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    • 专利摘要:

    公开号:SE0850068A1
    申请号:SE0850068
    申请日:2008-11-06
    公开日:2010-05-07
    发明作者:Odd Sandberg
    申请人:Uddeholm Tooling Ab；
    IPC主号:
    专利说明:

    15 20 25 30 35 2 (36) the components, s.k. "Galling", which makes it necessary to carry out regular maintenance in the form of grinding, repair welding or valve replacement.
    A steel alloy for the construction of a sealing surface in a valve is defined by its: 0 Manufacturability 0 Compatibility in the valve structure 0 Friction value 0 Bile behavior 0 Resistance to abrasion 0 Ductility / toughness 0 Temperature stability 0 Resistance to corrosion 0 Resistance to indentation (ie hardness) 0 Cuttability, abrasiveness and polishability 0 Radiation activity.
    In valves for the nuclear power industry, for example, the Stellite 6 alloy (trademark of Deloro Stellite Company) has largely become the standard material for abrasion-resistant materials. Stellite 6 is a Co-Cr alloy with 1.3% C, 1.1% Si, 0.1% Mn, 30% Cr, 2.3% Ni, 0.1% Mo, 4.7% W, 2.3% Fe and Residue Co. Stellite 6 is applied to the support by manual metal arc welding, forming a dendritic austenitic Co matrix with a high volume fraction of chromium carbides, which are unevenly distributed in the matrix. The application of Stellite 6 by welding can from the outset or during operation cause macroscopic cracking in the sealing surfaces due to the stresses that arise during the welding process or during operation. This results in leakage and reduced stability against cutting, which leads to an increased need for costly maintenance in an environment with strict safety requirements. A more optimal welding is the use of laser welding or plasma welding using powder of Stellite 6, whereby cracks and defects can be minimized.
    It has been found that the coefficient of friction of Stellite alloys varies depending on the temperature and pressure during operation. At lower operating temperatures, ~ 20 ° C, and lower pressures, <60 MPa, the coefficient of friction is quite high, ~ 0.55-0.60, while at high pressures, above about 100-200 MPa, and at operating temperatures above about 50- At 80 ° C, the coefficient of friction is significantly lower, ~ 0.25. This has been explained as such that in a first step, under heavy load, a deformation hardening of Stellite 6 takes place and a phase conversion is obtained from surface-centered cubic (FFC) crystal structure, which gives high friction, to hexagonal tightly packed 10 15 20 25 3 (36) ( HCP) crystal structure, and in a second step a rearrangement takes place at the surface, so that some HCP base planes become parallel to the surface and thereby create a structure in which shear easily occurs. At lower pressures, this second step does not occur.
    Stellite 6 is in many respects an excellent material, but it helps to increase the level of background radiation in the primary circuit in boiling water reactors. This is because abrasion and corrosion release ions of the isotope 59Co, which are activated by neutron capture as it circulates through the primary circuit to the radioactive isotope 60Co, which emits harmful gamma radiation when it decays to 59Co. Due to this disadvantage, attempts have been made in recent decades to develop a Co-free alloy, which has good resistance to abrasion and corrosion and is therefore suitable for use in radioactive environments.
    Such Co-free alloys are described in e.g. US 4,803,045, can be applied by welding and has the following composition in% by weight: C Mn Si Cr Ni Mo N Nb Ti Ta Fe 5-13 18-27 4-12 <6 balance 0, s5-1.4 1 , 5-5,5 0,1-o, 3 <1 <1 <1 The alloys have a microstructure which mainly consists of an austenitic matrix and eutectic alloy carbides.
    A further development of these weldable Co-free hard welded alloys is described in US 5,702,668 and has the following composition in% by weight: C Mn Si Cr Ni Mo NPSB Fe 1.1-1.35 4-5 3-3.5 22.5 -26 3.7-4.2 1.8-2.2 0.02-0.18 <0.018 <0.01 <0.002 bal These alloys also have a microstructure which mainly consists of an austenitic matrix and eutectic alloy carbides.
    Other weldable Co-free hard welding alloys are marketed by Böhler Welding under the brand name SkWam and have the following composition in% by weight: C Si Mn Cr Mo Ni Fe SkWam-IG 0.2 0.65 0.55 17.0 1.1 0, 4 balance Fox SkWam 0.22 0.4 0.4 17.0 1.3 balance Since the Co-free hard weld coatings are also applied by welding, macroscopic cracking can occur from the beginning or during operation, as with the application of Stellite. in the sealing surfaces due to the stresses that arise 10 15 20 25 30 4 (36) during the welding process or during operation. This results in leakage and reduced stability against cutting, which leads to an increased need for costly maintenance in an environment with strict safety requirements.
    Furthermore, WO 2007/024192 A1 (Uddeholm Tooling Aktiebolag) describes a powder metallurgically manufactured steel alloy and tools or components made of the alloy. The alloy has the following composition in% by weight: 0.01-2 C, 0.6-10 N, 0.01-3.0 Si, 0.01-10.0 Mn, 16-30 Cr, 0.01- Ni, 0.01-5.0 (Mo + W / 2), 0.01-9 Co, max. 0.5 S and 0.5-14 (V + Nb / 2), where the content of on the one hand N and on the other hand (V + Nb / 2) are balanced in relation to each other so that the content of these elements is within a area bounded by the coordinates A ', B', G, H, A ', where [N, (V + Nb / 2)] - the coordinates of these points are: A °: [0,6, 0,5]; B °: [1.6, 0.5]; G: [9.8, 14.0]; H: [2.6, 14.0], and max. 7 of any of Ti, Zr and Al, essentially only iron and impurities remained at normal levels. The steel is intended for use in the manufacture of tools for injection molding, pre-pressing and extrusion of plastic components as well as corrosion-prone tools for cold work. Furthermore, also construction components, e.g. injection nozzles for motors, wear parts, pump parts, bearing components, etc.
    Another area of application is the use of the steel alloy for the manufacture of knives in the food industry.
    SUMMARY OF THE INVENTION An object of the invention is to provide a method for manufacturing a compound product, in which the application of the hard coating does not take place by welding.
    This object is achieved in the process indicated in the first paragraph above in that it comprises the following steps according to the invention: - production by powder metallurgical of a durable steel material with the following composition in% by weight: C Si Mn Cr Ni M0 + W / 2 Co SN 0.01 ~ 2 0.01f3.0 0.01 ~ 10.0 16 ~ 33 maxs 0, o1 ~ 5.0 max.9 max.0.5 0.640 further 0.5-14 off (V + Nb / 2 ), where the contents of on the one hand N and on the other hand (V + Nb / 2) are so balanced in relation to each other that the contents of said substances are within an area A ", B °, G, H, A" in a rectangular, flat coordinate system where the content N is abscissa and the content V + Nb / 2 is ordinate and where the coordinates of said points are 10 15 20 25 5 (36) A = BGHN 0.6 1.6 9.8 2.6 v + Nb / z 0.5 0.5 14.0 14.0 and max. 7 of any of Ti, Zr and Al, essentially only iron and unavoidable impurities, - application of the durable steel material to said surface area of the support, and - hetisostatic compacting the carrier with the coating to a completely dense or at least close to a completely dense body.
    An object connected with the above-mentioned purpose is to provide a compound product in which a wear surface meets high demands on resistance to abrasion and corrosion and also in Co-free design is free from macroscopic cracking.
    This object is achieved in the compound product stated in the second paragraph above in accordance with the invention, in that - it comprises a carrier material for a wear surface, where the carrier material has a first composition, - that the wear surface comprises a durable steel material with a second composition which comprises in% by weight : C Si Mn Cr Ni Mo + W / 2 Co SN 0.01-2 0.01-3.0 0.01-10.0 16-33 1116665 0.01-5.0 m6x.9 m6x.0, 0.6-io further 0.5-14 of (V + Nb / 2), where the contents of on the one hand N and on the other hand (V + Nb / 2) are so balanced in relation to each other that the contents of said substances lie within an area A °, B °, G, H, A "in a right-angled, flat coordinate system where the content N is abscissa and the content V + Nb / 2 is ordinate and where the coordinates of said points are A 'B" GHN 0 , 6 1,6 9,8 2,6 v + Nb / z 0,5 0,5 14,0 14,0 and max 7 of any of Ti, Zr and Al, essentially only residual and unavoidable impurities, - that the durable steel material has a microstructure that includes an even distribution of up to 50% by volume of M2X, MX and / or M23C6 / M7C3 type hard phase particles whose sizes are at their longest extent 1-10 μm, where the content of these hard phase particles are distributed so that up to 20% by volume consist of MgX carbides, nitrides and / or carbonitrides, where M is mainly V and Cr and X is mainly N, and 5-40% by volume of MX carbides, nitrides and / or carbonitrides, where M is substantially V and X is substantially N, where the average size of these MX particles is less than 3 μm, preferably less than 2 μm and even more preferably less than 1 μm.
