av carbidkornene bør således være mindre enn 1,6 micron, It is of crucial importance that the alloy has a certain structure with respect to the alloy phases and the grain size of the carbides in order to achieve the unexpected improvement in properties characteristic of the present alloy. The average grain size of the carbide grains should thus be less than 1.6 micron,
fortrinnsvis mindre enn 1,5 micron, og samtidig bør legeringen fremstilles på en preferably less than 1.5 micron, and at the same time the alloy should be produced on a
slik måte at den i volumprosent inneholder 37,5 ± 7,5 pst. av gamma-fase, 8,5 ± 1 pst. av [3-fase, (bindemetall), idet resten består in such a way that it contains, by volume, 37.5 ± 7.5 percent of gamma phase, 8.5 ± 1 percent of [3 phase, (binding metal), the rest consisting
hovedsakelig av a-fase. Ubetydelige mengder av én eller flere ytterligere faser som eta-fase kan eventuelt også være tilstede. En karakteristisk egenskap ved foreliggende legering er at den har en meget finkornet struktur i forhold til ovenstående fasefordeling. mainly of a-phase. Insignificant amounts of one or more additional phases such as eta phase may also be present. A characteristic feature of the present alloy is that it has a very fine-grained structure in relation to the above phase distribution.
Gamma-fasen er i denne forbindelse en fase som består av én eller flere kubiske carbider som TiC, TaC, NbC, VC, ZrC og HfC og som i fast oppløsning inneholder en ikke ubetydelig del WC. (3-fasen er en bindemetallfase som inneholder f. eks. Co, mens a-fasen består av rent WC, eventuelt inneholdende en liten del Mo i fast opp-løsning. I tillegg hertil kan der opptre mindre mengder av andre faser, f. eks. en fase bestående av Mo2C. In this connection, the gamma phase is a phase which consists of one or more cubic carbides such as TiC, TaC, NbC, VC, ZrC and HfC and which in solid solution contains a not insignificant part of WC. (The 3-phase is a binder metal phase containing e.g. Co, while the a-phase consists of pure WC, possibly containing a small amount of Mo in solid solution. In addition to this, smaller amounts of other phases may occur, e.g. eg a phase consisting of Mo2C.
Særlig gode resultater har vært opp-nådd når gamma-fasen utgjør 40 ± 5 volumprosent. Det har vist seg at fS-fasen bør ha flatesentrert kubisk og/eller hexa-gonalt tettpakket krystallgitter. I denne hensikt bør bindemetallet fortrinnsvis inneholde en vesentlig del kobolt og/eller nikkel. Bindemetallet kan inneholde jern, idet kobolten og/eller nikkelen er delvis erstattet av jern, fortrinnsvis maksimalt i en slik grad at bindemetallfasen ikke mister sitt flatesentrert kubiske og/eller hexa-gonal tettpakkede gitter. Particularly good results have been achieved when the gamma phase makes up 40 ± 5 volume percent. It has been shown that the fS phase should have a face-centered cubic and/or hexagonal close-packed crystal lattice. For this purpose, the bonding metal should preferably contain a significant proportion of cobalt and/or nickel. The binder metal may contain iron, the cobalt and/or nickel being partially replaced by iron, preferably to a maximum extent such that the binder metal phase does not lose its face-centered cubic and/or hexagonal close-packed lattice.
For fagfolk er der ingen spesiell van-skeligheter ved å oppnå ovennevnte smale faseområder ved fremstilling av legeringen, idet legeringen og dennes struktur er de-finert og på velkjent vis avhengig av sint-ringstemperaturen, sintringstiden og det anvendte utgangsmateriale. Fremgangs-måten ved fremstilingen utgjør derfor ikke noen del av foreliggende oppfinnelse. For professionals, there are no particular difficulties in achieving the above-mentioned narrow phase areas when producing the alloy, as the alloy and its structure are defined and in a well-known manner dependent on the sintering temperature, the sintering time and the starting material used. The manufacturing process therefore does not form any part of the present invention.
