DE2018662A1 - Composite material for cutting tools - Google Patents

Composite material for cutting tools

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Publication number
DE2018662A1
DE2018662A1 DE19702018662 DE2018662A DE2018662A1 DE 2018662 A1 DE2018662 A1 DE 2018662A1 DE 19702018662 DE19702018662 DE 19702018662 DE 2018662 A DE2018662 A DE 2018662A DE 2018662 A1 DE2018662 A1 DE 2018662A1
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Prior art keywords
substrate
intermediate layer
carbide
chromium
layer
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DE19702018662
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German (de)
Inventor
Hans Erich Dr. Anet; Gass Hans; Härter Dorothea Dipl.-Ing.; Hänni Werner; NeuchStel; Hintermann (Schweiz)
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Laboratoire Suisse de Recherches Horlogeres, NeuchStel (Schweiz)
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    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C30/00Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C23C30/005Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
    • CCHEMISTRY; METALLURGY
    • C01INORGANIC CHEMISTRY
    • C01BNON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B32/00Carbon; Compounds thereof
    • C01B32/90Carbides
    • CCHEMISTRY; METALLURGY
    • C01INORGANIC CHEMISTRY
    • C01BNON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B32/00Carbon; Compounds thereof
    • C01B32/90Carbides
    • C01B32/907Oxycarbides; Sulfocarbides; Mixture of carbides
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/06Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of metallic material
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/06Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of metallic material
    • C23C16/08Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of metallic material from metal halides
    • C23C16/10Deposition of chromium only
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/06Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of metallic material
    • C23C16/08Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of metallic material from metal halides
    • C23C16/14Deposition of only one other metal element
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/32Carbides
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/38Borides
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/40Oxides
    • C23C16/403Oxides of aluminium, magnesium or beryllium
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C16/00Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/42Silicides
    • CCHEMISTRY; METALLURGY
    • C23COATING 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
    • C23CCOATING 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
    • C23C28/00Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • CCHEMISTRY; METALLURGY
    • C01INORGANIC CHEMISTRY
    • C01PINDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2004/00Particle morphology
    • C01P2004/80Particles consisting of a mixture of two or more inorganic phases
    • CCHEMISTRY; METALLURGY
    • C01INORGANIC CHEMISTRY
    • C01PINDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2006/00Physical properties of inorganic compounds
    • C01P2006/80Compositional purity

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  • Chemical & Material Sciences (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • General Chemical & Material Sciences (AREA)
  • Inorganic Chemistry (AREA)
  • Chemical Vapour Deposition (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Ceramic Products (AREA)

Description

DR.-INQ. UlP-.-l^a. M. «Ο. ΟΙβ^.-ΡΗΥβ. DR. DIPI..PHY».DR.-INQ. UlP -.- l ^ a. M. «Ο. ΟΙβ ^ .- ΡΗΥβ. DR. DIPI..PHY ». HÖGER-STELLRECHT-GRIESSBACH-HAECKERHÖGER-STELLRECHT-GRIESSBACH-HAECKER PATENTANWÄLTE IN STUTTGARTPATENT LAWYERS IN STUTTGART

■λ 38 112 b 2018662■ λ 38 112 b 2018662

13. April 197oApril 13, 197o

Laboratoire Suisse de RecherchesLaboratoire Suisse de Recherches

Horlogeres,
Rue Breguet 2, Neuchatel (Schweiz)
Horlogeres,
Rue Breguet 2, Neuchatel (Switzerland)

Verbundwerkstoff für SchneidwerkzeugeComposite material for cutting tools

009860/1398009860/1398

Vi. V i.

Die heute zur spanabhebenden Bearbeitung verwendeten Schneidewerkstoffe stellen einen Kompromiss zwischen ihrer Verschleissfestigkeit und ihrer Zähigkeit dar. So ist z.B. der äusserst verschlelssfeste Diamant sehr spröde und findet daher nur in Sonderfallen Verwendung. Der heute noch vielfach verwendete ' Schnellsohnittstahl ist zwar relativ zäh, jedoch wenig verschleissfest. Those used today for machining Cutting materials represent a compromise between their wear resistance and their toughness. For example, the extremely wear-resistant diamond is very brittle and therefore only finds use in special cases. The high-speed steel, which is still widely used today, is relatively tough, but not very wear-resistant.

Es ist nun denkbar, ein zähes Material mit einer harten, abriebfesten Schicht zu Überziehen, um dadurch einen Idealen Schneidewerkstoff zu erhalten, der sowohl zäh als auch verschleissfest ist.It is now conceivable to use a tough material with a hard, wear-resistant layer to cover, thereby creating an ideal To obtain cutting material that is both tough and wear-resistant is.