    Because the abrasion-resistant coating is not applied by welding, it is avoided that macroscopic cracking occurs in the sealing surfaces from the beginning or during operation due to the stresses that arise during the welding process or during operation. This eliminates the risk of leakage and reduced stability against cutting, which provides the advantage of reduced need for costly maintenance in an environment with strict safety requirements. Due to the fact that the durable material has a composition as above, which is balanced with respect to the content of nitrogen in relation to the content of vanadium and any niobium present, a durable surface layer can be obtained on the compound product. Because the microstructure has a high content of very hard, stable hard phase particles, a wear surface can be achieved that well and well meets high requirements for anti-bile and anti-fretting properties while it exhibits very good corrosion properties.
    Another object connected with the above-mentioned object is to provide a new use for the steel alloy manufactured according to the above-known powder metallurgy.
    This object is achieved by according to the invention a steel material with the following composition in% by weight: C Si Mn Cr Ni Mo + W / 2 Co SN 0.01 ~ 2 0.01 ~ 3.0 0.01 ~ 10.0 16 ~ s3 0.01 ~ 5 0.01f5.0 max 166660; 0.640 further 0.5-14 of (V + Nb / 2), where the contents of on the one hand N and on the other hand (V + Nb / 2) are so balanced in relation to each other that the contents of said substances are within an area A ", B", G, H, A "in a right-angled, flat coordinate system where the content N is abscissa and the content V + Nb / 2 is ordinate and where the coordinates of said points are A" B "GHN 0.6 1.6 9.8 2.6 v + Nb / z 0.5 0.5 14.0 14.0 and 10 15 20 25 30 35 7 (36) max 7 of any of Ti, Zr and Al, essentially only iron and unavoidable contaminants, are used to provide a durable surface area on a support of a metallic material with a different, first composition, said surface area preferably constituting a wear surface on a valve, e.g. a valve in a nuclear power plant, more specifically a valve in the primary circuit of a nuclear power plant.
    This enables the use of the powder material produced by powder metallurgy for products that require very good abrasion resistance of a surface area of the product, while the product must meet requirements for corrosion resistance, machinability, ductility, cutability, hardness, heat treatment response both in terms of carrier and wear layer.
    Further characterizing features of various embodiments of the invention and what is achieved thereby appear from the following detailed description and the claims.
    BRIEF DESCRIPTION OF THE DRAWINGS In the following, the invention will be described in more detail with reference to preferred embodiments and the accompanying drawings.
    Figure 1 is a microstructure image taken with an electron microscope over an interconnect area between a carrier of AISI 316L to the hard coating of Vanax 75 (according to the invention) after hetisostatic compaction.
    Figure 2 is a graph showing the levels of vanadium, chromium, nickel and manganese in a compound product upon transition from a carrier of AISI 316L via a capsule wall of nickel to the hard coating of Vanax 75 (according to the invention) after hetisostatic compaction.
    Figure 3 is a graph showing the levels of carbon and nitrogen in a compound product upon transition from a carrier of AISI 3 16L via a nickel capsule wall to the hard coating of Vanax 75 (according to the invention) after hetisostatic compaction. 10 15 20 25 30 35 Figure 4 Figure 5 Figure 6 Figure 7 Figure 8 Figure 9 Figure 10 Figure 11 Figure 12 Figure 13 Figure 14 Figure 15 8 (36) is a diagram showing the analyzed composition of the steel material at transition from a support of AISI 316L via a nickel capsule wall to the hard coating of Vanax 75 (according to the invention) after hetisostatic compaction. shows the ratio between the content N and the content (V + Nb / 2) of the steel used in the form of a coordinate system. is a diagram comparing the abrasion resistance of the three alloys tested. is a diagram comparing the corrosion resistance of the three alloys tested. shows the microstructure of an abrasion resistant layer made of powder metallurgically produced steel material which has been compacted hot isostatically and then heat treated according to a preferred embodiment of the invention. shows the microstructure of an abrasion-resistant layer made by welding Stellite 6 (reference material). shows the microstructure of an abrasion-resistant layer made by welding Skwam (reference material). is a diagram showing the friction properties of Stellite 6. is a diagram showing the friction properties of Skwam. is a diagram showing the friction properties of Vanax 75. is a diagram showing the friction properties of Vanax 75 against Stellite 6. is a diagram comparing the hardness depending on the tempering temperature between the durable steel material according to the invention and Stellite 6. 10 15 20 25 30 35 9 (36) Figure 16 is a diagram comparing the cutability between the durable steel material of the invention and Stellite 6.
    DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS MANUFACTURE OF A COMPONENT PRODUCT In the method according to the invention for manufacturing a compound product, the durable steel material is applied to a surface area of a carrier of a first metallic material, which shall provide the required strength / strength product. The product thus obtained is hot isostatically compacted into a completely dense or at least almost completely dense body.
    According to a first preferred embodiment of the method, a putty of the first metallic material is placed, i.e. the carrier, in the capsule, and powder of the durable steel material is applied to said surface area of the pellet. Thereafter, the capsule is sealed and evacuated on gas and the capsule with contents is then compacted hetisostatically to a completely dense or at least near completely dense body.
    According to a second preferred embodiment of the method, powder of the durable steel material is applied to a surface area of at least to some extent finished putty of the first metallic material, i.e. the carrier, and a hood-like capsule is welded to the pellet so that the powder is enclosed in the hood towards the surface area. This can be done, for example, in such a way that powder is filled in a hood-like capsule which is placed with its open part against the surface area of the pellet so that the powder will abut against the pellet, after which welding of the hood and evacuation of gas in the hood is performed. Another way of applying the powder to the wear surface can be to mechanically adhere to the powder against the wear surface. Application of the powder by using any suitable binder is also conceivable.
    By applying the powder to the wear surface, a non-completely dense layer of powder can be built up, which is durable enough to handle the necessary handling in connection with hetisostatic compaction. The powder layer can then be consolidated into a complete or at least a complete design by hetisostatic compaction. No encapsulating capsule is required in this procedure.
    According to a third preferred embodiment of the method, an intermediate product of the durable steel material is prepared by bonding the powder grains in powder of the durable steel material, and this intermediate product is applied to a pellet of the first (36) metallic material, i.e. the carrier, after which the resulting unit is enclosed in the capsule.
    The powder cumin is preferably bonded together by sintering or hetisostatic compaction and the resulting body can also undergo some form of heat treatment, e.g. forge. A further processing to obtain a suitable shape e.g. band, ring or disc shape, is of course possible.
    Fig. 1 shows a microstructure image taken with an electron microscope over a bonding area between the carrier material 1 and the durable steel material 2.
    The joint 3 is clearly seen as a nearly sharp line between the two materials.
    The content of the alloying elements vanadium, chromium, manganese, nickel, carbon and nitrogen has been analyzed at regular intervals along an imaginary line from the support material 1 (points 1-5), over the joint 3 (points 6-8) and further into the durable steel material 2 (paragraphs 9-20).
    Fig. 2 shows a diagram of the content of the alloying elements vanadium, chromium, manganese, nickel. The measurement shows that the content of all elements is at an even level in the carrier material. The variations in the levels of vanadium and chromium in the durable steel material can be attributed to the presence of hard phase particles in the material.
    Fig. 3 shows how the contents of carbon and nitrogen vary along the test line and it is clear that neither the content of carbon nor nitrogen has changed in the carrier material. This can be considered very positive because both carbon and nitrogen are elements that are very mobile because they dissolve interstitially, and therefore there were fears that they would diffuse into the carrier material. Such a diffusion would be very serious because both carbon and nitrogen would then combine with primarily chromium and form chromium carbides in the grain boundaries. This depletes the carrier material on chromium and there is a risk of intercrystalline corrosion.
