CA2414305C - Material with high ballistic protective effect - Google Patents
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- CA2414305C CA2414305C CA002414305A CA2414305A CA2414305C CA 2414305 C CA2414305 C CA 2414305C CA 002414305 A CA002414305 A CA 002414305A CA 2414305 A CA2414305 A CA 2414305A CA 2414305 C CA2414305 C CA 2414305C
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Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F41—WEAPONS
- F41H—ARMOUR; ARMOURED TURRETS; ARMOURED OR ARMED VEHICLES; MEANS OF ATTACK OR DEFENCE, e.g. CAMOUFLAGE, IN GENERAL
- F41H5/00—Armour; Armour plates
- F41H5/02—Plate construction
- F41H5/04—Plate construction composed of more than one layer
- F41H5/0442—Layered armour containing metal
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Ceramic Engineering (AREA)
- General Engineering & Computer Science (AREA)
- Aiming, Guidance, Guns With A Light Source, Armor, Camouflage, And Targets (AREA)
- Powder Metallurgy (AREA)
- Heat Treatment Of Steel (AREA)
- Laminated Bodies (AREA)
Abstract
A process for making an article with ballistic protective effect and an article obtainable thereby, as well as a method of providing an object with ballistic protection provided by a corresponding material. The alloys used for making the article comprise the elements C, Si, Mn, Cr, Ni, Mo and V within certain concentration ranges and contain a limited amount of impurities. This abstract is neither intended to define the invention disclosed in this specification nor intended to limit the scope of the invention in any way.
Description
MATERIAL WITH HIGH BALLISTIC PROTECTIVE EFFECT
The invention relates to the use of known steel alloys as materials for the production of articles with high ballistic protective effect.
The ballistic protective effect of articles, in particular of those made of two-dimensional material, is generally characterized by their security against a puncture by projectiles and fragments when high-energy weapons act upon them. To an increasing degree there is a demand for a high protective effect and simultaneously, a reduced weight of the article or part and an improved economic efficiency of the production thereof.
According to the recognized opinion of those skilled in the art, the mechanical data obtained from conventional tensile impact and notched impact tests do not allow a direct conclusion with respect to the properties of a material under ballistic stress.
Nevertheless, in many cases the values of hardness, impact strength and strength of the material are used as at least a point of reference for predicting the penetration resistance of a protective part. However, ultimately, the "stopped shots" of a sheet metal part characterize its ballistic protective effect.
Assuming by way of approximation that the strength, hardness and toughness of a material do not change with the speed of the stress, it can be predicted that the material of protective parts must have both maximum hardness as well as utmost toughness in order to withstand destruction under ballistic bombardment and to exert a breaking effect on projectiles. For steels and alloys these properties are opposed with respect to their simultaneous maximization so that in terms of stress, in addition to a general improvement of the same, a good balance of toughness and strength of the material is required, in particular upon heat treatment.
Depending upon the desired property profile, carbon steels, low and medium-alloy steels, high-alloy steels and precipitation hardenable alloys with, if necessary, an iron content of less than SS percent by weight have been proposed for products with ballistic protective effect, and in many cases a composite structure and/or a hard layer on the outer surface of the protective part are recognized as being advantageous.
For example, EP-A-180,805 discloses a steel helmet made of a low-alloy boron steel, which steel helmet is sandblasted after heat treatment.
An armor plate with a heat-treated microstructure is known from European Patent 1,052,296, granted December 15, 2004, to ThyssenKrupp Stahl AG, which plate has a yield point of > 1100 N/mm2 as well as a hardness of > 400 HB and, with a carbon content in percent by weight of 0.15 to 0.2, essentially comprises 1 to 2 percent by weight chromium (Cr), 0.2 to 0.7 percent by weight molybdenum (Mo), 1.0 to 2.5 percent by weight nickel (Ni), 0.05 to 0.25 percent by weight vanadium (V), the balance being iron (Fe).
From EP-A-580,062 there is known a process for the manufacture of thick armor plates, in which process the above alloy, with an increased content of carbon and nickel, is first heated in a slab mold to a temperature of above 1150° C, allowed to cool in a forced manner and rolled to the final thickness in the range of 1050 to 900° C, each time with a high forming degree.
A steel armor plate with improved penetration strength against projectiles is described in EP-B-731,332. The plate has a plurality of inclusions which are oriented essentially parallel to the surface of the plate and are concentrated in a region comprising one quarter to three quarters of the thickness of the plate.
EP-B-247,020 discloses an armor plate having a base material of tough steel, onto which is applied by cladding at least one hard steel layer that is to face the impact and is comprised of 0.6 to 1.0 percent by weight carbon (C), 0.2 to 2.0 percent by weight silicon (5i), 0.2 to 2.0 percent by weight manganese (Mn), 0.8 to 2.0 percent by weight chromium (Cr), 0.05 to 1.0 percent by weight molybdenum (Mo), 0.05 to 0.35 percent by weight vanadium (V), the balance being iron (Fe) and steel accompanying impurities. In this case, an interlayer of pure nickel or pure iron having a thickness between 0.1 and 15% of the total plate thickness is arranged between the base material and the cladding, which interlayer is connected to the base material and the cladding by roll-bonding. The interlayer not only facilitates the cladding of the base material, but also prevents the cladding material from flaking off, which cladding material, though heat-treatable to a hardness of 55 to 60 HRC, apparently has low toughness as a result.
In addition to the above low and medium alloy steels, high-alloy chromium steel alloys (CH-A-648,354) and precipitation-hardened or maraging steels (AT-336,659, DE-C-19921961, EP-A-1,008,659) have also been proposed for ballistic protection as an individual part or in composite structure with a hard outer layer, if necessary. Although these types of steels with a high content of alloying elements of up to 50%
can be used advantageously as a material for components with highly effective ballistic protection, they have the disadvantage of'being very expensive.
In view of the foregoing, it would be desirable to have available materials from which products with high ballistic protective effect and a low weight can be manufactured economically and in ,a simple manner. These products or parts should have a high bullet or projectile breaking effect, be made of an iron-based alloy, and should have toughness and strength properties that are adjustable by means of heat treatment, with maximization of both properties. Moreover, the material should be suitable for the production of composites and mufti-layered parts and should also be capable of being surface hardened and welded.
The present invention provides an article having a ballistic protective effect, a process for making such an article which comprises the provision of an alloy and the shaping thereof, and its use in a method of providing ballistic protection.
In the present specification and in the appended claims all concentrations are based on the total weight of the composition (e.g:; alloy), unless indicated otherwise.
Moreover, in the context of concentrations, the term "less than" includes 0 %
by weight, i.e., complete absence. Also, it should be understood that the numerical values given herein are approximate values, i.e., are not limited to the exact value indicated herein.
According to one alternative, the alloy comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities.
In the alloy, the total concentration of phosphorus (P) plus sulfur (S) is Iess than 0.025 P + S < 0.025 percent by weight;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28 percent by weight;
and the total of the grain-boundary active impurity elements arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.01 I
As + Sb + Bi + Sn + Zn + B < O.OI 1 percent by weight. .
The invention relates to the use of known steel alloys as materials for the production of articles with high ballistic protective effect.
The ballistic protective effect of articles, in particular of those made of two-dimensional material, is generally characterized by their security against a puncture by projectiles and fragments when high-energy weapons act upon them. To an increasing degree there is a demand for a high protective effect and simultaneously, a reduced weight of the article or part and an improved economic efficiency of the production thereof.
According to the recognized opinion of those skilled in the art, the mechanical data obtained from conventional tensile impact and notched impact tests do not allow a direct conclusion with respect to the properties of a material under ballistic stress.
Nevertheless, in many cases the values of hardness, impact strength and strength of the material are used as at least a point of reference for predicting the penetration resistance of a protective part. However, ultimately, the "stopped shots" of a sheet metal part characterize its ballistic protective effect.