Foruten det nevnte forhold mellom Besides the aforementioned relationship between
fasene skal legeringen som nevnt ha en kornstruktur som er usedvanlig finkornet ved et slikt faseforhold. Dette er av stor viktighet for å oppnå de ønskede verdifulle egenskaper i forbindelse med legeringens skjæreevne for anvendelse ved bearbeid-ning. Koersitivkraften, som er lett målbar, bør ikke være under 200 og fortrinnsvis ikke under 220 Oersted, i det minste når bindefasen består hovedsakelig av kobolt. Som regel bør kornstørrelsen ha en slik verdi at koersitivkraften er 230—330 Oersted. phases, the alloy must, as mentioned, have a grain structure that is exceptionally fine-grained at such a phase ratio. This is of great importance in order to achieve the desired valuable properties in connection with the alloy's cutting ability for use in processing. The coercive force, which is easily measurable, should not be below 200 and preferably not below 220 Oersted, at least when the binding phase consists mainly of cobalt. As a rule, the grain size should have such a value that the coercive force is 230-330 Oersted.
Det er vel kjent at koersitivkraften er It is well known that the coercive force is
avhengig av kornstørrelsen av carbidkornene i et sintret hårdmetall på en slik måte at en minskning av kornstørrelsen fører til en økning av koersitivkraften og omvendt. Det er derfor mulig å anvende koersitivkraften som mål på kornstørrelsen. Der er visse avvikelser fra denne generelle regel. En stor mengde jern i bindemetallfasen senker koersitivkraften og noen komplekse carbider som eta-fase, hever koersitivkraften. Også nikkel kan gi avvikelse fra nevnte regel. depending on the grain size of the carbide grains in a sintered carbide in such a way that a decrease in grain size leads to an increase in coercive force and vice versa. It is therefore possible to use the coercive force as a measure of the grain size. There are certain deviations from this general rule. A large amount of iron in the bonding metal phase lowers the coercive force and some complex carbides such as eta phase raise the coercive force. Nickel can also cause a deviation from the aforementioned rule.
Foreliggende legering kan få de samme fremragende kvaliteter selv om kobolt helt eller delvis er erstattet av nikkel, eller om kobolt og/eller nikkel er delvis erstattet av jern. Denne erstatning bør som nevnt bare utføres i en slik grad at |3-fasen be-holder sitt flatesentrerte kubiske og/eller hexagonale tettpakkede gitter. Videre bør kornstørrelsen svare til kornstørrelsen av en legering med kobolt eller med kobolt og inntil1 0,5 volumprosent av såvel nikkel som jern som bindemetall, idet sammen-setningen og fasestrukturen i andre hen-seender er den samme, idet sistnevnte legering har en slik kornstørrelse at koersitivkraften er minst 200 og fortrinnsvis minst 220 Oersted. Bestemmelsen av korn-størrelsen i slike legeringer hvori kobolt som ovenfor anført, er helt eller delvis erstattet, kan utføres ved å sammenligne strukturene av legeringene i et lys- eller elektronmikroskop med strukturen av en legering som ovenfor nevnt inneholdende kobolt eller kobolt og maksimalt 0,5 volumprosent av såvel nikkel som jern i bindemetallfasen. The present alloy can obtain the same outstanding qualities even if cobalt is completely or partially replaced by nickel, or if cobalt and/or nickel is partially replaced by iron. As mentioned, this replacement should only be carried out to such an extent that the |3 phase retains its face-centred cubic and/or hexagonal close-packed lattice. Furthermore, the grain size should correspond to the grain size of an alloy with cobalt or with cobalt and up to 1 0.5 volume percent of both nickel and iron as binder metal, the composition and phase structure being the same in other respects, the latter alloy having such a grain size that the coercive force is at least 200 and preferably at least 220 Oersted. The determination of the grain size in such alloys in which cobalt, as stated above, is wholly or partially replaced, can be carried out by comparing the structures of the alloys in a light or electron microscope with the structure of an alloy as mentioned above containing cobalt or cobalt and a maximum of 0, 5 percent by volume of both nickel and iron in the binder metal phase.