    Since a harmful diffusion between the durable steel material and the first metallic material could occur during the heat isostatic compaction, it is suitable that the two steel materials are kept separate by a diffusion barrier in the form of a housing wall. Such an enclosure wall preferably consists at least substantially of nickel or monel and may have a thickness of the order of 1 mm. In the case of hetisostatic compaction, it is in fact inappropriate for carbon and nitrogen to diffuse into the carrier material, if it is a stainless steel, since the stainless steel would then be susceptible to intercrystalline corrosion. 10 15 20 25 30 35 11 (36) Fig. 4 shows a diagram illustrating the content of certain critical alloying elements during transition from a support of AISI 316L (analysis points no. 1-11) via a capsule wall of nickel (analysis points no. 12 -19) to a recoverable hard coating of Vanax 75 (analysis points no. 20-32) after hetisostatic compaction. The slightly uneven curves in the Vanax 75 phase closest to the nickel phase can be attributed to hard phase particles.
    According to a fourth preferred embodiment of the method, the carrier is manufactured at the same time as the application of the abrasion-resistant coating. This can be done by filling an inner capsule with powder that the steel material that will give the wearer the required strength / strength. This capsule is sealed, evacuated on gas and positioned in an outer capsule, in which powder of the durable steel material is applied / applied. It is understood that the amount of powder of the respective steel material as well as the mutual placement of the inner capsule and the powder of the durable steel material, respectively, depend on your factors, e.g. the shape of the desired compound product, the thickness of the wear layer, the thickness of the carrier and the volume change (shrinkage) of the powder during compaction, and may be adjusted accordingly. Thereafter, the outer capsule is sealed and evacuated on gas and all is compacted hot isostatically. An alternative method according to this fourth embodiment is not to use an inner capsule but instead let powders of different steel materials be filled in a common capsule, where powders of the different steel materials are placed in a suitable place in the capsule to provide a compound product according to the invention, i.e. a carrier with a wear surface comprising a durable steel material.
    The hetisostatic compaction is suitably carried out for a time of the order of 3 hours at 1000-1350 ° C, preferably 1100-1150 ° C and a pressure of the order of 100 MPa.
    In all cases, the mentioned steps of machining to the intended dimensions and heat treatment are followed. This is followed by heat treatment, preferably by curing from an austenitizing temperature of 95 DEG-150 DEG C. and low temperature annealing at 200-450 ° C, 2 x 2 hours, or high temperature annealing at 450-700 ° C, 2 x 2 hours. Suitable temperatures are selected for to achieve desirable properties of the wear surface of the durable steel material, which will be discussed in detail later.
    Furthermore, in all cases the metallic material in the carrier is chosen to withstand hetisostatic compaction at 1100-1150 ° C and it is further important that the carrier material is selected so that it has heat treatment properties which are compatible with the durable steel material. In compound products for valves, it is suitable that the carrier consists of a steel (36) steel with intended properties in terms of corrosion, ductility and hardness and which, where applicable, meets pressure vessel standards. Examples which may be mentioned are ferritic, austenitic or ferritaustenitic materials in the stainless steel segment and examples of such materials are AISI 316L, AISI 304. A carrier material in, for example, AISI 316L is compatible for heat treatment in the temperature range 1050-1100 ° C, when an extinguishing annealing of The AISI 316L material is made. For other less demanding applications, other materials can be selected, e.g. carbon steel, pressure vessel steel, tool steel, cast iron, and also brass or copper, whereby a diffusion barrier of e.g. nickel or monel should be used where required.
    Within the scope of this invention, the term coating refers to the fact that the coating constitutes a relatively thin surface layer relative to the carrier, i.e. the thickness of the goods in the carrier far exceeds the thickness of the coating. However, it also refers to the fact that the thickness of the coating is substantially equal to the thickness of the carrier.
    In exceptional cases where circumstances require it, e.g. where the abrasion-exposed part of the product will form a protruding part and the carrier forms a fastening part, it will be appreciated that the coating of the durable steel material may constitute the major proportion of the compound product, and the term coating thus also includes the fact that the wall thickness of the durable steel material is significant. thicker than the wall thickness of the carrier. Thus, within the scope of the invention, the coating may have a thickness of 0.5-1000 mm, but in most applications the thickness most likely does not exceed 50 mm, and even more likely the thickness does not exceed 30 mm. In most cases, the coating will have a thickness of 0.5-10 mm, more preferably 3-5 mm.
    In a particularly preferred embodiment of the invention, where the compound product constitutes a component exposed to wear in a valve, and the material in the carrier consists of pressure vessel steel, it is then suitable that the durable steel material is free from intentionally added cobalt and forms wear surface on a wear exposed component in a valve in a nuclear power plant, and that the material in the carrier has a composition corresponding to AISI 3l6L. The valve is in the order of 100 mm in diameter and has a length of about 50-150 mm. The thickness of the wear layer after hetisostatic compaction, machining and possible grinding to the required surface finish is about 0.5-20 mm thick, preferably 3-5 mm thick.
    By not applying the abrasion-resistant coating by welding, it is avoided that macroscopic cracking occurs in the sealing surfaces from the beginning or during operation due to the stresses that arise during the welding process or during operation. This eliminates the risk of leakage and reduced stability against cutting, which provides the advantage of reduced need for costly maintenance in an environment with strict safety requirements. THE STEEL MATERIAL ITSELF The steel material used according to the invention is manufactured powder metallurgically, which is a condition for the steel to be largely free of oxidic inclusions and to obtain a microstructure which comprises that the durable steel material has a microstructure comprising an even distribution of up to 50 vol -% hard phase particles of M2X, MX and / or M23C6 / MyCg type whose sizes are at their longest extent 1-10 μm, where the content of these hard phase particles is distributed so that up to 20% by volume consists of MgX carbides, nitrides and / or carbonitrides, where M is mainly V and Cr and X are mainly N, and 5-40% by volume of MX carbides, nitrides and / or carbonitrides, where M is mainly V and X is mainly N, where the average size of these MX particles are less than 3 μm, preferably less than 2 μm and even more preferably less than 1 μm. Preferably, the powder metallurgical production comprises gas atomization of a steel melt with nitrogen as atomizing gas, which gives the steel alloy a certain minimum content of nitrogen. By solid phase nitriding of the powder, a higher, desirable nitrogen content can be achieved.
    The following also applies to the alloying elements in the steel.
    In the first place, carbon must be present in the recoverable steel in a sufficient amount to, together with nitrogen in solid solution in the steel matrix, contribute to the steel in its hardened and tempered state being given a high hardness, up to 60-62 HRC. Together with nitrogen, carbon can also be included in primarily precipitated MZX nitrides, carbides and / or carbonitrides where M is mainly V and Cr and X is mainly N and in primarily precipitated MX nitrides, carbides and / or carbonitrides, and M mainly consists of V and X mainly consists of N, and is included in any, MBCÖ and / or M7C3 carbides.
    Carbon together with nitrogen must give the desired hardness and form the constituent hard phases.
    The content of carbon in the steel, ie. carbon dissolved in the steel matrix plus the carbon bound in carbides and / or carbonitrides must be kept at as low a level as can be justified for production economic reasons and in phases. The steel must be able to be austenitized and converted to martensite during hardening. If necessary, the material is deep-cooled to avoid residual austenite. Preferably the carbon content should be at least 0.01%, even more preferably at least 14% (36) 0.05% and most preferably at least 0.1%. The maximum content of carbon can be allowed to amount to max. 2%. Depending on the application area, the carbon content is adjusted in relation to the amount of nitrogen in the steel and to the total content of primarily the carbide-forming elements vanadium, molybdenum and chromium in the steel so that the steel is given a content of MgX carbides, nitrides and / or carbonitrides of up to 20% by volume and a content of MX carbides, nitrides and / or carbonitrides of 5-40% by volume. M23C6 and / or M7C3 carbides can also be present in concentrations up to 8-10% by weight, especially at very high chromium concentrations. However, the total content of MX-, MgX- and / or M23C6 / M7C3 carbides, nitrides and / or carbonitrides in the steel shall not exceed 50% by volume. In addition, the presence of additional carbides in the steel must be minimized so that the content of dissolved chromium in the austenite is not less than 12%, preferably at least 13% and even more preferably at least 16%, which ensures that the steel obtains a good corrosion resistance.