Assuming by way of approximation that the strength, hardness and toughness of a material do not change with the speed of the stress, it can be predicted that the material of protective parts must have both maximum hardness as well as utmost toughness in order to withstand destruction under ballistic bombardment and to exert a breaking effect on projectiles. For steels and alloys these properties are opposed with respect to their simultaneous maximization so that in terms of stress, in addition to a general improvement of the same, a good balance of toughness and strength of the material is required, in particular upon heat treatment.
Depending upon the desired property profile, carbon steels, low and medium-alloy steels, high-alloy steels and precipitation hardenable alloys with, if necessary, an iron content of less than SS percent by weight have been proposed for products with ballistic protective effect, and in many cases a composite structure and/or a hard layer on the outer surface of the protective part are recognized as being advantageous.
For example, EP-A-180,805 discloses a steel helmet made of a low-alloy boron steel, which steel helmet is sandblasted after heat treatment.
An armor plate with a heat-treated microstructure is known from European Patent 1,052,296, granted December 15, 2004, to ThyssenKrupp Stahl AG, which plate has a yield point of > 1100 N/mm2 as well as a hardness of > 400 HB and, with a carbon content in percent by weight of 0.15 to 0.2, essentially comprises 1 to 2 percent by weight chromium (Cr), 0.2 to 0.7 percent by weight molybdenum (Mo), 1.0 to 2.5 percent by weight nickel (Ni), 0.05 to 0.25 percent by weight vanadium (V), the balance being iron (Fe).
From EP-A-580,062 there is known a process for the manufacture of thick armor plates, in which process the above alloy, with an increased content of carbon and nickel, is first heated in a slab mold to a temperature of above 1150° C, allowed to cool in a forced manner and rolled to the final thickness in the range of 1050 to 900° C, each time with a high forming degree.
A steel armor plate with improved penetration strength against projectiles is described in EP-B-731,332. The plate has a plurality of inclusions which are oriented essentially parallel to the surface of the plate and are concentrated in a region comprising one quarter to three quarters of the thickness of the plate.
EP-B-247,020 discloses an armor plate having a base material of tough steel, onto which is applied by cladding at least one hard steel layer that is to face the impact and is comprised of 0.6 to 1.0 percent by weight carbon (C), 0.2 to 2.0 percent by weight silicon (5i), 0.2 to 2.0 percent by weight manganese (Mn), 0.8 to 2.0 percent by weight chromium (Cr), 0.05 to 1.0 percent by weight molybdenum (Mo), 0.05 to 0.35 percent by weight vanadium (V), the balance being iron (Fe) and steel accompanying impurities. In this case, an interlayer of pure nickel or pure iron having a thickness between 0.1 and 15% of the total plate thickness is arranged between the base material and the cladding, which interlayer is connected to the base material and the cladding by roll-bonding. The interlayer not only facilitates the cladding of the base material, but also prevents the cladding material from flaking off, which cladding material, though heat-treatable to a hardness of 55 to 60 HRC, apparently has low toughness as a result.
In addition to the above low and medium alloy steels, high-alloy chromium steel alloys (CH-A-648,354) and precipitation-hardened or maraging steels (AT-336,659, DE-C-19921961, EP-A-1,008,659) have also been proposed for ballistic protection as an individual part or in composite structure with a hard outer layer, if necessary. Although these types of steels with a high content of alloying elements of up to 50%
can be used advantageously as a material for components with highly effective ballistic protection, they have the disadvantage of'being very expensive.
In view of the foregoing, it would be desirable to have available materials from which products with high ballistic protective effect and a low weight can be manufactured economically and in ,a simple manner. These products or parts should have a high bullet or projectile breaking effect, be made of an iron-based alloy, and should have toughness and strength properties that are adjustable by means of heat treatment, with maximization of both properties. Moreover, the material should be suitable for the production of composites and mufti-layered parts and should also be capable of being surface hardened and welded.
The present invention provides an article having a ballistic protective effect, a process for making such an article which comprises the provision of an alloy and the shaping thereof, and its use in a method of providing ballistic protection.
In the present specification and in the appended claims all concentrations are based on the total weight of the composition (e.g:; alloy), unless indicated otherwise.
Moreover, in the context of concentrations, the term "less than" includes 0 %
by weight, i.e., complete absence. Also, it should be understood that the numerical values given herein are approximate values, i.e., are not limited to the exact value indicated herein.
According to one alternative, the alloy comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities.
In the alloy, the total concentration of phosphorus (P) plus sulfur (S) is Iess than 0.025 P + S < 0.025 percent by weight;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28 percent by weight;
and the total of the grain-boundary active impurity elements arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.01 I
As + Sb + Bi + Sn + Zn + B < O.OI 1 percent by weight. .
In a preferred embodiment according to this alternative, the alloy comprises one or more elements have the concentrations, in percent by weight:
Carbon (C) 0.36 to ' 0.64, preferably 0.41 to 0.58;
Silicon (Si) 0.36 to 0.9, preferably 0.41 to 0.68;
Manganese (Mn) 0.36 to 0.7, preferably 0.41 to 0.59;
Chromium (Cr) I .7 to 5.95, preferably 2.61 to 5.2;
Molybdenum (Mo) 1.05 to 2.9, preferably 1.3 to 2:7;
Vanadium (V) 0.36 to I.25, preferably' 0.39 to 0.83:
According to a second alternative, the alloy comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) O.I to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni} 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities.
In the alloy, the total concentration of phosphorus (P) plus sulfur (S) is less than 0.025 P + S < 0.025 percent by weight;
the concentration of molybdenum (Mo) is less than 0.34 and that of tungsten (W} is below 0.29, with the total value of molybdenunn (Mo) plus tungsten (W) divided by two not exceeding 0.38 Mo < 0.34 percent by weight;
W < 0.29 percent by weight;
Mo + ~ < 0.38 percent by weight;
and the total of the grain-boundary active impurity elements arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011 percent by weight.
In a preferred aspect according to this alternative, the alloy comprises one or more elements of the same having the concentrations, in percent by weight:
Carbon (C) 0.36 to 0.54, preferably 0.41 to 0.49;
Silicon (Si) 0.11 to 0.39;
Manganese (Mn) 0.18 to 0.49, preferably 0.25 to 0.38;
Chromium (Cr) 1.15 to 1.4;
Nickel (Ni) 2.56 to 4.9, preferably 2.9 to 3.9;
Carbon (C) 0.36 to ' 0.64, preferably 0.41 to 0.58;
Silicon (Si) 0.36 to 0.9, preferably 0.41 to 0.68;
Manganese (Mn) 0.36 to 0.7, preferably 0.41 to 0.59;
Chromium (Cr) I .7 to 5.95, preferably 2.61 to 5.2;
Molybdenum (Mo) 1.05 to 2.9, preferably 1.3 to 2:7;
Vanadium (V) 0.36 to I.25, preferably' 0.39 to 0.83:
According to a second alternative, the alloy comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) O.I to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni} 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities.
In the alloy, the total concentration of phosphorus (P) plus sulfur (S) is less than 0.025 P + S < 0.025 percent by weight;
the concentration of molybdenum (Mo) is less than 0.34 and that of tungsten (W} is below 0.29, with the total value of molybdenunn (Mo) plus tungsten (W) divided by two not exceeding 0.38 Mo < 0.34 percent by weight;
W < 0.29 percent by weight;
Mo + ~ < 0.38 percent by weight;
and the total of the grain-boundary active impurity elements arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011 percent by weight.
In a preferred aspect according to this alternative, the alloy comprises one or more elements of the same having the concentrations, in percent by weight:
Carbon (C) 0.36 to 0.54, preferably 0.41 to 0.49;
Silicon (Si) 0.11 to 0.39;
Manganese (Mn) 0.18 to 0.49, preferably 0.25 to 0.38;
Chromium (Cr) 1.15 to 1.4;
Nickel (Ni) 2.56 to 4.9, preferably 2.9 to 3.9;
for use as a material, and improved properties can be achieved by these in a firing test. A
further increase in the property profile is obtained by reducing the sulfur content to below 0.005 percent by weight.