PUr solche abriebfesten Schichten kommen eine Anzahl metallischer und nicht metallischer Hartstoffe in Präge, wie etwa Karbide, Boride, Nitride und Suizide der Uebergangsmetalle der Gruppen K bis 6 des Periodensystems, Diamant, Korund, harte Minerallen, Borkarbid, Siliziumkarbid, kub. Bornitrid und Aluminiumnitrid. In kompakter Form sind diese Stoffe ausserordentlich spröde. Sie lassen sich jedoch zum Teil als dünne Schichten auf geeigneten Trägermaterialien (Substraten) abscheiden und können in dieser Porm sehr duktil sein. Als Beispiel sei die T+tankarbld-Beschichtung von Stahl durch thermochemische Abscheidung aus der Qasphase angeführt. Eine einfache Kombination eines zähen Substrats mit einer sehr harten, nur wenige jum starken Hartstoffschicht, führt jedoch auf arund der stark voneinander abweichenden Eigenschaften von Schicht- und Substratmaterial zu einem Werkstoff, der den hohen Anforderungen, die an einen Schneidewerkstoff gestellt werden, nicht genügt. ■ ■For such abrasion-resistant layers, a number of metallic and non-metallic hard materials are embossed, such as carbides, borides, nitrides and suicides of the transition metals of groups K to 6 of the periodic table, diamond, corundum, hard minerals, boron carbide, silicon carbide, cub. Boron nitride and aluminum nitride. In compact form, these substances are extremely brittle. However, some of them can be deposited as thin layers on suitable carrier materials (substrates) and in this form can be very ductile. An example is the T + tank carbide coating of steel by thermochemical deposition from the Qas phase. A simple combination of a tough substrate with a very hard, only a few inches thick hard material layer, however, due to the widely differing properties of the layer and substrate material, leads to a material that does not meet the high requirements placed on a cutting material. ■ ■

Es wurde nun gefunden, dass wenn man zwischen dem zähen Substrat und der harten Deckschicht mindestens eine Zwischenschicht mit ganz bestimmten Eigenschaften vorsieht, man einen Verbundwerkstoff für Schneidwerkzeuge erhalten kann, der ein Vielfaches der Verschleissfestigkeit der härtesten Hartmetalle aufweist und darüber hinaus mit einer Biegebruchfestigkaife von z.B. mehr als 200 kg/mm2 die Zähigkeit der handelsüblichen SinUrhartot balle erreicht bzw. zum Teil übertrifft.It has now been found that if at least one intermediate layer with very specific properties is provided between the tough substrate and the hard cover layer, a composite material for cutting tools can be obtained that has a multiple of the wear resistance of the hardest hard metals and also has a flexural strength of, for example more than 200 kg / mm 2 the toughness of the commercially available SinUrhartot balls is reached or partly exceeded.

008850/1398008850/1398

Der erflndungsgemässe Verbundwerkstoff ist gekennzeichnet durch ein metallisches oder nichtmetallisches Substrat, mindestens eine Zwischenschicht und eine verschlelssfeste Deckschicht, wobei die Zwischenschicht folgende Eigenschaften aufweistιThe composite material according to the invention is marked by a metallic or non-metallic substrate, at least one intermediate layer and a wear-resistant cover layer, the intermediate layer having the following properties

a) ihre Harte liegt zwischen derjenigen des Substrats und derjenigen der Deckschicht,a) their hardness lies between that of the substrate and that of the top layer,

b) sie ist duktiler als die Deckschicht,b) it is more ductile than the top layer,

c) ihr thermischer Ausdehnungskoeffizient liegt zwisohen demjenigen des Substrats und demjenigen der Deckschicht,c) their coefficient of thermal expansion is between that of the substrate and that of the top layer,

d) sie ist sowohl im Substrat wie in der Deckschicht teilweise gelöst,d) it is partially dissolved both in the substrate and in the top layer,

e) ihr Schmelzpunkt 1st höher als die zum Aufbringen der Deckschicht notwendigen Temperaturen,e) their melting point is higher than that for application temperatures necessary for the surface layer,

fJ die mittlere Korngröase 1st wesentlich kleiner als die Schichtdicke.The mean grain size is much smaller than the layer thickness.

Der Zwischenschicht und ihren Eigenschaften kommt also die wesentliche Bedeutung der vorliegenden Erfindung zu. Dank den erwähnten Eigenschaften 1st sie so abgestimmt, dass ein stufenweiser Uebergang zwischen Substrat und Deckschicht gewährleistet ist. .So comes the intermediate layer and its properties the essential importance of the present invention. Thanks to the The properties mentioned above are coordinated in such a way that a gradual transition between substrate and top layer is ensured is. .

Je feiner die Abstufung zwisohen mehreren Zwischenschichten ist, desto besser lassen sich Substrat und Deckschicht miteinander verbinden. Oft genügen jedoch schon eine bis zwei Zwischenschichten. Dies gilt besondere für Diffusionsschiohten.The finer the gradation between several intermediate layers is, the better the substrate and top layer can be combined with one another associate. Often, however, one or two intermediate layers are sufficient. This is especially true for diffusion layers.

