Patent Application
20180066331
The present disclosure relates to a method of producing a tube of a duplex stainless steel, in particular a duplex stainless steel suitable for use in fuel injection systems for injection of fuel into the combustion chamber of a combustion engine.
In connection to the design of Gasoline Direct Injection (GDI) systems for the automotive industry, it has been suggested to use duplex stainless steel for the rails used for conducting fuel to be injected into the combustion chamber of a combustion engine.
The requirements on a tube to be used as a GDI-rail are several, and must be considered when designing the duplex stainless steel to be used in such an application. It is thus of importance to select a chemical composition of the duplex stainless steel that, in combination with a properly chosen tube manufacturing process, results in a predetermined austenite/ferrite ratio, a requested corrosion resistance (resistance against general corrosion as well as against pitting corrosion), a microstructure essentially free from intermetallic phases, in particular sigma phase and chromium nitrides, a predetermined impact toughness, a predetermined tensile strength and a predetermined fatigue strength.
Furthermore, the mechanical properties of the duplex steel should be such that the obtained tube will present a predetermined burst pressure, i.e. internal pressure until failure, which is high enough for the envisaged application, also when the wall thickness of the tube is relatively small, thereby enabling a GDI-rail that requires less space and weight. The corrosion and fatigue properties should guarantee the endurance of the tube over time.
Designing of a duplex stainless steel and the process of producing a tube thereof assumed to meet the requirements of a GDI-rail is therefore a complex task. The selected chemical composition and the production process parameters must be tuned with regard to each other. Accordingly, once a nominal chemical composition has been decided for the duplex stainless steel, the production process parameters must also be selected with regard thereto. The chemical composition of the duplex stainless steel should also promote a cost efficient production process. In other words, the chemical composition should not be such that it will require excessively complicated, energy-consuming or time-consuming production steps.
The aspect of the present disclosure is to present a method of producing a tube of a duplex stainless steel that enables the production of a tube of said duplex stainless steel presenting properties making the tube suitable to applications in which there are high requirements on corrosion resistance (resistance against general corrosion as well as against pitting corrosion), a predetermined impact toughness, a predetermined tensile strength and a predetermined fatigue strength.
One such application is a GDI-rail for conducting fuel to be injected into the combustion chamber of a combustion engine. The duplex stainless steel of said tube should present a microstructure essentially free from intermetallic phases, in particular sigma phase and chromium nitrides. The chemical composition of the duplex stainless steel shall enable cost-efficient production of a tube thereof in terms of promoting the use of cost-efficient process steps.
The aspects mentioned above are achieved by the present disclosure which provides a method of producing a tube of duplex stainless steel comprising the following composition, in weight % (wt %),
and
Thus, it has been found that to reach optimal material properties, the annealing temperature, the annealing time and the annealing atmosphere. It has been found that the annealing temperature should be in the range of from 950 to 1060° C. and the atmosphere should comprise a gas mixture of 1-6 vol % nitrogen and the remainder is selected from H2 or an inert gas and the annealing should be performed in a time period of from 0.3-10 minutes
If lower annealing temperatures are used, there is a risk of forming un-wanted precipitates, such as intermetallic phases. Additionally, the recrystallization will be slower and therefore an increased soaking time will be required for completing the recrystallization, thus having a negative impact on productivity.
In principal, the upper temperature limit for the annealing step is set by the temperature at which the duplex stainless steel will start to melt. However, there are also practical reasons for why the annealing temperature shall be further restricted. At temperatures higher than the provided interval, the duplex stainless steel will become softer, which will increase the risk of damages during the annealing step. Also, at high temperatures, the grain growth will increase making it more difficult to obtain a good process and grain size control.
It is also very important to use an annealing temperature which will balance the phase fraction, a too low temperature will cause too low ferrite content and a too high temperature will provide too high ferrite content. The temperature of the annealing step will also influence the chemical composition of the ferrite and the austenite phase, so the annealing temperature needs to be balanced together with the chemical composition to ensure that both these phases will have good corrosion resistance.
The time period for which the tube is subjected to the annealing temperature should be between 0.3 to 10 minutes, such as 0.3 to 5 minutes, such as 0.3 to 2.5-minutes. This time period needs to be long enough to ensure complete recrystallization. However, if said time period is too long, the obtained tube will have a coarse structure which will have a negative impact on the mechanical properties. The larger the thickness of the tube wall, the longer the annealing time. Wall thicknesses of from about 1 mm up to about 5 mm are conceived.