The process of the invention can further comprise subjecting the alloy to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum-arc remelting, electrosIag remelting (optionally under pressure), powder metallurgy or any combination thereof.
In another aspect of the article is subjected to a heat treatment to a strength of higher than 1800 N/mm2, e.g., higher than 2000 N/mm2, or even higher than 2100 N/mm2.
The invention further provides an article for providing ballistic protection.
The article comprises an alloy as set forth above (first and second alternatives), has a strength of higher than 1800 NImm2, e.g., higher than 2000 N/mm2 or even higher than N/mm2, and may have been processed as indicated above. Preferably, the article has a toughness at room temperature of higher than SEP 150 J, e.g., higher than SEP
185 J, or even higher than SEP 245 J. The article can comprise a plate, e.g., a plate having a thickness of at least 5 mm.
The invention also provides a method of providing an object (including the human or animal body) with ballistic protection. According to this method, at least one of the surfaces of the object is covered (completely or partially) with a material comprising an alloy selected from those indicated above. The alloy and/or the material may have been processed as set forth above. Furthermore, the material may show the strength and toughness properties indicated.
The advantages achieved with the invention according to the first alternative as set forth above essentially can be seen in that limiting the content of the impurity elements sulfur and phosphorus to a combined value of less than 0.025 percent by weight results in a high toughness of the material, if, as has been found, at the same time the total concentration of the additional impurity components arsenic, antimony, bismuth, tin, zinc and boron is kept below 0.011 percent by weight. Because nickel in interaction with the other alloying elements, in particular molybdenum and vanadium, surprisingly increases the danger of a grain-boundary coating, the upper limit of the nickel content is less than 0.28 percent by weight. The advantageous properties achieved by the invention manifest themselves in a firing test by a high proportion of stopped shots, and are particularly apparent in parts that have been heat-treated to a strength of higher than 1900 N/mm2. A still further improvement in the properties of the material is achieved when the sulfur content is kept below 0.005 percent by weight.
Excellent results are achieved in a firing test if one or more of the above elements are present in the following concentrations, in percent by weight:
Carbon (C) 0.36 to 0.64, preferably0.4I to 0.58;
Silicon (Si) 0.36 to 0.9, preferably0.41 to 0.68;
Manganese (Mn) 0.36 to 0.7, preferably0,4I to 0.59;
Chromium (Cr} 1.7 to 5.95, preferably2.61 to 5.2;
Molybdenum (Mo)1.05 to 2.9, preferably1.3 to 2.7;
Vanadium (V) 0.36 to 1.25, preferably0.39 to 0.83.
When present in the above concentrations, the selected elements, in close coordination with the other alloying elements, have a positive effect on the microstructural transformations during heat treatment, i.e., promote an increase in hardness without interfering regions at the grain boundaries, and guarantee the formation of a largely homogeneous heat-treated microstructure during tempering.
It also has been found that, in addition to the above-mentioned high purity or low content of impurity elements, respectively, of the material used according to the invention, the manufacturing technology has an effect on the ballistic protective effect of parts made thereof. In other words, the manufacturing technologies Ladle metallurgy, vacuum 'treatment, vacuum smelting or vacuum-arc remelting, electroslag remelting (optionally under pressure) and powder metallurgy, individually and in any combination thereof, can have an improving effect on the ballistic protection provided by parts produced in such manner, because the isotropy of the material in particular is promoted thereby. In this regard, a heat treatment can produce higher strength values with improved material toughness; whereby the product is given a substantially increased resistance to puncture by projectiles.
If the material has a strength of higher than 1800 N/mmz, preferably higher than 2000 N/mm2, in particular above 2100 N/mm2, with a toughness at room temperature of higher than SEP 150 J, preferably higher than I85 J, in particular above 245 J, measured in accordance with SEP 1314 (Stahl Eisen Prufblatt = Steel Iron Testing Standard), the maximum penetration resistance or strength, respectively, can be achieved with low alloying costs of the products.
The advantages achieved with the invention according to the second alternative as set forth above essentially~can be seen in that, on the one hand, by selecting the alloying elements and their respective concentrations, a desired high material strength can be achieved by means of a heat treatment: As has been found, a high toughness of the material can, on the other hand, be achieved by means of three additional alloying measures. By limiting the total concentration of sulfur and phosphorus, which elements may interact with respect to a formation of inclusions and embrittlement caused by the coating of grain boundaries, at least the prerequisite for high toughness of the material is provided. The elements molybdenum and tungsten which per se can have a strength increasing effect in alloys, individually and in combination show the tendency to concentrate in an embrittling manner at grain boundaries in the material so that the above-mentioned limitation of the concentrations thereof has a toughness promoting effect. It has also been found that, even in low concentrations, the impurity elements arsenic, antimony, bismuth, tin, zinc, and boron cause a steep drop in the toughness of the material when high mechanical stresses act on the material abruptly, as in the case of, e.g., the bombardment of a part made thereof, which is the reason why the total concentration thereof is limited according to the invention. As also mentioned at the outset, the mechanical properties of a material as determined by means of conventional tests may change substantially when a high-energy weapon acts on the material so that, strictly speaking, the penetration resistance to bullets or fragments as well as the cracking behavior of protective parts can only be evaluated by means of a firing test.
The alloy used according to the present invention shows special advantages as a material for products with high ballistic protective effect, not only because of the improved properties associated therewith, but also for economic reasons. In particular, the total concentration of the alloying elements in the alloy is below 8.8 percent by weight, and a low-distortion heat treatment can be performed therewith. The material also shows adequate weldability for component production, e.g., for armor-plating limousines.
Even further improved properties can be achieved in a bring test if one or more of the above elements are present the following concentrations, in percent by weight:
Carbon (C) 0.36 to 0.54, preferably 0.41 to 0.49;
Silicon (Si) 0.11 to 0.39;
Manganese 0.18 to 0.49, preferably 0.25 to 0.38;
(Mn) Chromium (Cr)1.15 to 1.4;
Nickel (Ni) 2.9 to 4.9, preferably 2.56 to 3.9.
A further improvement in the property profile is obtained by reducing the sulfur content to below 0.005 percent by weight.
The advantageous properties of the material that are achieved according to the second alternative of the invention are particularly apparent during a bombardment, if the parts are heat-treated to strength values of above 1900 N/mm2. One of the reasons therefor is that a narrower range of the concentration of a respective alloying element which interacts with the other components of the alloy favorably influences the transformation and the development of the microstructure of the material during heat treatment, whereby the increase in hardness and the tempering behavior are improved, resulting in an extensive isotropy with low internal stresses.
The manufacturing technologies ladle metallurgy, vacuum treatment, vacuum smelting or vacuum arc remelting, electroslag remelting (optionally under pressure) and powder metallurgy, individually and in any combination thereof, can have an improving effect on the ballistic protection provided by parts produced in such manner, because the isotropy of the material in particular is promoted thereby, also with regard to microsegregations. In this way, an increase in the toughness of the material can occur in all directions even with heat treatment to higher strengths of the material, and the resistance to puncture by projectiles can be increased.
When the material has a strength of higher than 1800 NImm2, preferably higher . than 2000 N/mm2, in particular above 2100 N/mm2, with a toughness at room temperature of higher than SEP 150 J, preferably higher than 185 J, in particular above 245 J, measured in accordance with SEP 1314 ~Stahl Eisen Priifblatt = Steel Iron Testing Standard), products and protective components, respectively, with a maximum penetration resistance can be produced therefrom.
The present invention is further described in the detailed description which follows, with reference to the noted plurality of drawings by way of non-limiting examples of exemplary embodiments of the present invention, in which like reference numerals represent similar parts throughout the several views of the drawings, and wherein:
Fig. 1 shows the percentage of stopped shots as a function of the thickness of a plate made of an alloy used according to the first alternative of the present invention, a managing steel and a carbon steel, respectively; and Fig. 2 shows the percentage of stopped shots as a function of the thickness of a plate made of an alloy used according to the second alternative of the present invention, a managing steel and a carbon steel, respectively.