Man kann zweckmKssig z.B. eine carbldhaltlge Deckschicht erzeugen und dabei als Kohlenstoffquelle gegebenenfalls substituierte aliphatisch^, aromatische, cycloaliphatische oder heterocyclische Kohlenwasserstoffe verwenden. Sehr geeignet sind z.B. Nethan oder Dioyclopentadien.
Beispiele
One can expediently produce, for example, a carbide-containing top layer and use optionally substituted aliphatic, aromatic, cycloaliphatic or heterocyclic hydrocarbons as the carbon source. Nethane or dioyclopentadiene, for example, are very suitable.
Examples

1. Bin ledeburitisoher Chromstahl liegt in Form quadratischer SohneideplMt tonen vor. Br wird in ein Pulvergemisch bestehend aus einer inerten keramischen Nasse, Chrom und Ammoniumohlorid eingepackt und auf 90O0C aufceheizt. Eb bildet sich Chromchlorid, welches Über die Oasphase transportiert und an der Ober-1. Chromium steel, made from ledeburitis, is in the form of square sonic plates. Br is packed in a powder mixture consisting of an inert ceramic Wet, chromium and Ammoniumohlorid and aufceheizt to 90O 0 C. Eb forms of chromium chloride, which transported over the Oasphase and at the top

009850/1398009850/1398

fläche der Stahlteile zersetzt wird. Das abgeschiedene Chrom wird teilweise in die Oberfläche eindiffundiert und bildet dort zusammen mit dem Kohlenstoff des arundmaterlals eine 5 um starke« harte« mit Cnpoaoarhlden angereicherte Schicht· Die darüberliegende Chroneohioht beträgt 1 bis 2 /im. Die so behandelten Teile werden in einem Oae-Gemisoh aus 96 VoI* H2 + 2 VoI* CH^ ♦ 2 VoI* TiCl4 bei 900°C und einem Druck von 20 Torr mit einer 6 um dicken TiC-Sohloht Überzogen. Hierbei bildet sich eine Uebergangsone« in der das Chrom duroh Diffusion des Kohlenstoffes teilweise in Chromoarbld umgewandelt wird. Das so vergütete Sohneldeplättohen kann ohne Nachbearbeitung eingesetzt werden. Es werden bein Feindrehen von Messing MS 58 und 1 * C-Stahl 5-bls 20-fache Standzeiterhuhungen erreicht.surface of the steel parts is decomposed. The deposited chromium is partially diffused into the surface and forms, together with the carbon of the base material, a 5 .mu.m thick "hard" layer enriched with carbon halides. The overlying chromium is 1 to 2 / µm. The parts treated in this way are coated in an Oae-Gemisoh of 96 VolI * H 2 + 2 VolI * CH ^ ♦ 2 VolI * TiCl 4 at 900 ° C and a pressure of 20 Torr with a 6 µm thick TiC-sole. Here a transition zone is formed in which the chromium is partially converted into chromium by diffusion of the carbon. The so-remunerated Sohneldeplättohen can be used without post-processing. With fine turning of brass MS 58 and 1 * C-steel 5-to-20-fold increases in service life are achieved.

2. Sin Hartmetailachneldeplättohen bestehend aus den Karbiden WC« TiC« NbC oder VC und Co als Binder wird in einem Oas« gemlsoh aus 97 VoI* IL, + <- VoI* CH4 + 1 VoI* CrCU auf 102O0C erhitzt. Nach Abscheidung einer Chrom + ChromoarbidschiGht von 1 bis 2 um Dicke werden dem Qa* 2 VoI* TiCl^ zugenisoht und der Druck auf 10 Torr reduziert. Nach h h hat sich eine 3 bis 4 um dicke« schwach ohroracarbidhaltlge Tltankarbldeohloht gebildet. Diese 1st härter als das reine Titankarbid. Durch die befichrleranen Mausenahmen konnte aueserdmn an der ursprunglichen Hartmetalloberflache eine Härtesteigerung erzielt werden» indem durch Heaktion dee Kobaltbindera mit den Carbiden ternäre Legierungen des Typs W5Co3C gebildet wurden.2. Sin Hartmetailachneldeplättohen consisting of the carbides WC "TiC" NbC or VC and Co as a binder is in a Oas "gemlsoh 97 VoI * IL, + <- heated VoI * CH 4 + 1 * VoI CrCu at 102O 0 C. After a chromium + chromium carbide layer 1 to 2 μm thick has been deposited, 2% TiCl ^ are added to the Qa * and the pressure is reduced to 10 Torr. After h h a 3 to 4 micron thick "weak ohroracarbidhaltlge Tltankarbldeohloht has formed. This is harder than pure titanium carbide. Through the use of the mouse, it was possible to increase the hardness of the original hard metal surface by forming ternary alloys of the W 5 Co 3 C type with the carbides.

Beim Drehen gegen einen Stahl der Werkstoff Nr. QiOCWl wurde mit de» unoehandelten Hartmetallplättohen nach 12 min ein Abrieb von 0«2 mm und damit die Obergrenze des susutbaren Versohleissee erreicht. An einem vergüteten Plättohen wurde dagegen unter glelohen Schnlttbedlngungen nach 30 Bin ein Abrieb von nur 0,005 bsi nachgewiesen.When turning against a steel, the material no. QiOCWl was treated with the untreated hard metal plates after 12 minutes Abrasion of 0 «2 mm and thus the upper limit of the susceptible insole achieved. On a remunerated platoon, however, was under smooth cutting conditions after 30 am an abrasion of only 0.005 bsi detected.