Furthermore, the atmosphere of the annealing step is very important. An atmosphere comprising nitrogen will affect the content of nitrogen in the surface of the duplex stainless steel. Hence, the role of nitrogen in the atmosphere is to maintain the nitrogen content of the material at the surface. At the annealing temperature of the present method, nitrogen will diffuse into and out from the material. The nitrogen content should be selected so that the nitrogen content in the surface is maintained. It has been found that too low nitrogen content in the atmosphere where the annealing is performed will result in a net loss of nitrogen in the surface, which will affect the corrosion resistance and the mechanical properties of the duplex stainless steel as defined hereinabove or hereinafter negatively. It has also been found that too high nitrogen levels in the atmosphere where annealing is performed will result in an increase of nitrogen in the surface of the material during annealing and as nitrogen is a strong austenite former, a change in the nitrogen content may therefore influence the phase balance. Hence, a high content of nitrogen in the atmosphere will provide for the formation of austenite in the surface. The nitrogen content in the surface of the material will also influence the structure stability with respect to the sensitivity of forming precipitates, such as chromium nitrides. The formation of precipitates will have a negative impact on the corrosion resistance of the duplex stainless steel as defined hereinabove or hereinafter.
The pitting corrosion resistance equivalent PRE is defined as PRE=Cr(wt %)+3.3 Mo(wt %)+16N(wt %). A PRE of at least about 23.0 indicates that, with the above-defined composition, all three of chromium, molybdenum and nitrogen are not allowed to be at their minimum simultaneously but must be combined such that the defined PRE-value is obtained. According to another embodiment, the PRE-value is at least about 24.0. The term “about” as used hereinabove and hereinafter indicates +/−10% of an integer.
According to one embodiment, the temperature range of the annealing step (step g) is of from 970° C. to 1040° C. According to yet another embodiment, said temperature range is of from 1000° C. to 1040° C.
According to one embodiment, said annealing step comprises subjecting said tube to said temperature for a time period of from 0.5-5 minutes, such as of from 0.5 to 1.5 minutes.
According to one embodiment, the inert gas is argon or helium or a mixture thereof.
According to one embodiment, the content of nitrogen gas in the gas mixture is equal to or less than 4 vol %. According to another embodiment the content of nitrogen gas in said gas mixture is equal to or less than 3 vol %. According to yet one embodiment, the content of nitrogen gas in said gas mixture is equal to or above 1.5 vol %.
According to one embodiment, said hot extrusion step (step e) comprises subjecting said tube to hot extrusion at a temperature in the range of from 1100° C.-1200° C. and a cross-sectional area reduction thereof in the range of from 92-98%. According to one embodiment, said hot extrusion step (step e) comprises subjecting said tube to hot extrusion at a temperature in the range of from 1100° C.-1170° C. and a cross-sectional area reduction thereof in the range of from 92-98%. The cross-sectional area reduction is defined as (cross-sectional area (of tube) before extrusion minus cross-sectional area after extrusion)/(cross-sectional area before extrusion). The extrusion temperature and deformation degree is chosen with regard to the chemical composition of the duplex stainless steel such that it will not have a detrimental effect on the microstructure of the duplex stainless steel or will result in cracks or the like therein that would be detrimental to the mechanical properties of the final product.
According to one embodiment, the cold deformation step (step f) comprises subjecting the tube to cold deformation without pre-heating the tube. According to one embodiment, said cold deformation step (step f) comprises subjecting said tube to a cross sectional area reduction thereof in the range of 50-90%. Cross-sectional area reduction is defined as (cross-sectional area (of tube) before pilgering minus cross-sectional area after pilgering)/(cross-sectional area before pilgering). The chemical composition of the duplex stainless steel is selected to enable such cold deformation thereof without unwanted crack-generation in the material or any detrimental negative effects on the microstructure of the material.
According to one embodiment of the method as defined hereinabove or hereinafter, the cold deformation is either pilgering or cold drawing.
According to one embodiment, when the cold deformation is pilgering, the relationship between the wall thickness reduction and the outer diameter reduction of the tube is expressed as the Q-value, wherein
Q-value=(Wallh−Wallt)*(Odh−Wallh)/Wallh ((Odh−Wallh)−(Odt−Wallt)),
wherein
Wallh=hollow wall=the thickness of the wall before pilgering
Wallt=tube wall=the thickness of the wall after pilgering
Odh=hollow OD=the diameter of the tube before pilgering
Odt=tube OD=the diameter of the tube after pilgering,
and wherein Q is in the range of 0.5-2.5. If the area reduction is too high, the force will be too high and the material might crack.
According to yet another embodiment, Q is in the range of from 0.9-1.1.
According to one embodiment, said duplex stainless steel has the following composition, in weight %:
balance Fe and unavoidable impurities.