    Nitrogen constitutes an essential alloying element for the steel according to the invention. Like carbon, nitrogen must be included in solid solution in the steel matrix to give the steel adequate hardness and to form the desired hard phases. Preferably, nitrogen is used as the atomizing gas in the powder metallurgical process for the production of metal powder. Through such a powder production, the steel will contain a maximum of about 0.2-0.3% nitrogen. This metal powder can then be given a desired nitrogen content according to any known technique, e.g. by pressurizing in nitrogen gas or by solid phase nitriding of produced powder, so that the steel suitably contains at least 0.6%, preferably at least 0.8% and most preferably at least 1.2% nitrogen. By applying pressurization in nitrogen gas or solid phase nitriding, it is of course possible to allow the atomization to take place with another atomizing gas, e.g. argon.
    In order not to cause brittleness problems and give residual austenite, the nitrogen content is maximized to 10%, preferably 8% and even more preferably a maximum of 6%. By changing vanadium but also strong nitride / carbide formers, e.g. chromium and molybdenum, have a tendency to react with nitrogen and carbon, the carbon content should at the same time be adapted to this high nitrogen content so that the carbon content is maximized to 2%, preferably a maximum of 1.5%, preferably a maximum of 1.2% for the above nitrogen contents. In doing so, however, it should be taken into account that the corrosion resistance decreases with a higher carbon content and that the gall resistance can also decrease, which is a disadvantage, above all due to that relatively large chromium carbides, M23C6 and / or M7C3 can be formed, compared with if the steel according to the invention is given a lower carbon content than the highest contents stated above. 10 15 20 25 30 35 15 (36) In cases where it is sufficient to give the steel lower nitrogen contents, it is therefore desirable to also lower the carbon content. Preferably the carbon content is limited to as low levels as can be justified for cost reasons, but according to the inventive idea the content of carbon can be varied at a given content of nitrogen whereby the steel content of hard phase particles and its hardness can be adjusted depending on which application area the steel is intended for. Nitrogen also helps to promote the formation of MX carbonitrides at given levels of the anti-corrosion alloying elements chromium and molybdenum and to suppress the formation of M23C6 and / or M7C3 which adversely reduce the corrosion properties of the steel.
    Silicon is included as a residue from steel production and occurs in a minimum content of 0.01%. At higher levels, silicon gives a solution-hardening, but also a certain brittleness.
    Silicon is also a strong ferrite former and must therefore not be present in concentrations above 3.0%.
    Preferably the steel does not contain more than max. 1.0% silicon, preferably max. 0.8%. A nominal silicon content is 0.3%.
    Manganese helps to give the steel good hardenability. To avoid brittleness problems, manganese must not be present in concentrations above 10.0%. Preferably the steel does not contain more than max. 5.0% manganese, preferably max. 2.0% manganese. In embodiments where the curability is not of equal importance, manganese is present in low levels in the steel as a residual substance from the steel's production and binds the amounts of sulfur that can be present by forming manganese sulphide. Manganese should therefore be present in a content of at least 0.01% and a suitable manganese range is within 0.2-0.4%.
    Chromium should be present in a minimum content of 16%, preferably at least 17% and even more preferably at least 18%, to give the steel the desired corrosion resistance. Chromium is also an important nitride former and as such an element must be present in the steel in order to, together with nitrogen, give the steel a content of hard phase particles which contribute to giving the steel the desired grinding and abrasion resistance. Of these hard phase particles, up to 20% by volume may consist of MZX carbides, nitrides and / or carbonitrides, where M consists mainly of Cr but also a certain lower proportion of V, Mo and Fe, and 5-40% by volume. % may consist of MX carbides, nitrides and / or carbonitrides, where M consists mainly of V. However, chromium is a strong ferrite former. To avoid ferrite after curing, the chromium content must not exceed 33%, preferably a maximum of 30%, preferably a maximum of 27%, and even more preferably a maximum of 25%. 10 15 20 25 30 35 16 (36) Nickel is an optional substance and as such may be included as an austenite stabilizing substance in a content of a maximum of 5.0% and suitably a maximum of 3.0% to balance the high steel. levels of the ferrite-forming substances chromium and molybdenum. Preferably, however, the steel according to the invention does not contain any intentionally added amount of nickel.
    Nickel can, however, be tolerated as an unavoidable pollutant, which as such can be as high as about 0.8% Cobalt is also an optional substance and as such may possibly be included in a content of max 9% and preferably max 5%, to improve tempering resistance. In hard coatings in e.g. valves for nuclear power plants and other applications where radioactivity occurs, however, the steel should not contain any cobalt.
    Molybdenum should be present in the steel as it helps to give the steel the desired corrosion resistance, in particular good point corrosion resistance. However, molybdenum is a strong ferrite former, so the steel must not contain more than max. 5.0%, preferably max. 4.0%, preferably a maximum of 3.5% Mo. A nominal molybdenum content is 1.3%. Molybdenum can in principle be completely or partially replaced by tungsten, which, however, does not give the same improvement in corrosion resistance. In addition, twice as much tungsten as molybdenum is required, which is a disadvantage. In addition to this, scrap handling is also made more difficult.
    Vanadium should be present in the steel in a content of 0.5-14%, preferably 1.0-13%, preferably 2.0-12% in order to form together with nitrogen and the carbon present the said MX nitrides, carbides and / or -carbonitrides. According to a first preferred embodiment of the invention, the vanadium content is in the range 0.5-1.5%. According to a second preferred embodiment, the vanadium content is in the range 1.5-4.0, preferably 2.0-3.5 and even more preferably 2.5-3.0%. A nominal vanadium content according to this second preferred embodiment is 2.85%. According to a third embodiment of the invention, the vanadium content is in the range 4.0-7.5, preferably 5.0-6.5 and even more preferably 5.3-5.7%. A nominal vanadium content according to this third preferred embodiment is 5.5%. According to a fourth embodiment of the invention, the vanadium content is in the range 7.5-11.0, preferably 8.5-10.0 and even more preferably 8.8-9.2%. A nominal vanadium content according to this fourth preferred embodiment is 9.0%. Within the scope of the inventive idea, it is conceivable to allow vanadium contents up to about 14% in combination with nitrogen contents up to about 10% and carbon contents in the range 0.1-2%, which gives the steel desirable properties, especially when used as hard material coatings in mold and cutting tools with high demands on corrosion resistance in combination with high hardness (up to 60-62 HRC) and moderate ductility and extremely high demands on abrasion resistance (abrasive / adhesive / coating / fretting).
    In principle, vanadium can be replaced by niobium to form MX nitrides, carbides and / or carbonitrides, but this requires a larger amount compared to vanadium, which is a disadvantage. In addition, niobium causes the nitrides, carbides and / or carbonitrides to have a more angular shape and become larger than pure vanadium nitrides, carbides and / or carbonitrides, which can initiate fractures or ices and thus lower the toughness and polishability of the material. This can be particularly serious for steel in cases where the composition has been optimized with the aim of, in terms of the mechanical properties of the material, achieving excellent abrasion resistance in combination with good ductility and high hardness. In these cases, the steel must therefore not contain more than a maximum of 2%, preferably a maximum of 0.5%, preferably max. 0.1% niobium. In terms of production, there are also problems as Nb (C, N) can cause clogging of the pin jet from the ladle during atomization. According to this first embodiment, the steel must therefore not contain more than a maximum of 6%, preferably a maximum of 2.5%, preferably max. 0.5% niobium. In the most preferred embodiment, niobium is no longer tolerated as an unavoidable contaminant in the form of residual elements derived from raw materials in the manufacture of steel.
    In addition to the alloying elements mentioned, the steel need not, and should not, contain any additional alloying elements in significant contents. Some elements are explicitly undesirable, as they affect the properties of the steel in an undesirable way. This applies to e.g. phosphorus which should be kept as low as possible, preferably max. 0.03%, so as not to adversely affect the toughness of the steel. Sulfur is also an undesirable element in most respects, but its negative effect on mainly toughness can be substantially neutralized with the help of manganese, which forms essentially amorphous manganese sulphides and can therefore be tolerated at a maximum content of 0.5% to improve the steel's machinability. Titanium, zirconium and aluminum are also undesirable in most respects but can together be permitted at a maximum content of 7%, but nonnally at significantly lower levels, <0.1%, together.