Weitere Beispiel® für Kooblnatlomn, die durch geeignet« ZwlaohensohJ ^,ehten ähnlich» Qu&lltfteverbeseerungsn bringeniFurther Example® for Kooblnatlomn, which by suitable « ZwlaohensohJ ^, similar to "bring quality enhancements"

009850/139 8009850/139 8

S-S-

Matrixmatrix ZwischenschichtenIntermediate layers Fe-Silizide
-.
Fe-Silicides
-.
DeckschichtTop layer
NIMONIC
(z.B. 80 % Nl +
20 % Cr)
NIMONIC
(e.g. 80 % Nl +
20 % Cr)
T
t Ni,Al j NiAl
1 j
T
t Ni, Al j NiAl
1 y
ZrB2 ZrB 2
STELLIT
(z.B. 20JiCr, 15# W,
5i#Co, ca. 10 # Nl,
1,4 % Mn, 1,7JiPe)
STELLITE
(e.g. 20JiCr, 15 # W,
5i # Co, approx. 10 # Nl,
1.4 % Mn, 1.7JiPe)
-
Cr-Carbide
-
Cr carbides
ZrCZrC
Cr-Mo-C-Stahl
mit 33 % TiC
" I
Cr-Mo-C steel
with 33 % TiC
"I.
i
I Mo j MbC
i
I Mo j MbC
B4CB 4 C
Stahl lufthXrtend j B
ι
Steel air supply j B
ι
TiB2 TiB 2
Schnelldrehstahl j
S 10-4-3-iO i
High speed steel j
S 10-4-3-ok ok
ZrB2 ZrB 2
Cermet
(Cr-Borid mit !
Cr-Mo-Binder)
Cermet
(Cr boride with!
Cr-Mo binder)
B4CB 4 C

Beispiel 9Example 9

Ein Schneidplättchen bestehend im wesentlichen aus Al2C und Ni als Binder wird in Wasserstoff auf 900°C aufgeheizt. Nach Zudosieren von 0,5 VoI % CrCl, und 0,2 VoI % Dicyclopentadien in gasförmigem Zustand wird der Totaldruok auf 15 Torr reduziert. Naoh 30 min wird die Temperatur auf 8500C erniedrigt und als weiteres Realttlonsgas 2 VoI % TiCl4 zudosiert. Naoh weiteren 60 min werden die Reaktionsgase durch Argon ersetzt und die Probe auf Raumtemperatur abgekühlt. Auf dem Schneidplättchen hat sich eine 1 bis 2 pm dioke Chromkarbldsohioht und darauf eine 8 bis 10 um dicke Chromkarbid-dotierte Tltankarbidsohloht gebildet.A cutting tip consisting essentially of Al 2 C and Ni as a binder is heated to 900 ° C. in hydrogen. After adding 0.5 % by volume of CrCl and 0.2 % by volume of dicyclopentadiene in the gaseous state, the total pressure is reduced to 15 Torr. NaOH for 30 min the temperature to 850 0 C is added as a further lowered and Realttlonsgas 2% by volume of TiCl 4. After a further 60 minutes, the reaction gases are replaced by argon and the sample is cooled to room temperature. On the cutting tip has a 1 to 2 pm dioke Chromkarbldsohioht formed thereon and an 8 to 10 micron thick doped chromium carbide Tltankarbidsohloht.

Bei der Zerspannung von Stahlguss wies der naoh dem beschriebenen Verfahren hergestellte Verbundwerkstoff die 6 bis 10-fach· Standzeit der Üblicherweise für Stahlguss verwendetenWhen machining cast steel, the naoh pointed out the described Process produced composite material 6 to 10 times the service life of that usually used for cast steel

Sohneldaaterlallen auf.Sohneldaaterlallen on.

00 9850/139800 9850/1398

2018 G 6 22018 G 6 2

Erflndungcgemäsa können folgende Vorteile erhalten werden:According to the invention, the following advantages can be obtained will:

- Hohe Zähigkeit bei geringes Versohleiss, dadurch höhere Standzelten der Werkzeugej höhere Schnittgeschwindigkeiten verbunden mit Produktionast©igerung.- High toughness with low insole, therefore higher Stand tents of the toolsj higher cutting speeds associated with production branch.

- Möglichkeiten zur Verwendung von z.T. billigen und leicht zu bearbeitenden Substratmaterialien mit hoher Zähigkeit, die bis heute wegen mangelnder Veraohleissfestigkeit als Schneidewerkstoffe nicht in Frage kamen, wie nahezu alle härtbaren Stähle , verschiedene Nickel-. Kupfer-, Titan-, Kobalt- und Alumlnium-- Possibilities for the use of partly cheap and easy to work substrate materials with high toughness, which are still used today as cutting materials because of their lack of resistance to cracking out of the question, like almost all hardenable steels, various nickel-. Copper, titanium, cobalt and aluminum

P legierungen, Hartmetalleorten, die sich in Sohneid·versuch als zu weich erwiesen, keramische Sinterwerkstoffe mit grossem Binderanteil. P alloys, hard metal grades, which in son · attempt as to Proven to be soft, ceramic sintered materials with a large proportion of binder.