For å oppnå de ønskede kvaliteter med To achieve the desired qualities with
hensyn til slitestyrke og seighet bør foreliggende legering som nevnt ovenfor, være usedvanlig finkornet i lys av det relativt høye innhold av gamma-fase. Den gjennomsnittlige kornstørrelse av carbidkornene bør således ligge under 1,6 micron og fortrinnsvis under 1,5 micron. Som en la-vere grense kan nevnes 0,5 micron. Vanligvis bør gjennomsnittskornstørrelsen ligge i området 0,7—1,4 micron. Ved visse meget seige kvaliteter har området 0,8—1,2 micron vist seg særlig fordelaktig. in terms of wear resistance and toughness, the present alloy, as mentioned above, should be exceptionally fine-grained in light of the relatively high content of gamma phase. The average grain size of the carbide grains should thus be below 1.6 microns and preferably below 1.5 microns. As a lower limit, 0.5 micron can be mentioned. Generally, the average grain size should be in the range of 0.7-1.4 micron. For certain very tough qualities, the range 0.8-1.2 micron has proven particularly advantageous.
Den støkiometriske sammensetning av legeringen er selvsagt også viktig for å oppnå de ønskede kvaliteter. Sammenset-ningen bør velges innen de tidligere angitte grenser. Således bør innholdet av WC i volumprosent ligge innen området 60—80 pst. Som regel har det snevrere område 65—70 pst. vist seg særlig egnet. Legeringen bør også Inneholde 10—25, fortrinnsvis 15— 25 volpst. TiC. Legeringen kan videre inneholde opp til 20 volpst. TaC, NbC og/eller VC. Hvis den inneholder bare TaC og/eller NbC bør innholdet av disse legeringsele-menter normalt ikke overstige 15 pst. Legeringen bør fortrinnsvis inneholde en relativt liten mengde, 0,5—10 pst. TaC og/eller NbC. I tillegg hertil kan legeringen inneholde opp til 10 volpst. Cr2C:!, ZrC og/eller HfC og inntil 5 pst. Mo. Molybdenet for-andres i det minste delvis til carbid som Mo;1C2 og MoC under sintringen av legeringen. I denne forbindelse kan nevnes at noe molybden kan danne en fast oppløs-ning i a-fasen, som består av WC. Innholdet av kobolt og/eller nikkel bør maksimalt være 9,5 volpst. De kan som nevnt delvis erstattes av jern, men bare i en slik grad at bindemetallfasen ikke mister sitt flatesentrert kubiske og/eller hexagonale tettpakkede gitter. Jerninnholdet bør maksimalt være 6 volpst.- og totalinnholdet av kobolt og/eller nikkel og jern 9,5 volpst. Vanligvis er jerninnholdet maksimalt 1 eller 0,5 volpst. Innholdet av bindemetall, som helt eller for en vesentlig del består av kobolt og/eller nikkel med eller uten en viss del jern, bør minst være 7,5 og maksimalt 9,5 volpst. Området 8—9 volpst. har vist seg særlig egnet. The stoichiometric composition of the alloy is of course also important to achieve the desired qualities. The composition should be chosen within the previously stated limits. Thus, the content of WC in volume percentage should lie within the range 60-80 per cent. As a rule, the narrower range of 65-70 per cent has proven particularly suitable. The alloy should also contain 10-25, preferably 15-25 volpst. TiC. The alloy can also contain up to 20 volpst. TaC, NbC and/or VC. If it contains only TaC and/or NbC, the content of these alloying elements should not normally exceed 15 per cent. The alloy should preferably contain a relatively small amount, 0.5-10 per cent TaC and/or NbC. In addition to this, the alloy can contain up to 10 volpst. Cr2C:!, ZrC and/or HfC and up to 5 percent Mo. The molybdenum is at least partially converted to carbides such as Mo;1C2 and MoC during the sintering of the alloy. In this connection, it can be mentioned that some molybdenum can form a solid solution in the a-phase, which consists of WC. The content of cobalt and/or nickel should be a maximum of 9.5 volpst. As mentioned, they can be partially replaced by iron, but only to such an extent that the bonding metal phase does not lose its face-centred cubic and/or hexagonal close-packed lattice. The iron content should be a maximum of 6 volps and the total content of cobalt and/or nickel and iron 9.5 volps. Usually the iron content is a maximum of 1 or 0.5 volpst. The content of binder metal, which consists entirely or for a significant part of cobalt and/or nickel with or without a certain amount of iron, should be at least 7.5 and a maximum of 9.5 volpst. The area 8-9 volpst. has proven particularly suitable.