The particulars shown herein are by way of example and for purposes of illustrative discussion of the embodiments of the present invention only and are presented in the cause of providing what is believed to be the most useful and readily understood description of the principles and conceptual aspects of the present invention.
In this regard, no attempt is made to show structural details of the present invention in more detail than is necessary for the fundamental understanding of the present invention, the description taken with the drawings making apparent to those skilled in the art how the several forms of the present invention may be embodied in practice.
The invention according to the first alternative will in the following be explained in greater detail, with reference to Examples 1 and 2.
Example 1 A plate made of an ESU (electroslag remelting) block and having a plate thickness of 6.6 mm and a composition, in percent by weight, of 0.49 carbon (C), 0.59 silicon (Si), 0.3 manganese (Mn), 0.004 sulfur (S), 0.019 phosphorus (P), 3.23 chromium (Cr), 1.37 molybdenum (Mo), 0.29 vanadium (V) as well as 0.19 nickel (Ni), the balance being iron (Fe) and accompanying elements (arsenic, antimony, bismuth, tin, zinc and boron) in a total concentration of 0.008 was heat-treated to a hardness of 56 ~ 1 HRC and subjected to a firing test with 100 rounds, of which 93 shots were stopped. A
plate made of heat-treated carbon steel was also tested under the same firing conditions, and stopped 57 shots.
Example 2 A plate made of Cr-Mo-V steel, treated by ladle metallurgy and vacuum degassed and having a composition, in percent by weight, of 0.45 carbon (C), 0.62 silicon (Si), 0.64 manganese (Mn), 0.016 phosphorus (P), 0.007 sulfur (S), 3.35 chromium (Cr), 1.62 molybdenum (Mo), and 0.32 vanadium (V) was rolled from a slab ingot to a thickness of 7.5 mm. Specimens were fabricated from the plate, heat treated with different technologies and tested. Table 1 shows the heat treatment parameters and the mechanical values obtained.
Table 1 SpecimenHardeningTemperingNumberRm Rpp A Notched Hardness No. Temperature 2 impact strength C C N/mm'N/mm' % 3 Mean HRC
A 930 300 I 1941 1441 6.2167 180166 171 55 B 930 300 1 1872 1471 7.684 209160 151 53 C 950 300 I 1975 1576 5.661 201171 144 55 The effect of different heat treatment parameters on the mechanical properties of the material is evident from the above results. This clearly suggests an easy adjustment of the desired product properties according to the invention.
About 60% more shots were stopped in the firing test by the plate according to the invention as compared with a plate of heat-treated carbon steel of the same thickness.
In another test, a comparison was made of plates according to the invention with plates made of carbon steel and maraging steel with regard to stopped shots. The indicated values (those plotted in Fig. 1 ) represent respective mean values of results from at least three shots.
Fig. 1 shows the percentage of stopped shots as a function of the plate thickness.
Starting from a sheet thickness of 6 mm upwards, the proportion of shots stopped by a plate produced according to the present invention and a plate produced from a maraging steel is virtually the same under the same bombardment conditions. With regard to economic efficiency, it should be noted that in the material according to the invention, the concentration of alloying elements is about 6%, whereas it is 41.5% in the maraging steel (comparison material), which makes the latter material substantially more expensive than the former.
The invention according to the second alternative will be explained in greater detail with reference to Examples 3 and 4.
Example 3 A plate having a thickness of 6.8 mm was rolled from a slab ingot made of a vacuum treated steel having a composition, in percent by weight, of 0.5 carbon (C), 0.32 silicon (Si), 0.45 manganese (Mn), 0.017 phosphorus (P), 0.006 sulfur (S), 1.25 chromium (Cr), 0.18 molybdenum (Mo), 0.21 tungsten (W), and 3.97 nickel (Ni), the total concentration of arsenic, antimony, bismuth, tin, and boron being equal to 0.0085.
This rolling stock was tested mechanically after the application of different heat treatment technologies. The results of the corresponding tests are summarized in Table 2.
Table 2 SpecimenHardeningTemperingNumberRm Rpo,2 A Notched Hardness No. Temperature impact - - strength _ o C o C N/mmzN/mmz % J Mean HRC
AA 840 120 1 2229 1207 6.1225 245228 232 55.5 BB 870 120 1 2227 1133 8.6220 245218 227 50 CC 840 120 I 2282 1306 5.595 233173 167 57 'The firing test showed that the plate with the specimen designation AA had a shot stopping capability of 95; whereas a heat treated-plate made of carbon steel of the same thickness withstood only 56 of 100 bombardments from shots.
Example 4 A plate having a thickness of 7.5 mm was manufactured from steel treated by ladle metallurgy and having a composition, in percent by weight, of 0.52 carbon (C), 0.12 silicon (Si), 0.22 manganese (Mn), 0.014 phosphorus (P), 0.003 sulfur (S), I.42 chromium (Cr), O.I 1 molybdenum (Mo), 0.09 tungsten (W), and 0.004 (As + Sb +
Bi +
Sn + Zn + B). The steel had subsequently been subjected to electroslag remelting. Heat treatment to a hardness of 57 HRC, afforded, at a hardening temperature of 880° C and with air cooling after tempering at 200° C, a yield point of the material of Rm = 2265 N/mm2, with an average notched impact strength of 202 J. In the firing test a 68.7%
higher number of stopped shots was recorded as colilpared to a plate made of heat-treated carbon steel under otherwise identical conditions.
In one of the other tests, a comparison was made by means of a firing test with plates according to the present invention and plates made of carbon steel and maraging steel, each heat-treated to the maximum values. Fig. 2 shows the percentage of stopped shots as a function of the plate thickness. Starting at a plate thickness of 5 mm up to a thickness of IO mm, the shots stopped by the maraging steel and those stopped by the steel according to the invention were proportionally essentially the same, with slight advantages for the material according to the invention in the plate thickness range of above 6 mm.
It can be seen from the above results that the use of a material according to the invention has, one the one hand, a clearly higher ballistic protective effect compared with a material made of carbon steel under the same product form and stress conditions and, on the other hand, has a substantially lower proportion of alloying elements than a managing steel and, thus, shows economic advantages in the production thereof.
It is noted that the foregoing examples have been provided, merely for the purpose of explanation and are in no way to be construed as limiting of the present invention.
While the present invention has been described with reference to an exemplary embodiment, it is understood that the words which have been used herein are words of description and illustration, rather than words of limitation. Changes may be made, within the purview of the appended claims, as presently stated. and as amended, without departing from the scope and spirit of the present invention in its aspects.
Although the present invention has been described herein with reference to particular means, materials and embodiments, the present invention is not intended to be limited to the particulars disclosed herein; rather, the present invention extends to all functionally equivalent structures, methods and uses, such as are within the scope of the appended claims.
further increase in the property profile is obtained by reducing the sulfur content to below 0.005 percent by weight.
The process of the invention can further comprise subjecting the alloy to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum-arc remelting, electrosIag remelting (optionally under pressure), powder metallurgy or any combination thereof.
In another aspect of the article is subjected to a heat treatment to a strength of higher than 1800 N/mm2, e.g., higher than 2000 N/mm2, or even higher than 2100 N/mm2.
The invention further provides an article for providing ballistic protection.
The article comprises an alloy as set forth above (first and second alternatives), has a strength of higher than 1800 NImm2, e.g., higher than 2000 N/mm2 or even higher than N/mm2, and may have been processed as indicated above. Preferably, the article has a toughness at room temperature of higher than SEP 150 J, e.g., higher than SEP
185 J, or even higher than SEP 245 J. The article can comprise a plate, e.g., a plate having a thickness of at least 5 mm.
The invention also provides a method of providing an object (including the human or animal body) with ballistic protection. According to this method, at least one of the surfaces of the object is covered (completely or partially) with a material comprising an alloy selected from those indicated above. The alloy and/or the material may have been processed as set forth above. Furthermore, the material may show the strength and toughness properties indicated.