- Verbesserungen der Versöhleissfestigkeit der handelsüblichen Schneidewerkstoffe un das 2 bis 20 fache bei Beibehaltung ihrer Zähigkeit.- Improvements in the reconciliation resistance of the commercial ones Cutting materials un 2 to 20 times while maintaining their toughness.

- Werkstoffe, die sehr schwierig zu bearbeiten sind, werden durch das vorliegend· Sohneidematerial der spanabhebenden Formgebung zugänglich ge«acht.- Materials that are very difficult to work with are replaced by the material to be machined Design accessible.

Di· beiliegende Zeichnung ««igt die Abhängigkeit der Härte von der Biegefestigkeit ftlr verschiedene Schneidewerketoffe. _ Di· Biegebruchfestigkeit nimmt wesentlich Einfluss auf die Zähig- keit; die Härte steht in engen Zusammenhang mit der Versohleissfestigkeit des Werkstoffes. Der Bereich A bezieht sich auf bekannte Sehneldmaterlallen, wie Sonderhartmetalle 1, Schneidkeramik 2, Sinterhartmetall· jj und Sohnelldrehatähle 4. Der Bereich B bezieht sich auf die neuen Verbündwerkstoffe.The accompanying drawing shows the dependence of hardness on flexural strength for various cutting materials. _ The · bending strength has a significant influence on the toughness ; the hardness is closely related to the insole resistance of the material. Area A relates to known sehneldmaterlallen, such as special hard metals 1, cutting ceramics 2, sintered carbide · jj and Sohnell lathe tools 4. Area B relates to the new composite materials.

0098 50/ 13 980098 50/13 98

Claims (1)