For å oppnå den ovennevnte forbaus-ende forbedring av evnen til å skjære såvel støpejern som stål er det nødvendig at legeringen har den ovenfor angitte sammensetning. Strukturen av legeringen med hensyn til fasesammensetningen og korn-størrelsen er av avgjørende viktighet for resultatet og det er også nødvendig at de ovenfor angitte betingelser i denne hense-ende samtidig oppfylles. In order to achieve the above-mentioned astonishing improvement in the ability to cut both cast iron and steel, it is necessary that the alloy has the above-mentioned composition. The structure of the alloy with regard to the phase composition and the grain size is of decisive importance for the result and it is also necessary that the conditions stated above in this respect are simultaneously fulfilled.
Det følgende viser eksempler på sam-mensetninger og faseforhold i volpst. for to legeringer ifølge oppfinnelsen: The following shows examples of compositions and phase relationships in volpst. for two alloys according to the invention:
I det følgende er gitt noen sammenlig-nende eksempler på arbeidsprøver med en legering ifølge oppfinnelsen og andre legeringer som betraktes som egnet for an-gjeldende formål. I den følgende tabell refererer kolonne A seg til legeringen iføl-ge oppfinnelsen og kolonnene B—G til sammenligningslegeringer. Legeringene B, C, D. og F er eksempler på legeringer som vanligvis anvendes for bearbeidelse av støpejern, mens legering E er beregnet på såkalt universalbearbeidelse, dvs. bearbeidelse såvel av støpejern som stål og legering G er beregnet på bearbeidelse av stål. Legeringssammensetningen og fasemeng-dene er i tabellen angitt i volpst. Det kan pekes på at legeringene C og F er finkor-nede, men har et innhold av gamma-fase som er bare henholdsvis 4 og 2 volpst. In the following, some comparative examples of working samples with an alloy according to the invention and other alloys which are considered suitable for the purpose in question are given. In the following table, column A refers to the alloy according to the invention and columns B—G to comparative alloys. Alloys B, C, D. and F are examples of alloys that are usually used for processing cast iron, while alloy E is intended for so-called universal processing, i.e. processing both cast iron and steel, and alloy G is intended for processing steel. The alloy composition and phase quantities are given in the table in volpst. It can be pointed out that alloys C and F are fine-grained, but have a content of gamma phase which is only 4 and 2 volpst respectively.
Ovenfor sintrede hårdmetallegeringer er blitt prøvet praktisk og sammenlignet. Den efterfølgende rapport fra prøvene inn-befatter eksempler 1—3 som angår bearbeidelse av støpejern og eksempel 4 som angår bearbeidelse av stål. Slitestyrken av legeringene ble bestemt ved å måle slitasjen av sideflaten og toppflaten av skjæret, dvs. faseslitasje og kraterdannelse. Eksemplene viser klart at slitestyrken av legeringene ifølge foreliggende oppfinnelse er over-legne sammenlignet med de andre legeringer som ble prøvet. Above sintered carbide alloys have been tested practically and compared. The subsequent report from the tests includes examples 1-3 which concern the processing of cast iron and example 4 which concerns the processing of steel. The wear resistance of the alloys was determined by measuring the wear of the side surface and the top surface of the cutting, i.e. phase wear and cratering. The examples clearly show that the wear resistance of the alloys according to the present invention are superior compared to the other alloys that were tested.