The advantages achieved with the invention according to the first alternative as set forth above essentially can be seen in that limiting the content of the impurity elements sulfur and phosphorus to a combined value of less than 0.025 percent by weight results in a high toughness of the material, if, as has been found, at the same time the total concentration of the additional impurity components arsenic, antimony, bismuth, tin, zinc and boron is kept below 0.011 percent by weight. Because nickel in interaction with the other alloying elements, in particular molybdenum and vanadium, surprisingly increases the danger of a grain-boundary coating, the upper limit of the nickel content is less than 0.28 percent by weight. The advantageous properties achieved by the invention manifest themselves in a firing test by a high proportion of stopped shots, and are particularly apparent in parts that have been heat-treated to a strength of higher than 1900 N/mm2. A still further improvement in the properties of the material is achieved when the sulfur content is kept below 0.005 percent by weight.
Excellent results are achieved in a firing test if one or more of the above elements are present in the following concentrations, in percent by weight:
Carbon (C) 0.36 to 0.64, preferably0.4I to 0.58;
Silicon (Si) 0.36 to 0.9, preferably0.41 to 0.68;
Manganese (Mn) 0.36 to 0.7, preferably0,4I to 0.59;
Chromium (Cr} 1.7 to 5.95, preferably2.61 to 5.2;
Molybdenum (Mo)1.05 to 2.9, preferably1.3 to 2.7;
Vanadium (V) 0.36 to 1.25, preferably0.39 to 0.83.
When present in the above concentrations, the selected elements, in close coordination with the other alloying elements, have a positive effect on the microstructural transformations during heat treatment, i.e., promote an increase in hardness without interfering regions at the grain boundaries, and guarantee the formation of a largely homogeneous heat-treated microstructure during tempering.
It also has been found that, in addition to the above-mentioned high purity or low content of impurity elements, respectively, of the material used according to the invention, the manufacturing technology has an effect on the ballistic protective effect of parts made thereof. In other words, the manufacturing technologies Ladle metallurgy, vacuum 'treatment, vacuum smelting or vacuum-arc remelting, electroslag remelting (optionally under pressure) and powder metallurgy, individually and in any combination thereof, can have an improving effect on the ballistic protection provided by parts produced in such manner, because the isotropy of the material in particular is promoted thereby. In this regard, a heat treatment can produce higher strength values with improved material toughness; whereby the product is given a substantially increased resistance to puncture by projectiles.
If the material has a strength of higher than 1800 N/mmz, preferably higher than 2000 N/mm2, in particular above 2100 N/mm2, with a toughness at room temperature of higher than SEP 150 J, preferably higher than I85 J, in particular above 245 J, measured in accordance with SEP 1314 (Stahl Eisen Prufblatt = Steel Iron Testing Standard), the maximum penetration resistance or strength, respectively, can be achieved with low alloying costs of the products.
The advantages achieved with the invention according to the second alternative as set forth above essentially~can be seen in that, on the one hand, by selecting the alloying elements and their respective concentrations, a desired high material strength can be achieved by means of a heat treatment: As has been found, a high toughness of the material can, on the other hand, be achieved by means of three additional alloying measures. By limiting the total concentration of sulfur and phosphorus, which elements may interact with respect to a formation of inclusions and embrittlement caused by the coating of grain boundaries, at least the prerequisite for high toughness of the material is provided. The elements molybdenum and tungsten which per se can have a strength increasing effect in alloys, individually and in combination show the tendency to concentrate in an embrittling manner at grain boundaries in the material so that the above-mentioned limitation of the concentrations thereof has a toughness promoting effect. It has also been found that, even in low concentrations, the impurity elements arsenic, antimony, bismuth, tin, zinc, and boron cause a steep drop in the toughness of the material when high mechanical stresses act on the material abruptly, as in the case of, e.g., the bombardment of a part made thereof, which is the reason why the total concentration thereof is limited according to the invention. As also mentioned at the outset, the mechanical properties of a material as determined by means of conventional tests may change substantially when a high-energy weapon acts on the material so that, strictly speaking, the penetration resistance to bullets or fragments as well as the cracking behavior of protective parts can only be evaluated by means of a firing test.
The alloy used according to the present invention shows special advantages as a material for products with high ballistic protective effect, not only because of the improved properties associated therewith, but also for economic reasons. In particular, the total concentration of the alloying elements in the alloy is below 8.8 percent by weight, and a low-distortion heat treatment can be performed therewith. The material also shows adequate weldability for component production, e.g., for armor-plating limousines.
Even further improved properties can be achieved in a bring test if one or more of the above elements are present the following concentrations, in percent by weight:
Carbon (C) 0.36 to 0.54, preferably 0.41 to 0.49;
Silicon (Si) 0.11 to 0.39;
Manganese 0.18 to 0.49, preferably 0.25 to 0.38;
(Mn) Chromium (Cr)1.15 to 1.4;
Nickel (Ni) 2.9 to 4.9, preferably 2.56 to 3.9.
A further improvement in the property profile is obtained by reducing the sulfur content to below 0.005 percent by weight.
The advantageous properties of the material that are achieved according to the second alternative of the invention are particularly apparent during a bombardment, if the parts are heat-treated to strength values of above 1900 N/mm2. One of the reasons therefor is that a narrower range of the concentration of a respective alloying element which interacts with the other components of the alloy favorably influences the transformation and the development of the microstructure of the material during heat treatment, whereby the increase in hardness and the tempering behavior are improved, resulting in an extensive isotropy with low internal stresses.
The manufacturing technologies ladle metallurgy, vacuum treatment, vacuum smelting or vacuum arc remelting, electroslag remelting (optionally under pressure) and powder metallurgy, individually and in any combination thereof, can have an improving effect on the ballistic protection provided by parts produced in such manner, because the isotropy of the material in particular is promoted thereby, also with regard to microsegregations. In this way, an increase in the toughness of the material can occur in all directions even with heat treatment to higher strengths of the material, and the resistance to puncture by projectiles can be increased.
When the material has a strength of higher than 1800 NImm2, preferably higher . than 2000 N/mm2, in particular above 2100 N/mm2, with a toughness at room temperature of higher than SEP 150 J, preferably higher than 185 J, in particular above 245 J, measured in accordance with SEP 1314 ~Stahl Eisen Priifblatt = Steel Iron Testing Standard), products and protective components, respectively, with a maximum penetration resistance can be produced therefrom.
The present invention is further described in the detailed description which follows, with reference to the noted plurality of drawings by way of non-limiting examples of exemplary embodiments of the present invention, in which like reference numerals represent similar parts throughout the several views of the drawings, and wherein:
Fig. 1 shows the percentage of stopped shots as a function of the thickness of a plate made of an alloy used according to the first alternative of the present invention, a managing steel and a carbon steel, respectively; and Fig. 2 shows the percentage of stopped shots as a function of the thickness of a plate made of an alloy used according to the second alternative of the present invention, a managing steel and a carbon steel, respectively.
The particulars shown herein are by way of example and for purposes of illustrative discussion of the embodiments of the present invention only and are presented in the cause of providing what is believed to be the most useful and readily understood description of the principles and conceptual aspects of the present invention.
In this regard, no attempt is made to show structural details of the present invention in more detail than is necessary for the fundamental understanding of the present invention, the description taken with the drawings making apparent to those skilled in the art how the several forms of the present invention may be embodied in practice.
The invention according to the first alternative will in the following be explained in greater detail, with reference to Examples 1 and 2.
Example 1 A plate made of an ESU (electroslag remelting) block and having a plate thickness of 6.6 mm and a composition, in percent by weight, of 0.49 carbon (C), 0.59 silicon (Si), 0.3 manganese (Mn), 0.004 sulfur (S), 0.019 phosphorus (P), 3.23 chromium (Cr), 1.37 molybdenum (Mo), 0.29 vanadium (V) as well as 0.19 nickel (Ni), the balance being iron (Fe) and accompanying elements (arsenic, antimony, bismuth, tin, zinc and boron) in a total concentration of 0.008 was heat-treated to a hardness of 56 ~ 1 HRC and subjected to a firing test with 100 rounds, of which 93 shots were stopped. A
plate made of heat-treated carbon steel was also tested under the same firing conditions, and stopped 57 shots.