    As mentioned, the nitrogen content must be adapted to the content of vanadium and any niobium present in the material in order to give the steel a content of 5-40% by volume of MX carbides, nitrides and / or carbonitrides. The conditions for the ratios between N and (V + Nb / 2) are shown in Fig. 1, which shows the content N coupled to the content (V + Nb / 2) of the steel according to the invention. The high points in the areas shown have coordinates according to the following table: 10 18 (36) Table 1, the ratios between N and (V + Nb / 2) N v + Nb / 2 A 0.8 0.5 A ”0.6 0, 5 E 1.4 0.5 E ”1.6 0.5 c 8.0 14.0 4.3 14.0 E 1.9 1.5 E” 3.1 4.0 E ”” 4.8 7.5 6.5 11.0 E 2.2 1.5 E ”3.7 4.0 E” ”5.8 7.5 8.0 11.0 G 9.8 14.0 H 2.6 14.0 1 0.7 1.5 1 ”1.1 4.0 1” 1.6 7.5 J ”” ”2.1 11.0 J 1.1 1.5 J” 1.7 4, 0 J "2.6 7.5 J" "" 3.5 11.0 According to a first aspect of the steel used according to the invention, the content of on the one hand N and on the other hand (V + Nb / 2) must be so balanced in relation to each other that the content of these elements is within an area limited by the coordinates A ", B °, G, H, A" in the coordinate system in Fig. 5.
    According to a first preferred embodiment of the invention, the content of nitrogen, vanadium and any niobium present in the steel should be so balanced in relation to each other that the contents are within the range defined by the coordinates A °, B °, E, I, A ", and more preferably within A, B, E, J, A. 10 15 20 19 (36) According to a second preferred embodiment of the invention, the content of nitrogen, vanadium and any niobium present in the steel should be so balanced in relation to each other that the contents are within the range defined by the coordinates I, F, F °, I °, I and more preferably E, E °, J ', J, E.
    According to a third preferred embodiment, the content of nitrogen, vanadium and any niobium present in the steel should be so balanced in relation to each other that the contents are within the range defined by the coordinates I °, F ", F", I ", I" and more preferably E °, E ", J", J °, E ".
    According to a fourth preferred embodiment, the content of nitrogen, vanadium and any niobium present in the steel must be so balanced in relation to each other that the contents are within the range defined by the coordinates I ", F", F "°, I °", I " and more preferably J ", E", E ° ", J °", J ".
    Table 2 shows the composition ranges in% by weight of a steel according to the first preferred embodiment of the invention.
    Table 2: Subject C Si Mn Cr Mo V N Min. 0.10 0.01 0.01 0.01 18.0 0.01 0.5 0.8 Nominal value 0.20 0.30 0.30 21.0 1.3 1.0 0.95 Max. 0.50 1.5 1.5 21.5 2.5 2.0 2.0 Table 3 shows the composition ranges in% by weight of a steel according to the second preferred embodiment of the invention.
    Table 3 Topic C Si Mn Cr Mo V N Min. 0.10 0.01 0.01 13.0 0.01 2.0 1.3 Guide value 0.20 0.30 0.30 21.0 1.3 2.85 2.1 Max. 0.50 1.5 1.5 21.5 2.5 4.0 3.0 10 15 20 20 (36) Preferably the content of V is between 2.5 and 3.0% by weight and the content of N is between 1 , 3 and 2.0% by weight. As an illustrative example, a complete analysis of such a steel, including impurities, can give the following composition in% by weight: Table 4 C Si Mn PS Cr Ni Mo W Co 0.18 0.34 0.38 0.007 0.006 20.1 0.009 1 , 32 0.003 0.009 V Ti Nb Cu Sn Al NB Ca Mg 2.87 0.006 0.002 0.005 0.002 0.001 1.65 0.0001 0.0005 0.00010 The steel according to the second embodiment is suitable for use where there are high requirements for corrosion resistance in combination with high hardness (up to 60-62 HRC) and good ductility as well as increasing demands on resistance to both abrasive and adhesive wear as well as galling and fretting. With a composition according to the table, the steel has a matrix which, after curing from an austenitizing temperature of 950-1150 ° C and low temperature annealing at about 200-450 ° C, 2 x 2 h, or high temperature annealing at 450-700 ° C, 2 x 2 h, consists of tempered martensite with a hard phase amount consisting of up to about 10% by volume each of MgX, where M is mainly Cr and X is mainly N, and MX, where M is mainly V and Cr and X in mainly consists of N.
    Table 5 shows the composition ranges in% by weight of a steel according to the third preferred embodiment of the invention.
    Table 5: Subject c si Mn Cr M0 Min. 0.10 0.01 0.01 18.0 0.01 4.0 1.5 Guideline 0.20 0.30 0.30 21.0 1.3 5.5 3.0 Max. 0.80 1.5 1.5 21.5 2.5 7.5 5.0 Table 6 shows the composition ranges in% by weight of a steel according to the fourth preferred embodiment of the invention. 10 15 20 25 21 (36) Table 6 Topic C Si Mn Cr Mo V N Min. 0.10 0.01 0.01 18.0 0.01 7.5 2.5 Guide value 0.20 0.30 0.30 21.0 1.3 9.0 4.3 Max. 1.5 1.5 1.5 21.5 2.5 11 6.5 The steel according to the second embodiment is suitable for use wear surfaces on products with high requirements for corrosion resistance in combination with high hardness (up to 60-62 HRC) and relatively good ductility and very high requirements for abrasion resistance (abrasive / adhesive / galling / fretting). With a composition according to the table, the steel has a matrix which, after hardening from an austenitizing temperature of about 1080 ° C and low-temperature annealing at about 200-450 ° C, 2 x 2 h, or high-temperature annealing at 450-700 ° C, 2 x 2 h, of tempered martensite with a hard phase amount consisting of about 3-15 vol-% of MzX, where M consists mainly of Cr and V and X mainly consists of N, and 15-25%, where M consists mainly of V and X mainly consists of N.
    Table 7 shows the composition ranges in% by weight of a steel according to a further preferred embodiment of the invention.
    Table 7 Topic C Si Mn Cr Mo V N Min. 0.10 0.01 0.01 30.0 0.01 7.5 4.0 Guide value 0.20 0.30 0.30 32.0 1.3 9.0 5.6 Max. 1.5 1.5 1.5 33.0 2.5 11 7.0 Within the scope of the inventive concept, it is conceivable to allow nitrogen contents up to about 10% which in combination with vanadium contents up to about 14% and carbon contents in the range 0.1- 2% gives the steel desirable properties, especially when used for wear surfaces on products with high demands on corrosion resistance in combination with high hardness (up to 60-62 HRC) and moderate ductility and extremely high demands on abrasion resistance (abrasive / adhesive / cladding / fretting ). The steel according to this embodiment has a matrix which, after curing from an austenitizing temperature of about 1100 ° C and low temperature annealing at about 200-450 ° C, 2 x 2 hours, or annealing at 450-700 ° C, 2 x 2 hours, is formed. of annealed martensite with a hard phase amount consisting of about 2-15 and 30 15% by volume of MZX, respectively, where M consists essentially of Cr and V and X consists essentially of N, and MX, where M is essentially V and X is essentially N.
    The steel according to the embodiments described above has been found to be suitable for use as wear surfaces on products which are subjected to large mixed adhesive and abrasive wear, in particular galling and fretting. . It also exhibits high hardness and very good corrosion resistance, which is why it is suitable for use as wear surfaces on products in the food industry, offshore industry and other corrosion-prone products, e.g. injection nozzles for engines, bearing components etc. Because the durable steel material is relatively hard and brittle, it can withstand relatively poorly the loads that occur with screw joints. By using the steel material in a compound product, a product is obtained where the carrier material is responsible for the product meeting other conditions that the wear material does not meet, e.g. required ductility, machinability and machinability. Examples of such products are valves, wear details in pumps, wear bodies and other complex abrasive parts.