2 01 8 β 6 22 01 8 β 6 2 AN3PRUECHE 1. Verbundwerkstoff fur Sohneidwerkzeuge, gekennzeichnet durch ein metallisches oder nicht metallisches Substrat» mindesten« eine Zwischenschicht und eine verschleißfeste Deckschicht, wobei die Zwischenschicht folgende Eigenschaften aufweist:1. Composite material for sons tools, characterized by a metallic or non-metallic substrate "at least" an intermediate layer and a wear-resistant top layer, the intermediate layer having the following properties: a) ihre Härte liegt zwischen derjenigen des Substrats und derjenigen der Deckschicht»a) their hardness is between that of the substrate and that of the top layer » b) sie ist duktiler als die Deckschicht«b) it is more ductile than the top layer " c) ihr thermischer Ausdehnungskoeffizient liegt zwischen demjenigen des Substrats und desjenigen der Deckschicht,c) their coefficient of thermal expansion is between that of the substrate and that of the top layer, d) sie ist sowohl la Substrat wie in der Deckschicht teilweise gelöst,d) it is both la substrate and in the top layer partially solved, e) ihr Schmelzpunkt ist. höher als die zu« Aufbringen der Deckschicht notwendigen Temperaturen,e) is their melting point. higher than that to «muster temperatures necessary for the surface layer, f) die mittlere Korngrösse ist wesentlich kleiner als die Schichtdicke.f) the mean grain size is much smaller than the layer thickness. 2. Werkstoff nach Anspruch 1, gekennzeichnet durch ein Substrat aus ledeburltisohem Chromstahl, eine Zwischenschicht aus Chrom und eine Deckschicht aus Titanoarbid, wobei in den aneinander grenzenden Bereichen des Substrats, der Zwischenschicht und der Deckschicht Chromoarbid enthalten 1st.2. Material according to claim 1, characterized by a Substrate made of chrome steel, an intermediate layer Chromium and a top layer of titanium carbide, being in the one another Adjacent areas of the substrate, the intermediate layer and the top layer contain chromo carbide. 3. Werkstoff nach Anspruch 1, gekennzeichnet durch ein Substrat aus Wolfram-, Titan-, Niob- und/oder Vanadiumoarbid mit einem Cobaltbinder, eine Zwischenschicht aus Chrom und eine Deckschicht aus Titanoarbid, wobei in den aneinander grenzenden Bereichen des Substrats, der Zwischenschicht, und der Deckschicht Chromoarbid enthalten ist.3. Material according to claim 1, characterized by a Substrate made of tungsten, titanium, niobium and / or vanadium carbide with a cobalt binder, an intermediate layer made of chromium and a cover layer made of titanium carbide, in the adjoining areas of the substrate, the intermediate layer and the cover layer Chromoarbide is included. A. Werkstoff nach Anspruch 1, gekennzeichnet durch ein Substrat aus einer Legierung von 80 % Nl und 20 % Cr, eine erste Zwischenschicht aus Ni,Al, eine zweite Zwischenschicht aus NiAl und eine Deckschicht aus 2 A. Material according to claim 1, characterized by a substrate made of an alloy of 80 % Ni and 20 % Cr, a first intermediate layer made of Ni, Al, a second intermediate layer made of NiAl and a cover layer made of 2 5. Werkstoff nach Anspruch 1, gekennzeichnet durch ein Substrat aus 20 % Cr, 15 % W, 51 % Co, ca. 10 % Nl4 1,4 % Mn, 1,7 * Fe, tine Zwischenschicht aus Chromoarblden und eine5. Material according to claim 1, characterized by a substrate made of 20 % Cr, 15 % W, 51 % Co, approx. 10 % Nl 4 1.4 % Mn, 1.7 * Fe, tine intermediate layer made of chromium blades and one 009850/1398009850/1398 2018R622018R62 Deoksohioht «us Zirkonoarbid.Deoxohioht "from zirconium carbide. 6. Werkstoff naoh Anapruoh 1, gekennzeichnet durch ein Substrat aus «inen härtbaren Stahl mit bis zu 50 % TiC, eine erste Zwlscheniohioht aus Molybdän, eine zweite Zwischenschicht aus Molybdäncarbid und eine Deckschicht aus Borcarbid der Formel B^C.6. Material naoh Anapruoh 1, characterized by a substrate made of hardenable steel with up to 50 % TiC, a first intermediate layer made of molybdenum, a second intermediate layer made of molybdenum carbide and a top layer made of boron carbide of the formula B ^ C. 7. Werkstoff naoh Anspruch 1« gekennzeichnet durch ein Substrat aus einem lufthärtenden Stahl, eine Zwischenschicht aus Bor und eine Deckschicht aus Tltanborid der Formel TiB2*7. Material naoh claim 1 «characterized by a substrate made of an air-hardening steel, an intermediate layer made of boron and a top layer made of titanium boride of the formula TiB 2 * 8. Werkstoff naoh Anspruch 1, gekennzeichnet duroh ein Substrat aus einem Sohnelldrehstahl, eine Zwischenschicht aus Bisensllloiden und eine Deoksohloht aus Zlrkonborid der Formel ZrB2.8. Material naoh claim 1, characterized duroh a substrate made of a sonic turning steel, an intermediate layer made of bisensilloids and a deoxa made of Zlrkonborid of the formula ZrB 2 . 9. Werkstoff naoh Anspruch 1, gekennzeichnet duroh ein Substrat aus einem metallkeramisohen Cr-Borid mit Cr-Mo-Binder, eine Zwischenschicht aus Zirkonborid der Formel ZrBg und eine Deckschicht aus Borcarbid der Formel B^C.9. Material naoh claim 1, characterized duroh a substrate made of a Metallkeramisohen Cr boride with Cr-Mo binder, an intermediate layer of zirconium boride of the formula ZrBg and one Top layer made of boron carbide of the formula B ^ C. 10. Werkstoff naoh Anspruch 1« gekennzeichnet duroh ein Substrat aus einem haftbaren Stahl mit bis zu 50 % TiC, einer Zwischenschicht aus Chrom und einer Deoksohloht aus Titanoarbid, wobei in den aneinander grenzenden Berelohen des Substrats, der Zwischenschicht und der Deoksohioht Chromoarbid enthalten ist.10. Material naoh claim 1 «characterized duroh a substrate made of an adhesive steel with up to 50 % TiC, an intermediate layer of chromium and a Deoksohloht made of titanium carbide, wherein in the adjoining Berelohen of the substrate, the intermediate layer and the Deoksohioht chromoarbide is included. 11. Verfahren zur Herstellung eine· Verbundwerk^stoffe naoh den Ansprüche 1-10, dadurch gekennzeichnet, dass man auf dem Substrat das Zwlsohensohlohtmaterlal duroh chemieοhe Reaktion aus der Gasphase abscheidet, wobei Substratmaterial und Zwleohensohlohtmaterial ineinander diffundieren, und dass man die Deokaohioht duroh chemische Reaktion aus der Qaephase auf der Zwischenschicht abscheidet, wobei Deckschiohtmaterial und Zwlsohensohlohtmaterlal Ineinander diffundieren.11. Process for the production of a composite material naoh the claims 1-10, characterized in that the Zwlsohensohlohtmaterlal duroh chemical reaction on the substrate the gas phase is deposited, whereby substrate material and Zwleohensohlohtmaterial diffuse into each other, and that one deokaohioht duroh chemical reaction from the Qaephase on the Interlayer deposited, with cover layer material and Diffuse evenly into one another. 12. Verfahren naoh Anspruch 11, dadurch gekennzeichnet, dass man «Ine carbidhaltige Deckschicht erzeugt und dabei als Kohlenstofff^quelle gegebenenfalls substituierte eliphatisohe, aromatische, cycloaliphatische oder heterocyclische Kohlenwasserstoffe verwendet.12. The method according to claim 11, characterized in that that «Ine carbide-containing top layer is produced and thereby as Carbon source optionally substituted eliphatic, aromatic, cycloaliphatic or heterocyclic hydrocarbons used. 009850/1398009850/1398 15. Verfahren nach Anspruch 12, dadurch gekennzeichnet/ dass man als Kohlenstoffquelle Methan verwendet.15. The method according to claim 12, characterized in / that methane is used as a carbon source. 14. Verfahren nach Anspruch 12, dadurch gekennzeichnet« dass man als Kohlenstoffquelle Dicyclopentadien verwendet.14. The method according to claim 12, characterized in that « that dicyclopentadiene is used as a carbon source. 15. Verfahren nach Anspruch 11, zur Herstellung des Werkstoffs nach Anspruch 2, dadurch gekennzeichnet» dass man Sehneideplättchen aus ledeburitischem Chromstahl in ein Pulvergemisch aus einer inerten keramischen Masse, Chrom und Ammoniumchlorid taucht, das Gemisch auf 9000C erhitzt, wobei gasförmiges Chromohlorid an der Oberfläche der Plättchen zersetzt wird und sich eine Chromschicht bildet, die teilweise in die Plättchenoberfläche eindiffundiert und Chromcarbld enthält, und dass man diese Zwischenschicht durch Reaktion In der Gasphase mit einem Gemisch von Wasserstoff, Methan und TiCl^ bei 90O0C und 20 Torr mit Titanoarbid Überzieht, wobei Chrom und Titancarbid teilweise ineinander diffundieren und Chromcarbld gebildet wird.15. The method according to claim 11, for the preparation of the material according to claim 2, characterized in 'that Sehneideplättchen from ledeburitic chrome steel in a powder mixture of an inert ceramic material, chromium and ammonium chloride appeared, the mixture heated to 900 0 C, whereby gaseous Chromohlorid to the surface of the platelets is decomposed and a chromium layer is formed, which partially diffuses into the platelet surface and contains chromium carbide, and that this intermediate layer can be obtained by reaction in the gas phase with a mixture of hydrogen, methane and TiCl ^ at 90O 0 C and 20 Torr Titanium carbide Coating, whereby chromium and titanium carbide partially diffuse into one another and chromium carbide is formed. 16. Verfahren nach Anspruch 11, zur Herstellung des Werkstoffs naoh Anspruch 3, dadurch gekennzeichnet, dass man ein Substrat aus Wolfram-, Titan-, Niob- oder Vanadiumcarbid mit einen Cobaltbinder durch Reaktion mit eines Gasgemisches aus Wasserstoff Methan und CrCl, bei 10200C Bit einer Chromschicht überzieht, wobei Chrom teilweise in die Substratoberfläche diffundiert und Chromcarbid bildet, und dass man anschliessend im Gasgemisch das CrCl. teilweise durch TiCl^ ersetzt und auf der Zwischenschicht bei 20 Torr eine mit Chromcarbid dotierte Titancarbidschicht bildet. 16. The method according to claim 11, for the production of the material naoh claim 3, characterized in that a substrate made of tungsten, titanium, niobium or vanadium carbide with a cobalt binder by reaction with a gas mixture of hydrogen, methane and CrCl, at 1020 0 C bit is coated with a chromium layer, with chromium partially diffusing into the substrate surface and forming chromium carbide, and then the CrCl. partially replaced by TiCl ^ and forms a titanium carbide layer doped with chromium carbide on the intermediate layer at 20 Torr. 17. Verfahren nach Anspruch 11, zur Herstellung eines Werkstoffs naoh Anspruch 10, dadurch gekennzeichnet, dass man ein Schneidplättchen, das im wesentlichen aus Al2O, mit Ni als Binder besteht, in Wasserstoff auf 90O0C heizt, naoh Zugabe von gasförmigem CrCl, und Dioyolopentadien den Druok auf etwa 16 Torr reduziert und Chroacarbid als Zwischenschicht abscheidet, und sodann naoh Zugabe von gasförmige« TiCI4 eine alt Chroaoarbid dotiert« Deckschicht aus Titanoarbid bildet.17. The method according to claim 11, for the production of a material according to claim 10, characterized in that a cutting tip, which consists essentially of Al 2 O, with Ni as a binder, is heated in hydrogen to 90O 0 C, after addition of gaseous CrCl , and dioyolopentadiene reduces the Druok to about 16 Torr and deposits chroacarbide as an intermediate layer, and then, after adding gaseous "TiCl4", forms an old chroaoarbide-doped top layer of titanium carbide. 009850/1398009850/1398 LeerseiteBlank page
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DE2225135A1 (en) * 1971-05-26 1972-11-30 Gen Electric Coated cemented carbide
DE2233700A1 (en) * 1971-07-07 1973-01-25 Battelle Memorial Institute PROCESS FOR INCREASING THE ABRASION RESISTANCE OF THE SURFACE OF CUTTING TOOLS ETC. CARBIDE PARTS
DE2253745A1 (en) * 1971-11-12 1973-05-17 Sandvik Ab CARBIDE BODY
DE2317447A1 (en) * 1973-04-06 1974-10-24 Sandvik Ab Coating carbide cutting tools with oxides - by pretreating carbide surface to prevent binder or carbon diffusion into oxide
DE2625940A1 (en) * 1975-06-12 1976-12-23 Gen Electric PROCESS FOR COATING CARBIDE PRODUCTS
EP0018432A1 (en) * 1979-05-04 1980-11-12 GebràœDer Sulzer Aktiengesellschaft Metallic article provided with a wear and corrosion resistant protective coating of tungsten carbide
USRE32110E (en) * 1971-05-26 1986-04-15 General Electric Co. Aluminum oxide coated cemented carbide product
US7264883B2 (en) 2002-12-27 2007-09-04 Kobe Steel, Ltd. Hard coating film excellent in adhesion and manufacturing method thereof