Example 2 A plate made of Cr-Mo-V steel, treated by ladle metallurgy and vacuum degassed and having a composition, in percent by weight, of 0.45 carbon (C), 0.62 silicon (Si), 0.64 manganese (Mn), 0.016 phosphorus (P), 0.007 sulfur (S), 3.35 chromium (Cr), 1.62 molybdenum (Mo), and 0.32 vanadium (V) was rolled from a slab ingot to a thickness of 7.5 mm. Specimens were fabricated from the plate, heat treated with different technologies and tested. Table 1 shows the heat treatment parameters and the mechanical values obtained.
Table 1 SpecimenHardeningTemperingNumberRm Rpp A Notched Hardness No. Temperature 2 impact strength C C N/mm'N/mm' % 3 Mean HRC
A 930 300 I 1941 1441 6.2167 180166 171 55 B 930 300 1 1872 1471 7.684 209160 151 53 C 950 300 I 1975 1576 5.661 201171 144 55 The effect of different heat treatment parameters on the mechanical properties of the material is evident from the above results. This clearly suggests an easy adjustment of the desired product properties according to the invention.
About 60% more shots were stopped in the firing test by the plate according to the invention as compared with a plate of heat-treated carbon steel of the same thickness.
In another test, a comparison was made of plates according to the invention with plates made of carbon steel and maraging steel with regard to stopped shots. The indicated values (those plotted in Fig. 1 ) represent respective mean values of results from at least three shots.
Fig. 1 shows the percentage of stopped shots as a function of the plate thickness.
Starting from a sheet thickness of 6 mm upwards, the proportion of shots stopped by a plate produced according to the present invention and a plate produced from a maraging steel is virtually the same under the same bombardment conditions. With regard to economic efficiency, it should be noted that in the material according to the invention, the concentration of alloying elements is about 6%, whereas it is 41.5% in the maraging steel (comparison material), which makes the latter material substantially more expensive than the former.
The invention according to the second alternative will be explained in greater detail with reference to Examples 3 and 4.
Example 3 A plate having a thickness of 6.8 mm was rolled from a slab ingot made of a vacuum treated steel having a composition, in percent by weight, of 0.5 carbon (C), 0.32 silicon (Si), 0.45 manganese (Mn), 0.017 phosphorus (P), 0.006 sulfur (S), 1.25 chromium (Cr), 0.18 molybdenum (Mo), 0.21 tungsten (W), and 3.97 nickel (Ni), the total concentration of arsenic, antimony, bismuth, tin, and boron being equal to 0.0085.
This rolling stock was tested mechanically after the application of different heat treatment technologies. The results of the corresponding tests are summarized in Table 2.
Table 2 SpecimenHardeningTemperingNumberRm Rpo,2 A Notched Hardness No. Temperature impact - - strength _ o C o C N/mmzN/mmz % J Mean HRC
AA 840 120 1 2229 1207 6.1225 245228 232 55.5 BB 870 120 1 2227 1133 8.6220 245218 227 50 CC 840 120 I 2282 1306 5.595 233173 167 57 'The firing test showed that the plate with the specimen designation AA had a shot stopping capability of 95; whereas a heat treated-plate made of carbon steel of the same thickness withstood only 56 of 100 bombardments from shots.
Example 4 A plate having a thickness of 7.5 mm was manufactured from steel treated by ladle metallurgy and having a composition, in percent by weight, of 0.52 carbon (C), 0.12 silicon (Si), 0.22 manganese (Mn), 0.014 phosphorus (P), 0.003 sulfur (S), I.42 chromium (Cr), O.I 1 molybdenum (Mo), 0.09 tungsten (W), and 0.004 (As + Sb +
Bi +
Sn + Zn + B). The steel had subsequently been subjected to electroslag remelting. Heat treatment to a hardness of 57 HRC, afforded, at a hardening temperature of 880° C and with air cooling after tempering at 200° C, a yield point of the material of Rm = 2265 N/mm2, with an average notched impact strength of 202 J. In the firing test a 68.7%
higher number of stopped shots was recorded as colilpared to a plate made of heat-treated carbon steel under otherwise identical conditions.
In one of the other tests, a comparison was made by means of a firing test with plates according to the present invention and plates made of carbon steel and maraging steel, each heat-treated to the maximum values. Fig. 2 shows the percentage of stopped shots as a function of the plate thickness. Starting at a plate thickness of 5 mm up to a thickness of IO mm, the shots stopped by the maraging steel and those stopped by the steel according to the invention were proportionally essentially the same, with slight advantages for the material according to the invention in the plate thickness range of above 6 mm.
It can be seen from the above results that the use of a material according to the invention has, one the one hand, a clearly higher ballistic protective effect compared with a material made of carbon steel under the same product form and stress conditions and, on the other hand, has a substantially lower proportion of alloying elements than a managing steel and, thus, shows economic advantages in the production thereof.
It is noted that the foregoing examples have been provided, merely for the purpose of explanation and are in no way to be construed as limiting of the present invention.
While the present invention has been described with reference to an exemplary embodiment, it is understood that the words which have been used herein are words of description and illustration, rather than words of limitation. Changes may be made, within the purview of the appended claims, as presently stated. and as amended, without departing from the scope and spirit of the present invention in its aspects.
Although the present invention has been described herein with reference to particular means, materials and embodiments, the present invention is not intended to be limited to the particulars disclosed herein; rather, the present invention extends to all functionally equivalent structures, methods and uses, such as are within the scope of the appended claims.
Claims (61)
1. A method for making an article with a ballistic-protective effect, comprising:
providing an alloy which comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011; and shaping the alloy to form the article.
providing an alloy which comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011; and shaping the alloy to form the article.
2. The method of claim 1, wherein the alloy comprises one or more of C, Si, Mn, Cr, Mo, and V in the following concentrations, in percent by weight:
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
3. The method of claim 1 or 2, wherein the alloy comprises one or more of C, Si, Mn, Cr, Mo, and V in the following concentrations, in percent by weight:
C 0.41 to 0.58;
Si 0.41 to 0.68;
Mn 0.41 to 0.59;
Cr 2.61 to 5.2;
Mo 1.3 to 2.7;
V 0.39 to 0.83.
C 0.41 to 0.58;
Si 0.41 to 0.68;
Mn 0.41 to 0.59;
Cr 2.61 to 5.2;
Mo 1.3 to 2.7;
V 0.39 to 0.83.
4. The method of claim 1, 2 or 3, wherein the concentration of sulfur in the alloy is less than 0.005 percent by weight.
5. The method of any one of claims 1 to 4, which further comprises subjecting the alloy to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum-arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
6. The method of any one of claims 1 to 5, which further comprises subjecting the article to a heat treatment to a strength of higher than 1800 N/mm2.
7. The method of claim 6, which further comprises subjecting the article to a heat treatment to a strength of higher than 2000 N/mm2.
8. The method of claim 7, which further comprises subjecting the article to a heat treatment to a strength of higher than 2100 N/mm2.
9. An article obtained by the method of any one of claims 1 to 8.
10. An article for providing ballistic protection, the article comprising an alloy which comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011;
and the article having a strength of higher than 1800 N/mm2.
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011;
and the article having a strength of higher than 1800 N/mm2.