    When heat treating the compound product, the durable steel material is austenitized at a temperature between 950 ° C and 1150 ° C, preferably between 1020 ° C and 1130 ° C, preferably between 1050 ° C and 1120 ° C. Higher austenitization temperature is in principle conceivable but is unsuitable in view of the fact that normally occurring curing ovens are not adapted for higher temperatures. A suitable holding time at the austenitization temperature is 10-30 minutes. From said austenitization temperature, the steel is cooled to room temperature or lower, e.g. to -40 ° C. In order to eliminate existing residual austenite in order to give the product the desired dimensional stability, deep cooling can be applied which is suitably carried out in carbon dioxide snow (dry ice) to about -70 to -80 ° C or in surface nitrogen at about -196 ° C. To obtain optimum corrosion resistance, the tool is tempered at 200-300 ° C at least once, preferably twice. If, instead, it is desired to optimize the steel to obtain a secondary hardening high temperature, the product is tempered at least once, preferably twice and possibly several times at a temperature between 400-560 ° C, preferably at 450-525 ° C. After each such tempering treatment, the product is cooled. Preferably, deep cooling as above is also applied in this case to further ensure the desired dimensional stability by eliminating any remaining residual austenite. The holding time at the tempering temperature can be 1-10 hours, preferably 1-2 hours. The composition of the durable steel material used gives a very good tempering resistance. 10 15 20 25 30 35 23 (36) In connection with the various heat treatments to which the durable steel material is subjected, for example in the hetisostatic compaction to form a composite compound product, and in the hardening of the finished compound product, adjacent carbides, nitrides and / or carbonitrides in the durable steel material coalesce to form larger aggregates. The size of these hard phase particles in the wear layer in the finished, heat-treated product can therefore amount to more than 3 μm.
    The main part expressed in% by volume is in the range 1-10 μm calculated in the longest extent of the particles and the average size of the particles is less than 1 μm. The total amount of hard phase depends on the nitrogen content and the amount of nitride formers, ie. mainly vanadium and chromium. In general, the total amount of hard phase in the wear layer in the finished product is in the range of 5-40% by volume.
    Powders of the durable steel material are prepared by distributing a melt with the composition specified for the durable steel material, with the exception of nitrogen, by blowing inert gas, preferably nitrogen, through a jet of the melt which splits into droplets which are allowed to solidify, after which it the powder obtained is subjected to solid phase nitration to the desired nitrogen content.
    EXECUTIONS PERFORMED Preparation of samples On a surface area of each platform carrier, Stellite 6 and SkWam were applied by four-layer welding. The thickness of the applied layer was 5 mm.
    The test surfaces themselves were then ground and polished to a surface finish required for valves, ie. Ra ~ 0.05 um. Even after polishing, the welded surfaces had small pores, which could be distinguished with the naked eye.
    After welding, Stellite 6 and Skwam have a hardness of 42 HRC according to data sheets from the manufacturers, and this was confirmed by laboratory measurement.
    Samples of Vanax 75, a powder metallurgically produced steel having a composition within the limits set forth in claim 1, were cut from a HIP body and ground and polished to the same surface unit as the welds applied by welding coating.
    The test pieces of Vanax 75 were heat treated in a vacuum oven using nitrogen gas as a rapid coolant. The heat treatment cycle used was austenitization at an austenitization temperature, TA = 1080 ° C for 30 minutes followed by deep cooling in liquid nitrogen and double annealing at an annealing temperature of 400 ° C for two hours (2 x 2 hours). ).
    Chemical composition The guideline values for the chemical compositions in% by weight of the alloys used in the test program are shown in Table 6.
    Table 6 Alloy Leg-base CN Si Mn Cr Ni Mo WV Fe Co Stellite 6 Co 1.3 ~ l, l 0.1 30 2.3 0.1 4.7 ~ 2.5 bal Skwam Fe 0.2 ~ 0 .4 0.4 17 ~ 1.3 ~ f bal ~ Vanax 75 Fe 0.2 4.3 0.3 0.3 21 ~ 1.3 f 9 bal ~ Abrasion resistance The abrasion resistance was assessed using a stick-to-disc -Test. A sandpaper with A120; (1500 mesh) was used in the sample and the pressure in the sample was 0.4 MPa. The wear loss in mg / min for the three tested alloys is shown in Fig. 6. The figure shows that the durable steel material according to the invention, Vanax75, has a considerably much better abrasion resistance than the two comparison materials Stellite 6 and Skwam.
    Corrosion resistance The corrosion resistance of AISI 316L, Vanax 75 and Skwam was assessed using a standard cyclic polarization method according to ASTM 65 to determine the breakdown voltage of the oxide layer on the alloys in an aqueous solution containing 3500 or 35000 ppm C17. All tests were performed at room temperature. Fig. 7 shows the corrosion resistance as the breakdown voltage in mV in chloride-containing water. For each alloy, two bars are displayed next to each other. The left bar shows the result at a chloride content of 3500 ppm Cl * while the right one refers to a ten times higher content, 35000 ppm Cl ”. All tests were performed at room temperature, and higher value indicates better corrosion resistance. The figure shows that the Vanax 75 has better corrosion resistance than the Skwam but worse than the AISI 316L. For AISI 316L, however, it should be pointed out that there is a certain spread, which seems to be linked to the dimension of the steel and how it has been machined. Practical experiments have shown breakdown voltages down to 600 mV. 10 15 20 25 30 35 25 (36) Hardness After welding, Stellite 6 and SkWam have a hardness of 42 HRC. The test pieces of Vanax 75 have a hardness of 61 HRC after curing and low temperature annealing according to OVaII.
    Microstructure The microstructure of Vanax 75 consists of a martensitic matrix and 23% by volume of a hard phase of the MX type, where M represents V and X represents N and C. The size of the hard phase particles is on average less than 3 μm, preferably less than 2 μm. and even more preferably less than 1 μm. The hard phase particles are homogeneously distributed in the matrix, see Fig. 8.
    After welding, the microstructure of Stellite 6 consists of a dendritic austenitic cobalt matrix and a high volume fraction of relatively very coarse, elongated chromium carbides. The chromium carbides occur in the dendritic residual melting regions and are thus very unevenly distributed in the matrix, see Fig. 9.
    After welding, the microstructure of SkWam consists of a martensitic matrix with interdendritic chromium carbides. The coarse chromium carbide units are unevenly distributed in the matrix, see Fig. 10.
    Friction properties The friction properties of steel materials are of great interest for certain applications, e.g. for valves, as they affect the energy consumption of the motors and affect the type of motors that can be used for the actuators of the valves. Electric motors can handle lower loads, while larger loads require pneumatically or hydraulically regulated actuators. This in turn affects which equipment can be used.
    The friction properties are affected by the steel's anti - gall properties and these were tested by abrasion steel against steel where a test rod of one material is placed against a rotating disk of another or the same steel material. The testing was performed in deionized water at a temperature of 80 ° C, max. contact pressure = 720 MPa, surface unit, Ra ~ 0.02 pm, relative sliding speed = 0.02 m / s, test time / test length = 1000 s / 20 min. 10 15 20 25 30 35 26 (36) The result for testing Stellite 6 against Stellite 6 is shown in Fig. 11. Initially, the friction increases and then decreases and ends up at an even level, u about 0.25, which confirms the effects of the types initially described.
    Fig. 12 shows the friction properties of two surfaces of Skwam tested against each other. As can be seen, a gradually increasing coefficient of friction is obtained during the test, which is due to alternating cold welding and release between the materials.
    The friction properties when two surfaces of Vanax 75 were tested against each other are shown in Fig. 13. This material exhibits good friction properties which are at a blank level, u about 0.36, which can be attributed to the even distribution of very fine and hard hard phase particles.
    Finally, a surface of Stellite 6 was tested against a surface of Vanax 75. The result can be seen in Fig. 14. Initially, a certain small increase in the coefficient of friction is obtained, significantly less than when Stellite 6 constituted both wear surfaces, and then the coefficient of friction decreases and settles. a level around 0.22, i.e. better than when Stellite 6 is used for both contact surfaces. This is very remarkable and shows that the friction can be kept at a possible lower level, which enables the use of electrically powered equipment, which gives greater flexibility than with pneumatic and hydraulic equipment.