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AT336905B (en) * 1975-02-10 1977-06-10 Plansee Metallwerk WEAR PART FOR CHIPPING AND CHANDELESS FORMING
DE2525185C3 (en) * 1975-06-06 1986-04-17 Fried. Krupp Gmbh, 4300 Essen Hard metal body
FR2447612A1 (en) * 1979-01-26 1980-08-22 Thomson Csf HETEROJUNCTION SEMICONDUCTOR COMPONENT
US4517217A (en) * 1980-09-09 1985-05-14 Westinghouse Electric Corp. Protective coating means for articles such as gold-plated jewelry and wristwatch components
US4610931A (en) * 1981-03-27 1986-09-09 Kennametal Inc. Preferentially binder enriched cemented carbide bodies and method of manufacture
USRE34180E (en) * 1981-03-27 1993-02-16 Kennametal Inc. Preferentially binder enriched cemented carbide bodies and method of manufacture
US5073411A (en) * 1981-12-16 1991-12-17 Carboloy, Inc. Process for forming a surface oxidized binding layer on hard substrates
US4490191A (en) * 1981-12-16 1984-12-25 General Electric Company Coated product and process
DE3318999A1 (en) * 1983-05-25 1984-11-29 M.A.N. Maschinenfabrik Augsburg-Nürnberg AG, 8000 München COATED METAL OBJECT AND METHOD FOR THE PRODUCTION THEREOF
US4594294A (en) * 1983-09-23 1986-06-10 Energy Conversion Devices, Inc. Multilayer coating including disordered, wear resistant boron carbon external coating
DE3515919A1 (en) * 1985-05-03 1986-11-06 Fried. Krupp Gmbh, 4300 Essen WEAR-RESISTANT COATED HARD METAL BODY AND METHOD FOR THE PRODUCTION THEREOF
US5879823A (en) * 1995-12-12 1999-03-09 Kennametal Inc. Coated cutting tool
GB2308133B (en) * 1995-12-13 2000-06-21 Kennametal Inc Cutting tool for machining titanium and titanium alloys
US5984593A (en) * 1997-03-12 1999-11-16 Kennametal Inc. Cutting insert for milling titanium and titanium alloys
DE10109523A1 (en) * 2001-02-28 2002-09-05 Ceram Tec Ag Innovative Cerami Component used for processing workpieces has hard material coating comprising intermediate layer between layers
US6589602B2 (en) 2001-04-17 2003-07-08 Toshiba Tungaloy Co., Ltd. Highly adhesive surface-coated cemented carbide and method for producing the same
CN112846259B (en) * 2021-01-05 2022-09-30 崇义章源钨业股份有限公司 Cutter for steel turning and preparation method thereof