Eksempel 3. I Eksempel k- I Example 3. I Example k- I
Claims (8)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE2909628A DE2909628C2 (en) | 1979-03-12 | 1979-03-12 | Device for regulating the KATA value |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| NO794210L NO794210L (en) | 1980-09-15 |
| NO153838B true NO153838B (en) | 1986-02-24 |
| NO153838C NO153838C (en) | 1986-06-04 |
Family
ID=6065138
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO794210A NO153838C (en) | 1979-03-12 | 1979-12-20 | DEVICE FOR REGULATION OF THE KATA VALUE. |
Country Status (4)
| Country | Link |
|---|---|
| CH (1) | CH641412A5 (en) |
| DE (1) | DE2909628C2 (en) |
| NO (1) | NO153838C (en) |
| SE (1) | SE439904B (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| IL66297A0 (en) * | 1982-07-12 | 1982-11-30 | Amcor Ltd | Apparatus for improvement of air quality in passenger airplane cabins |
| FR2549602B1 (en) * | 1983-07-18 | 1985-10-04 | Metraflu | CALIBRATION BLOWER FOR CARRYING OUT FLUID MECHANICAL MEASUREMENTS |
| DE3510648C2 (en) * | 1985-03-23 | 1996-04-18 | Vdo Schindling | Device for regulating the interior temperature of a vehicle, in particular a motor vehicle |
| US4836095A (en) * | 1986-12-01 | 1989-06-06 | Carrier Corporation | Static pressure control in variable air volume delivery system |
| IT1310766B1 (en) * | 1999-12-03 | 2002-02-22 | Fiat Auto Spa | AIR SUPPLY GROUP FOR THE INTAKE OF AIR IN THE INTERIOR OF A VEHICLE. |
| FR2834247B1 (en) * | 2001-12-27 | 2004-09-10 | Renault | METHOD FOR AIR CONDITIONING THE INTERIOR OF A MOTOR VEHICLE |
| EP1323555A1 (en) * | 2001-12-27 | 2003-07-02 | Renault s.a.s. | Air conditioning device and method for the passenger compartment of a motor vehicle |
| DE102008031695B4 (en) * | 2008-07-04 | 2012-03-22 | Bayerische Motoren Werke Aktiengesellschaft | Method for air conditioning a vehicle |
| DE102010029367A1 (en) * | 2010-05-27 | 2011-12-01 | Preh Gmbh | Improved air conditioning control |
| JP6012970B2 (en) * | 2012-01-25 | 2016-10-25 | 川崎重工業株式会社 | Vehicle air conditioning ducts and railway vehicles |
| CZ305093B6 (en) * | 2013-06-26 | 2015-04-29 | Technická univerzita v Liberci | Compensation device for proportional pneumatic distributor |
| DE102018203428B3 (en) | 2018-03-07 | 2019-05-09 | Siemens Aktiengesellschaft | Vehicle with a climate arrangement |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE2711816A1 (en) * | 1977-03-18 | 1978-09-21 | Walter Holzer | Temp. control for inside of bus - has electronic sensors for separately controlled outlets receiving air via. duct from pressure region in front of vehicle |
-
1979
- 1979-03-12 DE DE2909628A patent/DE2909628C2/en not_active Expired
- 1979-12-20 NO NO794210A patent/NO153838C/en unknown
-
1980
- 1980-01-25 SE SE8000596A patent/SE439904B/en not_active IP Right Cessation
- 1980-01-26 CH CH61080A patent/CH641412A5/en not_active IP Right Cessation
Also Published As
| Publication number | Publication date |
|---|---|
| CH641412A5 (en) | 1984-02-29 |
| DE2909628C2 (en) | 1984-11-15 |
| DE2909628A1 (en) | 1980-09-25 |
| SE439904B (en) | 1985-07-08 |
| SE8000596L (en) | 1980-09-13 |
| NO153838C (en) | 1986-06-04 |
| NO794210L (en) | 1980-09-15 |
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