    Annealing resistance The annealing resistance of the durable steel material, Vanax 75, was tested. The result shown in Fig. 15 shows that the durable steel material has a very good annealing resistance. For Vanax 75 in a deep-frozen state, a hardness of about 60-62 HRC is obtained when tempering up to about 500 ° C. Thereafter, the hardness decreases, but still a hardness is obtained that well exceeds that which can be achieved with Stellite 6, which is around 42 HRC, regardless of tempering temperature. Vanax 75 in the non-deep-frozen state shows a good tempering resistance and obtains a hardness of around 51-55 HRC.
    High temperature resistance The high temperature resistance of the durable steel material was investigated by studying how the hard phase particles were affected when heated to different temperatures up to just over 1300 ° C. It could be stated that the hard phase particles were very stable. In principle, no or only very little growth of the hard phase particles took place, despite the high temperatures used. This is very advantageous if the material is to be used at high operating temperatures (700-800 ° C) and long operating times. As an example can be mentioned 10 15 20 25 30 35 27 (36) steam or gas turbine plants in the power industry where the operation takes place at very high temperatures and also during extremely long operating times, up to 60 years for such a plant.
    Cuttability The machinability of the durable steel material according to the invention was examined and compared with Stellite 6. The machinability of Vanax 75 was examined in delivery condition, ie. HIP and soft annealed state (35 HRC), and in hardened and annealed state (60 HRC) while the machinability of Stellite 6 was investigated in delivery state (46 HRC).
    The machinability of the Vanax 75 in delivery condition was the reference value. Fig. 16 shows that Vanax 75 is in a hardened and tempered state and Stellite 6 has comparable machinability (around 0.30). Application tests have t.o.m. has shown that Vanax 75 in hardened and tempered condition has slightly better cutability than Stellite 6. Vanax 75 in delivery condition has the best cutability (1.0).
    DISCUSSION The results of the experiments reported above show that a durable surface layer with a composition according to claim 1 can very successfully be applied to a metallic support without the support risking being depleted locally on anti-corrosion alloying elements. The joining of the two materials preferably takes place by hetisostatic compaction. In the case of hetisiostatic compaction, the durable steel material or carrier can consist of: a) powder or solid material, b) powder and powder, respectively, with or without barrier layer, or c) of solid material and solid material, respectively.
    The product obtained is particularly suitable for use on components which are subjected to hard surface pressures, i.e. in abrasion-prone applications where abrasive wear and wear due to cold welding between the components, so-called galling, is particularly pronounced. Thanks to the fact that the durable steel material also has very good corrosion resistance, it can be used to advantage in the offshore industry, the food industry, the process industry and the pulp industry where corrosion resistance is also required and they are found in valves, pumps and fasteners. Through the manufacturing process according to the invention it has been found possible to produce a compound product which is particularly suitable for use as a valve for regulating the fate of steam and water in the primary circuit of a nuclear power plant and it seems possible to replace current valves containing a wear surface. of the cobalt-based alloy 28 (36) Stellite 6. This adds another advantage. Due to the fact that the durable steel material does not contain any cobalt, today's problems with an increasing level of background radiation in the primary circuit in boiling water reactors can be avoided. It has also been shown that the inventive steel material has excellent friction properties and it seems possible to offer products that help reduce energy consumption and enable the choice of electrically driven control equipment, which provides greater flexibility than when pneumatic and hydraulic components must be used.
    权利要求:
    Claims (1)
    [1]
    A method for manufacturing a compound product comprising a carrier of a first metallic material, which gives the required strength / strength to the product, and a coating of durable steel material applied to a surface area of the carrier, characterized of the following steps: - production by powder metallurgy of a durable steel material with the following composition in% by weight: C Si Mn Cr Ni Mo + l / zW Co SN 0.0l ~ 2 0.0l ~ 3.0 0.0l ~ l0.0 l6f33 max.5 0.0l ~ 5.0 max.9 max.0.5 0.6 ~ l0 further 0.5-14 of (V + Nb / 2), where the content of on the one hand N and on the other hand (V + Nb / 2) are so balanced in relation to each other that the contents of said substances are within an area A °, B °, G, H, A 'in a right-angled, flat coordinate system where the content N constitutes an abscissa and the content V + Nb / 2 is ordinate and where the coordinates of the mentioned points are A "B" GHN 0.6 1.6 9.8 2.6 v + Nb / z 0.5 0.5 14.0 14.0 and max 7 of any of Ti, Zr and Al, traveled essentially only jäm and oun ductile impurities, - application of the wear-resistant steel material to said surface area of the carrier, and - heat isostatic compaction of the carrier with the coating into a completely tight or at least close to completely tight body. Method according to claim 1, characterized in that it also comprises - enclosing the carrier with the coating in a capsule, - evacuation of gas in the capsule, and after the hetisostatic compaction, - removal of the capsule or at least the part of the capsule covering it durable steel material. Method according to claim 2, characterized in that a pellet of the first metallic material is placed in the capsule, and that powder of the durable steel material is applied to said surface area of the pellet, after which the capsule is closed. A method according to claim 1, characterized in that powder of the durable steel material is applied to a surface area of an at least partially finished putty of the first metallic material, and that a hood-like capsule is arranged to enclose said powder and is welded to sides of the pellet. Method according to claim 2, characterized in that an intermediate product of the durable steel material is prepared by bonding the powder grains in powder of the durable steel material, and that this intermediate product is applied to a pellet of the first metallic material, after which the obtained unit is enclosed in the capsule. Process according to Claim 5, characterized in that the intermediate product is band-shaped, annular or disc-shaped. Method according to Claim 5 or 6, characterized in that the powder cumin is bonded together by hetisostatic compaction. Method according to one of Claims 2 to 7, characterized in that the two steel materials are kept separate by a housing wall in order to avoid a harmful diffusion of easily movable alloying elements, e.g. C or N, between the durable steel material and the first metallic material. Method according to claim 8, characterized in that the encapsulation wall consists mainly of nickel or monel. A method according to claim 2, characterized in that also the first metallic material consists of a powder which is placed in said capsule. Method according to claim 2, characterized in that said capsule constitutes a first capsule, that a second capsule is filled with powder of the first metallic material, i.e. the carrier, that the second capsule is sealed and placed in the first capsule, that powder of the durable steel material is filled into the second capsule so that it is applied next to the enclosure wall adjacent to at least said surface area of the carrier, after which the first capsule is sealed. Method according to one of Claims 1 to 11, characterized in that powder of the durable steel material is produced by atomizing a melt with the composition specified for the durable steel material, with the exception of nitrogen, 10 15 20 25 30 13. 14. 15 16. 17. 18. 19. 