11. The article of claim 10, wherein the article has a toughness at room temperature of higher than SEP 150 J.
12. The article of claim 11, wherein the article has a strength of higher than N/mm2.
13. The article of claim 12, wherein the article has a toughness at room temperature of higher than SEP 185 J.
14. The article of claim 13, wherein the article has a strength of higher than N/mm2.
15. The article of claim 14, wherein the article has a toughness at room temperature of higher than SEP 245 J.
16. The article of any one of claims 10 to 15, wherein the article comprises a plate.
17. The article of claim 16, wherein the plate has a thickness of at least 5 mm.
18. The article of any one of claims 10 to 17, wherein the alloy comprises one or more of C, Si, Mn, Cr, Mo, and V in the following concentrations, in percent by weight:
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
19. The article of any one of claims 10 to 17, wherein the alloy comprises one or more of C, Si, Mn, Cr, Mo, and V in the following concentrations, in percent by weight:
C 0.41 to 0.58;
Si 0.41 to 0.68;
Mn 0.41 to 0.59;
Cr 2.61 to 5.2;
Mo 1.3 to 2.7;
V 0.39 to 0.83.
C 0.41 to 0.58;
Si 0.41 to 0.68;
Mn 0.41 to 0.59;
Cr 2.61 to 5.2;
Mo 1.3 to 2.7;
V 0.39 to 0.83.
20. The article of any one of claims 10 to 19, wherein the alloy has been subjected to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum-arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
21. A method of providing an object with ballistic protection, the method comprising:
covering at least one of the surfaces of the object with a material of an alloy which comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011.
covering at least one of the surfaces of the object with a material of an alloy which comprises, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011.
22. The method of claim 21, wherein the alloy comprises C, Si, Mn, Cr, Mo, and V in the following concentrations, in percent by weight:
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
23. The method of claim 21 or 22, wherein the alloy has been subjected to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
24. The method of any one of claims 21, 22 or 23, wherein the material has a strength of higher than 1800 N/mm2 and a toughness at room temperature of higher than SEP 150 J.
25. The method of claim 24, wherein the material has a strength of higher than N/mm2.
26. The method of claim 25, wherein the material has a toughness at room temperature of higher than SEP 185 J.
27. A method for making an article with a ballistic-protective effect, comprising:
providing an alloy which comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011;
and shaping the alloy to form the article.
providing an alloy which comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011;
and shaping the alloy to form the article.
28. The method of claim 27, wherein the alloy comprises one or more of C, Si, Mn, Cr, and Ni in the following concentrations, in percent by weight:
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
29. The method of claim 27 or 28, wherein the alloy comprises one or more of C, Mn, and Ni in the following concentrations, in percent by weight:
C 0.41 to 0.49;
Mn 0.25 to 0.38;
Ni 2.9 to 3.9.
C 0.41 to 0.49;
Mn 0.25 to 0.38;
Ni 2.9 to 3.9.
30. The method of claim 27, 28 or 29, wherein the concentration of sulfur in the alloy is less than 0.005 percent by weight.
31. The method of any one of claims 27 to 30, which further comprises subjecting the alloy to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum-arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
32. The method of any one of claims 27 to 31, which further comprises subjecting the article to a heat treatment to a strength of higher than 1800 N/mm2.
33. The method of claim 32, which further comprises subjecting the article to a heat treatment to a strength of higher than 2000 N/mm2.
34. The method of claim 33, which further comprises subjecting the article to a heat treatment to a strength of higher than 2100 N/mm2.
35. An article obtained by the method of any one of claims 27 to 34.
36. An article for providing ballistic protection, the article comprising an alloy which comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011;
and the article having a strength of higher than 1800 N/mm2.
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As + Sb + Bi + Sn + Zn + B < 0.011;
and the article having a strength of higher than 1800 N/mm2.
37. The article of claim 36, wherein the article has a toughness at room temperature of higher than SEP 150 J.
38. The article of claim 37, wherein the article has a strength of higher than N/mm2.
39. The article of claim 38, wherein the article has a toughness at room temperature of higher than SEP 185 J.
40. The article of claim 39, wherein the article has a strength of higher than N/mm2.
41. The article of claim 40, wherein the article has a toughness at room temperature of higher than SEP 245 J.
42. The article of any one of claims 36 to 41, wherein the article comprises a plate.
43. The article of claim 42, wherein the plate has a thickness of at least 5 mm.
44. The article of any one of claims 36 to 43, wherein the alloy comprises one or more of C, Si, Mn, Cr, and Ni in the following concentrations, in percent by weight:
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
45. The article of any one of claims 36 to 43, wherein the alloy comprises one or more of C, Si, Mn, Cr, and Ni in the following concentrations, in percent by weight:
C 0.41 to 0.49;
Si 0.11 to 0.39;
Mn 0.25 to 0.38;
Cr 1.15 to 1.4;
Ni 2.9 to 3.9.
C 0.41 to 0.49;
Si 0.11 to 0.39;
Mn 0.25 to 0.38;
Cr 1.15 to 1.4;
Ni 2.9 to 3.9.
46. The article of any one of claims 36 to 45, wherein the alloy has been subjected to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
47. A method of providing an object with ballistic protection, the method comprising:
covering at least one of the surfaces of the object with a material of an alloy which comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As+Sb+Bi+Sn+Zn+B < 0.011.
covering at least one of the surfaces of the object with a material of an alloy which comprises, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As+Sb+Bi+Sn+Zn+B < 0.011.
48. The method of claim 47, wherein the alloy comprises C, Si, Mn, Cr, and Ni in the following concentrations, in percent by weight:
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
49. The method of claim 47 or 48, wherein the alloy has been subjected to a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
50. The method of claim 47, 48 or 49, wherein the material has a strength of higher than 1800 N/mm2 and a toughness at room temperature of higher than SEP 150 J.
51. The method of claim 50, wherein the material has a strength of higher than N/mm2.
52. The method of claim 51, wherein the material has a toughness at room temperature of higher than SEP 185 J.
53. Use of an alloy as material for metal sheets which provide ballistic protection, the alloy comprising, in percent by weight:
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As+Sb+Bi+Sn+Zn+B < 0.011.
Carbon (C) 0.26 to 0.79;
Silicon (Si) 0.2 to 1.2;
Manganese (Mn) 0.2 to 0.9;
Chromium (Cr) 1.1 to 7.94;
Molybdenum (Mo) 0.56 to 3.49;
Vanadium (V) 0.26 to 1.74;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of nickel (Ni) is less than 0.28 Ni < 0.28;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As+Sb+Bi+Sn+Zn+B < 0.011.
54. The use of an alloy according to claim 53, wherein the alloy comprises one or more of C, Si, Mn, Cr, Mo; and V in the following concentrations, in percent by weight:
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
C 0.36 to 0.64;
Si 0.36 to 0.9;
Mn 0.36 to 0.7;
Cr 1.7 to 5.95;
Mo 1.05 to 2.9;
V 0.36 to 1.25.
55. The use of an alloy according to claim 53 or 54, wherein the alloy comprises one or more of C, Si, Mn, Cr, Mo, and V in the following concentrations, in percent by weight:
C 0.41 to 0.58;
Si 0.41 to 0.68;
Mn 0.41 to 0.59;
Cr 2.61 to 5.2;
Mo 1.3 to 2.7;
V 0.39 to 0.83.
C 0.41 to 0.58;
Si 0.41 to 0.68;
Mn 0.41 to 0.59;
Cr 2.61 to 5.2;
Mo 1.3 to 2.7;
V 0.39 to 0.83.
56. Use of an alloy as a material for metal sheets which provide ballistic protection, the alloy comprising, in percent by weight:
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As+Sb+Bi+Sn+Zn+B < 0.011,
Carbon (C) 0.3 to 0.6;
Silicon (Si) 0.08 to 0.59;
Manganese (Mn) 0.1 to 0.6;
Chromium (Cr) 0.9 to 1.5;
Nickel (Ni) 2.4 to 5.5;
the balance being iron (Fe) as well as accompanying elements and impurities, provided that the total concentration of phosphorus (P) and sulfur (S) is less than 0.025 P + S < 0.025;
the concentration of molybdenum (Mo) is less than 0.34 and the concentration of tungsten (W) is less than 0.29, with the total of the concentration of molybdenum and the concentration of tungsten divided by 2 not exceeding 0.38 Mo < 0.34;
W < 0.29;
Mo + ~ < 0.38;
and the total concentration of arsenic (As), antimony (Sb), bismuth (Bi), tin (Sn), zinc (Zn) and boron (B) is less than 0.011 As+Sb+Bi+Sn+Zn+B < 0.011,
57. The use of an alloy according to claim 56, wherein the alloy comprises one or more of C, Si, Mn, Cr, and Ni in the following concentrations, in percent by weight:
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
C 0.36 to 0.54;
Si 0.11 to 0.39;
Mn 0.18 to 0.49;
Cr 1.15 to 1.4;
Ni 2.56 to 4.9.