A duplex stainless steel with this chemical composition is particularly suitable to be subjected to the above-mentioned process steps with the above-mentioned process parameters. In other words, the process steps and parameters as defined hereinabove or hereinafter are selected to be particularly suitable on a duplex stainless steel with this chemical composition and to result in a tube with properties that makes it particularly suitably in an application as GDI-rail for conduction of a fuel in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine.
According to another embodiment, the tube is a tube for conduction of a fuel in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine. The present disclosure may, as an alternative, be defined as a process of producing a fuel conductor in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine, wherein said process comprises the method defined hereinabove and/or hereinafter for producing a tube of duplex stainless steel. Such a process includes attaching the tube of duplex stainless steel to a further structural member of said combustion engine by means of brazing. The further structural member may be metal, typically austenitic or duplex steel. The method of producing the tube, including the selection of the chemical composition of the duplex stainless steel, also aims at achieving a tube with advantageous brazing properties, in particular a low susceptibility to liquid metal induced embrittlement (LMIE) caused by liquid metal penetration. The brazing includes copper brazing, possibly in a continuous furnace at temperature in the range of from 1100° C.-1140° C.
According to one embodiment, the tube has an outer diameter in the range of from 15-35 mm after said pilgering step. According to one embodiment, this tube is used as a GDI-rail in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
According to another embodiment, the tube has an outer diameter of from 7-10 mm after said pilgering step. According to one embodiment, this tube is used as a fuel line in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
The functions and effects of essential alloying elements of the duplex stainless steel defined hereinabove and hereinafter will be presented in the following paragraphs. The listing of functions and effects of the respective alloying elements is not to be seen as complete, but there may be further functions and effects of said alloying elements. However, it provides a view of the underlying knowledge that should be considered when designing the duplex stainless steel as well as the process parameters of a method for the production of a tube of said duplex stainless steel, in particular a duplex stainless tube aimed for conduction of a fuel in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine.
Carbon, C, has an austenite stabilizing effect and counteracts the transformation from austenitic to martensitic structure upon deformation of the duplex stainless steel. C has a positive effect on the strength of the duplex stainless steel. Therefore, the content of C should be equal to or above 0.01 wt %. However, at too high levels, carbon tends to form unwanted carbides with other alloying elements. The content of C should therefore not be above 0.06 wt %. According to one embodiment, the content of C should not be above 0.025 wt %.
Chromium, Cr, has strong impact on the corrosion resistance of the duplex stainless steel, especially pitting corrosion. According to the present disclosure, the PRE-value is above 23.0. Moreover, Cr improves the yield strength, and counteracts transformation of austenitic structure to martensitic structure upon deformation of the duplex stainless steel. Therefore, the content of Cr should be equal to or above 21.0 wt %. At high levels, an increasing content of Cr results in a higher temperature for unwanted stable sigma phase and a more rapid generation of sigma phase. Therefore, the content of Cr is equal to or less than 24.5 wt %. Cr also has a ferrite-stabilizing effect on the duplex stainless steel. According to one embodiment the content of Cr is equal to or less than 23.5 wt %.
Nickel, Ni, has a positive effect on the resistance against general corrosion. Ni also has a strong austenite-stabilizing effect and counteracts transformation from austenitic to martensitic structure upon deformation of the duplex stainless steel. The content of Ni is therefore equal to or more than 2.0 wt %. According to another embodiment the content of Ni is equal to or more than 3.5 wt %. To some extent the austenite-stabilizing effect of Ni may be compensated for by adjusting the Cr content. The content of Ni should, however, not be more than or equal to 5.5 wt %.
Silicon, Si, is often present in the duplex stainless steel since it may have been used for deoxidization of the steel melt. Si is a ferrite stabilizer but also counteracts transformation of austenite to martensite in connection to deformation of the duplex stainless steel. It may also improve the corrosion resistance in some environments. However, Si reduces the solubility of nitrogen and carbon and may form unwanted silicides if present at too high levels. Therefore, according to one embodiment, the content of Si in the duplex stainless steel is not more than 1.5 wt %. According to one embodiment, the content of Si in the duplex stainless steel is not more than 0.6 wt %. According to one embodiment the content of Si may be as low as about 0 wt %. According to one embodiment, the content of Si should be equal to or more than 0.35 wt %.
Molybdenum, Mo, has a strong influence on the corrosion resistance of the duplex stainless steel. It heavily influences the PRE thereof. Mo is added in amount of equal to or more than 0.01 wt %. It also has a ferrite-stabilizing effect on the duplex stainless steel. According to one embodiment, the content of Mo is above 0.10 wt %. Mo also increases the temperature at which unwanted sigma-phases are stable and promotes the rate of generation thereof. It is also a relatively expensive alloying element. Therefore, the content of Mo should be equal to or less than 1.0 wt %.