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DE2225135A1 (en) * 1971-05-26 1972-11-30 Gen Electric Coated cemented carbide
DE2265603C2 (en) * 1971-05-26 1983-02-03 General Electric Co., Schenectady, N.Y. Cutting insert with a non-metallic intermediate layer between the base body and the top coating and method for its manufacture
USRE32110E (en) * 1971-05-26 1986-04-15 General Electric Co. Aluminum oxide coated cemented carbide product
DE2233700A1 (en) * 1971-07-07 1973-01-25 Battelle Memorial Institute PROCESS FOR INCREASING THE ABRASION RESISTANCE OF THE SURFACE OF CUTTING TOOLS ETC. CARBIDE PARTS
DE2253745A1 (en) * 1971-11-12 1973-05-17 Sandvik Ab CARBIDE BODY
DE2317447A1 (en) * 1973-04-06 1974-10-24 Sandvik Ab Coating carbide cutting tools with oxides - by pretreating carbide surface to prevent binder or carbon diffusion into oxide
DE2625940A1 (en) * 1975-06-12 1976-12-23 Gen Electric PROCESS FOR COATING CARBIDE PRODUCTS
EP0018432A1 (en) * 1979-05-04 1980-11-12 GebràœDer Sulzer Aktiengesellschaft Metallic article provided with a wear and corrosion resistant protective coating of tungsten carbide
US7264883B2 (en) 2002-12-27 2007-09-04 Kobe Steel, Ltd. Hard coating film excellent in adhesion and manufacturing method thereof
DE10360482B4 (en) * 2002-12-27 2014-07-31 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel Co., Ltd.) Hard coating with excellent adhesion
DE10362382B3 (en) * 2002-12-27 2017-08-17 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel Co., Ltd.) Hard coating with excellent adhesion

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GB1284030A (en) 1972-08-02
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FR2045776B1 (en) 1974-06-14

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