31 (36) by blowing inert gas, preferably nitrogen, through a jet of the melt which splits into droplets which are allowed to solidify, after which the powder obtained is subjected to solid phase nitration to the desired nitrogen content. Process according to any one of claims 1-12, characterized in that the hetisostatic compaction is carried out for a time of the order of 3 hours at 1000-1350 ° C, preferably 1100-1150 ° C and a pressure of the order of 100 MPa. Method according to any one of claims 1-13, characterized in that the said steps are followed by machining to the intended dimensions and heat treatment. Method according to any one of claims 1-14, characterized in that the coating has a thickness of 0.5-1000 mm, preferably 0.5-50 mm, and even more preferably 0.5-30 mm. Method according to any one of claims 1-15, characterized in that the coating has a thickness of 0.5-10 mm, more preferably 3-5 mm. Process according to Claim 14, characterized in that the heat treatment is carried out by curing from an austenitizing temperature of 950-1150 ° C and low-temperature annealing at 200-450 ° C, 2 x 2 hours, or high-temperature annealing at 450-700 ° C, 2 x 2 h. Process according to one of Claims 1 to 17, characterized in that the durable steel material contains the following substances with the stated contents in% by weight: Substance C Si Mn Cr Mo VN Min. 0.10 0.01 0.01 18.0 0.01 2.0 1.3 RilítVäfCl fi 0.20 0.30 0.30 21.0 1.3 2.85 2.1 MaX. 0.50 1.5 1.5 21.5 2.5 4.0 3.0 Process according to claims 1-17, characterized in that the content of V is between 2.5 and 3.0% by weight and the content of N between 1.3 and 2.0% by weight. Process according to one of Claims 1 to 17, characterized in that the durable steel material contains the following substances with the specified contents in% by weight: Substance C Si Mn Cr Mo VN Mm. 0.10 0.01 0.01 18.0 0.01 7.5 2.5 Rikwäfde 0.20 0.30 0.30 21.0 1.3 9.0 4.3 Max. 1.5 1.5 1.5 21.5 2.5 11 6.5 21. Process according to one of Claims 1 to 17, characterized in that the durable steel material contains carbon up to a content of 0.1 2% by weight, nitrogen to a content of up to about 10% by weight and vanadium with a content of up to about 14% by weight. Compound product comprising a support of a first metallic material, which gives the required strength / strength to the product, and a coating of durable steel material applied to a surface area of the support, characterized in that: - it comprises a support material for a wear surface, where the support material has a first composition, - that the wear surface comprises a durable steel material with a second composition which comprises in% by weight: C Si Mn Cr Ni Mo + W / 2 Co SN 0.0142 0.01 ~ 3.0 0.01 ~ 10 .0 16433 mms 0.0145.0 max »max.0.5 0.6410 further 0.5-14 of (V + Nb / 2), where the content of on the one hand N and on the other hand (V + Nb / 2) are so balanced in relation to each other that the contents of said substances are within an area A ", B °, G, H, A" in a right-angled, flat coordinate system where the content N is abscissa and the content V + Nb / 2 is ordinate and where the coordinates of said points are A * B * GHN 0.6 1.6 9.8 2.6 v + Nb / z 0.5 0.5 14.0 14.0 and max 7 of any of Ti, Zr and Al, rest essentially only iron and unavoidable impurities, - that the durable steel material has a microstructure which comprises an even distribution of up to 50% by volume of hard phase particles of M2X, MX and / or M23C6 / M7C3 type whose sizes at their longest extent are 1-10 μm, where the content of these hard phase particles is distributed so that up to 20% by volume consists of MgX carbides, nitrides and / or carbonitrides, where M is mainly Cr and X is mainly N, and 5-40% by volume of MX carbides, nitrides and / or carbonitrides, where M is mainly V and Cr and X is mainly N, where the average size of these MX particles is less than 3 μm, preferably less than 2 μm, and than more preferably less than 1 μm. 23. 24. 25. Compound product according to claim 22, characterized in that - the durable steel material is applied to the support by hetisostatic compaction to obtain a compacted product, - that the compacted product is machined to the intended dimensions, and - that it is heat treated by hardening from an austenitizing temperature of 950-1150 ° C and low temperature annealing at 200-450 ° C, 2 x 2 hours, or high temperature annealing at 450-700 ° C, 2 x 2 hours. Compound product according to claim 22 or 23, characterized in that in the the durable steel material includes the following substances with the specified contents in% by weight: Substance C Si Mn Cr Mo VN Min. 0.10 0.01 0.01 18.0 0.01 2.0 1.3 Rich value 0.20 0.30 0.30 21.0 1.3 2.85 2.1 Max. 0.50 1.5 1.5 21.5 2.5 4.0 3.0 Compound product according to claim 24, characterized in that the content of V is between 2.5 and 3.0% by weight and the content of N between 1.3 and 2.0% by weight. Compound product according to Claim 22 or 23, characterized in that the durable steel material contains the following substances with the stated contents in% by weight: Substance C Si Mn Cr Mo V N Min. 0.10 0.01 0.01 18.0 0.01 7.5 2.5 Guide value 0.20 0.30 0.30 21.0 1.3 9.0 4.3 Max. 1.5 1.5 1.5 21.5 2.5 11 6.5 10 15 20 25 30 27. 26. 27. 28. 29. 30. 31. 32. 34 (36) Compound product according to claim 22 or 23 , characterized in that the durable steel material contains carbon to a content of 0.1-2% by weight, nitrogen to a content of up to about 10% by weight and vanadium with a content of up to about 14% by weight. Compound product according to one of Claims 20 to 24, characterized in that the metallic material in the stretcher is chosen to withstand hetisostatic compaction at 1100-1150 ° C and to be heat-treatment compatible with the durable steel material. Compound product according to claim 26, characterized in that it constitutes a component exposed to wear in a valve, and that the material in the carrier consists of pressure vessel steel. Compound product according to claim 27, characterized in that the durable steel material is free from intentionally added cobalt and forms a wear surface on a component exposed to wear in a valve in a nuclear power plant, the material in the carrier having a composition corresponding to AISI 316L. Compound product according to claim 26, characterized in that it constitutes a wear part, pump part, motor part, roller or other component with a wear surface of the wear-resistant steel material and in such an application that the entire component cannot consist of the wear-resistant steel material. Compound product according to claim 22, characterized in that the coating has a thickness of 0.5-1000 mm, preferably 0.5 -50 mm, and more preferably 0.5-30 IIIIII. Compound product according to claim 23, characterized in that the coating has a thickness of 0.5-10 mm, more preferably 3-5 mm. Use of a steel material produced by powder metallurgy with the following composition in% by weight: C Si Mn Cr Ni M0 + 1 / zW Co S N 0.012 0.01 ~ 3.0 0.01 ~ 10.0 1643 max. 5 0.01f5.0 max. 9 max. 0.5 0.640 further 0.5-14 of (V + Nb / 2), where the content of on the one hand N and on the other hand (V + Nb / 2) is so balanced in relation to each other that the contents of said substances are 33 15 within an area A ', B °, G, H, A' in a right-angled, plane coordinate system where the content N is abscissa and the content V + Nb / 2 is ordinate and where the coordinates of said points are ABGHN 0.6 1.6 9.8 2.6 V + Nb / z 0.5 0.5 14.0 14.0 and max 7 of any of Ti, Zr and Al, residues essentially only iron and unavoidable impurities , for providing a durable surface area on a support of a metallic material with a different, first composition, said surface area preferably constituting a wear surface on a valve. Use according to claim 32, characterized in that said valve is a valve in a nuclear power plant, preferably a valve in the primary circuit of a nuclear power plant.
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    同族专利:
    公开号 | 公开日
    EP2349615A4|2013-09-25|
    KR20110089338A|2011-08-05|
    EP2349615A1|2011-08-03|
    WO2010053431A1|2010-05-14|
    RU2011116293A|2012-12-20|
    US20110217567A1|2011-09-08|
    SE533991C2|2011-03-22|
    CN102271843A|2011-12-07|
    TW201026495A|2010-07-16|
    CA2740971A1|2010-05-14|
    JP2012507636A|2012-03-29|
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    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    SE0850068A|SE533991C2|2008-11-06|2008-11-06|Process for the manufacture of a compound product having an area of durable coating, such a compound product and the use of a steel material to provide the coating|SE0850068A| SE533991C2|2008-11-06|2008-11-06|Process for the manufacture of a compound product having an area of durable coating, such a compound product and the use of a steel material to provide the coating|
    RU2011116293/02A| RU2011116293A|2008-11-06|2009-11-03|METHOD FOR PRODUCING A COMPOSITE PRODUCT WITH A SURFACE AREA OF WEAR-RESISTANT COATING, PRODUCT AND APPLICATION OF STEEL FOR PRODUCING A COATING|
    EP09825059.0A| EP2349615A4|2008-11-06|2009-11-03|Method for the manufacture of a compound product with a surface region of a wear resistant coating, such a product and the use of a steel material for obtaining the coating|
    US13/126,030| US20110217567A1|2008-11-06|2009-11-03|Method for the manufacture of a compound product with a surface region of a wear resistant coating, such a product and the use of a steel material for obtaining the coating|
    KR1020117013024A| KR20110089338A|2008-11-06|2009-11-03|Method for the manufacture of a compound product with a surface region of a wear resistant coating, such a product and the use of a steel material for obtaining the coating|
    PCT/SE2009/051242| WO2010053431A1|2008-11-06|2009-11-03|Method for the manufacture of a compound product with a surface region of a wear resistant coating, such a product and the use of a steel material for obtaining the coating|
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    CA2740971A| CA2740971A1|2008-11-06|2009-11-03|Method for the manufacture of a compound product with a surface region of a wear resistant coating, such a product and the use of a steel material for obtaining the coating|
    TW098137519A| TW201026495A|2008-11-06|2009-11-05|Method for the manufacture of a compound product with a surface region of a wear resistant coating, such a product and the use of a steel material for obtaining the coating|
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