Copper, Cu, has a positive effect on the corrosion resistance. Cu also counteracts transformation of austenite to martensite upon deformation of the duplex stainless steel. It is thus optional to purposively add Cu to the duplex stainless steel. Often, Cu is present in scrapped goods used for the production of steel, and is allowed to remain in the steel at moderate levels. According to one embodiment, the content of Cu may be equal to or more than 0.01 wt %. According to another embodiment, the content of Cu is equal to or more than 0.15 wt %. According to one embodiment, the content of Cu is equal to or less than 1.0 wt %. According to another embodiment, the content of Cu is equal to or less than 0.7 wt %.
Manganese, Mn, has a deformation hardening effect on the duplex stainless steel, and it counteracts the transformation from austenitic to martensitic structure upon deformation of the duplex stainless steel. Mn also has an austenite stabilizing effect. According to one embodiment, the content of Mn in the duplex stainless steel should be equal to or above 0.8 wt %. However, Mn has a negative impact on the corrosion resistance in acids and chloride-containing environments, and it increases the tendency to generation of intermetallic phases. Therefore, the maximum content of Mn should not be above 2.0 wt %. According to one embodiment, the content of Mn is equal to or less than 1.0 wt %.
Nitrogen, N, has a positive effect on the corrosion resistance of the duplex stainless steel and also contributes to deformation hardening. It has a strong effect on the pitting corrosion resistance equivalent PRE. It also has a strong austenite stabilizing effect and counteracts transformation from austenitic structure to martensitic structure upon plastic deformation of the duplex stainless steel, and is therefore added in an amount of 0.05 wt % or higher. According to one embodiment, the content of N should be equal to or more above 0.090 wt %. At too high levels, N tends to form chromium nitrides in the duplex stainless steel, which should be avoided due to its negative effect on ductility and corrosion resistance. Therefore, the content of N should be equal to or lower than 0.3 wt %. According to one embodiment, the content of N is equal to or less than 0.25 wt %.
Phosphorus, P, is an impurity contained in the duplex stainless steel and it is well known that P affects the hot workability negatively. Accordingly, the content of P is set at 0.03 wt % or less.
Sulphur, S, is an impurity contained in the austenitic stainless steel and it will deteriorate the hot workability. Accordingly, the allowable content of S is less than or equal to 0.03 wt %, such as less than or equal to 0.005 wt %.
The duplex stainless steel as defined hereinabove or herein after may optionally comprise one or more of the following elements selected from the group of Al, V, Nb, Ti, O, Zr, Hf, Ta, Mg, Ca, La, Ce, Y and B. These elements may be added during the manufacturing process in order to enhance e.g. deoxidation, corrosion resistance, hot ductility or machinability. However, as known in the art, the addition of these elements has to be limited depending on which element is present. Thus, if added the total content of these elements is less than or equal to 1.0 wt %.
The term “impurities” as referred to herein is intended to mean substances that will contaminate the duplex stainless steel when it is industrially produced, due to the raw materials such as ores and scraps, and due to various other factors in the production process, and are allowed to contaminate within the ranges not adversely affecting the duplex stainless steel as defined hereinabove or hereinafter.
The present disclosure is further illustrated by the following non-limiting examples.
Two melts were made having the following compositions: Fe is the balance for both
The obtained melts were then processed accordingly:
They were casted to bodies by using continuous casting.
Round bars were then formed by forging and the tubes were then formed by boring a hole therein. The diameter of the tubes was then reduced by by using hot extrusion at a temperature in the range of from 1120° C.-1150° C., the obtained tubes had a cross-sectional area reduction of 96-98%. The hot extrusion was followed by pickling to remove glass beads.
The diameter was further reduced by pilgering and subjecting the tubes to a cross sectional area reduction thereof in the range of 80-86%.
The pilgered tubes were then annealed in an atmosphere consisting of a gas mixture comprising about 2% nitrogen gas and remainder argon gas and subjecting the tubes to a temperature of about 1030° C. for a time period of about 1 minute.
In the pilgering step Q is about 1.0.
After annealing, the obtained tubes were subjected to a straightening step. Straightening was performed in a roll straightening machine with a combination of bending and ovalization. The tubes were passed through a series of angled rollers which rotated the tube and applied to it a series of bending movements. During straightening the yield strength is exceeded in order to get a permanent change in shape to obtain a straight tube.
The obtained tubes had on outer diameter in the of 30 mm and the tubes are to be used as a GDI-rail in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
One additional tube of melt 1 was also manufactured according to the method disclosed above. This tube had an outer diameter of from 8 mm after the pilgering step. This tube was also used as a fuel line in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
| Number | Date | Country | Kind |
|---|---|---|---|
| 15163187.6 | Apr 2015 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2016/057831 | 4/8/2016 | WO | 00 |