58. The use of an alloy according to claim 56 or 57, wherein the alloy comprises one or more of C, Mn, and Ni in the following concentrations, in percent by weight:
C 0.41 to 0.49;
Mn 0.25 to 0.38;
Ni 2.9 to 3.9.
C 0.41 to 0.49;
Mn 0.25 to 0.38;
Ni 2.9 to 3.9.
59. The use of an alloy according to any one of claims 53 to 58, wherein the concentration of sulfur in the alloy is less than 0.005 percent by weight.
60. The use of an alloy according to any one of claims 53 to 59, wherein the alloy has been produced by a technology selected from ladle metallurgy, vacuum treatment, vacuum smelting, vacuum-arc remelting, electroslag remelting, powder metallurgy and combinations thereof.
61. The use of an alloy according to any one of claims 53 to 60, wherein the alloy has a strength of higher than 1800 N/mm2 and a toughness at room temperature of higher than SEP 150 J.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| AT1992/2001 | 2001-12-19 | ||
| AT1991/2001 | 2001-12-19 | ||
| AT19912001A AT411268B (en) | 2001-12-19 | 2001-12-19 | Iron alloy containing carbon, silicon, manganese, chromium, molybdenum and vanadium is used as a material for products having high ballistic protective action |
| AT19922001A AT411267B (en) | 2001-12-19 | 2001-12-19 | Iron alloy containing carbon, silicon, manganese, chromium and nickel is used as a material for products having a high ballistic protective action |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2414305A1 CA2414305A1 (en) | 2003-06-19 |
| CA2414305C true CA2414305C (en) | 2006-08-15 |
Family
ID=25608562
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002414305A Expired - Fee Related CA2414305C (en) | 2001-12-19 | 2002-12-13 | Material with high ballistic protective effect |
Country Status (6)
| Country | Link |
|---|---|
| US (2) | US20040031353A1 (en) |
| EP (1) | EP1321535B1 (en) |
| BR (1) | BR0205411A (en) |
| CA (1) | CA2414305C (en) |
| DE (1) | DE50202536D1 (en) |
| ES (1) | ES2238556T3 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102007039993A1 (en) * | 2007-08-23 | 2009-02-26 | Edag Gmbh & Co. Kgaa | Structural part for use in vehicle e.g. passenger car, has ballistic plate three-dimensionally molded into piece by using process of hot deformation in molding press and hardened by using vacuum oven after hot deformation |
| DE102008014914B4 (en) * | 2007-08-23 | 2013-07-04 | Vps Vehicle Protection Systems Gmbh | Structural part for a vehicle armor |
| WO2010042260A2 (en) * | 2008-07-11 | 2010-04-15 | Safariland, L Lc | Vacuum sealed protective cover for ballistic panel |
| DE102008052632A1 (en) * | 2008-10-22 | 2010-05-27 | Benteler Automobiltechnik Gmbh | The security cabinet |
| JP5672255B2 (en) | 2012-02-21 | 2015-02-18 | 新日鐵住金株式会社 | Manufacturing method of forged steel roll |
| DE102019116363A1 (en) | 2019-06-17 | 2020-12-17 | Benteler Automobiltechnik Gmbh | Method for the production of an armor component for motor vehicles |
Family Cites Families (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB577133A (en) * | 1940-04-12 | 1946-05-07 | William Herbert Hatfield | A process for improving the properties of iron alloy castings |
| DE1207635B (en) * | 1959-10-13 | 1965-12-23 | Deutsche Edelstahlwerke Ag | Use of a steel alloy as a material for helmets |
| FR2106939A5 (en) * | 1970-09-30 | 1972-05-05 | Creusot Forges Ateliers | Weldable clad steel sheet - for armour plate |
| US3694174A (en) * | 1971-05-13 | 1972-09-26 | Us Army | Dual property steel armor |
| DE2921854C1 (en) * | 1979-05-30 | 1990-11-15 | Thyssen Ind Ag Maschb | Process for producing armor made of multi-layer steel |
| FR2509640A1 (en) * | 1981-07-17 | 1983-01-21 | Creusot Loire | PROCESS FOR PRODUCING A COMPOSITE METAL PART AND PRODUCTS OBTAINED |
| DE3340031C2 (en) * | 1983-11-05 | 1985-11-21 | Thyssen Stahl AG, 4100 Duisburg | Armored sheet metal and process for its manufacture |
| ATA109386A (en) * | 1986-04-23 | 1993-06-15 | Voest Alpine Stahl Linz | TANK PANEL |
| FR2619577B1 (en) * | 1987-08-17 | 1993-02-19 | Aubert & Duval Acieries | SILICON-CHROMIUM-MOLYBDENE-VANADIUM STEEL COMPOSITION AND ITS APPLICATION TO PERFORATING CORES OF ANTI-ARMOR PROJECTILES |
| FR2652821B1 (en) * | 1989-10-09 | 1994-02-18 | Creusot Loire Industrie | HIGH-HARDNESS STEEL FOR SHIELDING AND PROCESS FOR PREPARING SUCH STEEL. |
| DE4223895C1 (en) * | 1992-07-21 | 1994-03-17 | Thyssen Stahl Ag | Process for the production of thick armored sheets |
| US5749140A (en) * | 1995-03-06 | 1998-05-12 | Allegheny Ludlum Corporation | Ballistic resistant metal armor plate |
| JP2000080444A (en) * | 1998-08-31 | 2000-03-21 | Sumitomo Heavy Ind Ltd | Alloy steel for gun barrel |
| EP1052296B1 (en) * | 1999-05-08 | 2004-12-15 | ThyssenKrupp Stahl AG | Use of a steel for the manufacture of amour plates |
| DE19921961C1 (en) * | 1999-05-11 | 2001-02-01 | Dillinger Huettenwerke Ag | Process for producing a composite steel sheet, in particular for protecting vehicles against shelling |
| DE10111304C2 (en) * | 2001-03-09 | 2003-03-20 | Buderus Edelstahlwerke Ag | Process for the production of tubes for heavy guns |
-
2002
- 2002-12-09 EP EP02450278A patent/EP1321535B1/en not_active Expired - Lifetime
- 2002-12-09 DE DE50202536T patent/DE50202536D1/en not_active Expired - Lifetime
- 2002-12-09 ES ES02450278T patent/ES2238556T3/en not_active Expired - Lifetime
- 2002-12-13 CA CA002414305A patent/CA2414305C/en not_active Expired - Fee Related
- 2002-12-17 BR BR0205411-6A patent/BR0205411A/en not_active Application Discontinuation
- 2002-12-18 US US10/321,451 patent/US20040031353A1/en not_active Abandoned
-
2007
- 2007-07-24 US US11/878,344 patent/US20080181807A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| BR0205411A (en) | 2004-07-20 |
| EP1321535A2 (en) | 2003-06-25 |
| US20040031353A1 (en) | 2004-02-19 |
| US20080181807A1 (en) | 2008-07-31 |
| EP1321535A3 (en) | 2003-08-13 |
| DE50202536D1 (en) | 2005-04-28 |
| EP1321535B1 (en) | 2005-03-23 |
| ES2238556T3 (en) | 2005-09-01 |
| CA2414305A1 (en) | 2003-06-19 |
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|
| MKLA | Lapsed |
Effective date: 20191213 |